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The organic-inorganic lead halide perovskite layer is a crucial factor for the high performance perovskite solar cell (PSC). We introduce CH3NH3Br in the precursor solution to prepare CH3NH3PbI3−xBrx hybrid perovskite, and an uniform perovskite layer with improved crystallinity and apparent grain contour is obtained, resulting in the significant improvement of photovoltaic performance of PSCs. The effects of CH3NH3Br on the perovskite morphology, crystallinity, absorption property, charge carrier dynamics and device characteristics are discussed, and the improvement of open circuit voltage of the device depended on Br doping is confirmed. Based on above, the device based on CH3NH3PbI2.86Br0.14 exhibits a champion power conversion efficiency (PCE) of 18.02%. This study represents an efficient method for high-performance perovskite solar cell by modulating CH3NH3PbI3−xBrx film.
Recent years, the solar cells based on organic-inorganic lead halide perovskite are considered as one of the most important developments in the field of solar energy due to their many advantages including low cost, facile preparation process, good stability and high power conversion efficiency (PCE)1,2,3,4, meanwhile, organic-inorganic lead halide perovskite unique feature such as broad and strong light absorption5, longer carrier lifetimes6, long charge carrier diffusion length7,8, and low exciton binding energy9. The perovskite solar cells (PSCs) are generally composed of transparent conducting oxide substrate (TCO), a n-type compact blocking layer, alkylammonium lead halide perovskite layer with or without scaffold layer, a p-type hole-transporting material (HTM) layer and a metal back electrode1,2. To date, the power conversion efficiency (PCE) of PSC has reached 20.8%10. More recently, the highest reported PCE of PSCs has reached 22.1%11.
The perovskite layer is a crucial factor for the high performance perovskite solar cells1,2,12,13 because perovskite as light harvester absorbs incident irradiation, its energy level dominates the photovoltage and photocurrent of the device, and its morphology affects the charge carrier transportation and the photoelectric properties of the solar cells. Perovskite layers mainly are prepared by sequential deposition14, solvent engineering15, vapour-assisted deposition16, and vacuum evaporation17. The most-studied perovskite layers are CH3NH3PbI318, CH3NH3PbI3−xClx19, CH3NH3PbBr313, etc. Noticeably, most high efficiency perovskite solar cells are based on CH3NH3PbI3 or CH3NH3PbI3−xClx perovskites20. Engineering halide perovskite through mixing halogen elements, such as CH3NH3PbI3−xClx and CH3NH3PbI3−xBrx, is a viable way to increase the perovskite stability, enhance carrier transport and turn band gap21. Recently, CH3NH3PbI3−xBrx based on perovskite solar cells have drawn much attention owing to their variable energy band gaps by adjusting the bromide-iodide ratio22. However, the power conversion efficiencies of the perovskite solar cells based on CH3NH3PbI3−xBrx are still lower21. As examples, Seok et al. reported the meso-structured perovskite solar cells with a PCE of 12.3% by utilizing the traditional one-step spin-coating method for CH3NH3PbI3−xBrx deposition22. Huang et al. achieved a PCE of 13.1% in CH3NH3PbI3−xBrx-based planar perovskite solar cells by using the two-step spin-coating method with the solvent annealing process23. Yuan et al. achieved a high fill factor exceeding 85% and a power conversion efficiency exceeding 13% in CH3NH3PbI3−xBrx based perovskite solar cells20.
Herein, we introduce CH3NH3Br in the precursor solution to prepare mixed methylammonium lead halide CH3NH3PbI3−xBrx, which results in the significant improvement of photovoltaic performance of PSCs. Firstly, uniform perovskite layer with improved crystallinity and apparent grain contour is obtained, less grain boundaries will facilitate the transmission of charge. Secondly, owing to the introduction of Br into CH3NH3PbI3, the energy band of perovskite is expanded and leads to a higher photovoltage (VOC) of the device. Thirdly, the modulation of Br is beneficial to the interfacial energy match between TiO2/perovskite/spiro-OMeTAD, the injection and extraction of charge carriers are improved and thus the photocurrent and fill factor of the device are enhanced. Under optimal conditions, the device with CH3NH3PbI2.86Br0.14 exhibits high reproducibility and a champion PCE of 18.02%.
