Characterization of copper selenide thin films deposited by chemical bath deposition technique
Transcript of Characterization of copper selenide thin films deposited by chemical bath deposition technique
Characterization of copper selenide thin films deposited
by chemical bath deposition technique
Al-Mamun, A.B.M.O. Islam*
Department of Physics, University of Dhaka, Dhaka 1000, Bangladesh
Available online 28 July 2004
Abstract
A low-cost chemical bath deposition (CBD) technique has been used for the preparation of Cu2�xSe thin films onto glass
substrates and deposited films were characterized by X-ray diffractometry (XRD), X-ray photoelectron spectroscopy (XPS),
atomic force microscopy (AFM) and UV–vis spectrophotometry. Good quality thin films of smooth surface of copper selenide
thin films were deposited using sodium selenosulfate as a source of selenide ions. The structural and optical behaviour of the
films are discussed in the light of the observed data.
# 2004 Elsevier B.V. All rights reserved.
Keywords: AFM; CBD; Copper selenide; XPS; XRD
1. Introduction
Most of the semiconducting metal chalcogenides
are important materials for applications in various
photoelectric and other kinds of devices. Thin films
of metal chalcogenides can be deposited on to glass,
metal, plastics and other substrates by a variety of
techniques, such as flash evaporation [1,2], vacuum
evaporation [3], electrodeposition [4], and electroless
deposition [5], to the simplest method of chemical
bath deposition (CBD) [6–16]. The optical and elec-
trical characteristics of the deposited materials often
depend on the deposition technique used. In this
experiment copper selenide thin films with various
ratios of copper and selenium were deposited onto
glass substrates using low-cost CBD method. This
paper describes the results observed by XRD, XPS,
AFM and optical investigations on the Cu2�xSe film
prepared by CBD.
2. Experimental details
The chemicals, used for the preparation of thin
films, were LR grade (Merck) cupric chloride dihy-
drate (CuCl2�2H2O), selenium powder (BDH) of
99.99% purity, sodium sulfite (Na2SO3) (Merck),
triethanol amine (TEA) (Merck) and ammonium
hydroxide (NH4OH) (Merck). At first, selenium was
used for the preparation of sodium selenosulfate.
Second, CuCl2�2H2O solution was mixed with
NaSeSO3 at constant stirring. Ten milliliters of TEA
(0.1 M) was added to this solution. Thirty percent of
NH4OH solution was used to adjust the pH of the
reaction bath. Microscope glass slides were used as
substrates and they were cleaned well with detergent
and distilled water, and were kept in H2SO4 for about
1 h. The substrates were then washed first under
Applied Surface Science 238 (2004) 184–188
* Corresponding author. Fax: þ880 2 8615583.
E-mail address: [email protected] (A.B.M.O. Islam).
0169-4332/$ – see front matter # 2004 Elsevier B.V. All rights reserved.
doi:10.1016/j.apsusc.2004.05.208
running tap water to clean the acid off and then
cleaned with acetone. Just after cleaning with acetone,
they were washed with running tap water and finally
cleaned with distilled water and were dried in air prior
to film deposition. The substrates were then immersed
vertically into the deposition bath against the wall of
the beaker containing the reaction mixture. The
deposition was allowed to proceed at room tempera-
ture for different time durations from 15 to 180 min.
After deposition, the glass slides were taken out from
the bath, washed with distilled water and were dried in
blowing air. The thicknesses of the films for about 1 h
deposition were obtained in the range 0.12–0.18 mm.
Identification of the deposited film material was
carried out by a Philips X’Pert X-ray diffractometer.
XPS experiments were performed in a VG ESCALAB
MkII photoelectron spectrometer. Electrons were
excited with an X-ray source (Mg Ka: hn ¼1253.6 eV). A Thermomicroscopes AFM was used
for morphological study. The optical measurements
were performed using a UV-121V spectrophotometer,
Shimadzu, Japan.
