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Hindawi Publishing CorporationJournal of SpectroscopyVolume 2013 Article ID 217268 13 pageshttpdxdoiorg1011552013217268
Research ArticleXPS Study of Mechanically Activated YBa2Cu3O6+120575 andNdBa2Cu3O6+120575
A V Fetisov1 G A Kozhina1 S Kh Estemirova1 V B Fetisov2 V Ya Mitrofanov1
S A Uporov1 and L B Vedmidrsquo1
1 Institute of Metallurgy Ural Branch of the Russian Academy of Sciences 101 Amundsen Street Ekaterinburg 620016 Russia2 Ural State Academy of Agriculture Karl Liebknecht Street 42 Ekaterinburg 620075 Russia
Correspondence should be addressed to G A Kozhina gakozhinayandexru
Received 27 February 2013 Accepted 30 March 2013
Academic Editor Kong-Thon Tsen
Copyright copy 2013 A V Fetisov et al This is an open access article distributed under the Creative Commons Attribution Licensewhich permits unrestricted use distribution and reproduction in any medium provided the original work is properly cited
Oxides RBa2Cu3O6+120575
(R=Y Nd) subjected to mechanical activation in AGO-2mill have been studied by X-ray photoelectron spec-troscopy (XPS) thermal analysis and magnetometry It has been shown that mechanoactivation accelerates chemical degradationunder the impact of H
2O andCO
2in YBa
2Cu3O6+120575
samples Degradation occurs in the standard way Investigation ofmechanicallyactivated NdBa
2Cu3O6+120575
has revealed other results It has been suggested that CO2can diffuse into its structure more freely
than in YBa2Cu3O6+120575
as a result carbonization may proceed directly in the volume of NdBa2Cu3O6+120575
and independently of thehydrolysis process In addition the mechanism of interaction between the oxide and water is not active and not ldquotraditionalrdquo for thehomologous series REBa
2Cu3O6+120575
(where RE = rare earth and Y)mdashthe characteristic ldquocolorrdquo phase (Nd2BaCuO
5) is not formed
during hydrolysis It is known that high-temperature treatment of NdBa2Cu3O6+120575
oxide results in partial substitution of cationsBa by Nd which is accompanied by decrease in the superconducting transition temperature and formation of the impurity phaseBa2Cu3O5+119910
According to our data mechanical activation of the resulting solid solution Nd1+119909
Ba2minus119909
Cu3O6+120575
unexpectedly hasled to the reverse redistribution of cations which has been manifested in the complete disappearance of the impurity phase andincrease in T
119888
1 Introduction
Compounds RBa2Cu3O6+120575
(R=Y and Ln elements) are wellknown as high-temperature superconductors with the tem-perature of the transition to the superconducting state of 90ndash93K [1] The composition with R=Y is a standard materialfor superconducting electronics under development cooledwith liquid nitrogen [2 3] the magnetic field sensor of 120587SQUID type [2] high current cables [4] and other productsBesides this compound has very significant oxygen diffusionparameters and there is an intention to use it as oxygen-ionconductor [5]
It is also known that the replacement of yttrium byneodymium results in the emergence of so-called ldquoanomalouspeak effectrdquo [6] which leads to significant improvementof the superconducting transport properties of the mate-rial An additional advantage of the oxide NdBa
2Cu3O6+120575
(Nd-123) is its higher chemical stability by comparison with
YBa2Cu3O6+120575
(Y-123) [7 8] The disadvantage of Nd-123is ease of substitution of neodymium by barium ions intheir structural positions during high temperature anneal-ing [8ndash10] with the result that the temperature of thetransition to the superconducting state (119879
119888) of the solid
solution Nd1+xBa2minusxCu3O6+120575 appears to be relatively low and
it decreases rapidly with increasing 119909 (maximum 119879119888equal
to 94K was recorded at 119909 = 0 [9] and 119879119888asymp 80 j 60K
were reported for 119909 = 008 j 016 resp [10]) Effect ofsubstitution of barium by neodymium is amplified at highvalues of temperature and oxygen partial pressure [8 9]Simultaneously with the enrichment of the superconductingoxide by neodymium to comply with cation balance in thesystem the impurity phase depleted in this element (egBaCuO
2[9]) is formed
It should be noted that the superconducting propertiesof the solid solution Nd
1+xBa2minusxCu3O6+120575 can be significantlyreduced even when 119909 rarr 0 due to the mutual penetration
2 Journal of Spectroscopy
of Nd and Ba in the structural position of each other whichcan occur during high-temperature annealing in an oxygenenriched atmosphere [9]
It is known [11] that high-intensity mechanical activa-tion processing (hereinafter MA) can significantly modifyphysicochemical properties of various materials At the sametime such researches focused on the change of the functionalproperties of superconducting oxides RBa
2Cu3O6+120575
(R-123)and to our knowledge have not yet been carried out (existingworks like [12] are devoted to mechanical activation ofprecursors) Apparently this is related to the fact that thechemical stability of these oxides to the impact of air atmo-sphere components is not high even in the normal state [1]Besides mechanical treatment leads to substantial increaseand activation of the free surface contacting with the atmo-sphere and during grinding spalling of R-123 particles occursmainly along the basal plane of the crystallites and exposesthe chemically active structural layer BaO [13] Neverthelessin the present study we have attempted to assess how muchthe surface of R-123 actually degrades under MA and justas importantly what is the influence of this effect on thefunctional properties of these superconducting oxides Wehave limited our investigations to compounds with R=Y Ndwhich are promising for applied developments
Thus the objectives of this work were (1) analysis of thechemical composition of the surface of mechanoactivatedR-123 powders (hereinafter MP) and determination of thedegree of its chemical degradation under the influence ofaggressive components of the environment H
2O and CO
2
(2) analysis of the effect of mechanical activation on thefunctional properties of the superconducting material
To fulfill the tasks we used the following methods X-raydiffraction (XRD) thermal analysis magnetometry and X-ray photoelectron spectroscopy (XPS) The latter is a power-ful tool to study the chemical and even phase compositionof the material locallymdashin the thin layer (nearly 10 nm inthickness) of the external boundary This method allowsdetecting impurity phases occurring at the average volumeconcentration outside the sensitivity of X-ray diffraction andalso phases in the amorphous state
2 Experimental Technique
Oxides R-123 were obtained by stepwise annealing a mixtureof barium nitrate Ba(NO
3)2(ldquochemically purerdquo grade) the
corresponding oxide of the rare earth element (RE) and basiccopper carbonate CuCO
3times Cu(OH)
2(ldquoespecially purerdquo
grade) at 798K for 5 h 998K (5 h) and 1213 K (140 h) Theproducts were subjected to oxidative annealing by slow (withfurnace) cooling from the synthesis temperature to 673K andexposed to this temperature in air for 3 hours The oxygencontent of the samples (6 + 120575) according to the oxidativeannealing conditions can be estimated as 690 plusmn 003 [1] Thethus obtained material was ldquoinitial samplerdquo (hereinafter IP)
In the course of our research we also needed to obtainsamples of Nd
2BaCuO
5and Y
2BaCuO
5to determine the
spectral parameters of these compounds as we did not find
relevant and reliable data in the literature They were synthe-sized at 1000∘C for 23 h from previously obtained Nd-123 andY-123 with the addition of necessary amounts of BaCO
3and
Nd2O3(Y2O3) Before the synthesis homogenized mixtures
of reagents were compressed into tabletsMechanical activation of the synthesized oxides Nd-123
and Y-123 was performed in a high energy AGO-2 planetaryball mill (set material Fe) with acceleration of milling bodiesof 60 g The initial powders were dry milled for 05 1 2 and10min The obtained materials were mechanically activatedpowders (hereinafter MP) referred to respectively as N-05N-1 N-2 N-10 (series of Nd-123) and Y-05 Y-2 Y-10 (seriesof Y-123) The particles size was determined using a scanningelectron microscope Carl Zeiss EVO 40 (Germany) andamounted to (3ndash5) sdot 10minus6m while the particles themselveswere agglomerates consisting of stuck together crystalliteswith the size of nearly 03 sdot 10minus6m
X-ray examination of samples was carried out usinga diffractometer Shimadzu XRD-7000 (Japan) The size ofcoherent scattering regions (CSR) was determined by X-raydiffraction analysis using the approximation method [14]Silicon powder was used to determine the instrumentalbroadening of the diffraction lines Selection of the functionfor approximating diffraction peaks was made using theprogram [15]
Thermal studies were carried out using the thermal ana-lyzer Netzsch STA 449C Jupiter (Germany) combined witha mass spectrometer Netzsch QMS 403C Aeolos (Germany)for evolved gas analysis The rates of heating and cooling ofsamples were 10 Kmin
Themagnetization (119898) wasmeasured using a commercialvibrating sample magnetometer Cryogenic CFS-9T-CVTIin the temperature range 42ndash300K The measurements inthe heating mode were performed on samples cooled in amagnetic field (field cooling FC) and in the absence of mag-netic field (zero field cooling ZFC)
XPS study was performed on a OmicronMultiprob spec-trometer (Germany) The test sample (RBa
2Cu3O6+120575
powderand R
2BaCuO
5ceramic tablet where R=Y Nd) was attached
to the sample holder using conductive double-sided adhesivetape and moved into the workspace of the spectrometerCeramic samples were subjected to scribing in ultrahighvacuum before study The source of the exciting radiation forXPSwasMg-anode of X-ray gunwith 170WThe energy scaleof the spectrometer was calibrated by the binding energiesof the peaks Au 4f
72(8400 eV) Ag 3d
52(36829 eV) and
Cu 2p32
(93267 eV) The value of samples surface chargewas determined by the difference between the measuredbinding energy of the C 1s signal due to CndashH groups and thevalue of 2850 eV Wide-scan survey spectra were recordedwith 05 eV energy step and the signal accumulation timeof 1 s at the pass energy (119864PE) of 100 eV High-resolutionspectrum was recorded with 005 eV energy step exposuretime of 75 s (15 scans by 05 s) and 119864PE = 20 eV Theaccuracy of peak position determination in the latter case was01 eV Decomposition of the spectra into components andextraction of the background were performed by the Shirleymethod using the program XPSPeak 41
Journal of Spectroscopy 3
3 Experimental Results
31 Oxides Y2BaCuO
5and Nd
2BaCuO
5
Attestation of Y2BaCuO
5and Nd
2BaCuO
5Oxides by XRD
and XPS Methods X-ray analysis has not shown the presenceof any impurity phases in the synthesized oxides Y
2BaCuO
5
and Nd2BaCuO
5 Syngony space group and lattice param-
eters for Y2BaCuO
5oxide are respectively orthorhombic
Pbnm a = 71304(6) A b = 121761(10) A c = 56571(6) A forNd2BaCuO
5oxide tetragonal P4mbm a = 66950(5) A c =
58188(9) AThe results of XPS study of these oxides are shown in
Figure 1 Decomposition of the obtained electronic spectrawas carried out on the basis of choosing the most appropriatemodel for the phase composition of the surface and themutual coherence between the spectra of different elements(with adjustments taking into account the analyzer trans-mission efficiency and differences in the photoionizationcross-section) The spectrometric data for oxides BaO Y
2O3
Nd2O3 and barium carbonate were taken from [16 33ndash35]
respectivelyLet us discuss some controversial points arising during
decomposition of the spectra As can be seen from Figure 1in the spectra of the sample containing neodymium thereare the intense peaks at 7790 (Ba 3d
52) and 5286 (O 1s)
eV which coincide with the signal from BaO [33] with highaccuracy This can mean that the synthesis of the samplehas not been completed and the unspent furnace chargecomponents have been localized in the surface layer of thematerial (location explains the fact that X-ray analysis unlikeXPS has not revealed the presence of impurity oxides inthe sample) hiding the main compound (Nd
2BaCuO
5) and
making its identification ambiguous To test this hypothesiswe have prepared one more sample Nd
2BaCuO
5at more
high the synthesis temperaturemdash1050∘C It was expected thatif indicated signals belonged to BaO their intensity wouldsignificantly decrease along with increase in intensity of themain compound peaks after the new heat treatment Butnothing like this has happenedmdashthe intensity of all the peaksstayed the sameThat proves that the peaks at 7790 (Ba 3d
52)
and 5286 (O 1s) eV relate directly to the oxide Nd2BaCuO
5
In addition to the main compound there is a bariumcarbonate on the surface of Nd
2BaCuO
5sample that is
confirmed by the peak of corresponding intensity at 2891 eVin the spectrum of C 1s see Figure 1 This presence is appar-ently due to insufficiently complete decomposition of sourceBaCO
3involved in the synthesis (there was not barium
carbonate on the surface of the sample synthesized at 1050∘Chowever there was a similar amount of unidentified bariumcompound with the binding energy of Ba 3d
52electronic
level of 7807 eV)Next we turn our attention to the sample Y
2BaCuO
5 for
which the intensity of the barium oxide peak in O 1s spec-trum according to calculations should be negligible andamount to sim150 of the main compound peak intensityHowever in a given location of the spectrum (more preciselynear 529 eV) there is a clear peak whose intensity is about 14of the intensity of the peak that is near (referred to Y
2BaCuO
5
compound) We suppose that this small peak also belongsto the main compound Indeed O 1s peak of Y
2BaCuO
5at
5313 eV is located near the corresponding peak of the yttriumoxide (see Figure 1) which is explained by the presence of thesame type of YndashO bond in both oxides Meanwhile there isalso a BandashO bond in Y
2BaCuO
5compound which should
be reflected by additional oxygen peak located near the O 1s-peak of barium oxide Note that only one peak was enough todescribe O 1s spectrum of Nd
2BaCuO
5
Quantitative analysis of the elements carried out on thebasis of the decomposition of the spectra has shown a goodagreement with formula composition for both compoundsunder study
32 Oxides YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
321 X-Ray Diffraction Study of Oxides YBa2Cu3O6+120575
andNdBa
2Cu3O6+120575
Theobtained lattice parameters data and thesize of the coherent scattering region are presented in Table 1One can see that the first 1-2 minutes of grinding lead to asignificant decrease in the size of CSR in both superconduc-tors that is refinement of the microstructure With increas-ing milling duration up to 10min further changes of CSR-size practically do not occur However there is a fundamentaldifference in the effect of mechanical activation on the phasecomposition of Y-123 andNd-123 In the initially single-phaseyttrium superconductor with increasingmilling duration theamount of impurity phase (Y
2BaCuO
5) increases continu-
ously whereas in the neodymium superconductor it is viceversamdasha small amount of impurity phase (Ba
2Cu3O5+x) exist-
ing in the initial sample is not observed in all mechanicallyactivated samples This confirms the findings of the highchemical stability of Nd-123 oxide by comparison with itsyttrium homologue
Another interesting point worthy of discussion is the factthat there is no more than one impurity in all the testedsamples (Y-123 and Nd-123) that according to the massbalance should affect the cation stoichiometry in the mainphase of the sample
As for Nd-123 samples deviations from the ideal cationstoichiometry after a long (150 hours) high-temperatureannealing is just a characteristic feature of them [9] Appear-ance of impurity Ba
2Cu3O5+x phase in an amount of 3
indicates that the IP of Nd-123 (sample N-0) is in fact a solidsolution Nd
103Ba197
Cu3O6+120575
Unspent Ba (in amount ofsim3) seems to form under atmospheric moist air the X-rayamorphous phase of Ba(OH)
2sdot nH2O which is easily trans-
formed into BaCO3from the surface due to the presence of
CO2in the air
Y-123 MP which contains a rich by yttrium impurityY2BaCuO
5 to comply with the ion balance should include
the phase not containing this element Since these phaseswere not detected by XRD we have assumed that as a resultof mechanical activation they became X-ray amorphous Infact they were later identified by us with the use of XPS seelater
322 XPS Study of YBa2Cu3O6+120575
Oxide Figure 2 shows thesurvey spectra of the powders YBa
2Cu3O6+120575
under study
4 Journal of Spectroscopy
Cu 2p
Nd2BaCuO5
Y2BaCuO5
930 940 950 960Binding energy (eV)
(a)
Nd2BaCuO5
Y2BaCuO5
280 282 284 286 288 290Binding energy (eV)
C 1s
(b)
Nd2BaCuO5
BaCO3
Y2BaCuO5
BaO
776 780 784 788 792 796 800 804Binding energy (eV)
Ba 3d
(c)
BaCO3
Y2BaCuO5
524 526 528 530 532 534 536 538Binding energy (eV)
Y2O3
Nd2BaCuO5
Nd2O3
O 1s
(d)
Nd2O3
Nd2BaCuO5
116112 120 124 128 132Binding energy (eV)
Nd 4d
(e)
Y 3d
Y2BaCuO5
Y2O3
148 150 152 154 156 158 160 162 164Binding energy (eV)
(f)
Figure 1 XPS spectra of Y2BaCuO
5and Nd
2BaCuO
5oxides The peaks related to the main oxide are marked by bold lines The ordinate
hereinafter is the intensity of the XPS signal in arbitrary units To reduce the figure size the y-axis itself is not shown
Journal of Spectroscopy 5
Table 1 Phase composition lattice parameters and the size of coherent scattering regions (119871) for YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
beforeand after mechanical treatment
Crystallographic parameters Milling duration in AGO-2(1) YBa
2Cu3O6+120575
powders0 s
(sample Y-0)30 s
(sample Y-05)2min
(sample Y-2)10min
(sample Y-10)The main phasemdashorthorhombic SG Pmmm119886 A 38208(3) 38218(3) 38287(10) 38344(10)119887 A 38884(5) 38893(5) 38938(15) 38879(15)119888 A 116809(11) 116793(12) 116739(33) 116663(31)119881 A3 173541(53) 173599(55) 174036(161) 173919(158)Impurity mass mdash sim5 Y
2BaCuO
5sim5 Y
2BaCuO
5sim7 Y
2BaCuO
5
119871 nm 167 57 25 20(2) NdBa
2Cu3O6+120575
powders0 s
(sample N-0)30 s
(sample N-05)2min
(sample N-2)10min
(sample N-10)The main phasemdashorthorhombic SG Pmmm119886 A 38677(1) 38731(3) 38727(12) 38754(12)119887 A 39202(1) 39206(10) 39225(14) 39161(15)119888 A 117612(3) 117622(24) 117630(39) 117661(24)119881 A3 178328(6) 178608(118) 178688(178) 178564(212)Impurity mass sim3 Ba
2Cu3O5+119909
mdash mdash mdash119871 HM 1792 325 229 169
200 400 600 800 1000 1200Binding energy (eV)
Y-10Cu 2p
Y-2Fe 2pY-05
Y 3d Y-0Ba 4d
Ba 3d
C 1s
O 1s
0
Figure 2 XPS survey spectra of the initial and mechanoactivatedYBa2Cu3O6+120575
samples
Recording such spectra conducted in high sensitivity mode(at high 119864PE) allows to consider the main lines of all elementspresented in the surface layer of the material in amountsgreater than 03 at As could be expected there are peaks ofthe electronic levels of yttrium barium copper and oxygencontained in the composition of the oxide under study TheC 1s peak includes a signal from the carbon contamination ofthe random nature
One can see (Figure 2) that on the surface of MP sam-ples there is no iron (mill headsets material) leading tothe appearance of specific magnetic and superconductingproperties of the material Strongly increased barium peak
(represented as a doublet of Ba 3d52minusBa 3d
32) in the spectra
of activated samples testifies the redistribution of elementsbetween the volume and surface occurs which is usuallythe result of chemical degradation of the surface under theinfluence of an environment In this case it could be a well-established [36] reactions as follows
2YBa2Cu3O65+119909+ 3H2O
997888rarr Y2BaCuO
5+ 3Ba(OH)
2+ 5CuO+ uarr119909O
2
(1)
Ba(OH)2+ CO2997888rarr BaCO
3+H2O (2)
Table 2 summarizes the obtained BaCO3of CP grade cal-
cinated at 700∘C Y2BaCuO
5and taken from the literature of
spectrometric data for the reactants involved in the reactions(1) and (2) for reliable identification of the peaks of thesecompounds in the spectra of the samples under study
High-resolution XPS spectra showing the characteristicelectronic levels of the elements constituting Y-123 samplesare presented in Figure 3
The analysis of the Ba 3d spectra has showed that in addi-tion to barium carbonate (line Ba 3d
52at 7799 eV) there is
the phase Y2BaCuO
5(line Ba 3d
52at sim782 eV) on the surface
of the samplesThe line Ba 3d52
at 7780 eVwhich is observedonly in the IP is directly owned by Y-123 (see Table 2)The Y 3d spectra confirm the presence of Y
2BaCuO
5-phase
on the surface of samples the substancersquos line Y 3d52
at1587 eV is clearly visible in these spectra (see Table 2)Besides the Y 3d spectra reveal the surface contains thefollowing oxides Y
2O3[34] (line Y 3d
52at 1569 eV) Y-123
6 Journal of Spectroscopy
Ba 3d
Y-10
Y-2
Y-05
Y-0
776 780 784 788 792 796 800Binding energy (eV)
3d523d32
(a)
Binding energy (eV)
Y 3d
Y-10
Y-2
Y-05
Y-0
150 152 154 156 158 160 162 164 166
(b)
Cu 2p
Y-10 Satellite I Satellite II
Y-2
Y-05
Y-0
930 940 950 960 970Binding energy (eV)
2p32
2p12
(c)
Figure 3 XPS spectra of YBa2Cu3O6+120575
powders Dark shading the main phase signal light shading Y2BaCuO
5signal
Table 2 The positions of the characteristic XPS lines of barium compounds
Electron orbital BaCO3 Ba(OH)2 Y-123 Y2BaCuO
5
Binding energy eV
Ba 3d52
7799 [16 17]7798lowast
7813 plusmn 01[18 19]
7777 plusmn 01[20ndash23] 7819lowast
Ba 4d52 893lowast 875
[22]
Y 3d52
1560 plusmn 02[21 24 25] 1587lowast
Cu 2p32
9335[21 26] 9356lowast
O 1s5314 plusmn 01[16 17]5314lowast
5312 qB[27]
52845 plusmn 005 qB[20ndash23] (5291 5313)lowast
C 1s28925 plusmn 015 qB
[16 17]2894lowast
lowastOur data
(line Y 3d52
at 1560 eV in the spectrum of IP) and the phaseY2(C2O4)3[37] (line Y 3d
52at 1601 eV) The presence of
Y2BaCuO
5compound in samples is also reflected in the
spectra of Cu 2p a high-energy doublet (main peak at9356 eV) corresponds to it At the same time the low-energyCu 2p-doublet parameters are close to those found in [22] forY-123 the main peak at 9335 eV a satellite at sim943 eV as wellas parameters relating to copper oxide Cu (II) [28] 9336 eVand 9425 eV respectively However from the analysis of thespectra of Ba 3d and Y 3d (see earlier) it can be argued that
the Cu 2p signal from the phase of Y-123 may be only in thespectrum of IP samples
Thus in addition to the main phase the surface of IPcontains the final products of the reactions (1) + (2) and Y
2O3
phase probably sourced by the initial precursor incompletelyconsumed during the synthesis of YBa
2Cu3O6+120575
As a resultof MA treatment the surface of the powder is covered with alayer of yttriumoxide and the products of reactions (1) + (2) toa considerable depth of at least 10 nm (judging by the amountof Y2BaCuO
5phase in the samples determined by XRD)
Journal of Spectroscopy 7
323 XPS Study of NdBa2Cu3O6+120575
Oxide Figure 4 demon-strates the survey spectra of Nd-123 powders One can seethat as in the case of Y-123 samples the signal representingthe iron was not observed for any intensive milling durationThe feature of Nd-123 samples is rather low intensity of the Ba3d and Ba 4d peaks for powders activated for 05 and 2min(compare Figure 4 with Figure 2 for Y-123 powder) Bariumpeaks has markedly increased (as well as oxygen O 1s peak)only at 10min of activation
Figure 5 shows the high-resolution spectra of the elec-tronic levels of barium (3d and 4d) neodymium (4d) andcopper (2p) in powders with different activation prehistoryIn the barium spectra the high-intensity peaks at 7799 eV(3d52
) and 893 eV (4d52
) are obviously responsible for thecompound BaCO
3 and the low-intensity peaks at 7780 and
876 eV which are observed only in IP samples (dark shadedin Figure 5) correspond to the main phase by analogy withY-123 samples The analysis of Cu 2p spectra has revealed thepresence of copper ions with the electronic structure similarto that in Y-123 or in CuO oxide
However as seen in Figure 5 the state Cu 2p with highbinding energy (9359 plusmn 03 eV) is also present in all Nd-123samples According to our data (see Table 3) this state is nottypical for simple and ternary compounds of copper DuringMA processing its share in Cu 2p spectra changes in strictaccordancewith the high energy components of the Ba 3d andBa 4d spectra light shaded in Figure 5 (at 7817 eV (Ba 3d
53)
and 919 plusmn 03 eV (Ba 4d53
)) which implies that a doubleoxide of barium-copper was on the surface of the samplesWe tend to identify this oxide as Ba
2Cu3O5+x phase which
was detected by X-ray diffraction analysis of IP samples (seeTable 1) Despite the fact that this phase was not found byXRD in samples N-05 N-1 and N-2 it is visible in the XPSspectra due to the effect of spatial localization
According to Figure 5 the surface of the samples alsocontained the oxide Nd
2O3(line Nd 4d
52at 1211 eV) which
under intense grinding at the initial stages was partly trans-formed into Nd
2(C2O4)3[37] (line Nd 4d
52at sim1225 eV)
Based on the analysis of possible superpositions of the spectraof Ba 3d Ba 4d and Cu 2p the low-energy Nd 4d doublet(line Nd 4d
52at 1157 eV) the intensity of which is almost
independent of the MA duration belongs to a double oxideNdCu
119910O15+y+z of undetermined composition The Nd 4d
doublet of themain compound apparently overlaps with oneof the previously noted signals and so it is shown explicitlyin Figure 5
On the intensity ratios of the peaks in Figure 5 one canconstruct a model of the relative position of the phases Nd-123 BaCO
3 and Ba
2Cu3O5+x in the surface layer of the
material (this method has been used eg in [22] to analyzethe relative position of the layers Y-123 and BaCuO
2) To
realize this we use the dependence of the layer thicknessanalyzed by XPS (usually taken as 3 sdot 120582
119898) on the kinetic
energy of the electrons [38] referring to the electrons givingthe corresponding lines in the spectra of Ba 3d and Ba 4d asfollows
120582119898= 2170119864
minus2
119896+ 072(119886119864
119896)12 (3)
Ba 3d
N-10Cu 2pN-2Fe 2p
O 1sN-05
N-0Cu LVVCu 3s C 1sNd 4d
Ba 4d200 400 600 800 1000
Binding energy (eV)0
Figure 4 XPS survey spectra of the initial and mechanoactivatedNdBa
2Cu3O6+120575
samples
where 120582119898is the electron mean free path expressed in mono-
layers 119886 is monolayer thickness in nm 119864119896is kinetic energy
in eV (119864119896= ℎ] minus 119864BE minus 120593) ℎ] = 12536 eV is the energy of
the exciting radiation used inXPS analysis119864BE is the bindingenergy of the electronic level under analysis and120593 is theworkfunction of the spectrometer (346 eV)
According to this relationship the thickness of the layerunder analysis increases monotonically with increasing 119864
119896
in the range 119864119896gt 40 eV As can be seen from Figure 6
increase in the thickness of the layer under analysis canaffect the following volume ratios detectable by XPS phaseIphase III and phase IIphase III and has no influence onthe volume relation phase Iphase II The phase fractionto a first approximation is proportional to the area undercorresponding XPS peak Therefore based on the ratio ofareas of the different lines in the spectra in Figure 5 one canconclude that both barium-containing products of chemicaldecomposition of Nd-123 are located atop of the main oxidethat is correspond to phases I and II in Figure 6 The thick-ness of the degraded layer in N-10 sample is sim10 nm (as theoriginal phase is barely visible through it) and in IP (N-0)sample it is estimated to be 5-6 nm
It should be noted however that such a small thicknessof Ba2Cu3O5+x layer in IP has not prevented this phase to be
recognized by XRD analysis (see Table 1) One can thereforeconclude that IP particles contain in addition a considerableamount of Ba
2Cu3O5+x in the form of individual inclusions
in bulk (as a result of this oxide synthesis features seeSection 1) DuringMA processing material particles crackedand inclusions went outside resulting in the fraction ofBa2Cu3O5+x phase on the surface increased up to a point
(up to 1min inclusive) The subsequent decrease in thisphase (see Figure 5) is apparently due to the fact that anotherprocess also developed on the surface during grindingspending of Ba
2Cu3O5+x involving the original solid solution
Nd1+xBa2minusxCu3O6+120575 to formation of cation-stoichiometric
NdBa2Cu3O6+120575
To prove the occurrence of such interaction
8 Journal of Spectroscopy
Ba 3d
N-10
N-2
N-1
N-05
N-0
770 775 780 785 790 795 800 805Binding energy (eV)
(a)
N-10
N-1
Binding energy (eV)
Ba 4d
Ba 4d
N-2
N-05
N-0
68 72 80 84 88 92 96
Cu 3p X-ra
ysa
telli
tes
76
(b)
N-10
N-2
N-1
N-05
N-0
930 940 950 960 970Binding energy (eV)
Satellite I Satellite II
Cu 2p2p32
2p12
(c)
N-10
N-2
N-1
N-05
N-0
110 115 120 125 130 135Binding energy (eV)
Nd 4d
(d)
Figure 5 XPS spectra of NdBa2Cu3O6+120575
powders
119864119896 (Ba 3d) 119864119896 (Ba 4d)
Phase I Phase II
Phase III
Phase I Phase II
Phase III
31205823120582
XPS
study
area
XPS
study
area
lt
Figure 6 Analysis of the mutual arrangement phases in the surface layer of the material and their volume relations from XPS data
Journal of Spectroscopy 9
Table 3 Characteristic spectral parameters of different copper compounds
Electron orbital CuO CuCO3 Cu(OH)2 Cu2CO3(OH)2 Nd2BaCuO5
Binding energy eVBa 3d
527790lowast
Nd 4d52
1182lowast
Cu 2p32
9337 plusmn 1[28ndash30]
9348[28]
93474 plusmn 006[29 31]
9347[32] 9335lowast
O 1s 52974 plusmn 006[30 31]
53124[31] 5286lowast
lowastOur data
later we present the data of magnetic measurements whichindicate that MA treatment results in significant increase inthe temperature of the superconducting transition in separateregions of the material
324 Thermal Analysis of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
Samples of R-123 have been studied by thermogravimetrycoupled withmass-spectrometry to analyze the gases evolvedduring experiments Results of the study are summarizedin Figure 7 It is seen that reversible change in mass of IP-samples occurs in the range of 430ndash900∘C that must be dueto oxygen exchange between nonstoichiometric R-123 oxidesand the gas phase taking place at these temperatures [1] MPsamples start losing mass sharply around 70∘C when heatedMass spectrometry analysis of thermal desorption productsindicates the presence of large amount of water and a smallamount of carbon dioxide contained in the samples in theform of BaCO
3(the temperature range in which the CO
2
was released and the value of 119901CO2used for thermal analysis
of the atmosphere was consistent with conditions of bariumcarbonate decomposition)
325 Study of Magnetic Properties of YBa2Cu3O6+120575
andNdBa
2Cu3O6+120575
Temperature dependences of ZFC magne-tization of the samples Y-0 Y-05 Y-2 and Y-10 are shownin Figure 8 A sharp downturn in magnetization at sim90Kobserved in the samples Y-0 Y-05 and Y-2 clearly showsthe presence of the superconducting phase Superconductingtransition temperatures of the samples Y-0 Y-05 and Y-2have been determined by taking the derivative of the mag-netization against the temperature (119889119898119889119879) Thus definedtemperatures 119879
119888are equal to 91 K for the samples Y-0 and
Y-05 and 88K for the sample Y-2 A wide transition widtharound 119879
119888= 90K indicates that both the initial and MP
samples contain inhomogeneous superconductor phaseswithdifferent 119879
119888 The following facts indicate the presence of
paramagnetic contribution in the magnetization behavior ofMP samples and its growth with increasing milling durationa significant increase in magnetization 119898 of the samples Y-05 and Y-2 compared with the initial sample Y-0 at thetemperatures 119879 gt 119879
119888 weak temperature dependence 119898(119879)
in the temperature range 100ndash300 K for MP samples asignificant increase in themagnetization of Y-10 sample at lowtemperatures
100
99
98
97
96
95
94
93
92
100
99
98
97
96
95
94
93
92
0 200 400 600 800 1000
0 200 400 600 800 1000
14
12
10
8
6
4
3
2
Temperature (∘C)
Ion
curr
ent (
A)
Ion
curr
ent (
A)
Sam
ple w
eigh
t (
)
H2O
CO2
H2O (times1010) CO2 (times1011)
3
2
1
3998400
1998400
2998400
Figure 7 Thermal analysis results for samples Y-0 (1) N-0 (11015840) Y-2 (2) N-2 (21015840) and Y-10 (3) N-10 (31015840) Mass spectrometry data arerelated to the samples Y-10 (solid curves) and N-10 (dashed lines)
For comparison Figure 9 shows the temperature depen-dence of the FC magnetization in a magnetic field 119867 =500Oe for two new samples of Y-123 (120575 asymp 07) The firstsample has been freshly prepared and the other one has beensubjected to treatment at 297 plusmn 1K for 120 h at absolutehumidity of 23 120581Pa The sample with low oxygen content(and as a consequence with low 119879
119888) has been chosen due
to its relatively easy moisture saturation in these conditionswithout the use of MA (moisture saturation was controlledby the increase in weight which eventually was sim4wt)One can see that the sample saturated with water has apositive magnetic moment above the temperature 119879
119888and
shows an increase inmagnetic moment on cooling below this
10 Journal of Spectroscopy
N-0
N-1
N-10N-2
Y-2
Y-05
N-05
Y-0
Y-10
005 0005
0004
0003
0002
0001
0
0
minus005
minus01
minus015
minus02
minus025
minus03
minus01
minus02
minus03
003
002
001
0
0
0minus001
20 40 60 80 100 120 140119879 (K)
119898(e
mu
g)119898
(em
ug)
119898(e
mu
g)119898
(em
ug)
Figure 8 ZFC magnetizations as a function of temperature at119867 = 50Oe for the initial and mechanically activated samplesYBa2Cu3O6+120575
(top) NdBa2Cu3O6+120575
(bottom)
temperature similarly to Y-10 sample Onset temperature ofthe magnetic anomaly in the hydrated sample is the sameas that in the freshly prepared sample This experimentdemonstrates that the presence of water in MP sampleshas a significant effect on the temperature dependences ofthe magnetization observed in samples of Y-123 series (seeFigure 8)
Temperature dependences of ZFC magnetization of MPsamples in Nd-123 series are shown in Figure 8 The super-conducting transition temperatures of the samples N-0 N-05 and N-1 are independent of milling duration and equal to119879119888sim 57KMechanical treatment leads to a substantial change
in the magnetization of MP samples throughout the inves-tigated temperature range MP samples exhibit near-room-temperature hysteretic behavior that is ZFC magnetizationis more diamagnetic than FCmagnetization It may be due tomagnetic particles of mechanoactivatedNd-123 samples or tothe presence of impurity phases whose low content or highlydisordered crystal structures do not allow to observe thesephases by X-ray diffraction measurements We also cannotexclude the formation of CuO phase (119879
119873sim 220K) at the
surface of large NdBa2Cu3O6+120575
particles proceeding undermechanical activationAt the same time a significant increasein the paramagnetic contribution to the magnetization withincreasing milling duration is observed
004
002
0
minus002
minus004
minus006
minus0080 20 40 60 80 100 120 140
0 20 40 60 80 100 120 140
119898(e
mu)
119898(e
mu)
119879 (K)
119879 (K)
004
0038
0036
0034
Figure 9 FCmagnetizations as a function of temperature of freshlyprepared YBa
2Cu3O6+120575
sample (empty points) and of hydrated sam-ple (black points) at119867 = 500Oe Inset the temperature dependenceof magnetization of hydrated sample at119867 = 10 kOe
A wide transition width around 119879119888= 57K (|Δ119879
119888sim 20K|)
in MP samples of Nd-123 series cannot be explained only bythe presence of water in the structure The observed changesindicate that during MA treatment diffusion processes asso-ciated with the ordering of the cations Nd3+ and Ba2+ appa-rently occur according to [8ndash10] that has a significant effecton 119879119888
4 Discussion of Results
41 Interaction of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
withCO2 From comparison of Figures 4 and 5 it is clear that with
increasing duration of MA processing (120591119892) the amount of
barium-containing impurities on the surface of Nd-123 sam-ples continuously increases up to 120591
119892= 10min in contrast
to the situation for the oxide Y-123 for which initially (up120591119892= 05min) sudden change and subsequent (after 120591
119892=
05min) almost stagnation in the accumulation of chemicaldegradation products were observed (see Figures 2 and 3 anddata on the impurities in YBa
2Cu3O6+120575
sample) One can seefrom Figure 7 that the degree of water saturation (120578) of bothoxides (this parameter can be traced by sharp descendingbranch of sample mass change in the temperature range of30ndash450∘C) obeys similar relationships with increasing 120591
119892 its
growth with increasing MA duration close to proportionalfor Nd-123 (120578 sim 120591
119892) and tendency of 120578 to decrease for Y-123
(120578 = 155 sdot 120591119892
03) which is close to the root dependence char-
acteristic of reagent diffusion through the reaction productslayer
Taking into account the data in [1] stating the chemicaldegradation of Y-123 is carried out on the interface betweenY-123 and gas phase and one can explain sharply fallingrates of change in concentration of its products as well as ofH2O dissolved in the oxide the diffusion path length of H
2O
and CO2reactants to the location of the reactions (1) and
(2) increases with time 120591119892 However the uniformity of the
absorption of H2O and CO
2gases by MP of Nd-123 testifies
Journal of Spectroscopy 11
that the thickness of the degraded layer on the surface variesslightly Apparently it does not exceed 10 nm as indicated bya weak but clear signal of the main phase which appeared inthe Ba 4d-spectrum of N-10 sample (see Figure 5) Howeverit should be noted that Nd-123 MP sample actively entersinto chemical reactionwith atmospheric CO
2 the gas escapes
from the samples quite intensively when heated in the rangeof 800ndash900∘C (see Figure 7) Therefore the question oflocalization place of products of interaction between Nd-123and atmospheric components arises
Homogeneous nucleation and growth of interaction pro-ducts in the volume of Nd
1+xBa2minusxCu3O6+120575 parent phasemaybe the answer This assumption is based on the fact that theproducts of thermal desorption of N-10 sample (see Figure 7)contain weakly bound form of CO
2escaping in a wide tem-
perature range of 200ndash550∘C Obviously it is a form of gasdissolved in the structure Since the carbonization energy ofBa2+ ions is quite high homogeneous nucleation of carbonatephase at a certain concentration (equivactivity) of CO
2in the
structure facilitated by the participation of structural defects(whose concentration should be significant in MP samples)seems quite possible
42 Interaction of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
withWater In the Introductionwe have put links toworks statingthat the crucial feature for the practical application of thesuperconductor Nd-123 is its high resistance to chemicaldegradation under moisture Additional information thatexpands understanding of this feature has been received inour study Thus it is shown (see Figure 7) that a high con-centration of water accumulates in MP samples of Nd-123 indissolved form but the hydrolysis reaction development isquite limited as evidenced by the relatively low temperatureof H2O release from this oxide Moreover the results of
XRD and XPS analyzes have not detected even traces of theternary compound Nd
2BaCuO
5in these samples while it is
the compounds R2BaCuO
5due their characteristic colours
that are indicators of the hydrolysis reaction for the wholefamily of compounds R-123 [1 39 40] Thus if the hydrolysisreaction develops (there is a small peak on H
2O desorption
curve for sample N-10 at sim455∘C that can be attributed tothe chemically bound water) then it proceeds through non-traditional mechanism and with low rate
According to [41] the hydration mechanism for thehomologous series of R-123 compounds is in four stages Atthe initial stage water molecules penetrate into the bulk ofthe crystallites through the structural channels [(12) b 0]located in interspaces between CuO-chains typical for thistype of superconductors At the next stage protons whichare located in the oxygen positions of CuO-chains can besplit up of watermoleculesThis proton transfer is consideredto cause an internal (within the [CundashO]+-system) chargetransfer resulting in formation of molecular oxygen leavingthe structure At high concentrations of hydroxide ionsaccumulated in the structure the chemical decompositionof the initial oxide occurs Based on the previous schemeone can understand the reasons for high resistivity of N-123superconductor to chemical interaction with water
The authors of [42] discussed the high corrosion resis-tance of Nd-123 films in the water compared to the filmstructures of Y-123 and Eu-123 which was attributed to thepartial oxygen disorder in the planes of CuO-chains Sucha disorder should occur in Nd-123 due to the presence ofsome amount of Nd3+ ions in the sites nearby to CuO-planesof divalent barium According to the authors that shouldlead to overlapping structural channels for H
2O diffusion
and hence blocking the hydration process However ourdata on the thermal analysis (see Figure 7) illustrate thatthe saturation of Nd-123 structure with water during MAtreatment proceeds almost as fast as in Y-123 (in the rangeof 2ndash10 minutes even faster) Therefore the sought causeof the chemical stability of Nd-123 MP cannot be related toproblems of H
2O diffusion
The stage of removing oxygen from the structure is con-sidered [41 42] to be extremely important for the hydrationprocess of R-123 Thus the chemical degradation of Y-123oxide immersed in the water is completely stopped underpotential of 08 V relative to the standard electrode-saturatedsodium calomel [41] It is expected that the substitutionNd3+ rarr Ba2+ inNd-123 in addition to oxygen disordering inthe base structural plane should also lead to the strengtheningof its bondwith the lattice (due to electrostatic effect of highlycharged Nd3+ ion) [42] According to the authors [42] thisshould inhibit the reduction stage of hydration However it isimportant to consider the fact that the structure ofMP of Nd-123 contains a large amount of weakly bound CO
2 located
near Ba ions (since there is a tendency to the formation ofBaCO
3) therefore localized in the channels of the base plane
[(12) b 0] where also there is water In our opinion just theseCO2particles block channels of oxygen desorption which is
the main reason for the high stability of Nd-123 in relation tothe hydrolysis reaction
5 Conclusion
Thus as a result of mechanical activation treatment thesurface of YBa
2Cu3O6+120575
is covered by products of hydrolysisand carbonization to a considerable depth The chemicaldegradation process proceeds the normal waymdashthrough theformation of Y
2BaCuO
5phase
Chemical degradation of mechanoactivatedNdBa
2Cu3O6+120575
powders under the impact of CO2
isnot directly connected to hydrolysis process as occurs inYBa2Cu3O6+120575
(see reactions (1) and (2)) Carbonizationproceeds homogeneously through the stage of carbondioxide dissolution in the lattice of NdBa
2Cu3O6+120575
In itsturn the presence of CO
2molecules in the structure of
mechanoactivated NdBa2Cu3O6+120575
powders leads to a radicalchange in the mechanism of interaction between the super-conductor and water This mechanism eliminates the normalfor a homologous series of RBa
2Cu3O6+120575
the hydrolysisreaction with the formation of characteristic ldquocolorrdquoR2BaCuO
5phases The rate of chemical decomposition of
mechanically activated NdBa2Cu3O6+120575
by the new mecha-nism (not yet studied) is quite low
12 Journal of Spectroscopy
Mechanical treatment affects the temperature depen-dence of the magnetization of RBa
2Cu3O6+120575
compoundsThere is a significant increase in the paramagnetic and ferro-magnetic contributions to the magnetization with increasingmilling duration The latter leads to near-room-temperaturehysteretic behavior of NdBa
2Cu3O6+120575
samples between ZFCandFC regimes Itmay be due tomagnetic particles ofmecha-noactivated NdBa
2Cu3O6+120575
samples or to the presence ofimpurity phases whose low content or highly disorderedcrystal structures do not allow to observe these phases byX-ray diffraction measurements The mechanical treatmentdoes not have substantial influence on the transition tem-peratures of superconducting phases 119879
119888in the RBa
2Cu3O6+120575
compounds but a wide transition width around 119879119888indicates
that mechanically activated samples contain inhomogeneoussuperconductor phases with different 119879
119888 The broadening
of the superconducting transition in mechanically activatedNdBa
2Cu3O6+120575
samples may be due to redistribution ofcations between Nd- and Ba-sublattice
Finally we note that the high temperature superconduc-tor RBa
2Cu3O6+120575
subjected to mechanical activation cer-tainly has no significant advantages over conventional non-mechanoactivated material but it is obvious that physical-chemical studies of such powders reveal results interestingfrom the point of view of fundamental science
Acknowledgment
This work was supported by Russian Foundation for BasicResearch (Grant no 11-03-00317-a)
References
[1] I E Graboi A R Kaulrsquo and G Yu Metlin ldquoAdvances in scienceand technologyrdquo in Solid State Chemistry pp 3ndash142 VINITIANSSSR Moscow Russia 1989
[2] S Anders M G Blamire F-Im Buchholz et al ldquoEuropeanroadmap on superconductive electronicsmdashstatus and perspec-tivesrdquo Physica C vol 470 no 23-24 pp 2079ndash2126 2010
[3] B Ruck B Oelze R Dittmann et al ldquoMeasurement of thedynamic error rate of a high temperature superconductor rapidsingle flux quantum comparatorrdquo Applied Physics Letters vol72 no 18 pp 2328ndash2330 1998
[4] M W Rupich X Li C Thieme et al ldquoAdvances in secondgeneration high temperature superconducting wire manufac-turing and RampD at American superconductor corporationrdquoSuperconductor Science and Technology vol 23 no 1 Article ID014015 2010
[5] A Rakitin M Kobayashi and A P Litvinchuk ldquoSuperi-onic behavior of high-temperature superconductorsrdquo PhysicalReview B vol 55 no 1 pp 89ndash92 1997
[6] T Kagiyama J Shimoyama K D Otzschi et al ldquoEffect of cationcomposition and oxygen nonstoichiometry on 119869
119888-119861 properties
of Nd123rdquo Physica C vol 341ndash348 no 2 pp 1445ndash1446 2000
[7] M Badaye J G Wen K Fukushima et al ldquoSuperior propertiesof NdBa
2Cu3O119910over YBa
2Cu3O119909thin filmsrdquo Superconductor
Science and Technology vol 10 no 11 pp 825ndash830 1997
[8] C Cantoni D P Norton D M Kroeger et al ldquoPhase stabilityfor the in situ growth of Nd
1+119909Ba2minus119909
Cu3O119910films using pulsed-
laser depositionrdquo Applied Physics Letters vol 74 no 1 pp 96ndash98 1999
[9] E A Goodilin N N Oleynikov E V Antipov et al ldquoPhasestability for the in situ growth of Nd
1+119909Ba2minus119909
Cu3O119910films using
pulsed-laser depositionrdquo Physica C vol 272 6578 pages 1996[10] E Guilmeau F Giovannelli I Monot-Laffez S Marinel J
Provost and G Desgardin ldquoTop seeding melt texture growthof NdBaCuO pellets in airrdquoThe European Physical Journal vol13 no 3 pp 157ndash160 2001
[11] A I Ancharov T F Grigorrsquoeva T Yu Kiseleva A A Novakovaet al inMechanocomposites-Precursorsfor the Creation of Mate-rials with New Properties O I Lomovskii Ed p 424 Izd-voSO RAN Novosibirsk Russia 2010
[12] A Hamrita F Ben Azzouz A Madani and M Ben SalemldquoMagnetoresistivity and microstructure of YBa
2Cu3O119910pre-
pared using planetary ball millingrdquo Physica C vol 472 no 1pp 34ndash38 2012
[13] R P Vasquez ldquoIntrinsic photoemission signals surface prepa-ration and surface stability of high temperature superconduc-torsrdquo Journal of Electron Spectroscopy and Related Phenomenavol 66 no 3-4 pp 209ndash222 1994
[14] S S Gorelik L N Rastorguev and A Yu Skakov in Rentgeno-graphIcheskII I ElektronographIcheskII AnalIz p 368 Izd-voMetallurgia Moscow Russia 1970
[15] M V Reshetniak and O V Sobol Program for diffractionanalysis ldquoNew Profilerdquo(Last update 10 02 2007) Version 3 4400 (Freeware) WIN9xMENT2KXP Copyright (c) 1992-2007 ReMax SoftWare 2000
[16] M Wegmann L Watson and A Hendry ldquoXPS analysis of sub-micrometer barium titanate powderrdquo Journal of the AmericanCeramic Society vol 87 no 3 pp 371ndash377 2004
[17] A B Christie J Lee I Sutherland and J M Walls ldquoAn XPSstudy of ion-induced compositional changes with group II andgroup IV compoundsrdquo Applications of Surface Science vol 15no 1ndash4 pp 224ndash237 1983
[18] U A Joshi S Yoon S Balk and J S Lee ldquoSurfactant-freehydrothermal synthesis of highly tetragonal barium titanatenanowires a structural investigationrdquo Journal of Physical Chem-istry B vol 110 no 25 pp 12249ndash12256 2006
[19] R Caracciolo ldquoChemical characterization techniques for thinfilmsrdquo in Ceramic Films and Coatings J B Wachtman and R AHaber Eds p 376 New Jersey NJ USA 1992
[20] I N Shabanova Y A Naimushina and N S Terebova ldquoCom-position and temperature dependence of a Y-Ba-Cu-O HTSCelectronic structurerdquo Superconductor Science and Technologyvol 15 no 7 pp 1030ndash1033 2002
[21] J Beyer T Schurig S Menkel Z Quan and H Koch ldquoXPSinvestigation of the surface composition of sputtered YBCOthin filmsrdquo Physica C vol 246 no 1-2 pp 156ndash162 1995
[22] C C Chang M S Hegde X D Wu et al ldquoSurface layers onsuperconducting Y-Ba-Cu-O films studied with x-ray photo-electron spectroscopyrdquo Applied Physics Letters vol 55 no 16pp 1680ndash1682 1989
[23] X D Wu A Inam M S Hegde et al ldquoCrystalline perfectionof as-deposited high-Tc superconducting thin-film surfacesion channeling and x-ray photoelectron spectroscopy studyrdquoPhysical Review B vol 38 no 13 pp 9307ndash9310 1988
[24] P Rajasekar P Chakraborty S K Bandyopadhyay P Barat andP Sen ldquoX-ray photoelectron spectroscopy study of oxygen and
Journal of Spectroscopy 13
argon annealed YBa22Cu3O7minus120575
rdquo Modern Physics Letters B vol12 no 6-7 pp 239ndash245 1998
