Table of Contents Author Guidelines Submit a Manuscript
Journal of Nanomaterials
Volume 2013, Article ID 320375, 5 pages
Research Article

Fabrication and Characterization of Thin Film Solar Cell Made from CuIn0.75Ga0.25S2 Wurtzite Nanoparticles

1Institute for Solar Energy, Xiamen University, Xiamen, Fujian, China
2Department of Chemistry, Idaho State University, Pocatello, ID 83209, USA

Received 20 February 2013; Revised 17 April 2013; Accepted 7 May 2013

Academic Editor: Weidong Zhou

Copyright © 2013 Fengyan Zhang et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.


CuIn0.75Ga0.25S2 (CIGS) thin film solar cells have been successfully fabricated using CIGS Wurtzite phase nanoparticles for the first time. The structure of the cell is Glass/Mo/CIGS/CdS/ZnO/ZnO:Al/Ag. The light absorption layer is made from CIGS Wurtzite phase nanoparticles that are formed from single-source precursors through a microwave irradiation. The Wurtzite phase nanoparticles were converted to Chalcopyrite phase film through a single-step annealing process in the presence of argon and sulfur at 450°C. The solar cell made from Wurtzite phase nanoparticles showed 1.6% efficiency and 0.42 fill factor.

1. Introduction

Current CIGS thin film solar cells using evaporation or sputtering processes are expensive, and the composition uniformity is difficult to control on a large scale. Recent studies show that through spraying or printing, the light absorption layer can be made from a nanoparticle ink, which shows promise to reduce the fabrication cost of the solar cell significantly [15]. But, the process to convert nanoparticle layers into a dense film with large grain-sizes and a pin hole/crack-free surface is difficult to achieve. Large particle sizes with more labile passivation ligands are preferred in order to lower the thermal budget and reduce the cost of the sintering process. More labile ligands require a lower temperature for their removal, and larger particles have less passivation layer to remove, relatively speaking, since their surface area to volume ratio is lower. The solution method does not lend itself well to the growth of larger CIGS nanoparticles in the Chalcopyrite phase. In our case, we chose to use large-sized CIGS particles in a different metastable phase, Wurtzite particles, and then convert them into a Chalcopyrite phase CIGS thin film at higher temperature.

The CIGS Wurtzite phase has been prepared by several research groups recently [615], and it has the same composition as the Chalcopyrite phase. Wurtzite phase is a cation disordered polymorph of Chalcopyrite with copper and indium cations randomly sharing common lattice sites. It belongs to space group P63mc with nm and nm. The hexagonal plate-shaped nanocrystals offer potential to be packed differently compared to spherical Chalcopyrite nanoparticles and ultimately produce a large grain size and better connectivity in the resulting film when annealed. Since the CIGS Wurtzite phase is a metastable phase, it can be effectively converted to a Chalcopyrite phase via simple thermal treatment at high temperature [6]. The growth process of the Wurtzite phase nanoparticles is also controllable, and it has been demonstrated that certain reaction conditions can be used to produce large-sized hexagonal plate particles with a lower surface area to volume ratio than smaller Chalcopyrite particles. Steinhagen et al. recently reported the use of CuInSe2 Wurtzite nanowires in the fabrication of solar cells with 0.1% efficiency [15]. To the best of our knowledge, Wurtzite structured CIGS nanoparticles have not been fabricated into a solar cell. In this paper, we describe the procedures of fabricating a CIGS thin film solar cell from large metastable Wurtzite phase nanoparticles.

2. Experimental

2.1. Device Construction

The device structure used in these studies is one that is commonly used for CIGS thin film cell construction, Glass/Mo/CIGS/CdS/ZnO/ZnO:Al/Ag [16]. The Mo layer was deposited by DC sputtering using a Denton Desktop Pro. The current used was 300 mA and the pressure was held at 0.67 Pa. The thickness of Mo layer was 0.5 μm with resistivity of 5 × 10−5 ohm-cm. Thin film of Wurtzite CIGS absorber layer was deposited using an ink containing 20 wt% nanoparticles in toluene on top of the Mo.

The CIGS nanoparticles were synthesized by decomposing the appropriate single source precursors (SSPs), (Ph3P)2Cu(μ-SC2H5)2In(SC2H5)2 (1) and (Ph3P)2Cu(μ-SC2H5)2Ga(SC2H5)2 (2), as described in the literature [1721]. Using this established procedure, CIGS nanoparticles containing 75% In and 25% Ga, in primarily Wurtzite phase, were obtained. In Figure 1, the TEM micrograph of CIGS nanoparticles clearly shows hexagonal plate features of Wurtzite phase mixed with some very smaller Chalcopyrite nanoparticles. The SAED data is consistent with predominant Wurtzite phase mixed in with Chalcopyrite (Figure 1).