3. Results and discussion
3.1. XRD measurement
Fig. 1 shows the XRD pattern of Cu2�xSe thin film.
Fig. 1(a) is for the as-deposited Cu2�xSe thin film and
Fig. 1(b) for the Cu2�xSe thin film followed by
annealing at 523 K in air. Lot of noise is observed
in the XRD pattern which may be due to the growth of
disorder film. From this pattern it shows that no well-
defined peak was found and no well-defined plane was
obtained in the case of as-deposited films, which
suggests that the as-deposited films were disorder.
A little tendency of growing peaks is found at the
angles 2y ¼ 27.308, 45.358 and 52.788. The intensity
of the observed peaks is very low, which become
stronger due to annealing at 250 8C. Fig. 1(b) shows
well-defined peaks suggesting the formation of crys-
talline film due to annealing at higher temperatures. A
comparison of the observed pattern with the standard
JCPDS cards shows that the annealed samples with
above condition possess a structure matching the
mineral spherulites (JCPDS 26-512) [17], Cu2�xSe
with x ¼ 0.2 belongs to the cubic system with
a ¼ 5.697 A. Garcıa et al. observed the crystalline
structure in case of as-deposited Cu2�xSe (x ¼ 0.15)
films and possessed the structure matching the mineral
berelianite (JCPDS 6-680) [13]. In our case, the films
may not be thick enough to give sufficient intensity for
distinguishing the peaks from the noise. We have tried
to deposit thicker film, but the powder formation
occurs in case of thicker film. However, the observed
peak positions of the annealed sample are in well
agreement with those due to reflection from (1 1 1),
(2 2 0) and (3 1 1) planes of the reported structure. The
same reflection plane was observed for as-deposited
Cu2�xSe thin film prepared by CBD method using
CuSO4 and trisodium citrate solution [13,15,16]. The
average grain diameter for as-deposited sample was
found to be 0.025 nm that increases for annealed
samples to 0.724 nm. Very low grain size is observed
for as-deposited samples, which was increased about
30% owing to annealing. It is necessary to mention
here that the crystallite grain size in the films was
calculated using Scherrer formula [18].
3.2. XPS measurements
The XP spectra of different copper selenide thin
film of as-deposited sample presented in Fig. 2. In the
Fig. 1. XRD pattern of Cu2�xSe thin film: (a) as-deposited and (b)
after annealing at 523 K for 1 h in air.
Al-Mamun, A.B.M.O. Islam / Applied Surface Science 238 (2004) 184–188 185
figure, spectrum a represents for as-deposited sample,
while spectrum b for the sample annealed at 473 K for
30 min in UHV and spectrum c for the sample
annealed at 523 K for 30 min in UHV. It is observed
that the as-deposited film is mostly covered with
oxygen (at 531 eV) and carbon (at 285 eV) (spectrum
a). Whereas, the peak intensity of Cu and Se are very
weak. It is usual that the chemically deposited sample
may be contaminated with oxygen and carbon from
the environment as the sample is exposed to environ-
ment during preparation. It is seen that the peaks
corresponding to Cu and Se become prominent in
the sample annealed at 473 K (spectrum b) and after
annealing at 523 K, the intensity of Cu and Se peaks
become more prominent, thereby indicating lowering
of contamination owing to annealing at 523 K (spec-
trum c). Further annealing at around 573 K, Se starts to
desorb from the surface (data are not shown), which
means that copper selenide film remains stable below
573 K. The amount of oxygen decreases significantly
but Se is also started to decrease due to annealing at
above 573 K. The core level spectra of Cu 2p and Se
3d were also measured (data are not shown). The peak
area of Cu 2p and Se 3d has been calculated. Cu/Se
mole ratio has been calculated from the height ratio of
Cu 2p and Se 3d. It was also confirmed using the
formula
Ni
Nj
¼ Ii=Si
Ij=Sj
� �(1)
where N’s are the concentrations, I’s are the intensities
of photoelectron emission peaks after removing the
background and S’s are the ASFs (atomic sensitivity
factor) of the respective elements. The Cu/Se ratio is
estimated to be 1.8 for sample. Similarly different
samples have been deposited with different Cu and Se
ratio. The depth profile of the Cu2�xSe films by XPS
showed compositional uniformity along the depth.