[25] J Halbritter P Walk H J Mathes B Haeuser and H RogallaldquoARXPS-studies of c-axis textured YBa
2Cu3O119909-filmsrdquo Physica
C vol 153ndash155 no 1 pp 127ndash128 1988[26] T J Sarapatka and P Mikusık ldquoXPS study of PbYBaCuO thin-
film tunnel contactrdquo Applied Surface Science vol 68 no 1 pp35ndash40 1993
[27] J A T Verhoeven and H Van Doveren ldquoAn XPS investigationof the interaction of CH
4 C2H2 C2H4and C
2H6with a barium
surfacerdquo Surface Science vol 123 no 2-3 pp 369ndash383 1982[28] C D Wagner W M Riggs L E Davis J F Moulder and G
E Mullenberg Handbook of X-Ray Photoelectron SpectroscopyPerkin-Elmer Corp Eden Prairie Minn USA 1979
[29] M C Biesinger L W M Lau A R Gerson and R S C SmartldquoResolving surface chemical states in XPS analysis of first rowtransition metals oxides and hydroxides Sc Ti V Cu and ZnrdquoApplied Surface Science vol 257 no 3 pp 887ndash898 2010
[30] X Y Fan Z GWu P X Yan et al ldquoFabrication of well-orderedCuO nanowire arrays by direct oxidation of sputter-depositedCu3N filmrdquo Materials Letters vol 62 no 12-13 pp 1805ndash1808
2008[31] S J Kerber J J Bruckner K Wozniak S Seal S Hardcastle
and T L Barr ldquoNature of hydrogen in x-ray photoelectronspectroscopy general patterns from hydroxides to hydrogenbondingrdquo Journal of Vacuum Science and Technology A vol 14no 3 pp 1314ndash1320 1996
[32] G Moretti G Fierro M Lo Jacono and P Porta ldquoCharac-terization of CuO-ZnO catalysts by X-ray photoelectron spec-troscopy precursors calcined and reduced samplesrdquo Surfaceand Interface Analysis vol 14 no 6-7 pp 325ndash336 1989
[33] H Van Doveren and J A T H Verhoeven ldquoXPS spectra of CaSr Ba and their oxidesrdquo Journal of Electron Spectroscopy andRelated Phenomena vol 21 no 3 pp 265ndash273 1980
[34] B V Crist Handbooks of Monochromatic XPS Spectra Volume2mdashCommercially pure binary oxides XPS International LLCLeona Tex USA 2005
[35] D D Sarma and C N R Rao ldquoXPES studies of oxides ofsecond- and third-row transition metals including rare earthsrdquoJournal of Electron Spectroscopy and Related Phenomena vol 20no 1 pp 25ndash45 1980
[36] V I Nefedov and A N Sokolov ldquoDegradatzia visokotemper-aturnich sverchprovodnikov pri khimicheskich vozdeistviachrdquoZhurnal Neorganicheskoi Khimii vol 34 no 11 pp 2723ndash27391989
[37] Y Uwamino T Ishizuka and H Yamatera ldquoX-ray photoelec-tron spectroscopy of rare-earth compoundsrdquo Journal of ElectronSpectroscopy and Related Phenomena vol 34 no 1 pp 67ndash781984
[38] M P Seah and W A Dench ldquoQuantitative electron spec-troscopy of surfaces a standard data base for electron inelasticmean free paths in solidsrdquo Surface and Interface Analysis vol 1no 1 pp 2ndash11 1979
[39] C H Lin H C I Kao and C M Wang ldquoKinetics andstability of R(Ba
15Sr05)Cu3O119910(R = La Nd Sm Eu Gd Dy Ho)
superconductors inwaterrdquoMaterials Chemistry and Physics vol82 no 2 pp 435ndash439 2003
[40] A G Knizhnik R A Stukan and G O Eremenko ldquoStudy theinteraction between europium HTSC of 123 type and waterrdquoSverkhprovodimost vol 4 no 1 pp 177ndash182 1991 (Russian)
[41] J Zhou R K Lo J T McDevitt et al ldquoDevelopment of areliable materials base for superconducting electronicsrdquo Journalof Materials Research vol 12 no 11 pp 2958ndash2975 1997
[42] S B Schougaard M F Ali and J T McDevitt ldquoEvidence forhigh stability against water corrosion of NdBa
2Cu3O7plusmn120575
relativeto YBa
2Cu3OO7minus120575
and EuBa2Cu3OO7minus120575
rdquo Applied Physics Let-ters vol 84 no 7 pp 1144ndash1146 2004
Submit your manuscripts athttpwwwhindawicom
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
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Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
CatalystsJournal of
2 Journal of Spectroscopy
of Nd and Ba in the structural position of each other whichcan occur during high-temperature annealing in an oxygenenriched atmosphere [9]
It is known [11] that high-intensity mechanical activa-tion processing (hereinafter MA) can significantly modifyphysicochemical properties of various materials At the sametime such researches focused on the change of the functionalproperties of superconducting oxides RBa
2Cu3O6+120575
(R-123)and to our knowledge have not yet been carried out (existingworks like [12] are devoted to mechanical activation ofprecursors) Apparently this is related to the fact that thechemical stability of these oxides to the impact of air atmo-sphere components is not high even in the normal state [1]Besides mechanical treatment leads to substantial increaseand activation of the free surface contacting with the atmo-sphere and during grinding spalling of R-123 particles occursmainly along the basal plane of the crystallites and exposesthe chemically active structural layer BaO [13] Neverthelessin the present study we have attempted to assess how muchthe surface of R-123 actually degrades under MA and justas importantly what is the influence of this effect on thefunctional properties of these superconducting oxides Wehave limited our investigations to compounds with R=Y Ndwhich are promising for applied developments
Thus the objectives of this work were (1) analysis of thechemical composition of the surface of mechanoactivatedR-123 powders (hereinafter MP) and determination of thedegree of its chemical degradation under the influence ofaggressive components of the environment H
2O and CO
2
(2) analysis of the effect of mechanical activation on thefunctional properties of the superconducting material
To fulfill the tasks we used the following methods X-raydiffraction (XRD) thermal analysis magnetometry and X-ray photoelectron spectroscopy (XPS) The latter is a power-ful tool to study the chemical and even phase compositionof the material locallymdashin the thin layer (nearly 10 nm inthickness) of the external boundary This method allowsdetecting impurity phases occurring at the average volumeconcentration outside the sensitivity of X-ray diffraction andalso phases in the amorphous state
2 Experimental Technique
Oxides R-123 were obtained by stepwise annealing a mixtureof barium nitrate Ba(NO
3)2(ldquochemically purerdquo grade) the
corresponding oxide of the rare earth element (RE) and basiccopper carbonate CuCO
3times Cu(OH)
2(ldquoespecially purerdquo
grade) at 798K for 5 h 998K (5 h) and 1213 K (140 h) Theproducts were subjected to oxidative annealing by slow (withfurnace) cooling from the synthesis temperature to 673K andexposed to this temperature in air for 3 hours The oxygencontent of the samples (6 + 120575) according to the oxidativeannealing conditions can be estimated as 690 plusmn 003 [1] Thethus obtained material was ldquoinitial samplerdquo (hereinafter IP)
In the course of our research we also needed to obtainsamples of Nd
2BaCuO
5and Y
2BaCuO
5to determine the
spectral parameters of these compounds as we did not find
relevant and reliable data in the literature They were synthe-sized at 1000∘C for 23 h from previously obtained Nd-123 andY-123 with the addition of necessary amounts of BaCO
3and
Nd2O3(Y2O3) Before the synthesis homogenized mixtures
of reagents were compressed into tabletsMechanical activation of the synthesized oxides Nd-123
and Y-123 was performed in a high energy AGO-2 planetaryball mill (set material Fe) with acceleration of milling bodiesof 60 g The initial powders were dry milled for 05 1 2 and10min The obtained materials were mechanically activatedpowders (hereinafter MP) referred to respectively as N-05N-1 N-2 N-10 (series of Nd-123) and Y-05 Y-2 Y-10 (seriesof Y-123) The particles size was determined using a scanningelectron microscope Carl Zeiss EVO 40 (Germany) andamounted to (3ndash5) sdot 10minus6m while the particles themselveswere agglomerates consisting of stuck together crystalliteswith the size of nearly 03 sdot 10minus6m
X-ray examination of samples was carried out usinga diffractometer Shimadzu XRD-7000 (Japan) The size ofcoherent scattering regions (CSR) was determined by X-raydiffraction analysis using the approximation method [14]Silicon powder was used to determine the instrumentalbroadening of the diffraction lines Selection of the functionfor approximating diffraction peaks was made using theprogram [15]
Thermal studies were carried out using the thermal ana-lyzer Netzsch STA 449C Jupiter (Germany) combined witha mass spectrometer Netzsch QMS 403C Aeolos (Germany)for evolved gas analysis The rates of heating and cooling ofsamples were 10 Kmin
Themagnetization (119898) wasmeasured using a commercialvibrating sample magnetometer Cryogenic CFS-9T-CVTIin the temperature range 42ndash300K The measurements inthe heating mode were performed on samples cooled in amagnetic field (field cooling FC) and in the absence of mag-netic field (zero field cooling ZFC)
XPS study was performed on a OmicronMultiprob spec-trometer (Germany) The test sample (RBa
2Cu3O6+120575
powderand R
2BaCuO
5ceramic tablet where R=Y Nd) was attached
to the sample holder using conductive double-sided adhesivetape and moved into the workspace of the spectrometerCeramic samples were subjected to scribing in ultrahighvacuum before study The source of the exciting radiation forXPSwasMg-anode of X-ray gunwith 170WThe energy scaleof the spectrometer was calibrated by the binding energiesof the peaks Au 4f
72(8400 eV) Ag 3d
52(36829 eV) and
Cu 2p32
(93267 eV) The value of samples surface chargewas determined by the difference between the measuredbinding energy of the C 1s signal due to CndashH groups and thevalue of 2850 eV Wide-scan survey spectra were recordedwith 05 eV energy step and the signal accumulation timeof 1 s at the pass energy (119864PE) of 100 eV High-resolutionspectrum was recorded with 005 eV energy step exposuretime of 75 s (15 scans by 05 s) and 119864PE = 20 eV Theaccuracy of peak position determination in the latter case was01 eV Decomposition of the spectra into components andextraction of the background were performed by the Shirleymethod using the program XPSPeak 41
Journal of Spectroscopy 3
3 Experimental Results
31 Oxides Y2BaCuO
5and Nd
2BaCuO
5
Attestation of Y2BaCuO
5and Nd
2BaCuO
5Oxides by XRD
and XPS Methods X-ray analysis has not shown the presenceof any impurity phases in the synthesized oxides Y
2BaCuO
5
and Nd2BaCuO
5 Syngony space group and lattice param-
eters for Y2BaCuO
5oxide are respectively orthorhombic
Pbnm a = 71304(6) A b = 121761(10) A c = 56571(6) A forNd2BaCuO
5oxide tetragonal P4mbm a = 66950(5) A c =
58188(9) AThe results of XPS study of these oxides are shown in
Figure 1 Decomposition of the obtained electronic spectrawas carried out on the basis of choosing the most appropriatemodel for the phase composition of the surface and themutual coherence between the spectra of different elements(with adjustments taking into account the analyzer trans-mission efficiency and differences in the photoionizationcross-section) The spectrometric data for oxides BaO Y
2O3
Nd2O3 and barium carbonate were taken from [16 33ndash35]
respectivelyLet us discuss some controversial points arising during
decomposition of the spectra As can be seen from Figure 1in the spectra of the sample containing neodymium thereare the intense peaks at 7790 (Ba 3d
52) and 5286 (O 1s)
eV which coincide with the signal from BaO [33] with highaccuracy This can mean that the synthesis of the samplehas not been completed and the unspent furnace chargecomponents have been localized in the surface layer of thematerial (location explains the fact that X-ray analysis unlikeXPS has not revealed the presence of impurity oxides inthe sample) hiding the main compound (Nd
2BaCuO
5) and
making its identification ambiguous To test this hypothesiswe have prepared one more sample Nd
2BaCuO
5at more
high the synthesis temperaturemdash1050∘C It was expected thatif indicated signals belonged to BaO their intensity wouldsignificantly decrease along with increase in intensity of themain compound peaks after the new heat treatment Butnothing like this has happenedmdashthe intensity of all the peaksstayed the sameThat proves that the peaks at 7790 (Ba 3d
52)
and 5286 (O 1s) eV relate directly to the oxide Nd2BaCuO
5
In addition to the main compound there is a bariumcarbonate on the surface of Nd
2BaCuO
5sample that is
confirmed by the peak of corresponding intensity at 2891 eVin the spectrum of C 1s see Figure 1 This presence is appar-ently due to insufficiently complete decomposition of sourceBaCO
3involved in the synthesis (there was not barium
carbonate on the surface of the sample synthesized at 1050∘Chowever there was a similar amount of unidentified bariumcompound with the binding energy of Ba 3d
52electronic
level of 7807 eV)Next we turn our attention to the sample Y
2BaCuO
5 for
which the intensity of the barium oxide peak in O 1s spec-trum according to calculations should be negligible andamount to sim150 of the main compound peak intensityHowever in a given location of the spectrum (more preciselynear 529 eV) there is a clear peak whose intensity is about 14of the intensity of the peak that is near (referred to Y
2BaCuO
5
compound) We suppose that this small peak also belongsto the main compound Indeed O 1s peak of Y
2BaCuO
5at
5313 eV is located near the corresponding peak of the yttriumoxide (see Figure 1) which is explained by the presence of thesame type of YndashO bond in both oxides Meanwhile there isalso a BandashO bond in Y
2BaCuO
5compound which should
be reflected by additional oxygen peak located near the O 1s-peak of barium oxide Note that only one peak was enough todescribe O 1s spectrum of Nd
2BaCuO
5
Quantitative analysis of the elements carried out on thebasis of the decomposition of the spectra has shown a goodagreement with formula composition for both compoundsunder study
32 Oxides YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
321 X-Ray Diffraction Study of Oxides YBa2Cu3O6+120575
andNdBa
2Cu3O6+120575
Theobtained lattice parameters data and thesize of the coherent scattering region are presented in Table 1One can see that the first 1-2 minutes of grinding lead to asignificant decrease in the size of CSR in both superconduc-tors that is refinement of the microstructure With increas-ing milling duration up to 10min further changes of CSR-size practically do not occur However there is a fundamentaldifference in the effect of mechanical activation on the phasecomposition of Y-123 andNd-123 In the initially single-phaseyttrium superconductor with increasingmilling duration theamount of impurity phase (Y
2BaCuO
5) increases continu-
ously whereas in the neodymium superconductor it is viceversamdasha small amount of impurity phase (Ba
2Cu3O5+x) exist-
ing in the initial sample is not observed in all mechanicallyactivated samples This confirms the findings of the highchemical stability of Nd-123 oxide by comparison with itsyttrium homologue
Another interesting point worthy of discussion is the factthat there is no more than one impurity in all the testedsamples (Y-123 and Nd-123) that according to the massbalance should affect the cation stoichiometry in the mainphase of the sample
As for Nd-123 samples deviations from the ideal cationstoichiometry after a long (150 hours) high-temperatureannealing is just a characteristic feature of them [9] Appear-ance of impurity Ba
2Cu3O5+x phase in an amount of 3
indicates that the IP of Nd-123 (sample N-0) is in fact a solidsolution Nd
103Ba197
Cu3O6+120575
Unspent Ba (in amount ofsim3) seems to form under atmospheric moist air the X-rayamorphous phase of Ba(OH)
2sdot nH2O which is easily trans-
formed into BaCO3from the surface due to the presence of
CO2in the air
Y-123 MP which contains a rich by yttrium impurityY2BaCuO
5 to comply with the ion balance should include
the phase not containing this element Since these phaseswere not detected by XRD we have assumed that as a resultof mechanical activation they became X-ray amorphous Infact they were later identified by us with the use of XPS seelater
322 XPS Study of YBa2Cu3O6+120575
Oxide Figure 2 shows thesurvey spectra of the powders YBa
2Cu3O6+120575
under study
4 Journal of Spectroscopy
Cu 2p
Nd2BaCuO5
Y2BaCuO5
930 940 950 960Binding energy (eV)
(a)
Nd2BaCuO5
Y2BaCuO5
280 282 284 286 288 290Binding energy (eV)
C 1s
(b)
Nd2BaCuO5
BaCO3
Y2BaCuO5
BaO
776 780 784 788 792 796 800 804Binding energy (eV)
Ba 3d
(c)
BaCO3
Y2BaCuO5
524 526 528 530 532 534 536 538Binding energy (eV)
Y2O3
Nd2BaCuO5
Nd2O3
O 1s
(d)
Nd2O3
Nd2BaCuO5
116112 120 124 128 132Binding energy (eV)
Nd 4d
(e)
Y 3d
Y2BaCuO5
Y2O3
148 150 152 154 156 158 160 162 164Binding energy (eV)
(f)
Figure 1 XPS spectra of Y2BaCuO
5and Nd
2BaCuO
5oxides The peaks related to the main oxide are marked by bold lines The ordinate
hereinafter is the intensity of the XPS signal in arbitrary units To reduce the figure size the y-axis itself is not shown
Journal of Spectroscopy 5
Table 1 Phase composition lattice parameters and the size of coherent scattering regions (119871) for YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
beforeand after mechanical treatment
Crystallographic parameters Milling duration in AGO-2(1) YBa
2Cu3O6+120575
powders0 s
(sample Y-0)30 s
(sample Y-05)2min
(sample Y-2)10min
(sample Y-10)The main phasemdashorthorhombic SG Pmmm119886 A 38208(3) 38218(3) 38287(10) 38344(10)119887 A 38884(5) 38893(5) 38938(15) 38879(15)119888 A 116809(11) 116793(12) 116739(33) 116663(31)119881 A3 173541(53) 173599(55) 174036(161) 173919(158)Impurity mass mdash sim5 Y
2BaCuO
5sim5 Y
2BaCuO
5sim7 Y
2BaCuO
5
119871 nm 167 57 25 20(2) NdBa
2Cu3O6+120575
powders0 s
(sample N-0)30 s
(sample N-05)2min
(sample N-2)10min
(sample N-10)The main phasemdashorthorhombic SG Pmmm119886 A 38677(1) 38731(3) 38727(12) 38754(12)119887 A 39202(1) 39206(10) 39225(14) 39161(15)119888 A 117612(3) 117622(24) 117630(39) 117661(24)119881 A3 178328(6) 178608(118) 178688(178) 178564(212)Impurity mass sim3 Ba
2Cu3O5+119909
mdash mdash mdash119871 HM 1792 325 229 169
200 400 600 800 1000 1200Binding energy (eV)
Y-10Cu 2p
Y-2Fe 2pY-05
Y 3d Y-0Ba 4d
Ba 3d
C 1s
O 1s
0
Figure 2 XPS survey spectra of the initial and mechanoactivatedYBa2Cu3O6+120575
samples
Recording such spectra conducted in high sensitivity mode(at high 119864PE) allows to consider the main lines of all elementspresented in the surface layer of the material in amountsgreater than 03 at As could be expected there are peaks ofthe electronic levels of yttrium barium copper and oxygencontained in the composition of the oxide under study TheC 1s peak includes a signal from the carbon contamination ofthe random nature
One can see (Figure 2) that on the surface of MP sam-ples there is no iron (mill headsets material) leading tothe appearance of specific magnetic and superconductingproperties of the material Strongly increased barium peak
(represented as a doublet of Ba 3d52minusBa 3d
32) in the spectra
of activated samples testifies the redistribution of elementsbetween the volume and surface occurs which is usuallythe result of chemical degradation of the surface under theinfluence of an environment In this case it could be a well-established [36] reactions as follows
2YBa2Cu3O65+119909+ 3H2O
997888rarr Y2BaCuO
5+ 3Ba(OH)
2+ 5CuO+ uarr119909O
2
(1)
Ba(OH)2+ CO2997888rarr BaCO
3+H2O (2)
Table 2 summarizes the obtained BaCO3of CP grade cal-
cinated at 700∘C Y2BaCuO
5and taken from the literature of
spectrometric data for the reactants involved in the reactions(1) and (2) for reliable identification of the peaks of thesecompounds in the spectra of the samples under study
High-resolution XPS spectra showing the characteristicelectronic levels of the elements constituting Y-123 samplesare presented in Figure 3
The analysis of the Ba 3d spectra has showed that in addi-tion to barium carbonate (line Ba 3d
52at 7799 eV) there is
the phase Y2BaCuO
5(line Ba 3d
52at sim782 eV) on the surface
of the samplesThe line Ba 3d52
at 7780 eVwhich is observedonly in the IP is directly owned by Y-123 (see Table 2)The Y 3d spectra confirm the presence of Y
2BaCuO
5-phase
on the surface of samples the substancersquos line Y 3d52
at1587 eV is clearly visible in these spectra (see Table 2)Besides the Y 3d spectra reveal the surface contains thefollowing oxides Y
2O3[34] (line Y 3d
52at 1569 eV) Y-123
6 Journal of Spectroscopy
Ba 3d
Y-10
Y-2
Y-05
Y-0
776 780 784 788 792 796 800Binding energy (eV)
3d523d32
(a)
Binding energy (eV)
Y 3d
Y-10
Y-2
Y-05
Y-0
150 152 154 156 158 160 162 164 166
(b)
Cu 2p
Y-10 Satellite I Satellite II
Y-2
Y-05
Y-0
930 940 950 960 970Binding energy (eV)
2p32
2p12
(c)
Figure 3 XPS spectra of YBa2Cu3O6+120575
powders Dark shading the main phase signal light shading Y2BaCuO
5signal
Table 2 The positions of the characteristic XPS lines of barium compounds
Electron orbital BaCO3 Ba(OH)2 Y-123 Y2BaCuO
5
Binding energy eV
Ba 3d52
7799 [16 17]7798lowast
7813 plusmn 01[18 19]
7777 plusmn 01[20ndash23] 7819lowast
Ba 4d52 893lowast 875
[22]
Y 3d52
1560 plusmn 02[21 24 25] 1587lowast
Cu 2p32
9335[21 26] 9356lowast
O 1s5314 plusmn 01[16 17]5314lowast
5312 qB[27]
52845 plusmn 005 qB[20ndash23] (5291 5313)lowast
C 1s28925 plusmn 015 qB
[16 17]2894lowast
lowastOur data
(line Y 3d52
at 1560 eV in the spectrum of IP) and the phaseY2(C2O4)3[37] (line Y 3d
52at 1601 eV) The presence of
Y2BaCuO
5compound in samples is also reflected in the
spectra of Cu 2p a high-energy doublet (main peak at9356 eV) corresponds to it At the same time the low-energyCu 2p-doublet parameters are close to those found in [22] forY-123 the main peak at 9335 eV a satellite at sim943 eV as wellas parameters relating to copper oxide Cu (II) [28] 9336 eVand 9425 eV respectively However from the analysis of thespectra of Ba 3d and Y 3d (see earlier) it can be argued that
the Cu 2p signal from the phase of Y-123 may be only in thespectrum of IP samples
Thus in addition to the main phase the surface of IPcontains the final products of the reactions (1) + (2) and Y
2O3
phase probably sourced by the initial precursor incompletelyconsumed during the synthesis of YBa
2Cu3O6+120575
As a resultof MA treatment the surface of the powder is covered with alayer of yttriumoxide and the products of reactions (1) + (2) toa considerable depth of at least 10 nm (judging by the amountof Y2BaCuO
5phase in the samples determined by XRD)
Journal of Spectroscopy 7
323 XPS Study of NdBa2Cu3O6+120575
Oxide Figure 4 demon-strates the survey spectra of Nd-123 powders One can seethat as in the case of Y-123 samples the signal representingthe iron was not observed for any intensive milling durationThe feature of Nd-123 samples is rather low intensity of the Ba3d and Ba 4d peaks for powders activated for 05 and 2min(compare Figure 4 with Figure 2 for Y-123 powder) Bariumpeaks has markedly increased (as well as oxygen O 1s peak)only at 10min of activation
Figure 5 shows the high-resolution spectra of the elec-tronic levels of barium (3d and 4d) neodymium (4d) andcopper (2p) in powders with different activation prehistoryIn the barium spectra the high-intensity peaks at 7799 eV(3d52
) and 893 eV (4d52
) are obviously responsible for thecompound BaCO
3 and the low-intensity peaks at 7780 and
876 eV which are observed only in IP samples (dark shadedin Figure 5) correspond to the main phase by analogy withY-123 samples The analysis of Cu 2p spectra has revealed thepresence of copper ions with the electronic structure similarto that in Y-123 or in CuO oxide
However as seen in Figure 5 the state Cu 2p with highbinding energy (9359 plusmn 03 eV) is also present in all Nd-123samples According to our data (see Table 3) this state is nottypical for simple and ternary compounds of copper DuringMA processing its share in Cu 2p spectra changes in strictaccordancewith the high energy components of the Ba 3d andBa 4d spectra light shaded in Figure 5 (at 7817 eV (Ba 3d
53)
and 919 plusmn 03 eV (Ba 4d53
)) which implies that a doubleoxide of barium-copper was on the surface of the samplesWe tend to identify this oxide as Ba
2Cu3O5+x phase which
was detected by X-ray diffraction analysis of IP samples (seeTable 1) Despite the fact that this phase was not found byXRD in samples N-05 N-1 and N-2 it is visible in the XPSspectra due to the effect of spatial localization
According to Figure 5 the surface of the samples alsocontained the oxide Nd
2O3(line Nd 4d
52at 1211 eV) which
under intense grinding at the initial stages was partly trans-formed into Nd
2(C2O4)3[37] (line Nd 4d
52at sim1225 eV)
Based on the analysis of possible superpositions of the spectraof Ba 3d Ba 4d and Cu 2p the low-energy Nd 4d doublet(line Nd 4d
52at 1157 eV) the intensity of which is almost
independent of the MA duration belongs to a double oxideNdCu
119910O15+y+z of undetermined composition The Nd 4d
doublet of themain compound apparently overlaps with oneof the previously noted signals and so it is shown explicitlyin Figure 5
On the intensity ratios of the peaks in Figure 5 one canconstruct a model of the relative position of the phases Nd-123 BaCO
3 and Ba
2Cu3O5+x in the surface layer of the
material (this method has been used eg in [22] to analyzethe relative position of the layers Y-123 and BaCuO
2) To
realize this we use the dependence of the layer thicknessanalyzed by XPS (usually taken as 3 sdot 120582
119898) on the kinetic
energy of the electrons [38] referring to the electrons givingthe corresponding lines in the spectra of Ba 3d and Ba 4d asfollows
120582119898= 2170119864
minus2
119896+ 072(119886119864
119896)12 (3)
Ba 3d
N-10Cu 2pN-2Fe 2p
O 1sN-05
N-0Cu LVVCu 3s C 1sNd 4d
Ba 4d200 400 600 800 1000
Binding energy (eV)0
Figure 4 XPS survey spectra of the initial and mechanoactivatedNdBa
2Cu3O6+120575
samples
where 120582119898is the electron mean free path expressed in mono-
layers 119886 is monolayer thickness in nm 119864119896is kinetic energy
in eV (119864119896= ℎ] minus 119864BE minus 120593) ℎ] = 12536 eV is the energy of
the exciting radiation used inXPS analysis119864BE is the bindingenergy of the electronic level under analysis and120593 is theworkfunction of the spectrometer (346 eV)
According to this relationship the thickness of the layerunder analysis increases monotonically with increasing 119864
119896
in the range 119864119896gt 40 eV As can be seen from Figure 6
increase in the thickness of the layer under analysis canaffect the following volume ratios detectable by XPS phaseIphase III and phase IIphase III and has no influence onthe volume relation phase Iphase II The phase fractionto a first approximation is proportional to the area undercorresponding XPS peak Therefore based on the ratio ofareas of the different lines in the spectra in Figure 5 one canconclude that both barium-containing products of chemicaldecomposition of Nd-123 are located atop of the main oxidethat is correspond to phases I and II in Figure 6 The thick-ness of the degraded layer in N-10 sample is sim10 nm (as theoriginal phase is barely visible through it) and in IP (N-0)sample it is estimated to be 5-6 nm
It should be noted however that such a small thicknessof Ba2Cu3O5+x layer in IP has not prevented this phase to be
recognized by XRD analysis (see Table 1) One can thereforeconclude that IP particles contain in addition a considerableamount of Ba
2Cu3O5+x in the form of individual inclusions
in bulk (as a result of this oxide synthesis features seeSection 1) DuringMA processing material particles crackedand inclusions went outside resulting in the fraction ofBa2Cu3O5+x phase on the surface increased up to a point
(up to 1min inclusive) The subsequent decrease in thisphase (see Figure 5) is apparently due to the fact that anotherprocess also developed on the surface during grindingspending of Ba
2Cu3O5+x involving the original solid solution
Nd1+xBa2minusxCu3O6+120575 to formation of cation-stoichiometric
NdBa2Cu3O6+120575
To prove the occurrence of such interaction
8 Journal of Spectroscopy
Ba 3d
N-10
N-2
N-1
N-05
N-0
770 775 780 785 790 795 800 805Binding energy (eV)
(a)
N-10
N-1
Binding energy (eV)
Ba 4d
Ba 4d
N-2
N-05
N-0
68 72 80 84 88 92 96
Cu 3p X-ra
ysa
telli
tes
76
(b)
N-10
N-2
N-1
N-05
N-0
930 940 950 960 970Binding energy (eV)
Satellite I Satellite II
Cu 2p2p32
2p12
(c)
N-10
N-2
N-1
N-05
N-0
110 115 120 125 130 135Binding energy (eV)
Nd 4d
(d)
Figure 5 XPS spectra of NdBa2Cu3O6+120575
powders
119864119896 (Ba 3d) 119864119896 (Ba 4d)
Phase I Phase II
Phase III
Phase I Phase II
Phase III
31205823120582
XPS
study
area
XPS
study
area
lt
Figure 6 Analysis of the mutual arrangement phases in the surface layer of the material and their volume relations from XPS data
Journal of Spectroscopy 9
Table 3 Characteristic spectral parameters of different copper compounds
Electron orbital CuO CuCO3 Cu(OH)2 Cu2CO3(OH)2 Nd2BaCuO5
Binding energy eVBa 3d
527790lowast
Nd 4d52
1182lowast
Cu 2p32
9337 plusmn 1[28ndash30]
9348[28]
93474 plusmn 006[29 31]
9347[32] 9335lowast
O 1s 52974 plusmn 006[30 31]
53124[31] 5286lowast
lowastOur data
later we present the data of magnetic measurements whichindicate that MA treatment results in significant increase inthe temperature of the superconducting transition in separateregions of the material
324 Thermal Analysis of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
Samples of R-123 have been studied by thermogravimetrycoupled withmass-spectrometry to analyze the gases evolvedduring experiments Results of the study are summarizedin Figure 7 It is seen that reversible change in mass of IP-samples occurs in the range of 430ndash900∘C that must be dueto oxygen exchange between nonstoichiometric R-123 oxidesand the gas phase taking place at these temperatures [1] MPsamples start losing mass sharply around 70∘C when heatedMass spectrometry analysis of thermal desorption productsindicates the presence of large amount of water and a smallamount of carbon dioxide contained in the samples in theform of BaCO
3(the temperature range in which the CO
2
was released and the value of 119901CO2used for thermal analysis
of the atmosphere was consistent with conditions of bariumcarbonate decomposition)
325 Study of Magnetic Properties of YBa2Cu3O6+120575
andNdBa
2Cu3O6+120575
Temperature dependences of ZFC magne-tization of the samples Y-0 Y-05 Y-2 and Y-10 are shownin Figure 8 A sharp downturn in magnetization at sim90Kobserved in the samples Y-0 Y-05 and Y-2 clearly showsthe presence of the superconducting phase Superconductingtransition temperatures of the samples Y-0 Y-05 and Y-2have been determined by taking the derivative of the mag-netization against the temperature (119889119898119889119879) Thus definedtemperatures 119879
119888are equal to 91 K for the samples Y-0 and
Y-05 and 88K for the sample Y-2 A wide transition widtharound 119879
119888= 90K indicates that both the initial and MP
samples contain inhomogeneous superconductor phaseswithdifferent 119879
119888 The following facts indicate the presence of
paramagnetic contribution in the magnetization behavior ofMP samples and its growth with increasing milling durationa significant increase in magnetization 119898 of the samples Y-05 and Y-2 compared with the initial sample Y-0 at thetemperatures 119879 gt 119879
119888 weak temperature dependence 119898(119879)
in the temperature range 100ndash300 K for MP samples asignificant increase in themagnetization of Y-10 sample at lowtemperatures
100
99
98
97
96
95
94
93
92
100
99
98
97
96
95
94
93
92
0 200 400 600 800 1000
0 200 400 600 800 1000
14
12
10
8
6
4
3
2
Temperature (∘C)
Ion
curr
ent (
A)
Ion
curr
ent (
A)
Sam
ple w
eigh
t (
)
H2O
CO2
H2O (times1010) CO2 (times1011)
3
2
1
3998400
1998400
2998400
Figure 7 Thermal analysis results for samples Y-0 (1) N-0 (11015840) Y-2 (2) N-2 (21015840) and Y-10 (3) N-10 (31015840) Mass spectrometry data arerelated to the samples Y-10 (solid curves) and N-10 (dashed lines)
For comparison Figure 9 shows the temperature depen-dence of the FC magnetization in a magnetic field 119867 =500Oe for two new samples of Y-123 (120575 asymp 07) The firstsample has been freshly prepared and the other one has beensubjected to treatment at 297 plusmn 1K for 120 h at absolutehumidity of 23 120581Pa The sample with low oxygen content(and as a consequence with low 119879
119888) has been chosen due
to its relatively easy moisture saturation in these conditionswithout the use of MA (moisture saturation was controlledby the increase in weight which eventually was sim4wt)One can see that the sample saturated with water has apositive magnetic moment above the temperature 119879
119888and
shows an increase inmagnetic moment on cooling below this
10 Journal of Spectroscopy
N-0
N-1
N-10N-2
Y-2
Y-05
N-05
Y-0
Y-10
005 0005
0004
0003
0002
0001
0
0
minus005
minus01
minus015
minus02
minus025
minus03
minus01
minus02
minus03
003
002
001
0
0
0minus001
20 40 60 80 100 120 140119879 (K)
119898(e
mu
g)119898
(em
ug)
119898(e
mu
g)119898
(em
ug)
Figure 8 ZFC magnetizations as a function of temperature at119867 = 50Oe for the initial and mechanically activated samplesYBa2Cu3O6+120575
(top) NdBa2Cu3O6+120575
(bottom)
temperature similarly to Y-10 sample Onset temperature ofthe magnetic anomaly in the hydrated sample is the sameas that in the freshly prepared sample This experimentdemonstrates that the presence of water in MP sampleshas a significant effect on the temperature dependences ofthe magnetization observed in samples of Y-123 series (seeFigure 8)
Temperature dependences of ZFC magnetization of MPsamples in Nd-123 series are shown in Figure 8 The super-conducting transition temperatures of the samples N-0 N-05 and N-1 are independent of milling duration and equal to119879119888sim 57KMechanical treatment leads to a substantial change
in the magnetization of MP samples throughout the inves-tigated temperature range MP samples exhibit near-room-temperature hysteretic behavior that is ZFC magnetizationis more diamagnetic than FCmagnetization It may be due tomagnetic particles of mechanoactivatedNd-123 samples or tothe presence of impurity phases whose low content or highlydisordered crystal structures do not allow to observe thesephases by X-ray diffraction measurements We also cannotexclude the formation of CuO phase (119879
119873sim 220K) at the
surface of large NdBa2Cu3O6+120575
particles proceeding undermechanical activationAt the same time a significant increasein the paramagnetic contribution to the magnetization withincreasing milling duration is observed
004
002
0
minus002
minus004
minus006
minus0080 20 40 60 80 100 120 140
0 20 40 60 80 100 120 140
119898(e
mu)
119898(e
mu)
119879 (K)
119879 (K)
004
0038
0036
0034
Figure 9 FCmagnetizations as a function of temperature of freshlyprepared YBa
2Cu3O6+120575
sample (empty points) and of hydrated sam-ple (black points) at119867 = 500Oe Inset the temperature dependenceof magnetization of hydrated sample at119867 = 10 kOe
A wide transition width around 119879119888= 57K (|Δ119879
119888sim 20K|)
in MP samples of Nd-123 series cannot be explained only bythe presence of water in the structure The observed changesindicate that during MA treatment diffusion processes asso-ciated with the ordering of the cations Nd3+ and Ba2+ appa-rently occur according to [8ndash10] that has a significant effecton 119879119888
4 Discussion of Results
41 Interaction of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
withCO2 From comparison of Figures 4 and 5 it is clear that with
increasing duration of MA processing (120591119892) the amount of
barium-containing impurities on the surface of Nd-123 sam-ples continuously increases up to 120591
119892= 10min in contrast
to the situation for the oxide Y-123 for which initially (up120591119892= 05min) sudden change and subsequent (after 120591
119892=
05min) almost stagnation in the accumulation of chemicaldegradation products were observed (see Figures 2 and 3 anddata on the impurities in YBa
2Cu3O6+120575
sample) One can seefrom Figure 7 that the degree of water saturation (120578) of bothoxides (this parameter can be traced by sharp descendingbranch of sample mass change in the temperature range of30ndash450∘C) obeys similar relationships with increasing 120591
119892 its
growth with increasing MA duration close to proportionalfor Nd-123 (120578 sim 120591
119892) and tendency of 120578 to decrease for Y-123
(120578 = 155 sdot 120591119892
03) which is close to the root dependence char-
acteristic of reagent diffusion through the reaction productslayer
Taking into account the data in [1] stating the chemicaldegradation of Y-123 is carried out on the interface betweenY-123 and gas phase and one can explain sharply fallingrates of change in concentration of its products as well as ofH2O dissolved in the oxide the diffusion path length of H
2O
and CO2reactants to the location of the reactions (1) and
(2) increases with time 120591119892 However the uniformity of the
absorption of H2O and CO
2gases by MP of Nd-123 testifies
Journal of Spectroscopy 11
that the thickness of the degraded layer on the surface variesslightly Apparently it does not exceed 10 nm as indicated bya weak but clear signal of the main phase which appeared inthe Ba 4d-spectrum of N-10 sample (see Figure 5) Howeverit should be noted that Nd-123 MP sample actively entersinto chemical reactionwith atmospheric CO
2 the gas escapes
from the samples quite intensively when heated in the rangeof 800ndash900∘C (see Figure 7) Therefore the question oflocalization place of products of interaction between Nd-123and atmospheric components arises
Homogeneous nucleation and growth of interaction pro-ducts in the volume of Nd
1+xBa2minusxCu3O6+120575 parent phasemaybe the answer This assumption is based on the fact that theproducts of thermal desorption of N-10 sample (see Figure 7)contain weakly bound form of CO
2escaping in a wide tem-
perature range of 200ndash550∘C Obviously it is a form of gasdissolved in the structure Since the carbonization energy ofBa2+ ions is quite high homogeneous nucleation of carbonatephase at a certain concentration (equivactivity) of CO
2in the
structure facilitated by the participation of structural defects(whose concentration should be significant in MP samples)seems quite possible
42 Interaction of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
withWater In the Introductionwe have put links toworks statingthat the crucial feature for the practical application of thesuperconductor Nd-123 is its high resistance to chemicaldegradation under moisture Additional information thatexpands understanding of this feature has been received inour study Thus it is shown (see Figure 7) that a high con-centration of water accumulates in MP samples of Nd-123 indissolved form but the hydrolysis reaction development isquite limited as evidenced by the relatively low temperatureof H2O release from this oxide Moreover the results of
XRD and XPS analyzes have not detected even traces of theternary compound Nd
2BaCuO
5in these samples while it is
the compounds R2BaCuO
5due their characteristic colours
that are indicators of the hydrolysis reaction for the wholefamily of compounds R-123 [1 39 40] Thus if the hydrolysisreaction develops (there is a small peak on H
2O desorption
curve for sample N-10 at sim455∘C that can be attributed tothe chemically bound water) then it proceeds through non-traditional mechanism and with low rate
According to [41] the hydration mechanism for thehomologous series of R-123 compounds is in four stages Atthe initial stage water molecules penetrate into the bulk ofthe crystallites through the structural channels [(12) b 0]located in interspaces between CuO-chains typical for thistype of superconductors At the next stage protons whichare located in the oxygen positions of CuO-chains can besplit up of watermoleculesThis proton transfer is consideredto cause an internal (within the [CundashO]+-system) chargetransfer resulting in formation of molecular oxygen leavingthe structure At high concentrations of hydroxide ionsaccumulated in the structure the chemical decompositionof the initial oxide occurs Based on the previous schemeone can understand the reasons for high resistivity of N-123superconductor to chemical interaction with water
The authors of [42] discussed the high corrosion resis-tance of Nd-123 films in the water compared to the filmstructures of Y-123 and Eu-123 which was attributed to thepartial oxygen disorder in the planes of CuO-chains Sucha disorder should occur in Nd-123 due to the presence ofsome amount of Nd3+ ions in the sites nearby to CuO-planesof divalent barium According to the authors that shouldlead to overlapping structural channels for H
2O diffusion
and hence blocking the hydration process However ourdata on the thermal analysis (see Figure 7) illustrate thatthe saturation of Nd-123 structure with water during MAtreatment proceeds almost as fast as in Y-123 (in the rangeof 2ndash10 minutes even faster) Therefore the sought causeof the chemical stability of Nd-123 MP cannot be related toproblems of H
2O diffusion
The stage of removing oxygen from the structure is con-sidered [41 42] to be extremely important for the hydrationprocess of R-123 Thus the chemical degradation of Y-123oxide immersed in the water is completely stopped underpotential of 08 V relative to the standard electrode-saturatedsodium calomel [41] It is expected that the substitutionNd3+ rarr Ba2+ inNd-123 in addition to oxygen disordering inthe base structural plane should also lead to the strengtheningof its bondwith the lattice (due to electrostatic effect of highlycharged Nd3+ ion) [42] According to the authors [42] thisshould inhibit the reduction stage of hydration However it isimportant to consider the fact that the structure ofMP of Nd-123 contains a large amount of weakly bound CO
2 located
near Ba ions (since there is a tendency to the formation ofBaCO
3) therefore localized in the channels of the base plane
[(12) b 0] where also there is water In our opinion just theseCO2particles block channels of oxygen desorption which is
the main reason for the high stability of Nd-123 in relation tothe hydrolysis reaction
5 Conclusion
Thus as a result of mechanical activation treatment thesurface of YBa
2Cu3O6+120575
is covered by products of hydrolysisand carbonization to a considerable depth The chemicaldegradation process proceeds the normal waymdashthrough theformation of Y
2BaCuO
5phase
Chemical degradation of mechanoactivatedNdBa
2Cu3O6+120575
powders under the impact of CO2
isnot directly connected to hydrolysis process as occurs inYBa2Cu3O6+120575
(see reactions (1) and (2)) Carbonizationproceeds homogeneously through the stage of carbondioxide dissolution in the lattice of NdBa
2Cu3O6+120575
In itsturn the presence of CO
2molecules in the structure of
mechanoactivated NdBa2Cu3O6+120575
powders leads to a radicalchange in the mechanism of interaction between the super-conductor and water This mechanism eliminates the normalfor a homologous series of RBa
2Cu3O6+120575
the hydrolysisreaction with the formation of characteristic ldquocolorrdquoR2BaCuO
5phases The rate of chemical decomposition of
mechanically activated NdBa2Cu3O6+120575
by the new mecha-nism (not yet studied) is quite low
12 Journal of Spectroscopy
Mechanical treatment affects the temperature depen-dence of the magnetization of RBa
2Cu3O6+120575
compoundsThere is a significant increase in the paramagnetic and ferro-magnetic contributions to the magnetization with increasingmilling duration The latter leads to near-room-temperaturehysteretic behavior of NdBa
2Cu3O6+120575
samples between ZFCandFC regimes Itmay be due tomagnetic particles ofmecha-noactivated NdBa
2Cu3O6+120575
samples or to the presence ofimpurity phases whose low content or highly disorderedcrystal structures do not allow to observe these phases byX-ray diffraction measurements The mechanical treatmentdoes not have substantial influence on the transition tem-peratures of superconducting phases 119879
119888in the RBa
2Cu3O6+120575
compounds but a wide transition width around 119879119888indicates
that mechanically activated samples contain inhomogeneoussuperconductor phases with different 119879
119888 The broadening
of the superconducting transition in mechanically activatedNdBa
2Cu3O6+120575
samples may be due to redistribution ofcations between Nd- and Ba-sublattice
Finally we note that the high temperature superconduc-tor RBa
2Cu3O6+120575
subjected to mechanical activation cer-tainly has no significant advantages over conventional non-mechanoactivated material but it is obvious that physical-chemical studies of such powders reveal results interestingfrom the point of view of fundamental science
Acknowledgment
This work was supported by Russian Foundation for BasicResearch (Grant no 11-03-00317-a)
References
[1] I E Graboi A R Kaulrsquo and G Yu Metlin ldquoAdvances in scienceand technologyrdquo in Solid State Chemistry pp 3ndash142 VINITIANSSSR Moscow Russia 1989
[2] S Anders M G Blamire F-Im Buchholz et al ldquoEuropeanroadmap on superconductive electronicsmdashstatus and perspec-tivesrdquo Physica C vol 470 no 23-24 pp 2079ndash2126 2010
[3] B Ruck B Oelze R Dittmann et al ldquoMeasurement of thedynamic error rate of a high temperature superconductor rapidsingle flux quantum comparatorrdquo Applied Physics Letters vol72 no 18 pp 2328ndash2330 1998
[4] M W Rupich X Li C Thieme et al ldquoAdvances in secondgeneration high temperature superconducting wire manufac-turing and RampD at American superconductor corporationrdquoSuperconductor Science and Technology vol 23 no 1 Article ID014015 2010
[5] A Rakitin M Kobayashi and A P Litvinchuk ldquoSuperi-onic behavior of high-temperature superconductorsrdquo PhysicalReview B vol 55 no 1 pp 89ndash92 1997
[6] T Kagiyama J Shimoyama K D Otzschi et al ldquoEffect of cationcomposition and oxygen nonstoichiometry on 119869
119888-119861 properties
of Nd123rdquo Physica C vol 341ndash348 no 2 pp 1445ndash1446 2000
[7] M Badaye J G Wen K Fukushima et al ldquoSuperior propertiesof NdBa
2Cu3O119910over YBa
2Cu3O119909thin filmsrdquo Superconductor
Science and Technology vol 10 no 11 pp 825ndash830 1997
[8] C Cantoni D P Norton D M Kroeger et al ldquoPhase stabilityfor the in situ growth of Nd
1+119909Ba2minus119909
Cu3O119910films using pulsed-
laser depositionrdquo Applied Physics Letters vol 74 no 1 pp 96ndash98 1999
[9] E A Goodilin N N Oleynikov E V Antipov et al ldquoPhasestability for the in situ growth of Nd
1+119909Ba2minus119909
Cu3O119910films using
pulsed-laser depositionrdquo Physica C vol 272 6578 pages 1996[10] E Guilmeau F Giovannelli I Monot-Laffez S Marinel J
Provost and G Desgardin ldquoTop seeding melt texture growthof NdBaCuO pellets in airrdquoThe European Physical Journal vol13 no 3 pp 157ndash160 2001
[11] A I Ancharov T F Grigorrsquoeva T Yu Kiseleva A A Novakovaet al inMechanocomposites-Precursorsfor the Creation of Mate-rials with New Properties O I Lomovskii Ed p 424 Izd-voSO RAN Novosibirsk Russia 2010
[12] A Hamrita F Ben Azzouz A Madani and M Ben SalemldquoMagnetoresistivity and microstructure of YBa
2Cu3O119910pre-
pared using planetary ball millingrdquo Physica C vol 472 no 1pp 34ndash38 2012
[13] R P Vasquez ldquoIntrinsic photoemission signals surface prepa-ration and surface stability of high temperature superconduc-torsrdquo Journal of Electron Spectroscopy and Related Phenomenavol 66 no 3-4 pp 209ndash222 1994
[14] S S Gorelik L N Rastorguev and A Yu Skakov in Rentgeno-graphIcheskII I ElektronographIcheskII AnalIz p 368 Izd-voMetallurgia Moscow Russia 1970
[15] M V Reshetniak and O V Sobol Program for diffractionanalysis ldquoNew Profilerdquo(Last update 10 02 2007) Version 3 4400 (Freeware) WIN9xMENT2KXP Copyright (c) 1992-2007 ReMax SoftWare 2000
[16] M Wegmann L Watson and A Hendry ldquoXPS analysis of sub-micrometer barium titanate powderrdquo Journal of the AmericanCeramic Society vol 87 no 3 pp 371ndash377 2004
[17] A B Christie J Lee I Sutherland and J M Walls ldquoAn XPSstudy of ion-induced compositional changes with group II andgroup IV compoundsrdquo Applications of Surface Science vol 15no 1ndash4 pp 224ndash237 1983
[18] U A Joshi S Yoon S Balk and J S Lee ldquoSurfactant-freehydrothermal synthesis of highly tetragonal barium titanatenanowires a structural investigationrdquo Journal of Physical Chem-istry B vol 110 no 25 pp 12249ndash12256 2006
[19] R Caracciolo ldquoChemical characterization techniques for thinfilmsrdquo in Ceramic Films and Coatings J B Wachtman and R AHaber Eds p 376 New Jersey NJ USA 1992
[20] I N Shabanova Y A Naimushina and N S Terebova ldquoCom-position and temperature dependence of a Y-Ba-Cu-O HTSCelectronic structurerdquo Superconductor Science and Technologyvol 15 no 7 pp 1030ndash1033 2002
[21] J Beyer T Schurig S Menkel Z Quan and H Koch ldquoXPSinvestigation of the surface composition of sputtered YBCOthin filmsrdquo Physica C vol 246 no 1-2 pp 156ndash162 1995
[22] C C Chang M S Hegde X D Wu et al ldquoSurface layers onsuperconducting Y-Ba-Cu-O films studied with x-ray photo-electron spectroscopyrdquo Applied Physics Letters vol 55 no 16pp 1680ndash1682 1989
[23] X D Wu A Inam M S Hegde et al ldquoCrystalline perfectionof as-deposited high-Tc superconducting thin-film surfacesion channeling and x-ray photoelectron spectroscopy studyrdquoPhysical Review B vol 38 no 13 pp 9307ndash9310 1988
[24] P Rajasekar P Chakraborty S K Bandyopadhyay P Barat andP Sen ldquoX-ray photoelectron spectroscopy study of oxygen and
Journal of Spectroscopy 13
argon annealed YBa22Cu3O7minus120575
rdquo Modern Physics Letters B vol12 no 6-7 pp 239ndash245 1998
[25] J Halbritter P Walk H J Mathes B Haeuser and H RogallaldquoARXPS-studies of c-axis textured YBa
2Cu3O119909-filmsrdquo Physica
C vol 153ndash155 no 1 pp 127ndash128 1988[26] T J Sarapatka and P Mikusık ldquoXPS study of PbYBaCuO thin-
film tunnel contactrdquo Applied Surface Science vol 68 no 1 pp35ndash40 1993
[27] J A T Verhoeven and H Van Doveren ldquoAn XPS investigationof the interaction of CH
4 C2H2 C2H4and C
2H6with a barium
surfacerdquo Surface Science vol 123 no 2-3 pp 369ndash383 1982[28] C D Wagner W M Riggs L E Davis J F Moulder and G