CH3NH3PbI3−xBrx perovskites were prepared by controlling different iodide/bromide molar ratio in perovskite precursor solutions. The resultant mixed methylammonium lead halides are termed as CH3NH3PbI3, CH3NH3PbI2.91Br0.09, CH3NH3PbI2.89Br0.11, CH3NH3PbI2.86Br0.14, CH3NH3PbI2.8Br0.2, and CH3NH3PbI2Br, respectively. Figure 1 shows the XRD patterns of the CH3NH3PbI3−xBrx perovskite films. The two main peaks for all CH3NH3PbI3−xBrx films approximately located at 14.2° and 28.4° can be indexed to the (110) and (220) planes24,25, confirming the presence of the tetragonal perovskite phase in all of the prepared films. In order to examine the influence of Br amount on the crystallinity of the perovskite films, XRD patterns of CH3NH3PbI3−xBrx films at 13.5°~15.5° were measured and shown in Figure S1. The FWHM values of the strong diffraction peaks of the (110) face are calculated using JADE 6.026,27. The FWHM values of the CH3NH3PbI3−xBrx films are 0.17°, 0.18°, 0.16°, 0.14°, 0.13° and 0.12°, corresponding to the CH3NH3PbI3−xBrx, x=0, 0.09, 0.11, 0.14, 0.20, and 1, respectively. Small FWHM value means a sharper XRD pattern28,29. On the other hand, the characteristic (110) peak has shifted from CH3NH3PbI3 at 14.30° to CH3NH3PbI2Br at 14.09°, corresponding to a reduction in the lattice parameter from a=0.616nm to a=0.604nm with the increase in the Br content due to the difference in the ionic radius of Br− (1.96A) and I− (2.2A), which is consistent with the literatures22,30.
Top-view SEM images of as-prepared CH3NH3PbI3−xBrx hybrid perovskite films are shown in Fig. 2. It can be seen that the Br amount has a mild influence on the grain size of the hybrid perovskite. CH3NH3PbI2.86Br0.14 and CH3NH3PbI2.8Br0.2 present compact, pinhole-free perovskite films and enlarged average grain size, which will minimize the grain boundary energy and be beneficial to the charge transportation. For CH3NH3PbI2Br, there are some pinholes appearing in the film, marked by white circles. The pinholes will produce direct contacts of spiro-OMeTAD and electron transporting layer, leading to a shunting path which probably decreases fill factor and open-circuit voltage for the device with CH3NH3PbI2Br17.
Figure 3 shows the cross-view SEM images as-prepared CH3NH3PbI3−xBrx perovskite films. Surprisingly, there are some stark contrasts of the perovskite film in vertical direction. The cementite appears as small granular grain in the capping perovskite layer for CH3NH3PbI3 and CH3NH3PbI2.91Br0.09. With the increase of Br amount from CH3NH3PbI3 to CH3NH3PbI2Br, the big grain contour becomes gradually obvious. The grain size is commensurate with its thickness among CH3NH3PbI2.86Br0.14, CH3NH3PbI2.8Br0.2 and CH3NH3PbI2Br, most of the grain boundaries are perpendicular to the mesoporous layer to minimize the grain boundaries. As well known that the less grain boundaries will facilitate the transportation of charge29,31, thus it is expected that the fill factor of the corresponding device is improved by adjusting Br amount in CH3NH3PbI3−xBrx hybrid perovskite.
However, for CH3NH3PbI2Br, there are many voids at the bottom of the perovskite layer which may be attributed to the dewetting during anti-solvent washing and subsequent growth29,31,32. In the specific experimental operation of CH3NH3PbI2Br, the viscosity of the precursor solution may vary owing to different compositions in the precursor solution and the methylammonium halide was composed entirely of MABr. As the nucleation grows the material dewets at the interface between solution-phase and solid-phase, meaning that it is pulled away from the regions surrounding the crystals, resulting in the formation of large voids in the film. So a distinguishing crystallization behavior was obtained without MAI in the precursor solution. Many voids in the perovskite layer will result in inferior photovoltaic performance of PSCs.
