Table of Contents Author Guidelines Submit a Manuscript
Advances in Materials Science and Engineering
Volume 2016, Article ID 4126163, 12 pages
http://dx.doi.org/10.1155/2016/4126163
Review Article

Effects of Solution-Based Fabrication Conditions on Morphology of Lead Halide Perovskite Thin Film Solar Cells

California State University, Chico, 400 W. 1st Street, Chico, CA 95929-0210, USA

Received 9 April 2016; Revised 5 June 2016; Accepted 19 June 2016

Academic Editor: Rafiq Ahmad

Copyright © 2016 Jeremy L. Barnett 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.

Abstract

We present a critical review of the effects of processing conditions on the morphology of methylammonium lead iodide (CH3NH3PbI3) perovskite solar cells. Though difficult to decouple from synthetic and film formation effects, a single morphological feature, specifically grain size, has been evidently linked to the photovoltaic performance of this class of solar cells. Herein, we discuss experimental aspects of optimizing the (a) temperature and time of annealing, (b) spin-coating parameters, and (c) solution temperature of methylammonium iodide (MAI) solution.

1. Introduction

Lead halide perovskite, specifically methylammonium lead iodide (CH3NH3PbI3), is of great recent interest. Endowed with a crystal structure ABX3, in which the A and B cations are coordinated with the X anions, this class of perovskites has exhibited eye-catching photovoltaic performance numbers and triggered much research interest. This is largely due to its ease of processability and low cost of materials. First reported in 2012 with a 10% efficiency, the lead halide perovskite-based absorbers have more than doubled in the last four years alone. In 2016, the highest reported efficiency was 22.1%, comparable with common inorganic photovoltaic materials, such as copper indium gallium selenide and cadmium telluride.

These rapid performance milestones have been reached due to the multiple fabrication methodologies developed for these devices. Despite the plethora of recent developments, there is still uncovered ground in exploring the intimate coupling of cell processing and their resultant morphology and performance metrics. The scope of this review will focus only on the most common perovskite (CH3NH3PbI3) model. Specifically, we will survey the effects of solution-based fabrication conditions on morphology in lead halide perovskite solar cells. Since solution processed methylammonium lead iodide perovskite thin film solar cells involving sequential deposition [13], solvent engineering [4], and one-step deposition have been discussed by others [58], we have omitted them in this review and exclusively focus on two-step deposition methods. For the most part, we have also omitted work focusing on nucleation and growth processes [9], mechanistic studies [5, 6, 10], and stability of perovskites against moisture, air, and light, since that has been discussed elsewhere [1117]. Importantly, this perspective does not focus on reporting devices yielding the highest efficiencies. Rather, we survey select ways of optimizing solution processing methods of perovskite solar cells. This is achieved by examining relevant literature examples, investigating the effects of (a) annealing temperature and time, (b) general spin-coating conditions, and (c) methylammonium iodide solution (MAI) temperature.

2. Annealing Temperature and Time

Since perovskite formation requires a certain amount of energy to drive the crystal growth [18, 19], thermal annealing is typically used for formation of perovskite films. Dualeh and colleagues found that changing the annealing temperature dramatically changed the film morphology, resulting in different photovoltaic performances [20].

The effect of annealing temperature on film morphology is clearly elucidated via scanning electron microscopy (SEM) in Figure 1. Samples thermally annealed at 60°C show large islands of precursor materials. At 80°C and 100°C, there is increased coverage of more defined crystals of perovskites. At 120°C, the film exhibits larger sheets of perovskite. Therefore, increasing the annealing temperature leads to the merging of nuclei into sheets of material.

Figure 1: SEM images of perovskite annealed at (a) 60°C, (b) 80°C, (c) 100°C, (d) 120°C, (e) 150°C, and (f) 175°C. Reproduced from [20] with permission from Wiley-VCH.

There is a correlation between annealing temperature and photovoltaic performance of the devices. Samples annealed at 100°C yielded the highest power conversion efficiency (PCE) of 11.66%, followed closely by devices annealed at 80°C yielding PCE of 10.64% (Table 1). These similar PCEs are attributed to the interconnected film morphology observed in Figures 1(b) and 1(c). As annealing temperature increases, the rate of crystallization increases. High temperatures result in rapid formation of large sheets from various nucleation sites. On the other hand, lower temperatures allow for slower growth and formation of smaller islands.

Table 1: Relevant photovoltaic performance data for devices annealed at various temperatures. Reproduced from [20] with permission from Wiley-VCH.

