Low Pressure Vapor-assisted Solution Process for Tunable Band Gap Pinhole-free Methylammonium Lead Halide Perovskite Films

Carolin M. Sutter-Fella; Yanbo Li; Nicola Cefarin; Aya Buckley; Quynh Phuong Ngo; Ali Javey; Ian D. Sharp; Francesca M. Toma

doi:10.3791/55404

JoVE Journal > Chemistry

Quimica

Low Pressure Vapor-assisted Solution Process for Tunable Band Gap Pinhole-free Methylammonium Lead Halide Perovskite Films

Published: September 08, 2017

doi:

10.3791/55404

Carolin M. Sutter-Fella*^1,2,3, Yanbo Li*^1,4, Nicola Cefarin^1,5,6, Aya Buckley^1,7, Quynh Phuong Ngo^8,9, Ali Javey^2,3, Ian D. Sharp¹, Francesca M. Toma¹

¹Joint Center for Artificial Photosynthesis, Chemical Sciences Division,Lawrence Berkeley National Laboratory, ²Electrical Engineering and Computer Sciences,University of California, Berkeley, ³Materials Science Division,Lawrence Berkeley National Laboratory, ⁴Institute of Fundamental and Frontier Sciences,University of Electronic Science and Technology of China, ⁵Department of Physics, Graduate School of Nanotechnology,University of Trieste, ⁶TASC Laboratory,IOM-CNR – Istituto Officina dei Materiali, ⁷Department of Chemistry,University of California, Berkeley, ⁸Materials Science and Engineering,University of California, Berkeley, ⁹Joint Center for Artificial Photosynthesis,Lawrence Berkeley National Laboratory

Summary

Here, we present a protocol for the synthesis of CH₃NH₃I and CH₃NH₃Br precursors and the subsequent formation of pinhole-free, continuous CH₃NH₃PbI_3-xBr_x thin films for the application in high efficiency solar cells and other optoelectronic devices.

Abstract

Organo-lead halide perovskites have recently attracted great interest for potential applications in thin-film photovoltaics and optoelectronics. Herein, we present a protocol for the fabrication of this material via the low-pressure vapor assisted solution process (LP-VASP) method, which yields ~19% power conversion efficiency in planar heterojunction perovskite solar cells. First, we report the synthesis of methylammonium iodide (CH₃NH₃I) and methylammonium bromide (CH₃NH₃Br) from methylamine and the corresponding halide acid (HI or HBr). Then, we describe the fabrication of pinhole-free, continuous methylammonium-lead halide perovskite (CH₃NH₃PbX₃ with X = I, Br, Cl and their mixture) films with the LP-VASP. This process is based on two steps: i) spin-coating of a homogenous layer of lead halide precursor onto a substrate, and ii) conversion of this layer to CH₃NH₃PbI_3-xBr_x by exposing the substrate to vapors of a mixture of CH₃NH₃I and CH₃NH₃Br at reduced pressure and 120 °C. Through slow diffusion of the methylammonium halide vapor into the lead halide precursor, we achieve slow and controlled growth of a continuous, pinhole-free perovskite film. The LP-VASP allows synthetic access to the full halide composition space in CH₃NH₃PbI_3-xBr_x with 0 ≤ x ≤ 3. Depending on the composition of the vapor phase, the bandgap can be tuned between 1.6 eV ≤ E_g≤ 2.3 eV. In addition, by varying the composition of the halide precursor and of the vapor phase, we can also obtain CH₃NH₃PbI_3-xCl_x. Films obtained from the LP-VASP are reproducible, phase pure as confirmed by X-ray diffraction measurements, and show high photoluminescence quantum yield. The process does not require the use of a glovebox.

Introduction

Hybrid organic-inorganic lead halide perovskites (CH₃NH₃PbX₃, X = I, Br, Cl) are a new class of semiconductors that has emerged rapidly within the last few years. This material class shows excellent semiconductor properties, such as high absorption coefficient¹, tunable bandgap², long charge carrier diffusion length³, high defect tolerance⁴, and high photoluminescence quantum yield⁵^,⁶. The unique combination of these characteristics makes lead halide perovskites very attractive for application in optoelectronic devices, such as single junction⁷^,⁸ and multijunction photovoltaics⁹^,¹⁰, lasers¹¹^,¹², and LEDs¹³.

