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Defect Study of CU2ZnSn(S,Se)4 Thin Film with Different Cu/Sn Ratio by Admittance Spectroscopy
Xianj ia Luo I ,Muhammad Monirul Islam I, Mohammad Abdul Halim I , Chong Xu I, Takeaki Sakurai I, Noriyuki Sakai2, Takuya Kato2, Hiroki Sugimoto2, Hitoshi Tampo3, Hajime Shibata3, Shigeru Niki3,
Katsuhiro Akimoto I
�Institute of A�plied �hysics, University of Tsukuba: 1-1-1 Tennodai, Tsukuba, Ibaraki,305-8573, Japan, Energy SolutIOn Busmess Center, Showa Shell SekIyu K.K., 2-3-2 Daiba, Minato-ku, Tokyo 135-8074,
Japan, 3National Institute of Advanced Industrial Science and Technology (AIST), 1-1-1 Umezono, Tsukuba, Ibaraki 305-8568, Japan
Abstract - Defect properties of CU2ZnSn(S"Sel.,)4 (CZTSSe) were investigated by admittance spectroscopy (AS). Two defect states (labeled EAt and EA2) were observed in CZTSSe (x=O.15) with different CutSn ratio. When the CutSn ratio increased from 1.75 to 1.95, the activation energy of EAt and EA2 decreased and the defect densities increased. The capture cross sections of EAt and EA2 defects are in the order from 10.16 cm
2 to 10.18 cm
2,
indicating that these two defects possibly do not impact on device
performance.
Keywords-Cu2ZnSnS4, CU2ZnSn(S,Se)4, admittance spectroscopy, defects, capture cross section.
I. INTRODUCTION
CU2ZnSn(Sx,Se\.x)4 (CZTSSe) has been considered as a
sustainable alternative to Cu(In,Ga)Se2 (CIGS) thin film solar
cells and has attracted significant attention, due to its low
toxicity and abundance [1]. The CZTSSe is a semiconductor
with a direct band gap varying from 1.0 e V to 1.4 e V and high
absorption coefficient in the order of lO4 cm·1 [2,3]. It has
been reported that CZTSSe alloys with high selenium content
have higher efficiency than those with high sulfur content [3].
Sugimoto et al. have reported that its efficiency mainly
depends on Cu/Sn ratio rather than Zn!Sn ratio [4]. Recently
the highest efficiencies of CZTSSe solar cells have reached
toI2.6% [5]. However, knowledge about defects of these
materials and their impact on the device performance remains
unclear. A complete understanding of the defects properties of
these materials could improve the device performance.
In this work, in order to understand the defect properties in
CZTSSe (x=0.15), admittance measurements were performed
in CZTSSe solar cell structure with different Cu/Sn ratio. The
admittance spectroscopy (AS) shows two defect states in all
CZTSSe samples. With increasing Cu/Sn ratio, the activation
energy of the both defects decreased and the defect density
increased. The capture cross section for both defects has been
estimated and the effect on the device performance is
discussed.
978-1-4799-4398-2/14/$31.00 ©2014 IEEE
II. EXPERIMENTAL
The CZTSSe thin film solar cells with different Cu/Sn ratio,
namely 1.65, 1.75 and 1.85, were fabricated in Energy
Solution Business Center, Showa Shell Sekiyu K.K.. The
detailed fabrication conditions for CZTSSe solar cells have
been described elsewhere [4]. The S concentration was fixed
at S/(S+Se)� 15% for three samples.
For AS measurements, samples were mounted inside a Janis
closed-cycle cryostat and measurements were performed in
the temperature range from 20 k to 340 k using Agilent 4284
A LCR meter with the ac frequencies from 1 KHz to 1 MHz
and 25 mV AC modulation voltage. The activation energy of
defects and defect density has been estimated by AS
measurements [6].
III. RESULTS AND DISCUSSION
Fig. 1 shows the admittance (dC/dlnco) spectra of CZTSSe
(x=0.15) with the Cu/Sn ratio of 1.75, 1.85 and 1.95. Two
peaks were detected labeled as EAI and EA2. A small peak in
CZTSSe sample with the Cu/Sn ratio of 1.75 was observed in
the lower temperature range as shown in the inset of Fig. 1.