While others have investigated the effect of annealing temperature and time at select temperature and time points [25], Bi and colleagues have more thoroughly demonstrated that increasing the time the perovskite film is thermally annealed will allow more interdiffusion to occur resulting in a more homogeneous film [21]. In this work, both PbI2 and MAI were spin-coated, and subsequent devices were constructed with a structure of ITO/PEDOT:PSS (25 nm)/MAPbI3 (280 nm)/PCBM (20 nm)/C60 (20 nm)/BCP (8 nm)/aluminium (100 nm) [3, 21].

As depicted in Figure 2, absorption spans from 400 to 800 nm, meaning the perovskite is forming within each thin film. Even the film that was only dried at 70°C for 15 minutes, having not been thermally annealed after, shows an absorption edge at about 800 nm suggesting that some perovskite is forming during the drying process. The wavelength range from 600–800 nm shows a steady increase in absorption after 1 hour and then levels off. This steady increase in absorbance suggests that the perovskite film is not fully forming after the drying step or even after 15 minutes of annealing. In order to reach maximum absorption with a constant annealing temperature of 105°C, perovskite films must be annealed for at least 1 hour after drying. Annealing after 1 hour will virtually have no effect on the amount of light being absorbed by the perovskite film. These results emphasize the importance that thermal annealing has on the interdiffusion of solution processed perovskite films.

Figure 2: Overlaid absorption spectra of lead-based perovskite films. Films were dried at 75°C for 15 min and then annealed at 105°C with varying annealing times. Reproduced from [21] with permission from the Royal Society of Chemistry.

X-ray diffraction (XRD) measurements are each labeled in the overlaid spectra in Figure 3(a). After the first 15 minutes of thermal annealing, there are no visible PbI2 or MAI peaks. These peaks usually appear at 2θ = 15°. There are clear XRD peaks observed at 2θ = 16.69°, 23.50°, 33.40°, and 37.45°. These peaks are assigned to the specific crystal planes of the MAPbI3 structure. The longer the annealing time is, the sharper and stronger the XRD peaks become. This is indicated by a decreasing FWHM as a function of annealing time for the (110) peak as indicated in Figure 3(b). Further, the XRD peaks increase in intensity as a function annealing time as shown in Figure 3(c). This is consistent with the SEMs in Figures 4(a)4(g).

Figure 3: As the annealing time changes, there is an evident evolution of (a) X-ray diffraction (XRD) peaks, (b) FWHM of the (110) diffraction peak, and (c) XRD intensities. Reproduced from [21] with permission from the Royal Society of Chemistry.
Figure 4: Grain sizes of perovskite crystal increase as a function of annealing time as shown in (a–g) top-down SEM images and (h) grain size distribution plot of films. Reproduced from [21] with permission from the Royal Society of Chemistry.

Noticeably, after 3 hours of annealing, a small amount of PbI2 appears in Figure 3(a). This suggests decomposition of the perovskite films. For trihalide perovskites, long-term annealing after 3 hours tends to decompose the perovskite film. On the other hand, short-term annealing of 15 minutes of trihalide perovskites does not improve the crystallinity of the perovskite film in Figure 4(a). A recent study by Ma and colleagues concluded that the crystallinity is influenced by the volatility of DMF used in the formation of PbI2 solution [22]. Further, they suggest that using a mixed halide solution will add excess chloride ions that help improve crystallinity and morphology.

Figures 4(a) and 4(b) display the film morphology with only 5 μm of magnification in the films after thermal annealing, for 15 minutes and 3 hours, respectively. The bright spots from Figure 4(a), the film with 15 minutes of annealing, are lighter in color than those in Figure 4(b), the film with 3 hours of annealing. The bright spots from Figure 4(a) film display more charge buildup than those in Figure 4(b), possibly due to the lack of interdiffusion of perovskite from the shorter annealing time. Figures 4(c)4(g) show the changes in morphology with increasing thermal annealing time. Figure 4(h) shows grain size distribution curves generated from the images.

