ResearchArticle - Hindawi Publishing Corporationdownloads.hindawi.com/journals/ijo/2019/6527327.pdf · ResearchArticle Collective Optical, FTIR, and Photoluminescence Spectra of CeO

Research ArticleCollective Optical FTIR and Photoluminescence Spectra ofCeO2 andor Sm2O3-Doped Na2OndashZnOndashP2O5 Glasses

M A Marzouk 1 H A ElBatal1 Y M Hamdy2 and F M Ezz-Eldin3

1Glass Research Department National Research Center 33 El Bohouth Street (formerly EL Tahrir) PO 12622 Dokki Giza Egypt2Spectroscopy Department National Research Center 33 El Bohouth Street (formerly EL Tahrir) PO 12622 Dokki Giza Egypt3National Center for Radiation Research amp Technology Egyptian Atomic Energy Authority Nasr City Cairo Egypt

Correspondence should be addressed to M A Marzouk marzouk nrcyahoocom

Received 5 November 2018 Accepted 20 December 2018 Published 3 February 2019

Academic Editor Sulaiman W Harun

Copyright copy 2019 M A Marzouk et alThis 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

Glasses with the Na2OndashZnOndashP2O5 composition and doped with single CeO2 Sm2O3 or mixed dopants were melted and studiedCollective optical photoluminescence and FT-infrared spectral studies were carried out CeO2-doped glasses show two extraUV absorption bands due to Ce4+ and Ce3+ ions while Sm2O3-doped samples reveal pronounced peaks collected into twosegments from 367 to 472nm and from 950 to 1623 nm which are characteristic of absorption from Sm3+ ions The mixed dopantsglasses show combined UV-visiblendashnear-IR absorption peaks due to cerium (Ce4+ Ce3+) ions and samarium (Sm3+) ions Thephotoluminescence spectra (PL) of the single CeO2-doped and Sm2O3-doped glasses and even the mixed dopant sample revealluminescence spectra after excitation which are characteristic of the rare-earth ions The intensities for both excited or emittedpeaks are found to increase with the increase of the rare-earth percent FTIR spectra of the glasses show pronounced vibrationalpeaks related to phosphate groups (Q2 and Q3 units) in accordance with the P2O5 percent (70mol )

1 Introduction

Phosphate glasses possess unique and interesting opticalthermal and electrical properties which make them can-didates for a wide range of applications [1 2] The lowchemical durability of phosphate glasses has been changedby the addition of multivalent oxides (such as Al2O3 PbOZnO Fe2O3) the resulting glasses have extended applicationsincluding sealing glass optical glass and biocompatible andbioactive glasses and even iron phosphate has been studiedextensively for encapsulation of some radioactive wastes [34]

Phosphate glasses doped with a transition metal or rare-earth ions are considered as valuable materials for bothoptical and electrical applications [4ndash7] They can incorpo-rate high percent of TMs or REs with brilliant colors anddistinctive optical and electrical properties [4 6]

Extended studies of 3d transitionmetal ions dopedwithindifferent phosphate glasses [8ndash12] indicated that most of theTMs ions exhibit their lower valencesThiswas assumed to be

due to the oxidoreduction equilibrium being shifted towardsthe reduced lower valence states [8] On the other hand mostrare-earth ions are stable in trivalent valence state and theircharacteristic optical spectra remain unaffected by the hostglasses when melted under normal atmospheric conditionbecause their electronic shell is protected from the effects ofthe ligand fields by the outer 5s and 5p electrons [13ndash15] Anexception is sometimes found in the lighter rare-earth ceriumions which are frequently identified in both the three- andfourndashvalence states [15]

Glasses with dopants of rare-earth ions have continuouslydrawn the attention through their potential applications insolid-state lasers optical amplifiers and three-dimensionaldisplays [16 17] Samarium ion (Sm3+-4f5) is one of the highlydistinguished lanthanide ions for being able to characterizethe fluorescence properties such as its emitting 4G52 levelThis mentioned level possesses relatively high quantumefficiency besides different quenching emission channels [18]

Cerium ions have the ability to exist in two possiblevalence states ie Ce3+ and Ce4+ whose percents depend

HindawiInternational Journal of OpticsVolume 2019 Article ID 6527327 11 pageshttpsdoiorg10115520196527327

2 International Journal of Optics

Table 1 Chemical composition of the prepared glasses

Sample Mol P2O5 ZnO Na2O Al2O3 CeO2 Sm2O3

G1 70 20 10 1 0 0G1 70 20 10 1 05 0G2 70 20 10 1 2 0G3 70 20 10 1 5 0G4 70 20 10 1 0 05G5 70 20 10 1 0 2G6 70 20 10 1 0 5G7 70 20 10 1 025 025G8 70 20 10 1 1 1G9 70 20 10 1 25 25

on the host material as well as on the preparation condition[19 20]

In a previous publication [21] combined optical FTIRand photoluminescence spectral analysis have been carriedout for Sm2O3 (02 997888rarr 3) doped in host NaFndashAlF3-phosphate glasses before and after successive gamma irra-diation Spectral data indicate the stability of the Sm3+ ionswith their characteristic absorption bands distributed intotwo regions at 350ndash900 and 1100-1600nm even after gammairradiation The same behavior holds for the luminescencespectra FTIR spectra of the mentioned fluorophosphatesglasses show phosphate groups (mainly of Q2 and Q3) withthe assumption of the formation of (PO3F) AlF4 or AlF6groups and the spectral data also show obvious stabilitytowards gamma irradiation

In the course of the present study the main objectiveis to study combined optical FTIR and photoluminescencespectra of prepared single doped rare-earth oxide of eitherCeO2 or Sm2O3 or with both the two RE oxides as mixeddopants in a host Na2OndashZnOndashP2O5 glass with added 1Al2O3 for stability The two selected rare-earth oxides areknown to exhibit different characteristics CeO2 is able toexist in two different valences (Ce3+ Ce4+) and their specificspectra are within the UVndashnear visible region On the otherhand Sm2O3 is accepted to be stable as trivalent Sm3+ ionsunder normal conditions and exhibits extended visible near-IR optical absorption

It is expected that the collective spectral studies will throwmore insight to find out the interferences or themixing effectsof both the two rare-earth oxides specifically the ability ofCeO2 to act as oxidoreduction agent in the studied hostglasses

2 Experimental Details

The glasses were prepared from laboratory chemicals includ-ing ammonium dihydrogen phosphate (NH4H2PO4) forP2O5 Na2O was added in the form of anhydrous sodiumcarbonate (Na2CO3) and ZnO and Al2O3 were added assuch The dopant rare-earth oxides were introduced as CeO2and Sm2O3 The detailed chemical compositions of theglasses are given in Table 1

The weighed batches were melted in covered aluminacrucibles at 1100∘C for 90 minutes in an electric SiC heatedfurnace (Vecstar UK) under ordinary atmospheric conditionThe melts were rotated at intervals of 20 minutes to reachmixing and homogeneity Then the melts were poured intothe stainless steel mold with the required dimensions Theprepared glasses were transferred immediately to an anneal-ing muffle regulated at 300∘C to obtain samples free fromstress or strains The annealing muffle was switched off after1 hour with the samples inside and left to cool to roomtemperature at a rate of 30∘Ch

