International Journal of Photoenergy

International Journal of Photoenergy / 2017 / Article

Review Article | Open Access

Volume 2017 |Article ID 6109092 | 10 pages | https://doi.org/10.1155/2017/6109092

Perovskite Thin Film Solar Cells Based on Inorganic Hole Conducting Materials

Academic Editor: Wilfried G.J.H.M. Van Sark
Received13 Oct 2016
Revised14 Feb 2017
Accepted23 Feb 2017
Published03 May 2017

Abstract

Organic-inorganic metal halide perovskites have recently shown great potential for application, due to their advantages of low-cost, excellent photoelectric properties and high power conversion efficiency. Perovskite-based thin film solar cells have achieved a power conversion efficiency (PCE) of up to 20%. Hole transport materials (HTMs) are one of the most important components of perovskite solar cells (PSCs), having functions of optimizing interface, adjusting the energy match, and helping to obtain higher PCE. Inorganic p-type semiconductors are alternative HTMs due to their chemical stability, higher mobility, high transparency in the visible region, and applicable valence band (VB) energy level. This review analyzed the advantages, disadvantages, and development prospects of several popular inorganic HTMs in PSCs.

1. Introduction

Perovskite solar cells (PSCs) based on organic-inorganic metal halide perovskites have recently attracted considerable attention as the power conversion efficiency (PCE) has increased dramatically from the initial 3.9% in 2009 to current 22.1% in a short span of several years [18]. Previous results demonstrated that PSCs may be the first in the history of photovoltaics (PV) combining high efficiency with low cost. The configurations of PSCs were evolved from dye-sensitized solar cells (DSSCs), and the key materials for the perovskite are compounds with the chemical formula ABX3 (), which have received extensive attention due to their favorable photovoltaic properties [9, 10]. Generally, the device structure of PSCs can be categorized into mesoporous structure (Figure 1(a)) and planar junction structure (Figure 1(b)) [11]. The main function of perovskite is absorbing light to generate and transmit electron-hole pairs under continuous illumination. Then, the electrons and holes pass through the perovskite and shift to electron-transporting layer (ETL) and hole transport layer (HTL), respectively, to generate current, as schematic presented in Figure 1(c).

While although a mass of efforts such as solvent additives, molecular dipoles, or interface modification has been devoted to optimize device efficiency, none of the present PSCs provides high PCE with long-term stability. Undoubtedly, a lack of confirmed stability may become the biggest barrier on the path of PSCs towards commercialization. HTL is one of the most important components of PSCs, having functions of optimizing interface, adjusting the energy-match, and helping obtain higher PCE, which has a great effect on device performance and stability [1214]. Poly(3,4-ethylenedioxythiophene)-polystyrenesulfonate (PEDOT:PSS) and 2,2′,7,7′-tetrakis (N,N-di-p-methoxyphenylamine)-9,9,-spirobifluorene (spiro-OMeTAD) have been widely employed as HTL in the field of PSCs. Although PSCs that applied PEDOT:PSS and spiro-OMeTAD as HTL have obtained high PCE, none of them can provide with long-term stability partly because of the problematic acidic and hygroscopic characteristics of the organic HTMs applied in PSCs [15, 16].

Recently, to improve the stability and reduce the cost of PSCs, various inorganic hole transport materials have been discovered and applied. In this review, PSCs employing different inorganic HTMs as hole transport layer (HTL) have been discussed and summarized. To date, a series of p-type inorganic metal compounds have been employed in PSCs, such as CuI [17], CuSCN [1820], NiO [2126], CuO [27], Cu2O [27, 28], MoO3 [2931], and VOx [32]. Compared to organic HTMs, inorganic p-type semiconductor materials have the advantages of high hole mobility, wide band gap, low cost, and solution-processed availability, which show promising prospects as hole-selective contacts in perovskite solar cells.

2. Inorganic HTMs for PSCs

There are some general requirements for inorganic HTMs used in PSCs, such as high transparency in the visible region, well chemical stability, higher mobility, and applicable valence band (VB) energy level. At present, inorganic HTMs such as CuI, CuSCN, NiO, CuO, Cu2O, MoO3, and VOx have already been used in PSCs and the solar cells employing inorganic p-type semiconductors as HTLs exhibited improvement in device performance and stability. Table 1 presents the band gap and deposition method of various HTMs reported in the literatures, as well as their photovoltaic parameters of top-performing PSCs based on these HTMs. In the following, we will analyze and discuss these frequently used inorganic HTMs, respectively.