Although a one-step deposition method was used for the XRD and SEM data in Figures 5(a) and 5(b), changing annealing time using the one-step method yields similar peaks and trends that agree with the two-step deposition method. In Figure 5(a), the SEM image indicates that trihalide perovskite films annealed for 15 mins at 100°C have grain sizes that are approximately 100 nm thick. There is also some PbI2 that shows up in the XRD. This could possibly be unreacted PbI2 or the fact that the decomposition process is starting to occur. Figure 5(b) illustrates a mixed halide system incorporating both MAPbI3 and MAPbCl3. Long-term annealing dramatically decreases the MAPbCl3 peak. Excess chlorine ions may form the chloride-containing amorphous phase that melts at around 100°C in mixed halide perovskite layers. During prolonged annealing, the “melted amorphous phase with highly moveable ions may supply ions needed for the growth of MAPbI3 crystals” [22]. The evaporation of excess ions, methylammonium and chloride, promotes the transformation of MAPbCl3 from MAPbI3. Crystallinity does indeed improve as seen in the SEM image in Figure 5(b). There are fewer pinholes. The film is more smooth and homogenous with grain sizes that are about 500 nm thick. The chloride ions are reported to act as dopants and surface passivant which facilitates charge transfer at grain boundaries and electrical interfaces [35]. Mixed halide perovskite films have shown great promise with PCEs now surpassing 19% [36]. It is evident that increasing the annealing time in a mixed halide system will increase the grain sizes and film homogeneity which may lead to higher efficiencies.

Figure 5: (a) XRD data for tri-iodide perovskite annealed at 100°C with varying annealing times. Inset shows SEM of perovskite film annealed for 15 mins at 100°C. (b) XRD data for mixed halide perovskite annealed at 100°C with varying annealing times. SEM of perovskite film annealed for 150 mins at 100°C. Reproduced from [22] with permission from the Royal Society of Chemistry.

There is a gradual increase in grain size as the thermal annealing time increases. This is consistent with the decreasing FWHM in the XRD data. After 15 minutes of thermal annealing, the average perovskite grain size is 190 nm. Films that were thermally annealed for 2 and 3 hours displayed the largest averages in grain size of about 350 nm and 380 nm. The maximum grain size was observed between 600 and 700 nm at films thermally annealed after 1.5 hours. Figure 6 suggests that the grain size increases the most (ca. 35%) between 60 and 90 minutes with grain sizes ranging between 230 and 310 nm. However, after 1.5 hrs of annealing, the grain sizes seem to level off. This suggests that grain sizes increase the most within the first 1.5 hrs of thermal annealing. The grain size is larger than or equal to the thickness of the film. It is clear that, with increasing thermal annealing time, the grain sizes will increase as well, allowing more interdiffusion [32]. This contributes to minimized grain boundary in the charge collection direction of the annealed perovskite films which may influence cells to have higher efficiencies [32].

Figure 6: Plot of highest percentage of grain size present in each film with increasing thermal annealing time.

From the previous results, the length of time during which the perovskite film is thermally annealed has a critical role in the formation and morphology of the crystalline film. Generally, an increase in grain size of the perovskite crystals forms a more compact film, resulting in a decrease in the grain boundaries. These boundaries act as trap sites for charges, ultimately reducing the photovoltaic performance of the perovskite thin film. After 2 hours of thermal annealing, increased from 14.9 mA cm−2 to 19 mA cm−2, while FF increased from 69% to 78% as shown in Figure 7(a). The FF did not decrease with further annealing as shown in Figure 7(b). The nearly 27% increase in and 13% increase in FF lead to optimized device performance. A PCE of 13.4% was obtained when cells were annealed at 105°C for 2 hours after drying. When the cells are thermally annealed for a longer time after drying, the series resistance decreases but exhibits more shunt resistance than those thermally annealed for shorter amount of time. In Table 2, the shunt resistance increased from 1.51 × 104 Ω to 3.71 × 104 Ω as a function of annealing time. Generally, series resistance tends to decrease, as the annealing time of perovskite film increases. In contrast, the shunt resistance increases with increasing annealing time of the perovskite film. Interestingly, a sample that was annealed for 2 hours showed the most shunt resistance at 3.83 × 104 Ω. Again, it is possible to improve the film morphology and increase the grain sizes by doping the perovskite film using mixed halides. This could improve efficiencies to 19% or higher [36].

Table 2: Shunt and series resistances of devices with perovskite films annealed at 105  with varying annealing times. Reproduced from [21] with permission from the Royal Society of Chemistry.
Figure 7: Electrical performance of devices with MAPbI3 perovskite films annealed at 105°C for varying annealing times: (a) J-V curves of the devices under simulated AM 15 irradiation (100 mW cm−2); (b) variation of device parameters, , , FF, and PCE, with increased annealing times. Reproduced from [21] with permission from the Royal Society of Chemistry.