Figure 4 shows the UV-visible absorption spectra of the CH3NH3PbI3−xBrx perovskite films with different iodide/bromide ratio. It can be seen that with the increase of Br amount from CH3NH3PbI3 to CH3NH3PbI2Br, the absorption edges of the hybrid perovskite films shift towards the shorter wavelength33. The bandgaps of crystallized perovskite films are 1.565, 1.579, 1.585, 1.591, 1.597, and 1.725eV, corresponding to the CH3NH3PbI3−xBrx, x=0, 0.09, 0.11, 0.14, 0.20, and 1, respectively, from the Taus plots34 shown in Figure S2. The corresponding absorption edge and band gap are listed in Table 1. The blue shift is found that: 782nm for CH3NH3PbI3 is shifted to 709nm for CH3NH3PbI2Br, consistent with the variety of the energy band levels of perovskite materials in Figure S3. According to the literatures34,35,36 and the energy level principle2,3,12,37,38, with the increase of Br amount in CH3NH3PbI3−xBrx the conduction band of the perovskite ascends and the valence band descends, resulting in the absorption edge shifted towards to shorter wavelength, which indicates the formation of wider energy band and a higher photovoltage (VOC) of the device.
Time resolved photoluminescence (TRPL) intensity decay measurements of CH3NH3PbI3−xBrx perovskite films offer a quantitative information on the dynamics of charge carrier recombination39, the samples were composed of FTO/CL-TiO2/mp-TiO2/perovskite, and corresponding results are presented in Fig. 5, of which the fitted time constants charge carrier lifetime (τ) are 52, 39, 35, 34, 33, and 15ns, corresponding to the CH3NH3PbI3−xBrx, x=0, 0.09, 0.11, 0.14, 0.20, and 1, respectively. The shorter τ value means that the charge more fast transfers from the perovskite to TiO2 layer40,41,42,43,44. The significantly reduced τ value with the increase of Br amount in the hybrid perovskite infers an efficient charge extraction process occurred at the perovskite/TiO2 interface. The CH3NH3PbI2Br yields the smallest τ value, meaning that the charge carriers extract very quickly, which may be attributed to the high conduction band of the perovskite. The high conduction band energy level is beneficial to the charge injection between the perovskite and the electron selective electrode, however, the device of CH3NH3PbI2Br presents the worst performance.
Nyquist plots of CH3NH3PbI3−xBrx films are shown in Fig. 6, and the corresponding equivalent circuit is inset. The radius of semi-circles corresponds to the interfacial charge transfers resistance45,46. It can be seen that with the increase of X (Br amount), the radii first decrease, and then increase. When X=0.14, the radius reaches the minimum, indicating the smallest interfacial charge transfers resistance among all CH3NH3PbI3−xBrx films. Therefore, the device based on CH3NH3PbI2.86Br0.14 film possesses superior charge injection characteristics and low internal resistance, resulting in better photovoltaic performance than others.
J-V curves (reverse scan) of the perovskite solar cells based on CH3NH3PbI3−xBrx hybrid perovskite are shown in Fig. 7 and the corresponding photovoltaic parameters are listed in Table 1. For the device based on ancestral CH3NH3PbI3 film, a PCE of 15.60% is obtained with short-circuit current density (JSC) of 22.92mA·cm–2, open-circuit photovoltage (VOC) of 1.016V and fill factor (FF) of 0.67. For the devices based on CH3NH3PbI3−xBrx films (x=0~0.14), the performance continuously improve with the increase of Br amount. Best performance is achieved in the PSC based on CH3NH3PbI2.86Br0.14, yielding a JSC of 23.52mA·cm−2, VOC of 1.064V, and FF of 0.72, resulting in a PCE of 18.02%. Further increasing the amount of Br in CH3NH3PbI2.8Br0.2 do not improve device performance, resulting from a lower JSC of 22.95mA·cm−2. Furthermore, the performance of the device based on CH3NH3PbI2Br shows a dramatic downward.
The reason for the increase and then decrease of power conversion efficiency (PCE) of the PSCs with the increase of Br amount lies in VOC, JSC and FF. From the aspect of PV energy devices3,17,37,38, with the increase of Br amount, the conduction band of the perovskite ascends and the valence band descends, the energy difference (ΔE1) between TiO2 Femi level and the valence band of perovskite expends, the energy difference (ΔE2) between the conduction band of perovskite and TiO2 Femi level also expends. The expanded ΔE1 increases VOC, however appropriate ΔE2 produces small energy loss and large JSC and FF; and excess ΔE2 by excessive Br leads to an opposite result. From the aspect of morphology, owing to a large amount of voids in CH3NH3PbI2Br perovskite by dewetting, the charge extraction process is limited at the interface of perovskite/TiO2. Combined above factors, photovoltaic parameters of the PSCs based on CH3NH3PbI3−xBrx increase and then decrease of with the increase of Br amount.