HTMBand gap (eV)Deposition methodVoc (V)Jsc (mA/cm2)FF (%)PCE (%)Reference

NiO3.5ALD1.0421.877216.40[37]
Cu:NiOx > 3.5Solution-processed1.1219.177315.40[24]
Mg:Li:NiOx > 3.5Solution-processed1.0720.627518.40[36]
CuI3.1Solution-processed1.0421.066213.58[40]
CuSCN3.8Electrodeposition1.0021.907616.60[46]
CuO1.3Solution-processed1.0615.827212.16[52]
Cu2O2.1Solution-processed1.0716.527513.35[52]
MoO33.4Thermal decomposition1.0021.496914.87[53]
VOx2.42Solution-processed0.9022.297114.23[55]

2.1. NiO

NiO is a well-known p-type semiconductor widely used as a p-sensitization electrode for DSSCs and a hole-selective contact for organic bulk heterojunction solar cells [33, 34].

Initially, NiO was widely applied in DSSCs. In recent years, nickel oxide (NiO) as a promising HTM has been studied by several groups. In 2014, the first announced PCE of PSCs using nickel oxide as HTL was up to 7.8% [35]. Then, NiO nanocrystals (NCs) were obtained by a simple sol-gel process adopted as the hole transport layer in an inverted PSC, which observed a high PCE of 9.11% [25]. In 2015, copper- (Cu-) doped NiO (Cu:NiO) as HTL of planar heterojunction PSCs achieved a PCE of 15.4% [24]. At present, the highest recorded PCE of PSCs using Li, Mg-codoped NiO (Li0.05Mg0.15Ni0.8O) as HTL was 18.4% [36]. This study developed heavily p-doped (p+) NixMg1–xO to extract photogenerated hole from perovskite layer, and large size (>1 cm2) PSCs with an efficiency of up to 16.2% were successfully fabricated. The latest reported PCE of PSCs employing pure NiO as HTL is up to 16.4%, and the NiO film was gotten by the atomic layer deposition (ALD) method [37].

NiO become a potential candidate for HTL, as its p-type characteristics of high optical transmittance, wide band gap (Eg > 3.50 eV), chemical stability, and an applicable valence band match with common light photoactive layers [33, 38]. The synthetic methods of NiO can be categorized into solution-processed and sol-gel, and NiO films can be prepared by various methods, such as pulsed laser deposition, electrodeposition, spray pyrolysis, spin coating, sputtering, and ALD method [37]. A frequently used method for preparing NiO is solution-processed technique by adding monoethanolamine and nickel acetate tetrahydrate in methoxyethanol then stirring for 10 hours to form NiO precursor solutions and via spin coating to achieve NiO film. The NiO film obtained by this way was composed of NiO nanoparticles (NCs), and the whole film was crack-free and smooth, as schematic presented in SEM and AFM (Figures 2(a), 2(b), and 2(c)). The photoluminescence (PL) quenching of perovskite based on NiO showed favorable charge transfer compatibility, presented in Figure 3. Perovskite excitation is at around 760 nm. Finally, PSC with NiO prepared by the above method as HTL obtained a 7.6% device performance [21].

Another common approach to achieve NiO is a simple sol-gel process. NiO film was fabricated by spin coating the sol-gel solution. This kind of NiO nanocrystal film with a flat and smooth surface guarantees the formation of a continuous and close-knit HTLs of PSCs as schematic presented in Figures 4(a) and 4(b). Hole extraction and transport properties of this film interfaced with the perovskite film were higher than those of organic HTLs, such as PEDOT:PSS, and perovskite deposited on NiO NC films is with homogeneous phase. The PSCs with HTL of NiO NC film at a thickness of around 35 nm exhibited the best PCE of 9.11%, as showed in Figure 4(c) [25].

Recently, ALD method has been used to fabricate ultrathin pure un-doped NiO films. And PSCs employing this kind of NiO film as HTL achieved a high PCE of 16.4%. We can fabricate highly sequential and dense ultrathin films at nanometer size following the ALD method. The effective work function (WF) of ultrathin NiO apparently increased, which enormously promoted the hole extraction performance. In addition, ultrathin NiO films have a higher transparency which highly contribute to the photovoltaic devices. The freshly ultrathin pure undoped NiO films deposited as HTL of PSCs exhibited a high PCE of 16.4% with , , and [37].

A salient weakness with PSCs’ use of NiO as HTL is that it is hard for NiO to support an ultrathin perovskite film (<60 nm) [22, 23], which has still limited the development of PCE of PSCs using NiO as HTLs. Another shortage with PSCs employing NiO as HTL is that FF and Voc are lower than the common organic HTMs, in particular when the NiO was achieved by the solution-processed method. These parameters greatly affect the device performance [37].