3. Spin-Coating Conditions

The morphology of perovskite layers is intimately correlated to the efficiency of the resulting lead halide perovskite solar cell device. To facilitate the formation of these layers, one must select specific processing techniques. Among the most popular deposition techniques for the application of the PbI2 layer and electron transporting layers is spin-coating. This technique involves the even application of thin layers of solution-based materials with adjustable spin time and rate. These parameters ultimately control the film thickness and uniformity. Unlike vapor deposition which requires a vacuum chamber for film deposition [23, 31, 37], spin-coating does not; it affords reproducible film uniformity while being more economically feasible.

Liu et al. compared the results of the spin-coating procedure of the PbI2 layer with that from vapor deposition [23]. After examining the films by SEM, conductivity, profilometry, UV-vis, XRD (unreacted PbI2), and power conversion efficiency, they showed that the samples made by spin-coating were nearly equivalent to those made by vapor deposition technique. In other words, even though vapor deposition differs from spin-coating by the former technique using a solvent-free deposition technique, this variation in technique resulted in similar properties in the films. For example, the XRD patterns of evaporated (E) and spin-coated (S) samples are nearly identical in Figure 8(a). Further, the top-down SEM images show roughly similar crystal grain sizes in Figures 8(b) and 8(c).

Figure 8: (a) XRD of evaporated and spin-coated layers. SEM of (b) spin-coated and (c) vapor deposited perovskite crystals. The XRD and SEM data suggest nearly identical crystal growth from spin-coating and vapor deposition of the PbI2 layer. Reproduced from [23] with permission from the Royal Society of Chemistry.

This suggests that either the two methods apply similar layers or the MAI application step plays a larger role in crystal growth. The - curves and incident photon-to-current efficiency (IPCE) spectra were also compared, showing nearly identical results in Figure 9.

Figure 9: (a) - curves and (b) IPCE spectra of vapor deposited (red line) versus spin-coated (black line) PbI2 layers in a perovskite cell. Reproduced from [23] with permission from the Royal Society of Chemistry.

Lastly, to compare crystallization and unreacted PbI2 in each application method, powder XRD was performed. Both processes failed to eliminate unreacted PbI2 and display only minor differences in crystal structure in Figure 10. This could be due to the short MAI dipping times, which were on the timescale of a few minutes. Previously, Liang and colleagues noted that 1 to 3 hours is required for complete conversion of the film to black and uniform CH3NH3PbI3 [38]. Notably, both methods form weakly crystalline PbI2 layer, as observed in the broad and weak peaks in the XRD. Wu et al. also previously showed that noncrystalline, amorphous PbI2 layers increased MAI interactions and improved perovskite formation [3].

Figure 10: PXRD of (a) bare ITO/ZnO, (b) PbI2, (c) calculated tetragonal CH3NH3PbI3, (d) 61 nm thick CH3NH3PbI3, (e) 200 nm CH3NH3PbI3, (f) 280 nm CH3NH3PbI3, (g) 400 nm CH3NH3PbI3, and (h) 560 nm CH3NH3PbI3. § refers to a peak that is indicative of crystalline PbI2 and is indicative of ITO glass substrate. As the perovskite layer thickness increases, the unreacted crystalline PbI2 also increases. Reproduced from [23] with permission from the Royal Society of Chemistry.

Currently, there is no comprehensive work on optimizing the spin-coating procedure, since optimization appears to be performed by individual labs. Though the time of spin-coating is often not specified, the speed and concentrations are noted. Authors report 1600–7000 rpm and 5–60 seconds of spin-coating [1, 23, 2630, 33, 34, 3841] with ca. 1 M concentrations of PbI2. These procedures result in PCEs of up to ca. 15%.

Table 3 compares various perovskite thin films, for which the lead iodide layer is applied with a spin coater. Efficiencies achieved are not directly attributed to the method of PbI2 application. Notably, quality perovskite photovoltaic cells can be produced using this facile application method. The spin-coating speeds and time of a coating do not tell the whole story, since many procedures are vastly different. For example, Shi and coworkers follow the application of PbI2 with a dipping method of MAI to form the perovskite crystal [29]. Eze et al. follow the PbI2 with a spin-coating of a MAI solution [28]. Interestingly, Yella et al. followed the PbI2 application by a 1-2-second dip of 2-propanol [40]. These protocols suggest that different procedures are often tailored for specific uses and layer thickness. Understanding the complexity and modularity of perovskite solar cells makes it difficult to specify which procedure is superior. However, it is beneficial to compare techniques and results from various groups, since spin-coating is one of the most adaptable thin film fabrication processes.

