Enhancing the light absorbance of polymer solar cells by introducing pulsed laser-deposited CuIn0.8Ga0.2Se2 nanoparticles
© Zhao et al.; licensee Springer. 2014
Received: 20 May 2014
Accepted: 7 June 2014
Published: 17 June 2014
Evenly separated crystalline CuIn0.8Ga0.2Se2 (CIGS) nanoparticles are deposited on ITO-glass substrate by pulsed laser deposition. Such CIGS layers are introduced between conjugated polymer layers and ITO-glass substrates for enhancing light absorbance of polymer solar cells. The P3HT:PCBM absorbance between 300 and 650 nm is enhanced obviously due to the introduction of CIGS nanoparticles. The current density-voltage curves of a P3HT:PCBM/CIGS solar cell demonstrate that the short-circuit current density is improved from 0.77 to 1.20 mA/cm2. The photoluminescence spectra show that the excitons in the polymer are obviously quenched, suggesting that the charge transfer between the P3HT:PCBM and CIGS occurred. The results reveal that the CIGS nanoparticles may exhibit the localized surface plasmon resonance effect just as metallic nanostructures.
61.46. + w; 61.41.e; 81.15.Fg; 81.07.b
KeywordsCuIn0.8Ga0.2Se2 nanoparticles P3HT:PCBM Pulsed laser deposition Absorption Polymer solar cells Photoluminescence
In recent years, polymer-fullerene-based bulk heterojunction (BHJ) solar cells aroused the interest of researchers and manufacturers due to their low cost, large areas, and flexibility [1–3]. However, compared with crystalline silicon cells, the efficiency of polymer-fullerene BHJ solar cells is still much lower. One of the main factors limiting their efficiency is the low light absorption and low charge carrier mobility of polymer absorbers. For example, the poly(3-hexylthiophene) (P3HT) mixed with phenyl-C61-butyric acid methyl ester (PCBM), a commonly used conjugated polymer absorber in polymer-fullerene BHJ solar cells, has quite a large bandgap of about 2.1 eV, determining that it can only absorb the incident light whose wavelength is shorter than 590 nm. Moreover, the carrier mobility of P3HT is only in magnitude of 10-3cm2V-1s-1, which will lead to severe carrier recombination in transport through the thick P3HT:PCBM active layer. So, the practical thickness of the P3HT:PCBM active layer is commonly limited to be about 200 nm, and almost half of incident light can not be absorbed by the active layer. In order to resolve these problems, various inorganic materials with shorter bandgaps or higher carrier mobility including CdS, CdSe, and CuInS2 were introduced into organic solar cells to fabricate hybrid solar cells to enhance their light absorption and carrier mobility [4–7]. For example, nanoparticles of CuInS2 have been embedded into conjugated polymer blends to fabricate hybrid solar cells . Compared with these inorganic materials, CuInSe2 has a lower energy gap (1.02 eV), which leads to a considerably high absorption coefficient (about 105 cm-1), even higher than that of CuInS2. If different element ratios of Ga are added into CuInSe2, the bandgap and energy level of the formed CuInxGa1- xSe2 (CIGS) can be adjusted to match better with those of ITO electrodes and organic materials to achieve higher open voltage . Furthermore, the CIGS has good conductivity, and its conductivity type depends on its stoichiometry, which can easily be varied in the synthesis processes according to the design of the solar cell. This is beneficial to fabricate the hybrid solar cells with different structures. Therefore, the CIGS is potential for use as inorganic absorbers in the hybrid solar cells.
So far, several deposition and post-treatment techniques, such as thermal co-evaporation, sputtering, electrodeposition, and selenization of prefabricated metallic layers, have been tried to achieve the requirements for CIGS syntheses [9–12]. The difficulties to control the stoichiometry of the CIGS thin films make these processes very complicated and much expensive. As one of the alternative techniques, pulsed laser deposition (PLD) is a convenient, economical, and effective method to deposit multi-component films because of its congruent ablation proceedings [13, 14]. In this article, a YAG:Nd laser was used in PLD to deposit CuIn0.8Ga0.2Se2 nanoparticles on ITO-glass substrates. The CIGS nanoparticles deposited at 400°C were introduced between the conjugated polymer layers and ITO electrodes in the photovoltaic structures of polymer solar cells to improve their light absorption and current density-voltage performance. The mechanism of the enhancement of the light absorption and photoelectric conversion of the photovoltaic structure was investigated.
