Methylammonium Lead Tri-Iodide Perovskite Solar Cells with Varying Equimolar Concentrations of Perovskite Precursors

During recent years, power conversion efficiencies (PCEs) of organic-inorganic halide perovskite solar cells (PSCs) have shown remarkable progress. The emergence of various thin film deposition processes to produce perovskite films, notably using solution processing techniques, can be credited in part for this achievement. The engineering of chemical precursors using solution processing routes is a powerful approach for enabling low-cost and scalable solar fabrication processes. In the present study, we have conducted a systematic study to tune the equimolar precursor ratio of the organic halide (methylammonium iodide; MAI) and metal halide (lead iodide; PbI2) in a fixed solvent mixture of N,N-dimethylformamide (DMF):dimethylsulfoxide (DMSO). The surface morphology, optical characteristics, and crystallinity of the films produced with these four distinct solutions were investigated, and our analysis shows that the MAI:PbI2 (1.5:1.5) film is optimal under the current conditions. The PSCs fabricated from the (1.5:1.5) formulation were then integrated into the n-i-p solar cell architecture on fluorine-doped tin oxide (FTO) substrates, which exhibited a PCE of ~14.56%. Stability testing on this PSC device without encapsulation at 29 ◦C (ambient temperature) and 60% relative humidity (RH) under one-sun illumination while keeping the device at its maximum power point showed the device retained ~60% of initial PCE value after 10 h of continuous operation. Moreover, the recombination analysis between all four formulations showed that the bimolecular recombination and trap-assisted recombination appeared to be suppressed in the more optimal (1.5:1.5) PSC device when compared to the other formulations used in the n-i-p


Introduction
The past decade has witnessed increasing interest in novel materials such as graphene and its hybrids [1,2], transition metal dichalcogenides (TMDCs) [3], black phosphorus [4], and organic-inorganic metal halide perovskites as promising optoelectronic materials for solid-state photovoltaics [5], light-emitting diodes (LEDs) [6], lasers [7], photodetectors [8][9][10], and photocatalysts [11]. Perovskite materials exhibit many remarkable optoelectronic properties such as broad bandgap tunability [12,13], high absorption coefficients [5], ambipolar charge transport properties [14], long charge carrier diffusion lengths (>1 µm) [15], high charge carrier mobilities [16], low non-radiative recombination rates [17,18], and high emission color purity [19]. Aside from that, ionic conductivity in perovskites arises from ion/defect migration, which has revealed a fascinating feature toward switchable resistance depending on the history of the last applied bias. This ability to reliably regulate ion migration and hysteresis has aided in the development of memristors devices (memory + resistor) based on the unique structural properties provided by perovskites [20]. These remarkable properties make perovskites ideal candidates for their use as light-harvesting materials in solar cells and various other devices. The solvent engineering method is a variation of the one-step approach, in which all perovskite precursors are deposited in a single step, followed by the application of an antisolvent, which causes the rapid crystallization of the perovskite layer [34]. This method provides the ease of the one-step method and, at the same time, results in better film morphology, similar to that observed for the two-step method. The use of a suitable amount of DMSO (Lewis base) in combination with DMF can form the Lewis acid-base adduct with PbI2 (Lewis acid), which results in the formation of a dense perovskite layer via the MAI-PbI2-DMSO intermediate phase. The antisolvent treatment enables the elimination of the host solvent(s) and initiates crystallization of the perovskite film during this intermediate phase, which helps regulate crystal development and morphology of the film. However, the use of an excessive amount of DMSO may lead to pinholes in the perovskite film, and thus, a small volume of DMSO is usually preferred with DMF; here, we used DMF:DMSO (4:1) [33,35]. The rate at which the antisolvent is applied is crucial and one of the decisive steps to determine film quality; thus, an appropriate rate of antisolvent dropping should be optimized for different antisolvents [36]. The convenience and simplicity of solution-processed perovskite layers by spin coating, which can be conducted in practically any laboratory without the need of expensive and sophisticated vacuum apparatus, is one of the primary advantages of this method. Another important benefit is the ability to introduce additives to the perovskite precursor solution, which has proven to have a beneficial impact on the final perovskite structure [37]. Therefore, an organized study to optimize varying equimolar concentrations during the spin coating of perovskite precursors is highly beneficial in making MAPbI3 PSCs since these are often still used as a benchmark to compare with the growing family of other perovskite-based photoabsorbers for PSCs. Illustrated are the (a) one-step spin coating, (b) two-step spin coating, and (c) one-step spin coating via solvent engineering and antisolvent extraction methods. In our work, we have used the one-step coating and solvent engineering and antisolvent extraction approach to form our photoabsorber layers.
In the present report, we have conducted a systematic study in tuning the equimolar precursor ratio of the organic halide (MAI = 1 M, 1.2 M, 1.5 M, 1.6 M) and metal halide (lead iodide: PbI 2 = 1 M, 1.2 M, 1.5 M, 1.6 M) in a fixed solvent mixture of DMF:DMSO. Hereafter, the fabricated films and perovskite solar cells (PSCs) with these four different concentrations will be denoted as (1.0:1.0), (1.2:1.2), (1.5:1.5) and (1.6:1.6) in this study. These films were studied and discussed on the basis of their surface morphology, optical properties and crystallinity. Additionally, the n-i-p PSCs fabricated from all four formulations were analyzed for recombination losses and operational stability study, which we also discuss here.