Characterizations of the produced glasses were carriedout according procedures of the previouswork [22] as follows

Optical (UV-visiblendashNIR) absorption spectral measure-ments were carried out on polished glasses of equal thickness(2mm plusmn 01mm) using a recording spectrophotometer (typeJASCO V-570 JAPAN) covering the range 200 to 2500nm

Photoluminescence measurements were measured atroom temperature under different excitation wavelengthsusing a fluorescence spectrophotometer (type JASCO FP-6500 JAPAN) equipped with a xenon flash lamp as theexcitation light source The scan speed is 015 step-1 with astep length of 025 nm and slit width of 02 nm

The thermal expansion characteristics of the studiedglasses were measured through specified samples using arecording dilatometer (type NETZCH 1- 402 PC GeratebauGmbH Selb Germany) with a heating rate of 10∘Cmin upto both transformation region and dilatometric softeningtemperature The thermal data were collected and analyzed

FTIR measurements of the prepared glasses and theircorresponding glass-ceramic derivatives were carried out atroom temperature in the wavenumber range 4000ndash400 cmminus1by a Fourier transform computerized spectrometer (typeFTIRndash4600 JASCO Crop JAPAN) Through the KBr disctechnique glasses or glass-ceramics in the form of pulverizedpowder were examined by mixing 2mg of the powderedsamples and 200mg KBr and the mixtures were subjectedto a load of 5 tonscm2 in an evocable die to produceclear homogeneous discs The prepared discs were measureddirectly to avoid moisture attack Infrared spectra werecorrelated for the dark current noises and background usingthe two-point baseline correction

International Journal of Optics 3A

bsor

banc

e (a

u)

Wavelength (nm)

Wavelength (nm)

Abs

orba

nce (

au

)

305

234

12001000800600400200

400350300250200

Figure 1 Optical absorption spectrum of base undoped Na2OminusZnOndashP2O5 glass with the deconvoluted spectrum of the UV region200ndash400 nm

3 Results and Discussion

31 Optical Absorption Spectra of the Prepared GlassesFigure 1 shows the spectrum of the base undopedNa2OndashZnOndashP2O5 glass The spectrum reveals distinctand broad UV absorption with the deconvoluted spectrumshowing two peaks at 234 and 305 nm and without anyfurther absorption to the end of measurements

The undoped Na2OndashZnOndashP2O5 glass shows strong UVabsorption (Figure 1) which is attributed to unavoidabletrace iron impurities present within the chemicals used forthe preparation of such glass This assumption is based onextended postulations introduced by various scientists in thepast [23 24] and in recent studies on undoped phosphateglasses [7 11ndash15 24] The strong support of this assumptioncomes from the review article by Duffy [25] who classifiedcharge transfer UV spectra identified in undoped glassesHe claimed that the presence of traces from some transitionmetals (eg Fe3+ Cr6+) produces UV absorption bandsdeveloped through electron transfer mechanism finding thateven the traces of impurities are in the ppm level

We are accepting the previous assumptions about therelation between the observed UV absorption in the studiedundoped phosphate glass and traces iron (Fe3+) ions presentin the chemicals used

Figure 2 illustrates the UV-visible absorption spectra ofthe three glasses containing varying CeO2 contents (05 25 CeO2) The three glasses reveal the same strong UVabsorption extended from 200 nm to about 330 nm and theattached deconvoluted spectra show three peaks at 210 264and 300 nm The spectral curves are very close to each otherwithout any change with the increase of CeO2 content

The optical spectra of CeO2-doped glasses exhibitextendedUV absorption with three distinct peaks at 210 264and 300 nm and without any variations with the increase ofthe CeO2 content The interpretation of the optical spectra ofCeO2 -doped glasses can be introduced as follows

Abs

orba

nce (

au

)

Wavelength (nm)

Wavelength (nm)150 200 250 300 350 400

210

nm

264

nm

300

nm

05 CeO

2 CeO

5 CeO

24002200200018001600140012001000800600400200

Figure 2 Optical absorption spectra of CeO2-doped glasses withthe attached deconvoluted spectrum (200ndash400nm)

(1) The cerium ions belong to the lighter portion of thelanthanides and are recognized to be solely able toexist in two valences in glasses as Ce3+ and Ce4+ withthe electronic configuration of f4 and f0 respectively[15 26 27]

(2) The optical spectrum of Ce3+ ion is an allowedtransition (f4 997888rarrd1) which is accepted to appear as anintense broad band in many solid materials and theabsorption depends strongly on the host materialsbut in glasses the absorption of Ce4+ is charge transfer(O2+ 997888rarrCe4+) in nature and normally occurs atlonger wavelength in comparison with that for Ce3+[15 26 27]

(3) Based on previous considerations the optical absorp-tion band at 264 nm can be related to Ce4+ ions theband at 300 nm is correlated with Ce3+ ions and theband at 210 nm is the same as the undoped samplerelated to trace iron impurities

Figure 3 reveals absorption spectra of the three Sm2O3-doped glasses The optical spectrum of the first 05 Sm2O3glass shows extended UV-visible to near IR absorption

The optical spectrum consists of strong UV absorbedbands in the range 200ndash300 nm followed by the characteristicabsorption of Sm3+ ions extending into two regions the firstpart with 3 bands from about 367 to 472 nm and the secondpart extends within the region from about 950 to 1623 nmwith 10 peaksThe samples containing higher Sm2O3 contents(2 5) show an increase in the intensities of the peaks and arespecifically prominent in the second series

The spectra of the Sm2O3-doped glasses reveal distinctUV absorption besides distinct two absorption regions thefirst comprises three peaks from about 367 to 472 nm and thesecond consists of 10 peaks and extends from 950 to 1623 nm


Figure 3 Optical absorption spectra of Sm2O3-doped glasses withattached deconvoluted spectrum (UV 200ndash350 nm)

The overall extended optical spectrum covering the rangefrom 200 to about 1700nm is explained as follows

(i) The UV absorption band at 210 nm is correlated withtrace iron (Fe3+) present as impurities

(ii) It is recognized by many scientists [14ndash18 21 28ndash30]that the Sm3+ ion belongs to a d5 electron config-uration which is characterized by 1982s+1Lj free ionlevels In glasses the crystal field fine structure is notresolved due to an inhomogeneous line broadeningand the only absorption between 2s+1Lj manifoldsis observed experimentally The identified peaks areobserved to decrease with the presence of high atomicweights ions (Pb2+ Bi3+) [17 21]

(iii) The identified absorption peaks are considered tooriginate from transitions from ground state 6H52 tothe various excited states as cited in Table 2

Figure 4 presents the absorption spectral bands of thethree glasses containing mixed and equal dopants (025+02510+10 25 +25) of both Sm2O3 and CeO2 The spectra revealthe combination of theUV spectra due to cerium ions and thecharacteristic spectra of the two series of characteristic peaksdue to Sm3+ ions

32 Photoluminescence Spectra of the Studied Glasses Fig-ure 5 reveals the PL spectra of the three CeO2-doped glasses(05 2 5) The PL spectra show two broad emission bandsa highly intense one at 335nm and the second with mediumintensity at 658 nm after the excitation with 120582ex = 290nmand they increase in intensity with the increase of CeO2content On the other hand with the emission at 120582em =658 nm a very broad band extending to 290nm is identifiedwith its deconvoluted peaks The emission spectrum showstwo broad bands the first is at 332 nm and the second is