3.3. AFM measurements
AFM image of as-deposited copper selenide thin
film is shown in Fig. 3 for the scan area of 2 mm�2 mm. It seems that the overall film surface is almost
smooth. The film surfaces contained small islands, and
many continuous islands are overlapping on the glass
substrate. Itwasobservedfromtheprofilediagramof the
AFM image that the mean roughness and mean height
are in the range 2.9–3.4 and 11–15 A, respectively.
3.4. Analysis of the optical absorption
The variations of transmittance T (%) of Cu2�xSe
thin film with wavelength l for as-deposited samples,
Fig. 2. XP spectra of Cu2�xSe thin film: (a) as-deposited, (b) after
annealing at 473 K for 30 min in UHV and (c) after annealing at
523 K for 30 min in UHV.
Fig. 3. AFM image of as-deposited Cu2�xSe thin film for the scan
area of 2 mm � 2 mm.
186 Al-Mamun, A.B.M.O. Islam / Applied Surface Science 238 (2004) 184–188
annealed at different temperatures are shown in
Fig. 4(a). Transmittance is obtained to be about 5–
50% in the wavelength range 400–1100 nm. A gradual
decrease in transmittance on annealing is observed in
the lower wavelength region, which may be due to
absorption by free carrier in the degenerate films. The
peak values of transmission spectra are seen at around
820–980 nm means that the absorption started around
the same wavelength and the transmittance becomes
very low at l < 500 nm. In the near-infrared, the
transmittance decreases with the increase of wave-
length.
The variation of reflectance (R%) with l is shown in
Fig. 4(b). Reflectance is found to be about 2–20% at
the wavelength range 400–1100 nm. It is observed in
the R (%) versus l curves that there are two peaks
around 560–600 and 820–940 nm. Both the peaks shift
to higher wavelength with annealing temperature. The
second R (%) peak appears at the same wavelength
region where the transmittance peak appears in
Fig. 4(a). These behaviours are in well agreement
with the published results of Cu2�xSe thin film pre-
pared by CBD technique with CuSO4�5H2O at 298 K
for 8 h [14]. Noticeable change of reflectance is
observed due to annealing at different temperatures.
It is also observed the noticeable change of color of the
films due to annealing at different temperatures under
reflected and transmitted daylight condition. It is
observed that color of the film was changed from
greenish to orange due to annealing. It means that
as-deposited film is contaminated by oxygen, and
oxygen contamination starts to remove due to anneal-
ing. The color becomes greenish orange on annealing
at 473 K, and at 523 K, the color changes to fully
orange, which does not change on annealing above
573 K. Lakshmi et al. reported that the color of the as-
deposited Cu2�xSe film was reddish brown [15,16].
The direct and indirect bandgap values are obtained
from plots of a2 and a1/2, against the corresponding
value of the photon energy hn (eV), respectively
(figures are not shown). It is observed that the direct
bandgap varies in the range 1.9–2.3 eVand the indirect
bandgap is in the range 1.2–1.7 eV from as-deposited
sample to all annealed samples up to 523 K. The larger
bandgap values in the as-deposited samples compared
with that of the annealed samples are arising from
smaller grain size in the former [11]. All these optical
bandgap values are close to that Cu2�xSe thin film
prepared by CBD technique using CuSO4 and N,N-
dimethylselenourea [8,13,15,16]. It is observed that
both direct and indirect bandgap values of as-depos-
ited samples are higher compared with those of the
annealed samples. The decrease of bandgap due to
annealing may be understood by the improvement of
crystallinity of the as-deposited film on annealing as
observed in XRD.