CH₃NH₃PbX₃ films can be fabricated by a variety of synthetic methods¹⁴, which aim at improving the efficiency of this semiconducting material for energy applications¹⁵. However, optimization of photovoltaic devices relies on the quality of the halide perovskite active layer, as well as its interfaces with charge selective contacts (i.e. electron and hole transport layers), which facilitate photocarrier collection in these devices. Specifically, continuous, pinhole-free active layers are necessary to minimize shunt resistance, thereby improving device performance.

Among the most widespread methods for fabricating organo-lead halide perovskite thin films are solution-based and vacuum-based processes. The most common solution process uses equimolar ratios of lead halide and methylammonium halide dissolved in dimethylformamide (DMF), dimethylsulfoxide (DMSO), or γ-butyrolactone (GBL), or mixtures of these solvents.²^,¹⁶^,¹⁷ Precursor molarity and solvent type, as well as annealing temperature, time and atmosphere, must be precisely controlled to obtain continuous and pinhole-free films.¹⁶ For example, to improve surface coverage, a solvent-engineering technique was demonstrated to yield dense and extremely uniform films.¹⁷ In this technique, a non-solvent (toluene) is dripped onto the perovskite layer during the spinning of the perovskite solution.¹⁷ These approaches are usually well suited for mesoscopic heterojunctions, which employ mesoporous TiO₂ as an electron selective contact with increased contact area and reduced carrier transport length.

However, planar heterojunctions, which use selective contacts based on thin (usually TiO₂) films, are more desirable because they provide a simple and scalable configuration that can be more easily adopted in solar cell technology. Therefore, the development of organo-lead halide perovskite active layers that show high efficiency and stability under operation for planar heterojunctions may lead to technological advancements in this field. However, one of the main challenges to fabricate planar heterojunctions is still represented by the homogeneity of the active layer. A few attempts, based on vacuum processes, have been made to prepare uniform layers on thin TiO₂ films. For example, Snaith and collaborators have demonstrated a dual evaporation process, which yield highly homogenous perovskite layers with high power conversion efficiencies for photovoltaic applications.¹⁸ While this work represents a significant advancement in the field, the use of high vacuum systems and the lack of tunability of the composition of the active layer limit the applicability of this method. Interestingly, extremely high uniformity has been achieved with the vapor-assisted solution process (VASP)¹⁹ and modified low pressure VASP (LP-VASP)⁶^,²⁰. While the VASP, proposed by Yang and collaborators¹⁹, requires higher temperatures and the use of a glove box, the LP-VASP is based on the annealing of a lead halide precursor layer in the presence of methylammonium halide vapor, at reduce pressure and relatively low temperature in a fumehood. These specific conditions enable access mixed perovskite compositions, and fabrication of pure CH₃NH₃PbI₃, CH₃NH₃PbI_3-xCl_x, CH₃NH₃PbI_3-xBr_x, and CH₃NH₃PbBr₃ can be easily achieved. Specifically, CH₃NH₃PbI_3-xBr_x films over the full composition space can be synthesized with high optoelectronic quality and reproducibility⁶^,²⁰.

Herein, we provide a detailed description of the protocol for the synthesis of organic-inorganic lead halide perovskite layers via LP-VASP, including the procedure for synthesizing the methylammonium halide precursors. Once the precursors are synthesized, formation of CH₃NH₃PbX₃ films consists of a two-step procedure that comprises i) the spin-coating of the PbI₂/PbBr₂ (PbI₂, or PbI₂/PbCl₂) precursor on glass substrate or fluorine-doped tin oxide (FTO) coated glass substrate with planar TiO₂, as electron transport layer, and ii) the low pressure vapor-assisted annealing in mixtures of CH₃NH₃I and CH₃NH₃Br that can be finely adjusted depending on the desired optical bandgap (1.6 eV ≤ E_g ≤ 2.3 eV). Under these conditions, the methylammonium halide molecules present in the vapor phase slowly diffuse into the lead halide thin film yielding continuous, pinhole-free halide perovskite films. This process yields a two-fold volume expansion from the starting lead halide precursor layer to the completed organic-inorganic lead halide perovskite. The standard thickness of the perovskite film is about 400 nm. It is possible to vary this thickness between 100-500 nm by changing the speed of the second spin coating step. The presented technique results in films of high optoelectronic quality, which translates to photovoltaic devices with power conversion efficiencies of up to 19% using a Au/spiro-OMeTAD /CH₃NH₃PbI_3-xBr_x/compact TiO₂/ FTO/glass solar cell architecture.²¹

