Lead iodide (PbI₂, purity ≥ 99.99%), lead bromide (PbBr₂, ≥98%), methylammonium iodide (MAI), and methylammonium bromide (MABr) were used as precursors without further purification. Dimethylformamide (DMF) and dimethyl sulfoxide (DMSO) solvents were used to prepare the solutions, while toluene was used as an anti-solvent during deposition.

The precursor solutions MAPb(I_1−xBr_x)₃ (x = 0, 0.05, 0.1, 0.15) were prepared by precisely adjusting the molar proportions of PbI₂ and PbBr₂ to obtain the desired halogenated composition, while maintaining an overall 1:1 stoichiometric ratio between total lead and the MA⁺ cation. The total concentration was set at 1.3 M. The salts were dissolved in a DMF/DMSO mixture (4:1, V:V) under magnetic stirring at 65˚C at 600 rpm for 1 h to obtain homogeneous and transparent solutions. The solutions were then filtered using PTFE filters (0.45 µm) before deposition.

Fluorine-doped tin oxide (FTO) coated glass substrates were selected and successively cleaned by ultrasound in distilled water, acetone, and isopropanol, then dried under a nitrogen stream. Film deposition was performed by spin coating. The deposition was performed by applying 100µL of precursor solution to the substrate. This was followed by a first rotation at 1000 rpm for 6 seconds, then a second rotation at 4000 rpm for 30 seconds. During the rotation, precisely 20secondsafterthestartofthesecondrotation, 200µLoftoluene was deposited in the center of the forming film to induce rapid crystallization. The samples were then thermally annealed at 110˚C for 30 minutes to promote complete formation of the crystalline phase.

The exact conditions were not recorded by a continuous sensor, but the samples were stored in the dark in a closed cabinet within a temperature-controlled laboratory at the Polytechnic University of Valencia (Spain) in May 2025. During this period, the standard internal temperature was maintained at 22˚C ± 2˚C and the estimated ambient relative humidity within the cabinet was between 45% and 55% RH.

The crystalline structure of the thin films was studied by X-ray diffraction (XRD) using the RIGAKU-Ultima IV diffractometer, with a Cu Kα source (λ = 1.5406 Å). Angular scans were performed between 10˚ and 60˚. The optical properties were studied by UV-Visible spectroscopy using the Ocean spectrometer. Optics HR4000 was used in the visible and near-ultraviolet spectral range to analyze the absorption behavior of the films and estimate the optical band gap width as a function of halogen composition. Photoluminescence measurements were performed at room temperature to analyze radiative recombination processes. Surface morphology and grain size were examined by scanning electron microscopy (SEM).

The XRD diffractograms obtained for the thin films MAPb(I_1−xBr_x)₃ show intense and well-resolved peaks, attributed to the crystallographic planes typical of the perovskite structure [14]. These results confirm the formation of the perovskite crystalline phase for all the compositions studied.

Furthermore, no secondary peaks related to the presence of parasitic phases, such as PbI₂ or PbBr₂, were detected on the diffractograms (Figure 1). This suggests efficient conversion of precursors and good crystallization quality of the deposited films [14][15].

The progressive increase in bromide content is accompanied by a systematic shift of the diffraction peaks towards higher Bragg angles (2θ) (Figure 2). This shift is attributed to the decrease in the crystal lattice parameter resulting from the substitution of iodide ions (I⁻) by bromide ions (Br⁻), which have a smaller ionic radius. This behavior is consistent with Vegard’s law and has been widely reported in the literature for mixed I/Br hybrid perovskites [14].

Figure 1. XRD patterns obtained for different mixed halide perovskite films.

Figure 2. Diffractograms at MAPb(I_1−xBr_x)₃ approximately 14˚ and 28˚.

Furthermore, a decrease in the full width at half maximum (FWHM) of the diffraction peaks is observed overall, which suggests an improvement in the crystallinity of the films as well as an increase in the average size of the crystallites [16].

However, for compositions containing 5% and 10% bromide, a slight increase in full width at half maximum (FWHM) is observed at positions 2θ = 28.618˚ and 14.25˚, respectively (Table 1). This change can be attributed to the appearance of local crystal stresses or to a degree of structural disorder induced by the partial substitution of iodide ions by bromide ions within the perovskite lattice.

The crystallite sizes, estimated using the Scherrer method, nevertheless confirm the positive effect of moderate bromide incorporation on the crystalline quality of the films MAPb(I_1−xBr_x)₃.

Table 1. Scherrer table of MAPb(I_1−xBr_x)₃.

The size of the crystallites D is obtained using Scherrer’s formula:

where:

D = crystallite size (nm)

K = form factor equal to 0.9

λ = wavelength of X-ray radiation (1.5406 Å for Cu Kα)

β = FWHM in radians

θ = Bragg angle (˚) converted to radians (θ = ½ × 2θ)

UV-Visible absorbance spectra show a high absorption coefficient in the visible region of the electromagnetic spectrum, characteristic of organometallic hybrid perovskites and favorable to photovoltaic applications [14]. A progressive shift of the absorption edge towards shorter wavelengths is also observed with increasing bromide content (Figure 3), reflecting a broadening of the optical band gap of the thin films MAPb(I_1−xBr_x)₃ [14].