Table 2 Absorption peaks from Sm2O3-doped Na2OndashZnOndashP2O5glasses and their excitation levels ground state 6H52 997888rarr

Peaks nm Excited state367 4D12 +

4P72405 6P52

4K112472 4I12+

4I132+4M152

950 6F1121038 6F921238 6F721385 6F521489 6F321552 6F121623 6H152

Abs

orba

nce (

au

)

Wavelength (nm)

Wavelength (nm)

293

nm252

nm

206

nm

025 CeO - 025SmO

100 CeO - 100SmO

250 CeO - 250SmO

2000 2200 240018001600140012001000800600400200

200 250 300 35036

9 438

400

945

1085

1234

1381

1489

1548

1620

1590

472

Figure 4 Optical absorption spectra of CeO2 + Sm2O3-dopedglasses with attached deconvoluted spectrum (UV 200ndash350nm)

a broad curvature centered at about 658 nm after excitationwith 235nm The first band increases with the sharp peakwith the increase of CeO2 while the second band is retainingits broad feature

Figure 6 illustrates the PL spectra of the three Sm2O3-doped glasses (05 2 5) Figure 6(c) reveals the excitationspectra after 120582ex = 595nm showing 7 peaks extending from320 and 450 nm with the highest peak at 402 nm and theirintensities increase with the Sm2O3 content On the otherhand the emission spectrum after 120582ex = 365 nm reveals fourbroad bands which are identified at about 570 600 640 and700nm and their intensities increase with the increase ofSm2O3 contentWith excitation at120582ex = 402 nm the emissionspectra show the same peaks

Figure 7 shows the PL spectra of the samples withmixed dopants of (CeO2 + Sm2O3) The excitation spectraafter excitation with 120582em = 595 (Figure 7(c)) show multipleextended peaks from 320 to 450 nm with the highest peakat about 402 nm and with two attached small peaks The

International Journal of Optics 5

Inte

nsity

(au

)

335

nm 658 nmＲ=290 nm

Inte

nsity

(au

)

332

nm

658

nm

Ｒ=235 nm

05 CeO

2 CeO

5 CeO

235

290

320300280260240220200

Wavelength (nm)1000800 900600 700500400300200

(a)

(b)(c)

Figure 5 Photoluminescence spectra of CeO2-doped glasses (a) emission at 235 nm (b) emission at 120582ex = 290 nm and (c) excitations at 120582em= 658 nm

emission spectra reveal three peaks at about 560 595 and640 nm in both the excitations at 120582ex = 365 nm and at 120582ex= 402 nm and the second peak is the highest one On theother hand upon excitation at 120582ex = 290 nm three peaks areidentified at about 570 598 and 650 nm with the last onehaving the highest intensity Also the intensities increasewiththe increase of dopants

The PL spectra of the studied single or mixed dopedglasses are illustrated (Figures 5 6 and 7) The PL data areexplained as follows

(a) For CeO2 doped glasses

(i) The previous optical absorption data confirmthe assumption of the presence of cerium ionsin both the two valence states as both Ce3+ andCe4+ ions

(ii) The excitation spectra of CeO2-doped glassesare identified to be with different responses withthe excitation peaks 120582ex = 290 nm or 120582ex =

332nm In the first case two emission bands areobserved at 335 and 658 nm with high intensitywhile in the second case the identified bandsare low in intensity These observed emissionsand excitation data point out that the twovalence states of cerium ions can be realized andidentified in some excitations

(iii) The excitation spectra of CeO2-doped glassesreveal the main broad band at 290 nm

(b) For Sm2O3-doped glasses The PL spectra shownin Figure 6 of the Sm2O3-doped glasses agree toa large extent with the PL spectra identified bySm2O3-doped in fluorophosphate glasses previouslypublished by the same authors [21] These resultsare comparable with that reached by various authors[31 32] for Sm2O3-doped in binary alkali phosphatemixed alkali phosphate and also lead phosphateglassesThe four emission bands at 570 600 640 and


Inte

nsity

(au

)

05SmO

2 SmO

5 SmO

300 320 340 360 380 400 420

697

642

596

560

750700650600550500450

702

642

596

560

440 46034

4 362

375

402

416

440

333

Wavelength (nm)

(a)

(c)

(b)

Figure 6 Photoluminescence spectra of Sm2O3-doped glasses (a) emission at 365 nm (b) emission at 120582ex = 402 nm and (c) excitations at120582em = 595 nm

700nm can be assigned to transitions 4G52 997888rarr6H52

4G52 997888rarr6H72

4G52 997888rarr6H92 and

4G52 997888rarr6H132

respectively of Sm3+ ions as assigned by differentauthors [31 32]

(c) For mixed dopants of CeO2 + Sm2O3ndashglasses ThePL spectra of the mixed dopants glasses reveal quitesimilar data to that obtained by Sm2O3-doped glasses

This refers to the dominance of the photolumines-cence spectra of the Sm3+ ions than that for Ce3+ions which are restricted to absorption of a lighterlanthanide

33 ermal Expansion Measurements Figure 8 illustratesthe thermal expansion behavior of selected four glasses


Inte

nsity

(au

)

025 CeO2 +025 Sm2O31 CeO2 + 1 Sm2O325 CeO2 + 25 Sm2O3

Wavelength (nm)

(b)

(d)

(a)

700

642

595

560

642

596

560

650

596

561

800750700650600550500450400350

320 340 360 380 400 420 440 460

362

374

402

416

440

344

333

(c)

Figure 7 Photoluminescence spectra of mixed CeO2 + Sm2O3-doped glasses (a) emission at 120582ex =290 nm (b) emission at 120582ex = 365 nm (c)emission at 120582ex = 402nm and (d) excitations at 120582em = 595 nm

including the undoped sample 5 CeO2 doped sample5 Sm2O3-doped sample and sample containing mixeddopants of 25 CeO2 + 25 Sm2O3 All the glasses show eithernegative or low thermal expansion coefficient within thetemperature range 25ndash250∘C which then increases steadilywith temperature until reaching the transformation range fol-lowed by a high increase in expansion until the dilatometric

softening temperature After that a rapid drop is observedThe dilatometric softening temperature is very close in thefirst three samples (412ndash418∘C) and thenhighly increaseswiththe mixed sample to reach 453∘C

It is accepted that glass like most solids generallyexpands on heating The possible dimensional changes whichcan occur with heating are very interesting and of particular


Temperature ∘C

dLL

olowast10

-3

0 Base5 CeO25 Sm2O325 CeO2+ 25 Sm2O3

435 ∘C

418 ∘C412 ∘C

412 ∘C

500450400350300250200150100500

30

25

20

15

10

05

00

minus05

Figure 8 Dilatometric thermal expansion of some selected glasses

importance for the application in sealing purposes and thecapability of the glass to withstand thermal shock or cycling[4 33]