Protocol

Caution: Please consult all relevant material safety data sheets (MSDS) before use. Several of the chemicals used in these syntheses are acutely toxic, carcinogenic, and toxic to reproduction. Implosion and explosion risks are associated with the use of a Schlenk line. Please make sure to check the integrity of the glass apparatus before performing the procedure. Incorrect use of the Schlenk line in association with a liquid nitrogen cold trap may result in condensation of liquid oxygen (pale blue) that can become explosive. Please ensure to receive appropriate on the job training by experts before using vacuum-systems, Schlenk lines, and cryogenic liquids. Please use all appropriate safety practices when performing the synthesis including the use of engineering controls (fume hood) and personal protective equipment (safety glasses, gloves, lab coat, full length pants, closed-toe shoes). All of the following procedures described below are performed in a fume hood in air, unless stated differently.

1. Preparation of Methylammonium Halide

To a 250 mL round bottom flask equipped with a stir bar, add ethanol (100 mL) and methylamine (190 mmol, 16.5 mL, 40%_wt in H₂O), and cool the flask to 0 °C with an ice bath.
While the methylamine solution is stirring (for about 5 min at 600 revolution per min (rpm)), add HI (76 mmol, 10 mL, 57%_wt in H₂O) or HBr (76 mmol, 8.6 mL, 48%_wt in H₂O) dropwise, and seal the flask with a septum.
Allow the reaction to stir for 2 h at 0 ˚C.
Remove the reaction flask from the ice bath and evaporate the solvent and unreacted volatile components at reduced pressure (~50 Torr) with a rotary evaporator equipped with a water bath at 60 ˚C for 4 h or until the volatiles are removed.
To recrystallize the resulting solid, add warm (~50 °C) ethanol (100 mL) and dissolve the residual material.
Slowly add diethyl ether (200 mL) to induce crystallization of a white solid.
Vacuum filter the mixture over a coarse 50 mm glass frit filter.
Recover the supernatant and add diethyl ether (200 mL) to induce additional crystallization of white solid. Vacuum filter the mixture over a second coarse 50 mm glass frit filter.
Combine the white solids on a coarse 50 mm glass frit filter and, while vacuum filtering, wash the resulting powder with diethyl ether three times (~30 mL each time).
Dry the white solid under vacuum. This procedure yields (58.9 mmol, 9.360 g, 77%) of methylammonium iodide (CH₃NH₃I) and (55.5 mmol, 6.229 g, 73%) of methylammonium bromide (CH₃NH₃Br).
Store in the dark and in a desiccator at room temperature in order to minimize decomposition over time.

