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7/29/2019 Prijamboedi-B._Growth-and-morphology-of-c-axis-oriented-Nd1.85-Ce0.15CuO4-y-thin-films-prepared-by-pulsed-las
http:///reader/full/prijamboedi-bgrowth-and-morphology-of-c-axis-oriented-nd185-ce015cuo4-y-thin-films-prepared- 1/6
J Mater Sci: Mater Electron (2006) 17: 483488
DOI 10.1007/s10854-006-8222-4
Growth and morphology of c-axis oriented Nd1.85Ce0.15CuO4ythin films prepared by pulsed laser deposition technique
B. Prijamboedi S. Kashiwaya
Received: 12 August 2005 / Accepted: 24 February 2006C Springer Science+Business Media, LLC 2006
Abstract On the electron-doped superconductor of
Nd2xCexCuO4y (NCCO) thin film, the presence of
non-c-axis oriented grains, which are identified as (110)
reflection peak at 2= 32.5 in the x-ray diffraction (XRD)
spectrum is always observed. Meanwhile, high quality thin
films without having impurities are necessary for device
applications. We study the growth of NCCO thin film
prepared by pulsed laser deposition technique and found
that the volume fraction of (110) oriented grains depends
on the laser fluence. With the laser fluence of around
2.2 J/cm2, NCCO thin film, which is free from the presence
of non-c-axis oriented grains, could be obtained. The atomic
force microscope images show that with the absence of
(110) oriented grain the c-axis oriented grains grow into
rectangular shape with a spiral growth mode. The rocking
curve measurement for (004) peak give a full width at
half maximum value of 0.12, which confirms the superior
quality of the film and this film has superconducting critical
temperature (Tc) at 21 K with a transition width (Tc)
of 1 K.
1. Introduction
The discovery of superconductivity in Nd2xCexCuO4y(NCCO) has received much attention since this material has
unique properties compared with the hole-doped cuprates su-
perconductor [1]. The charge carrier type in this system as a
B. Prijamboedi () S. Kashiwaya
Nanoelectronics Research Institute of AIST Tsukuba Central 2,
Umezono 1-1-1, Tsukuba, Ibaraki 305-8568, JAPAN
e-mail: [email protected]
result of Ce4+ substitution is electron, which is confirmed by
Hall measurement [2]. The other unique properties are the
absent of apical oxygen atoms outside the CuO2 layer and
T2-like temperature dependence of resistivity in the normal
state. It is believed that this material could provide useful
information to elucidate the mechanism of superconductiv-
ity in the cuprates. Meanwhile, the NCCO has number of
difficulties and disadvantages for application such as a rela-
tively low superconducting critical temperature (Tc = 23 K
with x = 0.15), the presence of superconductivity within a
narrow Ce concentration range [1] and the necessity to re-
move oxygen atom in order to obtain high Tc value. Despite
these problems, NCCO has some advantages such as better
surface stability compared to YBa2Cu3O7y (YBCO) mate-
rial [3] and longer in-plane coherence length of 7080 A [4],
which make this material a potential candidate to be used
as device. The superconductor material could open new pos-
sibility in the development of new electronic devices such
as superconductor-semiconductor hybrid junction [5, 6],
hybrid Josepshon field effect transistor [7] and for
NCCO; it is a potential candidate for the fabrication of p-n
junction device from the hole- and electron-doped supercon-
ductors [8].
Thin film is the most suitable form for device applica-
tion. The common method to fabricate NCCO thin films
is by pulsed laser deposition (PLD) technique. This tech-
nique is simple, versatile and can reproduce the stoichiomet-
riccompositionof depositedthin filmfrom thetarget material
[9]. Meanwhile, the PLD technique also has some disadvan-
tages, such as medium quality of the thin film surface and
many interdependent deposition parameters. Some NCCO
thin films with high critical superconducting transition tem-
perature have been successfully fabricated by PLD methods
[1012]. However, the presence of peaks at 2= 32.5 and
Springer
7/29/2019 Prijamboedi-B._Growth-and-morphology-of-c-axis-oriented-Nd1.85-Ce0.15CuO4-y-thin-films-prepared-by-pulsed-las
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484 J Mater Sci: Mater Electron (2006) 17: 483488
68 in the X-ray diffraction (XRD) spectra are always re-
ported even in the sample prepared by RF-sputtering method
[13]. Those peaks indicate the presence of non-c-axis ori-
ented grains and it could induce defects on the film. There
were reports that discussed the origin of these peaks. Some
reported that these peaks come from the reflection of (110)
and (220) planes of NCCO crystal [14] and the other sug-
gested that it comes from the reflection of (400) and (800)plane of NdCeO3.5 (NCO) compound [15]. The same peaks
were also observed in the Ce-free Pr2CuO4y thin films [16]
and it raised a doubt that NCO compound is responsible for
the origin of those peaks.