Conventional polymer solar cells were fabricated in this following procedure: Cleaned ITO-glass substrates were spin-coated by highly conducting poly(3,4-ethylenedioxythiophene)/poly(styrene sulfonic acid) (PEDOT:PSS; Clevios 4083, Heraeus, Hanau, Germany) at 2,000 r/m for 40 s. After being annealed on a hot plate at 150°C for 10 min in order to remove moisture, the samples were spin-coated by a mixed solution of P3HT:PCBM with concentrations of 15 and 12 mg⋅ml-1 in dichlorobenzene at 2,000 r/m for 40 s. Then, the samples were annealed on a hot plate at 150°C for 20 min to remove dichlorobenzene. The whole process was completed in a nitrogen glove box. Finally, Al thin films with a thickness of 150 nm as the cathodes were deposited onto the above layers by magnetron sputtering method through a shadow mask, resulting in active device areas of 7 mm2. The completed photovoltaic structure of ITO/PEDOT:PSS/P3HT:PCBM/Al was annealed at 150°C for 30 min in the nitrogen glove box.
The surface and cross-sectional morphology of the CIGS layers and CIGS/P3HT:PCBM bilayer was characterized by scanning electron microscopy (SEM) (XL30FEG, Philips, Amsterdam, Netherlands). The composition of the CIGS nanoparticles was analyzed by energy dispersive spectroscopy (EDS) fitted on the SEM. The crystallinity of the CIGS layers was examined by X-ray diffraction (XRD) (D/MAX-IIA, Rigaku, Tokyo, Japan) using the Cu Kα radiation. The UV-vis absorption spectroscopy of the P3HT:PCBM blend monolayer and CIGS/P3HT:PCBM bilayer was detected by an ultraviolet-visible spectrophotometer (U-3000, Hitachi, Tokyo, Japan). The current density-voltage (J-V) characteristics of the unencapsulated samples were tested in air by using a Keithley 2400 SourceMeter (Cleveland, Ohio, USA) under air mass (AM) 1.5 global solar condition at 100 mW/cm2. The photoluminescence (PL) of the P3HT:PCBM blend monolayer and CIGS/P3HT:PCBM bilayer was measured at room temperature using a 325-nm He-Cd laser as the exciting light source. The PL spectra were detected by collecting the luminescence with a spectrometer (Spectra Pro 500i, Acton Research, Trenton, NJ, USA) and recorded by an intensified charge-coupled device (ICCD; iStar DH720, Andor Technology, Belfast, UK) installed on the exit port of the spectrometer.
Results and discussion
To investigate the effects of the CIGS nanoparticles on the light absorption and charge separation efficiency of the conjugated polymer active layers, we measured the UV-visible-infrared absorption and PL spectra of the P3HT:PCBM layers with and without the CIGS interlayers (prepared on ITO-glass substrates). Figure 4b displays the absorption spectra of CIGS/ITO, P3HT:PCBM/ITO, sum of CIGS and P3HT:PCBM, and P3HT:PCBM/CIGS/ITO. Obviously, the CIGS interlayer enhances the light absorption of the P3HT:PCBM active layer in the spectral range of 300 to 650 nm. More importantly, the absorption intensity of P3HT:PCBM/CIGS/ITO is much larger than that of the sum of CIGS/ITO and P3HT:PCBM/ITO. It should be noted that the thickness of the P3HT:PCBM monolayer is approximately equal to that of the CIGS/P3HT:PCBM bilayer (about 100 nm) according to the cross-sectional SEM image (see Figure 2c), i.e., the enhancement of light absorption is not due to the thickness change of the P3HT:PCBM layer. Moreover, the CIGS interlayer absorbs only very little incident light. Therefore, most of the increased absorption should come from the P3HT:PCBM close to the interfaces between the P3HT:PCBM and CIGS nanoparticles. The mechanism may be similar to the localized surface plasmon resonant (LSPR) effect [16–20]. It has been known that the excitation of the LSPR through the resonant interaction between the electromagnetic field of incident light and the surface charge of metallic nanostructures causes an electric field enhancement (that can be coupled to the photoactive absorption region) and increases the absorption of photoactive conjugate polymer or organic semiconductor [21–23]. The above results demonstrate that the semiconductor CIGS nanoparticles may also exhibit LSPR effect just as metallic nanostructures do. As demonstrated in Figure 4a, the incident light is trapped by the excitation of localized surface plasmons on the surface of CIGS nanoparticles embedded in P3HT, and the near field of the excited particles causes the creation of the electron-hole pairs in the P3HT. This is very important for the conjugated polymer layers of hybrid solar cells to absorb more incident light (through ITO-glass). If the introduced CIGS interlayer with a narrower bandgap is a continuous thin film rather than scattered nanoparticles, it may absorb too much incident light and decrease rather than increase the light absorption of the photoactive polymer layer behind it. Therefore, the light absorption enhancement induced by the CIGS nanoparticles could permit a considerable reduction in the physical thickness of the conjugated polymer layers in hybrid solar cells and yield some new options for hybrid solar cell design. The PL results in Figure 4c show that the excitons in the polymer are obviously quenched. It has been known that the charge transfer normally occurs with a very high efficiency if excitons are formed in a conducting polymer within approximately 20 nm of a CIGS/P3HT:PCBM interface [23, 24]. The above phenomenon suggests that polymer chains were successfully penetrated into the pores of the CIGS nanoparticles, and hole transfer from the polymer to CIGS occurred. The quenching efficiency of a hybrid system can be estimated by calculating the integrated area beneath each curve . The quenching efficiency of P3HT/CIGS in this experiment was calculated to be about 46%.