Figure 1: TEM micrograph with SAED inserts of the Wurtzite CIGS nanoparticles.

The Wurtzite CIGS nanoparticles were made into an ink containing 20 wt% nanoparticles in toluene. The doctor blade technique was used to apply the film onto the Mo surface; then a pressure of 68.9 MPa was used to increase the density of the film. Annealing in a sulfur and argon atmosphere was then performed at 450°C. This temperature was chosen because thermal gravimetric analysis/mass spectrometry analysis of Wurtzite nanoparticles indicated that alkyl sulfide passivating groups leave the CIGS nanoparticle at temperatures between 250 and 350°C [18]. In addition, the phase conversion from Wurtzite to Chalcopyrite, recrystallization and grain growth of the CIGS thin films normally occur between 450–600°C [6]. In order to minimize the defects in the CIGS film and to achieve the required thickness, three applications of the CIGS layer were performed followed by annealing at 450°C. The thickness of CIGS layer used in the solar cells was 5 μm based on SEM measurements. After forming the light absorbing layer, the rest of the CdS/ZnO/ZnO:Al layers were fabricated.

The CdS buffer layer was deposited on the CIGS using the chemical bath deposition method from aqueous solutions of CdCl2·2H2O, NH4OH, NH4Cl, and thiourea. The concentrations were 0.0036 M, 0.360 M, 0.024 M, and 0.009 M, respectively. The deposition temperature was kept at 70°C using a water bath, and the deposition time was 45 min with continuous stirring. The achieved film thickness was about 100 nm. After the CdS deposition, the Glass/Mo/CIGS/CdS portion of the cell was subjected to further annealing in a sulfur and argon atmosphere at 200°C for 30 min to increase the density of the CdS layer.

The ZnO film was then deposited using the Denton sputtering tool. Some experimentation with this layer was necessary in order to achieve a high transparency and low resistivity. The optimal parameters to form a 100 nm ZnO thin film were (1) the current at 80 mA, (2) an Ar/O2 flow of 21 sccm/14 sccm, (3) the chamber pressure of 0.67 Pa, and (4) a temperature of 160°C. The resulting ZnO film exhibited resistivity of  ohm-cm with 90% transparency. The ZnO:Al film was deposited with the same sputtering tool. However, for this layer, RF sputtering was used. The composition of the RF target was ZnO with 2 wt% Al2O3. The RF power was kept at 100 W and the substrate temperature was 160°C. The achieved resistivity of the RF sputtered ZnO:Al was  ohm-cm with 90% transparency at 700 nm wavelength. The thickness of the ZnO:Al used in the solar cell was around 400 nm.

The device was completed by applying Ag paste in a line for the top contact. The electrical contacts were then made to the silver paste on the top and the Mo layer on the bottom.

2.2. Synthesis of CuIn0.75Ga0.25S2 Wurtzite Nanoparticles

Equal amounts of SSPs 1 and 2, (Ph3P)2Cu(μ-SEt)2In(SEt)2 (SSP 1, 6.00 g, 6.33 mmol) and (Ph3P)2Cu(μ-SEt)2Ga(SEt)2 (SSP 2, 5.71 g, 6.33 mmol), are dissolved in dried benzene (60 mL) in the presence of one equiv of 1,2-ethanedithiol (1.06 mL, 12.66 mmol). The mixture was stirred at room temperature for 5 min and the liquid was evaporated off to afford a solid precursor 3. In a dry Milestone microwave vessel, the precursor 3 (1.714 g) and (Ph3P)2Cu(μ-SEt)2In(SEt)2 (SSP 1, 1.243 g) was dissolved in benzyl acetate (20.0 mL) followed by addition of 3-mercaptopropionic acid (4.0 mL). The solution was capped and stirred for 5 min at room temperature. The reaction mixture was then irradiated with microwaves in a Milestone Microwave (Labstation ETHOS EX). The reaction was ramped for 15 min to reach the temperature of 240°C and was held for 1 h. Upon completion, the reaction was cooled to room temperature to yield black precipitation of CuIn0.75Ga0.25S2 Wurtzite nanoparticles. The resulting nanoparticles were isolated from the benzyl acetate solution by centrifugation and washed three times with CH3OH to remove any impurities. The product was then dried in vacuo to provide a black powder. The nanoparticles were dispersed in toluene as 20 wt% ink.