2. Preparation of Methylammonium Lead Halide (CH₃NH₃PbI_3-xBr_x ) Thin Films⁶^,²⁰

Pre-conditioning of the Schlenk tube
1. Load a 50 mL Schlenk tube (diameter 2.5 cm) with 0.1 g of methylammonium halide. To prevent the chemicals sticking to the walls of the test tube, use a weighing paper cylinder to transfer the methylammonium halide into the tube.
  NOTE: The final ratio of I/(I+Br) in CH₃NH₃PbI_3-xBr_x is determined by the methylammonium halide composition in the test tube. For example, to achieve 30% I content, the Schlenk tube is loaded with 0.03 g CH₃NH₃I and 0.07 g CH₃NH₃Br. Actual obtained compositions may vary with experimental setup, so calibration of the synthesis conditions to yield specific target compositions is necessary. In the present case, this was accomplished by measuring halide content in the synthesized films via energy dispersive X-ray spectroscopy (EDX).
2. Use a Schlenk line equipped with a rotary pump to connect and evacuate the tube. Adjust the pressure to 0.185 Torr. Then, immerse the test tube in a silicone oil bath pre-heated to 120°C, with a magnetic stirrer (600 rpm) for 2 h (pre-conditioning of the Schlenk tube).
  NOTE: This step allows for sublimation of the methylammonium precursor along the sides of the Schlenk tube. It is important to ensure the sublimation of the methylammonium precursor during the two hours of pre-conditioning. A thin layer of methylammonium precursor will condense along the sides of the Schlenk tube to cover the lower half of the tube. If sublimation of the methylammonium precursor is not observed or is happening too fast, check if the pressure of the Schlenk line and the temperature of the oil bath are correct, or try to use fresh methylammonium halide precursor.
3. Remove Schlenk tube from the oil bath and leave methylammonium halide under an overpressure of flowing N₂ to avoid moisture intake.
Substrate preparation
1. Sonicate one substrate (glass or FTO coated glass, 14 x 16 mm²) with water (~3 mL) containing detergent for 15 min in a test tube (diameter 1.5 cm and height 15 cm) at 35 KHz.
2. Discard the detergent/water by rinsing with ultrapure water (~10 mL) 5 times.
3. Discard the ultrapure water, add acetone (~3 mL), and sonicate for 15 min at 35 KHz.
4. Discard the acetone, add isopropanol (~3 mL), and sonicate for 15 min at 35 KHz.
5. Discard the isopropanol, recover the substrate from the test tube with tweezers, and dry it with a N₂ gun for 15 s.
6. Deposit TiO₂ compact layer (100 nm) on FTO glass substrates by electron beam evaporation at a substrate temperature of 350 °C, and a deposition rate of 0.5 Å/s using substrate rotation.²¹
Preparation of the lead halide precursor solution
1. For the preparation of MAPbI_3-xBrx (0 < x < 3), dissolve PbI₂ (0.8 mmol, 0.369 g) and PbBr₂ (0.2 mmol, 0.073 g) in 1 mL DMF to achieve a final concentration of 0.8 M of PbI₂ and 0.2 M of PbBr₂. Sonicate for 5 min at 35 KHz to fully dissolve the precursor.
  1. For the preparation of pure iodine or bromine films, dissolve PbI₂ (1 mmol, 0.461 g) or PbBr₂ (0.8 mmol, 0.294 g) in 1 mL DMF, to achieve a final concentration of 1 M and 0.8 M, respectively. Sonicate for 5 min at 35 KHz to fully dissolve the precursor.
  2. For the preparation of chlorine-doped methylammonium lead iodide perovskite films, dissolve PbI₂ (0.369 g) and PbCl₂ (0.056 g) in 1 mL DMF, to achieve a final concentration of 0.8 M of PbI₂ and 0.2 M of PbCl₂. Sonicate for 5 min at 35 KHz to fully dissolve the precursor.
2. Filter the precursor solution with a 0.2 μm polytetrafluorethylene (PTFE) filter.
Lead halide deposition
1. Pre-heat the precursor solution on a hot plate set to 110 °C for 5 min.
2. With a micropipette, drop 80 μL of the pre-heated lead halide precursor solution onto the non-rotating substrate (glass or TiO₂ deposited on FTO coated glass; 14 x 16 mm² size). Spin at 500 rpm for 5 s with an acceleration rate of 500 rpm s^-1, and 1500 rpm for 3 min with an acceleration rate of 1,500 rpm s^-1.
3. In a fumehood, dry precursor film for 15 min at 110 °C on a hot plate under flowing N₂.
  NOTE: A crystalizing dish is used and placed over the substrate to allow the precursor to dry in a N₂ atmosphere. To vary the thickness of the resulting perovskite film, the speed of the second spin-coating step can be varied from 1,200 to 12,000 rpm to achieve film thickness in the range of 500 to 100 nm. To further decrease the film thickness, diluted precursor solution can be used.
Vapor-assisted annealing
1. Load sample into the Schlenk tube (prepared according to instructions in section 2.1.2). Adjust the pressure to 0.185 Torr.
  NOTE: The sample sits in the test tube above the methylammonium halide without being in direct contact with it. To slow down incorporation of methylammonium, the lead halide surface is oriented to face away from the methylammonium halide.
2. Immerse the Schlenk tube loaded with the sample in silicone oil bath heated to 120 °C for 2 h.
3. Take out the sample and quickly rinse it by dipping it in a beaker containing isopropyl alcohol. Immediately dry the rinsed sample with a N₂ gun.
  NOTE: To prepare pure CH₃NH₃PbI₃ use PbI₂ as the halide precursor and pure methylammonium iodide in the vapor-assisted annealing step. To prepare CH₃NH₃PbBr₃ use PbBr₂ as the halide precursor and pure methylammonium bromide in the vapor-assisted annealing step.