The CIGS nanoparticles with sizes of 20 to 70 nm and a distribution density of about 7 × 109 cm-2 were deposited on the ITO-glass substrates by PLD. Such CIGS layers were introduced between P3HT:PCBM photoactive layer and ITO-glass substrates to enhance the light absorption of the P3HT:PCBM layer. The UV-visible-infrared absorption and PL spectroscopy measurements of the P3HT:PCBM photoactive layers with and without the CIGS interlayers suggest that the polymer chains are coiled on the CIGS nanoparticles, which enhance the light absorption and improve the efficiency of the exciton separation. The J-V curves demonstrate that the short-circuit current density of the hybrid solar cells was improved compared with that of the conventional polymer solar cells. These results indicate that the CIGS interlayers composed of nanoparticles are potential to enhance the light absorption of conjugated polymers and improve the photovoltaic performance of polymer solar cells.
YZ, HL, XL, LG, and YL are graduate students major in fabrication of nanometer materials and optical devices. JS and ZY is an associate professor and MS-degree holder specializing in optics and optical devices. JW is a professor and PhD-degree holder specializing in optics and nanometer materials. NX is a professor and PhD-degree holder specializing in nanometer materials and optical devices, especially expert in nanoscaled optoelectronic devices.
localized surface plasmon resonant
pulsed laser deposition
scanning electron microscopy
This work is supported by the National Basic Research Program of China (973 Program, Grant No. 2012CB934303) and the National Natural Science Foundation of China.
- Yu G, Gao J, Hummelen JC, Wudl F, Heeger AJ: Polymer photovoltaic cells: enhanced efficiencies via a network of internal donor-acceptor heterojunctions. Science 1995, 270(5243):1789–1791. 10.1126/science.270.5243.1789View ArticleGoogle Scholar
- Thompson BC, Frechet JMJ: Polymer-fullerene composite solar cells. Chem IntEd 2008, 47(1):58–77.Google Scholar
- Brabec CJ, Gowrisanker S, Halls JJM, Laird D, Jia SJ, Wliiams SP: Polymer-fullerene bulk-heterojunction solar cells. Adv Mater 2010, 22(34):3839–3856. 10.1002/adma.200903697View ArticleGoogle Scholar
- Huynh WU, Dittmer JJ, Alivisatos AP: Hybrid nanorod-polymer solar cells. Science 2002, 295(5564):2425–2427. 10.1126/science.1069156View ArticleGoogle Scholar
- Chandrasekaran J, Nithyaprakash D, Ajjian KB, Maruthamuthu S, Manoh Aran D, Kumar S: Hybrid solar cell based on blending of organic and inorganic materials—an overview. Renew Sust Energ Rev 2011, 15(2):1228–1236. 10.1016/j.rser.2010.09.017View ArticleGoogle Scholar
- Bereznev S, Konovalov I, Opik A, Kois J, Meuikov E: Hybrid copper-indium disulfide/polypyrrole photovoltaic structures prepared by electrodeposition. Sol Energ Mat Sol Cell 2005, 87(1):197–206.View ArticleGoogle Scholar
- Arici E, Sariciftci NS, Meissner D: Hybrid solar cells based on nanoparticles of CuInS2in organic matrices. Adv Funct Mater 2003, 13(2):165–171. 10.1002/adfm.200390024View ArticleGoogle Scholar
- Scharber MC, Muhlbacher D, Koppe M, Denk P, Heeger AJ, Bra CJ: Design rules for donors in bulk-heterojunction solar cells—towards 10% energy-conversion efficiency. Adv Mater 2006, 18(6):789–794. 10.1002/adma.200501717View ArticleGoogle Scholar
- Contreras MA, Egaas B, Ramanathan K, Hiltner J, Swartzlander A, Hasoon F, Noufi R: Progress toward 20% efficiency in Cu(In, Ga)Se2 polycrystalline thin-film solar cells. Prog Photovolt Res Appl 1999, 7(4):311–316. 10.1002/(SICI)1099-159X(199907/08)7:4<311::AID-PIP274>3.0.CO;2-GView ArticleGoogle Scholar