Table 3: Solution processed perovskite (CH3NH3PbI3) solar cells fabricated under various conditions.

4. Methylammonium Iodide (MAI) Solution Temperature

A critical factor affecting the grain size of the perovskite crystals is the temperature at which the MAI is deposited onto the PbI2 layer. Ahn and colleagues performed an experiment where the solution temperature of 0.050 MAI was varied [24]. Both the substrate and the MAI solution are preheated at different temperatures of −10°C, 20°C, and 50°C, while MAI concentration is fixed at 0.050 M. SEM imaging elucidated how the grain size is, in fact, dependent on the solution temperature of MAI (Figure 11). A theoretical model was also proposed to rationalize the temperature dependence of perovskite crystal formation.

Figure 11: (a) Top-down SEM for −10°C. (b) Cross-sectional SEM for −10°C. (c) Top-down SEM for 20°C. (d) Cross-sectional SEM for 20°C. (e) Top-down SEM for 50°C. (f) Cross-sectional SEM for 50°C. Reproduced from [24] with permission from the Royal Society of Chemistry.

As temperature of the MAI solution increases, the equilibrium concentration of the chemical reaction increases due to increased solubility of the MAI. At high temperatures, the critical free energy is higher than at low temperatures which determines the number of nuclei. This results in a decrease of the number of nuclei growing into MAPbI3 crystals leading to an increase of MAPbI3 grain size. In Figure 11, the MAPbI3 grain size changes with temperature, which is consistent with computational analysis. An important observation is seen within Figure 11(f) where defects in the crystal structure are observed leading to direct contact between the electron transport layer (ETL) and hole transport layer (HTL).

The effect of reaction temperature on photovoltaic performance is shown in Table 4, namely, on short-circuit current density (), open-circuit voltage (), fill factor (FF), and power conversion efficiency (PCE). As seen in Table 4, increases as the reaction temperature increases, which may be related to the increase in light absorption seen with the UV-vis in Figure 12. The perovskite layer color becomes darker with increasing grain size.

Table 4: Electrical data for −10, 20, and 50. Reproduced from [24] with permission from the Royal Society of Chemistry.
Figure 12: Absorbance spectra for −10°C, 20°C, and 50°C. Reproduced from [24] with permission from the Royal Society of Chemistry.

However, as temperature increased, and FF decreased. This is most likely caused by defects seen in the SEM images. The defects, which were caused by the increase of grain size with temperature, serve as recombination sites between the HTL and ETL. Both and FF parameters are dependent on the thickness of the perovskite layer as well as the mesoporous TiO2 layer. The absorbance data seen in Figure 12 shows that absorbance is highest when the MAI solution is at 20°C and lowest for −10°C. This decrease in absorbance arises from decreasing grain size. This suggests that the low absorbance observed for crystals grown at −10°C results from crystals with small grain sizes.

To elucidate the relationship between grain size and temperature of MAI solution, Ahn and colleagues utilized a series of mathematical equations. They observed that as the temperature of the MAI solution increased, the equilibrium concentration of the chemical reaction and thereby the free energy increased. Indeed, the experimental observations were consistent with mathematical findings.

5. Future Outlook and Conclusions

Understanding the solution processing conditions of perovskite-based solar cells remains at a nascent stage. Nonetheless, there are important challenges that must be addressed in order to fully realize their applicability. Recognizing that the crystal growth depends on the temperature, one way of boosting grain size would be to improve solution deposition temperatures, annealing times, and annealing temperatures, for example, continuing to elucidate the relationship between solution temperatures of MAI and crystal growth, since this is an underexplored research area. Current work involves replacing MAI with formamidinium iodide (FAI) to improve the range of absorption [34]. No current study exists to show the effects of solution temperature of the FAI precursor on the crystal grain size. The trade-offs between crystal growth, grain boundary size, film thickness, film absorption, and so on are sufficiently intertwined. Optimization of trade-offs might benefit greatly from computational and mathematical modeling. Indeed, this idea has proven valuable in the context of perovskite application challenges but has been inadequately explored [11, 24]. The ties between the diversity of fabrication approaches and resulting film morphology and optoelectronic and performance properties must be simultaneously understood and optimized before we can move further in this field of research.

Over the past five years, the emergence of perovskite solar cells as energy conversion devices has advanced exponentially. This is due to the plethora of experimental and theoretical studies that have been contributed to the field. However, despite their popularity, there is much room for improvement. Recent studies have suggested the importance of understanding grain size and enhanced photovoltaic performance. We suspect that simultaneous optimization of processing conditions, resulting morphology, and performance of these thin films will be possible through a collaborative effort between synthetic, computational, and materials chemists. Only then can efficient, solution-processable perovskite-based solar cells advance forward as a commercializable technology.