We studied the growth of high quality c-axis oriented
NCCO thin films prepared by pulsed laser deposition tech-
nique, which do not show foreign peaks at 2= 34.5 and
68 in the XRD spectrum. High quality NCCO thin film with
less defect and impurity is necessary for the device applica-
tion since the cuprate based superconductor device is very
sensitive to the disorder [17]. We focused the study on the
effect of laser fluence on the target surface to the growth
and morphology of the NCCO thin film. We used a method
that has been reported before that the laser fluence could be
simply adjusted by shifting the distance between the waist
of the focusing laser lens and the target surface, d wt [18].
We found that the intensity of the foreign peaks decreases
with the decreasing of the laser fluence. We could prepare
high quality NCCO film without the presence of (110) ori-
ented grains as it was confirmed by XRD and atomic force
measurement (AFM) and found different morphology of the
NCCO thin film affected by the presence of (110) oriented
grains.
2. Experimental
Polished single crystal SrTiO3 (001) with thickness of
0.5 mm was used as substrate and it was glued on a stainless
steel block heater with silver paste. The deposition chamber
then was evacuated into a typical pressure of 1.33 104 Pa
and the heater temperature was raised to 820C. The tem-
perature was measured by a sheathed thermocouple inserted
into the block heater.During deposition,oxygen pressure was
maintained at 93.3 Pa by flooding the oxygen gas with flow
rate of 17.5 sccm into the chamber. An ArF excimer laser
(Compex 205 from LambdaPhysik, = 193 nm) with a rep-
etition rate of 2 Hz was used as excitation source. A mask with
an opening with size of 2 1 cm2 was put on the laser beam
output window. The laser energy measured after it passed the
mask is about 100 mJ. The laser beam is focused by a lens
with focal length of 50 cm onto the surface of NCCO ceramic
target prepared by a conventionalsolid-state reaction method.
Thepurity of theNCCO target(Dowa Co.Ltd.) is 99.9% (3N)
and with density of 90%. During deposition, target is rotated
at 10 rpm so that the laser beam does not impinge on the same
spot. The target-substrate distance was set at 32 mm. After
deposition, the NCCO thin film sample was subsequently
annealed at 700C in vacuum of 1.33 103 Pa for about
15 minutes.
To study the effect of the laser fluence on the growth of
NCCO thin films, some samples were prepared in different
distance between the waist of the lens and the target surface,dwt; sample A: 50 cm, sample B: 51.5 cm and sample C:
53 cm. The laser fluence was estimated by measuring the size
of the laser spot on the target for each different dwt value.
With constant deposition time (45 minutes), the thickness of
the films are 3300 A for sample A, 2200 A for sample B and
1600 A for sample C. Thin films sample then were charac-
terized by an atomic force microscope (AFM) to analyze its
surface morphology and it was performed in the air at room
temperature. The x-ray spectrometer was used to study the
NCCO thin film crystal structure and resistivity and super-
conducting critical temperature were measured by a standard
four-probe technique in the temperature range between 2 K
and 300 K.
3. Results and discussions
Figure 1 shows the x-ray diffraction spectra of NCCO thin
film sample prepared with different waist of the lens to tar-
get surface distance, dwt. The spectra show that it mainly
consists of the peaks from c-axis oriented grains of (001)
reflection planes and SrTiO3 substrate. In sample A and B,
peaks at 2= 32.5 and 68 are clearly observed, indicating
the presence of non-c-axis oriented grains. The same peaks
are not observed in sample C. The ratio between the intensity
of peak at 2= 32.5(I110) and the intensity of peak from the
(002) reflection (I002) is shown in Table 1 as well as the de-
position rate and the laser fluence on the target. It shows that
by increasing the waist of lens to the target surface distance
or decreasing the laser fluence, the deposition rate decreases
and it will reduce the volume fraction of non-c-axis oriented
grain on the NCCO film.