Morphology Characterization
Field-emission scanning electron microscopy (FE-SEM) was performed using an FEI-Quanta environmental SEM. One-dimensional X-ray diffraction (1D-XRD) measurements were conducted using a Rigaku Ultima III X-ray diffractometer.

Optical Characterization
Ultraviolet-visible (UV-vis) optical absorption spectroscopy of the synthesized films was conducted using the Agilent CARY 5000 spectrophotometer. The steady-state photoluminescence (PL) spectra were measured using a LabRAM HR Evolution spectrometer from HORIBA Scientific, equipped with a~532 nm laser source for optical excitation.

Device Fabrication
For the PSC device fabrication, first, pre-etched fluorine-doped tin oxide (FTO) coated glass substrates were cleaned rigorously using soapy water, deionized water (DI), ethanol and isopropanol (IPA) for 20 min each under sonication. After cleaning, the substrates were N 2 blow-dried to remove the residual solvents from the substrates and then thermally treated in a convection oven at 70 • C for 30 min. Cleaned substrates were further treated in a UV-ozone plasma for 20 min before starting the thin film deposition of the solar cell stacking layers. For the fabrication of the n-i-p structure, the cleaned FTO substrates were spin coated with a 0.15 M solution of titanium diisopropoxide bis(acetylacetonate) in ethanol at 3000 rpm for 20 s to form a compact titanium dioxide (c-TiO 2 ) electron transport layer (ETL) and subsequently annealed at 510 • C for 30 min. For the perovskite absorber layer, a perovskite precursor solution was prepared with an equimolar precursor ratio of the organic halide (MAI = 1 M, 1.2 M, 1.5 M, 1.6 M) and the metal halide (PbI 2 = 1 M, 1.2 M, 1.5 M, 1.6 M) in a fixed solvent formulation of DMF:DMSO (4:1); all four solutions were stirred at 65 • C overnight. The perovskite films were then deposited by spin coating these 4 precursor solutions on top of the c-TiO 2 layer via a spin coating program comprising of 8 s at 1000 rpm, with a subsequent ramp to 5100 rpm for 15 s. An amount of 0.1 mL of toluene, used as the anti-solvent, was dripped dynamically onto the underlying spinning substrate, for the last 5 s of the second stage ramp to 5100 rpm. The stack was then thermally treated at 125 • C for 20 min. For the hole transport layer (HTL), the spiro-OMeTAD (86 mg mL −1 in chlorobenzene) was doped with three solutions, all used in conjunction, consisting of 34 µL of TBP, 20 µL of Li-TFSI and 11 µL FK209. For the latter two solutions, i.e., Li-TFSI, a mother solution of 500 mg/mL in acetonitrile was used, while the FK209 required a mother solution of 300 mg/mL in acetonitrile. This spiro-OMeTAD solution was spin coated onto the underlying perovskite layer at 4000 rpm for 20 s to form the HTL in our PSC. Finally, an~80 nm thick Au top electrode was deposited using e-beam evaporation at a pressure of 10 −5 Torr.

PSC Device Characterization
The electrical characteristics of our fabricated PSCs were measured under one-sun optical illumination, i.e., 100 mW cm −2 , using the Oriel LSH-7320 LED solar simulator connected to a source meter unit from Ossila (Model: X200). The light was calibrated with a standard mono-Si solar cell (PVM-396, PV Measurements Inc., Boulder, CO, USA) certified by the US National Renewable Energy Laboratory (NREL).