4. Conclusion
Good quality thin films of smooth surface of copper
selenide thin films were deposited using sodium sele-
nosulfate as a source of selenide ions. The crystallinity
is very low in as-deposited samples, but that improves
Fig. 4. The optical transmittance (a) and reflectance (b) spectra of Cu2�xSe thin film: as-deposited films were annealed at different
temperature in the range 303–523 K.
Al-Mamun, A.B.M.O. Islam / Applied Surface Science 238 (2004) 184–188 187
on annealing in air at 523 K. The grain size of the as-
deposited samples was very small which is observed to
be increase about 30% owing to annealing in air at
523 K. Transmittance and reflectance were found in
the range 5–50 and 2–20%, respectively. The bandgap
for direct transitions varies in the range 1.9–2.3 eVand
that for indirect transition is in the range 1.2–1.7 eV
from as-deposited to annealed sample.
Acknowledgements
The authors are grateful to the Director and staff of
Semiconductor Technology Research Center (STRC),
University of Dhaka, for providing laboratory facil-
ities, and to the Bose Center for Advanced Study and
Research in Natural Sciences, University of Dhaka,
for financial support. The authors also like to acknowl-
edge Prof. W. Jaegermann, TU Darmstadt, Germany,
for allowing his laboratory to do the XPS and AFM
measurements during the research stay in Germany of
A.B.M.O.I.
References
[1] S.G. Ellis, J. Appl. Phys. 38 (1967) 2906.
[2] B. Tell, J.J. Wiegand, J. Appl. Phys. 48 (1977) 5321.
[3] A.M. Herman, L. Fabick, J. Cryst. Growth 61 (1983) 658.
[4] S. Massaccesi, S. Sanchez, J. Vedel, J. Electrochem. Soc. 140
(1993) 2540.
[5] S.K. Haram, K.S.V. Santhanam, Thin Solid Films 238 (1994)
21.
[6] A. Mondal, P. Pramanik, J. Solid State Chem. 55 (1984) 116.
[7] G.K. Padam, Thin Solid Films 150 (1987) L89.
[8] G. Hodes, A.A. Yayor, F. Decker, P. Motisuke, Phys. Rev. B
36 (1987) 4215.
[9] I. Grozdanov, Semicond. Sci. Technol. 9 (1994) 1234.
[10] C. Levy-Clement, M. Neumann-Spallart, S.K. Haram, K.S.V.
Santhanam, Thin Solid Films 302 (1997) 12.
[11] V.M. Garcıa, M.T.S. Nair, P.K. Nair, R.A. Zingaro, Semicond.
Sci. Technol. 12 (1997) 645.
[12] P.K. Nair, M.T.S. Nair, V.M. Garcıa, O.L. Arenas, Y. Pena, A.
Castillo, I.T. Ayala, O. Gomezdaza, A. Sanchez, J. Campos,
H. Hu, R. Suarez, M.E. Rincon, Sol. Energy Mater. Sol. Cells
52 (1998) 313.
[13] V.M. Garcıa, P.K. Nair, M.T.S. Nair, J. Cryst. Growth 203
(1999) 113.
[14] P.K. Nair, V.M. Garcia, O. Gomez-Daza, M.T.S. Nair,
Semicond. Sci. Technol. 16 (2001) 855.
[15] M. Lakshmi, K. Bindu, S. Bini, K.P. Vijaykumar, C. Sudha
Kartha, T. Abe, Y. Kashiwaba, Thin Solid Films 370 (2000)
89.
[16] M. Lakshmi, K. Bindu, S. Bini, K.P. Vijaykumar, C. Sudha
Kartha, T. Abe, Y. Kashiwaba, Thin Solid Films 386 (2001)
127.
[17] R. Heyding, R.M. Murray, Can. J. Chem. 54 (1976) 841.
[18] C.S. Barret, T.B. Massalski, Structure of Metals, McGraw-
Hill, New York, 1966, p. 155.
188 Al-Mamun, A.B.M.O. Islam / Applied Surface Science 238 (2004) 184–188