Thermal expansion of close-packed structure (such asNaCl) is a direct result of an increase in bond length withincreasing temperature While the simple lattice vibrationmodel works well for close-packed structures an additionalprocess can occur in less tightly packed network structuresor nonperiodic arrangement state such as those found inglasses Bond bending can alter the positions of atoms ascan rotation about an axis These processes can counterpartthe expansion of the bond length due to the increasedamplitude of vibrations resulting in a very low expansioncoefficient Filling of interstices inhibits these mentionedvibration processes and tends to cause an increase in thethermal expansion coefficient

The thermal data can thus be realized by the assumptionthat rare-earth ions are accepted to be situated within inter-stitial positions and thus lead to the identified increase of thedilatometric softening temperatures The more filling of theinterstices bymixed dopants is observed to givemore increasein the dilatometric softening temperature

34 FT-Infrared Absorption Spectra Figure 9 shows the FTIRspectra of the three CeO2-doped glasses The IR spectra ingeneral are almost similar and condensed extending from400to 1400 cmminus1 with distinct broad band at the far-IR regionpeaking at about 496 cmminus1 followed by a medium broad withtwo peaks at about 725 and 790 cmminus1 and succeeded by a verybroad and distinct connected bands extending from about850 to 1400 cmminus1 with four peaks at about 880 980 1086 and1246 cmminus1 The deconvoluted spectrum shows the following8 IR peaks 410 490 725 788 878 970 1089 and 1246 cmminus1

Figure 10 illustrates the FTIR spectra of Sm2O3-dopedglasses The IR spectra are observed to be the same asshown in Figure 9 and with similar spectral details The

deconvoluted spectrum shows 9 IR peaks at 417 463 535 684770 880 941 1072 and 1273 cmminus1

Figure 11 reveals the FTIR spectra of the glasses contain-ing mixed dopants of the two RE oxides The IR spectralcurves are comparable to the spectra shown in Figures 9 and10 The convoluted spectrum shows the following 8 IR peaks410 515 721 784 889 945 1083 and 1282 cmminus1

The FTIR spectra are shown in Figures 9 10 and 11revealing the detailed IR vibrational bands due to CeO2-doped glasses Sm2O3-doped glasses and selected mixeddopants glasses The IR spectral curves show composite andextended peaks extending from400 to 1400 cmminus1 and they areclearly analyzed through the deconvoluted process to indicateall the hidden or overlapped peaks of the glasses

The interpretation of the IR results can be clearly under-stood on the following basic parameters [34ndash38]

(a) The IR vibrational bands are considered to be fin-gerprints of the structural building units within thestudied glasses in comparison with that obtainedfrom crystalline analogs

(b) The structural building units are virtually emanatingor formed in relation to the chemical composition ofall the constituents The basic host glass is composedof main glass forming oxide (70 P2O5) whichindicates that the expected glass forming phosphategroups are (Q2ndashQ3) The true modifier oxide consti-tutes of (10 Na2O) while ZnO which is consideredas conditional oxide has the ability to be a modifieror can share as (ZnO4) groups in some cases whereoxygens are available from alkali oxide to be able toform such tetrahedral groups The 1 Al2O3 is addedonly to maintain chemical stability or preventingdevitrification

(c) Thedetailed attributions of the vibrational peaks fromthe deconvoluted spectrum of the base undoped glassare summarized as follows [22 34ndash39]

(i) The far-IR peaks at 410ndash490 cmminus1 can be relatedto OndashPndashO bending or lattice mode vibrations of120575(PO2)

(ii) The mid peaks at 725ndash790 cmminus1 are relatedto symmetric stretching vibrations of PndashOndashPbonding

(iii) The peaks at 878ndash970 1089 cmminus1 can be relatedto asymmetric stretching vibrations of PO2groups

(iv) The peak at 1296 cmminus1 can be correlated withasymmetric stretching of doubly bonded oxy-gen vibrations (P = O) modes

(v) The IR vibrational curves of the single doped(CeO2 Sm2O3) or mixed dopants reveal no dis-tinct variations but only some limited changesin some of the vibrational peaks and these canbe related to some limited depolymerization ofrare-earth oxides as dopants


Wavenumber (cm-1)

Abs

orba

nce (

au

)

400600800100012001400

(b)

(c)

(a) 410

490

725

878

788

970

1089

1246

Figure 9 FT-infrared absorption spectra of (a) 05 (b) 2 and (c) 5 CeO2-doped glasses

Wavenumber (cm-1)

Abs

orba

nce (

au

)

400600800100012001400

(b)

(c)

(a) 41746

3535

68478

0880

941

107212

73

Figure 10 FT-infrared absorption spectra of (a) 05 (b) 2 and (c) 5 Sm2O3-doped glasses

410

515

721

400600800100012001400Wavenumber (cm-1)

Abs

orba

nce (

au

)

(b)

(c)

(a)

784

889

945

1083

1282

Figure 11 FT-infrared absorption spectra of (a) 025 CeO2 + 025 Sm2O3 (b) 1 CeO2 + 1 Sm2O3 and (c) 25 CeO2 + 25 Sm2O3-doped glasses


4 Conclusion

Combined optical FTIR and photoluminescence spectrahave been carried out for CeO2- or Sm2O3-doped hostNa2OndashZnOndashP2O5 glasses or with combined mentioneddopants Optical data show UV absorption for the undopedglass with an extension to two additional UV bands due toboth Ce4+ and Ce3+ ions while Sm3+-doped glasses show twofurther additional series in the visible and near IR regionsPhotoluminescence spectra reveal characteristic excitationand emission bands for the CeO2ndash and Sm2O3ndashglasses FTIRspectra show extended vibrational bands within the region400ndash1700 cmminus1 correlated with phosphate groups (mainly Q2

and Q3 units) The IR spectra did not show additional bandsdue to the dopants indicating their housing in modifyingpositions Thermal expansion measurements confirm theprevious assumption and are reflected on the dilatometricsoftening temperature in the mixed dopant glasses Thevarious doped glasses reveal closely similar IR spectral curveswith minor variations in the intensities of some bands due todepolymerization effects of the rare-earth ions The thermalexpansion measurements indicate the housing of rare-earthions in modifying positions and the mixed dopants areassumed to cause more filing of the network structure

All the studied properties indicate that the optical spectraof the single dopant (CeO2 Sm2O3) are different althoughthey belong to the lanthanides On the other hand the IRspectra reveal similar spectral details for the two dopants(CeO2 Sm2O3) because they are housed in interstitial posi-tions and their low percent did not affect the vibrationalbands due to phosphate groups The same holds for thethermal properties The mixed dopant glasses show thecombined optical spectra for lanthanidesWhile FTIR spectracause no distinct effect the thermal data revel combinedeffect of two dopants

Data Availability

The data used to support the findings of this study areavailable from the corresponding author upon request

Conflicts of Interest

The authors declare that they have no conflicts of interest

References

[1] R K Brow ldquoReview the structure of simple phosphate glassesrdquoJournal of Non-Crystalline Solids vol 263-264 pp 1ndash28 2000

[2] J E Shelby Introduction to Glass Science and Technology TheRoyal Society of Chemistry Cambridge UK 2005

[3] M Karabulut G K Marasinghe C S Ray et al ldquoAn inves-tigation of the local iron environment in iron phosphateglasses having different Fe(II) concentrationsrdquo Journal of Non-Crystalline Solids vol 306 no 2 pp 182ndash192 2002