Competing Interests

The authors declare that there are no competing interests regarding the publication of this paper.

Authors’ Contributions

Jeremy L. Barnett, Vivien L. Cherrette, and Connor J. Hutcherson contributed equally to this work.

Acknowledgments

Monica C. So acknowledges financial support from the California State University, Chico.

References

  1. J. Burschka, N. Pellet, S.-J. Moon et al., “Sequential deposition as a route to high-performance perovskite-sensitized solar cells,” Nature, vol. 499, no. 7458, pp. 316–319, 2013. View at Publisher · View at Google Scholar · View at Scopus
  2. H.-B. Kim, H. Choi, J. Jeong et al., “Mixed solvents for the optimization of morphology in solution-processed, inverted-type perovskite/fullerene hybrid solar cells,” Nanoscale, vol. 6, no. 12, pp. 6679–6683, 2014. View at Publisher · View at Google Scholar · View at Scopus
  3. Y. Wu, A. Islam, X. Yang et al., “Retarding the crystallization of PbI2 for highly reproducible planar-structured perovskite solar cells via sequential deposition,” Energy and Environmental Science, vol. 7, no. 9, pp. 2934–2938, 2014. View at Publisher · View at Google Scholar · View at Scopus
  4. N. J. Jeon, J. H. Noh, Y. C. Kim, W. S. Yang, S. Ryu, and S. I. Seok, “Solvent engineering for high-performance inorganic—organic hybrid perovskite solar cells,” Nature Materials, vol. 13, no. 9, pp. 897–903, 2014. View at Publisher · View at Google Scholar · View at Scopus
  5. P. Gao, M. Grätzel, and M. K. Nazeeruddin, “Organohalide lead perovskites for photovoltaic applications,” Energy and Environmental Science, vol. 7, no. 8, pp. 2448–2463, 2014. View at Publisher · View at Google Scholar · View at Scopus
  6. H. S. Jung and N.-G. Park, “Perovskite solar cells: from materials to devices,” Small, vol. 11, no. 1, pp. 10–25, 2015. View at Publisher · View at Google Scholar · View at Scopus
  7. A. Sharenko and M. F. Toney, “Relationships between lead halide perovskite thin-film fabrication, morphology, and performance in solar cells,” Journal of the American Chemical Society, vol. 138, no. 2, pp. 463–470, 2016. View at Publisher · View at Google Scholar
  8. Y. Zhao and K. Zhu, “Solution chemistry engineering toward high-efficiency perovskite solar cells,” Journal of Physical Chemistry Letters, vol. 5, no. 23, pp. 4175–4186, 2014. View at Publisher · View at Google Scholar
  9. Y. Tidhar, E. Edri, H. Weissman et al., “Crystallization of methyl ammonium lead halide perovskites: implications for photovoltaic applications,” Journal of the American Chemical Society, vol. 136, no. 38, pp. 13249–13256, 2014. View at Publisher · View at Google Scholar · View at Scopus
  10. A. Marchioro, J. Teuscher, D. Friedrich et al., “Unravelling the mechanism of photoinduced charge transfer processes in lead iodide perovskite solar cells,” Nature Photonics, vol. 8, no. 3, pp. 250–255, 2014. View at Publisher · View at Google Scholar · View at Scopus
  11. J. Berry, T. Buonassisi, D. A. Egger et al., “Hybrid organic-inorganic perovskites (HOIPs): opportunities and challenges,” Advanced Materials, vol. 27, no. 35, pp. 5102–5112, 2015. View at Publisher · View at Google Scholar · View at Scopus
  12. G. E. Eperon, S. N. Habisreutinger, T. Leijtens et al., “The importance of moisture in hybrid lead halide perovskite thin film fabrication,” ACS Nano, vol. 9, no. 9, pp. 9380–9393, 2015. View at Publisher · View at Google Scholar · View at Scopus
  13. Y. Ma, S. Wang, L. Zheng et al., “Recent research developments of perovskite solar cells,” Chinese Journal of Chemistry, vol. 32, no. 10, pp. 957–963, 2014. View at Publisher · View at Google Scholar · View at Scopus
  14. J. S. Manser, M. I. Saidaminov, J. A. Christians, O. M. Bakr, and P. V. Kamat, “Making and breaking of lead halide perovskites,” Accounts of Chemical Research, vol. 49, no. 2, pp. 330–338, 2016. View at Publisher · View at Google Scholar · View at Scopus