E Mullenberg Handbook of X-Ray Photoelectron SpectroscopyPerkin-Elmer Corp Eden Prairie Minn USA 1979
[29] M C Biesinger L W M Lau A R Gerson and R S C SmartldquoResolving surface chemical states in XPS analysis of first rowtransition metals oxides and hydroxides Sc Ti V Cu and ZnrdquoApplied Surface Science vol 257 no 3 pp 887ndash898 2010
[30] X Y Fan Z GWu P X Yan et al ldquoFabrication of well-orderedCuO nanowire arrays by direct oxidation of sputter-depositedCu3N filmrdquo Materials Letters vol 62 no 12-13 pp 1805ndash1808
2008[31] S J Kerber J J Bruckner K Wozniak S Seal S Hardcastle
and T L Barr ldquoNature of hydrogen in x-ray photoelectronspectroscopy general patterns from hydroxides to hydrogenbondingrdquo Journal of Vacuum Science and Technology A vol 14no 3 pp 1314ndash1320 1996
[32] G Moretti G Fierro M Lo Jacono and P Porta ldquoCharac-terization of CuO-ZnO catalysts by X-ray photoelectron spec-troscopy precursors calcined and reduced samplesrdquo Surfaceand Interface Analysis vol 14 no 6-7 pp 325ndash336 1989
[33] H Van Doveren and J A T H Verhoeven ldquoXPS spectra of CaSr Ba and their oxidesrdquo Journal of Electron Spectroscopy andRelated Phenomena vol 21 no 3 pp 265ndash273 1980
[34] B V Crist Handbooks of Monochromatic XPS Spectra Volume2mdashCommercially pure binary oxides XPS International LLCLeona Tex USA 2005
[35] D D Sarma and C N R Rao ldquoXPES studies of oxides ofsecond- and third-row transition metals including rare earthsrdquoJournal of Electron Spectroscopy and Related Phenomena vol 20no 1 pp 25ndash45 1980
[36] V I Nefedov and A N Sokolov ldquoDegradatzia visokotemper-aturnich sverchprovodnikov pri khimicheskich vozdeistviachrdquoZhurnal Neorganicheskoi Khimii vol 34 no 11 pp 2723ndash27391989
[37] Y Uwamino T Ishizuka and H Yamatera ldquoX-ray photoelec-tron spectroscopy of rare-earth compoundsrdquo Journal of ElectronSpectroscopy and Related Phenomena vol 34 no 1 pp 67ndash781984
[38] M P Seah and W A Dench ldquoQuantitative electron spec-troscopy of surfaces a standard data base for electron inelasticmean free paths in solidsrdquo Surface and Interface Analysis vol 1no 1 pp 2ndash11 1979
[39] C H Lin H C I Kao and C M Wang ldquoKinetics andstability of R(Ba
15Sr05)Cu3O119910(R = La Nd Sm Eu Gd Dy Ho)
superconductors inwaterrdquoMaterials Chemistry and Physics vol82 no 2 pp 435ndash439 2003
[40] A G Knizhnik R A Stukan and G O Eremenko ldquoStudy theinteraction between europium HTSC of 123 type and waterrdquoSverkhprovodimost vol 4 no 1 pp 177ndash182 1991 (Russian)
[41] J Zhou R K Lo J T McDevitt et al ldquoDevelopment of areliable materials base for superconducting electronicsrdquo Journalof Materials Research vol 12 no 11 pp 2958ndash2975 1997
[42] S B Schougaard M F Ali and J T McDevitt ldquoEvidence forhigh stability against water corrosion of NdBa
2Cu3O7plusmn120575
relativeto YBa
2Cu3OO7minus120575
and EuBa2Cu3OO7minus120575
rdquo Applied Physics Let-ters vol 84 no 7 pp 1144ndash1146 2004
Submit your manuscripts athttpwwwhindawicom
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Inorganic ChemistryInternational Journal of
Hindawi Publishing Corporation httpwwwhindawicom Volume 2014
International Journal ofPhotoenergy
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Carbohydrate Chemistry
International Journal of
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Journal of
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Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
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Bioinorganic Chemistry and ApplicationsHindawi Publishing Corporationhttpwwwhindawicom Volume 2014
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The Scientific World JournalHindawi Publishing Corporation httpwwwhindawicom Volume 2014
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Chromatography Research International
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Applied ChemistryJournal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Theoretical ChemistryJournal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
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Analytical ChemistryInternational Journal of
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Quantum Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Organic Chemistry International
ElectrochemistryInternational Journal of
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Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
CatalystsJournal of
Journal of Spectroscopy 3
3 Experimental Results
31 Oxides Y2BaCuO
5and Nd
2BaCuO
5
Attestation of Y2BaCuO
5and Nd
2BaCuO
5Oxides by XRD
and XPS Methods X-ray analysis has not shown the presenceof any impurity phases in the synthesized oxides Y
2BaCuO
5
and Nd2BaCuO
5 Syngony space group and lattice param-
eters for Y2BaCuO
5oxide are respectively orthorhombic
Pbnm a = 71304(6) A b = 121761(10) A c = 56571(6) A forNd2BaCuO
5oxide tetragonal P4mbm a = 66950(5) A c =
58188(9) AThe results of XPS study of these oxides are shown in
Figure 1 Decomposition of the obtained electronic spectrawas carried out on the basis of choosing the most appropriatemodel for the phase composition of the surface and themutual coherence between the spectra of different elements(with adjustments taking into account the analyzer trans-mission efficiency and differences in the photoionizationcross-section) The spectrometric data for oxides BaO Y
2O3
Nd2O3 and barium carbonate were taken from [16 33ndash35]
respectivelyLet us discuss some controversial points arising during
decomposition of the spectra As can be seen from Figure 1in the spectra of the sample containing neodymium thereare the intense peaks at 7790 (Ba 3d
52) and 5286 (O 1s)
eV which coincide with the signal from BaO [33] with highaccuracy This can mean that the synthesis of the samplehas not been completed and the unspent furnace chargecomponents have been localized in the surface layer of thematerial (location explains the fact that X-ray analysis unlikeXPS has not revealed the presence of impurity oxides inthe sample) hiding the main compound (Nd
2BaCuO
5) and
making its identification ambiguous To test this hypothesiswe have prepared one more sample Nd
2BaCuO
5at more
high the synthesis temperaturemdash1050∘C It was expected thatif indicated signals belonged to BaO their intensity wouldsignificantly decrease along with increase in intensity of themain compound peaks after the new heat treatment Butnothing like this has happenedmdashthe intensity of all the peaksstayed the sameThat proves that the peaks at 7790 (Ba 3d
52)
and 5286 (O 1s) eV relate directly to the oxide Nd2BaCuO
5
In addition to the main compound there is a bariumcarbonate on the surface of Nd
2BaCuO
5sample that is
confirmed by the peak of corresponding intensity at 2891 eVin the spectrum of C 1s see Figure 1 This presence is appar-ently due to insufficiently complete decomposition of sourceBaCO
3involved in the synthesis (there was not barium
carbonate on the surface of the sample synthesized at 1050∘Chowever there was a similar amount of unidentified bariumcompound with the binding energy of Ba 3d
52electronic
level of 7807 eV)Next we turn our attention to the sample Y
2BaCuO
5 for
which the intensity of the barium oxide peak in O 1s spec-trum according to calculations should be negligible andamount to sim150 of the main compound peak intensityHowever in a given location of the spectrum (more preciselynear 529 eV) there is a clear peak whose intensity is about 14of the intensity of the peak that is near (referred to Y
2BaCuO
5
compound) We suppose that this small peak also belongsto the main compound Indeed O 1s peak of Y
2BaCuO
5at
5313 eV is located near the corresponding peak of the yttriumoxide (see Figure 1) which is explained by the presence of thesame type of YndashO bond in both oxides Meanwhile there isalso a BandashO bond in Y
2BaCuO
5compound which should
be reflected by additional oxygen peak located near the O 1s-peak of barium oxide Note that only one peak was enough todescribe O 1s spectrum of Nd
2BaCuO
5
Quantitative analysis of the elements carried out on thebasis of the decomposition of the spectra has shown a goodagreement with formula composition for both compoundsunder study
32 Oxides YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
321 X-Ray Diffraction Study of Oxides YBa2Cu3O6+120575
andNdBa
2Cu3O6+120575
Theobtained lattice parameters data and thesize of the coherent scattering region are presented in Table 1One can see that the first 1-2 minutes of grinding lead to asignificant decrease in the size of CSR in both superconduc-tors that is refinement of the microstructure With increas-ing milling duration up to 10min further changes of CSR-size practically do not occur However there is a fundamentaldifference in the effect of mechanical activation on the phasecomposition of Y-123 andNd-123 In the initially single-phaseyttrium superconductor with increasingmilling duration theamount of impurity phase (Y
2BaCuO
5) increases continu-
ously whereas in the neodymium superconductor it is viceversamdasha small amount of impurity phase (Ba
2Cu3O5+x) exist-
ing in the initial sample is not observed in all mechanicallyactivated samples This confirms the findings of the highchemical stability of Nd-123 oxide by comparison with itsyttrium homologue
Another interesting point worthy of discussion is the factthat there is no more than one impurity in all the testedsamples (Y-123 and Nd-123) that according to the massbalance should affect the cation stoichiometry in the mainphase of the sample
As for Nd-123 samples deviations from the ideal cationstoichiometry after a long (150 hours) high-temperatureannealing is just a characteristic feature of them [9] Appear-ance of impurity Ba
2Cu3O5+x phase in an amount of 3
indicates that the IP of Nd-123 (sample N-0) is in fact a solidsolution Nd
103Ba197
Cu3O6+120575
Unspent Ba (in amount ofsim3) seems to form under atmospheric moist air the X-rayamorphous phase of Ba(OH)
2sdot nH2O which is easily trans-
formed into BaCO3from the surface due to the presence of
CO2in the air
Y-123 MP which contains a rich by yttrium impurityY2BaCuO
5 to comply with the ion balance should include
the phase not containing this element Since these phaseswere not detected by XRD we have assumed that as a resultof mechanical activation they became X-ray amorphous Infact they were later identified by us with the use of XPS seelater
322 XPS Study of YBa2Cu3O6+120575
Oxide Figure 2 shows thesurvey spectra of the powders YBa
2Cu3O6+120575
under study
4 Journal of Spectroscopy
Cu 2p
Nd2BaCuO5
Y2BaCuO5
930 940 950 960Binding energy (eV)
(a)
Nd2BaCuO5
Y2BaCuO5
280 282 284 286 288 290Binding energy (eV)
C 1s
(b)
Nd2BaCuO5
BaCO3
Y2BaCuO5
BaO
776 780 784 788 792 796 800 804Binding energy (eV)
Ba 3d
(c)
BaCO3
Y2BaCuO5
524 526 528 530 532 534 536 538Binding energy (eV)
Y2O3
Nd2BaCuO5
Nd2O3
O 1s
(d)
Nd2O3
Nd2BaCuO5
116112 120 124 128 132Binding energy (eV)
Nd 4d
(e)
Y 3d
Y2BaCuO5
Y2O3
148 150 152 154 156 158 160 162 164Binding energy (eV)
(f)
Figure 1 XPS spectra of Y2BaCuO
5and Nd
2BaCuO
5oxides The peaks related to the main oxide are marked by bold lines The ordinate
hereinafter is the intensity of the XPS signal in arbitrary units To reduce the figure size the y-axis itself is not shown
Journal of Spectroscopy 5
Table 1 Phase composition lattice parameters and the size of coherent scattering regions (119871) for YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
beforeand after mechanical treatment
Crystallographic parameters Milling duration in AGO-2(1) YBa
2Cu3O6+120575
powders0 s
(sample Y-0)30 s
(sample Y-05)2min
(sample Y-2)10min
(sample Y-10)The main phasemdashorthorhombic SG Pmmm119886 A 38208(3) 38218(3) 38287(10) 38344(10)119887 A 38884(5) 38893(5) 38938(15) 38879(15)119888 A 116809(11) 116793(12) 116739(33) 116663(31)119881 A3 173541(53) 173599(55) 174036(161) 173919(158)Impurity mass mdash sim5 Y
2BaCuO
5sim5 Y
2BaCuO
5sim7 Y
2BaCuO
5
119871 nm 167 57 25 20(2) NdBa
2Cu3O6+120575
powders0 s
(sample N-0)30 s
(sample N-05)2min
(sample N-2)10min
(sample N-10)The main phasemdashorthorhombic SG Pmmm119886 A 38677(1) 38731(3) 38727(12) 38754(12)119887 A 39202(1) 39206(10) 39225(14) 39161(15)119888 A 117612(3) 117622(24) 117630(39) 117661(24)119881 A3 178328(6) 178608(118) 178688(178) 178564(212)Impurity mass sim3 Ba
2Cu3O5+119909
mdash mdash mdash119871 HM 1792 325 229 169
200 400 600 800 1000 1200Binding energy (eV)
Y-10Cu 2p
Y-2Fe 2pY-05
Y 3d Y-0Ba 4d
Ba 3d
C 1s
O 1s
0
Figure 2 XPS survey spectra of the initial and mechanoactivatedYBa2Cu3O6+120575
samples
Recording such spectra conducted in high sensitivity mode(at high 119864PE) allows to consider the main lines of all elementspresented in the surface layer of the material in amountsgreater than 03 at As could be expected there are peaks ofthe electronic levels of yttrium barium copper and oxygencontained in the composition of the oxide under study TheC 1s peak includes a signal from the carbon contamination ofthe random nature
One can see (Figure 2) that on the surface of MP sam-ples there is no iron (mill headsets material) leading tothe appearance of specific magnetic and superconductingproperties of the material Strongly increased barium peak
(represented as a doublet of Ba 3d52minusBa 3d
32) in the spectra
of activated samples testifies the redistribution of elementsbetween the volume and surface occurs which is usuallythe result of chemical degradation of the surface under theinfluence of an environment In this case it could be a well-established [36] reactions as follows
2YBa2Cu3O65+119909+ 3H2O
997888rarr Y2BaCuO
5+ 3Ba(OH)
2+ 5CuO+ uarr119909O
2
(1)
Ba(OH)2+ CO2997888rarr BaCO
3+H2O (2)
Table 2 summarizes the obtained BaCO3of CP grade cal-
cinated at 700∘C Y2BaCuO
5and taken from the literature of
spectrometric data for the reactants involved in the reactions(1) and (2) for reliable identification of the peaks of thesecompounds in the spectra of the samples under study
High-resolution XPS spectra showing the characteristicelectronic levels of the elements constituting Y-123 samplesare presented in Figure 3
The analysis of the Ba 3d spectra has showed that in addi-tion to barium carbonate (line Ba 3d
52at 7799 eV) there is
the phase Y2BaCuO
5(line Ba 3d
52at sim782 eV) on the surface
of the samplesThe line Ba 3d52
at 7780 eVwhich is observedonly in the IP is directly owned by Y-123 (see Table 2)The Y 3d spectra confirm the presence of Y
2BaCuO
5-phase
on the surface of samples the substancersquos line Y 3d52
at1587 eV is clearly visible in these spectra (see Table 2)Besides the Y 3d spectra reveal the surface contains thefollowing oxides Y
2O3[34] (line Y 3d
52at 1569 eV) Y-123
6 Journal of Spectroscopy
Ba 3d
Y-10
Y-2
Y-05
Y-0
776 780 784 788 792 796 800Binding energy (eV)
3d523d32
(a)
Binding energy (eV)
Y 3d
Y-10
Y-2
Y-05
Y-0
150 152 154 156 158 160 162 164 166
(b)
Cu 2p
Y-10 Satellite I Satellite II
Y-2
Y-05
Y-0
930 940 950 960 970Binding energy (eV)
2p32
2p12
(c)
Figure 3 XPS spectra of YBa2Cu3O6+120575
powders Dark shading the main phase signal light shading Y2BaCuO
5signal
Table 2 The positions of the characteristic XPS lines of barium compounds
Electron orbital BaCO3 Ba(OH)2 Y-123 Y2BaCuO
5
Binding energy eV
Ba 3d52
7799 [16 17]7798lowast
7813 plusmn 01[18 19]
7777 plusmn 01[20ndash23] 7819lowast
Ba 4d52 893lowast 875
[22]
Y 3d52
1560 plusmn 02[21 24 25] 1587lowast
Cu 2p32
9335[21 26] 9356lowast
O 1s5314 plusmn 01[16 17]5314lowast
5312 qB[27]
52845 plusmn 005 qB[20ndash23] (5291 5313)lowast
C 1s28925 plusmn 015 qB
[16 17]2894lowast
lowastOur data
(line Y 3d52
at 1560 eV in the spectrum of IP) and the phaseY2(C2O4)3[37] (line Y 3d
52at 1601 eV) The presence of
Y2BaCuO
5compound in samples is also reflected in the
spectra of Cu 2p a high-energy doublet (main peak at9356 eV) corresponds to it At the same time the low-energyCu 2p-doublet parameters are close to those found in [22] forY-123 the main peak at 9335 eV a satellite at sim943 eV as wellas parameters relating to copper oxide Cu (II) [28] 9336 eVand 9425 eV respectively However from the analysis of thespectra of Ba 3d and Y 3d (see earlier) it can be argued that
the Cu 2p signal from the phase of Y-123 may be only in thespectrum of IP samples
Thus in addition to the main phase the surface of IPcontains the final products of the reactions (1) + (2) and Y
2O3
phase probably sourced by the initial precursor incompletelyconsumed during the synthesis of YBa
2Cu3O6+120575
As a resultof MA treatment the surface of the powder is covered with alayer of yttriumoxide and the products of reactions (1) + (2) toa considerable depth of at least 10 nm (judging by the amountof Y2BaCuO
5phase in the samples determined by XRD)
Journal of Spectroscopy 7
323 XPS Study of NdBa2Cu3O6+120575
Oxide Figure 4 demon-strates the survey spectra of Nd-123 powders One can seethat as in the case of Y-123 samples the signal representingthe iron was not observed for any intensive milling durationThe feature of Nd-123 samples is rather low intensity of the Ba3d and Ba 4d peaks for powders activated for 05 and 2min(compare Figure 4 with Figure 2 for Y-123 powder) Bariumpeaks has markedly increased (as well as oxygen O 1s peak)only at 10min of activation
Figure 5 shows the high-resolution spectra of the elec-tronic levels of barium (3d and 4d) neodymium (4d) andcopper (2p) in powders with different activation prehistoryIn the barium spectra the high-intensity peaks at 7799 eV(3d52
) and 893 eV (4d52
) are obviously responsible for thecompound BaCO
3 and the low-intensity peaks at 7780 and
876 eV which are observed only in IP samples (dark shadedin Figure 5) correspond to the main phase by analogy withY-123 samples The analysis of Cu 2p spectra has revealed thepresence of copper ions with the electronic structure similarto that in Y-123 or in CuO oxide
However as seen in Figure 5 the state Cu 2p with highbinding energy (9359 plusmn 03 eV) is also present in all Nd-123samples According to our data (see Table 3) this state is nottypical for simple and ternary compounds of copper DuringMA processing its share in Cu 2p spectra changes in strictaccordancewith the high energy components of the Ba 3d andBa 4d spectra light shaded in Figure 5 (at 7817 eV (Ba 3d
53)
and 919 plusmn 03 eV (Ba 4d53
)) which implies that a doubleoxide of barium-copper was on the surface of the samplesWe tend to identify this oxide as Ba
2Cu3O5+x phase which
was detected by X-ray diffraction analysis of IP samples (seeTable 1) Despite the fact that this phase was not found byXRD in samples N-05 N-1 and N-2 it is visible in the XPSspectra due to the effect of spatial localization
According to Figure 5 the surface of the samples alsocontained the oxide Nd
2O3(line Nd 4d
52at 1211 eV) which
under intense grinding at the initial stages was partly trans-formed into Nd
2(C2O4)3[37] (line Nd 4d
52at sim1225 eV)
Based on the analysis of possible superpositions of the spectraof Ba 3d Ba 4d and Cu 2p the low-energy Nd 4d doublet(line Nd 4d
52at 1157 eV) the intensity of which is almost
independent of the MA duration belongs to a double oxideNdCu
119910O15+y+z of undetermined composition The Nd 4d
doublet of themain compound apparently overlaps with oneof the previously noted signals and so it is shown explicitlyin Figure 5
On the intensity ratios of the peaks in Figure 5 one canconstruct a model of the relative position of the phases Nd-123 BaCO
3 and Ba
2Cu3O5+x in the surface layer of the
material (this method has been used eg in [22] to analyzethe relative position of the layers Y-123 and BaCuO
2) To
realize this we use the dependence of the layer thicknessanalyzed by XPS (usually taken as 3 sdot 120582
119898) on the kinetic
energy of the electrons [38] referring to the electrons givingthe corresponding lines in the spectra of Ba 3d and Ba 4d asfollows
120582119898= 2170119864
minus2
119896+ 072(119886119864
119896)12 (3)
Ba 3d
N-10Cu 2pN-2Fe 2p
O 1sN-05
N-0Cu LVVCu 3s C 1sNd 4d
Ba 4d200 400 600 800 1000
Binding energy (eV)0
Figure 4 XPS survey spectra of the initial and mechanoactivatedNdBa
2Cu3O6+120575
samples
where 120582119898is the electron mean free path expressed in mono-
layers 119886 is monolayer thickness in nm 119864119896is kinetic energy
in eV (119864119896= ℎ] minus 119864BE minus 120593) ℎ] = 12536 eV is the energy of
the exciting radiation used inXPS analysis119864BE is the bindingenergy of the electronic level under analysis and120593 is theworkfunction of the spectrometer (346 eV)
According to this relationship the thickness of the layerunder analysis increases monotonically with increasing 119864
119896
in the range 119864119896gt 40 eV As can be seen from Figure 6
increase in the thickness of the layer under analysis canaffect the following volume ratios detectable by XPS phaseIphase III and phase IIphase III and has no influence onthe volume relation phase Iphase II The phase fractionto a first approximation is proportional to the area undercorresponding XPS peak Therefore based on the ratio ofareas of the different lines in the spectra in Figure 5 one canconclude that both barium-containing products of chemicaldecomposition of Nd-123 are located atop of the main oxidethat is correspond to phases I and II in Figure 6 The thick-ness of the degraded layer in N-10 sample is sim10 nm (as theoriginal phase is barely visible through it) and in IP (N-0)sample it is estimated to be 5-6 nm
It should be noted however that such a small thicknessof Ba2Cu3O5+x layer in IP has not prevented this phase to be
recognized by XRD analysis (see Table 1) One can thereforeconclude that IP particles contain in addition a considerableamount of Ba
2Cu3O5+x in the form of individual inclusions
in bulk (as a result of this oxide synthesis features seeSection 1) DuringMA processing material particles crackedand inclusions went outside resulting in the fraction ofBa2Cu3O5+x phase on the surface increased up to a point
(up to 1min inclusive) The subsequent decrease in thisphase (see Figure 5) is apparently due to the fact that anotherprocess also developed on the surface during grindingspending of Ba
2Cu3O5+x involving the original solid solution
Nd1+xBa2minusxCu3O6+120575 to formation of cation-stoichiometric
NdBa2Cu3O6+120575
To prove the occurrence of such interaction
8 Journal of Spectroscopy
Ba 3d
N-10
N-2
N-1
N-05
N-0
770 775 780 785 790 795 800 805Binding energy (eV)
(a)
N-10
N-1
Binding energy (eV)
Ba 4d
Ba 4d
N-2
N-05
N-0
68 72 80 84 88 92 96
Cu 3p X-ra
ysa
telli
tes
76
(b)
N-10
N-2
N-1
N-05
N-0
930 940 950 960 970Binding energy (eV)
Satellite I Satellite II
Cu 2p2p32
2p12
(c)
N-10
N-2
N-1
N-05
N-0
110 115 120 125 130 135Binding energy (eV)
Nd 4d
(d)
Figure 5 XPS spectra of NdBa2Cu3O6+120575
powders
119864119896 (Ba 3d) 119864119896 (Ba 4d)
Phase I Phase II
Phase III
Phase I Phase II
Phase III
31205823120582
XPS
study
area
XPS
study
area
lt
Figure 6 Analysis of the mutual arrangement phases in the surface layer of the material and their volume relations from XPS data
Journal of Spectroscopy 9
Table 3 Characteristic spectral parameters of different copper compounds
Electron orbital CuO CuCO3 Cu(OH)2 Cu2CO3(OH)2 Nd2BaCuO5
Binding energy eVBa 3d
527790lowast
Nd 4d52
1182lowast
Cu 2p32
9337 plusmn 1[28ndash30]
9348[28]
93474 plusmn 006[29 31]
9347[32] 9335lowast
O 1s 52974 plusmn 006[30 31]
53124[31] 5286lowast
lowastOur data
later we present the data of magnetic measurements whichindicate that MA treatment results in significant increase inthe temperature of the superconducting transition in separateregions of the material
324 Thermal Analysis of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
Samples of R-123 have been studied by thermogravimetrycoupled withmass-spectrometry to analyze the gases evolvedduring experiments Results of the study are summarizedin Figure 7 It is seen that reversible change in mass of IP-samples occurs in the range of 430ndash900∘C that must be dueto oxygen exchange between nonstoichiometric R-123 oxidesand the gas phase taking place at these temperatures [1] MPsamples start losing mass sharply around 70∘C when heatedMass spectrometry analysis of thermal desorption productsindicates the presence of large amount of water and a smallamount of carbon dioxide contained in the samples in theform of BaCO
3(the temperature range in which the CO
2
was released and the value of 119901CO2used for thermal analysis
of the atmosphere was consistent with conditions of bariumcarbonate decomposition)
325 Study of Magnetic Properties of YBa2Cu3O6+120575
andNdBa
2Cu3O6+120575
Temperature dependences of ZFC magne-tization of the samples Y-0 Y-05 Y-2 and Y-10 are shownin Figure 8 A sharp downturn in magnetization at sim90Kobserved in the samples Y-0 Y-05 and Y-2 clearly showsthe presence of the superconducting phase Superconductingtransition temperatures of the samples Y-0 Y-05 and Y-2have been determined by taking the derivative of the mag-netization against the temperature (119889119898119889119879) Thus definedtemperatures 119879
119888are equal to 91 K for the samples Y-0 and
Y-05 and 88K for the sample Y-2 A wide transition widtharound 119879
119888= 90K indicates that both the initial and MP
samples contain inhomogeneous superconductor phaseswithdifferent 119879
119888 The following facts indicate the presence of
paramagnetic contribution in the magnetization behavior ofMP samples and its growth with increasing milling durationa significant increase in magnetization 119898 of the samples Y-05 and Y-2 compared with the initial sample Y-0 at thetemperatures 119879 gt 119879
119888 weak temperature dependence 119898(119879)
in the temperature range 100ndash300 K for MP samples asignificant increase in themagnetization of Y-10 sample at lowtemperatures
100
99
98
97
96
95
94
93
92
100
99
98
97
96
95
94
93
92
0 200 400 600 800 1000
0 200 400 600 800 1000
14
12
10
8
6
4
3
2
Temperature (∘C)
Ion
curr
ent (
A)
Ion
curr
ent (
A)
Sam
ple w
eigh
t (
)
H2O
CO2
H2O (times1010) CO2 (times1011)
3
2
1
3998400
1998400
2998400
Figure 7 Thermal analysis results for samples Y-0 (1) N-0 (11015840) Y-2 (2) N-2 (21015840) and Y-10 (3) N-10 (31015840) Mass spectrometry data arerelated to the samples Y-10 (solid curves) and N-10 (dashed lines)
For comparison Figure 9 shows the temperature depen-dence of the FC magnetization in a magnetic field 119867 =500Oe for two new samples of Y-123 (120575 asymp 07) The firstsample has been freshly prepared and the other one has beensubjected to treatment at 297 plusmn 1K for 120 h at absolutehumidity of 23 120581Pa The sample with low oxygen content(and as a consequence with low 119879
119888) has been chosen due
to its relatively easy moisture saturation in these conditionswithout the use of MA (moisture saturation was controlledby the increase in weight which eventually was sim4wt)One can see that the sample saturated with water has apositive magnetic moment above the temperature 119879
119888and
shows an increase inmagnetic moment on cooling below this
10 Journal of Spectroscopy
N-0
N-1
N-10N-2
Y-2
Y-05
N-05
Y-0
Y-10
005 0005
0004
0003
0002
0001
0
0
minus005
minus01
minus015
minus02
minus025
minus03
minus01
minus02
minus03
003
002
001
0
0
0minus001
20 40 60 80 100 120 140119879 (K)
119898(e
mu
g)119898
(em
ug)
119898(e
mu
g)119898
(em
ug)
Figure 8 ZFC magnetizations as a function of temperature at119867 = 50Oe for the initial and mechanically activated samplesYBa2Cu3O6+120575
(top) NdBa2Cu3O6+120575
(bottom)
temperature similarly to Y-10 sample Onset temperature ofthe magnetic anomaly in the hydrated sample is the sameas that in the freshly prepared sample This experimentdemonstrates that the presence of water in MP sampleshas a significant effect on the temperature dependences ofthe magnetization observed in samples of Y-123 series (seeFigure 8)
Temperature dependences of ZFC magnetization of MPsamples in Nd-123 series are shown in Figure 8 The super-conducting transition temperatures of the samples N-0 N-05 and N-1 are independent of milling duration and equal to119879119888sim 57KMechanical treatment leads to a substantial change
in the magnetization of MP samples throughout the inves-tigated temperature range MP samples exhibit near-room-temperature hysteretic behavior that is ZFC magnetizationis more diamagnetic than FCmagnetization It may be due tomagnetic particles of mechanoactivatedNd-123 samples or tothe presence of impurity phases whose low content or highlydisordered crystal structures do not allow to observe thesephases by X-ray diffraction measurements We also cannotexclude the formation of CuO phase (119879
119873sim 220K) at the
surface of large NdBa2Cu3O6+120575
particles proceeding undermechanical activationAt the same time a significant increasein the paramagnetic contribution to the magnetization withincreasing milling duration is observed
004
002
0
minus002
minus004
minus006
minus0080 20 40 60 80 100 120 140
0 20 40 60 80 100 120 140
119898(e
mu)
119898(e
mu)
119879 (K)
119879 (K)
004
0038
0036
0034
Figure 9 FCmagnetizations as a function of temperature of freshlyprepared YBa
2Cu3O6+120575
sample (empty points) and of hydrated sam-ple (black points) at119867 = 500Oe Inset the temperature dependenceof magnetization of hydrated sample at119867 = 10 kOe
A wide transition width around 119879119888= 57K (|Δ119879
119888sim 20K|)
in MP samples of Nd-123 series cannot be explained only bythe presence of water in the structure The observed changesindicate that during MA treatment diffusion processes asso-ciated with the ordering of the cations Nd3+ and Ba2+ appa-rently occur according to [8ndash10] that has a significant effecton 119879119888
4 Discussion of Results
41 Interaction of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
withCO2 From comparison of Figures 4 and 5 it is clear that with
increasing duration of MA processing (120591119892) the amount of
barium-containing impurities on the surface of Nd-123 sam-ples continuously increases up to 120591
119892= 10min in contrast
to the situation for the oxide Y-123 for which initially (up120591119892= 05min) sudden change and subsequent (after 120591
119892=
05min) almost stagnation in the accumulation of chemicaldegradation products were observed (see Figures 2 and 3 anddata on the impurities in YBa
2Cu3O6+120575
sample) One can seefrom Figure 7 that the degree of water saturation (120578) of bothoxides (this parameter can be traced by sharp descendingbranch of sample mass change in the temperature range of30ndash450∘C) obeys similar relationships with increasing 120591
119892 its
growth with increasing MA duration close to proportionalfor Nd-123 (120578 sim 120591
119892) and tendency of 120578 to decrease for Y-123
(120578 = 155 sdot 120591119892
03) which is close to the root dependence char-
acteristic of reagent diffusion through the reaction productslayer
Taking into account the data in [1] stating the chemicaldegradation of Y-123 is carried out on the interface betweenY-123 and gas phase and one can explain sharply fallingrates of change in concentration of its products as well as ofH2O dissolved in the oxide the diffusion path length of H
2O
and CO2reactants to the location of the reactions (1) and
(2) increases with time 120591119892 However the uniformity of the
absorption of H2O and CO
2gases by MP of Nd-123 testifies
Journal of Spectroscopy 11
that the thickness of the degraded layer on the surface variesslightly Apparently it does not exceed 10 nm as indicated bya weak but clear signal of the main phase which appeared inthe Ba 4d-spectrum of N-10 sample (see Figure 5) Howeverit should be noted that Nd-123 MP sample actively entersinto chemical reactionwith atmospheric CO
2 the gas escapes
from the samples quite intensively when heated in the rangeof 800ndash900∘C (see Figure 7) Therefore the question oflocalization place of products of interaction between Nd-123and atmospheric components arises
Homogeneous nucleation and growth of interaction pro-ducts in the volume of Nd
1+xBa2minusxCu3O6+120575 parent phasemaybe the answer This assumption is based on the fact that theproducts of thermal desorption of N-10 sample (see Figure 7)contain weakly bound form of CO
2escaping in a wide tem-
perature range of 200ndash550∘C Obviously it is a form of gasdissolved in the structure Since the carbonization energy ofBa2+ ions is quite high homogeneous nucleation of carbonatephase at a certain concentration (equivactivity) of CO
2in the
structure facilitated by the participation of structural defects(whose concentration should be significant in MP samples)seems quite possible
42 Interaction of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
withWater In the Introductionwe have put links toworks statingthat the crucial feature for the practical application of thesuperconductor Nd-123 is its high resistance to chemicaldegradation under moisture Additional information thatexpands understanding of this feature has been received inour study Thus it is shown (see Figure 7) that a high con-centration of water accumulates in MP samples of Nd-123 indissolved form but the hydrolysis reaction development isquite limited as evidenced by the relatively low temperatureof H2O release from this oxide Moreover the results of
XRD and XPS analyzes have not detected even traces of theternary compound Nd
2BaCuO
5in these samples while it is
the compounds R2BaCuO
5due their characteristic colours
that are indicators of the hydrolysis reaction for the wholefamily of compounds R-123 [1 39 40] Thus if the hydrolysisreaction develops (there is a small peak on H
2O desorption
curve for sample N-10 at sim455∘C that can be attributed tothe chemically bound water) then it proceeds through non-traditional mechanism and with low rate
According to [41] the hydration mechanism for thehomologous series of R-123 compounds is in four stages Atthe initial stage water molecules penetrate into the bulk ofthe crystallites through the structural channels [(12) b 0]located in interspaces between CuO-chains typical for thistype of superconductors At the next stage protons whichare located in the oxygen positions of CuO-chains can besplit up of watermoleculesThis proton transfer is consideredto cause an internal (within the [CundashO]+-system) chargetransfer resulting in formation of molecular oxygen leavingthe structure At high concentrations of hydroxide ionsaccumulated in the structure the chemical decompositionof the initial oxide occurs Based on the previous schemeone can understand the reasons for high resistivity of N-123superconductor to chemical interaction with water
The authors of [42] discussed the high corrosion resis-tance of Nd-123 films in the water compared to the filmstructures of Y-123 and Eu-123 which was attributed to thepartial oxygen disorder in the planes of CuO-chains Sucha disorder should occur in Nd-123 due to the presence ofsome amount of Nd3+ ions in the sites nearby to CuO-planesof divalent barium According to the authors that shouldlead to overlapping structural channels for H
2O diffusion
and hence blocking the hydration process However ourdata on the thermal analysis (see Figure 7) illustrate thatthe saturation of Nd-123 structure with water during MAtreatment proceeds almost as fast as in Y-123 (in the rangeof 2ndash10 minutes even faster) Therefore the sought causeof the chemical stability of Nd-123 MP cannot be related toproblems of H
2O diffusion
The stage of removing oxygen from the structure is con-sidered [41 42] to be extremely important for the hydrationprocess of R-123 Thus the chemical degradation of Y-123oxide immersed in the water is completely stopped underpotential of 08 V relative to the standard electrode-saturatedsodium calomel [41] It is expected that the substitutionNd3+ rarr Ba2+ inNd-123 in addition to oxygen disordering inthe base structural plane should also lead to the strengtheningof its bondwith the lattice (due to electrostatic effect of highlycharged Nd3+ ion) [42] According to the authors [42] thisshould inhibit the reduction stage of hydration However it isimportant to consider the fact that the structure ofMP of Nd-123 contains a large amount of weakly bound CO
2 located
near Ba ions (since there is a tendency to the formation ofBaCO
3) therefore localized in the channels of the base plane
[(12) b 0] where also there is water In our opinion just theseCO2particles block channels of oxygen desorption which is
the main reason for the high stability of Nd-123 in relation tothe hydrolysis reaction
5 Conclusion
Thus as a result of mechanical activation treatment thesurface of YBa
2Cu3O6+120575
is covered by products of hydrolysisand carbonization to a considerable depth The chemicaldegradation process proceeds the normal waymdashthrough theformation of Y
2BaCuO
5phase
Chemical degradation of mechanoactivatedNdBa
2Cu3O6+120575
powders under the impact of CO2
isnot directly connected to hydrolysis process as occurs inYBa2Cu3O6+120575
(see reactions (1) and (2)) Carbonizationproceeds homogeneously through the stage of carbondioxide dissolution in the lattice of NdBa
2Cu3O6+120575
In itsturn the presence of CO
2molecules in the structure of
mechanoactivated NdBa2Cu3O6+120575
powders leads to a radicalchange in the mechanism of interaction between the super-conductor and water This mechanism eliminates the normalfor a homologous series of RBa
2Cu3O6+120575
the hydrolysisreaction with the formation of characteristic ldquocolorrdquoR2BaCuO
5phases The rate of chemical decomposition of
mechanically activated NdBa2Cu3O6+120575
by the new mecha-nism (not yet studied) is quite low
12 Journal of Spectroscopy
Mechanical treatment affects the temperature depen-dence of the magnetization of RBa
2Cu3O6+120575
compoundsThere is a significant increase in the paramagnetic and ferro-magnetic contributions to the magnetization with increasingmilling duration The latter leads to near-room-temperaturehysteretic behavior of NdBa
2Cu3O6+120575
samples between ZFCandFC regimes Itmay be due tomagnetic particles ofmecha-noactivated NdBa
2Cu3O6+120575
samples or to the presence ofimpurity phases whose low content or highly disorderedcrystal structures do not allow to observe these phases byX-ray diffraction measurements The mechanical treatmentdoes not have substantial influence on the transition tem-peratures of superconducting phases 119879
119888in the RBa
2Cu3O6+120575
compounds but a wide transition width around 119879119888indicates
that mechanically activated samples contain inhomogeneoussuperconductor phases with different 119879
119888 The broadening
of the superconducting transition in mechanically activatedNdBa
2Cu3O6+120575
samples may be due to redistribution ofcations between Nd- and Ba-sublattice
Finally we note that the high temperature superconduc-tor RBa
2Cu3O6+120575
subjected to mechanical activation cer-tainly has no significant advantages over conventional non-mechanoactivated material but it is obvious that physical-chemical studies of such powders reveal results interestingfrom the point of view of fundamental science
Acknowledgment
This work was supported by Russian Foundation for BasicResearch (Grant no 11-03-00317-a)
References
[1] I E Graboi A R Kaulrsquo and G Yu Metlin ldquoAdvances in scienceand technologyrdquo in Solid State Chemistry pp 3ndash142 VINITIANSSSR Moscow Russia 1989
[2] S Anders M G Blamire F-Im Buchholz et al ldquoEuropeanroadmap on superconductive electronicsmdashstatus and perspec-tivesrdquo Physica C vol 470 no 23-24 pp 2079ndash2126 2010
[3] B Ruck B Oelze R Dittmann et al ldquoMeasurement of thedynamic error rate of a high temperature superconductor rapidsingle flux quantum comparatorrdquo Applied Physics Letters vol72 no 18 pp 2328ndash2330 1998
[4] M W Rupich X Li C Thieme et al ldquoAdvances in secondgeneration high temperature superconducting wire manufac-turing and RampD at American superconductor corporationrdquoSuperconductor Science and Technology vol 23 no 1 Article ID014015 2010
[5] A Rakitin M Kobayashi and A P Litvinchuk ldquoSuperi-onic behavior of high-temperature superconductorsrdquo PhysicalReview B vol 55 no 1 pp 89ndash92 1997
[6] T Kagiyama J Shimoyama K D Otzschi et al ldquoEffect of cationcomposition and oxygen nonstoichiometry on 119869
119888-119861 properties
of Nd123rdquo Physica C vol 341ndash348 no 2 pp 1445ndash1446 2000
[7] M Badaye J G Wen K Fukushima et al ldquoSuperior propertiesof NdBa
2Cu3O119910over YBa
2Cu3O119909thin filmsrdquo Superconductor
Science and Technology vol 10 no 11 pp 825ndash830 1997
[8] C Cantoni D P Norton D M Kroeger et al ldquoPhase stabilityfor the in situ growth of Nd
1+119909Ba2minus119909
Cu3O119910films using pulsed-
laser depositionrdquo Applied Physics Letters vol 74 no 1 pp 96ndash98 1999
[9] E A Goodilin N N Oleynikov E V Antipov et al ldquoPhasestability for the in situ growth of Nd
1+119909Ba2minus119909
Cu3O119910films using
pulsed-laser depositionrdquo Physica C vol 272 6578 pages 1996[10] E Guilmeau F Giovannelli I Monot-Laffez S Marinel J
Provost and G Desgardin ldquoTop seeding melt texture growthof NdBaCuO pellets in airrdquoThe European Physical Journal vol13 no 3 pp 157ndash160 2001
[11] A I Ancharov T F Grigorrsquoeva T Yu Kiseleva A A Novakovaet al inMechanocomposites-Precursorsfor the Creation of Mate-rials with New Properties O I Lomovskii Ed p 424 Izd-voSO RAN Novosibirsk Russia 2010
[12] A Hamrita F Ben Azzouz A Madani and M Ben SalemldquoMagnetoresistivity and microstructure of YBa
2Cu3O119910pre-
pared using planetary ball millingrdquo Physica C vol 472 no 1pp 34ndash38 2012
[13] R P Vasquez ldquoIntrinsic photoemission signals surface prepa-ration and surface stability of high temperature superconduc-torsrdquo Journal of Electron Spectroscopy and Related Phenomenavol 66 no 3-4 pp 209ndash222 1994
[14] S S Gorelik L N Rastorguev and A Yu Skakov in Rentgeno-graphIcheskII I ElektronographIcheskII AnalIz p 368 Izd-voMetallurgia Moscow Russia 1970
[15] M V Reshetniak and O V Sobol Program for diffractionanalysis ldquoNew Profilerdquo(Last update 10 02 2007) Version 3 4400 (Freeware) WIN9xMENT2KXP Copyright (c) 1992-2007 ReMax SoftWare 2000
[16] M Wegmann L Watson and A Hendry ldquoXPS analysis of sub-micrometer barium titanate powderrdquo Journal of the AmericanCeramic Society vol 87 no 3 pp 371ndash377 2004
[17] A B Christie J Lee I Sutherland and J M Walls ldquoAn XPSstudy of ion-induced compositional changes with group II andgroup IV compoundsrdquo Applications of Surface Science vol 15no 1ndash4 pp 224ndash237 1983
[18] U A Joshi S Yoon S Balk and J S Lee ldquoSurfactant-freehydrothermal synthesis of highly tetragonal barium titanatenanowires a structural investigationrdquo Journal of Physical Chem-istry B vol 110 no 25 pp 12249ndash12256 2006
[19] R Caracciolo ldquoChemical characterization techniques for thinfilmsrdquo in Ceramic Films and Coatings J B Wachtman and R AHaber Eds p 376 New Jersey NJ USA 1992
[20] I N Shabanova Y A Naimushina and N S Terebova ldquoCom-position and temperature dependence of a Y-Ba-Cu-O HTSCelectronic structurerdquo Superconductor Science and Technologyvol 15 no 7 pp 1030ndash1033 2002
[21] J Beyer T Schurig S Menkel Z Quan and H Koch ldquoXPSinvestigation of the surface composition of sputtered YBCOthin filmsrdquo Physica C vol 246 no 1-2 pp 156ndash162 1995
[22] C C Chang M S Hegde X D Wu et al ldquoSurface layers onsuperconducting Y-Ba-Cu-O films studied with x-ray photo-electron spectroscopyrdquo Applied Physics Letters vol 55 no 16pp 1680ndash1682 1989
[23] X D Wu A Inam M S Hegde et al ldquoCrystalline perfectionof as-deposited high-Tc superconducting thin-film surfacesion channeling and x-ray photoelectron spectroscopy studyrdquoPhysical Review B vol 38 no 13 pp 9307ndash9310 1988
[24] P Rajasekar P Chakraborty S K Bandyopadhyay P Barat andP Sen ldquoX-ray photoelectron spectroscopy study of oxygen and
Journal of Spectroscopy 13
argon annealed YBa22Cu3O7minus120575
rdquo Modern Physics Letters B vol12 no 6-7 pp 239ndash245 1998
[25] J Halbritter P Walk H J Mathes B Haeuser and H RogallaldquoARXPS-studies of c-axis textured YBa
2Cu3O119909-filmsrdquo Physica
C vol 153ndash155 no 1 pp 127ndash128 1988[26] T J Sarapatka and P Mikusık ldquoXPS study of PbYBaCuO thin-
film tunnel contactrdquo Applied Surface Science vol 68 no 1 pp35ndash40 1993
[27] J A T Verhoeven and H Van Doveren ldquoAn XPS investigationof the interaction of CH
4 C2H2 C2H4and C
2H6with a barium
surfacerdquo Surface Science vol 123 no 2-3 pp 369ndash383 1982[28] C D Wagner W M Riggs L E Davis J F Moulder and G
E Mullenberg Handbook of X-Ray Photoelectron SpectroscopyPerkin-Elmer Corp Eden Prairie Minn USA 1979
[29] M C Biesinger L W M Lau A R Gerson and R S C SmartldquoResolving surface chemical states in XPS analysis of first rowtransition metals oxides and hydroxides Sc Ti V Cu and ZnrdquoApplied Surface Science vol 257 no 3 pp 887ndash898 2010
[30] X Y Fan Z GWu P X Yan et al ldquoFabrication of well-orderedCuO nanowire arrays by direct oxidation of sputter-depositedCu3N filmrdquo Materials Letters vol 62 no 12-13 pp 1805ndash1808
2008[31] S J Kerber J J Bruckner K Wozniak S Seal S Hardcastle
and T L Barr ldquoNature of hydrogen in x-ray photoelectronspectroscopy general patterns from hydroxides to hydrogenbondingrdquo Journal of Vacuum Science and Technology A vol 14no 3 pp 1314ndash1320 1996
[32] G Moretti G Fierro M Lo Jacono and P Porta ldquoCharac-terization of CuO-ZnO catalysts by X-ray photoelectron spec-troscopy precursors calcined and reduced samplesrdquo Surfaceand Interface Analysis vol 14 no 6-7 pp 325ndash336 1989
[33] H Van Doveren and J A T H Verhoeven ldquoXPS spectra of CaSr Ba and their oxidesrdquo Journal of Electron Spectroscopy andRelated Phenomena vol 21 no 3 pp 265ndash273 1980
[34] B V Crist Handbooks of Monochromatic XPS Spectra Volume2mdashCommercially pure binary oxides XPS International LLCLeona Tex USA 2005
[35] D D Sarma and C N R Rao ldquoXPES studies of oxides ofsecond- and third-row transition metals including rare earthsrdquoJournal of Electron Spectroscopy and Related Phenomena vol 20no 1 pp 25ndash45 1980
[36] V I Nefedov and A N Sokolov ldquoDegradatzia visokotemper-aturnich sverchprovodnikov pri khimicheskich vozdeistviachrdquoZhurnal Neorganicheskoi Khimii vol 34 no 11 pp 2723ndash27391989
[37] Y Uwamino T Ishizuka and H Yamatera ldquoX-ray photoelec-tron spectroscopy of rare-earth compoundsrdquo Journal of ElectronSpectroscopy and Related Phenomena vol 34 no 1 pp 67ndash781984
[38] M P Seah and W A Dench ldquoQuantitative electron spec-troscopy of surfaces a standard data base for electron inelasticmean free paths in solidsrdquo Surface and Interface Analysis vol 1no 1 pp 2ndash11 1979
[39] C H Lin H C I Kao and C M Wang ldquoKinetics andstability of R(Ba
15Sr05)Cu3O119910(R = La Nd Sm Eu Gd Dy Ho)
superconductors inwaterrdquoMaterials Chemistry and Physics vol82 no 2 pp 435ndash439 2003
[40] A G Knizhnik R A Stukan and G O Eremenko ldquoStudy theinteraction between europium HTSC of 123 type and waterrdquoSverkhprovodimost vol 4 no 1 pp 177ndash182 1991 (Russian)
[41] J Zhou R K Lo J T McDevitt et al ldquoDevelopment of areliable materials base for superconducting electronicsrdquo Journalof Materials Research vol 12 no 11 pp 2958ndash2975 1997
[42] S B Schougaard M F Ali and J T McDevitt ldquoEvidence forhigh stability against water corrosion of NdBa
2Cu3O7plusmn120575
relativeto YBa
2Cu3OO7minus120575
and EuBa2Cu3OO7minus120575
rdquo Applied Physics Let-ters vol 84 no 7 pp 1144ndash1146 2004
Submit your manuscripts athttpwwwhindawicom
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Inorganic ChemistryInternational Journal of
Hindawi Publishing Corporation httpwwwhindawicom Volume 2014
International Journal ofPhotoenergy
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Carbohydrate Chemistry
International Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Advances in
Physical Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom
Analytical Methods in Chemistry
Journal of
Volume 2014
Bioinorganic Chemistry and ApplicationsHindawi Publishing Corporationhttpwwwhindawicom Volume 2014
SpectroscopyInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
The Scientific World JournalHindawi Publishing Corporation httpwwwhindawicom Volume 2014
Medicinal ChemistryInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Chromatography Research International
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Applied ChemistryJournal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Theoretical ChemistryJournal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Spectroscopy
Analytical ChemistryInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Quantum Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Organic Chemistry International
ElectrochemistryInternational Journal of
Hindawi Publishing Corporation httpwwwhindawicom Volume 2014
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
CatalystsJournal of
4 Journal of Spectroscopy
Cu 2p
Nd2BaCuO5
Y2BaCuO5
930 940 950 960Binding energy (eV)
(a)
Nd2BaCuO5
Y2BaCuO5
280 282 284 286 288 290Binding energy (eV)
C 1s
(b)
Nd2BaCuO5
BaCO3
Y2BaCuO5
BaO
776 780 784 788 792 796 800 804Binding energy (eV)
Ba 3d
(c)
BaCO3
Y2BaCuO5
524 526 528 530 532 534 536 538Binding energy (eV)
Y2O3
Nd2BaCuO5
Nd2O3
O 1s
(d)
Nd2O3
Nd2BaCuO5
116112 120 124 128 132Binding energy (eV)
Nd 4d
(e)
Y 3d
Y2BaCuO5
Y2O3
148 150 152 154 156 158 160 162 164Binding energy (eV)
(f)
Figure 1 XPS spectra of Y2BaCuO
5and Nd
2BaCuO
5oxides The peaks related to the main oxide are marked by bold lines The ordinate
hereinafter is the intensity of the XPS signal in arbitrary units To reduce the figure size the y-axis itself is not shown
Journal of Spectroscopy 5
Table 1 Phase composition lattice parameters and the size of coherent scattering regions (119871) for YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
beforeand after mechanical treatment
Crystallographic parameters Milling duration in AGO-2(1) YBa
2Cu3O6+120575
powders0 s
(sample Y-0)30 s
(sample Y-05)2min
(sample Y-2)10min