[4] M Karabulut E Metwalli D E Day and R K BrowldquoMossbauer and IR investigations of iron ultraphosphateglassesrdquo Journal of Non-Crystalline Solids vol 328 no 1-3 pp199ndash206 2003

[5] C R Bamford Colour Generation and Control in Glass GlassScience and Technology vol 2 Elsevier Science PublisherAmsterdam Netherlands 1977

[6] N F Mott and E A Davis Eds Electronic Processes inNon-Crystalline Materials Clarendon Press Oxford UK 2ndedition 1979

[7] D Ehrt ldquoPhosphate and fluoride phosphate optical glasses -Properties structure and applicationsrdquoPhysics andChemistry ofGlasses European Journal of Glass Science and Technology PartB vol 56 no 6 pp 217ndash234 2015

[8] C Mercier G Palavit L Montagne and C Follet-HouttemaneldquoA survey of transition-metal-containing phosphate glassesrdquoComptes Rendus Chimie vol 5 no 11 pp 693ndash703 2002

[9] S Y Marzouk and F H Elbatal ldquoUltravioletndashvisible absorptionof gamma-irradiated transition metal ions doped in sodiummetaphosphate glassesrdquo Nuclear Instruments and Methods inPhysics Research Section B Beam InteractionswithMaterials andAtoms vol 248 no 1 pp 90ndash102 2006

[10] F H Elbatal M A Marzouk and A M Abdelghany ldquoUV-visible and infrared absorption spectra of gamma irradiated V2O5-doped in sodium phosphate lead phosphate zinc phos-phate glasses A comparative studyrdquo Journal of Non-CrystallineSolids vol 357 no 3 pp 1027ndash1036 2011

[11] A M Abdelghany H A ElBatal and F M EzzElDin ldquoGammaray interaction with vanadyl ions in barium metaphosphateglasses spectroscopic and ESR studiesrdquo Journal of MolecularStructure vol 1147 pp 33ndash39 2017

[12] AM Abdelghany I S Ali and H A ElBatal ldquoReducing powerof phosphate matrix in binary barium phosphate glasses dopedwith 3D transition metals and effects of gamma radiationrdquoSilicon vol 10 no 3 pp 1181ndash1186 2018

[13] M JWeber ldquoChromium - rare-earth energy transfer in YAlO3rdquoJournal of Applied Physics vol 44 no 9 pp 4058ndash4064 1973

[14] A Mohan Babu B C Jamalaiah T Sasikala S A Saleem andL Rama Moorthy ldquoAbsorption and emission spectral studies ofSm3+-doped lead tungstate tellurite glassesrdquo Journal of Alloysand Compounds vol 509 no 14 pp 4743ndash4747 2011

[15] M AMarzouk AM Abdelghany and H A Elbatal ldquoBismuthsilicate glass as hostmedia for some selected rare-earth ions andeffects of gamma irradiationrdquo Philosophical Magazine vol 93no 19 pp 2465ndash2484 2013

[16] E Malchukova B Boizot D Ghaleb and G Petite ldquoOpticalproperties of pristine and 120574-irradiatedSm-doped borosilicateglassesrdquo Nuclear Instruments and Methods in Physics ResearchSection A Accelerators Spectrometers Detectors and AssociatedEquipment vol 537 no 1-2 pp 411ndash414 2005

[17] R Praveena V Venkatramu P Babu and C K JayasankarldquoFluorescence spectroscopy of Sm3+ ions in P2O5- PbO-Nb2O5glassesrdquo Physica B Condensed Matter vol 403 no 19-20 pp3527ndash3534 2008

[18] V Venkatramu P Babu C K Jayasankar T Troster W Sieversand G Wortmann ldquoOptical spectroscopy of Sm3+ ions inphosphate and fluorophosphate glassesrdquo Optical Materials vol29 no 11 pp 1429ndash1439 2007

[19] J Bei G Qian X Liang S Yuan Y Yang andG Chen ldquoOpticalproperties of Ce3+-doped oxide glasses and correlations withoptical basicityrdquo Materials Research Bulletin vol 42 no 7 pp1195ndash1200 2007

[20] A D Sontakke J Ueda and S Tanabe ldquoEffect of synthesisconditions on Ce3 + luminescence in borate glassesrdquo Journal ofNon-Crystalline Solids vol 431 pp 150ndash153 2016


[21] M A Marzouk Y M Hamdy H A Elbatal and F M EzzEldin ldquoPhotoluminescence and spectroscopic dependence offluorophosphate glasses on samarium ions concentration andthe induced defects by gamma irradiationrdquo Journal of Lumines-cence vol 166 pp 295ndash303 2015

[22] M A Marzouk A M Fayad and H A ElBatal ldquoCorrelationbetween luminescence and crystallization characteristics ofDy3+ doped P2O5ndashBaOndashSeO2 glasses for white LED applica-tionsrdquo Journal of Materials Science Materials in Electronics vol28 no 17 pp 13101ndash13111 2017

[23] G H Sigel Jr and R J Ginther ldquoThe effect of iron on theultraviolet absorption of high purity soda-silica glassrdquo GlassTechnology vol 9 pp 66ndash70 1968

[24] L Cook and K H Mader ldquoUltraviolet transmission character-istics of a fluorophosphate laser glassrdquo e American CeramicSociety vol 65 pp 597ndash601 1982

[25] J A Duffy ldquoCharge transfer spectra of metal ions in glassrdquoPhysics and Chemistry of Glasses European Journal of GlassScience and Technology Part B vol 38 pp 289ndash294 1997

[26] M D Moncke ldquoPhoto-ionization of 3d-ions in fluoride-phos-phate glassesrdquo International Journal of AppliedGlass Science vol6 pp 249ndash267 2015

[27] G K Das Mohapatra ldquoA spectroscopic study of Ce3+ ion incalciummetaphosphate glassrdquo Physics and Chemistry of Glassesvol 39 pp 50ndash55 1998

[28] S Y Marzouk and F M EzzElDin ldquoOptical study of Ce3+ ionin gamma-irradiated binary barium-borate glassesrdquo Physica BCondensed Matter vol 403 no 18 pp 3307ndash3315 2008

[29] Y Ohishi and S Takahashi ldquoLow temperature optical absorp-tion for Sm3+ and Eu3+ ions in ZrF4-based fluoride glassrdquoJournal of Non-Crystalline Solids vol 74 no 2-3 pp 407ndash4101985

[30] R Van Deun K Binnemans C Cortler-Walrams and J LAdam ldquoSpectroscopic properties of trivalent samarium ions inglassesrdquo in Proceedings of the Rare-Earth-Doped Materials andDevices III vol 3622 April 1999

[31] S S Shanmuga K Marimuthu M Sivraman and S S BabuldquoComposition dependent structural and optical properties ofSm3+-doped sodium borate and sodium fluoroborate glassesrdquoJournal of Luminescence vol 130 no 7 pp 1313ndash1319 2010

[32] M Seshadri K V Rao J L Rao and Y C RatnakramldquoSpectroscopic and laser properties of Sm3+ doped differentphosphate glassesrdquo Journal of Alloys and Compounds vol 476no 1-2 pp 263ndash270 2009