  15. G. Niu, W. Li, F. Meng, L. Wang, H. Dong, and Y. Qiu, “Study on the stability of CH3NH3PbI3 films and the effect of post-modification by aluminum oxide in all-solid-state hybrid solar cells,” Journal of Materials Chemistry A, vol. 2, no. 3, pp. 705–710, 2014. View at Publisher · View at Google Scholar
  16. S. Pathak, A. Sepe, A. Sadhanala et al., “Atmospheric influence upon crystallization and electronic disorder and its impact on the photophysical properties of organic-inorganic perovskite solar cells,” ACS Nano, vol. 9, no. 3, pp. 2311–2320, 2015. View at Publisher · View at Google Scholar · View at Scopus
  17. S. Wozny, M. Yang, A. M. Nardes et al., “Controlled humidity study on the formation of higher efficiency formamidinium lead triiodide-based solar cells,” Chemistry of Materials, vol. 27, no. 13, pp. 4814–4820, 2015. View at Publisher · View at Google Scholar · View at Scopus
  18. D. Khatiwada, S. Venkatesan, N. Adhikari et al., “Efficient perovskite solar cells by temperature control in single and mixed halide precursor solutions and films,” Journal of Physical Chemistry C, vol. 119, no. 46, pp. 25747–25753, 2015. View at Publisher · View at Google Scholar · View at Scopus
  19. D. Wang, Z. Liu, Z. Zhou et al., “Reproducible one-step fabrication of compact MAPbI3-xClx thin films derived from mixed-lead-halide precursors,” Chemistry of Materials, vol. 26, no. 24, pp. 7145–7150, 2014. View at Publisher · View at Google Scholar
  20. A. Dualeh, N. Tétreault, T. Moehl, P. Gao, M. K. Nazeeruddin, and M. Grätzel, “Effect of annealing temperature on film morphology of organic-inorganic hybrid pervoskite solid-state solar cells,” Advanced Functional Materials, vol. 24, no. 21, pp. 3250–3258, 2014. View at Publisher · View at Google Scholar · View at Scopus
  21. C. Bi, Y. Shao, Y. Yuan et al., “Understanding the formation and evolution of interdiffusion grown organolead halide perovskite thin films by thermal annealing,” Journal of Materials Chemistry A, vol. 2, no. 43, pp. 18508–18514, 2014. View at Publisher · View at Google Scholar · View at Scopus
  22. T. Ma, M. Cagnoni, D. Tadaki, A. Hirano-Iwata, and M. Niwano, “Annealing-induced chemical and structural changes in tri-iodide and mixed-halide organometal perovskite layers,” Journal of Materials Chemistry A, vol. 3, no. 27, pp. 14195–14201, 2015. View at Publisher · View at Google Scholar · View at Scopus
  23. D. Liu, M. K. Gangishetty, and T. L. Kelly, “Effect of CH3NH3PbI3 thickness on device efficiency in planar heterojunction perovskite solar cells,” Journal of Materials Chemistry A, vol. 2, no. 46, pp. 19873–19881, 2014. View at Publisher · View at Google Scholar · View at Scopus
  24. N. Ahn, S. M. Kang, J.-W. Lee, M. Choi, and N.-G. Park, “Thermodynamic regulation of CH3NH3PbI3 crystal growth and its effect on photovoltaic performance of perovskite solar cells,” Journal of Materials Chemistry A, vol. 3, pp. 19901–19906, 2015. View at Publisher · View at Google Scholar
  25. M. Saliba, K. W. Tan, H. Sai et al., “Influence of thermal processing protocol upon the crystallization and photovoltaic performance of organic-inorganic lead trihalide perovskites,” Journal of Physical Chemistry C, vol. 118, no. 30, pp. 17171–17177, 2014. View at Publisher · View at Google Scholar · View at Scopus
  26. B. Jeong, S. M. Cho, S. H. Cho et al., “Humidity controlled crystallization of thin CH3NH3PbI3 films for high performance perovskite solar cell,” Physica Status Solidi (RRL)—Rapid Research Letters, vol. 10, no. 5, pp. 381–387, 2016. View at Publisher · View at Google Scholar
  27. P. Qin, S. Tanaka, S. Ito et al., “Inorganic hole conductor-based lead halide perovskite solar cells with 12.4% conversion efficiency,” Nature Communications, vol. 5, article 3834, 2014. View at Publisher · View at Google Scholar · View at Scopus