Briefly speaking, an ideal p-NiO film for high PV performance should (1) have high transparency, (2) have favorable hole extraction and transport performance properties, (3) have applicable energy levels, and (4) have low cost and easy access [33].

2.2. CuI

Inorganic p-type semiconductor copper iodide (CuI) becomes one of the promising HTLs for PSCs, due to its admirable properties such as wide band gap, high conductivity, low cost, and solution processable. At the beginning, CuI as hole conductors was employed in DSSCs and quantum dot-sensitized solar cells. In recent years, several groups have used CuI as HTLs for PSCs, and the first application of CuI for PSCs has successfully achieved a potential PCE of 6.0% [17]. Then, the PCE of PSCs using CuI as HTL increased to 7.5% [39]. In 2015, the PCE of PSCs applying CuI as HTL in inverted planar heterojunction perovskite solar cells reach up to 13.8% [40]. At present, the highest announced PCE of PSCs using CuI as HTL is 16.8% [41].

Solution-processed method is the frequently used approach to acquire CuI. The CuI films were prepared by spin coating CuI precursor solution in inert gas. Compared to PEDOT:PSS, CuI films exhibit higher transmittance in visible light from 450 to 800 nm (Figure 5), which make it potential to be used as a HTL. In addition, high transparency can allow more photo flux reach perovskite active layer to generate intense photocurrent. However, the surface morphology of CuI films is rough when compared to PEDOT:PSS films, which may be because of the existence of large CuI grains [40].

At present, PSCs employing CuI as HTLs have achieved a relatively high PCE of 13.58% [40]. Above all, PSCs using CuI as the HTL exhibited improved air stability when compared to PSCs employing PEDOT:PSS as the HTL (Figure 6). In this respect, CuI is an excellent choice, because long-term stability of PSCs is of vital significance for practical applications [40].

Although PSCs using CuI as HTLs can replace conventional organic HTMs, the device open-circuit voltage (Voc) is relatively low mainly because of a high recombination rate as determined by impedance spectroscopy. There are still numerous challenges in the optimization of PSC-employed CuI as HTLs. The primary problems include (1) how to control the surface morphology of CuI, (2) how to achieve favorable contacts between CuI layer and perovskite layer, and (3) how to dissolve CuI and eliminate large CuI grains.

2.3. CuSCN

As mentioned above, copper thiocyanate (CuSCN) appears to be a good candidate of inorganic HTLs for its internal p-type characteristics of a wide band gap and high optical transparency [4244].

CuSCN was first applied in mesoporous PSCs by Ito et al. with a device structure of FTO/TiO2/TiO2/CH3NH3PbI3/CuSCN/Au and achieved a PCE of 4.85% in 2013 [18]. Soon after, planar PSCs using CuSCN as a HTL received a PCE of 6.4%. There were reported low PCEs of PSCs based on CuSCN mainly because of the poor quality of CH3NH3PbI3 active layer films on top of the CuSCN layers. Grätzel et al. enhanced the device PCE to 12.4% [45], via optimizing perovskite surface morphology by two times of iodide deposition. Then, the PCE of the CuSCN-based PSCs has already been improved to 16.6% [46, 47]. The latest announced PCE of PSCs using CuI as HTL has reached up to 18% [48]. In spite of the relatively low PCE compared to efficiency of PSCs based on organic HTMs, the low cost and air stability of CuSCN make it become a promising inorganic HTM.

The high PCE (16.6%) photovoltaic device used a one-step fast deposition method to fabricate high-quality perovskite films based on a rough CuSCN. CH3NH3PbI3 prepared by a one-step faster deposition method with lower surface roughness and smaller interface contact resistance was compared to the perovskite films prepared by a conventional two-step deposition process, as showed in Figure 7 [46, 49].

Although cells using CuSCN as HTL have achieved considerable device efficiency, the CuSCN layer was fabricated via electrodeposition, which needs to be carefully compounded from a precursor solution containing potassium thiocyanate (KSCN), copper sulfate (CuSO4), and ethylenediaminetetraacetic acid (EDTA). And the CuSCN films achieved by the above method are relatively rough and unshaped, which affect further improvements of PSCs [46].