The peak position ofEAI and EA2 shifted to lower temperature
with higher Cu/Sn ratio. Therefore, these results suggest that
the activation energy of EAI and EA2 should decrease with
increasing Cu/Sn ratio. The activation energy of these defects,
EA, were obtained from the slope of the Arrhenius plot,
In(coo/T2) versus liT, using the following equation [7,8]:
(1)
(2)
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N = 2(2mn*kT)%
c,v h2
(3)
(4)
Where, COo is the characteristic frequency of capacitance,
�o is the temperature independent pre-exponential factor, Nc,v is the effective density of the band, Vth is the average thermal
velocity, (Jt is the capture cross section of defect, m* is the
hole effective mass, k is the Boltzmann constant, h is the
Plank constant and EA is the activation energy of the defect
The defect density Nt was calculated according to the
following equation [6]:
(5)
Where W, q, Vbi, and Eg are depletion width, elemental
charge, built-in-potential and band gap, respectively.
-50 o 50 100 150 200 250 300 350 400
Temperatrue (K)
Fig. 1. Temperature-dependent admittance spectra of CZTSSe with the Cu/Sn ration of 1.75, 1.85 and 1.95 at 10
45 Hz. The inset is the expanded admittance spectrum of CZTSSe with 1.75 Cu/Sn ratio.
978-1-4799-4398-2/14/$31.00 ©2014 IEEE
The activation energy for all samples obtained by AS is
listed in Table I, which shows two kinds of defect in CZTSSe.
The activation energy ofEAI defect in CZTSSe with the Cu/Sn
ratio of l.75, l.85 and l.95 are around 270 meV, 220 meV
and 90 meV, and the values ofEA2 defect are around 150 meV,
70 meV and 60 meV, respectively. These results indicate that
high CuiSn ratio results in low activation energy. Recently
Sugimoto et al. have found the activation energy of defect
decreased with increasing Cu/Sn ratio by photoluminescence
and external quantum efficiency [4]. They also reported that
the valence band maximum of high Cu/Sn ratio sample is
higher than that of low Cu/Sn ratio sample, which maybe
leads to the shift of activation energy of defect in high Cu/Sn
ratio. The origin of this shift remains unclear and needs further
studied.
a CufSn=1.75
0.2
b CufSn=1.B5
';" lE1B N...,=1.40xl0'· (cm·3) > Q)
M � lE17
� .� lE16 Q)
'0 Q.
0.3 0.4 0.5 0.6
� lE15 ������������
'? E !:!. lE1B � 'iii c: � lE17 Q. �
I- 1 E16 L-'l..........J...L.I....�-'--�-'-�--'-�---'_'-----' 0.0 0.1 0.2 0.3 0.4 0.5 0.6
Activation Energy (eV)
Fig. 2.Defect spectra derived from admittance measurements in
CZTSSe with the Cu/Sn ratio of 1.75 (a), 1.85 (b) and 1.95 (c).
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Table I
The activation energy, defect density and capture cross section of defects in CZTSSe grown with different Cu/Sn ratio
EAt EA(meV)
Cu/Sn=1.75 270
Cu/Sn=1.85 220
Cu/Sn=1.95 90
EA2 Cu/Sn=1.75 150
Cu/Sn=1.85 70
Cu/Sn=1.95 60
The two kinds of defect levels in CZTSSe were also found
by Kask et al. [9]. They have assumed that the EAl and EA2
state belong to an interface state and acceptor defect of CUzn antisite, respectively, on the basis of their AS measurement
and photoluminescence. However, these assignments need
further evidence. Similar defect levels in CIGS have been
found in our previous study [ 10, 11]. However, the shallower
acceptor lever of V Cu, as the main p-type source in CIGS, was
not observed in this experiment. Yang et al. found only one
defect level in CZTSSe by AS measurements [3]. Such
difference may be due to the growth process of CZTSSe.
Fig. 2 shows defect spectra of CZTSSe with the Cu/Sn ratio
of 1.75, 1.85 and 1.95 derived from AS. Defect density
obtained by AS for all samples are shown in Table I. The
Gaussian fit was utilized to calculate the defect density, as
shown by dashed line. Due to the small activation energy
difference between two defects in CZTSSe with 1.95 Cu/Sn
ratio, only one defect density peak was observed from the
spectra, as shown in Fig. 2 (c). The Gaussian fit shows that the
defect density of EAl and EA2 are in the order of 1016 cm-3 and
the density increased with increasing Cu/Sn ratio. These
results reveal that the high Cu/Sn ratio results in high defect
density.
The thermal capture cross sections of the defect were
calculated from the equation (2), (3) and (4) and the results are
shown in Table I. The hole effective masses of CZTSe have
been calculated by Liu et al. using first-principles [ 12]. Capture cross sections of EAl and EA2 defect states are in the
range from 10-18 cm2
to 10-16 cm2
depending on Cu/Sn ratio.