Noticeably, owing to different preparation conditions, materials and devices structure, the optimized bromide/iodide ratio may be different. For example, Jeon et al. reported an optimal perovskite CH3NH3PbI3−xBrx (x=0.3~0.45)15, and He et al. obtained an efficiency of 12.1% in planar heterojunction device by using CH3NH3PbI2.4Br0.647.
Figure S4 and Table S1 show the J-V curves and the photovoltaic parameters of the devices based on CH3NH3PbI3−xBrx films (x=0, 0.09, 0.14, and 1) under both reverse and forward bias scans. It can be seen that there are still noticeable hysteresis effects and instabilities for all samples. However, the device based on the champion film CH3NH3PbI2.86Br0.14 shows the highest reverse PCE (18.02%) and forward PCE (14.62%).
Statistic results of the cell performance are provided in Fig. 8 as histogram charts. It can be found that the devices with CH3NH3PbI2.86Br0.14 shows better performance and the average PCE is 17.37%. Meanwhile, the histogram chart demonstrates the high reproducibility of the devices (Each team is calculated from a batch of 50 cells). The corresponding incident-photon-to-current conversion efficiency (IPCE) spectra of PSC devices are shown in Figure S5.
J-V curves of the devices based on CH3NH3PbI2.86Br0.14 with various dwell time from 30ms to 800ms are shown in Figure S6, it can be seen that there are minor fluctuations. Figure S7 shows the steady-state photocurrent and output PCE of the device based on CH3NH3PbI2.86Br0.14 at the maximum power points with a stabilized current density output of 20.10mA·cm−2 (at the voltage of 0.88V), yielding a PCE of 17.68%.
In summary, we introduce CH3NH3Br in perovskite precursor solution to prepare CH3NH3PbI3−xBrx, leading to the significant improvement of photovoltaic performance of perovskite solar cell. Firstly, uniform perovskite layer with improved crystallinity and apparent grain contour is obtained, and less grain boundaries will facilitate the transportation of charges. Secondly, owing to the introduction of Br, the energy band of perovskite is expanded, resulting in a higher photovoltage of the device. Thirdly, the appropriate regulation of energy level by Br is beneficial to interfacial energy match and the charge injection and extraction at between TiO2/perovskite/spiro-OMeTAD and enhances photocurrent, which is certified by time-resolved photoluminescence intensity decay measurements. Under optimal conditions, the device based on CH3NH3PbI2.86Br0.14 achieves a champion PCE of 18.02% with a stabilized output efficiency of 17.68% at the maximum power point.
All of the materials were purchased from the Sigma-Aldrich Corp., if not specified. The Spiro-OMeTAD was from Luminescence Technology Corp. CH3NH3I was synthesized according to literature48.
461mg PbI2 (99.9985%, Alpha Aesar) and 78mg DMSO were mixed in 702μL DMF solution at room temperature. Then, mixed methylammonium halides (MAX, X=I, Br) were added to the above solution, the mole ratio of PbI2: MAX: DMSO was controlled at 1:1:1. The molar ratio of MAI: MABr in MAX was controlled at: 1:0, 10:1, 8:1, 6:1, 4:1, 0:1, respectively. Lastly, the solutions were stirred at room temperature for 1h in order to form a completely dissolved perovskite precursor solution. The resultant perovskites were termed as CH3NH3PbI3, CH3NH3PbI2.91Br0.09, CH3NH3PbI2.89Br0.11, CH3NH3PbI2.86Br0.14, CH3NH3PbI2.8Br0.2, and CH3NH3PbI2Br, respectively.