[33] M Resa Dousti S K Ghoshai R J Amjad M R Sahar andR F Namaz ldquoStructural and optical study of samarium dopedlead zinc phosphate glassesrdquo Optics Communications vol 300pp 204ndash209 2013

[34] D G Holloway e Physical Properties of Glass Wykehampublications Ltd London UK 1973

[35] A Abdel Kader A H Higazy and M M ElKholy ldquoCompo-sitional dependence of infrared absorption spectra studies forTeO2-P2O5 and TeO2-P2O5-Bi2O3 glassesrdquo Journal of MaterialsScience Materials in Electronics vol 2 no 3 pp 157ndash163 1991

[36] P Znasik and M Jamnicky ldquoPreparation infrared spectraand structure of glasses in the system CuClminusCu2Ominus(P2O5 +MoO3)rdquo Journal of Non-Crystalline Solids vol 146 pp 74ndash801992

[37] Y M Moustafa and K El-Egili ldquoInfrared spectra of sodiumphosphate glassesrdquo Journal of Non-Crystalline Solids vol 240no 1-3 pp 144ndash153 1998

[38] F H El-Batal ldquoGamma ray interaction with copper-dopedsodium phosphate glassesrdquo Journal of Materials Science vol 43no 3 pp 1070ndash1079 2008

[39] M A Marzouk F H ElBatal K M ElBadry and H AElBatal ldquoOptical structural and thermal properties of sodiummetaphosphate glasses containing Bi2O3 with interactionsof gamma raysrdquo Spectrochimica Acta Part A Molecular andBiomolecular Spectroscopy vol 171 pp 454ndash460 2017

Hindawiwwwhindawicom Volume 2018

Active and Passive Electronic Components


Shock and Vibration


High Energy PhysicsAdvances in

Hindawi Publishing Corporation httpwwwhindawicom Volume 2013Hindawiwwwhindawicom

The Scientific World Journal

Volume 2018

Acoustics and VibrationAdvances in



Advances in Condensed Matter Physics

OpticsInternational Journal of



AstronomyAdvances in

Antennas andPropagation

International Journal of




Geophysics

Advances inOpticalTechnologies

Hindawiwwwhindawicom

Volume 2018

Applied Bionics and BiomechanicsHindawiwwwhindawicom Volume 2018

Advances inOptoElectronics


Volume 2018


Mathematical PhysicsAdvances in


ChemistryAdvances in


Journal of

Chemistry


Advances inPhysical Chemistry


RotatingMachinery



Journal ofEngineeringVolume 2018

Submit your manuscripts atwwwhindawicom


Table 1 Chemical composition of the prepared glasses

Sample Mol P2O5 ZnO Na2O Al2O3 CeO2 Sm2O3

G1 70 20 10 1 0 0G1 70 20 10 1 05 0G2 70 20 10 1 2 0G3 70 20 10 1 5 0G4 70 20 10 1 0 05G5 70 20 10 1 0 2G6 70 20 10 1 0 5G7 70 20 10 1 025 025G8 70 20 10 1 1 1G9 70 20 10 1 25 25

on the host material as well as on the preparation condition[19 20]

In a previous publication [21] combined optical FTIRand photoluminescence spectral analysis have been carriedout for Sm2O3 (02 997888rarr 3) doped in host NaFndashAlF3-phosphate glasses before and after successive gamma irra-diation Spectral data indicate the stability of the Sm3+ ionswith their characteristic absorption bands distributed intotwo regions at 350ndash900 and 1100-1600nm even after gammairradiation The same behavior holds for the luminescencespectra FTIR spectra of the mentioned fluorophosphatesglasses show phosphate groups (mainly of Q2 and Q3) withthe assumption of the formation of (PO3F) AlF4 or AlF6groups and the spectral data also show obvious stabilitytowards gamma irradiation

In the course of the present study the main objectiveis to study combined optical FTIR and photoluminescencespectra of prepared single doped rare-earth oxide of eitherCeO2 or Sm2O3 or with both the two RE oxides as mixeddopants in a host Na2OndashZnOndashP2O5 glass with added 1Al2O3 for stability The two selected rare-earth oxides areknown to exhibit different characteristics CeO2 is able toexist in two different valences (Ce3+ Ce4+) and their specificspectra are within the UVndashnear visible region On the otherhand Sm2O3 is accepted to be stable as trivalent Sm3+ ionsunder normal conditions and exhibits extended visible near-IR optical absorption

It is expected that the collective spectral studies will throwmore insight to find out the interferences or themixing effectsof both the two rare-earth oxides specifically the ability ofCeO2 to act as oxidoreduction agent in the studied hostglasses

2 Experimental Details

The glasses were prepared from laboratory chemicals includ-ing ammonium dihydrogen phosphate (NH4H2PO4) forP2O5 Na2O was added in the form of anhydrous sodiumcarbonate (Na2CO3) and ZnO and Al2O3 were added assuch The dopant rare-earth oxides were introduced as CeO2and Sm2O3 The detailed chemical compositions of theglasses are given in Table 1

The weighed batches were melted in covered aluminacrucibles at 1100∘C for 90 minutes in an electric SiC heatedfurnace (Vecstar UK) under ordinary atmospheric conditionThe melts were rotated at intervals of 20 minutes to reachmixing and homogeneity Then the melts were poured intothe stainless steel mold with the required dimensions Theprepared glasses were transferred immediately to an anneal-ing muffle regulated at 300∘C to obtain samples free fromstress or strains The annealing muffle was switched off after1 hour with the samples inside and left to cool to roomtemperature at a rate of 30∘Ch

Characterizations of the produced glasses were carriedout according procedures of the previouswork [22] as follows

Optical (UV-visiblendashNIR) absorption spectral measure-ments were carried out on polished glasses of equal thickness(2mm plusmn 01mm) using a recording spectrophotometer (typeJASCO V-570 JAPAN) covering the range 200 to 2500nm

Photoluminescence measurements were measured atroom temperature under different excitation wavelengthsusing a fluorescence spectrophotometer (type JASCO FP-6500 JAPAN) equipped with a xenon flash lamp as theexcitation light source The scan speed is 015 step-1 with astep length of 025 nm and slit width of 02 nm

The thermal expansion characteristics of the studiedglasses were measured through specified samples using arecording dilatometer (type NETZCH 1- 402 PC GeratebauGmbH Selb Germany) with a heating rate of 10∘Cmin upto both transformation region and dilatometric softeningtemperature The thermal data were collected and analyzed

FTIR measurements of the prepared glasses and theircorresponding glass-ceramic derivatives were carried out atroom temperature in the wavenumber range 4000ndash400 cmminus1by a Fourier transform computerized spectrometer (typeFTIRndash4600 JASCO Crop JAPAN) Through the KBr disctechnique glasses or glass-ceramics in the form of pulverizedpowder were examined by mixing 2mg of the powderedsamples and 200mg KBr and the mixtures were subjectedto a load of 5 tonscm2 in an evocable die to produceclear homogeneous discs The prepared discs were measureddirectly to avoid moisture attack Infrared spectra werecorrelated for the dark current noises and background usingthe two-point baseline correction


bsor

banc

e (a

u)