- Song HK, Kim SG, Kim HJ, Kim SK, Kang KW, Lee JC, Yoon KH: Preparation of CuIn 1-x Ga x Se2thin films by sputtering and selenization process. Sol Energ Mat Sol Cell 2003, 75(1–2):145–253.View ArticleGoogle Scholar
- Kapur VK, Bansal A, Le P, Asensio OI: Non-vacuum processing of CuIn 1-x Ga x Se2solar cells on rigid and flexible substrates using nanoparticle precursor inks. Thin Solid Films 2003, 53: 431–432.Google Scholar
- Zhang L, He Q, Jiang WL, Liu FF, Jiang LC, Sun Y: Effects of substrate temperature on the structural and electrical properties of Cu(In, Ga)Se2 thin films. Sol Energ Mat Sol Cell 2009, 93(1):114–118. 10.1016/j.solmat.2008.09.002View ArticleGoogle Scholar
- Levoska J, Leppavuori S, Wang F, Kusmartseva O, Hill AE, Ahmed E, Tomlinson RD, Pilkington RD: Pulsed laser ablation deposition of CuInSe2and CuIn1-xGaxSe2thin films. Phys Scr 1994, T54: 244–249.View ArticleGoogle Scholar
- Pavlista M, Hrdlicka M, Nemec P, Prikryl J, Frumar M: Thickness distribution of thin amorphous chalcogenide films prepared by pulsed laser deposition. Appl Phys A 2008, 93(3):617–620. 10.1007/s00339-008-4687-8View ArticleGoogle Scholar
- Huang JS, Chou CY, Lin CF: Enhancing performance of organic–inorganic hybrid solar cells using a fullerene interlayer from all-solution processing. Sol Energ Mat Sol Cell 2010, 94(2):182–186. 10.1016/j.solmat.2009.08.019View ArticleGoogle Scholar
- Royer P, Goudonnet JP, Warmack RJ, Ferrell TL: Substrate effect on surface plasmon spectra in metal-island films. Phys Rev B 1987, 35(8):3753. 10.1103/PhysRevB.35.3753View ArticleGoogle Scholar
- Barnes WL, Dereux A, Ebbesen TW: Exploitation of localized surface plasmon resonance. Nature 2003, 16(19):424–824.Google Scholar
- Hagglund C, Zach M, Petersson G, Kasemo B: Electromagnetic coupling of light into a silicon solar cell by nanodisk plasmons. Appl Phys Lett 2008, 92(5):053110. 10.1063/1.2840676View ArticleGoogle Scholar
- Hagglund C, Kasemo B: Nanoparticle plasmonics for 2D-photovoltaics: mechanisms, optimization, and limits. Opt Express 2009, 17(14):11944–11957. 10.1364/OE.17.011944View ArticleGoogle Scholar
- Harry A, Albert P: Plasmonics for improved photovoltaic devices. Nat Mater 2010, 9(10):205–214.Google Scholar
- Pei JN, Tao JL, Zhou YH, Dong QF, Liu ZY, Li ZF, Chen FP, Zhang JB, Xu WQ, Tian WJ: Efficiency enhancement of polymer solar cells by incorporating a self-assembled layer of silver nanodisks. Sol Energ Mat Sol Cell 2011, 95(12):3281–3286. 10.1016/j.solmat.2011.07.007View ArticleGoogle Scholar
- Bellessa J, Bonnand C, Plenet JC, Mugnier J: Strong coupling between surface plasmons and excitons in an organic semiconductor. Phys Rev Lett 2004, 93(3):036404–036408.View ArticleGoogle Scholar
- Greenham NC, Peng X, Alivisatos AP: Charge separation and transport in conjugated-polymer/semiconductor-nanocrystal composites studied by photoluminescence quenching and photoconductivity. Phys Rev B 1996, 54(24):17628–17637. 10.1103/PhysRevB.54.17628View ArticleGoogle Scholar
- Hal PA, Christiaans MPT, Wienk MM, Kroon JM, Janssen RAJ: Photoinduced electron transfer from conjugated polymers to TiO2. J Phys Chem B 1999, 103(21):4352–4359. 10.1021/jp9901803View ArticleGoogle Scholar
- Coakley KM, Liu Y, McGehee MD, Frindell KM, Stucky GD: Infiltrating semiconducting polymers into self-assembled mesoporous titania films for photovoltaic applications. Adv Funct Mater 2003, 13(4):301–305. 10.1002/adfm.200304361View ArticleGoogle Scholar
This article is published under license to BioMed Central Ltd. This is an Open Access article distributed under the terms of the Creative Commons Attribution License (http://creativecommons.org/licenses/by/4.0), which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly credited.