(sample Y-10)The main phasemdashorthorhombic SG Pmmm119886 A 38208(3) 38218(3) 38287(10) 38344(10)119887 A 38884(5) 38893(5) 38938(15) 38879(15)119888 A 116809(11) 116793(12) 116739(33) 116663(31)119881 A3 173541(53) 173599(55) 174036(161) 173919(158)Impurity mass mdash sim5 Y
2BaCuO
5sim5 Y
2BaCuO
5sim7 Y
2BaCuO
5
119871 nm 167 57 25 20(2) NdBa
2Cu3O6+120575
powders0 s
(sample N-0)30 s
(sample N-05)2min
(sample N-2)10min
(sample N-10)The main phasemdashorthorhombic SG Pmmm119886 A 38677(1) 38731(3) 38727(12) 38754(12)119887 A 39202(1) 39206(10) 39225(14) 39161(15)119888 A 117612(3) 117622(24) 117630(39) 117661(24)119881 A3 178328(6) 178608(118) 178688(178) 178564(212)Impurity mass sim3 Ba
2Cu3O5+119909
mdash mdash mdash119871 HM 1792 325 229 169
200 400 600 800 1000 1200Binding energy (eV)
Y-10Cu 2p
Y-2Fe 2pY-05
Y 3d Y-0Ba 4d
Ba 3d
C 1s
O 1s
0
Figure 2 XPS survey spectra of the initial and mechanoactivatedYBa2Cu3O6+120575
samples
Recording such spectra conducted in high sensitivity mode(at high 119864PE) allows to consider the main lines of all elementspresented in the surface layer of the material in amountsgreater than 03 at As could be expected there are peaks ofthe electronic levels of yttrium barium copper and oxygencontained in the composition of the oxide under study TheC 1s peak includes a signal from the carbon contamination ofthe random nature
One can see (Figure 2) that on the surface of MP sam-ples there is no iron (mill headsets material) leading tothe appearance of specific magnetic and superconductingproperties of the material Strongly increased barium peak
(represented as a doublet of Ba 3d52minusBa 3d
32) in the spectra
of activated samples testifies the redistribution of elementsbetween the volume and surface occurs which is usuallythe result of chemical degradation of the surface under theinfluence of an environment In this case it could be a well-established [36] reactions as follows
2YBa2Cu3O65+119909+ 3H2O
997888rarr Y2BaCuO
5+ 3Ba(OH)
2+ 5CuO+ uarr119909O
2
(1)
Ba(OH)2+ CO2997888rarr BaCO
3+H2O (2)
Table 2 summarizes the obtained BaCO3of CP grade cal-
cinated at 700∘C Y2BaCuO
5and taken from the literature of
spectrometric data for the reactants involved in the reactions(1) and (2) for reliable identification of the peaks of thesecompounds in the spectra of the samples under study
High-resolution XPS spectra showing the characteristicelectronic levels of the elements constituting Y-123 samplesare presented in Figure 3
The analysis of the Ba 3d spectra has showed that in addi-tion to barium carbonate (line Ba 3d
52at 7799 eV) there is
the phase Y2BaCuO
5(line Ba 3d
52at sim782 eV) on the surface
of the samplesThe line Ba 3d52
at 7780 eVwhich is observedonly in the IP is directly owned by Y-123 (see Table 2)The Y 3d spectra confirm the presence of Y
2BaCuO
5-phase
on the surface of samples the substancersquos line Y 3d52
at1587 eV is clearly visible in these spectra (see Table 2)Besides the Y 3d spectra reveal the surface contains thefollowing oxides Y
2O3[34] (line Y 3d
52at 1569 eV) Y-123
6 Journal of Spectroscopy
Ba 3d
Y-10
Y-2
Y-05
Y-0
776 780 784 788 792 796 800Binding energy (eV)
3d523d32
(a)
Binding energy (eV)
Y 3d
Y-10
Y-2
Y-05
Y-0
150 152 154 156 158 160 162 164 166
(b)
Cu 2p
Y-10 Satellite I Satellite II
Y-2
Y-05
Y-0
930 940 950 960 970Binding energy (eV)
2p32
2p12
(c)
Figure 3 XPS spectra of YBa2Cu3O6+120575
powders Dark shading the main phase signal light shading Y2BaCuO
5signal
Table 2 The positions of the characteristic XPS lines of barium compounds
Electron orbital BaCO3 Ba(OH)2 Y-123 Y2BaCuO
5
Binding energy eV
Ba 3d52
7799 [16 17]7798lowast
7813 plusmn 01[18 19]
7777 plusmn 01[20ndash23] 7819lowast
Ba 4d52 893lowast 875
[22]
Y 3d52
1560 plusmn 02[21 24 25] 1587lowast
Cu 2p32
9335[21 26] 9356lowast
O 1s5314 plusmn 01[16 17]5314lowast
5312 qB[27]
52845 plusmn 005 qB[20ndash23] (5291 5313)lowast
C 1s28925 plusmn 015 qB
[16 17]2894lowast
lowastOur data
(line Y 3d52
at 1560 eV in the spectrum of IP) and the phaseY2(C2O4)3[37] (line Y 3d
52at 1601 eV) The presence of
Y2BaCuO
5compound in samples is also reflected in the
spectra of Cu 2p a high-energy doublet (main peak at9356 eV) corresponds to it At the same time the low-energyCu 2p-doublet parameters are close to those found in [22] forY-123 the main peak at 9335 eV a satellite at sim943 eV as wellas parameters relating to copper oxide Cu (II) [28] 9336 eVand 9425 eV respectively However from the analysis of thespectra of Ba 3d and Y 3d (see earlier) it can be argued that
the Cu 2p signal from the phase of Y-123 may be only in thespectrum of IP samples
Thus in addition to the main phase the surface of IPcontains the final products of the reactions (1) + (2) and Y
2O3
phase probably sourced by the initial precursor incompletelyconsumed during the synthesis of YBa
2Cu3O6+120575
As a resultof MA treatment the surface of the powder is covered with alayer of yttriumoxide and the products of reactions (1) + (2) toa considerable depth of at least 10 nm (judging by the amountof Y2BaCuO
5phase in the samples determined by XRD)
Journal of Spectroscopy 7
323 XPS Study of NdBa2Cu3O6+120575
Oxide Figure 4 demon-strates the survey spectra of Nd-123 powders One can seethat as in the case of Y-123 samples the signal representingthe iron was not observed for any intensive milling durationThe feature of Nd-123 samples is rather low intensity of the Ba3d and Ba 4d peaks for powders activated for 05 and 2min(compare Figure 4 with Figure 2 for Y-123 powder) Bariumpeaks has markedly increased (as well as oxygen O 1s peak)only at 10min of activation
Figure 5 shows the high-resolution spectra of the elec-tronic levels of barium (3d and 4d) neodymium (4d) andcopper (2p) in powders with different activation prehistoryIn the barium spectra the high-intensity peaks at 7799 eV(3d52
) and 893 eV (4d52
) are obviously responsible for thecompound BaCO
3 and the low-intensity peaks at 7780 and
876 eV which are observed only in IP samples (dark shadedin Figure 5) correspond to the main phase by analogy withY-123 samples The analysis of Cu 2p spectra has revealed thepresence of copper ions with the electronic structure similarto that in Y-123 or in CuO oxide
However as seen in Figure 5 the state Cu 2p with highbinding energy (9359 plusmn 03 eV) is also present in all Nd-123samples According to our data (see Table 3) this state is nottypical for simple and ternary compounds of copper DuringMA processing its share in Cu 2p spectra changes in strictaccordancewith the high energy components of the Ba 3d andBa 4d spectra light shaded in Figure 5 (at 7817 eV (Ba 3d
53)
and 919 plusmn 03 eV (Ba 4d53
)) which implies that a doubleoxide of barium-copper was on the surface of the samplesWe tend to identify this oxide as Ba
2Cu3O5+x phase which
was detected by X-ray diffraction analysis of IP samples (seeTable 1) Despite the fact that this phase was not found byXRD in samples N-05 N-1 and N-2 it is visible in the XPSspectra due to the effect of spatial localization
According to Figure 5 the surface of the samples alsocontained the oxide Nd
2O3(line Nd 4d
52at 1211 eV) which
under intense grinding at the initial stages was partly trans-formed into Nd
2(C2O4)3[37] (line Nd 4d
52at sim1225 eV)
Based on the analysis of possible superpositions of the spectraof Ba 3d Ba 4d and Cu 2p the low-energy Nd 4d doublet(line Nd 4d
52at 1157 eV) the intensity of which is almost
independent of the MA duration belongs to a double oxideNdCu
119910O15+y+z of undetermined composition The Nd 4d
doublet of themain compound apparently overlaps with oneof the previously noted signals and so it is shown explicitlyin Figure 5
On the intensity ratios of the peaks in Figure 5 one canconstruct a model of the relative position of the phases Nd-123 BaCO
3 and Ba
2Cu3O5+x in the surface layer of the
material (this method has been used eg in [22] to analyzethe relative position of the layers Y-123 and BaCuO
2) To
realize this we use the dependence of the layer thicknessanalyzed by XPS (usually taken as 3 sdot 120582
119898) on the kinetic
energy of the electrons [38] referring to the electrons givingthe corresponding lines in the spectra of Ba 3d and Ba 4d asfollows
120582119898= 2170119864
minus2
119896+ 072(119886119864
119896)12 (3)
Ba 3d
N-10Cu 2pN-2Fe 2p
O 1sN-05
N-0Cu LVVCu 3s C 1sNd 4d
Ba 4d200 400 600 800 1000
Binding energy (eV)0
Figure 4 XPS survey spectra of the initial and mechanoactivatedNdBa
2Cu3O6+120575
samples
where 120582119898is the electron mean free path expressed in mono-
layers 119886 is monolayer thickness in nm 119864119896is kinetic energy
in eV (119864119896= ℎ] minus 119864BE minus 120593) ℎ] = 12536 eV is the energy of
the exciting radiation used inXPS analysis119864BE is the bindingenergy of the electronic level under analysis and120593 is theworkfunction of the spectrometer (346 eV)
According to this relationship the thickness of the layerunder analysis increases monotonically with increasing 119864
119896
in the range 119864119896gt 40 eV As can be seen from Figure 6
increase in the thickness of the layer under analysis canaffect the following volume ratios detectable by XPS phaseIphase III and phase IIphase III and has no influence onthe volume relation phase Iphase II The phase fractionto a first approximation is proportional to the area undercorresponding XPS peak Therefore based on the ratio ofareas of the different lines in the spectra in Figure 5 one canconclude that both barium-containing products of chemicaldecomposition of Nd-123 are located atop of the main oxidethat is correspond to phases I and II in Figure 6 The thick-ness of the degraded layer in N-10 sample is sim10 nm (as theoriginal phase is barely visible through it) and in IP (N-0)sample it is estimated to be 5-6 nm
It should be noted however that such a small thicknessof Ba2Cu3O5+x layer in IP has not prevented this phase to be
recognized by XRD analysis (see Table 1) One can thereforeconclude that IP particles contain in addition a considerableamount of Ba
2Cu3O5+x in the form of individual inclusions
in bulk (as a result of this oxide synthesis features seeSection 1) DuringMA processing material particles crackedand inclusions went outside resulting in the fraction ofBa2Cu3O5+x phase on the surface increased up to a point
(up to 1min inclusive) The subsequent decrease in thisphase (see Figure 5) is apparently due to the fact that anotherprocess also developed on the surface during grindingspending of Ba
2Cu3O5+x involving the original solid solution
Nd1+xBa2minusxCu3O6+120575 to formation of cation-stoichiometric
NdBa2Cu3O6+120575
To prove the occurrence of such interaction
8 Journal of Spectroscopy
Ba 3d
N-10
N-2
N-1
N-05
N-0
770 775 780 785 790 795 800 805Binding energy (eV)
(a)
N-10
N-1
Binding energy (eV)
Ba 4d
Ba 4d
N-2
N-05
N-0
68 72 80 84 88 92 96
Cu 3p X-ra
ysa
telli
tes
76
(b)
N-10
N-2
N-1
N-05
N-0
930 940 950 960 970Binding energy (eV)
Satellite I Satellite II
Cu 2p2p32
2p12
(c)
N-10
N-2
N-1
N-05
N-0
110 115 120 125 130 135Binding energy (eV)
Nd 4d
(d)
Figure 5 XPS spectra of NdBa2Cu3O6+120575
powders
119864119896 (Ba 3d) 119864119896 (Ba 4d)
Phase I Phase II
Phase III
Phase I Phase II
Phase III
31205823120582
XPS
study
area
XPS
study
area
lt
Figure 6 Analysis of the mutual arrangement phases in the surface layer of the material and their volume relations from XPS data
Journal of Spectroscopy 9
Table 3 Characteristic spectral parameters of different copper compounds
Electron orbital CuO CuCO3 Cu(OH)2 Cu2CO3(OH)2 Nd2BaCuO5
Binding energy eVBa 3d
527790lowast
Nd 4d52
1182lowast
Cu 2p32
9337 plusmn 1[28ndash30]
9348[28]
93474 plusmn 006[29 31]
9347[32] 9335lowast
O 1s 52974 plusmn 006[30 31]
53124[31] 5286lowast
lowastOur data
later we present the data of magnetic measurements whichindicate that MA treatment results in significant increase inthe temperature of the superconducting transition in separateregions of the material
324 Thermal Analysis of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
Samples of R-123 have been studied by thermogravimetrycoupled withmass-spectrometry to analyze the gases evolvedduring experiments Results of the study are summarizedin Figure 7 It is seen that reversible change in mass of IP-samples occurs in the range of 430ndash900∘C that must be dueto oxygen exchange between nonstoichiometric R-123 oxidesand the gas phase taking place at these temperatures [1] MPsamples start losing mass sharply around 70∘C when heatedMass spectrometry analysis of thermal desorption productsindicates the presence of large amount of water and a smallamount of carbon dioxide contained in the samples in theform of BaCO
3(the temperature range in which the CO
2
was released and the value of 119901CO2used for thermal analysis
of the atmosphere was consistent with conditions of bariumcarbonate decomposition)
325 Study of Magnetic Properties of YBa2Cu3O6+120575
andNdBa
2Cu3O6+120575
Temperature dependences of ZFC magne-tization of the samples Y-0 Y-05 Y-2 and Y-10 are shownin Figure 8 A sharp downturn in magnetization at sim90Kobserved in the samples Y-0 Y-05 and Y-2 clearly showsthe presence of the superconducting phase Superconductingtransition temperatures of the samples Y-0 Y-05 and Y-2have been determined by taking the derivative of the mag-netization against the temperature (119889119898119889119879) Thus definedtemperatures 119879
119888are equal to 91 K for the samples Y-0 and
Y-05 and 88K for the sample Y-2 A wide transition widtharound 119879
119888= 90K indicates that both the initial and MP
samples contain inhomogeneous superconductor phaseswithdifferent 119879
119888 The following facts indicate the presence of
paramagnetic contribution in the magnetization behavior ofMP samples and its growth with increasing milling durationa significant increase in magnetization 119898 of the samples Y-05 and Y-2 compared with the initial sample Y-0 at thetemperatures 119879 gt 119879
119888 weak temperature dependence 119898(119879)
in the temperature range 100ndash300 K for MP samples asignificant increase in themagnetization of Y-10 sample at lowtemperatures
100
99
98
97
96
95
94
93
92
100
99
98
97
96
95
94
93
92
0 200 400 600 800 1000
0 200 400 600 800 1000
14
12
10
8
6
4
3
2
Temperature (∘C)
Ion
curr
ent (
A)
Ion
curr
ent (
A)
Sam
ple w
eigh
t (
)
H2O
CO2
H2O (times1010) CO2 (times1011)
3
2
1
3998400
1998400
2998400
Figure 7 Thermal analysis results for samples Y-0 (1) N-0 (11015840) Y-2 (2) N-2 (21015840) and Y-10 (3) N-10 (31015840) Mass spectrometry data arerelated to the samples Y-10 (solid curves) and N-10 (dashed lines)
For comparison Figure 9 shows the temperature depen-dence of the FC magnetization in a magnetic field 119867 =500Oe for two new samples of Y-123 (120575 asymp 07) The firstsample has been freshly prepared and the other one has beensubjected to treatment at 297 plusmn 1K for 120 h at absolutehumidity of 23 120581Pa The sample with low oxygen content(and as a consequence with low 119879
119888) has been chosen due
to its relatively easy moisture saturation in these conditionswithout the use of MA (moisture saturation was controlledby the increase in weight which eventually was sim4wt)One can see that the sample saturated with water has apositive magnetic moment above the temperature 119879
119888and
shows an increase inmagnetic moment on cooling below this
10 Journal of Spectroscopy
N-0
N-1
N-10N-2
Y-2
Y-05
N-05
Y-0
Y-10
005 0005
0004
0003
0002
0001
0
0
minus005
minus01
minus015
minus02
minus025
minus03
minus01
minus02
minus03
003
002
001
0
0
0minus001
20 40 60 80 100 120 140119879 (K)
119898(e
mu
g)119898
(em
ug)
119898(e
mu
g)119898
(em
ug)
Figure 8 ZFC magnetizations as a function of temperature at119867 = 50Oe for the initial and mechanically activated samplesYBa2Cu3O6+120575
(top) NdBa2Cu3O6+120575
(bottom)
temperature similarly to Y-10 sample Onset temperature ofthe magnetic anomaly in the hydrated sample is the sameas that in the freshly prepared sample This experimentdemonstrates that the presence of water in MP sampleshas a significant effect on the temperature dependences ofthe magnetization observed in samples of Y-123 series (seeFigure 8)
Temperature dependences of ZFC magnetization of MPsamples in Nd-123 series are shown in Figure 8 The super-conducting transition temperatures of the samples N-0 N-05 and N-1 are independent of milling duration and equal to119879119888sim 57KMechanical treatment leads to a substantial change
in the magnetization of MP samples throughout the inves-tigated temperature range MP samples exhibit near-room-temperature hysteretic behavior that is ZFC magnetizationis more diamagnetic than FCmagnetization It may be due tomagnetic particles of mechanoactivatedNd-123 samples or tothe presence of impurity phases whose low content or highlydisordered crystal structures do not allow to observe thesephases by X-ray diffraction measurements We also cannotexclude the formation of CuO phase (119879
119873sim 220K) at the
surface of large NdBa2Cu3O6+120575
particles proceeding undermechanical activationAt the same time a significant increasein the paramagnetic contribution to the magnetization withincreasing milling duration is observed
004
002
0
minus002
minus004
minus006
minus0080 20 40 60 80 100 120 140
0 20 40 60 80 100 120 140
119898(e
mu)
119898(e
mu)
119879 (K)
119879 (K)
004
0038
0036
0034
Figure 9 FCmagnetizations as a function of temperature of freshlyprepared YBa
2Cu3O6+120575
sample (empty points) and of hydrated sam-ple (black points) at119867 = 500Oe Inset the temperature dependenceof magnetization of hydrated sample at119867 = 10 kOe
A wide transition width around 119879119888= 57K (|Δ119879
119888sim 20K|)
in MP samples of Nd-123 series cannot be explained only bythe presence of water in the structure The observed changesindicate that during MA treatment diffusion processes asso-ciated with the ordering of the cations Nd3+ and Ba2+ appa-rently occur according to [8ndash10] that has a significant effecton 119879119888
4 Discussion of Results
41 Interaction of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
withCO2 From comparison of Figures 4 and 5 it is clear that with
increasing duration of MA processing (120591119892) the amount of
barium-containing impurities on the surface of Nd-123 sam-ples continuously increases up to 120591
119892= 10min in contrast
to the situation for the oxide Y-123 for which initially (up120591119892= 05min) sudden change and subsequent (after 120591
119892=
05min) almost stagnation in the accumulation of chemicaldegradation products were observed (see Figures 2 and 3 anddata on the impurities in YBa
2Cu3O6+120575
sample) One can seefrom Figure 7 that the degree of water saturation (120578) of bothoxides (this parameter can be traced by sharp descendingbranch of sample mass change in the temperature range of30ndash450∘C) obeys similar relationships with increasing 120591
119892 its
growth with increasing MA duration close to proportionalfor Nd-123 (120578 sim 120591
119892) and tendency of 120578 to decrease for Y-123
(120578 = 155 sdot 120591119892
03) which is close to the root dependence char-
acteristic of reagent diffusion through the reaction productslayer
Taking into account the data in [1] stating the chemicaldegradation of Y-123 is carried out on the interface betweenY-123 and gas phase and one can explain sharply fallingrates of change in concentration of its products as well as ofH2O dissolved in the oxide the diffusion path length of H
2O
and CO2reactants to the location of the reactions (1) and
(2) increases with time 120591119892 However the uniformity of the
absorption of H2O and CO
2gases by MP of Nd-123 testifies
Journal of Spectroscopy 11
that the thickness of the degraded layer on the surface variesslightly Apparently it does not exceed 10 nm as indicated bya weak but clear signal of the main phase which appeared inthe Ba 4d-spectrum of N-10 sample (see Figure 5) Howeverit should be noted that Nd-123 MP sample actively entersinto chemical reactionwith atmospheric CO
2 the gas escapes
from the samples quite intensively when heated in the rangeof 800ndash900∘C (see Figure 7) Therefore the question oflocalization place of products of interaction between Nd-123and atmospheric components arises
Homogeneous nucleation and growth of interaction pro-ducts in the volume of Nd
1+xBa2minusxCu3O6+120575 parent phasemaybe the answer This assumption is based on the fact that theproducts of thermal desorption of N-10 sample (see Figure 7)contain weakly bound form of CO
2escaping in a wide tem-
perature range of 200ndash550∘C Obviously it is a form of gasdissolved in the structure Since the carbonization energy ofBa2+ ions is quite high homogeneous nucleation of carbonatephase at a certain concentration (equivactivity) of CO
2in the
structure facilitated by the participation of structural defects(whose concentration should be significant in MP samples)seems quite possible
42 Interaction of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
withWater In the Introductionwe have put links toworks statingthat the crucial feature for the practical application of thesuperconductor Nd-123 is its high resistance to chemicaldegradation under moisture Additional information thatexpands understanding of this feature has been received inour study Thus it is shown (see Figure 7) that a high con-centration of water accumulates in MP samples of Nd-123 indissolved form but the hydrolysis reaction development isquite limited as evidenced by the relatively low temperatureof H2O release from this oxide Moreover the results of
XRD and XPS analyzes have not detected even traces of theternary compound Nd
2BaCuO
5in these samples while it is
the compounds R2BaCuO
5due their characteristic colours
that are indicators of the hydrolysis reaction for the wholefamily of compounds R-123 [1 39 40] Thus if the hydrolysisreaction develops (there is a small peak on H
2O desorption
curve for sample N-10 at sim455∘C that can be attributed tothe chemically bound water) then it proceeds through non-traditional mechanism and with low rate
According to [41] the hydration mechanism for thehomologous series of R-123 compounds is in four stages Atthe initial stage water molecules penetrate into the bulk ofthe crystallites through the structural channels [(12) b 0]located in interspaces between CuO-chains typical for thistype of superconductors At the next stage protons whichare located in the oxygen positions of CuO-chains can besplit up of watermoleculesThis proton transfer is consideredto cause an internal (within the [CundashO]+-system) chargetransfer resulting in formation of molecular oxygen leavingthe structure At high concentrations of hydroxide ionsaccumulated in the structure the chemical decompositionof the initial oxide occurs Based on the previous schemeone can understand the reasons for high resistivity of N-123superconductor to chemical interaction with water
The authors of [42] discussed the high corrosion resis-tance of Nd-123 films in the water compared to the filmstructures of Y-123 and Eu-123 which was attributed to thepartial oxygen disorder in the planes of CuO-chains Sucha disorder should occur in Nd-123 due to the presence ofsome amount of Nd3+ ions in the sites nearby to CuO-planesof divalent barium According to the authors that shouldlead to overlapping structural channels for H
2O diffusion
and hence blocking the hydration process However ourdata on the thermal analysis (see Figure 7) illustrate thatthe saturation of Nd-123 structure with water during MAtreatment proceeds almost as fast as in Y-123 (in the rangeof 2ndash10 minutes even faster) Therefore the sought causeof the chemical stability of Nd-123 MP cannot be related toproblems of H
2O diffusion
The stage of removing oxygen from the structure is con-sidered [41 42] to be extremely important for the hydrationprocess of R-123 Thus the chemical degradation of Y-123oxide immersed in the water is completely stopped underpotential of 08 V relative to the standard electrode-saturatedsodium calomel [41] It is expected that the substitutionNd3+ rarr Ba2+ inNd-123 in addition to oxygen disordering inthe base structural plane should also lead to the strengtheningof its bondwith the lattice (due to electrostatic effect of highlycharged Nd3+ ion) [42] According to the authors [42] thisshould inhibit the reduction stage of hydration However it isimportant to consider the fact that the structure ofMP of Nd-123 contains a large amount of weakly bound CO
2 located
near Ba ions (since there is a tendency to the formation ofBaCO
3) therefore localized in the channels of the base plane
[(12) b 0] where also there is water In our opinion just theseCO2particles block channels of oxygen desorption which is
the main reason for the high stability of Nd-123 in relation tothe hydrolysis reaction
5 Conclusion
Thus as a result of mechanical activation treatment thesurface of YBa
2Cu3O6+120575
is covered by products of hydrolysisand carbonization to a considerable depth The chemicaldegradation process proceeds the normal waymdashthrough theformation of Y
2BaCuO
5phase
Chemical degradation of mechanoactivatedNdBa
2Cu3O6+120575
powders under the impact of CO2
isnot directly connected to hydrolysis process as occurs inYBa2Cu3O6+120575
(see reactions (1) and (2)) Carbonizationproceeds homogeneously through the stage of carbondioxide dissolution in the lattice of NdBa
2Cu3O6+120575
In itsturn the presence of CO
2molecules in the structure of
mechanoactivated NdBa2Cu3O6+120575
powders leads to a radicalchange in the mechanism of interaction between the super-conductor and water This mechanism eliminates the normalfor a homologous series of RBa
2Cu3O6+120575
the hydrolysisreaction with the formation of characteristic ldquocolorrdquoR2BaCuO
5phases The rate of chemical decomposition of
mechanically activated NdBa2Cu3O6+120575
by the new mecha-nism (not yet studied) is quite low
12 Journal of Spectroscopy
Mechanical treatment affects the temperature depen-dence of the magnetization of RBa
2Cu3O6+120575
compoundsThere is a significant increase in the paramagnetic and ferro-magnetic contributions to the magnetization with increasingmilling duration The latter leads to near-room-temperaturehysteretic behavior of NdBa
2Cu3O6+120575
samples between ZFCandFC regimes Itmay be due tomagnetic particles ofmecha-noactivated NdBa
2Cu3O6+120575
samples or to the presence ofimpurity phases whose low content or highly disorderedcrystal structures do not allow to observe these phases byX-ray diffraction measurements The mechanical treatmentdoes not have substantial influence on the transition tem-peratures of superconducting phases 119879
119888in the RBa
2Cu3O6+120575
compounds but a wide transition width around 119879119888indicates
that mechanically activated samples contain inhomogeneoussuperconductor phases with different 119879
119888 The broadening
of the superconducting transition in mechanically activatedNdBa
2Cu3O6+120575
samples may be due to redistribution ofcations between Nd- and Ba-sublattice
Finally we note that the high temperature superconduc-tor RBa
2Cu3O6+120575
subjected to mechanical activation cer-tainly has no significant advantages over conventional non-mechanoactivated material but it is obvious that physical-chemical studies of such powders reveal results interestingfrom the point of view of fundamental science
Acknowledgment
This work was supported by Russian Foundation for BasicResearch (Grant no 11-03-00317-a)
References
[1] I E Graboi A R Kaulrsquo and G Yu Metlin ldquoAdvances in scienceand technologyrdquo in Solid State Chemistry pp 3ndash142 VINITIANSSSR Moscow Russia 1989
[2] S Anders M G Blamire F-Im Buchholz et al ldquoEuropeanroadmap on superconductive electronicsmdashstatus and perspec-tivesrdquo Physica C vol 470 no 23-24 pp 2079ndash2126 2010
[3] B Ruck B Oelze R Dittmann et al ldquoMeasurement of thedynamic error rate of a high temperature superconductor rapidsingle flux quantum comparatorrdquo Applied Physics Letters vol72 no 18 pp 2328ndash2330 1998
[4] M W Rupich X Li C Thieme et al ldquoAdvances in secondgeneration high temperature superconducting wire manufac-turing and RampD at American superconductor corporationrdquoSuperconductor Science and Technology vol 23 no 1 Article ID014015 2010
[5] A Rakitin M Kobayashi and A P Litvinchuk ldquoSuperi-onic behavior of high-temperature superconductorsrdquo PhysicalReview B vol 55 no 1 pp 89ndash92 1997
[6] T Kagiyama J Shimoyama K D Otzschi et al ldquoEffect of cationcomposition and oxygen nonstoichiometry on 119869
119888-119861 properties
of Nd123rdquo Physica C vol 341ndash348 no 2 pp 1445ndash1446 2000
[7] M Badaye J G Wen K Fukushima et al ldquoSuperior propertiesof NdBa
2Cu3O119910over YBa
2Cu3O119909thin filmsrdquo Superconductor
Science and Technology vol 10 no 11 pp 825ndash830 1997
[8] C Cantoni D P Norton D M Kroeger et al ldquoPhase stabilityfor the in situ growth of Nd
1+119909Ba2minus119909
Cu3O119910films using pulsed-
laser depositionrdquo Applied Physics Letters vol 74 no 1 pp 96ndash98 1999
[9] E A Goodilin N N Oleynikov E V Antipov et al ldquoPhasestability for the in situ growth of Nd
1+119909Ba2minus119909
Cu3O119910films using
pulsed-laser depositionrdquo Physica C vol 272 6578 pages 1996[10] E Guilmeau F Giovannelli I Monot-Laffez S Marinel J
Provost and G Desgardin ldquoTop seeding melt texture growthof NdBaCuO pellets in airrdquoThe European Physical Journal vol13 no 3 pp 157ndash160 2001
[11] A I Ancharov T F Grigorrsquoeva T Yu Kiseleva A A Novakovaet al inMechanocomposites-Precursorsfor the Creation of Mate-rials with New Properties O I Lomovskii Ed p 424 Izd-voSO RAN Novosibirsk Russia 2010
[12] A Hamrita F Ben Azzouz A Madani and M Ben SalemldquoMagnetoresistivity and microstructure of YBa
2Cu3O119910pre-
pared using planetary ball millingrdquo Physica C vol 472 no 1pp 34ndash38 2012
[13] R P Vasquez ldquoIntrinsic photoemission signals surface prepa-ration and surface stability of high temperature superconduc-torsrdquo Journal of Electron Spectroscopy and Related Phenomenavol 66 no 3-4 pp 209ndash222 1994
[14] S S Gorelik L N Rastorguev and A Yu Skakov in Rentgeno-graphIcheskII I ElektronographIcheskII AnalIz p 368 Izd-voMetallurgia Moscow Russia 1970
[15] M V Reshetniak and O V Sobol Program for diffractionanalysis ldquoNew Profilerdquo(Last update 10 02 2007) Version 3 4400 (Freeware) WIN9xMENT2KXP Copyright (c) 1992-2007 ReMax SoftWare 2000
[16] M Wegmann L Watson and A Hendry ldquoXPS analysis of sub-micrometer barium titanate powderrdquo Journal of the AmericanCeramic Society vol 87 no 3 pp 371ndash377 2004
[17] A B Christie J Lee I Sutherland and J M Walls ldquoAn XPSstudy of ion-induced compositional changes with group II andgroup IV compoundsrdquo Applications of Surface Science vol 15no 1ndash4 pp 224ndash237 1983
[18] U A Joshi S Yoon S Balk and J S Lee ldquoSurfactant-freehydrothermal synthesis of highly tetragonal barium titanatenanowires a structural investigationrdquo Journal of Physical Chem-istry B vol 110 no 25 pp 12249ndash12256 2006
[19] R Caracciolo ldquoChemical characterization techniques for thinfilmsrdquo in Ceramic Films and Coatings J B Wachtman and R AHaber Eds p 376 New Jersey NJ USA 1992
[20] I N Shabanova Y A Naimushina and N S Terebova ldquoCom-position and temperature dependence of a Y-Ba-Cu-O HTSCelectronic structurerdquo Superconductor Science and Technologyvol 15 no 7 pp 1030ndash1033 2002
[21] J Beyer T Schurig S Menkel Z Quan and H Koch ldquoXPSinvestigation of the surface composition of sputtered YBCOthin filmsrdquo Physica C vol 246 no 1-2 pp 156ndash162 1995
[22] C C Chang M S Hegde X D Wu et al ldquoSurface layers onsuperconducting Y-Ba-Cu-O films studied with x-ray photo-electron spectroscopyrdquo Applied Physics Letters vol 55 no 16pp 1680ndash1682 1989
[23] X D Wu A Inam M S Hegde et al ldquoCrystalline perfectionof as-deposited high-Tc superconducting thin-film surfacesion channeling and x-ray photoelectron spectroscopy studyrdquoPhysical Review B vol 38 no 13 pp 9307ndash9310 1988
[24] P Rajasekar P Chakraborty S K Bandyopadhyay P Barat andP Sen ldquoX-ray photoelectron spectroscopy study of oxygen and
Journal of Spectroscopy 13
argon annealed YBa22Cu3O7minus120575
rdquo Modern Physics Letters B vol12 no 6-7 pp 239ndash245 1998
[25] J Halbritter P Walk H J Mathes B Haeuser and H RogallaldquoARXPS-studies of c-axis textured YBa
2Cu3O119909-filmsrdquo Physica
C vol 153ndash155 no 1 pp 127ndash128 1988[26] T J Sarapatka and P Mikusık ldquoXPS study of PbYBaCuO thin-
film tunnel contactrdquo Applied Surface Science vol 68 no 1 pp35ndash40 1993
[27] J A T Verhoeven and H Van Doveren ldquoAn XPS investigationof the interaction of CH
4 C2H2 C2H4and C
2H6with a barium
surfacerdquo Surface Science vol 123 no 2-3 pp 369ndash383 1982[28] C D Wagner W M Riggs L E Davis J F Moulder and G
E Mullenberg Handbook of X-Ray Photoelectron SpectroscopyPerkin-Elmer Corp Eden Prairie Minn USA 1979
[29] M C Biesinger L W M Lau A R Gerson and R S C SmartldquoResolving surface chemical states in XPS analysis of first rowtransition metals oxides and hydroxides Sc Ti V Cu and ZnrdquoApplied Surface Science vol 257 no 3 pp 887ndash898 2010
[30] X Y Fan Z GWu P X Yan et al ldquoFabrication of well-orderedCuO nanowire arrays by direct oxidation of sputter-depositedCu3N filmrdquo Materials Letters vol 62 no 12-13 pp 1805ndash1808
2008[31] S J Kerber J J Bruckner K Wozniak S Seal S Hardcastle
and T L Barr ldquoNature of hydrogen in x-ray photoelectronspectroscopy general patterns from hydroxides to hydrogenbondingrdquo Journal of Vacuum Science and Technology A vol 14no 3 pp 1314ndash1320 1996
[32] G Moretti G Fierro M Lo Jacono and P Porta ldquoCharac-terization of CuO-ZnO catalysts by X-ray photoelectron spec-troscopy precursors calcined and reduced samplesrdquo Surfaceand Interface Analysis vol 14 no 6-7 pp 325ndash336 1989
[33] H Van Doveren and J A T H Verhoeven ldquoXPS spectra of CaSr Ba and their oxidesrdquo Journal of Electron Spectroscopy andRelated Phenomena vol 21 no 3 pp 265ndash273 1980
[34] B V Crist Handbooks of Monochromatic XPS Spectra Volume2mdashCommercially pure binary oxides XPS International LLCLeona Tex USA 2005
[35] D D Sarma and C N R Rao ldquoXPES studies of oxides ofsecond- and third-row transition metals including rare earthsrdquoJournal of Electron Spectroscopy and Related Phenomena vol 20no 1 pp 25ndash45 1980
[36] V I Nefedov and A N Sokolov ldquoDegradatzia visokotemper-aturnich sverchprovodnikov pri khimicheskich vozdeistviachrdquoZhurnal Neorganicheskoi Khimii vol 34 no 11 pp 2723ndash27391989
[37] Y Uwamino T Ishizuka and H Yamatera ldquoX-ray photoelec-tron spectroscopy of rare-earth compoundsrdquo Journal of ElectronSpectroscopy and Related Phenomena vol 34 no 1 pp 67ndash781984
[38] M P Seah and W A Dench ldquoQuantitative electron spec-troscopy of surfaces a standard data base for electron inelasticmean free paths in solidsrdquo Surface and Interface Analysis vol 1no 1 pp 2ndash11 1979
[39] C H Lin H C I Kao and C M Wang ldquoKinetics andstability of R(Ba
15Sr05)Cu3O119910(R = La Nd Sm Eu Gd Dy Ho)
superconductors inwaterrdquoMaterials Chemistry and Physics vol82 no 2 pp 435ndash439 2003
[40] A G Knizhnik R A Stukan and G O Eremenko ldquoStudy theinteraction between europium HTSC of 123 type and waterrdquoSverkhprovodimost vol 4 no 1 pp 177ndash182 1991 (Russian)
[41] J Zhou R K Lo J T McDevitt et al ldquoDevelopment of areliable materials base for superconducting electronicsrdquo Journalof Materials Research vol 12 no 11 pp 2958ndash2975 1997
[42] S B Schougaard M F Ali and J T McDevitt ldquoEvidence forhigh stability against water corrosion of NdBa
2Cu3O7plusmn120575
relativeto YBa
2Cu3OO7minus120575
and EuBa2Cu3OO7minus120575
rdquo Applied Physics Let-ters vol 84 no 7 pp 1144ndash1146 2004
Submit your manuscripts athttpwwwhindawicom
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Inorganic ChemistryInternational Journal of
Hindawi Publishing Corporation httpwwwhindawicom Volume 2014
International Journal ofPhotoenergy
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Carbohydrate Chemistry
International Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
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Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Advances in
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Analytical Methods in Chemistry
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Volume 2014
Bioinorganic Chemistry and ApplicationsHindawi Publishing Corporationhttpwwwhindawicom Volume 2014
SpectroscopyInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
The Scientific World JournalHindawi Publishing Corporation httpwwwhindawicom Volume 2014
Medicinal ChemistryInternational Journal of
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Chromatography Research International
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Applied ChemistryJournal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Theoretical ChemistryJournal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
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Analytical ChemistryInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
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Quantum Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Organic Chemistry International
ElectrochemistryInternational Journal of
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Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
CatalystsJournal of
Journal of Spectroscopy 5
Table 1 Phase composition lattice parameters and the size of coherent scattering regions (119871) for YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
beforeand after mechanical treatment
Crystallographic parameters Milling duration in AGO-2(1) YBa
2Cu3O6+120575
powders0 s
(sample Y-0)30 s
(sample Y-05)2min
(sample Y-2)10min
(sample Y-10)The main phasemdashorthorhombic SG Pmmm119886 A 38208(3) 38218(3) 38287(10) 38344(10)119887 A 38884(5) 38893(5) 38938(15) 38879(15)119888 A 116809(11) 116793(12) 116739(33) 116663(31)119881 A3 173541(53) 173599(55) 174036(161) 173919(158)Impurity mass mdash sim5 Y
2BaCuO
5sim5 Y
2BaCuO
5sim7 Y
2BaCuO
5
119871 nm 167 57 25 20(2) NdBa
2Cu3O6+120575
powders0 s
(sample N-0)30 s
(sample N-05)2min
(sample N-2)10min
(sample N-10)The main phasemdashorthorhombic SG Pmmm119886 A 38677(1) 38731(3) 38727(12) 38754(12)119887 A 39202(1) 39206(10) 39225(14) 39161(15)119888 A 117612(3) 117622(24) 117630(39) 117661(24)119881 A3 178328(6) 178608(118) 178688(178) 178564(212)Impurity mass sim3 Ba
2Cu3O5+119909
mdash mdash mdash119871 HM 1792 325 229 169
200 400 600 800 1000 1200Binding energy (eV)
Y-10Cu 2p
Y-2Fe 2pY-05
Y 3d Y-0Ba 4d
Ba 3d
C 1s
O 1s
0
Figure 2 XPS survey spectra of the initial and mechanoactivatedYBa2Cu3O6+120575
samples
Recording such spectra conducted in high sensitivity mode(at high 119864PE) allows to consider the main lines of all elementspresented in the surface layer of the material in amountsgreater than 03 at As could be expected there are peaks ofthe electronic levels of yttrium barium copper and oxygencontained in the composition of the oxide under study TheC 1s peak includes a signal from the carbon contamination ofthe random nature
One can see (Figure 2) that on the surface of MP sam-ples there is no iron (mill headsets material) leading tothe appearance of specific magnetic and superconductingproperties of the material Strongly increased barium peak
(represented as a doublet of Ba 3d52minusBa 3d
32) in the spectra
of activated samples testifies the redistribution of elementsbetween the volume and surface occurs which is usuallythe result of chemical degradation of the surface under theinfluence of an environment In this case it could be a well-established [36] reactions as follows
2YBa2Cu3O65+119909+ 3H2O
997888rarr Y2BaCuO
5+ 3Ba(OH)
2+ 5CuO+ uarr119909O
2
(1)
Ba(OH)2+ CO2997888rarr BaCO
3+H2O (2)
Table 2 summarizes the obtained BaCO3of CP grade cal-
cinated at 700∘C Y2BaCuO
5and taken from the literature of
spectrometric data for the reactants involved in the reactions(1) and (2) for reliable identification of the peaks of thesecompounds in the spectra of the samples under study
High-resolution XPS spectra showing the characteristicelectronic levels of the elements constituting Y-123 samplesare presented in Figure 3
The analysis of the Ba 3d spectra has showed that in addi-tion to barium carbonate (line Ba 3d
52at 7799 eV) there is
the phase Y2BaCuO
5(line Ba 3d
52at sim782 eV) on the surface
of the samplesThe line Ba 3d52
at 7780 eVwhich is observedonly in the IP is directly owned by Y-123 (see Table 2)The Y 3d spectra confirm the presence of Y
2BaCuO
5-phase
on the surface of samples the substancersquos line Y 3d52
at1587 eV is clearly visible in these spectra (see Table 2)Besides the Y 3d spectra reveal the surface contains thefollowing oxides Y
2O3[34] (line Y 3d
52at 1569 eV) Y-123
6 Journal of Spectroscopy
Ba 3d
Y-10
Y-2
Y-05
Y-0
776 780 784 788 792 796 800Binding energy (eV)
3d523d32
(a)
Binding energy (eV)
Y 3d
Y-10
Y-2
Y-05
Y-0
150 152 154 156 158 160 162 164 166
(b)
Cu 2p
Y-10 Satellite I Satellite II
Y-2
Y-05
Y-0
930 940 950 960 970Binding energy (eV)
2p32
2p12
(c)
Figure 3 XPS spectra of YBa2Cu3O6+120575
powders Dark shading the main phase signal light shading Y2BaCuO
5signal
Table 2 The positions of the characteristic XPS lines of barium compounds
Electron orbital BaCO3 Ba(OH)2 Y-123 Y2BaCuO
5
Binding energy eV
Ba 3d52
7799 [16 17]7798lowast
7813 plusmn 01[18 19]
7777 plusmn 01[20ndash23] 7819lowast
Ba 4d52 893lowast 875
[22]
Y 3d52
1560 plusmn 02[21 24 25] 1587lowast
Cu 2p32
9335[21 26] 9356lowast
O 1s5314 plusmn 01[16 17]5314lowast
5312 qB[27]
52845 plusmn 005 qB[20ndash23] (5291 5313)lowast
C 1s28925 plusmn 015 qB
[16 17]2894lowast
lowastOur data
(line Y 3d52
at 1560 eV in the spectrum of IP) and the phaseY2(C2O4)3[37] (line Y 3d
52at 1601 eV) The presence of
Y2BaCuO
5compound in samples is also reflected in the
spectra of Cu 2p a high-energy doublet (main peak at9356 eV) corresponds to it At the same time the low-energyCu 2p-doublet parameters are close to those found in [22] forY-123 the main peak at 9335 eV a satellite at sim943 eV as wellas parameters relating to copper oxide Cu (II) [28] 9336 eVand 9425 eV respectively However from the analysis of thespectra of Ba 3d and Y 3d (see earlier) it can be argued that
the Cu 2p signal from the phase of Y-123 may be only in thespectrum of IP samples
Thus in addition to the main phase the surface of IPcontains the final products of the reactions (1) + (2) and Y
2O3
phase probably sourced by the initial precursor incompletelyconsumed during the synthesis of YBa
2Cu3O6+120575
As a resultof MA treatment the surface of the powder is covered with alayer of yttriumoxide and the products of reactions (1) + (2) toa considerable depth of at least 10 nm (judging by the amountof Y2BaCuO
5phase in the samples determined by XRD)
Journal of Spectroscopy 7
323 XPS Study of NdBa2Cu3O6+120575
Oxide Figure 4 demon-strates the survey spectra of Nd-123 powders One can seethat as in the case of Y-123 samples the signal representingthe iron was not observed for any intensive milling durationThe feature of Nd-123 samples is rather low intensity of the Ba3d and Ba 4d peaks for powders activated for 05 and 2min(compare Figure 4 with Figure 2 for Y-123 powder) Bariumpeaks has markedly increased (as well as oxygen O 1s peak)only at 10min of activation
Figure 5 shows the high-resolution spectra of the elec-tronic levels of barium (3d and 4d) neodymium (4d) andcopper (2p) in powders with different activation prehistoryIn the barium spectra the high-intensity peaks at 7799 eV(3d52
) and 893 eV (4d52
) are obviously responsible for thecompound BaCO
3 and the low-intensity peaks at 7780 and
876 eV which are observed only in IP samples (dark shadedin Figure 5) correspond to the main phase by analogy withY-123 samples The analysis of Cu 2p spectra has revealed thepresence of copper ions with the electronic structure similarto that in Y-123 or in CuO oxide
However as seen in Figure 5 the state Cu 2p with highbinding energy (9359 plusmn 03 eV) is also present in all Nd-123samples According to our data (see Table 3) this state is nottypical for simple and ternary compounds of copper DuringMA processing its share in Cu 2p spectra changes in strictaccordancewith the high energy components of the Ba 3d andBa 4d spectra light shaded in Figure 5 (at 7817 eV (Ba 3d
53)
and 919 plusmn 03 eV (Ba 4d53
)) which implies that a doubleoxide of barium-copper was on the surface of the samplesWe tend to identify this oxide as Ba
2Cu3O5+x phase which
was detected by X-ray diffraction analysis of IP samples (seeTable 1) Despite the fact that this phase was not found byXRD in samples N-05 N-1 and N-2 it is visible in the XPSspectra due to the effect of spatial localization
According to Figure 5 the surface of the samples alsocontained the oxide Nd
2O3(line Nd 4d
52at 1211 eV) which
under intense grinding at the initial stages was partly trans-formed into Nd
2(C2O4)3[37] (line Nd 4d
52at sim1225 eV)
Based on the analysis of possible superpositions of the spectraof Ba 3d Ba 4d and Cu 2p the low-energy Nd 4d doublet(line Nd 4d
52at 1157 eV) the intensity of which is almost
independent of the MA duration belongs to a double oxideNdCu
119910O15+y+z of undetermined composition The Nd 4d
doublet of themain compound apparently overlaps with oneof the previously noted signals and so it is shown explicitlyin Figure 5
On the intensity ratios of the peaks in Figure 5 one canconstruct a model of the relative position of the phases Nd-123 BaCO
3 and Ba
2Cu3O5+x in the surface layer of the
material (this method has been used eg in [22] to analyzethe relative position of the layers Y-123 and BaCuO
2) To
realize this we use the dependence of the layer thicknessanalyzed by XPS (usually taken as 3 sdot 120582
119898) on the kinetic
energy of the electrons [38] referring to the electrons givingthe corresponding lines in the spectra of Ba 3d and Ba 4d asfollows
120582119898= 2170119864
minus2
119896+ 072(119886119864
119896)12 (3)
Ba 3d
N-10Cu 2pN-2Fe 2p
O 1sN-05
N-0Cu LVVCu 3s C 1sNd 4d
Ba 4d200 400 600 800 1000
Binding energy (eV)0
Figure 4 XPS survey spectra of the initial and mechanoactivatedNdBa
2Cu3O6+120575
samples
where 120582119898is the electron mean free path expressed in mono-
layers 119886 is monolayer thickness in nm 119864119896is kinetic energy
in eV (119864119896= ℎ] minus 119864BE minus 120593) ℎ] = 12536 eV is the energy of
the exciting radiation used inXPS analysis119864BE is the bindingenergy of the electronic level under analysis and120593 is theworkfunction of the spectrometer (346 eV)
According to this relationship the thickness of the layerunder analysis increases monotonically with increasing 119864
119896
in the range 119864119896gt 40 eV As can be seen from Figure 6
increase in the thickness of the layer under analysis canaffect the following volume ratios detectable by XPS phaseIphase III and phase IIphase III and has no influence onthe volume relation phase Iphase II The phase fractionto a first approximation is proportional to the area undercorresponding XPS peak Therefore based on the ratio ofareas of the different lines in the spectra in Figure 5 one canconclude that both barium-containing products of chemicaldecomposition of Nd-123 are located atop of the main oxidethat is correspond to phases I and II in Figure 6 The thick-ness of the degraded layer in N-10 sample is sim10 nm (as theoriginal phase is barely visible through it) and in IP (N-0)sample it is estimated to be 5-6 nm
It should be noted however that such a small thicknessof Ba2Cu3O5+x layer in IP has not prevented this phase to be
recognized by XRD analysis (see Table 1) One can thereforeconclude that IP particles contain in addition a considerableamount of Ba
2Cu3O5+x in the form of individual inclusions
in bulk (as a result of this oxide synthesis features seeSection 1) DuringMA processing material particles crackedand inclusions went outside resulting in the fraction ofBa2Cu3O5+x phase on the surface increased up to a point
(up to 1min inclusive) The subsequent decrease in thisphase (see Figure 5) is apparently due to the fact that anotherprocess also developed on the surface during grindingspending of Ba
2Cu3O5+x involving the original solid solution
Nd1+xBa2minusxCu3O6+120575 to formation of cation-stoichiometric
NdBa2Cu3O6+120575
To prove the occurrence of such interaction
8 Journal of Spectroscopy
Ba 3d
N-10
N-2
N-1
N-05
N-0
770 775 780 785 790 795 800 805Binding energy (eV)
(a)
N-10
N-1
Binding energy (eV)
Ba 4d
Ba 4d
N-2
N-05
N-0
68 72 80 84 88 92 96
Cu 3p X-ra
ysa
telli
tes
76
(b)
N-10
N-2
N-1
N-05
N-0
930 940 950 960 970Binding energy (eV)
Satellite I Satellite II
Cu 2p2p32
2p12
(c)
N-10
N-2
N-1
N-05
N-0
110 115 120 125 130 135Binding energy (eV)
Nd 4d
(d)
Figure 5 XPS spectra of NdBa2Cu3O6+120575
powders
119864119896 (Ba 3d) 119864119896 (Ba 4d)
Phase I Phase II
Phase III
Phase I Phase II
Phase III
31205823120582
XPS
study
area
XPS
study
area
lt
Figure 6 Analysis of the mutual arrangement phases in the surface layer of the material and their volume relations from XPS data
Journal of Spectroscopy 9
Table 3 Characteristic spectral parameters of different copper compounds
Electron orbital CuO CuCO3 Cu(OH)2 Cu2CO3(OH)2 Nd2BaCuO5
Binding energy eVBa 3d
527790lowast
Nd 4d52
1182lowast
Cu 2p32
9337 plusmn 1[28ndash30]
9348[28]
93474 plusmn 006[29 31]
9347[32] 9335lowast
O 1s 52974 plusmn 006[30 31]
53124[31] 5286lowast
lowastOur data
later we present the data of magnetic measurements whichindicate that MA treatment results in significant increase inthe temperature of the superconducting transition in separateregions of the material
324 Thermal Analysis of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