Characterization of the nanoparticles was performed with a JEOL 2010 high-resolution transmission electron microscope (HRTEM) with a spatial resolution of 0.194 nm. Powder X-ray diffraction (XRD) patterns were acquired with a Bruker D8 Discover diffractometer using CuKa radiation and a scintillation detector. Scans were collected for 4 hrs employing a 0.06° step width at a rate of 10 s/step resulting in a 2θ scan range from 10–60°.

3. Results and Discussion

As seen in Figure 2, the XRD data of CIGS thin film made from the Wurtzite phase nanoparticles displays three characteristic peaks between 2θ of 25 and 33 with significant broadness indicating small nanoparticle sizes. Upon annealing at 450°C for 1 hour, in a sulfur and argon atmosphere, the peaks converged and the characteristic XRD pattern for Chalcopyrite phase emerged. The widths of the peaks in the post-annealed XRD trace clearly show that the films made from Wurtzite CIGS nanoparticles were converted into a large crystalline Chalcopyrite phase film indicated by sharp peaks [6].

Figure 2: XRD spectra of the nanoparticles before and after annealing.

In Figure 3, SEM images of thin films deposited with the Wurtzite nanoparticles before and after annealing show that the grain sizes have grown to about 150 nm after annealing. Although a significantly larger grain size cannot be clearly seen in the SEM images, the nanoparticles appear to have fused together to make a continuous path for the carriers.

Figure 3: SEM images of the Wurtzite nanoparticles deposited in a thin film. The preannealed image is on the left, and the postannealed figure is on the right.

The light collecting area of the solar cells was measured to be about 0.25 mm2. A Sciencetech AM 1.5 Solar Simulator was used as the light source and electrical characteristics were measured using a Keithley 2400 source meter. Calibration of the light intensity was accomplished with an Ocean Optics light sensor. Cell parameters were derived from the current-voltage ( - ) curves, (Figure 4), of the solar cell. The efficiency of our best CIGS Wurtzite solar cell was reported in Table 1 in comparison to our best CIGS Chalcopyrite solar cell. An efficiency of 1.6% with a fill factor (ff) of 0.42 was achieved for the solar cell made from CIGS Wurtzite phase nanoparticles.

Table 1: Comparison of cell properties including open-circuit voltage, short-circuit current, between Wurtzite-based and Chalcopyrite-based solar cells annealed at 450°C.
Figure 4: Representative - curves for a Wurtzite-based solar cell collected in the dark and in the light.

There are several potential explanations for why our Wurtzite-based solar cells had better efficiency than the cell constructed with Chalcopyrite nanoparticles. One explanation is that our hexagonal plate Wurtzite phase nanoparticles were much bigger in size thus had less surface area than smaller spherical Chalcopyrite phase nanoparticles. Less surface area means less organic passivation layer that needs to be removed to achieve a well-connected, large grain size CIGS layer. From our previous experience, the annealing temperature using Chalcopyrite phase nanoparticles normally needs to be 550°C or higher. We have observed that annealing Wurtzite nanoparticles at 450°C provide similar or better PV properties than Chalcopyrite nanoparticles that are annealed at 550°C.

A second explanation is that Wurtzite-based solar cells should show higher efficiency than our own Chalcopyrite-based solar cells is related to the relative stability of the Wurtzite phase. Since, the Wurtzite phase is a metastable phase, conversion to the Chalcopyrite phase results in a net release of energy, once the activation barrier has been overcome. The larger Wurtzite nanoparticles thus must lose energy to become large Chalcopyrite particles, and the excess energy could be used to shed the passivation layers allowing for a larger grain size.

Finally, when making solar cells using Wurtzite phase nanoparticles, the phase change of the nanoparticles from Wurtzite to Chalcopyrite is accompanied by a density change. For CuIn0.75Ga0.25S2, the unit cell parameters are  nm,  nm for Wurtzite and  nm,  nm for Chalcopyrite, and these values yield calculated densities of 4.57 g/cm3 and 4.24 g/cm3, respectively. The more dense Wurtzite material is converted to the less dense Chalcopyrite phase during the 450°C annealing step. The volume per mass must increase suggesting that the CIGS material must swell. This swelling would likely help reduce the presence of defect sites and produce a more efficient absorber layer in the final cell.