The photoluminescence (PL) spectra recorded at room temperature show intense and relatively narrow emission peaks for all the compositions studied. A progressive shift of the emission maximum towards shorter wavelengths is observed with increasing bromide content (Figure 4), consistent with the widening of the optical band gap highlighted by UV-Visible absorbance measurements.

Figure 3. Absorbance spectra of thin films MAPb(I_1−xBr_x)₃.

Figure 4. Normalized photoluminescence for perovskite films MAPb(I_1−xBr_x)₃.

The gap energy increases almost linearly with the bromide fraction x (Figure 5), in agreement with the results previously reported for MAPb(I_1−xBr_x)₃ [14]. This evolution reflects the changes in the electronic structure, in particular the shift in the valence and conduction band levels induced by halogenated substitution.

Furthermore, the intensity of photoluminescence (PL) is closely linked to the crystalline quality and morphology of thin films. A decrease in the density of non-radiative defects as well as better passivation of grain boundaries promotes more efficient radiative recombination, resulting in more intense PL emission [17] (Table 2).

Figure 6 schows a progressive increase in the band gap energy MAPb(I_1−xBr_x)₃ with increasing bromine content, reflecting the band gap widening by the partial substitution of I⁻ by Br²⁻. Indeed, the band gap energy increases from 1.60 eV for the bromine-free film (0%) to 1.68 eV for an incorporation rate of 15%.

Figure 5. Normalized photoluminescence of MAPb(I_1−xBr_x)₃ as a function of energy.

Table 2. Band gap energy of MAPb(I_1−xBr_x)₃.

Figure 6. Variation of the band gap energy as a function of the Br concentration.

The SEM images (Figure 7) show that the thin films are continuous and well-covered, composed of polycrystalline grains. The average grain size decreases slightly as the bromide content increases. This behavior could be associated with changes in nucleation and growth kinetics during solution deposition. A more homogeneous morphology and better substrate coverage generally help limit non-radiative recombination pathways, which may partly explain the trends observed in photoluminescence (PL) measurements. These observations highlight the importance of precise control of the halogen composition to simultaneously optimize the structural, optical, and morphological properties of the films.

Figure 7. SEM images of thin films MAPb(I_1−xBr_x)₃.

The long-term stability of the films MAPb(I_1−xBr_x)₃ was assessed by weekly monitoring of X-ray diffraction under ambient conditions.

To accurately assess the degradation kinetics without the substrate crushing effect, the XRD diagrams were normalized (Figure 8). Comparative analysis of the curves after 3 weeks of exposure (green curves) highlights the superiority of the 10% Br sample. While the main perovskite peaks at approximately 14.2˚ and 28.5˚ collapse almost completely for the pure compound (0% Br) and weaken for the 15% Br, they maintain their resolution and maximum relative intensity for the 10% Br composition. This result confirms the existence of an optimum at 10% bromine, limiting network amorphization while avoiding the local mechanical stresses suspected at the higher 15% concentration.

Monitoring by UV-Vis spectroscopy confirms structural trends while revealing the surface condition of the films.

For the 0% Br sample A progressive blurring of the absorption edge and a dramatic increase in the baseline are observed after 14 days. This vertical shift may not be an actual increase in absorption, but rather a sign of strong light scattering caused by physical degradation and increased film roughness following its structural collapse.

Figure 8. Diffractograms of fresh and 3-week-old thin layers MAPb(I_1−xBr_x)₃.

For mixed compositions (5% - 15% Br), the absorption front remains stable and sharp for at least 21 days. For the 10% Br sample, the spectrum retains its initial profile even after 28 days, showing only slight scattering at the end of the period. This could demonstrate that bromine not only stabilizes the internal structure but also preserves the optical quality of the interface [15][18] (Figure 9).

Photoluminescence (PL) spectra offer the finest understanding of electronic quality during aging.

A remarkable phenomenon of “humidity-assisted passivation” was observed for all bromine-doped samples. By the second week, the PL intensity increased significantly. This effect was maximal for the 10% Br sample, whose intensity was four times greater than that of the undamaged film. This luminescence peak suggests that controlled exposure to ambient humidity allows for the passivation of surface defects or the rearrangement of grain boundaries, thereby reducing non-radiative recombination.

Figure 9. Absorption of the different thin layers of MAPb(I_1−xBr_x)₃ fresh and old.

However, after 21 days, a competition arises between this passivation and chemical degradation. While the 15% Br sample experiences a rapid drop in PL intensity by week 4, the 10% Br sample maintains robust emission. This crucial result identifies the 10% Br ratio as the optimal threshold: it provides sufficient protection against moisture while avoiding excessive network stresses or microscopic segregation that could occur at higher bromine levels (Figure 10).

Figure 10. Photoluminescence of different thin layers of MAPb(I_1−xBr_x)₃ fresh and old.