Representative Results

Proton nuclear magnetic resonance (NMR) spectra were taken after the methylammonium halide synthesis to verify the molecule purity (Figure 1). Scanning electron microscopy (SEM) images were acquired before and after vapor annealing (Figure 2) to characterize the morphology and the homogeneity of both the mixed lead halide precursor and the CH₃NH₃PbI_3-xBr_x films. X-ray diffraction (XRD) patterns were collected to confirm phase purity and conversion of lead halide to CH₃NH₃PbI_3-xBr_x (Figure 3).

Figure 1: Nuclear magnetic resonance spectra. (a) ¹H NMR of CH₃NH₃Br in DMSO-d6. Peaks at δ 7.65 (br s, 3H) and 2.35 (s, 3H) ppm confirm the identity of the molecule.²² (b) ¹H NMR of CH₃NH₃I in DMSO-d6. Peaks at δ 7.45 (br s, 3H) and 2.37 (s, 3H) ppm confirm the identity of the molecule.²³ The peaks at 2.50 and 3.33 ppm are due to residual DMSO and water. Please click here to view a larger version of this figure.

Methylammonium bromide and methylammonium iodide may be readily characterized by ¹H NMR (Figure 1). The chemical shift of the methyl group is a sharp singlet centered at δ 2.35 ppm (3H) for the CH₃NH₃Br, and δ 2.37 ppm (3H) for CH₃NH₃I. The ammonium shift is a broad singlet centered at δ 7.65 ppm (3H), and δ 7.45 ppm (3H) for CH₃NH₃Br and CH₃NH₃I respectively. The difference in chemical shift of the two methylammonium halides is due to the different halide electronegativities, which affect (de)shielding of the protons present in the molecules. These chemical shifts are consistent with previously reported spectra²²^,²³.

Figure 2: Conversion of lead halide precursor to CH₃NH₃PbI_3-xBr_x. SEM images of the mixed lead halide precursor (a and b). Representative SEM images of CH₃NH₃PbI_3-xBr_x films annealed in 100% (c, d), 50% (e, f), and 30% (g, h) methylammonium iodide. The faceted films are pinhole free, and show grain sizes up to 700 nm. Scale bar = 5 µm (a, c, e, g), and 1 µm (b, d, f, h). Please click here to view a larger version of this figure.

Figures 2a and 2b show the homogeneous morphology of the lead halide precursor that is subsequently converted to CH₃NH₃PbI_3-xBr_x in mixtures of methylammonium iodide and bromide (c-h). The resulting perovskite films are continuous, pinhole-free with grain sizes up to 700 nm. The standard thickness of the perovskite film is about 400 nm, which is obtained by spin coating 1 M lead halide precursor solution at a speed of 1,500 rpm. The thickness can be changed by varying the rotational speed, with higher speeds yielding thinner films and vice versa. Interestingly, the conversion from the lead halide precursor layer to the resulting lead halide perovskite results in an approximate two-fold volume expansion.