Figure 4 shows the current-voltage ( ) plots in the light and in the dark of a solar cell processed from CIGS Wurtzite phase nanoparticles. These plots and the fill factor given in Table 1 are comparable with many published results using Chalcopyrite thin films, which were normally fabricated at 450°C or higher annealing temperatures [22]. In addition, for comparison, our own reference Chalcopyrite reference cells had much lower efficiency of 0.015% and a fill factor of 0.35 when constructed in analogous manner. Thus, the use of Wurtzite phase CIGS nanoparticles as a basis for the production of the absorber layer has no detrimental effects and has the potential to produce nanoparticle-based solar cells with higher efficiency than cells made from the Chalcopyrite phase nanoparticles.

4. Conclusion

In conclusion, an alternative route using CIGS Wurtzite nanoparticles for the fabrication of CIGS thin film photovoltaic devices has been demonstrated. The 0.25 mm2 solar cell showed an efficiency of 1.6% with a fill factor of 0.42. The and of the cell were 15 mA/cm2 and 230 mV, respectively after annealing the cell by a single step in a sulfur and argon atmosphere at 450°C. The utility of CIGS Wurtzite nanoparticles is promising for a high-throughput and high-yield process for low-cost thin film solar cells. The large Wurtzite particle size, less organic ligands, and density change associated with converting the Wurtzite phase to Chalcopyrite phase may all play an important role on making a better quality absorber layer with less defects and less energy. These properties are critical for improving the thin film CIGS solar cell’s performance. Further optimization of the annealing process by increasing the annealing temperature and adjusting the time or by using a RTA process will likely further improve the cell efficiency.


The authors Chivin Sun, Rene G. Rodriguez, and Joshua J. Pak would like to acknowledge partial support from DOE EPSCoR Grant no. (DE-FG02-04ER46142) for this work. Analysis of materials in this work was partially supported by the National Science Foundation under Grant no. (NSF CHE-1048714). Synthetic efforts in this work were partially supported by the National Science Foundation under Grant no. (NSF CHE-108952). The authors would also like to thank Anna Hoskins for help with the electrical measurements and Aaron Thurber at Boise State University for the assistance with TEM work.


