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Perovskite solar cells have attracted extensive attention because of their photoelectric characteristics. Since 2009, the photoelectric conversion rate of the solar cells has soared from 3.8% to 25.7%. Perovskite material has become a focus of extensive academic research due to its advantages of high carrier mobility, low exciton binding energy, wide absorption spectrum and high optical absorption coefficient. However, organic P-type semiconductor material is usually used as a hole transport layer in high efficiency perovskite solar cells, for example, Spiro-OMeTAD, PEDOT:PSS, and PTAA. Because Spiro-OMeTAD is difficult to purify, many hole transport materials containing triphenylamine like Spiro-OMeTAD have been synthesized, such as triphenylamine polymer PTAA. As the conjugate parts of these triphenylamine transport materials are not coplanar and the space is distorted, they cannot form ordered stacks by spin-coating method, so their charge properties are weak, and li-TFSI and tBP are often added to improve the hole transport, so as to achieve better device effects. Moreover, the PTAA has the problem of infiltration, and it is difficult to form a completely covered perovskite film on it, which seriously affects the quality and surface morphology of perovskite film. The PEDOT:PSS itself has an acidic and corrosive electrode, and is easy to absorb moisture, which will affect the stability of the solar cell. The performance of organic material will deteriorate seriously under environmental factors such as humidity, temperature and UV irradiation, which will accelerate the aging of perovskite solar cells and become one of the main obstacles to their practical applications. In this work, the inorganic cuprous thiocyanate (CuSCN) is used as a hole transport material, the CuSCN is a rich and stable P-type semiconductor material, which has the characteristics of abundance, low cost, high carrier mobility, appropriate energy level, low defect density, good thermal stability, and excellent light transmittance. The CuSCN is one of the few known compounds with both high optical transparency (its wide band gap is 3.7–3.9 eV) and significant P-type electrical conductivity. Most importantly, CuSCN is inexpensive and can be prepared by solution method at room temperature. And its hole transport properties are improved by lithium doping. On this basis, the surface of CuSCN is modified with PTAA to avoid the interaction between CuSCN and lead iodide (PbI2), and the large-grained and dense perovskite films are prepared. Finally, the performance of perovskite solar cells is effectively improved. This work provides a reference for the preparation of the stable and efficient perovskite solar cells.
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Keywords:
- perovskite solar cells /
- hole transport layer /
- cuprous thiocyanate /
- Li-doping
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图 1 不掺杂和CuSCN中掺杂不同体积比LiSCN所得薄膜的(a) UV-Vis-NIR透过光谱; (b) 根据UV-Vis光谱得到的Tauc曲线; (c) Urbach能计算结果
Figure 1. (a) UV-Vis-NIR transmission spectra of undoped and LiSCN doped CuSCN films with different volume ratios; (b) Tauc curves based on UV-Vis spectra; (c) calculated Urbach energy.
图 2 掺锂前后CuSCN TFT器件Vg-Id转移曲线图以及基于CuSCN的典型底部栅极、顶部接触TFT结构示意图( Vds是漏极-源极电压, L是TFT器件的长度, W是TFT器件的宽度)
Figure 2. Vg-Id transfer curves of TFT devices of CuSCN film before and after lithium doping and schematic diagram of typical bottom-gate and top-contact TFT based on CuSCN
图 3 不掺杂和CuSCN中掺杂不同体积比LiSCN所得薄膜上的钙钛矿薄膜 (a)稳态PL光谱; (b) TRPL光谱
Figure 3. (a) Steady state PL spectra and (b) TRPL spectra of perovskite films on CuSCN with different LiSCN doping ratio.
图 4 (a)无修饰和(b) PTAA修饰后CuSCN薄膜上的钙钛矿薄膜表面SEM图; (c)无修饰和PTAA修饰后CuSCN薄膜上的钙钛矿薄膜XRD图
Figure 4. (a), (b) SEM images of perovskite film surface on CuSCN film (a) without modification and (b) with PTAA modification; (c) XRD patterns of perovskite films on CuSCN films without modification and after PTAA modification.
图 5 引入了PTAA表面修饰层的器件的(a)结构图和(b)能带结构图
Figure 5. (a) Structure diagram and (b) band structure diagram of the device with PTAA modification.
图 6 典型器件的(a)正反扫J-V曲线(Jsc为短路电流密度, Voc为开路电压, FF为填充因子, PCE为光电转换效率)、(b) EQE光谱图以及积分电流曲线
Figure 6. Typical (a) J-V curves, (b) corresponding EQE spectrum and integrated current of solar cells.
图 7 无修饰和有PTAA修饰层的器件性能 (a)暗态J-V曲线; (b)基于ITO/CuSCN/Perovskite/Spiro-OMeTAD /Au的单空穴结构SCLC曲线(VTFL为陷阱填充极限电压); (c) Mott-Schottky曲线
Figure 7. Typical (a) dark state J-V curves, (b) SCLC curves, and (c) Mott-Schottky curves of device with and without PTAA modification.