Fluorine-doped tin oxide-coated (FTO) glass (Pilkington, TEC-8, 8Ω/sq) was cleaned by UV-ozone treatment for 15min, followed by cleaning with detergent and ethanol consecutively. The compact TiO2 blocking layers were deposited on FTO glass, which was prepared by spin-coating 0.15M titanium diisopropoxide bis(acetylacetonate) (75wt% in isopropanol, Aldrich) in 1-butanol (99.8%, Aldrich) solution, at 500rpm for 5s and 2000rpm for 30s and then dried at 125°C for 5min. A mesoporous TiO2 film was deposited on compact TiO2 layer by spin-coating TiO2 paste diluted in ethanol. TiO2 paste was prepared as described previously49,50,51. After drying at 100°C for 5min, the film was annealed at 450°C for 30min, providing a thickness of ca. 200nm. The mesoporous TiO2 film was immersed in 0.02M aqueous TiCl4 solution at 80°C for 20min. After washing with deionized water and alcohol, the film was heated at 500°C for 30min. 20μL precursor solution was dipped onto the mesoporous TiO2 layer and then spun at 4000rpm for 25sec. During spinning, 0.5mL of diethyl ether was slowly dripped on the rotating substrate within the first 7s. The film was finally heated to 60°C for about 2min and followed by 100°C for 10min.
A volume of 20μL of 2,2′,7,7′-tetrakis (N,N-di-p-methoxyphenylamine) −9,9-spirobifluorene (Spiro-OMeTAD) solution was spin-coated on the CH3NH3PbI3 perovskite layer at 4,000rpm for 30s. A Spiro-OMeTAD solution was prepared by dissolving 72.3mg of Spiro-OMeTAD in 1mL of chlorobenzene, to which 28.8μL of 4-tert-butyl pyridine and 17.5μL of lithium bis(trifluoromethanesulfonyl)imide (Li-TFSI) solution (520mg LI-TSFI in 1mL acetonitrile, Sigma-Aldrich, 99.8%) were added. All devices were stored in a desiccator (humidity<15%) in the dark for 12h. Finally, 80nm of gold was deposited under vacuum through a shadow mask.
The current density-voltage (J-V) curves were measured using a Keithley 2420 source-measure unit under AM1.5G illumination at 100mW·cm−2 provided by an Oriel Sol 3A solar simulator in ambient environment. The light intensity was adjusted using a NREL-calibrated Si solar cell equipped with KG-2 filter. The devices had an active area of 0.125cm2 without metal mask. The devices were measured by reverse (2.0 to −0.1V) and forward (−0.1 to 2.0V) voltage scanning at a scan step of about 21.2mV (100 data points in total). The pre-sweep delay time was 40ms, the dwell time at each voltage step was 30ms. Surface morphologies were characterized by field-emission scanning electron microscopy (SEM, Hitachi S-8000, Japan). The crystalline structures were examined using X-ray diffraction (XRD, Bruker AXS, D8 Advance). Impedance spectra (IS) for the solar cell were measured on a ZAHNER IM6e electrochemical workstation under 1 sun AM 1.5 illumination, by applying a 0V DC bias and a 5mV voltage perturbation in the frequency range from 0.1 to 106Hz. The impedance spectra were analyzed with Zview software. IPCE curves were measured as a function of wavelength from 300nm to 800nm using the Newport IPCE system (Newport, USA). The time-resolved photoluminescence spectrum was acquired using the time-correlated single-photon counting technique (Pico harp 300), and the excitation light pulse was provided using a picosecond diode laser at a wavelength of 760nm with a repetition frequency of 1MHz (PDL 800B).
How to cite this article: Tu, Y. et al. Modulated CH3NH3PbI3−xBrx film for efficient perovskite solar cells exceeding 18%. Sci. Rep. 7, 44603; doi: 10.1038/srep44603 (2017).
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The authors acknowledge the financial joint support by the National Natural Science Foundation of China (Nos 91422301, 51472094, 61474047, U1205112), and the Cultivation Program for Postgraduate in Scientific Research Innovation Ability of Huaqiao University (No. 1400102002).
The authors declare no competing financial interests.
Author Contributions J.W. conceived the project, J.W. and Y.T. designed the device and experiments, and Y.T. carried out most experiments. Y.T. wrote the first draft of the manuscript, and J.W. finished the submitted paper. All the authors Y.T., J.W., Z.L., X.H., J.D., J.J, P.G., J.L., M.H. and Y.H. discussed the results and approved publishing this paper.