Results and Discussion
Various perovskite films with an equimolar ratio of MAI:PbI 2 , i.e., (1.0:1.0), (1.2:1.2), (1.5:1.5), and (1.6:1.6), were synthesized as described in the device fabrication section and characterized using SEM, XRD, UV-vis, and PL. First, the morphological characteristics of the perovskite films prepared on the glass substrates were examined via SEM, as shown in Figure 2a-d. The SEM image of (1:1) film formulation shows that the perovskite crystallization process did not reach completion, given the very small size of the grains buried in the midst of cracked islands comprised of a significant density of pinholes. Similarly, the (1.2:1.2) and (1.6:1.6) formulations showed improper perovskite crystallization, again with a high density of cracks and pinholes. However, the (1.5:1.5) film appears to be much better than the rest of the films due to a denser morphology with a far lower density of visible pinholes and cracks for this composition.
fied by the US National Renewable Energy Laboratory (NREL).

Results and Discussion
Various perovskite films with an equimolar ratio of MAI:PbI2, i.e., (1.0:1.0), (1.2:1.2), (1.5:1.5), and (1.6:1.6), were synthesized as described in the device fabrication section and characterized using SEM, XRD, UV-vis, and PL. First, the morphological characteristics of the perovskite films prepared on the glass substrates were examined via SEM, as shown in Figure 2a-d. The SEM image of (1:1) film formulation shows that the perovskite crystallization process did not reach completion, given the very small size of the grains buried in the midst of cracked islands comprised of a significant density of pinholes. Similarly, the (1.2:1.2) and (1.6:1.6) formulations showed improper perovskite crystallization, again with a high density of cracks and pinholes. However, the (1.5:1.5) film appears to be much better than the rest of the films due to a denser morphology with a far lower density of visible pinholes and cracks for this composition. Shown in Figure 2e are the XRD spectra of the fabricated absorber layers at these four compositions, and the results are in good agreement with prior reports [38]. The (1.5:1.5) Shown in Figure 2e are the XRD spectra of the fabricated absorber layers at these four compositions, and the results are in good agreement with prior reports [38]. The (1.5:1.5) film shows relatively intense peaks for the (110), (112), (121), (020), (220), and (222) planes with their intensity counts being higher than the other films, suggesting the better crystallinity of the (1.5:1.5) film, as compared to the rest of the samples; this in alignment with the SEM data taken for the (1.5:1.5) composition, where a compact morphology is evident (Figure 2c). While the presence of the PbI 2 impurity peak for the (1.0:1.0) and (1.2:1.2) formulations located at~12.5-13 • is not ideal, this peak could also arise from the onset of post-synthesis degradation upon exposure to ambient conditions [39], or possible instrumentation resolution errors in measuring minute microgram resolution of precursor masses. Additionally, the magnified image of the XRD spectra for the (1:1) formulation at 13.14 • is shown in the inset of Figure 2e, bottom panel. The crystallite size as it pertains to the (110) peak was calculated using the Scherrer relation, S = Kλ βcosθ , where S is the estimated crystallite grain size, λ = 0.15406 Å for the wavelength of the X-rays used in the diffractometer, β represents the full-width-half-maximum (FWHM) in radians, θ is the diffraction Bragg angle, K is the Scherrer constant, which was taken to bẽ 0.94, as characteristic of spherical crystals with cubic symmetry, which we assumed likely for our samples [40]. Based on the above analysis, the crystallite size for the films was calculated to be 43.  Table 1. Even though the variation between the sizes is very small based on this calculation, the data are consistent with the crystallite size being largest for the (1.5:1.5) film compared to the other films. The thickness profile of the films is shown in Figure 3, measured using atomic force microscopy (AFM). The nominal film thickness h for the (1.0:1.0), (1.2:1.2), (1.5:1.5), and (1.6:1.6) formulations was measured to be 287 ± 97 nm < 317 ± 72 nm < 337 ± 58 nm < 346 ± 66 nm, respectively. The uncertainty values associated with each thickness (formulation) represent the average roughness (R avg ) acquired from the AFM, and a slight trending toward increasing nominal thickness was observed as the molar ratio was increased, despite the wide variability in R avg , not uncommon for spin-coated perovskite films. The slight increase in the average thickness with increasing concentration may be linked to the associated increase in viscosity since the spin coating parameters remained fixed.  The UV-vis optical absorption profiles for all the fabricated films are shown in Figure  4a. For comparison, the absorption profiles of all the MAPbI3 perovskite films were in agreement with the prior reported studies [41]. Here, it can be seen that the (1.5:1.5) film showed optimal absorption characteristics amongst all the films, which is consistent with its compact morphology, as corroborated through the SEM imaging results in Figure 2c  The UV-vis optical absorption profiles for all the fabricated films are shown in Figure 4a. For comparison, the absorption profiles of all the MAPbI 3 perovskite films were in agreement with the prior reported studies [41]. Here, it can be seen that the (1.5:1.5) film showed optimal absorption characteristics amongst all the films, which is consistent with its compact morphology, as corroborated through the SEM imaging re-sults in Figure 2c. A validation of the slight increase in thickness with an increase in concentration