Wavelength (nm)

Wavelength (nm)

Abs

orba

nce (

au

)

305

234

12001000800600400200

400350300250200








Abs

orba

nce (

au

)

Wavelength (nm)

Wavelength (nm)150 200 250 300 350 400

210

nm

264

nm

300

nm

05 CeO

2 CeO

5 CeO

24002200200018001600140012001000800600400200


















4P72405 6P52

4K112472 4I12+

4I132+4M152

950 6F1121038 6F921238 6F721385 6F521489 6F321552 6F121623 6H152

Abs

orba

nce (

au

)

Wavelength (nm)

Wavelength (nm)

293

nm252

nm

206

nm

025 CeO - 025SmO

100 CeO - 100SmO

250 CeO - 250SmO

2000 2200 240018001600140012001000800600400200

200 250 300 35036

9 438

400

945

1085

1234

1381

1489

1548

1620

1590

472






Inte

nsity

(au

)

335

nm 658 nmＲ=290 nm

Inte

nsity

(au

)

332

nm

658

nm

Ｒ=235 nm

05 CeO

2 CeO

5 CeO

235

290

320300280260240220200

Wavelength (nm)1000800 900600 700500400300200

(a)

(b)(c)











Inte

nsity

(au

)

05SmO

2 SmO

5 SmO

300 320 340 360 380 400 420

697

642

596

560

750700650600550500450

702

642

596

560

440 46034

4 362

375

402

416

440

333

Wavelength (nm)

(a)

(c)

(b)



4G52 997888rarr6H72

4G52 997888rarr6H92 and

4G52 997888rarr6H132






Inte

nsity

(au

)


Wavelength (nm)

(b)

(d)

(a)

700

642

595

560

642

596

560

650

596

561

800750700650600550500450400350

320 340 360 380 400 420 440 460

362

374

402

416

440

344

333

(c)






Temperature ∘C

dLL

olowast10

-3


435 ∘C

418 ∘C412 ∘C

412 ∘C

500450400350300250200150100500

30

25

20

15

10

05

00

minus05




















Wavenumber (cm-1)

Abs

orba

nce (

au

)

400600800100012001400

(b)

(c)

(a) 410

490

725

878

788

970

1089

1246


Wavenumber (cm-1)

Abs

orba

nce (

au

)

400600800100012001400

(b)

(c)

(a) 41746

3535

68478

0880

941

107212

73


410

515

721

400600800100012001400Wavenumber (cm-1)

Abs

orba

nce (

au

)

(b)

(c)

(a)

784

889

945

1083

1282



4 Conclusion




Data Availability




References












































Shock and Vibration





Volume 2018














Geophysics



Volume 2018




Volume 2018






Journal of

Chemistry




RotatingMachinery






bsor

banc

e (a

u)

Wavelength (nm)

Wavelength (nm)

Abs

orba

nce (

au

)

305

234

12001000800600400200

400350300250200








Abs

orba

nce (

au

)

Wavelength (nm)

Wavelength (nm)150 200 250 300 350 400

210

nm

264

nm

300

nm

05 CeO

2 CeO

5 CeO

24002200200018001600140012001000800600400200


















4P72405 6P52

4K112472 4I12+

4I132+4M152

950 6F1121038 6F921238 6F721385 6F521489 6F321552 6F121623 6H152

Abs

orba

nce (

au

)

Wavelength (nm)

Wavelength (nm)

293

nm252

nm

206

nm

025 CeO - 025SmO

100 CeO - 100SmO

250 CeO - 250SmO

2000 2200 240018001600140012001000800600400200

200 250 300 35036

9 438

400

945

1085

1234

1381

1489

1548

1620

1590

472






Inte

nsity

(au

)

335

nm 658 nmＲ=290 nm

Inte

nsity

(au

)

332

nm

658

nm

Ｒ=235 nm

05 CeO

2 CeO

5 CeO

235

290

320300280260240220200

Wavelength (nm)1000800 900600 700500400300200

(a)

(b)(c)











Inte

nsity

(au

)

05SmO

2 SmO

5 SmO

300 320 340 360 380 400 420

697

642

596

560

750700650600550500450

702

642

596

560

440 46034

4 362

375

402

416

440

333

Wavelength (nm)

(a)

(c)

(b)



4G52 997888rarr6H72

4G52 997888rarr6H92 and

4G52 997888rarr6H132






Inte

nsity

(au

)


Wavelength (nm)

(b)

(d)

(a)

700

642

595

560

642

596

560

650

596

561

800750700650600550500450400350

320 340 360 380 400 420 440 460

362

374

402

416

440

344

333

(c)






Temperature ∘C

dLL

olowast10

-3


435 ∘C

418 ∘C412 ∘C

412 ∘C

500450400350300250200150100500

30

25

20

15

10

05

00

minus05




















Wavenumber (cm-1)

Abs

orba

nce (

au

)

400600800100012001400

(b)

(c)

(a) 410

490

725

878

788

970

1089

1246


Wavenumber (cm-1)

Abs

orba

nce (

au

)

400600800100012001400

(b)

(c)

(a) 41746

3535

68478

0880

941

107212

73


410

515

721

400600800100012001400Wavenumber (cm-1)

Abs

orba

nce (

au

)

(b)

(c)

(a)

784

889

945

1083

1282



4 Conclusion




Data Availability




References












































Shock and Vibration





Volume 2018














Geophysics



Volume 2018




Volume 2018






Journal of

Chemistry




RotatingMachinery















4P72405 6P52

4K112472 4I12+

4I132+4M152

950 6F1121038 6F921238 6F721385 6F521489 6F321552 6F121623 6H152

Abs

orba

nce (

au

)

Wavelength (nm)

Wavelength (nm)

293

nm252

nm

206

nm

025 CeO - 025SmO

100 CeO - 100SmO

250 CeO - 250SmO

2000 2200 240018001600140012001000800600400200

200 250 300 35036

9 438

400

945

1085

1234

1381

1489

1548

1620

1590

472






Inte

nsity

(au

)

335

nm 658 nmＲ=290 nm

Inte

nsity

(au

)

332

nm

658

nm

Ｒ=235 nm

05 CeO

2 CeO

5 CeO

235

290

320300280260240220200

Wavelength (nm)1000800 900600 700500400300200

(a)

(b)(c)











Inte

nsity

(au

)

05SmO

2 SmO

5 SmO

300 320 340 360 380 400 420

697

642

596

560

750700650600550500450

702

642

596

560

440 46034

4 362

375

402

416

440

333

Wavelength (nm)

(a)

(c)

(b)



4G52 997888rarr6H72

4G52 997888rarr6H92 and

4G52 997888rarr6H132






Inte

nsity

(au

)


Wavelength (nm)

(b)

(d)

(a)

700

642

595

560

642

596

560

650

596

561

800750700650600550500450400350

320 340 360 380 400 420 440 460

362

374

402

416

440

344

333

(c)






Temperature ∘C

dLL

olowast10

-3


435 ∘C

418 ∘C412 ∘C

412 ∘C

500450400350300250200150100500

30

25

20

15

10

05

00

minus05




















Wavenumber (cm-1)

Abs

orba

nce (

au

)

400600800100012001400

(b)

(c)