The obtained value of the cross section is relatively small,
therefore, these defects possibly do not affect the device
performance.
978-1-4799-4398-2/14/$31.00 ©2014 IEEE
Nt (cm-J) (ft (cml)
3.1x1016 6.3xl0-17
3.5x1016 1.2xl0-16
5.7x1017 5.5xl0-18
1.1x1016 1.8xl0-17
1.4x1016 9.9xl0-18
5.1x1017 2.5xl0-17
IV. CONCLUSIONS
The activation energy, defect density and capture cross
section of defects in CZTSSe grown with different CU/Sn ratio
were obtained by AS measurements. We found two kinds of
defect levels in CZTSSe. With increasing Cu/Sn ratio in
CZTSSe, the activation energy of defects decreased. The
defect density increased with increasing Cu/Sn ratio. The
capture cross section of the two kinds of defect was estimated
to be in the range from 10-18 cm2
to 10-16 cm2
depending on
Cu/Sn ratio. From the value of the cross section, the defects
detected by AS possibly have no effective impact on the
CZTSSe solar cell performance.
REFERENCES [I] H. katagiri, "Cu2ZnSnS4 thin film solar cells," Thin Solid Films,
vol. 426, pp. 480-481, 200S. [2] H. katagiri, K. Jimbo, W. Maw, K. Oishi, M. Yamazaki, H.
Araki, A. Takeuchi, "Development of CZTS-based thin film solar cells," Thin Solid Films, vol.Sl7, pp.24SS-2460, 200S.
[3] H. Duan, W. Yang, B. Bob, C. Hsu, B. Lei, Y. Yang, "The role of sulfur in solution-processed CU2ZnSn(S,Se)4 and its effect on defect properties," Advanced Functional Materials, vol. 23, pp. 1466-1471, 2013.
[4] H. Sugimoto, C. Liao, H. Hiroi, N. Sakai, T. Kato, "Lifetime improvement for high efficiency Cu2ZnSnS4 submodules," in proceedings of the 391h IEEE photovoltaic specialist conference, 2013 . .
[S] W. Wang, M. T . Winkler, O. Gunawan, T. Gokmen, T . K. Todorov, Y. Zhu, and D. B.Mitzi, "Device Characteristics of CZTSSe Thin-Film Solar Cells with 12. 6% Efficiency," Advanced Energy Materials, doi:10. 1002/aenm.20130146S, 2013.
[6] T. Walter, R. Herberholz, C. Muller, H. Schock, "Determination of defect distributions from admittance measurements and
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application to Cu(ln,Ga)Se2 based heterojuncions," Journal of Applied Physics, vol. 80, pp. 4411-4420, 1996.
[7] D. Losee, "Admittance spectroscopy of impurity levels in schottky barriers," Journal of Applied Physics, vol. 46, pp. 2204-2214, 1975.
[8] M. Islam, N. Miyashita, N. Ahsan, Y. Okada, "Defect study of molecular beam epitaxy grown undoped GalnNAsSb thin film using junction-capacitance spectroscopy," Applied Physics Letters, vol. 102, pp. 74104-(1-5), 2013.
[9] E. Kask, M. Grossberg, R. Josepson, P. Salu, K. Timmo, 1. Krustok, "Defect studies in CU2ZnSnSe4 and CU2ZnSn(Seo7sSo2s)4by admittance and photoluminescence spectroscopy" Materials Science in Semiconductor Processing, vol. 16, pp. 992-996, 2013.
978-1-4799-4398-2/14/$31.00 ©2014 IEEE
[10] T. Sakurai, N. Ishida, S. Ishizuka, K. Matsubara, K. Sakurai, A. Yamada, G.K. Paul, K. Akimoto, S. Niki, "Investigation of relation between Ga concentration and defect levels of AI/Cu(ln,Ga)Se2 Schottky junctions using admittance spectroscopy" Thin Solids, vol. 515, pp. 6208-6211, 2007.
[11] T. Sakurai, M. Islam, H. Uehigashi, S. Ishizuka, A. Yamada, K. Matsubara, S. Niki, K. Akimoto, "Dependence of Se beam pressure on defect states in CIGS-based solar cells" Solar Energy Materials and Solar Cells, vol. 95, pp. 227-230, 2011.
[12] H. Liu, S. Chen, Y Zhai, H. Xiang, X. Gong, S Wei, "Firstprinciples study on the effective masses of zinc-blend-derived Cu2Zn-IV-VI4 (IV=Sn, Ge, Si and VI=S, Se)" Journal of Applied Physics, vol. 112, pp. 93717-(1-6), 2012.
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