is also evident in the absorption data, where the absorbance increased as the concentration increased, i.e., from the smallest concentration (1.0:1.0) to the highest concentrations, specifically (1.5:1.5) and (1.6:1.6). The absorbance of the (1.5:1.5) and (1.6:1.6) films was almost identical up until about 575 nm, and below 550 nm, the absorbance of the (1.5:1.5) film increased at these shorter wavelengths. This is likely due to the fact that the (1.5:1.5) film depicts a more compact morphology with fewer pinholes compared to all the other film formulations, which may contribute to its slight enhancement in absorbance when compared to the almost equally thick (1.6:1.6) film. The PL emission peak (Figure 4b), for all the fabricated perovskite samples, lies in the vicinity of~778 nm and aligns well with the prior literature for MAPbI 3 films [42]. The lesser PL counts or highest PL quenching for the (1.5:1.5) perovskite formulation on c-TiO 2 /FTO/glass substrates may be likely due to the more efficient charge extraction between the c-TiO 2 and perovskite layer, which further suggests that the (1.5:1.5) film is more suitable for the PSC devices. However, since PL quenching can also arise from non-radiative recombination, steady-state PL, when combined with time-resolved photoluminescence (TRPL), would provide a firmer validation of the efficiency of the charge carrier extraction process, which will be conducted in a future study.   Table 2. While there is scope to improve these parameters further, the PCE trend:   Table 2. While there is scope to improve these parameters further, the PCE trend: (1.5:1.5) > (1.6:1.6) > (1.2:1.2) > (1.0:1.0), lies in good agreement with the absorption and PL spectra.
The recombination losses for the fabricated PSCs were examined by recording the light intensity-dependent J-V Characteristics. Typically, the J SC of the devices follows a power-law relationship with the incident light intensity I such that, J SC ∝ I α , where α is extracted from the slope of the log-log J SC versus I plot, as shown in Figure 6a, and it represents the extent of bimolecular recombination [43,44]. Usually, α close to unity indicates the presence of weak bimolecular recombination. The α value for the PSCs were extracted as follows: α = 0.965 (1.5:1.5) > 0.950 (1.6:1.6) > 0.917 (1.2:1.2) > 0.910 (1.0:1.0). Thus, these data indicate the presence of minimal bimolecular recombination in the (1.5:1.5) PSC. Meanwhile, information about the trap-assisted recombination losses can be obtained from the dependence of the V OC and I, according to the following relation, where V OC ∝ nkT q ln(I). Here, n is a coefficient, k is the Boltzmann constant, T is the temperature in Kelvin, and q is the elementary charge. The value of the coefficient n usually ranges between 1 and 2, where an n~1 indicates the absence of trap-assisted recombination, while n > 1 suggests the presence of trap-assisted recombination [12,45]. From the fit in Figure 6b, the value of n in the devices was deduced to be: n = 1.57 (1.5:1.5) < 1.63 (1.6:1.6) < 1.78 (1.2:1.2) < 1.87 (1.0:1.0), which indicates that the (1.5:1.5) PSC has the least presence of trap-assisted recombination. Overall, both studies shown in Figure 6a,b suggest minimal bimolecular and trap-assisted recombination occurring in the (1.5:1.5) PSC, which also corroborates its higher PCE performance amongst all four formulations.  Table 2. While there is scope to improve these parameters further, the PCE trend:       Moreover, the continuous evolution of photovoltaic parameters for (1.5:1.5) PSC with time up to 10 h were monitored while keeping the device at its maximum power point, as shown by the data in Figure 7b. The relative humidity (RH) and ambient temperature during the experiment were noted to be~60% and~29 • C, respectively. It can be seen that the (1.5:1.5) PSC retained~90% of its initial V OC and FF after 10 h of continuous tracking, but the J SC and PCE decreased to~70% and~60%, respectively, of their initial values for the same duration. There might be a number of possible reasons for the J SC loss attributed to photo-oxidization, or degradation of the charge extraction layers, or their degraded interfaces with the perovskite reducing the charge extraction efficiency [46,47], which will be examined further in future work. 1 and 2, where an n~1 indicates the absence of trap-assisted recombination, while n > 1 suggests the presence of trap-assisted recombination [12,45]. From the fit in Figure 6b, the value of n in the devices was deduced to be: n = 1.57 (1.5:1.5) < 1.63 (1.6:1.6) < 1.78 (1.2:1.2) < 1.87 (1.0:1.0), which indicates that the (1.5:1.5) PSC has the least presence of trap-assisted recombination. Overall, both studies shown in Figure 6a,b suggest minimal bimolecular and trap-assisted recombination occurring in the (1.5:1.5) PSC, which also corroborates its higher PCE performance amongst all four formulations. Moreover, the continuous evolution of photovoltaic parameters for (1.5:1.5) PSC with time up to 10 h were monitored while keeping the device at its maximum power point, as shown by the data in Figure 7b. The relative humidity (RH) and ambient temperature during the experiment were noted to be ~60% and ~29 °C, respectively. It can be seen that the (1.5:1.5) PSC retained ~90% of its initial VOC and FF after 10 h of continuous tracking, but the JSC and PCE decreased to ~70% and ~60%, respectively, of their initial values for the same duration. There might be a number of possible reasons for the JSC loss attributed to photo-oxidization, or degradation of the charge extraction layers, or their degraded interfaces with the perovskite reducing the charge extraction efficiency [46,47], which will be examined further in future work.