(a) 410

490

725

878

788

970

1089

1246


Wavenumber (cm-1)

Abs

orba

nce (

au

)

400600800100012001400

(b)

(c)

(a) 41746

3535

68478

0880

941

107212

73


410

515

721

400600800100012001400Wavenumber (cm-1)

Abs

orba

nce (

au

)

(b)

(c)

(a)

784

889

945

1083

1282



4 Conclusion




Data Availability




References












































Shock and Vibration





Volume 2018














Geophysics



Volume 2018




Volume 2018






Journal of

Chemistry




RotatingMachinery






Inte

nsity

(au

)

335

nm 658 nmＲ=290 nm

Inte

nsity

(au

)

332

nm

658

nm

Ｒ=235 nm

05 CeO

2 CeO

5 CeO

235

290

320300280260240220200

Wavelength (nm)1000800 900600 700500400300200

(a)

(b)(c)











Inte

nsity

(au

)

05SmO

2 SmO

5 SmO

300 320 340 360 380 400 420

697

642

596

560

750700650600550500450

702

642

596

560

440 46034

4 362

375

402

416

440

333

Wavelength (nm)

(a)

(c)

(b)



4G52 997888rarr6H72

4G52 997888rarr6H92 and

4G52 997888rarr6H132






Inte

nsity

(au

)


Wavelength (nm)

(b)

(d)

(a)

700

642

595

560

642

596

560

650

596

561

800750700650600550500450400350

320 340 360 380 400 420 440 460

362

374

402

416

440

344

333

(c)






Temperature ∘C

dLL

olowast10

-3


435 ∘C

418 ∘C412 ∘C

412 ∘C

500450400350300250200150100500

30

25

20

15

10

05

00

minus05




















Wavenumber (cm-1)

Abs

orba

nce (

au

)

400600800100012001400

(b)

(c)

(a) 410

490

725

878

788

970

1089

1246


Wavenumber (cm-1)

Abs

orba

nce (

au

)

400600800100012001400

(b)

(c)

(a) 41746

3535

68478

0880

941

107212

73


410

515

721

400600800100012001400Wavenumber (cm-1)

Abs

orba

nce (

au

)

(b)

(c)

(a)

784

889

945

1083

1282



4 Conclusion




Data Availability




References












































Shock and Vibration





Volume 2018














Geophysics



Volume 2018




Volume 2018






Journal of

Chemistry




RotatingMachinery






Inte

nsity

(au

)

05SmO

2 SmO

5 SmO

300 320 340 360 380 400 420

697

642

596

560

750700650600550500450

702

642

596

560

440 46034

4 362

375

402

416

440

333

Wavelength (nm)

(a)

(c)

(b)



4G52 997888rarr6H72

4G52 997888rarr6H92 and

4G52 997888rarr6H132






Inte

nsity

(au

)


Wavelength (nm)

(b)

(d)

(a)

700

642

595

560

642

596

560

650

596

561

800750700650600550500450400350

320 340 360 380 400 420 440 460

362

374

402

416

440

344

333

(c)






Temperature ∘C

dLL

olowast10

-3


435 ∘C

418 ∘C412 ∘C

412 ∘C

500450400350300250200150100500

30

25

20

15

10

05

00

minus05




















Wavenumber (cm-1)

Abs

orba

nce (

au

)

400600800100012001400

(b)

(c)

(a) 410

490

725

878

788

970

1089

1246


Wavenumber (cm-1)

Abs

orba

nce (

au

)

400600800100012001400

(b)

(c)

(a) 41746

3535

68478

0880

941

107212

73


410

515

721

400600800100012001400Wavenumber (cm-1)

Abs

orba

nce (

au

)

(b)

(c)

(a)

784

889

945

1083

1282



4 Conclusion




Data Availability




References












































Shock and Vibration





Volume 2018














Geophysics



Volume 2018




Volume 2018






Journal of

Chemistry




RotatingMachinery






Inte

nsity

(au

)


Wavelength (nm)

(b)

(d)

(a)

700

642

595

560

642

596

560

650

596

561

800750700650600550500450400350

320 340 360 380 400 420 440 460

362

374

402

416

440

344

333

(c)






Temperature ∘C

dLL

olowast10

-3


435 ∘C

418 ∘C412 ∘C

412 ∘C

500450400350300250200150100500

30

25

20

15

10

05

00

minus05




















Wavenumber (cm-1)

Abs

orba

nce (

au

)

400600800100012001400

(b)

(c)

(a) 410

490

725

878

788

970

1089

1246


Wavenumber (cm-1)

Abs

orba

nce (

au

)

400600800100012001400

(b)

(c)

(a) 41746

3535

68478

0880

941

107212

73


410

515

721

400600800100012001400Wavenumber (cm-1)

Abs

orba

nce (

au

)

(b)

(c)

(a)

784

889

945

1083

1282



4 Conclusion




Data Availability




References












































Shock and Vibration





Volume 2018














Geophysics



Volume 2018




Volume 2018






Journal of

Chemistry




RotatingMachinery






Temperature ∘C

dLL

olowast10

-3


435 ∘C

418 ∘C412 ∘C

412 ∘C

500450400350300250200150100500

30

25

20

15

10

05

00

minus05




















Wavenumber (cm-1)

Abs

orba

nce (

au

)

400600800100012001400

(b)

(c)

(a) 410

490

725

878

788

970

1089

1246


Wavenumber (cm-1)

Abs

orba

nce (

au

)

400600800100012001400

(b)

(c)

(a) 41746

3535

68478

0880

941

107212

73


410

515

721

400600800100012001400Wavenumber (cm-1)

Abs

orba

nce (

au

)

(b)

(c)

(a)

784

889

945

1083

1282



4 Conclusion




Data Availability




References












































Shock and Vibration





Volume 2018














Geophysics



Volume 2018




Volume 2018






Journal of

Chemistry




RotatingMachinery






Wavenumber (cm-1)

Abs

orba

nce (

au

)

400600800100012001400

(b)

(c)

(a) 410

490

725

878

788

970

1089

1246


Wavenumber (cm-1)

Abs

orba

nce (

au

)

400600800100012001400

(b)

(c)

(a) 41746

3535

68478

0880

941

107212

73


410

515

721

400600800100012001400Wavenumber (cm-1)

Abs

orba

nce (

au

)

(b)

(c)

(a)

784

889

945

1083

1282



4 Conclusion




Data Availability




References












































Shock and Vibration





Volume 2018














Geophysics



Volume 2018




Volume 2018






Journal of

Chemistry




RotatingMachinery






4 Conclusion




Data Availability




References












































Shock and Vibration





Volume 2018














Geophysics



Volume 2018




Volume 2018






Journal of

Chemistry




RotatingMachinery




























Shock and Vibration





Volume 2018














Geophysics



Volume 2018




Volume 2018






Journal of

Chemistry




RotatingMachinery








Shock and Vibration





Volume 2018














Geophysics



Volume 2018




Volume 2018






Journal of

Chemistry




RotatingMachinery





Documents

ResearchArticle - Hindawi Publishing Corporationdownloads.hindawi.com/journals/ijo/2019/6527327.pdf · ResearchArticle Collective Optical, FTIR, and Photoluminescence Spectra of CeO