The temperature of 120 °C for the vapor phase anneal is chosen such that methylammonium halide sublimes, diffuses into the lead halide film, and the equilibrium between methylammonium halide vapor and solid CH₃NH₃PbI_3-xBr_x is in favor of the perovskite phase. In a previous study, we showed that annealing at 100 °C resulted in largely incomplete conversion to the perovskite phase and that device performance was best when synthesis was performed at 120 °C instead of 150 °C.²⁰ The phase characterization of precursor and CH₃NH₃PbI_3-xBr_x films on FTO glass substrates by XRD is presented in Figure 3a. The lead halide precursor (0.8 M PbI₂ and 0.2 M PbBr₂) shows PbI₂ phase with its main peak at approximately 12.7°. CH₃NH₃PbI_3-xBr_x films are phase pure and do not contain residual PbI₂ phase. The CH₃NH₃PbI_3-xBr_x XRD peaks exhibit a systematic shift to higher angles due to gradual replacement of the larger I atoms by smaller Br atoms leading to a decrease in lattice constant from ~6.29 Å (x = 0) to ~5.93 Å (x = 3)².

Figure 3: Phase analysis and full composition spectrum CH₃NH₃PbI_3-xBr_x films. (a) XRD patterns of lead halide precursor showing PbI₂ phase, and CH₃NH₃PbI_3-xBr_x films with decreasing iodine content. The magnified pattern clearly depicts the shift of the (110) peak position towards larger diffraction angles upon Br incorporation. (b) Picture of CH₃NH₃PbI_3-xBr_x films with gradual incorporation of Br (left to right: pure CH₃NH₃PbI₃, 90%, 80%, 70%, 50%, 40%, 30%, 20%, 10%, and pure CH₃NH₃PbBr₃). Please click here to view a larger version of this figure.

The picture of CH₃NH₃PbI_3-xBr_x films (Figure 3b) illustrates the gradual incorporation of Br, resulting in a band gap increase from 1.6 eV to 2.3 eV, and thus the change in visible appearance (left, pure CH₃NH₃PbI₃ to right, pure CH₃NH₃PbBr₃). The gradual increase of bandgap has been shown by photoluminescence measurements, which were previously reported on CH₃NH₃PbI_3-xBr_x films with high optoelectronic quality over the full composition space.⁶

Discussion

In order to fabricate highly efficient organo-lead planar perovskite heterojunctions, the homogeneity of the active layer is a key requirement. With respect to existing solution²^,¹⁶^,¹⁷ and vacuum-based¹⁸^,¹⁹ methodologies, our process is remarkably amenable to composition tunability of the active layer that can be synthesized over the full CH₃NH₃PbI_3-xBr_x composition space with high optoelectronic quality and reproducibility.⁶^,²⁰ In addition, this process allows for the use of reduced pressure and relatively low temperature in a fumehood without requiring the use of a glove box or high vacuum deposition.

While LP-VASP is highly reproducible and no modification to the protocol should be necessary, it is noted that the actual Br/(Br+I) composition in the film may be slightly lower than the initial composition of the Schlenk tube. To address this issue, it is critical to measure the halide content via EDX in the final film as well as to confirm the perovskite structure via XRD, in order to perform a calibration of the synthetic conditions yielding specific target compositions with respect to the utilized experimental setup.

In addition, there are a few useful recommendations that can ensure the correct reliability of our process. The quality of the starting materials is particularly important. Storing of both the organic (CH₃NH₃X) and inorganic (PbX₂) precursors in a desiccator under nitrogen atmosphere and controlled humidity is instrumental to ensure reproducibility in the synthesis. In addition, the organic precursors need to be very clean and all the traces of starting materials should be removed with careful washing.

We have demonstrated the synthesis of methylammonium halide and the subsequent transformation of lead halide precursors to CH₃NH₃PbI_3-xBr_x in mixtures thereof, resulting in smooth, pinhole free films that exhibit good optoelectronic quality. With respect to previous methods,²^,¹⁶^,¹⁷^,¹⁸^,¹⁹ this synthetic protocol is versatile and amenable to be adapted in different laboratories because it is easily carried out in a fumehood. In addition, LP-VASP allows for facile accessibility of different organo-lead halide perovskite composition and tuning of the band gap.

The presented film fabrication method provides superior morphology control as compared to pure solution coating methods, yielding highly efficient planar perovskite heterojunction solar cells. Because of the low processing temperature and of the use of standard equipment available in most laboratories (i.e. fumehoods and Schlenk lines), this methodology is especially suitable to fabricate single as well as multijunction solar cells, light emitting diodes, and lasers. We are currently developing a process that allows to deposit large (>2 cm²) area continuous perovskite thin films.