The rocking curve measurement ( scan) was carried out
for the (004) reflection plane of the NCCO thin films. In
Figure 2, the results of the rocking curve scan for (004) peak
from all samples are shown. The rocking curve measurement
gives full width at half maximum (FWHM) values of 0.9 for
sample A, 0.6 for sample B and 0.12 for sample C. The
small FWHM value obtained for sample C indicates a highly
oriented epitaxial growth of NCCO thin films characterized
by a narrow mosaic spread distribution.
In Figure 3(a) and 3(b), AFM images from sample A,
scanned from a 5 5 m2 and 0.5 0.5 m2 areas are
shown. On this film, we can clearly observed two different
types of grain. We notice some large and flat grains with size
Springer
7/29/2019 Prijamboedi-B._Growth-and-morphology-of-c-axis-oriented-Nd1.85-Ce0.15CuO4-y-thin-films-prepared-by-pulsed-las
http:///reader/full/prijamboedi-bgrowth-and-morphology-of-c-axis-oriented-nd185-ce015cuo4-y-thin-films-prepared- 3/6
J Mater Sci: Mater Electron (2006) 17: 483488 485
Fig. 1 Plots of intensity vs. 2 of x-ray diffraction spectra for
Nd1.85Ce0.15CuO4y thin film grown on SrTiO3 with different distance
between the waist of lens and target surface (dwt): a). Sample A;
dwt = 50 cm. b). Sample B; dwt = 51.5 cm. c). Sample C; dwt =
53 cm
around 80 200 nm2. The other grains have smaller size and
round shape with diameter around 60 nm2 and these grains
are higher than the previous mentioned one. The size of the
small grains is very homogenous and well distributed on the
thin film surface. The small grains observed on sample A
seem to be different with those of the spherical particulate or
droplet, which are commonly observed on the film prepared
by laser deposition technique since the particulates has in-
homogenous size. In sample B (Figure 3(c)), larger grains or
islands were observed compared to the previous film. These
Fig. 2 Graph of rocking curve measurement result for the (004) re-
flection peak for Nd1.85Ce0.15CuO4y thin films prepared with different
waist lens to target surface distance
grains are not regularly shaped. Detail scan on sample B
(Figure 3(d)) reveals the presence of nano-sized grains grow
between the large grains as well as on the top ones. TheAFMmicrographs of sample C are shown in Figure 3(e) and 3(f).
On the sample C, we can clearly see grains grow with rect-
angular shape. The grain is characterized by hillock growth
with a clearly seen terracing structure. Some screw disloca-
tions can be observed and it indicates the spiral growth mode
of the NCCO grains. The step height of the terrace is around
10 A, which was determined from a cross section analysis
and it is close to one unit cell c-axis length of NCCOof 12 A.
We can mention here that few nano-sized grains or particles
can still be observed on some of NCCO grains.
By comparing the AFM micrographs from these samples,
we realize that the population and size of small and sphericalgrains decreases as the intensity of (110) peak in the XRD
spectra decreases. It would indicate that these grains are re-
sponsible for the (110) and (220) peaks observed in the XRD
spectra. In sample A, the (110) oriented grains are dominant
compared with the c-axis oriented ones, where the c-axis
oriented grains are seen as flat grains and it is confirm with
the high value of I(110)/I(002). Meanwhile, in the sample B,
we should expect that the volume fraction of c-axis oriented
grains increases and it grows as large irregular shape islands.
As we saw on the AFM micrograph of sample A and B, the
non-c-axis grains hinder the growth of the large flat c-axis
Table 1 Values of some deposition parameters (waist of lens to target distance and laser fluence), NCCO growth
rate and ratio between the intensity of (110) and (002) reflection peaks of NCCO.