Samples of R-123 have been studied by thermogravimetrycoupled withmass-spectrometry to analyze the gases evolvedduring experiments Results of the study are summarizedin Figure 7 It is seen that reversible change in mass of IP-samples occurs in the range of 430ndash900∘C that must be dueto oxygen exchange between nonstoichiometric R-123 oxidesand the gas phase taking place at these temperatures [1] MPsamples start losing mass sharply around 70∘C when heatedMass spectrometry analysis of thermal desorption productsindicates the presence of large amount of water and a smallamount of carbon dioxide contained in the samples in theform of BaCO
3(the temperature range in which the CO
2
was released and the value of 119901CO2used for thermal analysis
of the atmosphere was consistent with conditions of bariumcarbonate decomposition)
325 Study of Magnetic Properties of YBa2Cu3O6+120575
andNdBa
2Cu3O6+120575
Temperature dependences of ZFC magne-tization of the samples Y-0 Y-05 Y-2 and Y-10 are shownin Figure 8 A sharp downturn in magnetization at sim90Kobserved in the samples Y-0 Y-05 and Y-2 clearly showsthe presence of the superconducting phase Superconductingtransition temperatures of the samples Y-0 Y-05 and Y-2have been determined by taking the derivative of the mag-netization against the temperature (119889119898119889119879) Thus definedtemperatures 119879
119888are equal to 91 K for the samples Y-0 and
Y-05 and 88K for the sample Y-2 A wide transition widtharound 119879
119888= 90K indicates that both the initial and MP
samples contain inhomogeneous superconductor phaseswithdifferent 119879
119888 The following facts indicate the presence of
paramagnetic contribution in the magnetization behavior ofMP samples and its growth with increasing milling durationa significant increase in magnetization 119898 of the samples Y-05 and Y-2 compared with the initial sample Y-0 at thetemperatures 119879 gt 119879
119888 weak temperature dependence 119898(119879)
in the temperature range 100ndash300 K for MP samples asignificant increase in themagnetization of Y-10 sample at lowtemperatures
100
99
98
97
96
95
94
93
92
100
99
98
97
96
95
94
93
92
0 200 400 600 800 1000
0 200 400 600 800 1000
14
12
10
8
6
4
3
2
Temperature (∘C)
Ion
curr
ent (
A)
Ion
curr
ent (
A)
Sam
ple w
eigh
t (
)
H2O
CO2
H2O (times1010) CO2 (times1011)
3
2
1
3998400
1998400
2998400
Figure 7 Thermal analysis results for samples Y-0 (1) N-0 (11015840) Y-2 (2) N-2 (21015840) and Y-10 (3) N-10 (31015840) Mass spectrometry data arerelated to the samples Y-10 (solid curves) and N-10 (dashed lines)
For comparison Figure 9 shows the temperature depen-dence of the FC magnetization in a magnetic field 119867 =500Oe for two new samples of Y-123 (120575 asymp 07) The firstsample has been freshly prepared and the other one has beensubjected to treatment at 297 plusmn 1K for 120 h at absolutehumidity of 23 120581Pa The sample with low oxygen content(and as a consequence with low 119879
119888) has been chosen due
to its relatively easy moisture saturation in these conditionswithout the use of MA (moisture saturation was controlledby the increase in weight which eventually was sim4wt)One can see that the sample saturated with water has apositive magnetic moment above the temperature 119879
119888and
shows an increase inmagnetic moment on cooling below this
10 Journal of Spectroscopy
N-0
N-1
N-10N-2
Y-2
Y-05
N-05
Y-0
Y-10
005 0005
0004
0003
0002
0001
0
0
minus005
minus01
minus015
minus02
minus025
minus03
minus01
minus02
minus03
003
002
001
0
0
0minus001
20 40 60 80 100 120 140119879 (K)
119898(e
mu
g)119898
(em
ug)
119898(e
mu
g)119898
(em
ug)
Figure 8 ZFC magnetizations as a function of temperature at119867 = 50Oe for the initial and mechanically activated samplesYBa2Cu3O6+120575
(top) NdBa2Cu3O6+120575
(bottom)
temperature similarly to Y-10 sample Onset temperature ofthe magnetic anomaly in the hydrated sample is the sameas that in the freshly prepared sample This experimentdemonstrates that the presence of water in MP sampleshas a significant effect on the temperature dependences ofthe magnetization observed in samples of Y-123 series (seeFigure 8)
Temperature dependences of ZFC magnetization of MPsamples in Nd-123 series are shown in Figure 8 The super-conducting transition temperatures of the samples N-0 N-05 and N-1 are independent of milling duration and equal to119879119888sim 57KMechanical treatment leads to a substantial change
in the magnetization of MP samples throughout the inves-tigated temperature range MP samples exhibit near-room-temperature hysteretic behavior that is ZFC magnetizationis more diamagnetic than FCmagnetization It may be due tomagnetic particles of mechanoactivatedNd-123 samples or tothe presence of impurity phases whose low content or highlydisordered crystal structures do not allow to observe thesephases by X-ray diffraction measurements We also cannotexclude the formation of CuO phase (119879
119873sim 220K) at the
surface of large NdBa2Cu3O6+120575
particles proceeding undermechanical activationAt the same time a significant increasein the paramagnetic contribution to the magnetization withincreasing milling duration is observed
004
002
0
minus002
minus004
minus006
minus0080 20 40 60 80 100 120 140
0 20 40 60 80 100 120 140
119898(e
mu)
119898(e
mu)
119879 (K)
119879 (K)
004
0038
0036
0034
Figure 9 FCmagnetizations as a function of temperature of freshlyprepared YBa
2Cu3O6+120575
sample (empty points) and of hydrated sam-ple (black points) at119867 = 500Oe Inset the temperature dependenceof magnetization of hydrated sample at119867 = 10 kOe
A wide transition width around 119879119888= 57K (|Δ119879
119888sim 20K|)
in MP samples of Nd-123 series cannot be explained only bythe presence of water in the structure The observed changesindicate that during MA treatment diffusion processes asso-ciated with the ordering of the cations Nd3+ and Ba2+ appa-rently occur according to [8ndash10] that has a significant effecton 119879119888
4 Discussion of Results
41 Interaction of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
withCO2 From comparison of Figures 4 and 5 it is clear that with
increasing duration of MA processing (120591119892) the amount of
barium-containing impurities on the surface of Nd-123 sam-ples continuously increases up to 120591
119892= 10min in contrast
to the situation for the oxide Y-123 for which initially (up120591119892= 05min) sudden change and subsequent (after 120591
119892=
05min) almost stagnation in the accumulation of chemicaldegradation products were observed (see Figures 2 and 3 anddata on the impurities in YBa
2Cu3O6+120575
sample) One can seefrom Figure 7 that the degree of water saturation (120578) of bothoxides (this parameter can be traced by sharp descendingbranch of sample mass change in the temperature range of30ndash450∘C) obeys similar relationships with increasing 120591
119892 its
growth with increasing MA duration close to proportionalfor Nd-123 (120578 sim 120591
119892) and tendency of 120578 to decrease for Y-123
(120578 = 155 sdot 120591119892
03) which is close to the root dependence char-
acteristic of reagent diffusion through the reaction productslayer
Taking into account the data in [1] stating the chemicaldegradation of Y-123 is carried out on the interface betweenY-123 and gas phase and one can explain sharply fallingrates of change in concentration of its products as well as ofH2O dissolved in the oxide the diffusion path length of H
2O
and CO2reactants to the location of the reactions (1) and
(2) increases with time 120591119892 However the uniformity of the
absorption of H2O and CO
2gases by MP of Nd-123 testifies
Journal of Spectroscopy 11
that the thickness of the degraded layer on the surface variesslightly Apparently it does not exceed 10 nm as indicated bya weak but clear signal of the main phase which appeared inthe Ba 4d-spectrum of N-10 sample (see Figure 5) Howeverit should be noted that Nd-123 MP sample actively entersinto chemical reactionwith atmospheric CO
2 the gas escapes
from the samples quite intensively when heated in the rangeof 800ndash900∘C (see Figure 7) Therefore the question oflocalization place of products of interaction between Nd-123and atmospheric components arises
Homogeneous nucleation and growth of interaction pro-ducts in the volume of Nd
1+xBa2minusxCu3O6+120575 parent phasemaybe the answer This assumption is based on the fact that theproducts of thermal desorption of N-10 sample (see Figure 7)contain weakly bound form of CO
2escaping in a wide tem-
perature range of 200ndash550∘C Obviously it is a form of gasdissolved in the structure Since the carbonization energy ofBa2+ ions is quite high homogeneous nucleation of carbonatephase at a certain concentration (equivactivity) of CO
2in the
structure facilitated by the participation of structural defects(whose concentration should be significant in MP samples)seems quite possible
42 Interaction of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
withWater In the Introductionwe have put links toworks statingthat the crucial feature for the practical application of thesuperconductor Nd-123 is its high resistance to chemicaldegradation under moisture Additional information thatexpands understanding of this feature has been received inour study Thus it is shown (see Figure 7) that a high con-centration of water accumulates in MP samples of Nd-123 indissolved form but the hydrolysis reaction development isquite limited as evidenced by the relatively low temperatureof H2O release from this oxide Moreover the results of
XRD and XPS analyzes have not detected even traces of theternary compound Nd
2BaCuO
5in these samples while it is
the compounds R2BaCuO
5due their characteristic colours
that are indicators of the hydrolysis reaction for the wholefamily of compounds R-123 [1 39 40] Thus if the hydrolysisreaction develops (there is a small peak on H
2O desorption
curve for sample N-10 at sim455∘C that can be attributed tothe chemically bound water) then it proceeds through non-traditional mechanism and with low rate
According to [41] the hydration mechanism for thehomologous series of R-123 compounds is in four stages Atthe initial stage water molecules penetrate into the bulk ofthe crystallites through the structural channels [(12) b 0]located in interspaces between CuO-chains typical for thistype of superconductors At the next stage protons whichare located in the oxygen positions of CuO-chains can besplit up of watermoleculesThis proton transfer is consideredto cause an internal (within the [CundashO]+-system) chargetransfer resulting in formation of molecular oxygen leavingthe structure At high concentrations of hydroxide ionsaccumulated in the structure the chemical decompositionof the initial oxide occurs Based on the previous schemeone can understand the reasons for high resistivity of N-123superconductor to chemical interaction with water
The authors of [42] discussed the high corrosion resis-tance of Nd-123 films in the water compared to the filmstructures of Y-123 and Eu-123 which was attributed to thepartial oxygen disorder in the planes of CuO-chains Sucha disorder should occur in Nd-123 due to the presence ofsome amount of Nd3+ ions in the sites nearby to CuO-planesof divalent barium According to the authors that shouldlead to overlapping structural channels for H
2O diffusion
and hence blocking the hydration process However ourdata on the thermal analysis (see Figure 7) illustrate thatthe saturation of Nd-123 structure with water during MAtreatment proceeds almost as fast as in Y-123 (in the rangeof 2ndash10 minutes even faster) Therefore the sought causeof the chemical stability of Nd-123 MP cannot be related toproblems of H
2O diffusion
The stage of removing oxygen from the structure is con-sidered [41 42] to be extremely important for the hydrationprocess of R-123 Thus the chemical degradation of Y-123oxide immersed in the water is completely stopped underpotential of 08 V relative to the standard electrode-saturatedsodium calomel [41] It is expected that the substitutionNd3+ rarr Ba2+ inNd-123 in addition to oxygen disordering inthe base structural plane should also lead to the strengtheningof its bondwith the lattice (due to electrostatic effect of highlycharged Nd3+ ion) [42] According to the authors [42] thisshould inhibit the reduction stage of hydration However it isimportant to consider the fact that the structure ofMP of Nd-123 contains a large amount of weakly bound CO
2 located
near Ba ions (since there is a tendency to the formation ofBaCO
3) therefore localized in the channels of the base plane
[(12) b 0] where also there is water In our opinion just theseCO2particles block channels of oxygen desorption which is
the main reason for the high stability of Nd-123 in relation tothe hydrolysis reaction
5 Conclusion
Thus as a result of mechanical activation treatment thesurface of YBa
2Cu3O6+120575
is covered by products of hydrolysisand carbonization to a considerable depth The chemicaldegradation process proceeds the normal waymdashthrough theformation of Y
2BaCuO
5phase
Chemical degradation of mechanoactivatedNdBa
2Cu3O6+120575
powders under the impact of CO2
isnot directly connected to hydrolysis process as occurs inYBa2Cu3O6+120575
(see reactions (1) and (2)) Carbonizationproceeds homogeneously through the stage of carbondioxide dissolution in the lattice of NdBa
2Cu3O6+120575
In itsturn the presence of CO
2molecules in the structure of
mechanoactivated NdBa2Cu3O6+120575
powders leads to a radicalchange in the mechanism of interaction between the super-conductor and water This mechanism eliminates the normalfor a homologous series of RBa
2Cu3O6+120575
the hydrolysisreaction with the formation of characteristic ldquocolorrdquoR2BaCuO
5phases The rate of chemical decomposition of
mechanically activated NdBa2Cu3O6+120575
by the new mecha-nism (not yet studied) is quite low
12 Journal of Spectroscopy
Mechanical treatment affects the temperature depen-dence of the magnetization of RBa
2Cu3O6+120575
compoundsThere is a significant increase in the paramagnetic and ferro-magnetic contributions to the magnetization with increasingmilling duration The latter leads to near-room-temperaturehysteretic behavior of NdBa
2Cu3O6+120575
samples between ZFCandFC regimes Itmay be due tomagnetic particles ofmecha-noactivated NdBa
2Cu3O6+120575
samples or to the presence ofimpurity phases whose low content or highly disorderedcrystal structures do not allow to observe these phases byX-ray diffraction measurements The mechanical treatmentdoes not have substantial influence on the transition tem-peratures of superconducting phases 119879
119888in the RBa
2Cu3O6+120575
compounds but a wide transition width around 119879119888indicates
that mechanically activated samples contain inhomogeneoussuperconductor phases with different 119879
119888 The broadening
of the superconducting transition in mechanically activatedNdBa
2Cu3O6+120575
samples may be due to redistribution ofcations between Nd- and Ba-sublattice
Finally we note that the high temperature superconduc-tor RBa
2Cu3O6+120575
subjected to mechanical activation cer-tainly has no significant advantages over conventional non-mechanoactivated material but it is obvious that physical-chemical studies of such powders reveal results interestingfrom the point of view of fundamental science
Acknowledgment
This work was supported by Russian Foundation for BasicResearch (Grant no 11-03-00317-a)
References
[1] I E Graboi A R Kaulrsquo and G Yu Metlin ldquoAdvances in scienceand technologyrdquo in Solid State Chemistry pp 3ndash142 VINITIANSSSR Moscow Russia 1989
[2] S Anders M G Blamire F-Im Buchholz et al ldquoEuropeanroadmap on superconductive electronicsmdashstatus and perspec-tivesrdquo Physica C vol 470 no 23-24 pp 2079ndash2126 2010
[3] B Ruck B Oelze R Dittmann et al ldquoMeasurement of thedynamic error rate of a high temperature superconductor rapidsingle flux quantum comparatorrdquo Applied Physics Letters vol72 no 18 pp 2328ndash2330 1998
[4] M W Rupich X Li C Thieme et al ldquoAdvances in secondgeneration high temperature superconducting wire manufac-turing and RampD at American superconductor corporationrdquoSuperconductor Science and Technology vol 23 no 1 Article ID014015 2010
[5] A Rakitin M Kobayashi and A P Litvinchuk ldquoSuperi-onic behavior of high-temperature superconductorsrdquo PhysicalReview B vol 55 no 1 pp 89ndash92 1997
[6] T Kagiyama J Shimoyama K D Otzschi et al ldquoEffect of cationcomposition and oxygen nonstoichiometry on 119869
119888-119861 properties
of Nd123rdquo Physica C vol 341ndash348 no 2 pp 1445ndash1446 2000
[7] M Badaye J G Wen K Fukushima et al ldquoSuperior propertiesof NdBa
2Cu3O119910over YBa
2Cu3O119909thin filmsrdquo Superconductor
Science and Technology vol 10 no 11 pp 825ndash830 1997
[8] C Cantoni D P Norton D M Kroeger et al ldquoPhase stabilityfor the in situ growth of Nd
1+119909Ba2minus119909
Cu3O119910films using pulsed-
laser depositionrdquo Applied Physics Letters vol 74 no 1 pp 96ndash98 1999
[9] E A Goodilin N N Oleynikov E V Antipov et al ldquoPhasestability for the in situ growth of Nd
1+119909Ba2minus119909
Cu3O119910films using
pulsed-laser depositionrdquo Physica C vol 272 6578 pages 1996[10] E Guilmeau F Giovannelli I Monot-Laffez S Marinel J
Provost and G Desgardin ldquoTop seeding melt texture growthof NdBaCuO pellets in airrdquoThe European Physical Journal vol13 no 3 pp 157ndash160 2001
[11] A I Ancharov T F Grigorrsquoeva T Yu Kiseleva A A Novakovaet al inMechanocomposites-Precursorsfor the Creation of Mate-rials with New Properties O I Lomovskii Ed p 424 Izd-voSO RAN Novosibirsk Russia 2010
[12] A Hamrita F Ben Azzouz A Madani and M Ben SalemldquoMagnetoresistivity and microstructure of YBa
2Cu3O119910pre-
pared using planetary ball millingrdquo Physica C vol 472 no 1pp 34ndash38 2012
[13] R P Vasquez ldquoIntrinsic photoemission signals surface prepa-ration and surface stability of high temperature superconduc-torsrdquo Journal of Electron Spectroscopy and Related Phenomenavol 66 no 3-4 pp 209ndash222 1994
[14] S S Gorelik L N Rastorguev and A Yu Skakov in Rentgeno-graphIcheskII I ElektronographIcheskII AnalIz p 368 Izd-voMetallurgia Moscow Russia 1970
[15] M V Reshetniak and O V Sobol Program for diffractionanalysis ldquoNew Profilerdquo(Last update 10 02 2007) Version 3 4400 (Freeware) WIN9xMENT2KXP Copyright (c) 1992-2007 ReMax SoftWare 2000
[16] M Wegmann L Watson and A Hendry ldquoXPS analysis of sub-micrometer barium titanate powderrdquo Journal of the AmericanCeramic Society vol 87 no 3 pp 371ndash377 2004
[17] A B Christie J Lee I Sutherland and J M Walls ldquoAn XPSstudy of ion-induced compositional changes with group II andgroup IV compoundsrdquo Applications of Surface Science vol 15no 1ndash4 pp 224ndash237 1983
[18] U A Joshi S Yoon S Balk and J S Lee ldquoSurfactant-freehydrothermal synthesis of highly tetragonal barium titanatenanowires a structural investigationrdquo Journal of Physical Chem-istry B vol 110 no 25 pp 12249ndash12256 2006
[19] R Caracciolo ldquoChemical characterization techniques for thinfilmsrdquo in Ceramic Films and Coatings J B Wachtman and R AHaber Eds p 376 New Jersey NJ USA 1992
[20] I N Shabanova Y A Naimushina and N S Terebova ldquoCom-position and temperature dependence of a Y-Ba-Cu-O HTSCelectronic structurerdquo Superconductor Science and Technologyvol 15 no 7 pp 1030ndash1033 2002
[21] J Beyer T Schurig S Menkel Z Quan and H Koch ldquoXPSinvestigation of the surface composition of sputtered YBCOthin filmsrdquo Physica C vol 246 no 1-2 pp 156ndash162 1995
[22] C C Chang M S Hegde X D Wu et al ldquoSurface layers onsuperconducting Y-Ba-Cu-O films studied with x-ray photo-electron spectroscopyrdquo Applied Physics Letters vol 55 no 16pp 1680ndash1682 1989
[23] X D Wu A Inam M S Hegde et al ldquoCrystalline perfectionof as-deposited high-Tc superconducting thin-film surfacesion channeling and x-ray photoelectron spectroscopy studyrdquoPhysical Review B vol 38 no 13 pp 9307ndash9310 1988
[24] P Rajasekar P Chakraborty S K Bandyopadhyay P Barat andP Sen ldquoX-ray photoelectron spectroscopy study of oxygen and
Journal of Spectroscopy 13
argon annealed YBa22Cu3O7minus120575
rdquo Modern Physics Letters B vol12 no 6-7 pp 239ndash245 1998
[25] J Halbritter P Walk H J Mathes B Haeuser and H RogallaldquoARXPS-studies of c-axis textured YBa
2Cu3O119909-filmsrdquo Physica
C vol 153ndash155 no 1 pp 127ndash128 1988[26] T J Sarapatka and P Mikusık ldquoXPS study of PbYBaCuO thin-
film tunnel contactrdquo Applied Surface Science vol 68 no 1 pp35ndash40 1993
[27] J A T Verhoeven and H Van Doveren ldquoAn XPS investigationof the interaction of CH
4 C2H2 C2H4and C
2H6with a barium
surfacerdquo Surface Science vol 123 no 2-3 pp 369ndash383 1982[28] C D Wagner W M Riggs L E Davis J F Moulder and G
E Mullenberg Handbook of X-Ray Photoelectron SpectroscopyPerkin-Elmer Corp Eden Prairie Minn USA 1979
[29] M C Biesinger L W M Lau A R Gerson and R S C SmartldquoResolving surface chemical states in XPS analysis of first rowtransition metals oxides and hydroxides Sc Ti V Cu and ZnrdquoApplied Surface Science vol 257 no 3 pp 887ndash898 2010
[30] X Y Fan Z GWu P X Yan et al ldquoFabrication of well-orderedCuO nanowire arrays by direct oxidation of sputter-depositedCu3N filmrdquo Materials Letters vol 62 no 12-13 pp 1805ndash1808
2008[31] S J Kerber J J Bruckner K Wozniak S Seal S Hardcastle
and T L Barr ldquoNature of hydrogen in x-ray photoelectronspectroscopy general patterns from hydroxides to hydrogenbondingrdquo Journal of Vacuum Science and Technology A vol 14no 3 pp 1314ndash1320 1996
[32] G Moretti G Fierro M Lo Jacono and P Porta ldquoCharac-terization of CuO-ZnO catalysts by X-ray photoelectron spec-troscopy precursors calcined and reduced samplesrdquo Surfaceand Interface Analysis vol 14 no 6-7 pp 325ndash336 1989
[33] H Van Doveren and J A T H Verhoeven ldquoXPS spectra of CaSr Ba and their oxidesrdquo Journal of Electron Spectroscopy andRelated Phenomena vol 21 no 3 pp 265ndash273 1980
[34] B V Crist Handbooks of Monochromatic XPS Spectra Volume2mdashCommercially pure binary oxides XPS International LLCLeona Tex USA 2005
[35] D D Sarma and C N R Rao ldquoXPES studies of oxides ofsecond- and third-row transition metals including rare earthsrdquoJournal of Electron Spectroscopy and Related Phenomena vol 20no 1 pp 25ndash45 1980
[36] V I Nefedov and A N Sokolov ldquoDegradatzia visokotemper-aturnich sverchprovodnikov pri khimicheskich vozdeistviachrdquoZhurnal Neorganicheskoi Khimii vol 34 no 11 pp 2723ndash27391989
[37] Y Uwamino T Ishizuka and H Yamatera ldquoX-ray photoelec-tron spectroscopy of rare-earth compoundsrdquo Journal of ElectronSpectroscopy and Related Phenomena vol 34 no 1 pp 67ndash781984
[38] M P Seah and W A Dench ldquoQuantitative electron spec-troscopy of surfaces a standard data base for electron inelasticmean free paths in solidsrdquo Surface and Interface Analysis vol 1no 1 pp 2ndash11 1979
[39] C H Lin H C I Kao and C M Wang ldquoKinetics andstability of R(Ba
15Sr05)Cu3O119910(R = La Nd Sm Eu Gd Dy Ho)
superconductors inwaterrdquoMaterials Chemistry and Physics vol82 no 2 pp 435ndash439 2003
[40] A G Knizhnik R A Stukan and G O Eremenko ldquoStudy theinteraction between europium HTSC of 123 type and waterrdquoSverkhprovodimost vol 4 no 1 pp 177ndash182 1991 (Russian)
[41] J Zhou R K Lo J T McDevitt et al ldquoDevelopment of areliable materials base for superconducting electronicsrdquo Journalof Materials Research vol 12 no 11 pp 2958ndash2975 1997
[42] S B Schougaard M F Ali and J T McDevitt ldquoEvidence forhigh stability against water corrosion of NdBa
2Cu3O7plusmn120575
relativeto YBa
2Cu3OO7minus120575
and EuBa2Cu3OO7minus120575
rdquo Applied Physics Let-ters vol 84 no 7 pp 1144ndash1146 2004
Submit your manuscripts athttpwwwhindawicom
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Inorganic ChemistryInternational Journal of
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Analytical ChemistryInternational Journal of
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CatalystsJournal of
6 Journal of Spectroscopy
Ba 3d
Y-10
Y-2
Y-05
Y-0
776 780 784 788 792 796 800Binding energy (eV)
3d523d32
(a)
Binding energy (eV)
Y 3d
Y-10
Y-2
Y-05
Y-0
150 152 154 156 158 160 162 164 166
(b)
Cu 2p
Y-10 Satellite I Satellite II
Y-2
Y-05
Y-0
930 940 950 960 970Binding energy (eV)
2p32
2p12
(c)
Figure 3 XPS spectra of YBa2Cu3O6+120575
powders Dark shading the main phase signal light shading Y2BaCuO
5signal
Table 2 The positions of the characteristic XPS lines of barium compounds
Electron orbital BaCO3 Ba(OH)2 Y-123 Y2BaCuO
5
Binding energy eV
Ba 3d52
7799 [16 17]7798lowast
7813 plusmn 01[18 19]
7777 plusmn 01[20ndash23] 7819lowast
Ba 4d52 893lowast 875
[22]
Y 3d52
1560 plusmn 02[21 24 25] 1587lowast
Cu 2p32
9335[21 26] 9356lowast
O 1s5314 plusmn 01[16 17]5314lowast
5312 qB[27]
52845 plusmn 005 qB[20ndash23] (5291 5313)lowast
C 1s28925 plusmn 015 qB
[16 17]2894lowast
lowastOur data
(line Y 3d52
at 1560 eV in the spectrum of IP) and the phaseY2(C2O4)3[37] (line Y 3d
52at 1601 eV) The presence of
Y2BaCuO
5compound in samples is also reflected in the
spectra of Cu 2p a high-energy doublet (main peak at9356 eV) corresponds to it At the same time the low-energyCu 2p-doublet parameters are close to those found in [22] forY-123 the main peak at 9335 eV a satellite at sim943 eV as wellas parameters relating to copper oxide Cu (II) [28] 9336 eVand 9425 eV respectively However from the analysis of thespectra of Ba 3d and Y 3d (see earlier) it can be argued that
the Cu 2p signal from the phase of Y-123 may be only in thespectrum of IP samples
Thus in addition to the main phase the surface of IPcontains the final products of the reactions (1) + (2) and Y
2O3
phase probably sourced by the initial precursor incompletelyconsumed during the synthesis of YBa
2Cu3O6+120575
As a resultof MA treatment the surface of the powder is covered with alayer of yttriumoxide and the products of reactions (1) + (2) toa considerable depth of at least 10 nm (judging by the amountof Y2BaCuO
5phase in the samples determined by XRD)
Journal of Spectroscopy 7
323 XPS Study of NdBa2Cu3O6+120575
Oxide Figure 4 demon-strates the survey spectra of Nd-123 powders One can seethat as in the case of Y-123 samples the signal representingthe iron was not observed for any intensive milling durationThe feature of Nd-123 samples is rather low intensity of the Ba3d and Ba 4d peaks for powders activated for 05 and 2min(compare Figure 4 with Figure 2 for Y-123 powder) Bariumpeaks has markedly increased (as well as oxygen O 1s peak)only at 10min of activation
Figure 5 shows the high-resolution spectra of the elec-tronic levels of barium (3d and 4d) neodymium (4d) andcopper (2p) in powders with different activation prehistoryIn the barium spectra the high-intensity peaks at 7799 eV(3d52
) and 893 eV (4d52
) are obviously responsible for thecompound BaCO
3 and the low-intensity peaks at 7780 and
876 eV which are observed only in IP samples (dark shadedin Figure 5) correspond to the main phase by analogy withY-123 samples The analysis of Cu 2p spectra has revealed thepresence of copper ions with the electronic structure similarto that in Y-123 or in CuO oxide
However as seen in Figure 5 the state Cu 2p with highbinding energy (9359 plusmn 03 eV) is also present in all Nd-123samples According to our data (see Table 3) this state is nottypical for simple and ternary compounds of copper DuringMA processing its share in Cu 2p spectra changes in strictaccordancewith the high energy components of the Ba 3d andBa 4d spectra light shaded in Figure 5 (at 7817 eV (Ba 3d
53)
and 919 plusmn 03 eV (Ba 4d53
)) which implies that a doubleoxide of barium-copper was on the surface of the samplesWe tend to identify this oxide as Ba
2Cu3O5+x phase which
was detected by X-ray diffraction analysis of IP samples (seeTable 1) Despite the fact that this phase was not found byXRD in samples N-05 N-1 and N-2 it is visible in the XPSspectra due to the effect of spatial localization
According to Figure 5 the surface of the samples alsocontained the oxide Nd
2O3(line Nd 4d
52at 1211 eV) which
under intense grinding at the initial stages was partly trans-formed into Nd
2(C2O4)3[37] (line Nd 4d
52at sim1225 eV)
Based on the analysis of possible superpositions of the spectraof Ba 3d Ba 4d and Cu 2p the low-energy Nd 4d doublet(line Nd 4d
52at 1157 eV) the intensity of which is almost
independent of the MA duration belongs to a double oxideNdCu
119910O15+y+z of undetermined composition The Nd 4d
doublet of themain compound apparently overlaps with oneof the previously noted signals and so it is shown explicitlyin Figure 5
On the intensity ratios of the peaks in Figure 5 one canconstruct a model of the relative position of the phases Nd-123 BaCO
3 and Ba
2Cu3O5+x in the surface layer of the
material (this method has been used eg in [22] to analyzethe relative position of the layers Y-123 and BaCuO
2) To
realize this we use the dependence of the layer thicknessanalyzed by XPS (usually taken as 3 sdot 120582
119898) on the kinetic
energy of the electrons [38] referring to the electrons givingthe corresponding lines in the spectra of Ba 3d and Ba 4d asfollows
120582119898= 2170119864
minus2
119896+ 072(119886119864
119896)12 (3)
Ba 3d
N-10Cu 2pN-2Fe 2p
O 1sN-05
N-0Cu LVVCu 3s C 1sNd 4d
Ba 4d200 400 600 800 1000
Binding energy (eV)0
Figure 4 XPS survey spectra of the initial and mechanoactivatedNdBa
2Cu3O6+120575
samples
where 120582119898is the electron mean free path expressed in mono-
layers 119886 is monolayer thickness in nm 119864119896is kinetic energy
in eV (119864119896= ℎ] minus 119864BE minus 120593) ℎ] = 12536 eV is the energy of
the exciting radiation used inXPS analysis119864BE is the bindingenergy of the electronic level under analysis and120593 is theworkfunction of the spectrometer (346 eV)
According to this relationship the thickness of the layerunder analysis increases monotonically with increasing 119864
119896
in the range 119864119896gt 40 eV As can be seen from Figure 6
increase in the thickness of the layer under analysis canaffect the following volume ratios detectable by XPS phaseIphase III and phase IIphase III and has no influence onthe volume relation phase Iphase II The phase fractionto a first approximation is proportional to the area undercorresponding XPS peak Therefore based on the ratio ofareas of the different lines in the spectra in Figure 5 one canconclude that both barium-containing products of chemicaldecomposition of Nd-123 are located atop of the main oxidethat is correspond to phases I and II in Figure 6 The thick-ness of the degraded layer in N-10 sample is sim10 nm (as theoriginal phase is barely visible through it) and in IP (N-0)sample it is estimated to be 5-6 nm
It should be noted however that such a small thicknessof Ba2Cu3O5+x layer in IP has not prevented this phase to be
recognized by XRD analysis (see Table 1) One can thereforeconclude that IP particles contain in addition a considerableamount of Ba
2Cu3O5+x in the form of individual inclusions
in bulk (as a result of this oxide synthesis features seeSection 1) DuringMA processing material particles crackedand inclusions went outside resulting in the fraction ofBa2Cu3O5+x phase on the surface increased up to a point
(up to 1min inclusive) The subsequent decrease in thisphase (see Figure 5) is apparently due to the fact that anotherprocess also developed on the surface during grindingspending of Ba
2Cu3O5+x involving the original solid solution
Nd1+xBa2minusxCu3O6+120575 to formation of cation-stoichiometric
NdBa2Cu3O6+120575
To prove the occurrence of such interaction
8 Journal of Spectroscopy
Ba 3d
N-10
N-2
N-1
N-05
N-0
770 775 780 785 790 795 800 805Binding energy (eV)
(a)
N-10
N-1
Binding energy (eV)
Ba 4d
Ba 4d
N-2
N-05
N-0
68 72 80 84 88 92 96
Cu 3p X-ra
ysa
telli
tes
76
(b)
N-10
N-2
N-1
N-05
N-0
930 940 950 960 970Binding energy (eV)
Satellite I Satellite II
Cu 2p2p32
2p12
(c)
N-10
N-2
N-1
N-05
N-0
110 115 120 125 130 135Binding energy (eV)
Nd 4d
(d)
Figure 5 XPS spectra of NdBa2Cu3O6+120575
powders
119864119896 (Ba 3d) 119864119896 (Ba 4d)
Phase I Phase II
Phase III
Phase I Phase II
Phase III
31205823120582
XPS
study
area
XPS
study
area
lt
Figure 6 Analysis of the mutual arrangement phases in the surface layer of the material and their volume relations from XPS data
Journal of Spectroscopy 9
Table 3 Characteristic spectral parameters of different copper compounds
Electron orbital CuO CuCO3 Cu(OH)2 Cu2CO3(OH)2 Nd2BaCuO5
Binding energy eVBa 3d
527790lowast
Nd 4d52
1182lowast
Cu 2p32
9337 plusmn 1[28ndash30]
9348[28]
93474 plusmn 006[29 31]
9347[32] 9335lowast
O 1s 52974 plusmn 006[30 31]
53124[31] 5286lowast
lowastOur data
later we present the data of magnetic measurements whichindicate that MA treatment results in significant increase inthe temperature of the superconducting transition in separateregions of the material
324 Thermal Analysis of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
Samples of R-123 have been studied by thermogravimetrycoupled withmass-spectrometry to analyze the gases evolvedduring experiments Results of the study are summarizedin Figure 7 It is seen that reversible change in mass of IP-samples occurs in the range of 430ndash900∘C that must be dueto oxygen exchange between nonstoichiometric R-123 oxidesand the gas phase taking place at these temperatures [1] MPsamples start losing mass sharply around 70∘C when heatedMass spectrometry analysis of thermal desorption productsindicates the presence of large amount of water and a smallamount of carbon dioxide contained in the samples in theform of BaCO
3(the temperature range in which the CO
2
was released and the value of 119901CO2used for thermal analysis
of the atmosphere was consistent with conditions of bariumcarbonate decomposition)
325 Study of Magnetic Properties of YBa2Cu3O6+120575
andNdBa
2Cu3O6+120575
Temperature dependences of ZFC magne-tization of the samples Y-0 Y-05 Y-2 and Y-10 are shownin Figure 8 A sharp downturn in magnetization at sim90Kobserved in the samples Y-0 Y-05 and Y-2 clearly showsthe presence of the superconducting phase Superconductingtransition temperatures of the samples Y-0 Y-05 and Y-2have been determined by taking the derivative of the mag-netization against the temperature (119889119898119889119879) Thus definedtemperatures 119879
119888are equal to 91 K for the samples Y-0 and
Y-05 and 88K for the sample Y-2 A wide transition widtharound 119879
119888= 90K indicates that both the initial and MP
samples contain inhomogeneous superconductor phaseswithdifferent 119879
119888 The following facts indicate the presence of
paramagnetic contribution in the magnetization behavior ofMP samples and its growth with increasing milling durationa significant increase in magnetization 119898 of the samples Y-05 and Y-2 compared with the initial sample Y-0 at thetemperatures 119879 gt 119879
119888 weak temperature dependence 119898(119879)
in the temperature range 100ndash300 K for MP samples asignificant increase in themagnetization of Y-10 sample at lowtemperatures
100
99
98
97
96
95
94
93
92
100
99
98
97
96
95
94
93
92
0 200 400 600 800 1000
0 200 400 600 800 1000
14
12
10
8
6
4
3
2
Temperature (∘C)
Ion
curr
ent (
A)
Ion
curr
ent (
A)
Sam
ple w
eigh
t (
)
H2O
CO2
H2O (times1010) CO2 (times1011)
3
2
1
3998400
1998400
2998400
Figure 7 Thermal analysis results for samples Y-0 (1) N-0 (11015840) Y-2 (2) N-2 (21015840) and Y-10 (3) N-10 (31015840) Mass spectrometry data arerelated to the samples Y-10 (solid curves) and N-10 (dashed lines)
For comparison Figure 9 shows the temperature depen-dence of the FC magnetization in a magnetic field 119867 =500Oe for two new samples of Y-123 (120575 asymp 07) The firstsample has been freshly prepared and the other one has beensubjected to treatment at 297 plusmn 1K for 120 h at absolutehumidity of 23 120581Pa The sample with low oxygen content(and as a consequence with low 119879
119888) has been chosen due
to its relatively easy moisture saturation in these conditionswithout the use of MA (moisture saturation was controlledby the increase in weight which eventually was sim4wt)One can see that the sample saturated with water has apositive magnetic moment above the temperature 119879
119888and
shows an increase inmagnetic moment on cooling below this
10 Journal of Spectroscopy
N-0
N-1
N-10N-2
Y-2
Y-05
N-05
Y-0
Y-10
005 0005
0004
0003
0002
0001
0
0
minus005
minus01
minus015
minus02
minus025
minus03
minus01
minus02
minus03
003
002
001
0
0
0minus001
20 40 60 80 100 120 140119879 (K)
119898(e
mu
g)119898
(em
ug)
119898(e
mu
g)119898
(em
ug)
Figure 8 ZFC magnetizations as a function of temperature at119867 = 50Oe for the initial and mechanically activated samplesYBa2Cu3O6+120575
(top) NdBa2Cu3O6+120575
(bottom)
temperature similarly to Y-10 sample Onset temperature ofthe magnetic anomaly in the hydrated sample is the sameas that in the freshly prepared sample This experimentdemonstrates that the presence of water in MP sampleshas a significant effect on the temperature dependences ofthe magnetization observed in samples of Y-123 series (seeFigure 8)
Temperature dependences of ZFC magnetization of MPsamples in Nd-123 series are shown in Figure 8 The super-conducting transition temperatures of the samples N-0 N-05 and N-1 are independent of milling duration and equal to119879119888sim 57KMechanical treatment leads to a substantial change
in the magnetization of MP samples throughout the inves-tigated temperature range MP samples exhibit near-room-temperature hysteretic behavior that is ZFC magnetizationis more diamagnetic than FCmagnetization It may be due tomagnetic particles of mechanoactivatedNd-123 samples or tothe presence of impurity phases whose low content or highlydisordered crystal structures do not allow to observe thesephases by X-ray diffraction measurements We also cannotexclude the formation of CuO phase (119879
119873sim 220K) at the
surface of large NdBa2Cu3O6+120575
particles proceeding undermechanical activationAt the same time a significant increasein the paramagnetic contribution to the magnetization withincreasing milling duration is observed
004
002
0
minus002
minus004
minus006
minus0080 20 40 60 80 100 120 140
0 20 40 60 80 100 120 140
119898(e
mu)
119898(e
mu)
119879 (K)
119879 (K)
004
0038
0036
0034
Figure 9 FCmagnetizations as a function of temperature of freshlyprepared YBa
2Cu3O6+120575
sample (empty points) and of hydrated sam-ple (black points) at119867 = 500Oe Inset the temperature dependenceof magnetization of hydrated sample at119867 = 10 kOe
A wide transition width around 119879119888= 57K (|Δ119879
119888sim 20K|)
in MP samples of Nd-123 series cannot be explained only bythe presence of water in the structure The observed changesindicate that during MA treatment diffusion processes asso-ciated with the ordering of the cations Nd3+ and Ba2+ appa-rently occur according to [8ndash10] that has a significant effecton 119879119888
4 Discussion of Results
41 Interaction of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
withCO2 From comparison of Figures 4 and 5 it is clear that with
increasing duration of MA processing (120591119892) the amount of
barium-containing impurities on the surface of Nd-123 sam-ples continuously increases up to 120591
119892= 10min in contrast
to the situation for the oxide Y-123 for which initially (up120591119892= 05min) sudden change and subsequent (after 120591
119892=
05min) almost stagnation in the accumulation of chemicaldegradation products were observed (see Figures 2 and 3 anddata on the impurities in YBa
2Cu3O6+120575
sample) One can seefrom Figure 7 that the degree of water saturation (120578) of bothoxides (this parameter can be traced by sharp descendingbranch of sample mass change in the temperature range of30ndash450∘C) obeys similar relationships with increasing 120591
119892 its
growth with increasing MA duration close to proportionalfor Nd-123 (120578 sim 120591
119892) and tendency of 120578 to decrease for Y-123
(120578 = 155 sdot 120591119892
03) which is close to the root dependence char-
acteristic of reagent diffusion through the reaction productslayer
Taking into account the data in [1] stating the chemicaldegradation of Y-123 is carried out on the interface betweenY-123 and gas phase and one can explain sharply fallingrates of change in concentration of its products as well as ofH2O dissolved in the oxide the diffusion path length of H
2O
and CO2reactants to the location of the reactions (1) and
(2) increases with time 120591119892 However the uniformity of the
absorption of H2O and CO
2gases by MP of Nd-123 testifies
Journal of Spectroscopy 11
that the thickness of the degraded layer on the surface variesslightly Apparently it does not exceed 10 nm as indicated bya weak but clear signal of the main phase which appeared inthe Ba 4d-spectrum of N-10 sample (see Figure 5) Howeverit should be noted that Nd-123 MP sample actively entersinto chemical reactionwith atmospheric CO
2 the gas escapes
from the samples quite intensively when heated in the rangeof 800ndash900∘C (see Figure 7) Therefore the question oflocalization place of products of interaction between Nd-123and atmospheric components arises
Homogeneous nucleation and growth of interaction pro-ducts in the volume of Nd
1+xBa2minusxCu3O6+120575 parent phasemaybe the answer This assumption is based on the fact that theproducts of thermal desorption of N-10 sample (see Figure 7)contain weakly bound form of CO
2escaping in a wide tem-
perature range of 200ndash550∘C Obviously it is a form of gasdissolved in the structure Since the carbonization energy ofBa2+ ions is quite high homogeneous nucleation of carbonatephase at a certain concentration (equivactivity) of CO
2in the
structure facilitated by the participation of structural defects(whose concentration should be significant in MP samples)seems quite possible
42 Interaction of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
withWater In the Introductionwe have put links toworks statingthat the crucial feature for the practical application of thesuperconductor Nd-123 is its high resistance to chemicaldegradation under moisture Additional information thatexpands understanding of this feature has been received inour study Thus it is shown (see Figure 7) that a high con-centration of water accumulates in MP samples of Nd-123 indissolved form but the hydrolysis reaction development isquite limited as evidenced by the relatively low temperatureof H2O release from this oxide Moreover the results of
XRD and XPS analyzes have not detected even traces of theternary compound Nd
2BaCuO
5in these samples while it is
the compounds R2BaCuO
5due their characteristic colours
that are indicators of the hydrolysis reaction for the wholefamily of compounds R-123 [1 39 40] Thus if the hydrolysisreaction develops (there is a small peak on H
2O desorption
curve for sample N-10 at sim455∘C that can be attributed tothe chemically bound water) then it proceeds through non-traditional mechanism and with low rate
According to [41] the hydration mechanism for thehomologous series of R-123 compounds is in four stages Atthe initial stage water molecules penetrate into the bulk ofthe crystallites through the structural channels [(12) b 0]located in interspaces between CuO-chains typical for thistype of superconductors At the next stage protons whichare located in the oxygen positions of CuO-chains can besplit up of watermoleculesThis proton transfer is consideredto cause an internal (within the [CundashO]+-system) chargetransfer resulting in formation of molecular oxygen leavingthe structure At high concentrations of hydroxide ionsaccumulated in the structure the chemical decompositionof the initial oxide occurs Based on the previous schemeone can understand the reasons for high resistivity of N-123superconductor to chemical interaction with water
The authors of [42] discussed the high corrosion resis-tance of Nd-123 films in the water compared to the filmstructures of Y-123 and Eu-123 which was attributed to thepartial oxygen disorder in the planes of CuO-chains Sucha disorder should occur in Nd-123 due to the presence ofsome amount of Nd3+ ions in the sites nearby to CuO-planesof divalent barium According to the authors that shouldlead to overlapping structural channels for H
2O diffusion
and hence blocking the hydration process However ourdata on the thermal analysis (see Figure 7) illustrate thatthe saturation of Nd-123 structure with water during MAtreatment proceeds almost as fast as in Y-123 (in the rangeof 2ndash10 minutes even faster) Therefore the sought causeof the chemical stability of Nd-123 MP cannot be related toproblems of H
2O diffusion
The stage of removing oxygen from the structure is con-sidered [41 42] to be extremely important for the hydrationprocess of R-123 Thus the chemical degradation of Y-123oxide immersed in the water is completely stopped underpotential of 08 V relative to the standard electrode-saturatedsodium calomel [41] It is expected that the substitutionNd3+ rarr Ba2+ inNd-123 in addition to oxygen disordering inthe base structural plane should also lead to the strengtheningof its bondwith the lattice (due to electrostatic effect of highlycharged Nd3+ ion) [42] According to the authors [42] thisshould inhibit the reduction stage of hydration However it isimportant to consider the fact that the structure ofMP of Nd-123 contains a large amount of weakly bound CO
2 located
near Ba ions (since there is a tendency to the formation ofBaCO
3) therefore localized in the channels of the base plane
[(12) b 0] where also there is water In our opinion just theseCO2particles block channels of oxygen desorption which is
the main reason for the high stability of Nd-123 in relation tothe hydrolysis reaction
5 Conclusion
Thus as a result of mechanical activation treatment thesurface of YBa
2Cu3O6+120575
is covered by products of hydrolysisand carbonization to a considerable depth The chemicaldegradation process proceeds the normal waymdashthrough theformation of Y
2BaCuO
5phase
Chemical degradation of mechanoactivatedNdBa
2Cu3O6+120575
powders under the impact of CO2
isnot directly connected to hydrolysis process as occurs inYBa2Cu3O6+120575
(see reactions (1) and (2)) Carbonizationproceeds homogeneously through the stage of carbondioxide dissolution in the lattice of NdBa
2Cu3O6+120575
In itsturn the presence of CO
2molecules in the structure of
mechanoactivated NdBa2Cu3O6+120575
powders leads to a radicalchange in the mechanism of interaction between the super-conductor and water This mechanism eliminates the normalfor a homologous series of RBa
2Cu3O6+120575
the hydrolysisreaction with the formation of characteristic ldquocolorrdquoR2BaCuO
5phases The rate of chemical decomposition of
mechanically activated NdBa2Cu3O6+120575
by the new mecha-nism (not yet studied) is quite low
12 Journal of Spectroscopy
Mechanical treatment affects the temperature depen-dence of the magnetization of RBa
2Cu3O6+120575
compoundsThere is a significant increase in the paramagnetic and ferro-magnetic contributions to the magnetization with increasingmilling duration The latter leads to near-room-temperaturehysteretic behavior of NdBa
2Cu3O6+120575
samples between ZFCandFC regimes Itmay be due tomagnetic particles ofmecha-noactivated NdBa
2Cu3O6+120575
samples or to the presence ofimpurity phases whose low content or highly disorderedcrystal structures do not allow to observe these phases byX-ray diffraction measurements The mechanical treatmentdoes not have substantial influence on the transition tem-peratures of superconducting phases 119879
119888in the RBa
2Cu3O6+120575
compounds but a wide transition width around 119879119888indicates
that mechanically activated samples contain inhomogeneoussuperconductor phases with different 119879
119888 The broadening
of the superconducting transition in mechanically activatedNdBa
2Cu3O6+120575
samples may be due to redistribution ofcations between Nd- and Ba-sublattice
Finally we note that the high temperature superconduc-tor RBa
2Cu3O6+120575
subjected to mechanical activation cer-tainly has no significant advantages over conventional non-mechanoactivated material but it is obvious that physical-chemical studies of such powders reveal results interestingfrom the point of view of fundamental science
Acknowledgment
This work was supported by Russian Foundation for BasicResearch (Grant no 11-03-00317-a)
References
[1] I E Graboi A R Kaulrsquo and G Yu Metlin ldquoAdvances in scienceand technologyrdquo in Solid State Chemistry pp 3ndash142 VINITIANSSSR Moscow Russia 1989
[2] S Anders M G Blamire F-Im Buchholz et al ldquoEuropeanroadmap on superconductive electronicsmdashstatus and perspec-tivesrdquo Physica C vol 470 no 23-24 pp 2079ndash2126 2010
[3] B Ruck B Oelze R Dittmann et al ldquoMeasurement of thedynamic error rate of a high temperature superconductor rapidsingle flux quantum comparatorrdquo Applied Physics Letters vol72 no 18 pp 2328ndash2330 1998
[4] M W Rupich X Li C Thieme et al ldquoAdvances in secondgeneration high temperature superconducting wire manufac-turing and RampD at American superconductor corporationrdquoSuperconductor Science and Technology vol 23 no 1 Article ID014015 2010
[5] A Rakitin M Kobayashi and A P Litvinchuk ldquoSuperi-onic behavior of high-temperature superconductorsrdquo PhysicalReview B vol 55 no 1 pp 89ndash92 1997
[6] T Kagiyama J Shimoyama K D Otzschi et al ldquoEffect of cationcomposition and oxygen nonstoichiometry on 119869
119888-119861 properties
of Nd123rdquo Physica C vol 341ndash348 no 2 pp 1445ndash1446 2000
[7] M Badaye J G Wen K Fukushima et al ldquoSuperior propertiesof NdBa
2Cu3O119910over YBa
2Cu3O119909thin filmsrdquo Superconductor
Science and Technology vol 10 no 11 pp 825ndash830 1997
[8] C Cantoni D P Norton D M Kroeger et al ldquoPhase stabilityfor the in situ growth of Nd
1+119909Ba2minus119909
Cu3O119910films using pulsed-
laser depositionrdquo Applied Physics Letters vol 74 no 1 pp 96ndash98 1999
[9] E A Goodilin N N Oleynikov E V Antipov et al ldquoPhasestability for the in situ growth of Nd
1+119909Ba2minus119909
Cu3O119910films using
pulsed-laser depositionrdquo Physica C vol 272 6578 pages 1996[10] E Guilmeau F Giovannelli I Monot-Laffez S Marinel J