Divulgaciones

The authors have nothing to disclose.

Acknowledgements

Perovskite process development, thin film synthesis, structural and morphological characterization were performed at the Joint Center for Artificial Photosynthesis, a DOE Energy Innovation Hub, supported through the Office of Science of the U.S. Department of Energy under Award Number DE-SC0004993. C.M.S.-F. acknowledges financial support from the Swiss National Science Foundation (P2EZP2_155586).

Materials

Lead (II) bromide, 99.999%	Sigma-Aldrich	398853	Acute toxicity, Carcinogenicity
Lead (II) Iodide, 99.9985%	Alfa Aesar	12724	Acute toxicity, light sensitive
N, N-Dimethylformamide, > 99.9%	Sigma-Aldrich	270547	Acute toxicity, flamable; store in well ventilated place
Isopropyl alcohol, 99.5%	BDH	BDH1133-4LP	Flamable
Methylamine ca. 40% in water	TCI	M0137	Acute toxicity, flamable; Corrosive
Hydrobromic acid 48 wt. % in H2O, ≥99.99%	Sigma-Aldrich	339245	Acute toxicity, Corrosive; air and light sensitive; store in well ventilated place
Hydroiodic acid 57 wt. % in H2O, distilled, stabilized, 99.95%	Sigma-Aldrich	210021	Corrosive; air and light sensitive; store in well ventilated place Recommended storage temperature 2/8 °C; air and light sensitiv
Ethyl Ether Anhydrous BHT Stabilized/Certified ACS	Fisher Chemicals	E 138-4	Acute toxicity, flamable
Ethanol Denatured (Reagent Alcohol), ACS	BDH	BDH1156-4LP	Flamable
Alconoxdetergent	Sigma-Aldrich	242985	Soap utilized for substrate cleaning
Milli-QIntegral 3 Water Purification System	EMD Millipore	ZRXQ003WW	Dispenser of ultrapure water
Fluorine-doped Thin Oxide (FTO) coated glass	Thin Film Devices	Custom	Glass: dimensions 13.8mm x 15.8mm ± 0.2mm, thickness 2.3mm ± 0.1mm; FTO: dimensions 3000Å ± 100Å, resistivity 7-10 ohms/sq, transmission 82% @ 550nm)
Glass substrates	C & A Scientific – Premiere	9101-E	Plain. Length: 75 mm, Width: 25 mm, Thickness: 1 mm
Ultrasonic Cleaner with Digital Timer and Heater	VWR	97043-992	2.8 L (0.7 gal.)24L x 14W x 10D cm (97/16x 51/2x 315/16")
Nuclear Magnetic Resonance Advance 500	Bruker	Z115311
Quanta 250 FEG Scanning Electron Microscope	FEI	743202032141	Equipped with a Bruker Xflash 5030 Energy-dispersive X-ray detector
SmartLab X-ray diffractometer	Rigaku	2080B411	Using Cu Kα radiation at 40 kV and 40 mA