The waist of lens
to target Laser fluence NCCO growth
Sample Name distance, dwt (cm) (J/cm2) rate (A/pulse) I110/I002
A 50 4.2 0.6 4.75
B 51.5 2.8 0.4 1
C 53 2.2 0.3 0
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486 J Mater Sci: Mater Electron (2006) 17: 483488
(a) (b)
(d)
(f)
(c)
(e)
Fig.3 AFMimages of Nd1.85Ce0.15CuO4y thin filmgrown on SrTiO3.
a). Sample A, scanned on 5 5 m2 surface area. b). Sample A,
scanned on 0.5 0.5 m2 surface area. c). Sample B, scanned on
5 5 m2 surface area. d). Sample B, scanned on 1 1 m2 surface
area. d). Sample C, scanned on 5 5 m2 surface area. e). Sample C,
scanned on 1 1 m2 surface area
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J Mater Sci: Mater Electron (2006) 17: 483488 487
oriented grains and as the result, we have very small c-axis
oriented grains in sample A and irregular shape of c-axis ori-
ented grains in sample B. The AFM image of sample C give
a detail image of defects caused by the small (110) oriented
grains on the c-axis oriented ones (Figure 3(f)) but since the
number of (110) oriented grains is so small, we could not see
the peaks at the XRD spectrum. The AFM analysis shows
that by reducing the laser fluence on the target surface wouldgive a favorable condition for c-axis oriented grains to grow
as large rectangular grains.
A slow growth rate as the result of low laser fluence on
target surface could be the factor for growing high qual-
ity c-axis oriented NCCO thin film. In the case of YBCO
thin film prepared by PLD method, the a-axis and c-axis ori-
ented grains both can grow on the films at a certain condition
[19]. According to the adatom migration model, the adatom
of each element would migrate in a relatively long distance
and climb steps before residing at the stable site if they are
forming c-axis oriented grains. Meanwhile, short distance
movement would be needed for a-axis oriented growth [20].
The same mechanism could be considered for the growth of
NCCO thin film and in this case, the growth of (110) oriented
grains seems to be similar with the growth of a-axis oriented
grain in YBCO. Since all three NCCO samples were pre-
pared only with different laser fluence on the target surface,
it could be assumed that the most relevant factor to be con-
sidered in the NCCO case is the density of evaporated atoms
that impinge the substrate surface. In the condition of low
evaporated atoms density, we could expect a lower probabil-
ity of inter collision and early reaction between atoms and
therefore, the mobility of the adatoms on the surface would
increase and it would give more opportunity for the adatoms
to find a stable position and to form c-axis oriented grains.
The kinetic model might explain that the observed (110) ori-
ented grains are smaller and higher than for c-axis oriented
ones since for this growth, the adatoms only need to move in
very short distance.
The result from resistivity measurement is shown in Fig-
ure 4. Sample A shows the highest resistivity compared with
other samples and has a minimum at temperature around
75 K. The onset of superconducting critical temperature
(Tc, onset) is at T = 18 K but the zero resistivity (Tc0) was
observed below 11 K. The resistivity was found to be lower
for sample B than for sample A with a minimum at tempera-
ture around 50 K. Tc0 for sample B is at 15 K. The resistivity
data of the two samples (A and B) show a characteristic of the
underdoped NCCO, which has a resistivity minimum above
Tc. However, as we have seen on the AFM micrographs, both
samples have poor inter-grain connection and dislocation de-
fect due to the presence of (110) oriented grains and it would
give high electrical resistance value. For sample C, Tc,onsetwas observed at around 22 K with Tc0 at21Kasitisshownin
the insert of Figure 4. The resistivity results again confirm the
Fig. 4 Graph of electrical resistivity vs. temperature of
Nd1.85Ce0.15CuO4y thin film grown on SrTiO3. The insert graph
shows the resistivity of sample C around its superconducting critical
temperature
quality of the NCCO thin film grown with low laser fluenceon the target surface.