表 1 掺锂前后CuSCN薄膜的μFE和Vth (Vd是漏电压)
Table 1. μFE and Vth of CuSCN films doped with or without Li.
Vd/V μFE/(cm2·(V·s)–1) Vth/V Control +1 0.031 –4.93 0.1%LiSCN+CuSCN +1 0.88 –1.72 0.5%LiSCN+CuSCN +1 1.13 4.35 1%LiSCN+CuSCN +1 2.28 –0.71 
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表 2 不掺杂和CuSCN中掺杂不同体积比LiSCN所得薄膜上的钙钛矿薄膜的TRPL拟合结果
Table 2. TRPL fitting results of perovskite films fabricated on CuSCN with different LiSCN doping ratio.
τ1/ns
A1/(A1+A2)/%
τ2/ns
A2/(A1+A2)/%
τave/nsControl 20.02 0.80 295.88 99.20 293.67 0.1%LiSCN+CuSCN 16.44 1.58 179.74 98.42 177.16 0.5%LiSCN+CuSCN 21.98 2.29 159.29 97.71 156.15 1%LiSCN+CuSCN 19.21 2.29 170.87 97.71 167.51
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[1] Kojima A, Teshima K, Shirai Y, Miyasaka T 2009 J. Am. Chem. Soc. 131 6050
Google Scholar
[2] Stranks S D, Eperon G E, Grancini G, Menelaou C, Alcocer M J P, Leijtens T, Herz L M, Petrozza A, Snaith H J 2013 Science 342 341
Google Scholar
[3] Zhang J, Zhang T, Jiang L, Bach U, Cheng Y B 2018 ACS Energy Lett. 3 1677
Google Scholar
[4] Petrus M L, Bein T, Dingemans T J, Docampo P 2015 J. Mater. Chem. A. 3 12159
Google Scholar
[5] Kim J Y, Jung J H, Lee D E, Joo J 2002 Synth. Met. 126 311
Google Scholar
[6] Li W, Liu C, Li Y, Kong W, Wang X, Chen H, Xu B, Cheng C 2018 Sol. RRL. 2 1800173
Google Scholar
[7] Jaffe J E, Kaspar T C, Droubay T C, Varga T, Bowden M E, Exarhos G J 2010 J. Phys. Chem. C 114 9111
Google Scholar
[8] Arora N, Dar M I, Hinderhofer A, Pellet N, Schreiber F, Zakeeruddin S M, Grätzel M 2017 Science 358 768
Google Scholar
[9] Ren X, Wang Z, Sha W E I, Choy W C H 2017 ACS Photonics 4 934
Google Scholar
[10] 周玚, 任信钢, 闫业强, 任昊, 杜红梅, 蔡雪原, 黄志祥 2022 71 208802
Google Scholar
Zhou Y, Ren X G, Yan Y Q, Ren H, Du H M, Cai X Y, Huang Z X 2022 Acta Phys. Sin. 71 208802
Google Scholar
[11] Zaumseil J, Sirringhaus H 2007 Chem. Rev. 107 1296
Google Scholar
[12] Zhang C, Chen P, Hu W 2016 Small 12 1252
Google Scholar
[13] Guo N, Li J, Yang S, Zhang J, Ni J, Cai H 2021 Nanotechnology 32 395704
Google Scholar
[14] Zhou H, Chen Q, Li G, Luo S, Song T B, Duan H S, Hong Z, You J, Liu Y, Yang Y 2014 Science 345 542
Google Scholar
[15] Yang J, Liu C, Cai C, Hu X, Huang Z, Duan X, Meng X, Yuan Z, Tan L, Chen Y 2019 Adv. Energy Mater. 9 1900198
Google Scholar
[16] Luo J, Xia J, Yang H, Malik H A, Han F, Shu H, Yao X, Wan Z, Jia C 2020 Nano Energy 70 104509
Google Scholar
[17] Son D Y, Kim S G, Seo J Y, Lee S H, Shin H, Lee D, Park N G 2018 J. Am. Chem. Soc. 140 1358
Google Scholar
[18] Wang S, Sakurai T, Wen W, Qi Y 2018 Adv. Mater. Interfaces 5 1800260
Google Scholar
[19] Sherkar T S, Momblona C, Gil-Escrig L, Bolink H J, Koster L J A 2017 Adv. Energy Mater. 7 1602432
Google Scholar
[20] Saliba M, Matsui T, Domanski K, Seo J Y, Ummadisingu A, Zakeeruddin S M, Correa-Baena J P, Tress W R, Abate A, Hagfeldt A, Grätzel M 2016 Science 354 206
Google Scholar
[21] Hou F, Shi B, Li T, Xin C, Ding Y, Wei C, Wang G, Li Y, Zhao Y, Zhang X 2019 ACS Appl. Mater. Interfaces 11 25218
Google Scholar
[22] Wang P, Li R, Chen B, Hou F, Zhang J, Zhao Y, Zhang X 2020 Adv. Mater. 32 1905766
Google Scholar
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