Referencias

De Wolf, S., et al. Organometallic Halide Perovskites: Sharp Optical Absorption Edge and Its Relation to Photovoltaic Performance. J. Phys. Chem. Lett. 5 (6), 1035-1039 (2014).
Noh, J. H., Im, S. H., Heo, J. H., Mandal, T. N., Seok, S. I. Chemical Management for Colorful, Efficient, and Stable Inorganic-Organic Hybrid Nanostructured Solar Cells. Nano Lett. 13 (4), 1764-1769 (2013).
Stranks, S. D., et al. Electron-Hole Diffusion Lengths Exceeding 1 Micrometer in an Organometal Trihalide Perovskite Absorber. Science. 342 (6156), 341-344 (2013).
Oga, H., Saeki, A., Ogomi, Y., Hayase, S., Seki, S. Improved Understanding of the Electronic and Energetic Landscapes of Perovskite Solar Cells: High Local Charge Carrier Mobility, Reduced Recombination, and Extremely Shallow Traps. J. Am. Chem. Soc. 136 (39), 13818-13825 (2014).
Deschler, F., et al. High Photoluminescence Efficiency and Optically Pumped Lasing in Solution-Processed Mixed Halide Perovskite Semiconductors. J. Phys. Chem. Lett. 5 (8), 1421-1426 (2014).
Sutter-Fella, C. M., et al. High Photoluminescence Quantum Yield in Band Gap Tunable Bromide Containing Mixed Halide Perovskites. Nano Lett. 16 (1), 800-806 (2016).
Chen, W., et al. Efficient and stable large-area perovskite solar cells with inorganic charge extraction layers. Science. 350 (6263), 944-948 (2015).
Bi, D., et al. Efficient luminescent solar cells based on tailored mixed-cation perovskites. Sci. Adv. 2 (1), e1501170 (2016).
Werner, J., et al. Efficient Monolithic Perovskite/Silicon Tandem Solar Cell with Cell Area >1 cm2. J. Phys. Chem. Lett. 7 (1), 161-166 (2016).
Kranz, L., et al. High-Efficiency Polycrystalline Thin Film Tandem Solar Cells. J. Phys. Chem. Lett. 6 (14), 2676-2681 (2015).
Xing, G., et al. Low-temperature solution-processed wavelength-tunable perovskites for lasing. Nat. Mater. 13, 476-480 (2014).
Deschler, F., et al. High Photoluminescence Efficiency and Optically Pumped Lasing in Solution-Processed Mixed Halide Perovskite Semiconductors. J. Phys. Chem. Lett. 5 (8), 1421-1426 (2014).
Tan, Z. -. K., et al. Bright light-emitting diodes based on organometal halide perovskite. Nat. Nanotechnol. 9, 687-692 (2014).
Stranks, S. D., Snaith, H. J. Metal-halide perovskites for photovoltaic and light-emitting devices. Nat. Nanotechnol. 10, 391-402 (2015).
Saliba, M., et al. Cesium-containing triple cation perovskite solar cells: improved stability, reproducibility and high efficiency. Energy Environ. Sci. 9, 1989-1997 (1989).
Eperon, G. E., Burlakov, V. M., Docampo, P., Goriely, A., Snaith, H. J. Morphological Control for High Performance, Solution-Processed Planar Heterojunction Perovskite Solar Cells. Adv. Funct. Mater. 24 (1), 151-157 (2014).
Jeon, N. J., et al. Solvent engineering for high-performance inorganic-organic hybrid perovskite solar cells. Nat. Mater. 13, 897-903 (2014).
Liu, M., Johnston, M. B., Snaith, H. J. Efficient planar heterojunction perovskite solar cells by vapour deposition. Nature. 501, 395-398 (2013).
Chen, Q., et al. Planar Heterojunction Perovskite Solar Cells via Vapor-Assisted Solution Process. J. Am. Chem. Soc. 136 (2), 622-625 (2014).
Li, Y., et al. Fabrication of Planar Heterojunction Perovskite Solar Cells by Controlled Low-Pressure Vapor Annealing. J. Phys. Chem. Lett. 6 (3), 493-499 (2015).
Li, Y., et al. Defective TiO2 with high photoconductive gain for efficient and stable planar heterojunction perovskite solar cells. Nat. Commun. 7, 12446 (2016).
Gonzalez-Carrero, S., Galian, R. E., Pérez-Prieto, J. Maximizing the emissive properties of CH3NH3PbBr3 perovskite nanoparticles. J. Mater. Chem. A. 3, 9187-9193 (2015).
Zhou, H., et al. Antisolvent diffusion-induced growth, equilibrium behaviours in aqueous solution and optical properties of CH3NH3PbI3 single crystals for photovoltaic applications. RSC Adv. 5, 85344-85349 (2015).

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Sutter-Fella, C. M., Li, Y., Cefarin, N., Buckley, A., Ngo, Q. P., Javey, A., Sharp, I. D., Toma, F. M. Low Pressure Vapor-assisted Solution Process for Tunable Band Gap Pinhole-free Methylammonium Lead Halide Perovskite Films. J. Vis. Exp. (127), e55404, doi:10.3791/55404 (2017).