4. Summary
High quality NCCO thin film has been fabricated by pulsed
laser deposition technique. The sample that did not show
(110) reflection peak in the XRD spectrum was fabricated
with low laser fluence on the target surface of 2.2 J/cm2 and
the fraction of the non-c-axis oriented grains on the NCCO
film can be controlled by changing the laser fluence on the
targetsurface.The rocking curve measurement of this NCCO
thin film gave a FHMW value of 0.12 and resistivity mea-
surement showed a Tc0 valueof 21K withTc = 1 K,which
confirm the high quality of the sample. The non-c-axis ori-
ented grains would induce some defects and change the mor-
phology on the c-axis oriented ones and the c-axis oriented
grains grew into rectangular shaped grains with a clear view
of the terracing structure.
Acknowledgements We would like to thank H. Yamasaki, Y. Naka-
gawa, and J. C. Nie for allowing us using some equipments and help
during measurement and deposition. B. P would thank M. Murugesan
for suggestion and discussion. This work was supported by the Japan
Society for the Promotion of Science (JSPS).
References
1. Y. TOKURA, H. TAKAGI and S. UCHIDA, Nature 337 (1989)
345.
2. H. TAKAGI, S. UCHIDA and Y. TOKURA, Phys. Rev. Lett. 62 (1989)
1197.
3. R. P. VASQUESZ, A. GUPTA and A. KUSSMAUL, Sol. State Commun.
78 (1991) 303.
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4. Y. HIDAKA and M. SUZUKI, Nature 338 (1989) 635.
5. T. van DUZER and S. KUMAR, Cryogenics 30 (1990) 1014.
6. M. AKANI, A. FROESE, G. STAIKOV, W. J. LORENZ, M. ROHNER, R.
HOPFENGARTNER and G. SAEMANN-ISCHENKO, Phys. C245 (1995)
131.
7. T. D. CLARK, R. J. PRANCE and A. D. C. GRASSIE, J. Appl. Phys. 51
(1980) 2736.
8. E. HANAMURA, Phys. Stat. Sol. B 234 (2002) 166.
9. P. R. WILLMOTT and J. R. HUBER, Rev. Mod. Phys. 72 (2000)
315.
10. S. N. MAO, X. X. XI, S. BHATTACHARYA, Q. LI, T. VENKATESAN, J.
L. PENG, R. L. GREENE, J. MAO, D. H. WU and S. M. ANLAGE, Appl.
Phys. Lett. 61 (1992) 2356.
11. Y. LU, R. A. HUGHES, T. STRACH, T. TIMUSK, D. POULIN and J. S.
PRESTON, Phys. C197 (1992) 75.
12. H. HAENSEL, A. BECK, F. GOLLNIK, R. GROSS, R. P. HUEBENER and
K. KNORR, Phys. C 244 (1995) 389.
13. H. ADACHI, S. HAYASHI, K. SETSUNE, S. HATTA, T. MITSUYU and K.
WASA, Appl. Phys. Lett. 54 (1989) 2713.
14. A. GUPTA, G. KOREN, C. C. TSUEI, A. SEGMULLER and T. R. MCGUIRE,
Appl. Phys. Lett. 55 (1989) 1795.
15. D. P. BEESABATHINA, L. SALAMANCA-RIBA, S. N. MAO, X. X. XI and
T. VENKATESAN, Appl. Phys. Lett. 62 (1993) 3022
16. E. MAISER, P. FOURNIER, J. L. PENG, F. M. ARAUJO-MOREIRA, T.
VENKATESAN, R. L. GREENE and G CZJZEK, Phys. C 297 (1998)
15.
17. M. APRILI, M. COVINGTON, E. PARAOANU, B. NIEDERMEIER and
L. H. GREENE, Phys. Rev. B 57 (1998) R8139.
18. N. CHERIEF, D. GIVORD, A. LIeNARD, K. MACKAY, O. F. K. MCGRATH,
J. P. REBOUILLAT, F. ROBAUT and Y. SOUCHE, J. of Magnetism and
Magnetic Mat. 121 (1993) 94.
19. M. MUKAIDA and S. MIYAZAWA,Jap. J. Appl. Phys. 32 (1993) 4521.
20. Y. ICHINO, Y. YOSHIDA, Y. TAKAI, K. MATSUMOTO, H. IKUTA AND U.
MIZUTANI, Supercond. Scie. and Tech. 17 (2004) 775.
Springer