Provost and G Desgardin ldquoTop seeding melt texture growthof NdBaCuO pellets in airrdquoThe European Physical Journal vol13 no 3 pp 157ndash160 2001
[11] A I Ancharov T F Grigorrsquoeva T Yu Kiseleva A A Novakovaet al inMechanocomposites-Precursorsfor the Creation of Mate-rials with New Properties O I Lomovskii Ed p 424 Izd-voSO RAN Novosibirsk Russia 2010
[12] A Hamrita F Ben Azzouz A Madani and M Ben SalemldquoMagnetoresistivity and microstructure of YBa
2Cu3O119910pre-
pared using planetary ball millingrdquo Physica C vol 472 no 1pp 34ndash38 2012
[13] R P Vasquez ldquoIntrinsic photoemission signals surface prepa-ration and surface stability of high temperature superconduc-torsrdquo Journal of Electron Spectroscopy and Related Phenomenavol 66 no 3-4 pp 209ndash222 1994
[14] S S Gorelik L N Rastorguev and A Yu Skakov in Rentgeno-graphIcheskII I ElektronographIcheskII AnalIz p 368 Izd-voMetallurgia Moscow Russia 1970
[15] M V Reshetniak and O V Sobol Program for diffractionanalysis ldquoNew Profilerdquo(Last update 10 02 2007) Version 3 4400 (Freeware) WIN9xMENT2KXP Copyright (c) 1992-2007 ReMax SoftWare 2000
[16] M Wegmann L Watson and A Hendry ldquoXPS analysis of sub-micrometer barium titanate powderrdquo Journal of the AmericanCeramic Society vol 87 no 3 pp 371ndash377 2004
[17] A B Christie J Lee I Sutherland and J M Walls ldquoAn XPSstudy of ion-induced compositional changes with group II andgroup IV compoundsrdquo Applications of Surface Science vol 15no 1ndash4 pp 224ndash237 1983
[18] U A Joshi S Yoon S Balk and J S Lee ldquoSurfactant-freehydrothermal synthesis of highly tetragonal barium titanatenanowires a structural investigationrdquo Journal of Physical Chem-istry B vol 110 no 25 pp 12249ndash12256 2006
[19] R Caracciolo ldquoChemical characterization techniques for thinfilmsrdquo in Ceramic Films and Coatings J B Wachtman and R AHaber Eds p 376 New Jersey NJ USA 1992
[20] I N Shabanova Y A Naimushina and N S Terebova ldquoCom-position and temperature dependence of a Y-Ba-Cu-O HTSCelectronic structurerdquo Superconductor Science and Technologyvol 15 no 7 pp 1030ndash1033 2002
[21] J Beyer T Schurig S Menkel Z Quan and H Koch ldquoXPSinvestigation of the surface composition of sputtered YBCOthin filmsrdquo Physica C vol 246 no 1-2 pp 156ndash162 1995
[22] C C Chang M S Hegde X D Wu et al ldquoSurface layers onsuperconducting Y-Ba-Cu-O films studied with x-ray photo-electron spectroscopyrdquo Applied Physics Letters vol 55 no 16pp 1680ndash1682 1989
[23] X D Wu A Inam M S Hegde et al ldquoCrystalline perfectionof as-deposited high-Tc superconducting thin-film surfacesion channeling and x-ray photoelectron spectroscopy studyrdquoPhysical Review B vol 38 no 13 pp 9307ndash9310 1988
[24] P Rajasekar P Chakraborty S K Bandyopadhyay P Barat andP Sen ldquoX-ray photoelectron spectroscopy study of oxygen and
Journal of Spectroscopy 13
argon annealed YBa22Cu3O7minus120575
rdquo Modern Physics Letters B vol12 no 6-7 pp 239ndash245 1998
[25] J Halbritter P Walk H J Mathes B Haeuser and H RogallaldquoARXPS-studies of c-axis textured YBa
2Cu3O119909-filmsrdquo Physica
C vol 153ndash155 no 1 pp 127ndash128 1988[26] T J Sarapatka and P Mikusık ldquoXPS study of PbYBaCuO thin-
film tunnel contactrdquo Applied Surface Science vol 68 no 1 pp35ndash40 1993
[27] J A T Verhoeven and H Van Doveren ldquoAn XPS investigationof the interaction of CH
4 C2H2 C2H4and C
2H6with a barium
surfacerdquo Surface Science vol 123 no 2-3 pp 369ndash383 1982[28] C D Wagner W M Riggs L E Davis J F Moulder and G
E Mullenberg Handbook of X-Ray Photoelectron SpectroscopyPerkin-Elmer Corp Eden Prairie Minn USA 1979
[29] M C Biesinger L W M Lau A R Gerson and R S C SmartldquoResolving surface chemical states in XPS analysis of first rowtransition metals oxides and hydroxides Sc Ti V Cu and ZnrdquoApplied Surface Science vol 257 no 3 pp 887ndash898 2010
[30] X Y Fan Z GWu P X Yan et al ldquoFabrication of well-orderedCuO nanowire arrays by direct oxidation of sputter-depositedCu3N filmrdquo Materials Letters vol 62 no 12-13 pp 1805ndash1808
2008[31] S J Kerber J J Bruckner K Wozniak S Seal S Hardcastle
and T L Barr ldquoNature of hydrogen in x-ray photoelectronspectroscopy general patterns from hydroxides to hydrogenbondingrdquo Journal of Vacuum Science and Technology A vol 14no 3 pp 1314ndash1320 1996
[32] G Moretti G Fierro M Lo Jacono and P Porta ldquoCharac-terization of CuO-ZnO catalysts by X-ray photoelectron spec-troscopy precursors calcined and reduced samplesrdquo Surfaceand Interface Analysis vol 14 no 6-7 pp 325ndash336 1989
[33] H Van Doveren and J A T H Verhoeven ldquoXPS spectra of CaSr Ba and their oxidesrdquo Journal of Electron Spectroscopy andRelated Phenomena vol 21 no 3 pp 265ndash273 1980
[34] B V Crist Handbooks of Monochromatic XPS Spectra Volume2mdashCommercially pure binary oxides XPS International LLCLeona Tex USA 2005
[35] D D Sarma and C N R Rao ldquoXPES studies of oxides ofsecond- and third-row transition metals including rare earthsrdquoJournal of Electron Spectroscopy and Related Phenomena vol 20no 1 pp 25ndash45 1980
[36] V I Nefedov and A N Sokolov ldquoDegradatzia visokotemper-aturnich sverchprovodnikov pri khimicheskich vozdeistviachrdquoZhurnal Neorganicheskoi Khimii vol 34 no 11 pp 2723ndash27391989
[37] Y Uwamino T Ishizuka and H Yamatera ldquoX-ray photoelec-tron spectroscopy of rare-earth compoundsrdquo Journal of ElectronSpectroscopy and Related Phenomena vol 34 no 1 pp 67ndash781984
[38] M P Seah and W A Dench ldquoQuantitative electron spec-troscopy of surfaces a standard data base for electron inelasticmean free paths in solidsrdquo Surface and Interface Analysis vol 1no 1 pp 2ndash11 1979
[39] C H Lin H C I Kao and C M Wang ldquoKinetics andstability of R(Ba
15Sr05)Cu3O119910(R = La Nd Sm Eu Gd Dy Ho)
superconductors inwaterrdquoMaterials Chemistry and Physics vol82 no 2 pp 435ndash439 2003
[40] A G Knizhnik R A Stukan and G O Eremenko ldquoStudy theinteraction between europium HTSC of 123 type and waterrdquoSverkhprovodimost vol 4 no 1 pp 177ndash182 1991 (Russian)
[41] J Zhou R K Lo J T McDevitt et al ldquoDevelopment of areliable materials base for superconducting electronicsrdquo Journalof Materials Research vol 12 no 11 pp 2958ndash2975 1997
[42] S B Schougaard M F Ali and J T McDevitt ldquoEvidence forhigh stability against water corrosion of NdBa
2Cu3O7plusmn120575
relativeto YBa
2Cu3OO7minus120575
and EuBa2Cu3OO7minus120575
rdquo Applied Physics Let-ters vol 84 no 7 pp 1144ndash1146 2004
Submit your manuscripts athttpwwwhindawicom
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Inorganic ChemistryInternational Journal of
Hindawi Publishing Corporation httpwwwhindawicom Volume 2014
International Journal ofPhotoenergy
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Carbohydrate Chemistry
International Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Advances in
Physical Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom
Analytical Methods in Chemistry
Journal of
Volume 2014
Bioinorganic Chemistry and ApplicationsHindawi Publishing Corporationhttpwwwhindawicom Volume 2014
SpectroscopyInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
The Scientific World JournalHindawi Publishing Corporation httpwwwhindawicom Volume 2014
Medicinal ChemistryInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Chromatography Research International
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Applied ChemistryJournal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Theoretical ChemistryJournal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Spectroscopy
Analytical ChemistryInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Quantum Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Organic Chemistry International
ElectrochemistryInternational Journal of
Hindawi Publishing Corporation httpwwwhindawicom Volume 2014
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
CatalystsJournal of
Journal of Spectroscopy 7
323 XPS Study of NdBa2Cu3O6+120575
Oxide Figure 4 demon-strates the survey spectra of Nd-123 powders One can seethat as in the case of Y-123 samples the signal representingthe iron was not observed for any intensive milling durationThe feature of Nd-123 samples is rather low intensity of the Ba3d and Ba 4d peaks for powders activated for 05 and 2min(compare Figure 4 with Figure 2 for Y-123 powder) Bariumpeaks has markedly increased (as well as oxygen O 1s peak)only at 10min of activation
Figure 5 shows the high-resolution spectra of the elec-tronic levels of barium (3d and 4d) neodymium (4d) andcopper (2p) in powders with different activation prehistoryIn the barium spectra the high-intensity peaks at 7799 eV(3d52
) and 893 eV (4d52
) are obviously responsible for thecompound BaCO
3 and the low-intensity peaks at 7780 and
876 eV which are observed only in IP samples (dark shadedin Figure 5) correspond to the main phase by analogy withY-123 samples The analysis of Cu 2p spectra has revealed thepresence of copper ions with the electronic structure similarto that in Y-123 or in CuO oxide
However as seen in Figure 5 the state Cu 2p with highbinding energy (9359 plusmn 03 eV) is also present in all Nd-123samples According to our data (see Table 3) this state is nottypical for simple and ternary compounds of copper DuringMA processing its share in Cu 2p spectra changes in strictaccordancewith the high energy components of the Ba 3d andBa 4d spectra light shaded in Figure 5 (at 7817 eV (Ba 3d
53)
and 919 plusmn 03 eV (Ba 4d53
)) which implies that a doubleoxide of barium-copper was on the surface of the samplesWe tend to identify this oxide as Ba
2Cu3O5+x phase which
was detected by X-ray diffraction analysis of IP samples (seeTable 1) Despite the fact that this phase was not found byXRD in samples N-05 N-1 and N-2 it is visible in the XPSspectra due to the effect of spatial localization
According to Figure 5 the surface of the samples alsocontained the oxide Nd
2O3(line Nd 4d
52at 1211 eV) which
under intense grinding at the initial stages was partly trans-formed into Nd
2(C2O4)3[37] (line Nd 4d
52at sim1225 eV)
Based on the analysis of possible superpositions of the spectraof Ba 3d Ba 4d and Cu 2p the low-energy Nd 4d doublet(line Nd 4d
52at 1157 eV) the intensity of which is almost
independent of the MA duration belongs to a double oxideNdCu
119910O15+y+z of undetermined composition The Nd 4d
doublet of themain compound apparently overlaps with oneof the previously noted signals and so it is shown explicitlyin Figure 5
On the intensity ratios of the peaks in Figure 5 one canconstruct a model of the relative position of the phases Nd-123 BaCO
3 and Ba
2Cu3O5+x in the surface layer of the
material (this method has been used eg in [22] to analyzethe relative position of the layers Y-123 and BaCuO
2) To
realize this we use the dependence of the layer thicknessanalyzed by XPS (usually taken as 3 sdot 120582
119898) on the kinetic
energy of the electrons [38] referring to the electrons givingthe corresponding lines in the spectra of Ba 3d and Ba 4d asfollows
120582119898= 2170119864
minus2
119896+ 072(119886119864
119896)12 (3)
Ba 3d
N-10Cu 2pN-2Fe 2p
O 1sN-05
N-0Cu LVVCu 3s C 1sNd 4d
Ba 4d200 400 600 800 1000
Binding energy (eV)0
Figure 4 XPS survey spectra of the initial and mechanoactivatedNdBa
2Cu3O6+120575
samples
where 120582119898is the electron mean free path expressed in mono-
layers 119886 is monolayer thickness in nm 119864119896is kinetic energy
in eV (119864119896= ℎ] minus 119864BE minus 120593) ℎ] = 12536 eV is the energy of
the exciting radiation used inXPS analysis119864BE is the bindingenergy of the electronic level under analysis and120593 is theworkfunction of the spectrometer (346 eV)
According to this relationship the thickness of the layerunder analysis increases monotonically with increasing 119864
119896
in the range 119864119896gt 40 eV As can be seen from Figure 6
increase in the thickness of the layer under analysis canaffect the following volume ratios detectable by XPS phaseIphase III and phase IIphase III and has no influence onthe volume relation phase Iphase II The phase fractionto a first approximation is proportional to the area undercorresponding XPS peak Therefore based on the ratio ofareas of the different lines in the spectra in Figure 5 one canconclude that both barium-containing products of chemicaldecomposition of Nd-123 are located atop of the main oxidethat is correspond to phases I and II in Figure 6 The thick-ness of the degraded layer in N-10 sample is sim10 nm (as theoriginal phase is barely visible through it) and in IP (N-0)sample it is estimated to be 5-6 nm
It should be noted however that such a small thicknessof Ba2Cu3O5+x layer in IP has not prevented this phase to be
recognized by XRD analysis (see Table 1) One can thereforeconclude that IP particles contain in addition a considerableamount of Ba
2Cu3O5+x in the form of individual inclusions
in bulk (as a result of this oxide synthesis features seeSection 1) DuringMA processing material particles crackedand inclusions went outside resulting in the fraction ofBa2Cu3O5+x phase on the surface increased up to a point
(up to 1min inclusive) The subsequent decrease in thisphase (see Figure 5) is apparently due to the fact that anotherprocess also developed on the surface during grindingspending of Ba
2Cu3O5+x involving the original solid solution
Nd1+xBa2minusxCu3O6+120575 to formation of cation-stoichiometric
NdBa2Cu3O6+120575
To prove the occurrence of such interaction
8 Journal of Spectroscopy
Ba 3d
N-10
N-2
N-1
N-05
N-0
770 775 780 785 790 795 800 805Binding energy (eV)
(a)
N-10
N-1
Binding energy (eV)
Ba 4d
Ba 4d
N-2
N-05
N-0
68 72 80 84 88 92 96
Cu 3p X-ra
ysa
telli
tes
76
(b)
N-10
N-2
N-1
N-05
N-0
930 940 950 960 970Binding energy (eV)
Satellite I Satellite II
Cu 2p2p32
2p12
(c)
N-10
N-2
N-1
N-05
N-0
110 115 120 125 130 135Binding energy (eV)
Nd 4d
(d)
Figure 5 XPS spectra of NdBa2Cu3O6+120575
powders
119864119896 (Ba 3d) 119864119896 (Ba 4d)
Phase I Phase II
Phase III
Phase I Phase II
Phase III
31205823120582
XPS
study
area
XPS
study
area
lt
Figure 6 Analysis of the mutual arrangement phases in the surface layer of the material and their volume relations from XPS data
Journal of Spectroscopy 9
Table 3 Characteristic spectral parameters of different copper compounds
Electron orbital CuO CuCO3 Cu(OH)2 Cu2CO3(OH)2 Nd2BaCuO5
Binding energy eVBa 3d
527790lowast
Nd 4d52
1182lowast
Cu 2p32
9337 plusmn 1[28ndash30]
9348[28]
93474 plusmn 006[29 31]
9347[32] 9335lowast
O 1s 52974 plusmn 006[30 31]
53124[31] 5286lowast
lowastOur data
later we present the data of magnetic measurements whichindicate that MA treatment results in significant increase inthe temperature of the superconducting transition in separateregions of the material
324 Thermal Analysis of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
Samples of R-123 have been studied by thermogravimetrycoupled withmass-spectrometry to analyze the gases evolvedduring experiments Results of the study are summarizedin Figure 7 It is seen that reversible change in mass of IP-samples occurs in the range of 430ndash900∘C that must be dueto oxygen exchange between nonstoichiometric R-123 oxidesand the gas phase taking place at these temperatures [1] MPsamples start losing mass sharply around 70∘C when heatedMass spectrometry analysis of thermal desorption productsindicates the presence of large amount of water and a smallamount of carbon dioxide contained in the samples in theform of BaCO
3(the temperature range in which the CO
2
was released and the value of 119901CO2used for thermal analysis
of the atmosphere was consistent with conditions of bariumcarbonate decomposition)
325 Study of Magnetic Properties of YBa2Cu3O6+120575
andNdBa
2Cu3O6+120575
Temperature dependences of ZFC magne-tization of the samples Y-0 Y-05 Y-2 and Y-10 are shownin Figure 8 A sharp downturn in magnetization at sim90Kobserved in the samples Y-0 Y-05 and Y-2 clearly showsthe presence of the superconducting phase Superconductingtransition temperatures of the samples Y-0 Y-05 and Y-2have been determined by taking the derivative of the mag-netization against the temperature (119889119898119889119879) Thus definedtemperatures 119879
119888are equal to 91 K for the samples Y-0 and
Y-05 and 88K for the sample Y-2 A wide transition widtharound 119879
119888= 90K indicates that both the initial and MP
samples contain inhomogeneous superconductor phaseswithdifferent 119879
119888 The following facts indicate the presence of
paramagnetic contribution in the magnetization behavior ofMP samples and its growth with increasing milling durationa significant increase in magnetization 119898 of the samples Y-05 and Y-2 compared with the initial sample Y-0 at thetemperatures 119879 gt 119879
119888 weak temperature dependence 119898(119879)
in the temperature range 100ndash300 K for MP samples asignificant increase in themagnetization of Y-10 sample at lowtemperatures
100
99
98
97
96
95
94
93
92
100
99
98
97
96
95
94
93
92
0 200 400 600 800 1000
0 200 400 600 800 1000
14
12
10
8
6
4
3
2
Temperature (∘C)
Ion
curr
ent (
A)
Ion
curr
ent (
A)
Sam
ple w
eigh
t (
)
H2O
CO2
H2O (times1010) CO2 (times1011)
3
2
1
3998400
1998400
2998400
Figure 7 Thermal analysis results for samples Y-0 (1) N-0 (11015840) Y-2 (2) N-2 (21015840) and Y-10 (3) N-10 (31015840) Mass spectrometry data arerelated to the samples Y-10 (solid curves) and N-10 (dashed lines)
For comparison Figure 9 shows the temperature depen-dence of the FC magnetization in a magnetic field 119867 =500Oe for two new samples of Y-123 (120575 asymp 07) The firstsample has been freshly prepared and the other one has beensubjected to treatment at 297 plusmn 1K for 120 h at absolutehumidity of 23 120581Pa The sample with low oxygen content(and as a consequence with low 119879
119888) has been chosen due
to its relatively easy moisture saturation in these conditionswithout the use of MA (moisture saturation was controlledby the increase in weight which eventually was sim4wt)One can see that the sample saturated with water has apositive magnetic moment above the temperature 119879
119888and
shows an increase inmagnetic moment on cooling below this
10 Journal of Spectroscopy
N-0
N-1
N-10N-2
Y-2
Y-05
N-05
Y-0
Y-10
005 0005
0004
0003
0002
0001
0
0
minus005
minus01
minus015
minus02
minus025
minus03
minus01
minus02
minus03
003
002
001
0
0
0minus001
20 40 60 80 100 120 140119879 (K)
119898(e
mu
g)119898
(em
ug)
119898(e
mu
g)119898
(em
ug)
Figure 8 ZFC magnetizations as a function of temperature at119867 = 50Oe for the initial and mechanically activated samplesYBa2Cu3O6+120575
(top) NdBa2Cu3O6+120575
(bottom)
temperature similarly to Y-10 sample Onset temperature ofthe magnetic anomaly in the hydrated sample is the sameas that in the freshly prepared sample This experimentdemonstrates that the presence of water in MP sampleshas a significant effect on the temperature dependences ofthe magnetization observed in samples of Y-123 series (seeFigure 8)
Temperature dependences of ZFC magnetization of MPsamples in Nd-123 series are shown in Figure 8 The super-conducting transition temperatures of the samples N-0 N-05 and N-1 are independent of milling duration and equal to119879119888sim 57KMechanical treatment leads to a substantial change
in the magnetization of MP samples throughout the inves-tigated temperature range MP samples exhibit near-room-temperature hysteretic behavior that is ZFC magnetizationis more diamagnetic than FCmagnetization It may be due tomagnetic particles of mechanoactivatedNd-123 samples or tothe presence of impurity phases whose low content or highlydisordered crystal structures do not allow to observe thesephases by X-ray diffraction measurements We also cannotexclude the formation of CuO phase (119879
119873sim 220K) at the
surface of large NdBa2Cu3O6+120575
particles proceeding undermechanical activationAt the same time a significant increasein the paramagnetic contribution to the magnetization withincreasing milling duration is observed
004
002
0
minus002
minus004
minus006
minus0080 20 40 60 80 100 120 140
0 20 40 60 80 100 120 140
119898(e
mu)
119898(e
mu)
119879 (K)
119879 (K)
004
0038
0036
0034
Figure 9 FCmagnetizations as a function of temperature of freshlyprepared YBa
2Cu3O6+120575
sample (empty points) and of hydrated sam-ple (black points) at119867 = 500Oe Inset the temperature dependenceof magnetization of hydrated sample at119867 = 10 kOe
A wide transition width around 119879119888= 57K (|Δ119879
119888sim 20K|)
in MP samples of Nd-123 series cannot be explained only bythe presence of water in the structure The observed changesindicate that during MA treatment diffusion processes asso-ciated with the ordering of the cations Nd3+ and Ba2+ appa-rently occur according to [8ndash10] that has a significant effecton 119879119888
4 Discussion of Results
41 Interaction of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
withCO2 From comparison of Figures 4 and 5 it is clear that with
increasing duration of MA processing (120591119892) the amount of
barium-containing impurities on the surface of Nd-123 sam-ples continuously increases up to 120591
119892= 10min in contrast
to the situation for the oxide Y-123 for which initially (up120591119892= 05min) sudden change and subsequent (after 120591
119892=
05min) almost stagnation in the accumulation of chemicaldegradation products were observed (see Figures 2 and 3 anddata on the impurities in YBa
2Cu3O6+120575
sample) One can seefrom Figure 7 that the degree of water saturation (120578) of bothoxides (this parameter can be traced by sharp descendingbranch of sample mass change in the temperature range of30ndash450∘C) obeys similar relationships with increasing 120591
119892 its
growth with increasing MA duration close to proportionalfor Nd-123 (120578 sim 120591
119892) and tendency of 120578 to decrease for Y-123
(120578 = 155 sdot 120591119892
03) which is close to the root dependence char-
acteristic of reagent diffusion through the reaction productslayer
Taking into account the data in [1] stating the chemicaldegradation of Y-123 is carried out on the interface betweenY-123 and gas phase and one can explain sharply fallingrates of change in concentration of its products as well as ofH2O dissolved in the oxide the diffusion path length of H
2O
and CO2reactants to the location of the reactions (1) and
(2) increases with time 120591119892 However the uniformity of the
absorption of H2O and CO
2gases by MP of Nd-123 testifies
Journal of Spectroscopy 11
that the thickness of the degraded layer on the surface variesslightly Apparently it does not exceed 10 nm as indicated bya weak but clear signal of the main phase which appeared inthe Ba 4d-spectrum of N-10 sample (see Figure 5) Howeverit should be noted that Nd-123 MP sample actively entersinto chemical reactionwith atmospheric CO
2 the gas escapes
from the samples quite intensively when heated in the rangeof 800ndash900∘C (see Figure 7) Therefore the question oflocalization place of products of interaction between Nd-123and atmospheric components arises
Homogeneous nucleation and growth of interaction pro-ducts in the volume of Nd
1+xBa2minusxCu3O6+120575 parent phasemaybe the answer This assumption is based on the fact that theproducts of thermal desorption of N-10 sample (see Figure 7)contain weakly bound form of CO
2escaping in a wide tem-
perature range of 200ndash550∘C Obviously it is a form of gasdissolved in the structure Since the carbonization energy ofBa2+ ions is quite high homogeneous nucleation of carbonatephase at a certain concentration (equivactivity) of CO
2in the
structure facilitated by the participation of structural defects(whose concentration should be significant in MP samples)seems quite possible
42 Interaction of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
withWater In the Introductionwe have put links toworks statingthat the crucial feature for the practical application of thesuperconductor Nd-123 is its high resistance to chemicaldegradation under moisture Additional information thatexpands understanding of this feature has been received inour study Thus it is shown (see Figure 7) that a high con-centration of water accumulates in MP samples of Nd-123 indissolved form but the hydrolysis reaction development isquite limited as evidenced by the relatively low temperatureof H2O release from this oxide Moreover the results of
XRD and XPS analyzes have not detected even traces of theternary compound Nd
2BaCuO
5in these samples while it is
the compounds R2BaCuO
5due their characteristic colours
that are indicators of the hydrolysis reaction for the wholefamily of compounds R-123 [1 39 40] Thus if the hydrolysisreaction develops (there is a small peak on H
2O desorption
curve for sample N-10 at sim455∘C that can be attributed tothe chemically bound water) then it proceeds through non-traditional mechanism and with low rate
According to [41] the hydration mechanism for thehomologous series of R-123 compounds is in four stages Atthe initial stage water molecules penetrate into the bulk ofthe crystallites through the structural channels [(12) b 0]located in interspaces between CuO-chains typical for thistype of superconductors At the next stage protons whichare located in the oxygen positions of CuO-chains can besplit up of watermoleculesThis proton transfer is consideredto cause an internal (within the [CundashO]+-system) chargetransfer resulting in formation of molecular oxygen leavingthe structure At high concentrations of hydroxide ionsaccumulated in the structure the chemical decompositionof the initial oxide occurs Based on the previous schemeone can understand the reasons for high resistivity of N-123superconductor to chemical interaction with water
The authors of [42] discussed the high corrosion resis-tance of Nd-123 films in the water compared to the filmstructures of Y-123 and Eu-123 which was attributed to thepartial oxygen disorder in the planes of CuO-chains Sucha disorder should occur in Nd-123 due to the presence ofsome amount of Nd3+ ions in the sites nearby to CuO-planesof divalent barium According to the authors that shouldlead to overlapping structural channels for H
2O diffusion
and hence blocking the hydration process However ourdata on the thermal analysis (see Figure 7) illustrate thatthe saturation of Nd-123 structure with water during MAtreatment proceeds almost as fast as in Y-123 (in the rangeof 2ndash10 minutes even faster) Therefore the sought causeof the chemical stability of Nd-123 MP cannot be related toproblems of H
2O diffusion
The stage of removing oxygen from the structure is con-sidered [41 42] to be extremely important for the hydrationprocess of R-123 Thus the chemical degradation of Y-123oxide immersed in the water is completely stopped underpotential of 08 V relative to the standard electrode-saturatedsodium calomel [41] It is expected that the substitutionNd3+ rarr Ba2+ inNd-123 in addition to oxygen disordering inthe base structural plane should also lead to the strengtheningof its bondwith the lattice (due to electrostatic effect of highlycharged Nd3+ ion) [42] According to the authors [42] thisshould inhibit the reduction stage of hydration However it isimportant to consider the fact that the structure ofMP of Nd-123 contains a large amount of weakly bound CO
2 located
near Ba ions (since there is a tendency to the formation ofBaCO
3) therefore localized in the channels of the base plane
[(12) b 0] where also there is water In our opinion just theseCO2particles block channels of oxygen desorption which is
the main reason for the high stability of Nd-123 in relation tothe hydrolysis reaction
5 Conclusion
Thus as a result of mechanical activation treatment thesurface of YBa
2Cu3O6+120575
is covered by products of hydrolysisand carbonization to a considerable depth The chemicaldegradation process proceeds the normal waymdashthrough theformation of Y
2BaCuO
5phase
Chemical degradation of mechanoactivatedNdBa
2Cu3O6+120575
powders under the impact of CO2
isnot directly connected to hydrolysis process as occurs inYBa2Cu3O6+120575
(see reactions (1) and (2)) Carbonizationproceeds homogeneously through the stage of carbondioxide dissolution in the lattice of NdBa
2Cu3O6+120575
In itsturn the presence of CO
2molecules in the structure of
mechanoactivated NdBa2Cu3O6+120575
powders leads to a radicalchange in the mechanism of interaction between the super-conductor and water This mechanism eliminates the normalfor a homologous series of RBa
2Cu3O6+120575
the hydrolysisreaction with the formation of characteristic ldquocolorrdquoR2BaCuO
5phases The rate of chemical decomposition of
mechanically activated NdBa2Cu3O6+120575
by the new mecha-nism (not yet studied) is quite low
12 Journal of Spectroscopy
Mechanical treatment affects the temperature depen-dence of the magnetization of RBa
2Cu3O6+120575
compoundsThere is a significant increase in the paramagnetic and ferro-magnetic contributions to the magnetization with increasingmilling duration The latter leads to near-room-temperaturehysteretic behavior of NdBa
2Cu3O6+120575
samples between ZFCandFC regimes Itmay be due tomagnetic particles ofmecha-noactivated NdBa
2Cu3O6+120575
samples or to the presence ofimpurity phases whose low content or highly disorderedcrystal structures do not allow to observe these phases byX-ray diffraction measurements The mechanical treatmentdoes not have substantial influence on the transition tem-peratures of superconducting phases 119879
119888in the RBa
2Cu3O6+120575
compounds but a wide transition width around 119879119888indicates
that mechanically activated samples contain inhomogeneoussuperconductor phases with different 119879
119888 The broadening
of the superconducting transition in mechanically activatedNdBa
2Cu3O6+120575
samples may be due to redistribution ofcations between Nd- and Ba-sublattice
Finally we note that the high temperature superconduc-tor RBa
2Cu3O6+120575
subjected to mechanical activation cer-tainly has no significant advantages over conventional non-mechanoactivated material but it is obvious that physical-chemical studies of such powders reveal results interestingfrom the point of view of fundamental science
Acknowledgment
This work was supported by Russian Foundation for BasicResearch (Grant no 11-03-00317-a)
References
[1] I E Graboi A R Kaulrsquo and G Yu Metlin ldquoAdvances in scienceand technologyrdquo in Solid State Chemistry pp 3ndash142 VINITIANSSSR Moscow Russia 1989
[2] S Anders M G Blamire F-Im Buchholz et al ldquoEuropeanroadmap on superconductive electronicsmdashstatus and perspec-tivesrdquo Physica C vol 470 no 23-24 pp 2079ndash2126 2010
[3] B Ruck B Oelze R Dittmann et al ldquoMeasurement of thedynamic error rate of a high temperature superconductor rapidsingle flux quantum comparatorrdquo Applied Physics Letters vol72 no 18 pp 2328ndash2330 1998
[4] M W Rupich X Li C Thieme et al ldquoAdvances in secondgeneration high temperature superconducting wire manufac-turing and RampD at American superconductor corporationrdquoSuperconductor Science and Technology vol 23 no 1 Article ID014015 2010
[5] A Rakitin M Kobayashi and A P Litvinchuk ldquoSuperi-onic behavior of high-temperature superconductorsrdquo PhysicalReview B vol 55 no 1 pp 89ndash92 1997
[6] T Kagiyama J Shimoyama K D Otzschi et al ldquoEffect of cationcomposition and oxygen nonstoichiometry on 119869
119888-119861 properties
of Nd123rdquo Physica C vol 341ndash348 no 2 pp 1445ndash1446 2000
[7] M Badaye J G Wen K Fukushima et al ldquoSuperior propertiesof NdBa
2Cu3O119910over YBa
2Cu3O119909thin filmsrdquo Superconductor
Science and Technology vol 10 no 11 pp 825ndash830 1997
[8] C Cantoni D P Norton D M Kroeger et al ldquoPhase stabilityfor the in situ growth of Nd
1+119909Ba2minus119909
Cu3O119910films using pulsed-
laser depositionrdquo Applied Physics Letters vol 74 no 1 pp 96ndash98 1999
[9] E A Goodilin N N Oleynikov E V Antipov et al ldquoPhasestability for the in situ growth of Nd
1+119909Ba2minus119909
Cu3O119910films using
pulsed-laser depositionrdquo Physica C vol 272 6578 pages 1996[10] E Guilmeau F Giovannelli I Monot-Laffez S Marinel J
Provost and G Desgardin ldquoTop seeding melt texture growthof NdBaCuO pellets in airrdquoThe European Physical Journal vol13 no 3 pp 157ndash160 2001
[11] A I Ancharov T F Grigorrsquoeva T Yu Kiseleva A A Novakovaet al inMechanocomposites-Precursorsfor the Creation of Mate-rials with New Properties O I Lomovskii Ed p 424 Izd-voSO RAN Novosibirsk Russia 2010
[12] A Hamrita F Ben Azzouz A Madani and M Ben SalemldquoMagnetoresistivity and microstructure of YBa
2Cu3O119910pre-
pared using planetary ball millingrdquo Physica C vol 472 no 1pp 34ndash38 2012
[13] R P Vasquez ldquoIntrinsic photoemission signals surface prepa-ration and surface stability of high temperature superconduc-torsrdquo Journal of Electron Spectroscopy and Related Phenomenavol 66 no 3-4 pp 209ndash222 1994
[14] S S Gorelik L N Rastorguev and A Yu Skakov in Rentgeno-graphIcheskII I ElektronographIcheskII AnalIz p 368 Izd-voMetallurgia Moscow Russia 1970
[15] M V Reshetniak and O V Sobol Program for diffractionanalysis ldquoNew Profilerdquo(Last update 10 02 2007) Version 3 4400 (Freeware) WIN9xMENT2KXP Copyright (c) 1992-2007 ReMax SoftWare 2000
[16] M Wegmann L Watson and A Hendry ldquoXPS analysis of sub-micrometer barium titanate powderrdquo Journal of the AmericanCeramic Society vol 87 no 3 pp 371ndash377 2004
[17] A B Christie J Lee I Sutherland and J M Walls ldquoAn XPSstudy of ion-induced compositional changes with group II andgroup IV compoundsrdquo Applications of Surface Science vol 15no 1ndash4 pp 224ndash237 1983
[18] U A Joshi S Yoon S Balk and J S Lee ldquoSurfactant-freehydrothermal synthesis of highly tetragonal barium titanatenanowires a structural investigationrdquo Journal of Physical Chem-istry B vol 110 no 25 pp 12249ndash12256 2006
[19] R Caracciolo ldquoChemical characterization techniques for thinfilmsrdquo in Ceramic Films and Coatings J B Wachtman and R AHaber Eds p 376 New Jersey NJ USA 1992
[20] I N Shabanova Y A Naimushina and N S Terebova ldquoCom-position and temperature dependence of a Y-Ba-Cu-O HTSCelectronic structurerdquo Superconductor Science and Technologyvol 15 no 7 pp 1030ndash1033 2002
[21] J Beyer T Schurig S Menkel Z Quan and H Koch ldquoXPSinvestigation of the surface composition of sputtered YBCOthin filmsrdquo Physica C vol 246 no 1-2 pp 156ndash162 1995
[22] C C Chang M S Hegde X D Wu et al ldquoSurface layers onsuperconducting Y-Ba-Cu-O films studied with x-ray photo-electron spectroscopyrdquo Applied Physics Letters vol 55 no 16pp 1680ndash1682 1989
[23] X D Wu A Inam M S Hegde et al ldquoCrystalline perfectionof as-deposited high-Tc superconducting thin-film surfacesion channeling and x-ray photoelectron spectroscopy studyrdquoPhysical Review B vol 38 no 13 pp 9307ndash9310 1988
[24] P Rajasekar P Chakraborty S K Bandyopadhyay P Barat andP Sen ldquoX-ray photoelectron spectroscopy study of oxygen and
Journal of Spectroscopy 13
argon annealed YBa22Cu3O7minus120575
rdquo Modern Physics Letters B vol12 no 6-7 pp 239ndash245 1998
[25] J Halbritter P Walk H J Mathes B Haeuser and H RogallaldquoARXPS-studies of c-axis textured YBa
2Cu3O119909-filmsrdquo Physica
C vol 153ndash155 no 1 pp 127ndash128 1988[26] T J Sarapatka and P Mikusık ldquoXPS study of PbYBaCuO thin-
film tunnel contactrdquo Applied Surface Science vol 68 no 1 pp35ndash40 1993
[27] J A T Verhoeven and H Van Doveren ldquoAn XPS investigationof the interaction of CH
4 C2H2 C2H4and C
2H6with a barium
surfacerdquo Surface Science vol 123 no 2-3 pp 369ndash383 1982[28] C D Wagner W M Riggs L E Davis J F Moulder and G
E Mullenberg Handbook of X-Ray Photoelectron SpectroscopyPerkin-Elmer Corp Eden Prairie Minn USA 1979
[29] M C Biesinger L W M Lau A R Gerson and R S C SmartldquoResolving surface chemical states in XPS analysis of first rowtransition metals oxides and hydroxides Sc Ti V Cu and ZnrdquoApplied Surface Science vol 257 no 3 pp 887ndash898 2010
[30] X Y Fan Z GWu P X Yan et al ldquoFabrication of well-orderedCuO nanowire arrays by direct oxidation of sputter-depositedCu3N filmrdquo Materials Letters vol 62 no 12-13 pp 1805ndash1808
2008[31] S J Kerber J J Bruckner K Wozniak S Seal S Hardcastle
and T L Barr ldquoNature of hydrogen in x-ray photoelectronspectroscopy general patterns from hydroxides to hydrogenbondingrdquo Journal of Vacuum Science and Technology A vol 14no 3 pp 1314ndash1320 1996
[32] G Moretti G Fierro M Lo Jacono and P Porta ldquoCharac-terization of CuO-ZnO catalysts by X-ray photoelectron spec-troscopy precursors calcined and reduced samplesrdquo Surfaceand Interface Analysis vol 14 no 6-7 pp 325ndash336 1989
[33] H Van Doveren and J A T H Verhoeven ldquoXPS spectra of CaSr Ba and their oxidesrdquo Journal of Electron Spectroscopy andRelated Phenomena vol 21 no 3 pp 265ndash273 1980
[34] B V Crist Handbooks of Monochromatic XPS Spectra Volume2mdashCommercially pure binary oxides XPS International LLCLeona Tex USA 2005
[35] D D Sarma and C N R Rao ldquoXPES studies of oxides ofsecond- and third-row transition metals including rare earthsrdquoJournal of Electron Spectroscopy and Related Phenomena vol 20no 1 pp 25ndash45 1980
[36] V I Nefedov and A N Sokolov ldquoDegradatzia visokotemper-aturnich sverchprovodnikov pri khimicheskich vozdeistviachrdquoZhurnal Neorganicheskoi Khimii vol 34 no 11 pp 2723ndash27391989
[37] Y Uwamino T Ishizuka and H Yamatera ldquoX-ray photoelec-tron spectroscopy of rare-earth compoundsrdquo Journal of ElectronSpectroscopy and Related Phenomena vol 34 no 1 pp 67ndash781984
[38] M P Seah and W A Dench ldquoQuantitative electron spec-troscopy of surfaces a standard data base for electron inelasticmean free paths in solidsrdquo Surface and Interface Analysis vol 1no 1 pp 2ndash11 1979
[39] C H Lin H C I Kao and C M Wang ldquoKinetics andstability of R(Ba
15Sr05)Cu3O119910(R = La Nd Sm Eu Gd Dy Ho)
superconductors inwaterrdquoMaterials Chemistry and Physics vol82 no 2 pp 435ndash439 2003
[40] A G Knizhnik R A Stukan and G O Eremenko ldquoStudy theinteraction between europium HTSC of 123 type and waterrdquoSverkhprovodimost vol 4 no 1 pp 177ndash182 1991 (Russian)
[41] J Zhou R K Lo J T McDevitt et al ldquoDevelopment of areliable materials base for superconducting electronicsrdquo Journalof Materials Research vol 12 no 11 pp 2958ndash2975 1997
[42] S B Schougaard M F Ali and J T McDevitt ldquoEvidence forhigh stability against water corrosion of NdBa
2Cu3O7plusmn120575
relativeto YBa
2Cu3OO7minus120575
and EuBa2Cu3OO7minus120575
rdquo Applied Physics Let-ters vol 84 no 7 pp 1144ndash1146 2004
Submit your manuscripts athttpwwwhindawicom
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Inorganic ChemistryInternational Journal of
Hindawi Publishing Corporation httpwwwhindawicom Volume 2014
International Journal ofPhotoenergy
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Carbohydrate Chemistry
International Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Advances in
Physical Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom
Analytical Methods in Chemistry
Journal of
Volume 2014
Bioinorganic Chemistry and ApplicationsHindawi Publishing Corporationhttpwwwhindawicom Volume 2014
SpectroscopyInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
The Scientific World JournalHindawi Publishing Corporation httpwwwhindawicom Volume 2014
Medicinal ChemistryInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Chromatography Research International
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Applied ChemistryJournal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Theoretical ChemistryJournal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Spectroscopy
Analytical ChemistryInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Quantum Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Organic Chemistry International
ElectrochemistryInternational Journal of
Hindawi Publishing Corporation httpwwwhindawicom Volume 2014
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
CatalystsJournal of
8 Journal of Spectroscopy
Ba 3d
N-10
N-2
N-1
N-05
N-0
770 775 780 785 790 795 800 805Binding energy (eV)
(a)
N-10
N-1
Binding energy (eV)
Ba 4d
Ba 4d
N-2
N-05
N-0
68 72 80 84 88 92 96
Cu 3p X-ra
ysa
telli
tes
76
(b)
N-10
N-2
N-1
N-05
N-0
930 940 950 960 970Binding energy (eV)
Satellite I Satellite II
Cu 2p2p32
2p12
(c)
N-10
N-2
N-1
N-05
N-0
110 115 120 125 130 135Binding energy (eV)
Nd 4d
(d)
Figure 5 XPS spectra of NdBa2Cu3O6+120575
powders
119864119896 (Ba 3d) 119864119896 (Ba 4d)
Phase I Phase II
Phase III
Phase I Phase II
Phase III
31205823120582
XPS
study
area
XPS
study
area
lt
Figure 6 Analysis of the mutual arrangement phases in the surface layer of the material and their volume relations from XPS data
Journal of Spectroscopy 9
Table 3 Characteristic spectral parameters of different copper compounds
Electron orbital CuO CuCO3 Cu(OH)2 Cu2CO3(OH)2 Nd2BaCuO5
Binding energy eVBa 3d
527790lowast
Nd 4d52
1182lowast
Cu 2p32
9337 plusmn 1[28ndash30]
9348[28]
93474 plusmn 006[29 31]
9347[32] 9335lowast
O 1s 52974 plusmn 006[30 31]
53124[31] 5286lowast
lowastOur data
later we present the data of magnetic measurements whichindicate that MA treatment results in significant increase inthe temperature of the superconducting transition in separateregions of the material
324 Thermal Analysis of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
Samples of R-123 have been studied by thermogravimetrycoupled withmass-spectrometry to analyze the gases evolvedduring experiments Results of the study are summarizedin Figure 7 It is seen that reversible change in mass of IP-samples occurs in the range of 430ndash900∘C that must be dueto oxygen exchange between nonstoichiometric R-123 oxidesand the gas phase taking place at these temperatures [1] MPsamples start losing mass sharply around 70∘C when heatedMass spectrometry analysis of thermal desorption productsindicates the presence of large amount of water and a smallamount of carbon dioxide contained in the samples in theform of BaCO
3(the temperature range in which the CO
2
was released and the value of 119901CO2used for thermal analysis
of the atmosphere was consistent with conditions of bariumcarbonate decomposition)
325 Study of Magnetic Properties of YBa2Cu3O6+120575
andNdBa
2Cu3O6+120575
Temperature dependences of ZFC magne-tization of the samples Y-0 Y-05 Y-2 and Y-10 are shownin Figure 8 A sharp downturn in magnetization at sim90Kobserved in the samples Y-0 Y-05 and Y-2 clearly showsthe presence of the superconducting phase Superconductingtransition temperatures of the samples Y-0 Y-05 and Y-2have been determined by taking the derivative of the mag-netization against the temperature (119889119898119889119879) Thus definedtemperatures 119879
119888are equal to 91 K for the samples Y-0 and
Y-05 and 88K for the sample Y-2 A wide transition widtharound 119879
119888= 90K indicates that both the initial and MP
samples contain inhomogeneous superconductor phaseswithdifferent 119879
119888 The following facts indicate the presence of
paramagnetic contribution in the magnetization behavior ofMP samples and its growth with increasing milling durationa significant increase in magnetization 119898 of the samples Y-05 and Y-2 compared with the initial sample Y-0 at thetemperatures 119879 gt 119879
119888 weak temperature dependence 119898(119879)
in the temperature range 100ndash300 K for MP samples asignificant increase in themagnetization of Y-10 sample at lowtemperatures
100
99
98
97
96
95
94
93
92
100
99
98
97
96
95
94
93
92
0 200 400 600 800 1000
0 200 400 600 800 1000
14
12
10
8
6
4
3
2
Temperature (∘C)
Ion
curr
ent (
A)
Ion
curr
ent (
A)
Sam
ple w
eigh
t (
)
H2O
CO2
H2O (times1010) CO2 (times1011)
3
2
1
3998400
1998400
2998400
Figure 7 Thermal analysis results for samples Y-0 (1) N-0 (11015840) Y-2 (2) N-2 (21015840) and Y-10 (3) N-10 (31015840) Mass spectrometry data arerelated to the samples Y-10 (solid curves) and N-10 (dashed lines)
For comparison Figure 9 shows the temperature depen-dence of the FC magnetization in a magnetic field 119867 =500Oe for two new samples of Y-123 (120575 asymp 07) The firstsample has been freshly prepared and the other one has beensubjected to treatment at 297 plusmn 1K for 120 h at absolutehumidity of 23 120581Pa The sample with low oxygen content(and as a consequence with low 119879
119888) has been chosen due
to its relatively easy moisture saturation in these conditionswithout the use of MA (moisture saturation was controlledby the increase in weight which eventually was sim4wt)One can see that the sample saturated with water has apositive magnetic moment above the temperature 119879
119888and
shows an increase inmagnetic moment on cooling below this
10 Journal of Spectroscopy
N-0
N-1
N-10N-2
Y-2
Y-05
N-05
Y-0
Y-10
005 0005
0004
0003
0002
0001
0
0
minus005
minus01
minus015
minus02
minus025
minus03
minus01
minus02
minus03
003
002
001
0
0
0minus001
20 40 60 80 100 120 140119879 (K)
119898(e
mu
g)119898
(em
ug)
119898(e
mu
g)119898
(em
ug)
Figure 8 ZFC magnetizations as a function of temperature at119867 = 50Oe for the initial and mechanically activated samplesYBa2Cu3O6+120575
(top) NdBa2Cu3O6+120575
(bottom)
temperature similarly to Y-10 sample Onset temperature ofthe magnetic anomaly in the hydrated sample is the sameas that in the freshly prepared sample This experimentdemonstrates that the presence of water in MP sampleshas a significant effect on the temperature dependences ofthe magnetization observed in samples of Y-123 series (seeFigure 8)
Temperature dependences of ZFC magnetization of MPsamples in Nd-123 series are shown in Figure 8 The super-conducting transition temperatures of the samples N-0 N-05 and N-1 are independent of milling duration and equal to119879119888sim 57KMechanical treatment leads to a substantial change
in the magnetization of MP samples throughout the inves-tigated temperature range MP samples exhibit near-room-temperature hysteretic behavior that is ZFC magnetizationis more diamagnetic than FCmagnetization It may be due tomagnetic particles of mechanoactivatedNd-123 samples or tothe presence of impurity phases whose low content or highlydisordered crystal structures do not allow to observe thesephases by X-ray diffraction measurements We also cannotexclude the formation of CuO phase (119879
119873sim 220K) at the
surface of large NdBa2Cu3O6+120575
particles proceeding undermechanical activationAt the same time a significant increasein the paramagnetic contribution to the magnetization withincreasing milling duration is observed
004
002
0
minus002
minus004
minus006
minus0080 20 40 60 80 100 120 140
0 20 40 60 80 100 120 140
119898(e
mu)
119898(e
mu)
119879 (K)
119879 (K)
004
0038
0036
0034
Figure 9 FCmagnetizations as a function of temperature of freshlyprepared YBa
2Cu3O6+120575
sample (empty points) and of hydrated sam-ple (black points) at119867 = 500Oe Inset the temperature dependenceof magnetization of hydrated sample at119867 = 10 kOe
A wide transition width around 119879119888= 57K (|Δ119879
119888sim 20K|)
in MP samples of Nd-123 series cannot be explained only bythe presence of water in the structure The observed changesindicate that during MA treatment diffusion processes asso-ciated with the ordering of the cations Nd3+ and Ba2+ appa-rently occur according to [8ndash10] that has a significant effecton 119879119888
4 Discussion of Results
41 Interaction of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
withCO2 From comparison of Figures 4 and 5 it is clear that with
increasing duration of MA processing (120591119892) the amount of
barium-containing impurities on the surface of Nd-123 sam-ples continuously increases up to 120591
119892= 10min in contrast
to the situation for the oxide Y-123 for which initially (up120591119892= 05min) sudden change and subsequent (after 120591
119892=
05min) almost stagnation in the accumulation of chemicaldegradation products were observed (see Figures 2 and 3 anddata on the impurities in YBa
2Cu3O6+120575
sample) One can seefrom Figure 7 that the degree of water saturation (120578) of bothoxides (this parameter can be traced by sharp descendingbranch of sample mass change in the temperature range of30ndash450∘C) obeys similar relationships with increasing 120591
119892 its
growth with increasing MA duration close to proportionalfor Nd-123 (120578 sim 120591
119892) and tendency of 120578 to decrease for Y-123
(120578 = 155 sdot 120591119892
03) which is close to the root dependence char-
acteristic of reagent diffusion through the reaction productslayer
Taking into account the data in [1] stating the chemicaldegradation of Y-123 is carried out on the interface betweenY-123 and gas phase and one can explain sharply fallingrates of change in concentration of its products as well as ofH2O dissolved in the oxide the diffusion path length of H
2O
and CO2reactants to the location of the reactions (1) and
(2) increases with time 120591119892 However the uniformity of the
absorption of H2O and CO
2gases by MP of Nd-123 testifies
Journal of Spectroscopy 11
that the thickness of the degraded layer on the surface variesslightly Apparently it does not exceed 10 nm as indicated bya weak but clear signal of the main phase which appeared inthe Ba 4d-spectrum of N-10 sample (see Figure 5) Howeverit should be noted that Nd-123 MP sample actively entersinto chemical reactionwith atmospheric CO
2 the gas escapes
from the samples quite intensively when heated in the rangeof 800ndash900∘C (see Figure 7) Therefore the question oflocalization place of products of interaction between Nd-123and atmospheric components arises
Homogeneous nucleation and growth of interaction pro-ducts in the volume of Nd
1+xBa2minusxCu3O6+120575 parent phasemaybe the answer This assumption is based on the fact that theproducts of thermal desorption of N-10 sample (see Figure 7)contain weakly bound form of CO
2escaping in a wide tem-