Conclusions
In summary, perovskite films with various equimolar concentrations of MAI and PbI2 were synthesized and analyzed. The (1.0:1.0), (1.2:1.2), and (1.6:1.6) films did not appear to be optimal and exhibited pinholes and cracks within the photoabsorber, and thus these films were not suitable for the PV device fabrication of the solar cell stack. However, the (1.5:1.5) formulation exhibited a compact morphology which appeared more suitable as a photoabsorber in the PSCs. Accordingly, PSCs fabricated using the (1.5:1.5) films exhibited a PCE of ~14.56% for the n-i-p structure. Operational stability analysis was conducted, and the continuous evolution of photovoltaic parameters with time up to 10 h was monitored while keeping the device at its maximum power point, which revealed that the (1.5:1.5) PSC retained ~90% of its initial VOC and FF after 10 h of continuous tracking, but the JSC and PCE decreased to ~70% and ~60%, respectively, of their initial values during the same amount of time. These results provide a benchmark to further tune the materials synthesis and device fabrication efforts to form higher performance PSCs in the future.

Conclusions
In summary, perovskite films with various equimolar concentrations of MAI and PbI 2 were synthesized and analyzed. The (1.0:1.0), (1.2:1.2), and (1.6:1.6) films did not appear to be optimal and exhibited pinholes and cracks within the photoabsorber, and thus these films were not suitable for the PV device fabrication of the solar cell stack. However, the (1.5:1.5) formulation exhibited a compact morphology which appeared more suitable as a photoabsorber in the PSCs. Accordingly, PSCs fabricated using the (1.5:1.5) films exhibited a PCE of~14.56% for the n-i-p structure. Operational stability analysis was conducted, and the continuous evolution of photovoltaic parameters with time up to 10 h was monitored while keeping the device at its maximum power point, which revealed that the (1.5:1.5) PSC retained~90% of its initial V OC and FF after 10 h of continuous tracking, but the J SC and PCE decreased to~70% and~60%, respectively, of their initial values during the same amount of time. These results provide a benchmark to further tune the materials synthesis and device fabrication efforts to form higher performance PSCs in the future.

Data Availability Statement:
The data presented in this study are available on request from the corresponding author.