  28. V. O. Eze, B. Lei, and T. Mori, “Air-assisted flow and two-step spin-coating for highly efficient CH3NH3PbI3 perovskite solar cells,” Japanese Journal of Applied Physics, vol. 55, Article ID 02BF08, 2016. View at Publisher · View at Google Scholar
  29. J. Shi, Y. Luo, H. Wei et al., “Modified two-step deposition method for high-efficiency TiO2/CH3NH3PbI3 heterojunction solar cells,” ACS Applied Materials and Interfaces, vol. 6, no. 12, pp. 9711–9718, 2014. View at Publisher · View at Google Scholar · View at Scopus
  30. L. Zheng, Y. Ma, S. Chu et al., “Improved light absorption and charge transport for perovskite solar cells with rough interfaces by sequential deposition,” Nanoscale, vol. 6, no. 14, pp. 8171–8176, 2014. View at Publisher · View at Google Scholar · View at Scopus
  31. R. Sheng, A. Ho-Baillie, S. Huang et al., “Methylammonium lead bromide perovskite-based solar cells by vapor-assisted deposition,” Journal of Physical Chemistry C, vol. 119, no. 7, pp. 3545–3549, 2015. View at Publisher · View at Google Scholar · View at Scopus
  32. P. Cui, P. Fu, D. Wei et al., “Reduced surface defects of organometallic perovskite by thermal annealing for highly efficient perovskite solar cells,” RSC Advances, vol. 5, no. 92, pp. 75622–75629, 2015. View at Publisher · View at Google Scholar · View at Scopus
  33. D. Bi, A. M. El-Zohry, A. Hagfeldt, and G. Boschloo, “Improved morphology control using a modified two-step method for efficient perovskite solar cells,” ACS Applied Materials and Interfaces, vol. 6, no. 21, pp. 18751–18757, 2014. View at Publisher · View at Google Scholar · View at Scopus
  34. N. Pellet, P. Gao, G. Gregori et al., “Mixed-organic-cation perovskite photovoltaics for enhanced solar-light harvesting,” Angewandte Chemie—International Edition, vol. 53, no. 12, pp. 3151–3157, 2014. View at Publisher · View at Google Scholar · View at Scopus
  35. E. L. Unger, A. R. Bowring, C. J. Tassone et al., “Chloride in lead chloride-derived organo-metal halides for perovskite-absorber solar cells,” Chemistry of Materials, vol. 26, no. 24, pp. 7158–7165, 2014. View at Publisher · View at Google Scholar · View at Scopus
  36. H. Zhou, Q. Chen, G. Li et al., “Interface engineering of highly efficient perovskite solar cells,” Science, vol. 345, no. 6196, pp. 542–546, 2014. View at Publisher · View at Google Scholar · View at Scopus
  37. C. W. Chen, H. W. Kang, S. Y. Hsiao, P. F. Yang, K. M. Chiang, and H. W. Lin, “Efficient and uniform planar-type perovskite solar cells by simple sequential vacuum deposition,” Advanced Materials, vol. 26, no. 38, pp. 6647–6652, 2014. View at Publisher · View at Google Scholar
  38. K. Liang, D. B. Mitzi, and M. T. Prikas, “Synthesis and characterization of organic-inorganic perovskite thin films prepared using a versatile two-step dipping technique,” Chemistry of Materials, vol. 10, no. 1, pp. 403–411, 1998. View at Publisher · View at Google Scholar · View at Scopus
  39. J. Jiang, H. Jun Tao, S. Chen et al., “Efficiency enhancement of perovskite solar cells by fabricating as-prepared film before sequential spin-coating procedure,” Applied Surface Science, vol. 371, pp. 289–295, 2016. View at Publisher · View at Google Scholar
  40. A. Yella, L.-P. Heiniger, P. Gao, M. K. Nazeeruddin, and M. Grätzel, “Nanocrystalline rutile electron extraction layer enables low-temperature solution processed perovskite photovoltaics with 13.7% efficiency,” Nano Letters, vol. 14, no. 5, pp. 2591–2596, 2014. View at Publisher · View at Google Scholar · View at Scopus
  41. H.-S. Kim and N.-G. Park, “Parameters affecting I-V hysteresis of CH3NH3PbI3 perovskite solar cells: effects of perovskite crystal size and mesoporous TiO2 layer,” Journal of Physical Chemistry Letters, vol. 5, no. 17, pp. 2927–2934, 2014. View at Publisher · View at Google Scholar