perature range of 200ndash550∘C Obviously it is a form of gasdissolved in the structure Since the carbonization energy ofBa2+ ions is quite high homogeneous nucleation of carbonatephase at a certain concentration (equivactivity) of CO
2in the
structure facilitated by the participation of structural defects(whose concentration should be significant in MP samples)seems quite possible
42 Interaction of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
withWater In the Introductionwe have put links toworks statingthat the crucial feature for the practical application of thesuperconductor Nd-123 is its high resistance to chemicaldegradation under moisture Additional information thatexpands understanding of this feature has been received inour study Thus it is shown (see Figure 7) that a high con-centration of water accumulates in MP samples of Nd-123 indissolved form but the hydrolysis reaction development isquite limited as evidenced by the relatively low temperatureof H2O release from this oxide Moreover the results of
XRD and XPS analyzes have not detected even traces of theternary compound Nd
2BaCuO
5in these samples while it is
the compounds R2BaCuO
5due their characteristic colours
that are indicators of the hydrolysis reaction for the wholefamily of compounds R-123 [1 39 40] Thus if the hydrolysisreaction develops (there is a small peak on H
2O desorption
curve for sample N-10 at sim455∘C that can be attributed tothe chemically bound water) then it proceeds through non-traditional mechanism and with low rate
According to [41] the hydration mechanism for thehomologous series of R-123 compounds is in four stages Atthe initial stage water molecules penetrate into the bulk ofthe crystallites through the structural channels [(12) b 0]located in interspaces between CuO-chains typical for thistype of superconductors At the next stage protons whichare located in the oxygen positions of CuO-chains can besplit up of watermoleculesThis proton transfer is consideredto cause an internal (within the [CundashO]+-system) chargetransfer resulting in formation of molecular oxygen leavingthe structure At high concentrations of hydroxide ionsaccumulated in the structure the chemical decompositionof the initial oxide occurs Based on the previous schemeone can understand the reasons for high resistivity of N-123superconductor to chemical interaction with water
The authors of [42] discussed the high corrosion resis-tance of Nd-123 films in the water compared to the filmstructures of Y-123 and Eu-123 which was attributed to thepartial oxygen disorder in the planes of CuO-chains Sucha disorder should occur in Nd-123 due to the presence ofsome amount of Nd3+ ions in the sites nearby to CuO-planesof divalent barium According to the authors that shouldlead to overlapping structural channels for H
2O diffusion
and hence blocking the hydration process However ourdata on the thermal analysis (see Figure 7) illustrate thatthe saturation of Nd-123 structure with water during MAtreatment proceeds almost as fast as in Y-123 (in the rangeof 2ndash10 minutes even faster) Therefore the sought causeof the chemical stability of Nd-123 MP cannot be related toproblems of H
2O diffusion
The stage of removing oxygen from the structure is con-sidered [41 42] to be extremely important for the hydrationprocess of R-123 Thus the chemical degradation of Y-123oxide immersed in the water is completely stopped underpotential of 08 V relative to the standard electrode-saturatedsodium calomel [41] It is expected that the substitutionNd3+ rarr Ba2+ inNd-123 in addition to oxygen disordering inthe base structural plane should also lead to the strengtheningof its bondwith the lattice (due to electrostatic effect of highlycharged Nd3+ ion) [42] According to the authors [42] thisshould inhibit the reduction stage of hydration However it isimportant to consider the fact that the structure ofMP of Nd-123 contains a large amount of weakly bound CO
2 located
near Ba ions (since there is a tendency to the formation ofBaCO
3) therefore localized in the channels of the base plane
[(12) b 0] where also there is water In our opinion just theseCO2particles block channels of oxygen desorption which is
the main reason for the high stability of Nd-123 in relation tothe hydrolysis reaction
5 Conclusion
Thus as a result of mechanical activation treatment thesurface of YBa
2Cu3O6+120575
is covered by products of hydrolysisand carbonization to a considerable depth The chemicaldegradation process proceeds the normal waymdashthrough theformation of Y
2BaCuO
5phase
Chemical degradation of mechanoactivatedNdBa
2Cu3O6+120575
powders under the impact of CO2
isnot directly connected to hydrolysis process as occurs inYBa2Cu3O6+120575
(see reactions (1) and (2)) Carbonizationproceeds homogeneously through the stage of carbondioxide dissolution in the lattice of NdBa
2Cu3O6+120575
In itsturn the presence of CO
2molecules in the structure of
mechanoactivated NdBa2Cu3O6+120575
powders leads to a radicalchange in the mechanism of interaction between the super-conductor and water This mechanism eliminates the normalfor a homologous series of RBa
2Cu3O6+120575
the hydrolysisreaction with the formation of characteristic ldquocolorrdquoR2BaCuO
5phases The rate of chemical decomposition of
mechanically activated NdBa2Cu3O6+120575
by the new mecha-nism (not yet studied) is quite low
12 Journal of Spectroscopy
Mechanical treatment affects the temperature depen-dence of the magnetization of RBa
2Cu3O6+120575
compoundsThere is a significant increase in the paramagnetic and ferro-magnetic contributions to the magnetization with increasingmilling duration The latter leads to near-room-temperaturehysteretic behavior of NdBa
2Cu3O6+120575
samples between ZFCandFC regimes Itmay be due tomagnetic particles ofmecha-noactivated NdBa
2Cu3O6+120575
samples or to the presence ofimpurity phases whose low content or highly disorderedcrystal structures do not allow to observe these phases byX-ray diffraction measurements The mechanical treatmentdoes not have substantial influence on the transition tem-peratures of superconducting phases 119879
119888in the RBa
2Cu3O6+120575
compounds but a wide transition width around 119879119888indicates
that mechanically activated samples contain inhomogeneoussuperconductor phases with different 119879
119888 The broadening
of the superconducting transition in mechanically activatedNdBa
2Cu3O6+120575
samples may be due to redistribution ofcations between Nd- and Ba-sublattice
Finally we note that the high temperature superconduc-tor RBa
2Cu3O6+120575
subjected to mechanical activation cer-tainly has no significant advantages over conventional non-mechanoactivated material but it is obvious that physical-chemical studies of such powders reveal results interestingfrom the point of view of fundamental science
Acknowledgment
This work was supported by Russian Foundation for BasicResearch (Grant no 11-03-00317-a)
References
[1] I E Graboi A R Kaulrsquo and G Yu Metlin ldquoAdvances in scienceand technologyrdquo in Solid State Chemistry pp 3ndash142 VINITIANSSSR Moscow Russia 1989
[2] S Anders M G Blamire F-Im Buchholz et al ldquoEuropeanroadmap on superconductive electronicsmdashstatus and perspec-tivesrdquo Physica C vol 470 no 23-24 pp 2079ndash2126 2010
[3] B Ruck B Oelze R Dittmann et al ldquoMeasurement of thedynamic error rate of a high temperature superconductor rapidsingle flux quantum comparatorrdquo Applied Physics Letters vol72 no 18 pp 2328ndash2330 1998
[4] M W Rupich X Li C Thieme et al ldquoAdvances in secondgeneration high temperature superconducting wire manufac-turing and RampD at American superconductor corporationrdquoSuperconductor Science and Technology vol 23 no 1 Article ID014015 2010
[5] A Rakitin M Kobayashi and A P Litvinchuk ldquoSuperi-onic behavior of high-temperature superconductorsrdquo PhysicalReview B vol 55 no 1 pp 89ndash92 1997
[6] T Kagiyama J Shimoyama K D Otzschi et al ldquoEffect of cationcomposition and oxygen nonstoichiometry on 119869
119888-119861 properties
of Nd123rdquo Physica C vol 341ndash348 no 2 pp 1445ndash1446 2000
[7] M Badaye J G Wen K Fukushima et al ldquoSuperior propertiesof NdBa
2Cu3O119910over YBa
2Cu3O119909thin filmsrdquo Superconductor
Science and Technology vol 10 no 11 pp 825ndash830 1997
[8] C Cantoni D P Norton D M Kroeger et al ldquoPhase stabilityfor the in situ growth of Nd
1+119909Ba2minus119909
Cu3O119910films using pulsed-
laser depositionrdquo Applied Physics Letters vol 74 no 1 pp 96ndash98 1999
[9] E A Goodilin N N Oleynikov E V Antipov et al ldquoPhasestability for the in situ growth of Nd
1+119909Ba2minus119909
Cu3O119910films using
pulsed-laser depositionrdquo Physica C vol 272 6578 pages 1996[10] E Guilmeau F Giovannelli I Monot-Laffez S Marinel J
Provost and G Desgardin ldquoTop seeding melt texture growthof NdBaCuO pellets in airrdquoThe European Physical Journal vol13 no 3 pp 157ndash160 2001
[11] A I Ancharov T F Grigorrsquoeva T Yu Kiseleva A A Novakovaet al inMechanocomposites-Precursorsfor the Creation of Mate-rials with New Properties O I Lomovskii Ed p 424 Izd-voSO RAN Novosibirsk Russia 2010
[12] A Hamrita F Ben Azzouz A Madani and M Ben SalemldquoMagnetoresistivity and microstructure of YBa
2Cu3O119910pre-
pared using planetary ball millingrdquo Physica C vol 472 no 1pp 34ndash38 2012
[13] R P Vasquez ldquoIntrinsic photoemission signals surface prepa-ration and surface stability of high temperature superconduc-torsrdquo Journal of Electron Spectroscopy and Related Phenomenavol 66 no 3-4 pp 209ndash222 1994
[14] S S Gorelik L N Rastorguev and A Yu Skakov in Rentgeno-graphIcheskII I ElektronographIcheskII AnalIz p 368 Izd-voMetallurgia Moscow Russia 1970
[15] M V Reshetniak and O V Sobol Program for diffractionanalysis ldquoNew Profilerdquo(Last update 10 02 2007) Version 3 4400 (Freeware) WIN9xMENT2KXP Copyright (c) 1992-2007 ReMax SoftWare 2000
[16] M Wegmann L Watson and A Hendry ldquoXPS analysis of sub-micrometer barium titanate powderrdquo Journal of the AmericanCeramic Society vol 87 no 3 pp 371ndash377 2004
[17] A B Christie J Lee I Sutherland and J M Walls ldquoAn XPSstudy of ion-induced compositional changes with group II andgroup IV compoundsrdquo Applications of Surface Science vol 15no 1ndash4 pp 224ndash237 1983
[18] U A Joshi S Yoon S Balk and J S Lee ldquoSurfactant-freehydrothermal synthesis of highly tetragonal barium titanatenanowires a structural investigationrdquo Journal of Physical Chem-istry B vol 110 no 25 pp 12249ndash12256 2006
[19] R Caracciolo ldquoChemical characterization techniques for thinfilmsrdquo in Ceramic Films and Coatings J B Wachtman and R AHaber Eds p 376 New Jersey NJ USA 1992
[20] I N Shabanova Y A Naimushina and N S Terebova ldquoCom-position and temperature dependence of a Y-Ba-Cu-O HTSCelectronic structurerdquo Superconductor Science and Technologyvol 15 no 7 pp 1030ndash1033 2002
[21] J Beyer T Schurig S Menkel Z Quan and H Koch ldquoXPSinvestigation of the surface composition of sputtered YBCOthin filmsrdquo Physica C vol 246 no 1-2 pp 156ndash162 1995
[22] C C Chang M S Hegde X D Wu et al ldquoSurface layers onsuperconducting Y-Ba-Cu-O films studied with x-ray photo-electron spectroscopyrdquo Applied Physics Letters vol 55 no 16pp 1680ndash1682 1989
[23] X D Wu A Inam M S Hegde et al ldquoCrystalline perfectionof as-deposited high-Tc superconducting thin-film surfacesion channeling and x-ray photoelectron spectroscopy studyrdquoPhysical Review B vol 38 no 13 pp 9307ndash9310 1988
[24] P Rajasekar P Chakraborty S K Bandyopadhyay P Barat andP Sen ldquoX-ray photoelectron spectroscopy study of oxygen and
Journal of Spectroscopy 13
argon annealed YBa22Cu3O7minus120575
rdquo Modern Physics Letters B vol12 no 6-7 pp 239ndash245 1998
[25] J Halbritter P Walk H J Mathes B Haeuser and H RogallaldquoARXPS-studies of c-axis textured YBa
2Cu3O119909-filmsrdquo Physica
C vol 153ndash155 no 1 pp 127ndash128 1988[26] T J Sarapatka and P Mikusık ldquoXPS study of PbYBaCuO thin-
film tunnel contactrdquo Applied Surface Science vol 68 no 1 pp35ndash40 1993
[27] J A T Verhoeven and H Van Doveren ldquoAn XPS investigationof the interaction of CH
4 C2H2 C2H4and C
2H6with a barium
surfacerdquo Surface Science vol 123 no 2-3 pp 369ndash383 1982[28] C D Wagner W M Riggs L E Davis J F Moulder and G
E Mullenberg Handbook of X-Ray Photoelectron SpectroscopyPerkin-Elmer Corp Eden Prairie Minn USA 1979
[29] M C Biesinger L W M Lau A R Gerson and R S C SmartldquoResolving surface chemical states in XPS analysis of first rowtransition metals oxides and hydroxides Sc Ti V Cu and ZnrdquoApplied Surface Science vol 257 no 3 pp 887ndash898 2010
[30] X Y Fan Z GWu P X Yan et al ldquoFabrication of well-orderedCuO nanowire arrays by direct oxidation of sputter-depositedCu3N filmrdquo Materials Letters vol 62 no 12-13 pp 1805ndash1808
2008[31] S J Kerber J J Bruckner K Wozniak S Seal S Hardcastle
and T L Barr ldquoNature of hydrogen in x-ray photoelectronspectroscopy general patterns from hydroxides to hydrogenbondingrdquo Journal of Vacuum Science and Technology A vol 14no 3 pp 1314ndash1320 1996
[32] G Moretti G Fierro M Lo Jacono and P Porta ldquoCharac-terization of CuO-ZnO catalysts by X-ray photoelectron spec-troscopy precursors calcined and reduced samplesrdquo Surfaceand Interface Analysis vol 14 no 6-7 pp 325ndash336 1989
[33] H Van Doveren and J A T H Verhoeven ldquoXPS spectra of CaSr Ba and their oxidesrdquo Journal of Electron Spectroscopy andRelated Phenomena vol 21 no 3 pp 265ndash273 1980
[34] B V Crist Handbooks of Monochromatic XPS Spectra Volume2mdashCommercially pure binary oxides XPS International LLCLeona Tex USA 2005
[35] D D Sarma and C N R Rao ldquoXPES studies of oxides ofsecond- and third-row transition metals including rare earthsrdquoJournal of Electron Spectroscopy and Related Phenomena vol 20no 1 pp 25ndash45 1980
[36] V I Nefedov and A N Sokolov ldquoDegradatzia visokotemper-aturnich sverchprovodnikov pri khimicheskich vozdeistviachrdquoZhurnal Neorganicheskoi Khimii vol 34 no 11 pp 2723ndash27391989
[37] Y Uwamino T Ishizuka and H Yamatera ldquoX-ray photoelec-tron spectroscopy of rare-earth compoundsrdquo Journal of ElectronSpectroscopy and Related Phenomena vol 34 no 1 pp 67ndash781984
[38] M P Seah and W A Dench ldquoQuantitative electron spec-troscopy of surfaces a standard data base for electron inelasticmean free paths in solidsrdquo Surface and Interface Analysis vol 1no 1 pp 2ndash11 1979
[39] C H Lin H C I Kao and C M Wang ldquoKinetics andstability of R(Ba
15Sr05)Cu3O119910(R = La Nd Sm Eu Gd Dy Ho)
superconductors inwaterrdquoMaterials Chemistry and Physics vol82 no 2 pp 435ndash439 2003
[40] A G Knizhnik R A Stukan and G O Eremenko ldquoStudy theinteraction between europium HTSC of 123 type and waterrdquoSverkhprovodimost vol 4 no 1 pp 177ndash182 1991 (Russian)
[41] J Zhou R K Lo J T McDevitt et al ldquoDevelopment of areliable materials base for superconducting electronicsrdquo Journalof Materials Research vol 12 no 11 pp 2958ndash2975 1997
[42] S B Schougaard M F Ali and J T McDevitt ldquoEvidence forhigh stability against water corrosion of NdBa
2Cu3O7plusmn120575
relativeto YBa
2Cu3OO7minus120575
and EuBa2Cu3OO7minus120575
rdquo Applied Physics Let-ters vol 84 no 7 pp 1144ndash1146 2004
Submit your manuscripts athttpwwwhindawicom
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Inorganic ChemistryInternational Journal of
Hindawi Publishing Corporation httpwwwhindawicom Volume 2014
International Journal ofPhotoenergy
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Carbohydrate Chemistry
International Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Advances in
Physical Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom
Analytical Methods in Chemistry
Journal of
Volume 2014
Bioinorganic Chemistry and ApplicationsHindawi Publishing Corporationhttpwwwhindawicom Volume 2014
SpectroscopyInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
The Scientific World JournalHindawi Publishing Corporation httpwwwhindawicom Volume 2014
Medicinal ChemistryInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Chromatography Research International
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Applied ChemistryJournal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Theoretical ChemistryJournal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Spectroscopy
Analytical ChemistryInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Quantum Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Organic Chemistry International
ElectrochemistryInternational Journal of
Hindawi Publishing Corporation httpwwwhindawicom Volume 2014
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
CatalystsJournal of
Journal of Spectroscopy 9
Table 3 Characteristic spectral parameters of different copper compounds
Electron orbital CuO CuCO3 Cu(OH)2 Cu2CO3(OH)2 Nd2BaCuO5
Binding energy eVBa 3d
527790lowast
Nd 4d52
1182lowast
Cu 2p32
9337 plusmn 1[28ndash30]
9348[28]
93474 plusmn 006[29 31]
9347[32] 9335lowast
O 1s 52974 plusmn 006[30 31]
53124[31] 5286lowast
lowastOur data
later we present the data of magnetic measurements whichindicate that MA treatment results in significant increase inthe temperature of the superconducting transition in separateregions of the material
324 Thermal Analysis of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
Samples of R-123 have been studied by thermogravimetrycoupled withmass-spectrometry to analyze the gases evolvedduring experiments Results of the study are summarizedin Figure 7 It is seen that reversible change in mass of IP-samples occurs in the range of 430ndash900∘C that must be dueto oxygen exchange between nonstoichiometric R-123 oxidesand the gas phase taking place at these temperatures [1] MPsamples start losing mass sharply around 70∘C when heatedMass spectrometry analysis of thermal desorption productsindicates the presence of large amount of water and a smallamount of carbon dioxide contained in the samples in theform of BaCO
3(the temperature range in which the CO
2
was released and the value of 119901CO2used for thermal analysis
of the atmosphere was consistent with conditions of bariumcarbonate decomposition)
325 Study of Magnetic Properties of YBa2Cu3O6+120575
andNdBa
2Cu3O6+120575
Temperature dependences of ZFC magne-tization of the samples Y-0 Y-05 Y-2 and Y-10 are shownin Figure 8 A sharp downturn in magnetization at sim90Kobserved in the samples Y-0 Y-05 and Y-2 clearly showsthe presence of the superconducting phase Superconductingtransition temperatures of the samples Y-0 Y-05 and Y-2have been determined by taking the derivative of the mag-netization against the temperature (119889119898119889119879) Thus definedtemperatures 119879
119888are equal to 91 K for the samples Y-0 and
Y-05 and 88K for the sample Y-2 A wide transition widtharound 119879
119888= 90K indicates that both the initial and MP
samples contain inhomogeneous superconductor phaseswithdifferent 119879
119888 The following facts indicate the presence of
paramagnetic contribution in the magnetization behavior ofMP samples and its growth with increasing milling durationa significant increase in magnetization 119898 of the samples Y-05 and Y-2 compared with the initial sample Y-0 at thetemperatures 119879 gt 119879
119888 weak temperature dependence 119898(119879)
in the temperature range 100ndash300 K for MP samples asignificant increase in themagnetization of Y-10 sample at lowtemperatures
100
99
98
97
96
95
94
93
92
100
99
98
97
96
95
94
93
92
0 200 400 600 800 1000
0 200 400 600 800 1000
14
12
10
8
6
4
3
2
Temperature (∘C)
Ion
curr
ent (
A)
Ion
curr
ent (
A)
Sam
ple w
eigh
t (
)
H2O
CO2
H2O (times1010) CO2 (times1011)
3
2
1
3998400
1998400
2998400
Figure 7 Thermal analysis results for samples Y-0 (1) N-0 (11015840) Y-2 (2) N-2 (21015840) and Y-10 (3) N-10 (31015840) Mass spectrometry data arerelated to the samples Y-10 (solid curves) and N-10 (dashed lines)
For comparison Figure 9 shows the temperature depen-dence of the FC magnetization in a magnetic field 119867 =500Oe for two new samples of Y-123 (120575 asymp 07) The firstsample has been freshly prepared and the other one has beensubjected to treatment at 297 plusmn 1K for 120 h at absolutehumidity of 23 120581Pa The sample with low oxygen content(and as a consequence with low 119879
119888) has been chosen due
to its relatively easy moisture saturation in these conditionswithout the use of MA (moisture saturation was controlledby the increase in weight which eventually was sim4wt)One can see that the sample saturated with water has apositive magnetic moment above the temperature 119879
119888and
shows an increase inmagnetic moment on cooling below this
10 Journal of Spectroscopy
N-0
N-1
N-10N-2
Y-2
Y-05
N-05
Y-0
Y-10
005 0005
0004
0003
0002
0001
0
0
minus005
minus01
minus015
minus02
minus025
minus03
minus01
minus02
minus03
003
002
001
0
0
0minus001
20 40 60 80 100 120 140119879 (K)
119898(e
mu
g)119898
(em
ug)
119898(e
mu
g)119898
(em
ug)
Figure 8 ZFC magnetizations as a function of temperature at119867 = 50Oe for the initial and mechanically activated samplesYBa2Cu3O6+120575
(top) NdBa2Cu3O6+120575
(bottom)
temperature similarly to Y-10 sample Onset temperature ofthe magnetic anomaly in the hydrated sample is the sameas that in the freshly prepared sample This experimentdemonstrates that the presence of water in MP sampleshas a significant effect on the temperature dependences ofthe magnetization observed in samples of Y-123 series (seeFigure 8)
Temperature dependences of ZFC magnetization of MPsamples in Nd-123 series are shown in Figure 8 The super-conducting transition temperatures of the samples N-0 N-05 and N-1 are independent of milling duration and equal to119879119888sim 57KMechanical treatment leads to a substantial change
in the magnetization of MP samples throughout the inves-tigated temperature range MP samples exhibit near-room-temperature hysteretic behavior that is ZFC magnetizationis more diamagnetic than FCmagnetization It may be due tomagnetic particles of mechanoactivatedNd-123 samples or tothe presence of impurity phases whose low content or highlydisordered crystal structures do not allow to observe thesephases by X-ray diffraction measurements We also cannotexclude the formation of CuO phase (119879
119873sim 220K) at the
surface of large NdBa2Cu3O6+120575
particles proceeding undermechanical activationAt the same time a significant increasein the paramagnetic contribution to the magnetization withincreasing milling duration is observed
004
002
0
minus002
minus004
minus006
minus0080 20 40 60 80 100 120 140
0 20 40 60 80 100 120 140
119898(e
mu)
119898(e
mu)
119879 (K)
119879 (K)
004
0038
0036
0034
Figure 9 FCmagnetizations as a function of temperature of freshlyprepared YBa
2Cu3O6+120575
sample (empty points) and of hydrated sam-ple (black points) at119867 = 500Oe Inset the temperature dependenceof magnetization of hydrated sample at119867 = 10 kOe
A wide transition width around 119879119888= 57K (|Δ119879
119888sim 20K|)
in MP samples of Nd-123 series cannot be explained only bythe presence of water in the structure The observed changesindicate that during MA treatment diffusion processes asso-ciated with the ordering of the cations Nd3+ and Ba2+ appa-rently occur according to [8ndash10] that has a significant effecton 119879119888
4 Discussion of Results
41 Interaction of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
withCO2 From comparison of Figures 4 and 5 it is clear that with
increasing duration of MA processing (120591119892) the amount of
barium-containing impurities on the surface of Nd-123 sam-ples continuously increases up to 120591
119892= 10min in contrast
to the situation for the oxide Y-123 for which initially (up120591119892= 05min) sudden change and subsequent (after 120591
119892=
05min) almost stagnation in the accumulation of chemicaldegradation products were observed (see Figures 2 and 3 anddata on the impurities in YBa
2Cu3O6+120575
sample) One can seefrom Figure 7 that the degree of water saturation (120578) of bothoxides (this parameter can be traced by sharp descendingbranch of sample mass change in the temperature range of30ndash450∘C) obeys similar relationships with increasing 120591
119892 its
growth with increasing MA duration close to proportionalfor Nd-123 (120578 sim 120591
119892) and tendency of 120578 to decrease for Y-123
(120578 = 155 sdot 120591119892
03) which is close to the root dependence char-
acteristic of reagent diffusion through the reaction productslayer
Taking into account the data in [1] stating the chemicaldegradation of Y-123 is carried out on the interface betweenY-123 and gas phase and one can explain sharply fallingrates of change in concentration of its products as well as ofH2O dissolved in the oxide the diffusion path length of H
2O
and CO2reactants to the location of the reactions (1) and
(2) increases with time 120591119892 However the uniformity of the
absorption of H2O and CO
2gases by MP of Nd-123 testifies
Journal of Spectroscopy 11
that the thickness of the degraded layer on the surface variesslightly Apparently it does not exceed 10 nm as indicated bya weak but clear signal of the main phase which appeared inthe Ba 4d-spectrum of N-10 sample (see Figure 5) Howeverit should be noted that Nd-123 MP sample actively entersinto chemical reactionwith atmospheric CO
2 the gas escapes
from the samples quite intensively when heated in the rangeof 800ndash900∘C (see Figure 7) Therefore the question oflocalization place of products of interaction between Nd-123and atmospheric components arises
Homogeneous nucleation and growth of interaction pro-ducts in the volume of Nd
1+xBa2minusxCu3O6+120575 parent phasemaybe the answer This assumption is based on the fact that theproducts of thermal desorption of N-10 sample (see Figure 7)contain weakly bound form of CO
2escaping in a wide tem-
perature range of 200ndash550∘C Obviously it is a form of gasdissolved in the structure Since the carbonization energy ofBa2+ ions is quite high homogeneous nucleation of carbonatephase at a certain concentration (equivactivity) of CO
2in the
structure facilitated by the participation of structural defects(whose concentration should be significant in MP samples)seems quite possible
42 Interaction of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
withWater In the Introductionwe have put links toworks statingthat the crucial feature for the practical application of thesuperconductor Nd-123 is its high resistance to chemicaldegradation under moisture Additional information thatexpands understanding of this feature has been received inour study Thus it is shown (see Figure 7) that a high con-centration of water accumulates in MP samples of Nd-123 indissolved form but the hydrolysis reaction development isquite limited as evidenced by the relatively low temperatureof H2O release from this oxide Moreover the results of
XRD and XPS analyzes have not detected even traces of theternary compound Nd
2BaCuO
5in these samples while it is
the compounds R2BaCuO
5due their characteristic colours
that are indicators of the hydrolysis reaction for the wholefamily of compounds R-123 [1 39 40] Thus if the hydrolysisreaction develops (there is a small peak on H
2O desorption
curve for sample N-10 at sim455∘C that can be attributed tothe chemically bound water) then it proceeds through non-traditional mechanism and with low rate
According to [41] the hydration mechanism for thehomologous series of R-123 compounds is in four stages Atthe initial stage water molecules penetrate into the bulk ofthe crystallites through the structural channels [(12) b 0]located in interspaces between CuO-chains typical for thistype of superconductors At the next stage protons whichare located in the oxygen positions of CuO-chains can besplit up of watermoleculesThis proton transfer is consideredto cause an internal (within the [CundashO]+-system) chargetransfer resulting in formation of molecular oxygen leavingthe structure At high concentrations of hydroxide ionsaccumulated in the structure the chemical decompositionof the initial oxide occurs Based on the previous schemeone can understand the reasons for high resistivity of N-123superconductor to chemical interaction with water
The authors of [42] discussed the high corrosion resis-tance of Nd-123 films in the water compared to the filmstructures of Y-123 and Eu-123 which was attributed to thepartial oxygen disorder in the planes of CuO-chains Sucha disorder should occur in Nd-123 due to the presence ofsome amount of Nd3+ ions in the sites nearby to CuO-planesof divalent barium According to the authors that shouldlead to overlapping structural channels for H
2O diffusion
and hence blocking the hydration process However ourdata on the thermal analysis (see Figure 7) illustrate thatthe saturation of Nd-123 structure with water during MAtreatment proceeds almost as fast as in Y-123 (in the rangeof 2ndash10 minutes even faster) Therefore the sought causeof the chemical stability of Nd-123 MP cannot be related toproblems of H
2O diffusion
The stage of removing oxygen from the structure is con-sidered [41 42] to be extremely important for the hydrationprocess of R-123 Thus the chemical degradation of Y-123oxide immersed in the water is completely stopped underpotential of 08 V relative to the standard electrode-saturatedsodium calomel [41] It is expected that the substitutionNd3+ rarr Ba2+ inNd-123 in addition to oxygen disordering inthe base structural plane should also lead to the strengtheningof its bondwith the lattice (due to electrostatic effect of highlycharged Nd3+ ion) [42] According to the authors [42] thisshould inhibit the reduction stage of hydration However it isimportant to consider the fact that the structure ofMP of Nd-123 contains a large amount of weakly bound CO
2 located
near Ba ions (since there is a tendency to the formation ofBaCO
3) therefore localized in the channels of the base plane
[(12) b 0] where also there is water In our opinion just theseCO2particles block channels of oxygen desorption which is
the main reason for the high stability of Nd-123 in relation tothe hydrolysis reaction
5 Conclusion
Thus as a result of mechanical activation treatment thesurface of YBa
2Cu3O6+120575
is covered by products of hydrolysisand carbonization to a considerable depth The chemicaldegradation process proceeds the normal waymdashthrough theformation of Y
2BaCuO
5phase
Chemical degradation of mechanoactivatedNdBa
2Cu3O6+120575
powders under the impact of CO2
isnot directly connected to hydrolysis process as occurs inYBa2Cu3O6+120575
(see reactions (1) and (2)) Carbonizationproceeds homogeneously through the stage of carbondioxide dissolution in the lattice of NdBa
2Cu3O6+120575
In itsturn the presence of CO
2molecules in the structure of
mechanoactivated NdBa2Cu3O6+120575
powders leads to a radicalchange in the mechanism of interaction between the super-conductor and water This mechanism eliminates the normalfor a homologous series of RBa
2Cu3O6+120575
the hydrolysisreaction with the formation of characteristic ldquocolorrdquoR2BaCuO
5phases The rate of chemical decomposition of
mechanically activated NdBa2Cu3O6+120575
by the new mecha-nism (not yet studied) is quite low
12 Journal of Spectroscopy
Mechanical treatment affects the temperature depen-dence of the magnetization of RBa
2Cu3O6+120575
compoundsThere is a significant increase in the paramagnetic and ferro-magnetic contributions to the magnetization with increasingmilling duration The latter leads to near-room-temperaturehysteretic behavior of NdBa
2Cu3O6+120575
samples between ZFCandFC regimes Itmay be due tomagnetic particles ofmecha-noactivated NdBa
2Cu3O6+120575
samples or to the presence ofimpurity phases whose low content or highly disorderedcrystal structures do not allow to observe these phases byX-ray diffraction measurements The mechanical treatmentdoes not have substantial influence on the transition tem-peratures of superconducting phases 119879
119888in the RBa
2Cu3O6+120575
compounds but a wide transition width around 119879119888indicates
that mechanically activated samples contain inhomogeneoussuperconductor phases with different 119879
119888 The broadening
of the superconducting transition in mechanically activatedNdBa
2Cu3O6+120575
samples may be due to redistribution ofcations between Nd- and Ba-sublattice
Finally we note that the high temperature superconduc-tor RBa
2Cu3O6+120575
subjected to mechanical activation cer-tainly has no significant advantages over conventional non-mechanoactivated material but it is obvious that physical-chemical studies of such powders reveal results interestingfrom the point of view of fundamental science
Acknowledgment
This work was supported by Russian Foundation for BasicResearch (Grant no 11-03-00317-a)
References
[1] I E Graboi A R Kaulrsquo and G Yu Metlin ldquoAdvances in scienceand technologyrdquo in Solid State Chemistry pp 3ndash142 VINITIANSSSR Moscow Russia 1989
[2] S Anders M G Blamire F-Im Buchholz et al ldquoEuropeanroadmap on superconductive electronicsmdashstatus and perspec-tivesrdquo Physica C vol 470 no 23-24 pp 2079ndash2126 2010
[3] B Ruck B Oelze R Dittmann et al ldquoMeasurement of thedynamic error rate of a high temperature superconductor rapidsingle flux quantum comparatorrdquo Applied Physics Letters vol72 no 18 pp 2328ndash2330 1998
[4] M W Rupich X Li C Thieme et al ldquoAdvances in secondgeneration high temperature superconducting wire manufac-turing and RampD at American superconductor corporationrdquoSuperconductor Science and Technology vol 23 no 1 Article ID014015 2010
[5] A Rakitin M Kobayashi and A P Litvinchuk ldquoSuperi-onic behavior of high-temperature superconductorsrdquo PhysicalReview B vol 55 no 1 pp 89ndash92 1997
[6] T Kagiyama J Shimoyama K D Otzschi et al ldquoEffect of cationcomposition and oxygen nonstoichiometry on 119869
119888-119861 properties
of Nd123rdquo Physica C vol 341ndash348 no 2 pp 1445ndash1446 2000
[7] M Badaye J G Wen K Fukushima et al ldquoSuperior propertiesof NdBa
2Cu3O119910over YBa
2Cu3O119909thin filmsrdquo Superconductor
Science and Technology vol 10 no 11 pp 825ndash830 1997
[8] C Cantoni D P Norton D M Kroeger et al ldquoPhase stabilityfor the in situ growth of Nd
1+119909Ba2minus119909
Cu3O119910films using pulsed-
laser depositionrdquo Applied Physics Letters vol 74 no 1 pp 96ndash98 1999
[9] E A Goodilin N N Oleynikov E V Antipov et al ldquoPhasestability for the in situ growth of Nd
1+119909Ba2minus119909
Cu3O119910films using
pulsed-laser depositionrdquo Physica C vol 272 6578 pages 1996[10] E Guilmeau F Giovannelli I Monot-Laffez S Marinel J
Provost and G Desgardin ldquoTop seeding melt texture growthof NdBaCuO pellets in airrdquoThe European Physical Journal vol13 no 3 pp 157ndash160 2001
[11] A I Ancharov T F Grigorrsquoeva T Yu Kiseleva A A Novakovaet al inMechanocomposites-Precursorsfor the Creation of Mate-rials with New Properties O I Lomovskii Ed p 424 Izd-voSO RAN Novosibirsk Russia 2010
[12] A Hamrita F Ben Azzouz A Madani and M Ben SalemldquoMagnetoresistivity and microstructure of YBa
2Cu3O119910pre-
pared using planetary ball millingrdquo Physica C vol 472 no 1pp 34ndash38 2012
[13] R P Vasquez ldquoIntrinsic photoemission signals surface prepa-ration and surface stability of high temperature superconduc-torsrdquo Journal of Electron Spectroscopy and Related Phenomenavol 66 no 3-4 pp 209ndash222 1994
[14] S S Gorelik L N Rastorguev and A Yu Skakov in Rentgeno-graphIcheskII I ElektronographIcheskII AnalIz p 368 Izd-voMetallurgia Moscow Russia 1970
[15] M V Reshetniak and O V Sobol Program for diffractionanalysis ldquoNew Profilerdquo(Last update 10 02 2007) Version 3 4400 (Freeware) WIN9xMENT2KXP Copyright (c) 1992-2007 ReMax SoftWare 2000
[16] M Wegmann L Watson and A Hendry ldquoXPS analysis of sub-micrometer barium titanate powderrdquo Journal of the AmericanCeramic Society vol 87 no 3 pp 371ndash377 2004
[17] A B Christie J Lee I Sutherland and J M Walls ldquoAn XPSstudy of ion-induced compositional changes with group II andgroup IV compoundsrdquo Applications of Surface Science vol 15no 1ndash4 pp 224ndash237 1983
[18] U A Joshi S Yoon S Balk and J S Lee ldquoSurfactant-freehydrothermal synthesis of highly tetragonal barium titanatenanowires a structural investigationrdquo Journal of Physical Chem-istry B vol 110 no 25 pp 12249ndash12256 2006
[19] R Caracciolo ldquoChemical characterization techniques for thinfilmsrdquo in Ceramic Films and Coatings J B Wachtman and R AHaber Eds p 376 New Jersey NJ USA 1992
[20] I N Shabanova Y A Naimushina and N S Terebova ldquoCom-position and temperature dependence of a Y-Ba-Cu-O HTSCelectronic structurerdquo Superconductor Science and Technologyvol 15 no 7 pp 1030ndash1033 2002
[21] J Beyer T Schurig S Menkel Z Quan and H Koch ldquoXPSinvestigation of the surface composition of sputtered YBCOthin filmsrdquo Physica C vol 246 no 1-2 pp 156ndash162 1995
[22] C C Chang M S Hegde X D Wu et al ldquoSurface layers onsuperconducting Y-Ba-Cu-O films studied with x-ray photo-electron spectroscopyrdquo Applied Physics Letters vol 55 no 16pp 1680ndash1682 1989
[23] X D Wu A Inam M S Hegde et al ldquoCrystalline perfectionof as-deposited high-Tc superconducting thin-film surfacesion channeling and x-ray photoelectron spectroscopy studyrdquoPhysical Review B vol 38 no 13 pp 9307ndash9310 1988
[24] P Rajasekar P Chakraborty S K Bandyopadhyay P Barat andP Sen ldquoX-ray photoelectron spectroscopy study of oxygen and
Journal of Spectroscopy 13
argon annealed YBa22Cu3O7minus120575
rdquo Modern Physics Letters B vol12 no 6-7 pp 239ndash245 1998
[25] J Halbritter P Walk H J Mathes B Haeuser and H RogallaldquoARXPS-studies of c-axis textured YBa
2Cu3O119909-filmsrdquo Physica
C vol 153ndash155 no 1 pp 127ndash128 1988[26] T J Sarapatka and P Mikusık ldquoXPS study of PbYBaCuO thin-
film tunnel contactrdquo Applied Surface Science vol 68 no 1 pp35ndash40 1993
[27] J A T Verhoeven and H Van Doveren ldquoAn XPS investigationof the interaction of CH
4 C2H2 C2H4and C
2H6with a barium
surfacerdquo Surface Science vol 123 no 2-3 pp 369ndash383 1982[28] C D Wagner W M Riggs L E Davis J F Moulder and G
E Mullenberg Handbook of X-Ray Photoelectron SpectroscopyPerkin-Elmer Corp Eden Prairie Minn USA 1979
[29] M C Biesinger L W M Lau A R Gerson and R S C SmartldquoResolving surface chemical states in XPS analysis of first rowtransition metals oxides and hydroxides Sc Ti V Cu and ZnrdquoApplied Surface Science vol 257 no 3 pp 887ndash898 2010
[30] X Y Fan Z GWu P X Yan et al ldquoFabrication of well-orderedCuO nanowire arrays by direct oxidation of sputter-depositedCu3N filmrdquo Materials Letters vol 62 no 12-13 pp 1805ndash1808
2008[31] S J Kerber J J Bruckner K Wozniak S Seal S Hardcastle
and T L Barr ldquoNature of hydrogen in x-ray photoelectronspectroscopy general patterns from hydroxides to hydrogenbondingrdquo Journal of Vacuum Science and Technology A vol 14no 3 pp 1314ndash1320 1996
[32] G Moretti G Fierro M Lo Jacono and P Porta ldquoCharac-terization of CuO-ZnO catalysts by X-ray photoelectron spec-troscopy precursors calcined and reduced samplesrdquo Surfaceand Interface Analysis vol 14 no 6-7 pp 325ndash336 1989
[33] H Van Doveren and J A T H Verhoeven ldquoXPS spectra of CaSr Ba and their oxidesrdquo Journal of Electron Spectroscopy andRelated Phenomena vol 21 no 3 pp 265ndash273 1980
[34] B V Crist Handbooks of Monochromatic XPS Spectra Volume2mdashCommercially pure binary oxides XPS International LLCLeona Tex USA 2005
[35] D D Sarma and C N R Rao ldquoXPES studies of oxides ofsecond- and third-row transition metals including rare earthsrdquoJournal of Electron Spectroscopy and Related Phenomena vol 20no 1 pp 25ndash45 1980
[36] V I Nefedov and A N Sokolov ldquoDegradatzia visokotemper-aturnich sverchprovodnikov pri khimicheskich vozdeistviachrdquoZhurnal Neorganicheskoi Khimii vol 34 no 11 pp 2723ndash27391989
[37] Y Uwamino T Ishizuka and H Yamatera ldquoX-ray photoelec-tron spectroscopy of rare-earth compoundsrdquo Journal of ElectronSpectroscopy and Related Phenomena vol 34 no 1 pp 67ndash781984
[38] M P Seah and W A Dench ldquoQuantitative electron spec-troscopy of surfaces a standard data base for electron inelasticmean free paths in solidsrdquo Surface and Interface Analysis vol 1no 1 pp 2ndash11 1979
[39] C H Lin H C I Kao and C M Wang ldquoKinetics andstability of R(Ba
15Sr05)Cu3O119910(R = La Nd Sm Eu Gd Dy Ho)
superconductors inwaterrdquoMaterials Chemistry and Physics vol82 no 2 pp 435ndash439 2003
[40] A G Knizhnik R A Stukan and G O Eremenko ldquoStudy theinteraction between europium HTSC of 123 type and waterrdquoSverkhprovodimost vol 4 no 1 pp 177ndash182 1991 (Russian)
[41] J Zhou R K Lo J T McDevitt et al ldquoDevelopment of areliable materials base for superconducting electronicsrdquo Journalof Materials Research vol 12 no 11 pp 2958ndash2975 1997
[42] S B Schougaard M F Ali and J T McDevitt ldquoEvidence forhigh stability against water corrosion of NdBa
2Cu3O7plusmn120575
relativeto YBa
2Cu3OO7minus120575
and EuBa2Cu3OO7minus120575
rdquo Applied Physics Let-ters vol 84 no 7 pp 1144ndash1146 2004
Submit your manuscripts athttpwwwhindawicom
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Inorganic ChemistryInternational Journal of
Hindawi Publishing Corporation httpwwwhindawicom Volume 2014
International Journal ofPhotoenergy
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Carbohydrate Chemistry
International Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Advances in
Physical Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom
Analytical Methods in Chemistry
Journal of
Volume 2014
Bioinorganic Chemistry and ApplicationsHindawi Publishing Corporationhttpwwwhindawicom Volume 2014
SpectroscopyInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
The Scientific World JournalHindawi Publishing Corporation httpwwwhindawicom Volume 2014
Medicinal ChemistryInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Chromatography Research International
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Applied ChemistryJournal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Theoretical ChemistryJournal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Spectroscopy
Analytical ChemistryInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Quantum Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Organic Chemistry International
ElectrochemistryInternational Journal of
Hindawi Publishing Corporation httpwwwhindawicom Volume 2014
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
CatalystsJournal of
10 Journal of Spectroscopy
N-0
N-1
N-10N-2
Y-2
Y-05
N-05
Y-0
Y-10
005 0005
0004
0003
0002
0001
0
0
minus005
minus01
minus015
minus02
minus025
minus03
minus01
minus02
minus03
003
002
001
0
0
0minus001
20 40 60 80 100 120 140119879 (K)
119898(e
mu
g)119898
(em
ug)
119898(e
mu
g)119898
(em
ug)
Figure 8 ZFC magnetizations as a function of temperature at119867 = 50Oe for the initial and mechanically activated samplesYBa2Cu3O6+120575
(top) NdBa2Cu3O6+120575
(bottom)
temperature similarly to Y-10 sample Onset temperature ofthe magnetic anomaly in the hydrated sample is the sameas that in the freshly prepared sample This experimentdemonstrates that the presence of water in MP sampleshas a significant effect on the temperature dependences ofthe magnetization observed in samples of Y-123 series (seeFigure 8)
Temperature dependences of ZFC magnetization of MPsamples in Nd-123 series are shown in Figure 8 The super-conducting transition temperatures of the samples N-0 N-05 and N-1 are independent of milling duration and equal to119879119888sim 57KMechanical treatment leads to a substantial change
in the magnetization of MP samples throughout the inves-tigated temperature range MP samples exhibit near-room-temperature hysteretic behavior that is ZFC magnetizationis more diamagnetic than FCmagnetization It may be due tomagnetic particles of mechanoactivatedNd-123 samples or tothe presence of impurity phases whose low content or highlydisordered crystal structures do not allow to observe thesephases by X-ray diffraction measurements We also cannotexclude the formation of CuO phase (119879
119873sim 220K) at the
surface of large NdBa2Cu3O6+120575
particles proceeding undermechanical activationAt the same time a significant increasein the paramagnetic contribution to the magnetization withincreasing milling duration is observed
004
002
0
minus002
minus004
minus006
minus0080 20 40 60 80 100 120 140
0 20 40 60 80 100 120 140
119898(e
mu)
119898(e
mu)
119879 (K)
119879 (K)
004
0038
0036
0034
Figure 9 FCmagnetizations as a function of temperature of freshlyprepared YBa
2Cu3O6+120575
sample (empty points) and of hydrated sam-ple (black points) at119867 = 500Oe Inset the temperature dependenceof magnetization of hydrated sample at119867 = 10 kOe
A wide transition width around 119879119888= 57K (|Δ119879
119888sim 20K|)
in MP samples of Nd-123 series cannot be explained only bythe presence of water in the structure The observed changesindicate that during MA treatment diffusion processes asso-ciated with the ordering of the cations Nd3+ and Ba2+ appa-rently occur according to [8ndash10] that has a significant effecton 119879119888
4 Discussion of Results
41 Interaction of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
withCO2 From comparison of Figures 4 and 5 it is clear that with
increasing duration of MA processing (120591119892) the amount of
barium-containing impurities on the surface of Nd-123 sam-ples continuously increases up to 120591
119892= 10min in contrast
to the situation for the oxide Y-123 for which initially (up120591119892= 05min) sudden change and subsequent (after 120591
119892=
05min) almost stagnation in the accumulation of chemicaldegradation products were observed (see Figures 2 and 3 anddata on the impurities in YBa
2Cu3O6+120575
sample) One can seefrom Figure 7 that the degree of water saturation (120578) of bothoxides (this parameter can be traced by sharp descendingbranch of sample mass change in the temperature range of30ndash450∘C) obeys similar relationships with increasing 120591
119892 its
growth with increasing MA duration close to proportionalfor Nd-123 (120578 sim 120591
119892) and tendency of 120578 to decrease for Y-123
(120578 = 155 sdot 120591119892
03) which is close to the root dependence char-
acteristic of reagent diffusion through the reaction productslayer
Taking into account the data in [1] stating the chemicaldegradation of Y-123 is carried out on the interface betweenY-123 and gas phase and one can explain sharply fallingrates of change in concentration of its products as well as ofH2O dissolved in the oxide the diffusion path length of H
2O
and CO2reactants to the location of the reactions (1) and
(2) increases with time 120591119892 However the uniformity of the
absorption of H2O and CO
2gases by MP of Nd-123 testifies
Journal of Spectroscopy 11
that the thickness of the degraded layer on the surface variesslightly Apparently it does not exceed 10 nm as indicated bya weak but clear signal of the main phase which appeared inthe Ba 4d-spectrum of N-10 sample (see Figure 5) Howeverit should be noted that Nd-123 MP sample actively entersinto chemical reactionwith atmospheric CO
2 the gas escapes
from the samples quite intensively when heated in the rangeof 800ndash900∘C (see Figure 7) Therefore the question oflocalization place of products of interaction between Nd-123and atmospheric components arises
Homogeneous nucleation and growth of interaction pro-ducts in the volume of Nd
1+xBa2minusxCu3O6+120575 parent phasemaybe the answer This assumption is based on the fact that theproducts of thermal desorption of N-10 sample (see Figure 7)contain weakly bound form of CO
2escaping in a wide tem-
perature range of 200ndash550∘C Obviously it is a form of gasdissolved in the structure Since the carbonization energy ofBa2+ ions is quite high homogeneous nucleation of carbonatephase at a certain concentration (equivactivity) of CO
2in the
structure facilitated by the participation of structural defects(whose concentration should be significant in MP samples)seems quite possible
42 Interaction of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
withWater In the Introductionwe have put links toworks statingthat the crucial feature for the practical application of thesuperconductor Nd-123 is its high resistance to chemicaldegradation under moisture Additional information thatexpands understanding of this feature has been received inour study Thus it is shown (see Figure 7) that a high con-centration of water accumulates in MP samples of Nd-123 indissolved form but the hydrolysis reaction development isquite limited as evidenced by the relatively low temperatureof H2O release from this oxide Moreover the results of
XRD and XPS analyzes have not detected even traces of theternary compound Nd
2BaCuO
5in these samples while it is
the compounds R2BaCuO
5due their characteristic colours
that are indicators of the hydrolysis reaction for the wholefamily of compounds R-123 [1 39 40] Thus if the hydrolysisreaction develops (there is a small peak on H
2O desorption
curve for sample N-10 at sim455∘C that can be attributed tothe chemically bound water) then it proceeds through non-traditional mechanism and with low rate
According to [41] the hydration mechanism for thehomologous series of R-123 compounds is in four stages Atthe initial stage water molecules penetrate into the bulk ofthe crystallites through the structural channels [(12) b 0]located in interspaces between CuO-chains typical for thistype of superconductors At the next stage protons whichare located in the oxygen positions of CuO-chains can besplit up of watermoleculesThis proton transfer is consideredto cause an internal (within the [CundashO]+-system) chargetransfer resulting in formation of molecular oxygen leavingthe structure At high concentrations of hydroxide ionsaccumulated in the structure the chemical decompositionof the initial oxide occurs Based on the previous schemeone can understand the reasons for high resistivity of N-123superconductor to chemical interaction with water