2.4. Cu2O and CuO

CuO and Cu2O are well-known p-type semiconductors [27, 28, 50]. There is a simple low-temperature method to synthesize Cu2O and CuO films and employ them as HTL for PSCs. Traditional methods for preparing Cu2O film are thermal oxidation, sputtering, electrodeposition, and metal-organic chemical vapor deposition [51]. Cu2O film can be obtained via in situ conversion of CuI film in aqueous NaOH solution, and CuO film is fabricated by heating Cu2O film in the air, as showed in Figure 8 [52].

PSCs using Cu2O and CuO as HTMs show observably increased Voc, Jsc, and PCE. Recently, PSCs using Cu2O and CuO as HTLs exhibited PCE of 13.35% and 12.16%, respectively [52]. Additionally, NH4Cl was added into CH3NH3PbI3 precursor to improve crystallinity of perovskite in Li et al. study. The increased Voc mainly owns the VB of Cu2O and CuO well matching with VB of the perovskite and favorable crystallinity of perovskite on Cu2O and CuO. What is more, well crystallinity enhanced the charge carrier transport and increased Jsc.

Compared to the PSCs employing NiO or Cu:NiO as HTLs, Cu2O-based cells showed a superior property due to the higher mobility of Cu2O, less energy loss, and favorable perovskite surface morphology on Cu2O film [21].

2.5. MoO3

MoO3 is another potential HTM owing to the advantage of nontoxicity and air stability. However, PSCs with MoO3 as HTL exhibit a low PCE mainly because of the poor quality of perovskite films deposited on MoO3 [29, 31].

MoO3 is a good HTM, but the poor perovskite films deposited on top of it limit further improvement. In order to solve the difficult problem, one simple solution would be to use an MoO3/PEDOT:PSS composite film as the HTL in PSCs to take advantage of the ambient condition stability and favorable photovoltaic properties of MoO3 and at the same time guarantee the admirable surface morphology of perovskite film [53].

Li et al. used a MoO3/PEDOT:PSS bilayer structure as the HTL for PSCs. MoO3 was prepared by a thermal decomposition of ammonium heptamolybdate () solution at 80°C. The PSCs have a structure of ITO/MoO3/PEDOT:PSS/CH3NH3PbI3/C60/Bphen/Ag. The application of an MoO3 layer between ITO and PEDOT:PSS not only enhanced the hole extraction efficiency from perovskite to the ITO electrode but also avoided direct contact between rough MoO3 and CH3NH3PbI3. By this way, we can obtain a high-quality perovskite films deposited on top of PEDOT:PSS. These improvements contribute to the increase of stability and PCE of PSCs compared to the cells employing only PEDOT:PSS. Finally, the optimized PSCs exhibit a PCE of 14.87% [53]. What is more, the device stability increases when a MoO3 layer is inserted between ITO and PEDOT:PSS as showed in Figure 9 [53].

2.6. VOx

VOx has become a favorable p-type semiconductor material primarily due to its higher work function (WF) and stability, and it can be prepared by low-temperature solution-processed method [32, 54]. At the beginning, VOx was used as HTL in organic solar cells (OSCs). Recently, VOx occurred as HTL for PSCs and achieved a relatively high PCE of 14.23% [55].

In general, VOx films are fabricated by spin coating and annealed sol-gel precursor solution of VOx. And the measurements of the VOx layer exhibit high transmittance and well-quenching efficiency (Figure 10(a)). The value of x in VOx was calculated at about 2.428 via X-ray photoelectron spectroscopy (XPS). High WF (Figure 10(b)) of VOx not only extremely benefits cells containing high ionization potential donor materials but also reduces losses in Voc and series resistance (Rs) [55]. However, VOx is still faulty for it poor surface morphology result in harsh deposition of perovskite films, as showed in Figures 10(c) and 10(d) [24, 45].

3. Conclusion

Inorganic semiconductor materials can be employed as hole-selective materials for PSCs due to their advantages of high hole mobility, wide band gap, and low cost, and they could be obtained by solution-processed method, showing promising respect of inorganic HTMs. What is more, the application of inorganic HTMs can enormously increase the stability and reduce cost of cells, which is very significant for PSCs. However, the reported device performance of most of the inorganic hole conductor-based PSCs is still much lower than that of cells with organic HTMs, which may result in the poor quality of perovskite films on top of the inorganic HTL.

Conflicts of Interest

The authors declare that there is no conflict of interest regarding the publication of this paper.

Acknowledgments

The authors would like to thank the National Natural Science Foundation of China (21271064 and 61306016), China Postdoctoral Science Foundation (2015M582179), and The Program for Changjiang Scholars and Innovative Research Team in the University (PCS IRT1126) of Henan University.

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Copyright © 2017 Pan-Pan 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.


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