  1. Q. Guo, G. M. Ford, H. W. Hillhouse, and R. Agrawal, “Sulfide nanocrystal inks for dense Cu(In1−xGax)(S1−ySey)2 absorber films and their photovoltaic performance,” Nano Letters, vol. 9, no. 8, pp. 3060–3065, 2009. View at Publisher · View at Google Scholar · View at Scopus
  2. Q. Guo, S. J. Kim, M. Kar et al., “Development of CulnSe2 nanocrystal and nanoring inks for low-cost solar cells,” Nano Letters, vol. 8, no. 9, pp. 2982–2987, 2008. View at Publisher · View at Google Scholar · View at Scopus
  3. B. D. Weil, S. T. Connor, and Y. Cui, “CuInS2 solar cells by air-stable ink rolling,” Journal of the American Chemical Society, vol. 132, no. 19, pp. 6642–6643, 2010. View at Publisher · View at Google Scholar · View at Scopus
  4. M. G. Panthani, V. Akhavan, B. Goodfellow et al., “Synthesis of CuInS2, CuInSe2, and Cu(InxGa1−x)Se2 (CIGS) nanocrystal “inks” for printable photovoltaics,” Journal of the American Chemical Society, vol. 130, no. 49, pp. 16770–16777, 2008. View at Publisher · View at Google Scholar · View at Scopus
  5. L. Li, N. Coates, and D. Moses, “Solution-processed inorganic solar cell based on in situ synthesis and film deposition of CuInS2 nanocrystals,” Journal of the American Chemical Society, vol. 132, no. 1, pp. 22–23, 2010. View at Publisher · View at Google Scholar · View at Scopus
  6. Q. Yunxia, L. Qiangchun, T. Kaibin, L. Zhenghua, R. Zhibiao, and L. Xianming, “Synthesis and characterization of nanostructured wurtzite CuInS2: a new cation disordered polymorph of CuInS2,” Journal of Physical Chemistry C, vol. 113, no. 10, pp. 3939–3944, 2009. View at Publisher · View at Google Scholar · View at Scopus
  7. M. E. Norako and R. L. Brutchey, “Synthesis of metastable wurtzite CuInSe2 nanocrystals,” Chemistry of Materials, vol. 22, no. 5, pp. 1613–1615, 2010. View at Publisher · View at Google Scholar · View at Scopus
  8. M. E. Norako, M. A. Franzman, and R. L. Brutchey, “Growth kinetics of monodisperse Cu-In-S nanocrystals using a dialkyl disulfide sulfur source,” Chemistry of Materials, vol. 21, no. 18, pp. 4299–4304, 2009. View at Publisher · View at Google Scholar · View at Scopus
  9. D. Pan, L. An, Z. Sun et al., “Synthesis of Cu-In-S ternary nanocrystals with tunable structure and composition,” Journal of the American Chemical Society, vol. 130, no. 17, pp. 5620–5621, 2008. View at Publisher · View at Google Scholar · View at Scopus
  10. S. K. Batabyal, L. Tian, N. Venkatram, W. Ji, and J. J. Vittal, “Phase-selective synthesis of CuInS2 nanocrystals,” Journal of Physical Chemistry C, vol. 113, no. 33, pp. 15037–15042, 2009. View at Publisher · View at Google Scholar · View at Scopus
  11. Y.-H. A. Wang, X. Zhang, N. Bao, B. Lin, and A. Gupta, “Synthesis of shape-controlled monodisperse wurtzite CuInxGa1−xS2 semiconductor nanocrystals with tunable band gap,” Journal of the American Chemical Society, vol. 133, no. 29, pp. 11072–11075, 2011. View at Publisher · View at Google Scholar · View at Scopus
  12. S. T. Connor, C.-M. Hsu, B. D. Weil, S. Aloni, and Y. Cui, “Phase transformation of biphasic Cu2S-CuInS2 to monophasic CuInS2 nanorods,” Journal of the American Chemical Society, vol. 131, no. 13, pp. 4962–4966, 2009. View at Publisher · View at Google Scholar · View at Scopus
  13. B. Koo, R. N. Patel, and B. A. Korgel, “Wurtzite-Chalcopyrite polytypism in CuInS2 nanodisks,” Chemistry of Materials, vol. 21, no. 9, pp. 1962–1966, 2009. View at Publisher · View at Google Scholar · View at Scopus
  14. K. Nose, Y. Soma, T. Omata, and S. Otsuka-Yao-Matsuo, “Synthesis of ternary CuInS2 nanocrystals; phase determination by complex ligand species,” Chemistry of Materials, vol. 21, no. 13, pp. 2607–2613, 2009. View at Publisher · View at Google Scholar · View at Scopus
  15. C. Steinhagen, V. A. Akhavan, B. W. Goodfellow et al., “Solution-liquid-solid synthesis of CuInSe2 nanowires and their implementation in photovoltaic devices,” ACS Applied Materials and Interfaces, vol. 3, no. 5, pp. 1781–1785, 2011. View at Publisher · View at Google Scholar · View at Scopus
  16. U. Rau and H. W. Schock, Clean Electricity from Photovolatics, vol. 1, Imperial College Press, London, UK, 2001.
  17. C. Sun, J. S. Gardner, G. Long et al., “Controlled stoichiometry for quaternary CuInxGa1-xS2 chalcopyrite nanoparticles from single-source precursors via microwave irradiation,” Chemistry of Materials, vol. 22, no. 9, pp. 2699–2701, 2010. View at Publisher · View at Google Scholar · View at Scopus
  18. C. Sun, R. D. Westover, G. Long et al., “A large-scale synthesis and characterization of quaternary CuInxGa1-xS2 chalcopyrite nanoparticles via microwave batch reactions,” International Journal of Chemical Engineering, vol. 2011, Article ID 545234, 8 pages, 2011. View at Publisher · View at Google Scholar · View at Scopus
  19. K. R. Margulieux, C. Sun, L. N. Zakharov, A. W. Holland, and J. J. Pak, “Stepwise introduction of thiolates in copper-indium binuclear complexes,” Inorganic Chemistry, vol. 49, no. 9, pp. 3959–3961, 2010. View at Publisher · View at Google Scholar · View at Scopus
  20. W. Hirpo, S. Dhingra, A. C. Sutorik, and M. G. Kanatzidis, “Synthesis of mixed copper-indium chalcogenolates. single-source precursors for the photovoltaic materials CuInQ2 (Q = S, Se),” Journal of the American Chemical Society, vol. 115, no. 4, pp. 1597–1599, 1993. View at Google Scholar · View at Scopus
  21. K. K. Banger, M. H.-C. Jin, J. D. Harris, P. E. Fanwick, and A. F. Hepp, “A new facile route for the preparation of single-source precursors for bulk, thin-film, and nanocrystallite I-III-VI semiconductors,” Inorganic Chemistry, vol. 42, no. 24, pp. 7713–7715, 2003. View at Publisher · View at Google Scholar · View at Scopus
  22. R. Brini, M. Kanzari, B. Rezig, and J. Werckmann, “Effect of annealing on properties of CuInS2 thin films,” The European Physical Journal Applied Physics, vol. 30, no. 3, pp. 153–158, 2005. View at Publisher · View at Google Scholar · View at Scopus