The authors of [42] discussed the high corrosion resis-tance of Nd-123 films in the water compared to the filmstructures of Y-123 and Eu-123 which was attributed to thepartial oxygen disorder in the planes of CuO-chains Sucha disorder should occur in Nd-123 due to the presence ofsome amount of Nd3+ ions in the sites nearby to CuO-planesof divalent barium According to the authors that shouldlead to overlapping structural channels for H
2O diffusion
and hence blocking the hydration process However ourdata on the thermal analysis (see Figure 7) illustrate thatthe saturation of Nd-123 structure with water during MAtreatment proceeds almost as fast as in Y-123 (in the rangeof 2ndash10 minutes even faster) Therefore the sought causeof the chemical stability of Nd-123 MP cannot be related toproblems of H
2O diffusion
The stage of removing oxygen from the structure is con-sidered [41 42] to be extremely important for the hydrationprocess of R-123 Thus the chemical degradation of Y-123oxide immersed in the water is completely stopped underpotential of 08 V relative to the standard electrode-saturatedsodium calomel [41] It is expected that the substitutionNd3+ rarr Ba2+ inNd-123 in addition to oxygen disordering inthe base structural plane should also lead to the strengtheningof its bondwith the lattice (due to electrostatic effect of highlycharged Nd3+ ion) [42] According to the authors [42] thisshould inhibit the reduction stage of hydration However it isimportant to consider the fact that the structure ofMP of Nd-123 contains a large amount of weakly bound CO
2 located
near Ba ions (since there is a tendency to the formation ofBaCO
3) therefore localized in the channels of the base plane
[(12) b 0] where also there is water In our opinion just theseCO2particles block channels of oxygen desorption which is
the main reason for the high stability of Nd-123 in relation tothe hydrolysis reaction
5 Conclusion
Thus as a result of mechanical activation treatment thesurface of YBa
2Cu3O6+120575
is covered by products of hydrolysisand carbonization to a considerable depth The chemicaldegradation process proceeds the normal waymdashthrough theformation of Y
2BaCuO
5phase
Chemical degradation of mechanoactivatedNdBa
2Cu3O6+120575
powders under the impact of CO2
isnot directly connected to hydrolysis process as occurs inYBa2Cu3O6+120575
(see reactions (1) and (2)) Carbonizationproceeds homogeneously through the stage of carbondioxide dissolution in the lattice of NdBa
2Cu3O6+120575
In itsturn the presence of CO
2molecules in the structure of
mechanoactivated NdBa2Cu3O6+120575
powders leads to a radicalchange in the mechanism of interaction between the super-conductor and water This mechanism eliminates the normalfor a homologous series of RBa
2Cu3O6+120575
the hydrolysisreaction with the formation of characteristic ldquocolorrdquoR2BaCuO
5phases The rate of chemical decomposition of
mechanically activated NdBa2Cu3O6+120575
by the new mecha-nism (not yet studied) is quite low
12 Journal of Spectroscopy
Mechanical treatment affects the temperature depen-dence of the magnetization of RBa
2Cu3O6+120575
compoundsThere is a significant increase in the paramagnetic and ferro-magnetic contributions to the magnetization with increasingmilling duration The latter leads to near-room-temperaturehysteretic behavior of NdBa
2Cu3O6+120575
samples between ZFCandFC regimes Itmay be due tomagnetic particles ofmecha-noactivated NdBa
2Cu3O6+120575
samples or to the presence ofimpurity phases whose low content or highly disorderedcrystal structures do not allow to observe these phases byX-ray diffraction measurements The mechanical treatmentdoes not have substantial influence on the transition tem-peratures of superconducting phases 119879
119888in the RBa
2Cu3O6+120575
compounds but a wide transition width around 119879119888indicates
that mechanically activated samples contain inhomogeneoussuperconductor phases with different 119879
119888 The broadening
of the superconducting transition in mechanically activatedNdBa
2Cu3O6+120575
samples may be due to redistribution ofcations between Nd- and Ba-sublattice
Finally we note that the high temperature superconduc-tor RBa
2Cu3O6+120575
subjected to mechanical activation cer-tainly has no significant advantages over conventional non-mechanoactivated material but it is obvious that physical-chemical studies of such powders reveal results interestingfrom the point of view of fundamental science
Acknowledgment
This work was supported by Russian Foundation for BasicResearch (Grant no 11-03-00317-a)
References
[1] I E Graboi A R Kaulrsquo and G Yu Metlin ldquoAdvances in scienceand technologyrdquo in Solid State Chemistry pp 3ndash142 VINITIANSSSR Moscow Russia 1989
[2] S Anders M G Blamire F-Im Buchholz et al ldquoEuropeanroadmap on superconductive electronicsmdashstatus and perspec-tivesrdquo Physica C vol 470 no 23-24 pp 2079ndash2126 2010
[3] B Ruck B Oelze R Dittmann et al ldquoMeasurement of thedynamic error rate of a high temperature superconductor rapidsingle flux quantum comparatorrdquo Applied Physics Letters vol72 no 18 pp 2328ndash2330 1998
[4] M W Rupich X Li C Thieme et al ldquoAdvances in secondgeneration high temperature superconducting wire manufac-turing and RampD at American superconductor corporationrdquoSuperconductor Science and Technology vol 23 no 1 Article ID014015 2010
[5] A Rakitin M Kobayashi and A P Litvinchuk ldquoSuperi-onic behavior of high-temperature superconductorsrdquo PhysicalReview B vol 55 no 1 pp 89ndash92 1997
[6] T Kagiyama J Shimoyama K D Otzschi et al ldquoEffect of cationcomposition and oxygen nonstoichiometry on 119869
119888-119861 properties
of Nd123rdquo Physica C vol 341ndash348 no 2 pp 1445ndash1446 2000
[7] M Badaye J G Wen K Fukushima et al ldquoSuperior propertiesof NdBa
2Cu3O119910over YBa
2Cu3O119909thin filmsrdquo Superconductor
Science and Technology vol 10 no 11 pp 825ndash830 1997
[8] C Cantoni D P Norton D M Kroeger et al ldquoPhase stabilityfor the in situ growth of Nd
1+119909Ba2minus119909
Cu3O119910films using pulsed-
laser depositionrdquo Applied Physics Letters vol 74 no 1 pp 96ndash98 1999
[9] E A Goodilin N N Oleynikov E V Antipov et al ldquoPhasestability for the in situ growth of Nd
1+119909Ba2minus119909
Cu3O119910films using
pulsed-laser depositionrdquo Physica C vol 272 6578 pages 1996[10] E Guilmeau F Giovannelli I Monot-Laffez S Marinel J
Provost and G Desgardin ldquoTop seeding melt texture growthof NdBaCuO pellets in airrdquoThe European Physical Journal vol13 no 3 pp 157ndash160 2001
[11] A I Ancharov T F Grigorrsquoeva T Yu Kiseleva A A Novakovaet al inMechanocomposites-Precursorsfor the Creation of Mate-rials with New Properties O I Lomovskii Ed p 424 Izd-voSO RAN Novosibirsk Russia 2010
[12] A Hamrita F Ben Azzouz A Madani and M Ben SalemldquoMagnetoresistivity and microstructure of YBa
2Cu3O119910pre-
pared using planetary ball millingrdquo Physica C vol 472 no 1pp 34ndash38 2012
[13] R P Vasquez ldquoIntrinsic photoemission signals surface prepa-ration and surface stability of high temperature superconduc-torsrdquo Journal of Electron Spectroscopy and Related Phenomenavol 66 no 3-4 pp 209ndash222 1994
[14] S S Gorelik L N Rastorguev and A Yu Skakov in Rentgeno-graphIcheskII I ElektronographIcheskII AnalIz p 368 Izd-voMetallurgia Moscow Russia 1970
[15] M V Reshetniak and O V Sobol Program for diffractionanalysis ldquoNew Profilerdquo(Last update 10 02 2007) Version 3 4400 (Freeware) WIN9xMENT2KXP Copyright (c) 1992-2007 ReMax SoftWare 2000
[16] M Wegmann L Watson and A Hendry ldquoXPS analysis of sub-micrometer barium titanate powderrdquo Journal of the AmericanCeramic Society vol 87 no 3 pp 371ndash377 2004
[17] A B Christie J Lee I Sutherland and J M Walls ldquoAn XPSstudy of ion-induced compositional changes with group II andgroup IV compoundsrdquo Applications of Surface Science vol 15no 1ndash4 pp 224ndash237 1983
[18] U A Joshi S Yoon S Balk and J S Lee ldquoSurfactant-freehydrothermal synthesis of highly tetragonal barium titanatenanowires a structural investigationrdquo Journal of Physical Chem-istry B vol 110 no 25 pp 12249ndash12256 2006
[19] R Caracciolo ldquoChemical characterization techniques for thinfilmsrdquo in Ceramic Films and Coatings J B Wachtman and R AHaber Eds p 376 New Jersey NJ USA 1992
[20] I N Shabanova Y A Naimushina and N S Terebova ldquoCom-position and temperature dependence of a Y-Ba-Cu-O HTSCelectronic structurerdquo Superconductor Science and Technologyvol 15 no 7 pp 1030ndash1033 2002
[21] J Beyer T Schurig S Menkel Z Quan and H Koch ldquoXPSinvestigation of the surface composition of sputtered YBCOthin filmsrdquo Physica C vol 246 no 1-2 pp 156ndash162 1995
[22] C C Chang M S Hegde X D Wu et al ldquoSurface layers onsuperconducting Y-Ba-Cu-O films studied with x-ray photo-electron spectroscopyrdquo Applied Physics Letters vol 55 no 16pp 1680ndash1682 1989
[23] X D Wu A Inam M S Hegde et al ldquoCrystalline perfectionof as-deposited high-Tc superconducting thin-film surfacesion channeling and x-ray photoelectron spectroscopy studyrdquoPhysical Review B vol 38 no 13 pp 9307ndash9310 1988
[24] P Rajasekar P Chakraborty S K Bandyopadhyay P Barat andP Sen ldquoX-ray photoelectron spectroscopy study of oxygen and
Journal of Spectroscopy 13
argon annealed YBa22Cu3O7minus120575
rdquo Modern Physics Letters B vol12 no 6-7 pp 239ndash245 1998
[25] J Halbritter P Walk H J Mathes B Haeuser and H RogallaldquoARXPS-studies of c-axis textured YBa
2Cu3O119909-filmsrdquo Physica
C vol 153ndash155 no 1 pp 127ndash128 1988[26] T J Sarapatka and P Mikusık ldquoXPS study of PbYBaCuO thin-
film tunnel contactrdquo Applied Surface Science vol 68 no 1 pp35ndash40 1993
[27] J A T Verhoeven and H Van Doveren ldquoAn XPS investigationof the interaction of CH
4 C2H2 C2H4and C
2H6with a barium
surfacerdquo Surface Science vol 123 no 2-3 pp 369ndash383 1982[28] C D Wagner W M Riggs L E Davis J F Moulder and G
E Mullenberg Handbook of X-Ray Photoelectron SpectroscopyPerkin-Elmer Corp Eden Prairie Minn USA 1979
[29] M C Biesinger L W M Lau A R Gerson and R S C SmartldquoResolving surface chemical states in XPS analysis of first rowtransition metals oxides and hydroxides Sc Ti V Cu and ZnrdquoApplied Surface Science vol 257 no 3 pp 887ndash898 2010
[30] X Y Fan Z GWu P X Yan et al ldquoFabrication of well-orderedCuO nanowire arrays by direct oxidation of sputter-depositedCu3N filmrdquo Materials Letters vol 62 no 12-13 pp 1805ndash1808
2008[31] S J Kerber J J Bruckner K Wozniak S Seal S Hardcastle
and T L Barr ldquoNature of hydrogen in x-ray photoelectronspectroscopy general patterns from hydroxides to hydrogenbondingrdquo Journal of Vacuum Science and Technology A vol 14no 3 pp 1314ndash1320 1996
[32] G Moretti G Fierro M Lo Jacono and P Porta ldquoCharac-terization of CuO-ZnO catalysts by X-ray photoelectron spec-troscopy precursors calcined and reduced samplesrdquo Surfaceand Interface Analysis vol 14 no 6-7 pp 325ndash336 1989
[33] H Van Doveren and J A T H Verhoeven ldquoXPS spectra of CaSr Ba and their oxidesrdquo Journal of Electron Spectroscopy andRelated Phenomena vol 21 no 3 pp 265ndash273 1980
[34] B V Crist Handbooks of Monochromatic XPS Spectra Volume2mdashCommercially pure binary oxides XPS International LLCLeona Tex USA 2005
[35] D D Sarma and C N R Rao ldquoXPES studies of oxides ofsecond- and third-row transition metals including rare earthsrdquoJournal of Electron Spectroscopy and Related Phenomena vol 20no 1 pp 25ndash45 1980
[36] V I Nefedov and A N Sokolov ldquoDegradatzia visokotemper-aturnich sverchprovodnikov pri khimicheskich vozdeistviachrdquoZhurnal Neorganicheskoi Khimii vol 34 no 11 pp 2723ndash27391989
[37] Y Uwamino T Ishizuka and H Yamatera ldquoX-ray photoelec-tron spectroscopy of rare-earth compoundsrdquo Journal of ElectronSpectroscopy and Related Phenomena vol 34 no 1 pp 67ndash781984
[38] M P Seah and W A Dench ldquoQuantitative electron spec-troscopy of surfaces a standard data base for electron inelasticmean free paths in solidsrdquo Surface and Interface Analysis vol 1no 1 pp 2ndash11 1979
[39] C H Lin H C I Kao and C M Wang ldquoKinetics andstability of R(Ba
15Sr05)Cu3O119910(R = La Nd Sm Eu Gd Dy Ho)
superconductors inwaterrdquoMaterials Chemistry and Physics vol82 no 2 pp 435ndash439 2003
[40] A G Knizhnik R A Stukan and G O Eremenko ldquoStudy theinteraction between europium HTSC of 123 type and waterrdquoSverkhprovodimost vol 4 no 1 pp 177ndash182 1991 (Russian)
[41] J Zhou R K Lo J T McDevitt et al ldquoDevelopment of areliable materials base for superconducting electronicsrdquo Journalof Materials Research vol 12 no 11 pp 2958ndash2975 1997
[42] S B Schougaard M F Ali and J T McDevitt ldquoEvidence forhigh stability against water corrosion of NdBa
2Cu3O7plusmn120575
relativeto YBa
2Cu3OO7minus120575
and EuBa2Cu3OO7minus120575
rdquo Applied Physics Let-ters vol 84 no 7 pp 1144ndash1146 2004
Submit your manuscripts athttpwwwhindawicom
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Inorganic ChemistryInternational Journal of
Hindawi Publishing Corporation httpwwwhindawicom Volume 2014
International Journal ofPhotoenergy
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Carbohydrate Chemistry
International Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Advances in
Physical Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom
Analytical Methods in Chemistry
Journal of
Volume 2014
Bioinorganic Chemistry and ApplicationsHindawi Publishing Corporationhttpwwwhindawicom Volume 2014
SpectroscopyInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
The Scientific World JournalHindawi Publishing Corporation httpwwwhindawicom Volume 2014
Medicinal ChemistryInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Chromatography Research International
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Applied ChemistryJournal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Theoretical ChemistryJournal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Spectroscopy
Analytical ChemistryInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Quantum Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Organic Chemistry International
ElectrochemistryInternational Journal of
Hindawi Publishing Corporation httpwwwhindawicom Volume 2014
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
CatalystsJournal of
Journal of Spectroscopy 11
that the thickness of the degraded layer on the surface variesslightly Apparently it does not exceed 10 nm as indicated bya weak but clear signal of the main phase which appeared inthe Ba 4d-spectrum of N-10 sample (see Figure 5) Howeverit should be noted that Nd-123 MP sample actively entersinto chemical reactionwith atmospheric CO
2 the gas escapes
from the samples quite intensively when heated in the rangeof 800ndash900∘C (see Figure 7) Therefore the question oflocalization place of products of interaction between Nd-123and atmospheric components arises
Homogeneous nucleation and growth of interaction pro-ducts in the volume of Nd
1+xBa2minusxCu3O6+120575 parent phasemaybe the answer This assumption is based on the fact that theproducts of thermal desorption of N-10 sample (see Figure 7)contain weakly bound form of CO
2escaping in a wide tem-
perature range of 200ndash550∘C Obviously it is a form of gasdissolved in the structure Since the carbonization energy ofBa2+ ions is quite high homogeneous nucleation of carbonatephase at a certain concentration (equivactivity) of CO
2in the
structure facilitated by the participation of structural defects(whose concentration should be significant in MP samples)seems quite possible
42 Interaction of YBa2Cu3O6+120575
and NdBa2Cu3O6+120575
withWater In the Introductionwe have put links toworks statingthat the crucial feature for the practical application of thesuperconductor Nd-123 is its high resistance to chemicaldegradation under moisture Additional information thatexpands understanding of this feature has been received inour study Thus it is shown (see Figure 7) that a high con-centration of water accumulates in MP samples of Nd-123 indissolved form but the hydrolysis reaction development isquite limited as evidenced by the relatively low temperatureof H2O release from this oxide Moreover the results of
XRD and XPS analyzes have not detected even traces of theternary compound Nd
2BaCuO
5in these samples while it is
the compounds R2BaCuO
5due their characteristic colours
that are indicators of the hydrolysis reaction for the wholefamily of compounds R-123 [1 39 40] Thus if the hydrolysisreaction develops (there is a small peak on H
2O desorption
curve for sample N-10 at sim455∘C that can be attributed tothe chemically bound water) then it proceeds through non-traditional mechanism and with low rate
According to [41] the hydration mechanism for thehomologous series of R-123 compounds is in four stages Atthe initial stage water molecules penetrate into the bulk ofthe crystallites through the structural channels [(12) b 0]located in interspaces between CuO-chains typical for thistype of superconductors At the next stage protons whichare located in the oxygen positions of CuO-chains can besplit up of watermoleculesThis proton transfer is consideredto cause an internal (within the [CundashO]+-system) chargetransfer resulting in formation of molecular oxygen leavingthe structure At high concentrations of hydroxide ionsaccumulated in the structure the chemical decompositionof the initial oxide occurs Based on the previous schemeone can understand the reasons for high resistivity of N-123superconductor to chemical interaction with water
The authors of [42] discussed the high corrosion resis-tance of Nd-123 films in the water compared to the filmstructures of Y-123 and Eu-123 which was attributed to thepartial oxygen disorder in the planes of CuO-chains Sucha disorder should occur in Nd-123 due to the presence ofsome amount of Nd3+ ions in the sites nearby to CuO-planesof divalent barium According to the authors that shouldlead to overlapping structural channels for H
2O diffusion
and hence blocking the hydration process However ourdata on the thermal analysis (see Figure 7) illustrate thatthe saturation of Nd-123 structure with water during MAtreatment proceeds almost as fast as in Y-123 (in the rangeof 2ndash10 minutes even faster) Therefore the sought causeof the chemical stability of Nd-123 MP cannot be related toproblems of H
2O diffusion
The stage of removing oxygen from the structure is con-sidered [41 42] to be extremely important for the hydrationprocess of R-123 Thus the chemical degradation of Y-123oxide immersed in the water is completely stopped underpotential of 08 V relative to the standard electrode-saturatedsodium calomel [41] It is expected that the substitutionNd3+ rarr Ba2+ inNd-123 in addition to oxygen disordering inthe base structural plane should also lead to the strengtheningof its bondwith the lattice (due to electrostatic effect of highlycharged Nd3+ ion) [42] According to the authors [42] thisshould inhibit the reduction stage of hydration However it isimportant to consider the fact that the structure ofMP of Nd-123 contains a large amount of weakly bound CO
2 located
near Ba ions (since there is a tendency to the formation ofBaCO
3) therefore localized in the channels of the base plane
[(12) b 0] where also there is water In our opinion just theseCO2particles block channels of oxygen desorption which is
the main reason for the high stability of Nd-123 in relation tothe hydrolysis reaction
5 Conclusion
Thus as a result of mechanical activation treatment thesurface of YBa
2Cu3O6+120575
is covered by products of hydrolysisand carbonization to a considerable depth The chemicaldegradation process proceeds the normal waymdashthrough theformation of Y
2BaCuO
5phase
Chemical degradation of mechanoactivatedNdBa
2Cu3O6+120575
powders under the impact of CO2
isnot directly connected to hydrolysis process as occurs inYBa2Cu3O6+120575
(see reactions (1) and (2)) Carbonizationproceeds homogeneously through the stage of carbondioxide dissolution in the lattice of NdBa
2Cu3O6+120575
In itsturn the presence of CO
2molecules in the structure of
mechanoactivated NdBa2Cu3O6+120575
powders leads to a radicalchange in the mechanism of interaction between the super-conductor and water This mechanism eliminates the normalfor a homologous series of RBa
2Cu3O6+120575
the hydrolysisreaction with the formation of characteristic ldquocolorrdquoR2BaCuO
5phases The rate of chemical decomposition of
mechanically activated NdBa2Cu3O6+120575
by the new mecha-nism (not yet studied) is quite low
12 Journal of Spectroscopy
Mechanical treatment affects the temperature depen-dence of the magnetization of RBa
2Cu3O6+120575
compoundsThere is a significant increase in the paramagnetic and ferro-magnetic contributions to the magnetization with increasingmilling duration The latter leads to near-room-temperaturehysteretic behavior of NdBa
2Cu3O6+120575
samples between ZFCandFC regimes Itmay be due tomagnetic particles ofmecha-noactivated NdBa
2Cu3O6+120575
samples or to the presence ofimpurity phases whose low content or highly disorderedcrystal structures do not allow to observe these phases byX-ray diffraction measurements The mechanical treatmentdoes not have substantial influence on the transition tem-peratures of superconducting phases 119879
119888in the RBa
2Cu3O6+120575
compounds but a wide transition width around 119879119888indicates
that mechanically activated samples contain inhomogeneoussuperconductor phases with different 119879
119888 The broadening
of the superconducting transition in mechanically activatedNdBa
2Cu3O6+120575
samples may be due to redistribution ofcations between Nd- and Ba-sublattice
Finally we note that the high temperature superconduc-tor RBa
2Cu3O6+120575
subjected to mechanical activation cer-tainly has no significant advantages over conventional non-mechanoactivated material but it is obvious that physical-chemical studies of such powders reveal results interestingfrom the point of view of fundamental science
Acknowledgment
This work was supported by Russian Foundation for BasicResearch (Grant no 11-03-00317-a)
References
[1] I E Graboi A R Kaulrsquo and G Yu Metlin ldquoAdvances in scienceand technologyrdquo in Solid State Chemistry pp 3ndash142 VINITIANSSSR Moscow Russia 1989
[2] S Anders M G Blamire F-Im Buchholz et al ldquoEuropeanroadmap on superconductive electronicsmdashstatus and perspec-tivesrdquo Physica C vol 470 no 23-24 pp 2079ndash2126 2010
[3] B Ruck B Oelze R Dittmann et al ldquoMeasurement of thedynamic error rate of a high temperature superconductor rapidsingle flux quantum comparatorrdquo Applied Physics Letters vol72 no 18 pp 2328ndash2330 1998
[4] M W Rupich X Li C Thieme et al ldquoAdvances in secondgeneration high temperature superconducting wire manufac-turing and RampD at American superconductor corporationrdquoSuperconductor Science and Technology vol 23 no 1 Article ID014015 2010
[5] A Rakitin M Kobayashi and A P Litvinchuk ldquoSuperi-onic behavior of high-temperature superconductorsrdquo PhysicalReview B vol 55 no 1 pp 89ndash92 1997
[6] T Kagiyama J Shimoyama K D Otzschi et al ldquoEffect of cationcomposition and oxygen nonstoichiometry on 119869
119888-119861 properties
of Nd123rdquo Physica C vol 341ndash348 no 2 pp 1445ndash1446 2000
[7] M Badaye J G Wen K Fukushima et al ldquoSuperior propertiesof NdBa
2Cu3O119910over YBa
2Cu3O119909thin filmsrdquo Superconductor
Science and Technology vol 10 no 11 pp 825ndash830 1997
[8] C Cantoni D P Norton D M Kroeger et al ldquoPhase stabilityfor the in situ growth of Nd
1+119909Ba2minus119909
Cu3O119910films using pulsed-
laser depositionrdquo Applied Physics Letters vol 74 no 1 pp 96ndash98 1999
[9] E A Goodilin N N Oleynikov E V Antipov et al ldquoPhasestability for the in situ growth of Nd
1+119909Ba2minus119909
Cu3O119910films using
pulsed-laser depositionrdquo Physica C vol 272 6578 pages 1996[10] E Guilmeau F Giovannelli I Monot-Laffez S Marinel J
Provost and G Desgardin ldquoTop seeding melt texture growthof NdBaCuO pellets in airrdquoThe European Physical Journal vol13 no 3 pp 157ndash160 2001
[11] A I Ancharov T F Grigorrsquoeva T Yu Kiseleva A A Novakovaet al inMechanocomposites-Precursorsfor the Creation of Mate-rials with New Properties O I Lomovskii Ed p 424 Izd-voSO RAN Novosibirsk Russia 2010
[12] A Hamrita F Ben Azzouz A Madani and M Ben SalemldquoMagnetoresistivity and microstructure of YBa
2Cu3O119910pre-
pared using planetary ball millingrdquo Physica C vol 472 no 1pp 34ndash38 2012
[13] R P Vasquez ldquoIntrinsic photoemission signals surface prepa-ration and surface stability of high temperature superconduc-torsrdquo Journal of Electron Spectroscopy and Related Phenomenavol 66 no 3-4 pp 209ndash222 1994
[14] S S Gorelik L N Rastorguev and A Yu Skakov in Rentgeno-graphIcheskII I ElektronographIcheskII AnalIz p 368 Izd-voMetallurgia Moscow Russia 1970
[15] M V Reshetniak and O V Sobol Program for diffractionanalysis ldquoNew Profilerdquo(Last update 10 02 2007) Version 3 4400 (Freeware) WIN9xMENT2KXP Copyright (c) 1992-2007 ReMax SoftWare 2000
[16] M Wegmann L Watson and A Hendry ldquoXPS analysis of sub-micrometer barium titanate powderrdquo Journal of the AmericanCeramic Society vol 87 no 3 pp 371ndash377 2004
[17] A B Christie J Lee I Sutherland and J M Walls ldquoAn XPSstudy of ion-induced compositional changes with group II andgroup IV compoundsrdquo Applications of Surface Science vol 15no 1ndash4 pp 224ndash237 1983
[18] U A Joshi S Yoon S Balk and J S Lee ldquoSurfactant-freehydrothermal synthesis of highly tetragonal barium titanatenanowires a structural investigationrdquo Journal of Physical Chem-istry B vol 110 no 25 pp 12249ndash12256 2006
[19] R Caracciolo ldquoChemical characterization techniques for thinfilmsrdquo in Ceramic Films and Coatings J B Wachtman and R AHaber Eds p 376 New Jersey NJ USA 1992
[20] I N Shabanova Y A Naimushina and N S Terebova ldquoCom-position and temperature dependence of a Y-Ba-Cu-O HTSCelectronic structurerdquo Superconductor Science and Technologyvol 15 no 7 pp 1030ndash1033 2002
[21] J Beyer T Schurig S Menkel Z Quan and H Koch ldquoXPSinvestigation of the surface composition of sputtered YBCOthin filmsrdquo Physica C vol 246 no 1-2 pp 156ndash162 1995
[22] C C Chang M S Hegde X D Wu et al ldquoSurface layers onsuperconducting Y-Ba-Cu-O films studied with x-ray photo-electron spectroscopyrdquo Applied Physics Letters vol 55 no 16pp 1680ndash1682 1989
[23] X D Wu A Inam M S Hegde et al ldquoCrystalline perfectionof as-deposited high-Tc superconducting thin-film surfacesion channeling and x-ray photoelectron spectroscopy studyrdquoPhysical Review B vol 38 no 13 pp 9307ndash9310 1988
[24] P Rajasekar P Chakraborty S K Bandyopadhyay P Barat andP Sen ldquoX-ray photoelectron spectroscopy study of oxygen and
Journal of Spectroscopy 13
argon annealed YBa22Cu3O7minus120575
rdquo Modern Physics Letters B vol12 no 6-7 pp 239ndash245 1998
[25] J Halbritter P Walk H J Mathes B Haeuser and H RogallaldquoARXPS-studies of c-axis textured YBa
2Cu3O119909-filmsrdquo Physica
C vol 153ndash155 no 1 pp 127ndash128 1988[26] T J Sarapatka and P Mikusık ldquoXPS study of PbYBaCuO thin-
film tunnel contactrdquo Applied Surface Science vol 68 no 1 pp35ndash40 1993
[27] J A T Verhoeven and H Van Doveren ldquoAn XPS investigationof the interaction of CH
4 C2H2 C2H4and C
2H6with a barium
surfacerdquo Surface Science vol 123 no 2-3 pp 369ndash383 1982[28] C D Wagner W M Riggs L E Davis J F Moulder and G
E Mullenberg Handbook of X-Ray Photoelectron SpectroscopyPerkin-Elmer Corp Eden Prairie Minn USA 1979
[29] M C Biesinger L W M Lau A R Gerson and R S C SmartldquoResolving surface chemical states in XPS analysis of first rowtransition metals oxides and hydroxides Sc Ti V Cu and ZnrdquoApplied Surface Science vol 257 no 3 pp 887ndash898 2010
[30] X Y Fan Z GWu P X Yan et al ldquoFabrication of well-orderedCuO nanowire arrays by direct oxidation of sputter-depositedCu3N filmrdquo Materials Letters vol 62 no 12-13 pp 1805ndash1808
2008[31] S J Kerber J J Bruckner K Wozniak S Seal S Hardcastle
and T L Barr ldquoNature of hydrogen in x-ray photoelectronspectroscopy general patterns from hydroxides to hydrogenbondingrdquo Journal of Vacuum Science and Technology A vol 14no 3 pp 1314ndash1320 1996
[32] G Moretti G Fierro M Lo Jacono and P Porta ldquoCharac-terization of CuO-ZnO catalysts by X-ray photoelectron spec-troscopy precursors calcined and reduced samplesrdquo Surfaceand Interface Analysis vol 14 no 6-7 pp 325ndash336 1989
[33] H Van Doveren and J A T H Verhoeven ldquoXPS spectra of CaSr Ba and their oxidesrdquo Journal of Electron Spectroscopy andRelated Phenomena vol 21 no 3 pp 265ndash273 1980
[34] B V Crist Handbooks of Monochromatic XPS Spectra Volume2mdashCommercially pure binary oxides XPS International LLCLeona Tex USA 2005
[35] D D Sarma and C N R Rao ldquoXPES studies of oxides ofsecond- and third-row transition metals including rare earthsrdquoJournal of Electron Spectroscopy and Related Phenomena vol 20no 1 pp 25ndash45 1980
[36] V I Nefedov and A N Sokolov ldquoDegradatzia visokotemper-aturnich sverchprovodnikov pri khimicheskich vozdeistviachrdquoZhurnal Neorganicheskoi Khimii vol 34 no 11 pp 2723ndash27391989
[37] Y Uwamino T Ishizuka and H Yamatera ldquoX-ray photoelec-tron spectroscopy of rare-earth compoundsrdquo Journal of ElectronSpectroscopy and Related Phenomena vol 34 no 1 pp 67ndash781984
[38] M P Seah and W A Dench ldquoQuantitative electron spec-troscopy of surfaces a standard data base for electron inelasticmean free paths in solidsrdquo Surface and Interface Analysis vol 1no 1 pp 2ndash11 1979
[39] C H Lin H C I Kao and C M Wang ldquoKinetics andstability of R(Ba
15Sr05)Cu3O119910(R = La Nd Sm Eu Gd Dy Ho)
superconductors inwaterrdquoMaterials Chemistry and Physics vol82 no 2 pp 435ndash439 2003
[40] A G Knizhnik R A Stukan and G O Eremenko ldquoStudy theinteraction between europium HTSC of 123 type and waterrdquoSverkhprovodimost vol 4 no 1 pp 177ndash182 1991 (Russian)
[41] J Zhou R K Lo J T McDevitt et al ldquoDevelopment of areliable materials base for superconducting electronicsrdquo Journalof Materials Research vol 12 no 11 pp 2958ndash2975 1997
[42] S B Schougaard M F Ali and J T McDevitt ldquoEvidence forhigh stability against water corrosion of NdBa
2Cu3O7plusmn120575
relativeto YBa
2Cu3OO7minus120575
and EuBa2Cu3OO7minus120575
rdquo Applied Physics Let-ters vol 84 no 7 pp 1144ndash1146 2004
Submit your manuscripts athttpwwwhindawicom
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Inorganic ChemistryInternational Journal of
Hindawi Publishing Corporation httpwwwhindawicom Volume 2014
International Journal ofPhotoenergy
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Carbohydrate Chemistry
International Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Advances in
Physical Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom
Analytical Methods in Chemistry
Journal of
Volume 2014
Bioinorganic Chemistry and ApplicationsHindawi Publishing Corporationhttpwwwhindawicom Volume 2014
SpectroscopyInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
The Scientific World JournalHindawi Publishing Corporation httpwwwhindawicom Volume 2014
Medicinal ChemistryInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Chromatography Research International
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Applied ChemistryJournal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Theoretical ChemistryJournal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Spectroscopy
Analytical ChemistryInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Quantum Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Organic Chemistry International
ElectrochemistryInternational Journal of
Hindawi Publishing Corporation httpwwwhindawicom Volume 2014
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
CatalystsJournal of
12 Journal of Spectroscopy
Mechanical treatment affects the temperature depen-dence of the magnetization of RBa
2Cu3O6+120575
compoundsThere is a significant increase in the paramagnetic and ferro-magnetic contributions to the magnetization with increasingmilling duration The latter leads to near-room-temperaturehysteretic behavior of NdBa
2Cu3O6+120575
samples between ZFCandFC regimes Itmay be due tomagnetic particles ofmecha-noactivated NdBa
2Cu3O6+120575
samples or to the presence ofimpurity phases whose low content or highly disorderedcrystal structures do not allow to observe these phases byX-ray diffraction measurements The mechanical treatmentdoes not have substantial influence on the transition tem-peratures of superconducting phases 119879
119888in the RBa
2Cu3O6+120575
compounds but a wide transition width around 119879119888indicates
that mechanically activated samples contain inhomogeneoussuperconductor phases with different 119879
119888 The broadening
of the superconducting transition in mechanically activatedNdBa
2Cu3O6+120575
samples may be due to redistribution ofcations between Nd- and Ba-sublattice
Finally we note that the high temperature superconduc-tor RBa
2Cu3O6+120575
subjected to mechanical activation cer-tainly has no significant advantages over conventional non-mechanoactivated material but it is obvious that physical-chemical studies of such powders reveal results interestingfrom the point of view of fundamental science
Acknowledgment
This work was supported by Russian Foundation for BasicResearch (Grant no 11-03-00317-a)
References
[1] I E Graboi A R Kaulrsquo and G Yu Metlin ldquoAdvances in scienceand technologyrdquo in Solid State Chemistry pp 3ndash142 VINITIANSSSR Moscow Russia 1989
[2] S Anders M G Blamire F-Im Buchholz et al ldquoEuropeanroadmap on superconductive electronicsmdashstatus and perspec-tivesrdquo Physica C vol 470 no 23-24 pp 2079ndash2126 2010
[3] B Ruck B Oelze R Dittmann et al ldquoMeasurement of thedynamic error rate of a high temperature superconductor rapidsingle flux quantum comparatorrdquo Applied Physics Letters vol72 no 18 pp 2328ndash2330 1998
[4] M W Rupich X Li C Thieme et al ldquoAdvances in secondgeneration high temperature superconducting wire manufac-turing and RampD at American superconductor corporationrdquoSuperconductor Science and Technology vol 23 no 1 Article ID014015 2010
[5] A Rakitin M Kobayashi and A P Litvinchuk ldquoSuperi-onic behavior of high-temperature superconductorsrdquo PhysicalReview B vol 55 no 1 pp 89ndash92 1997
[6] T Kagiyama J Shimoyama K D Otzschi et al ldquoEffect of cationcomposition and oxygen nonstoichiometry on 119869
119888-119861 properties
of Nd123rdquo Physica C vol 341ndash348 no 2 pp 1445ndash1446 2000
[7] M Badaye J G Wen K Fukushima et al ldquoSuperior propertiesof NdBa
2Cu3O119910over YBa
2Cu3O119909thin filmsrdquo Superconductor
Science and Technology vol 10 no 11 pp 825ndash830 1997
[8] C Cantoni D P Norton D M Kroeger et al ldquoPhase stabilityfor the in situ growth of Nd
1+119909Ba2minus119909
Cu3O119910films using pulsed-
laser depositionrdquo Applied Physics Letters vol 74 no 1 pp 96ndash98 1999
[9] E A Goodilin N N Oleynikov E V Antipov et al ldquoPhasestability for the in situ growth of Nd
1+119909Ba2minus119909
Cu3O119910films using
pulsed-laser depositionrdquo Physica C vol 272 6578 pages 1996[10] E Guilmeau F Giovannelli I Monot-Laffez S Marinel J
Provost and G Desgardin ldquoTop seeding melt texture growthof NdBaCuO pellets in airrdquoThe European Physical Journal vol13 no 3 pp 157ndash160 2001
[11] A I Ancharov T F Grigorrsquoeva T Yu Kiseleva A A Novakovaet al inMechanocomposites-Precursorsfor the Creation of Mate-rials with New Properties O I Lomovskii Ed p 424 Izd-voSO RAN Novosibirsk Russia 2010
[12] A Hamrita F Ben Azzouz A Madani and M Ben SalemldquoMagnetoresistivity and microstructure of YBa
2Cu3O119910pre-
pared using planetary ball millingrdquo Physica C vol 472 no 1pp 34ndash38 2012
[13] R P Vasquez ldquoIntrinsic photoemission signals surface prepa-ration and surface stability of high temperature superconduc-torsrdquo Journal of Electron Spectroscopy and Related Phenomenavol 66 no 3-4 pp 209ndash222 1994
[14] S S Gorelik L N Rastorguev and A Yu Skakov in Rentgeno-graphIcheskII I ElektronographIcheskII AnalIz p 368 Izd-voMetallurgia Moscow Russia 1970
[15] M V Reshetniak and O V Sobol Program for diffractionanalysis ldquoNew Profilerdquo(Last update 10 02 2007) Version 3 4400 (Freeware) WIN9xMENT2KXP Copyright (c) 1992-2007 ReMax SoftWare 2000
[16] M Wegmann L Watson and A Hendry ldquoXPS analysis of sub-micrometer barium titanate powderrdquo Journal of the AmericanCeramic Society vol 87 no 3 pp 371ndash377 2004
[17] A B Christie J Lee I Sutherland and J M Walls ldquoAn XPSstudy of ion-induced compositional changes with group II andgroup IV compoundsrdquo Applications of Surface Science vol 15no 1ndash4 pp 224ndash237 1983
[18] U A Joshi S Yoon S Balk and J S Lee ldquoSurfactant-freehydrothermal synthesis of highly tetragonal barium titanatenanowires a structural investigationrdquo Journal of Physical Chem-istry B vol 110 no 25 pp 12249ndash12256 2006
[19] R Caracciolo ldquoChemical characterization techniques for thinfilmsrdquo in Ceramic Films and Coatings J B Wachtman and R AHaber Eds p 376 New Jersey NJ USA 1992
[20] I N Shabanova Y A Naimushina and N S Terebova ldquoCom-position and temperature dependence of a Y-Ba-Cu-O HTSCelectronic structurerdquo Superconductor Science and Technologyvol 15 no 7 pp 1030ndash1033 2002
[21] J Beyer T Schurig S Menkel Z Quan and H Koch ldquoXPSinvestigation of the surface composition of sputtered YBCOthin filmsrdquo Physica C vol 246 no 1-2 pp 156ndash162 1995
[22] C C Chang M S Hegde X D Wu et al ldquoSurface layers onsuperconducting Y-Ba-Cu-O films studied with x-ray photo-electron spectroscopyrdquo Applied Physics Letters vol 55 no 16pp 1680ndash1682 1989
[23] X D Wu A Inam M S Hegde et al ldquoCrystalline perfectionof as-deposited high-Tc superconducting thin-film surfacesion channeling and x-ray photoelectron spectroscopy studyrdquoPhysical Review B vol 38 no 13 pp 9307ndash9310 1988
[24] P Rajasekar P Chakraborty S K Bandyopadhyay P Barat andP Sen ldquoX-ray photoelectron spectroscopy study of oxygen and
Journal of Spectroscopy 13
argon annealed YBa22Cu3O7minus120575
rdquo Modern Physics Letters B vol12 no 6-7 pp 239ndash245 1998
[25] J Halbritter P Walk H J Mathes B Haeuser and H RogallaldquoARXPS-studies of c-axis textured YBa
2Cu3O119909-filmsrdquo Physica
C vol 153ndash155 no 1 pp 127ndash128 1988[26] T J Sarapatka and P Mikusık ldquoXPS study of PbYBaCuO thin-
film tunnel contactrdquo Applied Surface Science vol 68 no 1 pp35ndash40 1993
[27] J A T Verhoeven and H Van Doveren ldquoAn XPS investigationof the interaction of CH
4 C2H2 C2H4and C
2H6with a barium
surfacerdquo Surface Science vol 123 no 2-3 pp 369ndash383 1982[28] C D Wagner W M Riggs L E Davis J F Moulder and G
E Mullenberg Handbook of X-Ray Photoelectron SpectroscopyPerkin-Elmer Corp Eden Prairie Minn USA 1979
[29] M C Biesinger L W M Lau A R Gerson and R S C SmartldquoResolving surface chemical states in XPS analysis of first rowtransition metals oxides and hydroxides Sc Ti V Cu and ZnrdquoApplied Surface Science vol 257 no 3 pp 887ndash898 2010
[30] X Y Fan Z GWu P X Yan et al ldquoFabrication of well-orderedCuO nanowire arrays by direct oxidation of sputter-depositedCu3N filmrdquo Materials Letters vol 62 no 12-13 pp 1805ndash1808
2008[31] S J Kerber J J Bruckner K Wozniak S Seal S Hardcastle
and T L Barr ldquoNature of hydrogen in x-ray photoelectronspectroscopy general patterns from hydroxides to hydrogenbondingrdquo Journal of Vacuum Science and Technology A vol 14no 3 pp 1314ndash1320 1996
[32] G Moretti G Fierro M Lo Jacono and P Porta ldquoCharac-terization of CuO-ZnO catalysts by X-ray photoelectron spec-troscopy precursors calcined and reduced samplesrdquo Surfaceand Interface Analysis vol 14 no 6-7 pp 325ndash336 1989
[33] H Van Doveren and J A T H Verhoeven ldquoXPS spectra of CaSr Ba and their oxidesrdquo Journal of Electron Spectroscopy andRelated Phenomena vol 21 no 3 pp 265ndash273 1980
[34] B V Crist Handbooks of Monochromatic XPS Spectra Volume2mdashCommercially pure binary oxides XPS International LLCLeona Tex USA 2005
[35] D D Sarma and C N R Rao ldquoXPES studies of oxides ofsecond- and third-row transition metals including rare earthsrdquoJournal of Electron Spectroscopy and Related Phenomena vol 20no 1 pp 25ndash45 1980
[36] V I Nefedov and A N Sokolov ldquoDegradatzia visokotemper-aturnich sverchprovodnikov pri khimicheskich vozdeistviachrdquoZhurnal Neorganicheskoi Khimii vol 34 no 11 pp 2723ndash27391989
[37] Y Uwamino T Ishizuka and H Yamatera ldquoX-ray photoelec-tron spectroscopy of rare-earth compoundsrdquo Journal of ElectronSpectroscopy and Related Phenomena vol 34 no 1 pp 67ndash781984
[38] M P Seah and W A Dench ldquoQuantitative electron spec-troscopy of surfaces a standard data base for electron inelasticmean free paths in solidsrdquo Surface and Interface Analysis vol 1no 1 pp 2ndash11 1979
[39] C H Lin H C I Kao and C M Wang ldquoKinetics andstability of R(Ba
15Sr05)Cu3O119910(R = La Nd Sm Eu Gd Dy Ho)
superconductors inwaterrdquoMaterials Chemistry and Physics vol82 no 2 pp 435ndash439 2003
[40] A G Knizhnik R A Stukan and G O Eremenko ldquoStudy theinteraction between europium HTSC of 123 type and waterrdquoSverkhprovodimost vol 4 no 1 pp 177ndash182 1991 (Russian)
[41] J Zhou R K Lo J T McDevitt et al ldquoDevelopment of areliable materials base for superconducting electronicsrdquo Journalof Materials Research vol 12 no 11 pp 2958ndash2975 1997
[42] S B Schougaard M F Ali and J T McDevitt ldquoEvidence forhigh stability against water corrosion of NdBa
2Cu3O7plusmn120575
relativeto YBa
2Cu3OO7minus120575
and EuBa2Cu3OO7minus120575
rdquo Applied Physics Let-ters vol 84 no 7 pp 1144ndash1146 2004
Submit your manuscripts athttpwwwhindawicom
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Inorganic ChemistryInternational Journal of
Hindawi Publishing Corporation httpwwwhindawicom Volume 2014
International Journal ofPhotoenergy
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Carbohydrate Chemistry
International Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Advances in
Physical Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom
Analytical Methods in Chemistry
Journal of
Volume 2014
Bioinorganic Chemistry and ApplicationsHindawi Publishing Corporationhttpwwwhindawicom Volume 2014
SpectroscopyInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
The Scientific World JournalHindawi Publishing Corporation httpwwwhindawicom Volume 2014
Medicinal ChemistryInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Chromatography Research International
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Applied ChemistryJournal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Theoretical ChemistryJournal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Spectroscopy
Analytical ChemistryInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Quantum Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Organic Chemistry International
ElectrochemistryInternational Journal of
Hindawi Publishing Corporation httpwwwhindawicom Volume 2014
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
CatalystsJournal of
Journal of Spectroscopy 13
argon annealed YBa22Cu3O7minus120575
rdquo Modern Physics Letters B vol12 no 6-7 pp 239ndash245 1998
[25] J Halbritter P Walk H J Mathes B Haeuser and H RogallaldquoARXPS-studies of c-axis textured YBa
2Cu3O119909-filmsrdquo Physica
C vol 153ndash155 no 1 pp 127ndash128 1988[26] T J Sarapatka and P Mikusık ldquoXPS study of PbYBaCuO thin-
film tunnel contactrdquo Applied Surface Science vol 68 no 1 pp35ndash40 1993
[27] J A T Verhoeven and H Van Doveren ldquoAn XPS investigationof the interaction of CH
4 C2H2 C2H4and C
2H6with a barium
surfacerdquo Surface Science vol 123 no 2-3 pp 369ndash383 1982[28] C D Wagner W M Riggs L E Davis J F Moulder and G
E Mullenberg Handbook of X-Ray Photoelectron SpectroscopyPerkin-Elmer Corp Eden Prairie Minn USA 1979
[29] M C Biesinger L W M Lau A R Gerson and R S C SmartldquoResolving surface chemical states in XPS analysis of first rowtransition metals oxides and hydroxides Sc Ti V Cu and ZnrdquoApplied Surface Science vol 257 no 3 pp 887ndash898 2010
[30] X Y Fan Z GWu P X Yan et al ldquoFabrication of well-orderedCuO nanowire arrays by direct oxidation of sputter-depositedCu3N filmrdquo Materials Letters vol 62 no 12-13 pp 1805ndash1808
2008[31] S J Kerber J J Bruckner K Wozniak S Seal S Hardcastle
and T L Barr ldquoNature of hydrogen in x-ray photoelectronspectroscopy general patterns from hydroxides to hydrogenbondingrdquo Journal of Vacuum Science and Technology A vol 14no 3 pp 1314ndash1320 1996
[32] G Moretti G Fierro M Lo Jacono and P Porta ldquoCharac-terization of CuO-ZnO catalysts by X-ray photoelectron spec-troscopy precursors calcined and reduced samplesrdquo Surfaceand Interface Analysis vol 14 no 6-7 pp 325ndash336 1989
[33] H Van Doveren and J A T H Verhoeven ldquoXPS spectra of CaSr Ba and their oxidesrdquo Journal of Electron Spectroscopy andRelated Phenomena vol 21 no 3 pp 265ndash273 1980
[34] B V Crist Handbooks of Monochromatic XPS Spectra Volume2mdashCommercially pure binary oxides XPS International LLCLeona Tex USA 2005
[35] D D Sarma and C N R Rao ldquoXPES studies of oxides ofsecond- and third-row transition metals including rare earthsrdquoJournal of Electron Spectroscopy and Related Phenomena vol 20no 1 pp 25ndash45 1980
[36] V I Nefedov and A N Sokolov ldquoDegradatzia visokotemper-aturnich sverchprovodnikov pri khimicheskich vozdeistviachrdquoZhurnal Neorganicheskoi Khimii vol 34 no 11 pp 2723ndash27391989
[37] Y Uwamino T Ishizuka and H Yamatera ldquoX-ray photoelec-tron spectroscopy of rare-earth compoundsrdquo Journal of ElectronSpectroscopy and Related Phenomena vol 34 no 1 pp 67ndash781984
[38] M P Seah and W A Dench ldquoQuantitative electron spec-troscopy of surfaces a standard data base for electron inelasticmean free paths in solidsrdquo Surface and Interface Analysis vol 1no 1 pp 2ndash11 1979
[39] C H Lin H C I Kao and C M Wang ldquoKinetics andstability of R(Ba
15Sr05)Cu3O119910(R = La Nd Sm Eu Gd Dy Ho)
superconductors inwaterrdquoMaterials Chemistry and Physics vol82 no 2 pp 435ndash439 2003
[40] A G Knizhnik R A Stukan and G O Eremenko ldquoStudy theinteraction between europium HTSC of 123 type and waterrdquoSverkhprovodimost vol 4 no 1 pp 177ndash182 1991 (Russian)
[41] J Zhou R K Lo J T McDevitt et al ldquoDevelopment of areliable materials base for superconducting electronicsrdquo Journalof Materials Research vol 12 no 11 pp 2958ndash2975 1997
[42] S B Schougaard M F Ali and J T McDevitt ldquoEvidence forhigh stability against water corrosion of NdBa
2Cu3O7plusmn120575
relativeto YBa
2Cu3OO7minus120575
and EuBa2Cu3OO7minus120575
rdquo Applied Physics Let-ters vol 84 no 7 pp 1144ndash1146 2004
Submit your manuscripts athttpwwwhindawicom
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Inorganic ChemistryInternational Journal of
Hindawi Publishing Corporation httpwwwhindawicom Volume 2014
International Journal ofPhotoenergy
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Carbohydrate Chemistry
International Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Advances in
Physical Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom
Analytical Methods in Chemistry
Journal of
Volume 2014
Bioinorganic Chemistry and ApplicationsHindawi Publishing Corporationhttpwwwhindawicom Volume 2014
SpectroscopyInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
The Scientific World JournalHindawi Publishing Corporation httpwwwhindawicom Volume 2014
Medicinal ChemistryInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Chromatography Research International
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Applied ChemistryJournal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Theoretical ChemistryJournal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Spectroscopy
Analytical ChemistryInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Quantum Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Organic Chemistry International
ElectrochemistryInternational Journal of
Hindawi Publishing Corporation httpwwwhindawicom Volume 2014
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
CatalystsJournal of
Submit your manuscripts athttpwwwhindawicom
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Inorganic ChemistryInternational Journal of
Hindawi Publishing Corporation httpwwwhindawicom Volume 2014
International Journal ofPhotoenergy
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Carbohydrate Chemistry
International Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Advances in
Physical Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom
Analytical Methods in Chemistry
Journal of
Volume 2014
Bioinorganic Chemistry and ApplicationsHindawi Publishing Corporationhttpwwwhindawicom Volume 2014
SpectroscopyInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
The Scientific World JournalHindawi Publishing Corporation httpwwwhindawicom Volume 2014
Medicinal ChemistryInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Chromatography Research International
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Applied ChemistryJournal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Theoretical ChemistryJournal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Spectroscopy
Analytical ChemistryInternational Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Journal of
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Quantum Chemistry
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
Organic Chemistry International
ElectrochemistryInternational Journal of
Hindawi Publishing Corporation httpwwwhindawicom Volume 2014
Hindawi Publishing Corporationhttpwwwhindawicom Volume 2014
CatalystsJournal of