Since their first appearance, organic-inorganic perovskite absorbers have been capturing the attention of the scientific community. While high efficiency devices highlight the importance of band level alignment, very little is known on the origin of the strong n-doping character observed in the perovskite. Here, by means of a highly accurate photoemission study, we shed light on the energy alignment in perovskite-based devices. Our results suggest that the interaction with the substrate may be the driver for the observed doping in the perovskite samples.
Since the discovery of Methylammonium Lead Iodide (MAPbI3) perovskite1, a tremendous effort of the scientific community made was focused on exploiting this material as a very efficient light absorber. Initially, perovskite has been used as sensitizer for all-solid-state dye-sensitized solar cells (DSSCs)2,3,4,5, but soon it has been clear that perovskite could act also as charge transport medium exploiting its charge transport properties2,4,6,7,8,9. This approach opened the route to planar architecture devices that revolutionized the photovoltaic research scenario of the recent years10,11,12,13,14,15,16.
Beside the benchmark molecular system MAPbI3, several alternative organic/inorganic perovskites have been developed. First attempts to replace the environmental problematic Lead with Tin have been performed17, along with the substitution of metylammonium with formamidinium cationic molecule18. Also the counterion of the perovskite has been subjected to substitutions, leading to a fine tuning of the band gap5,19, and stability improvement20.
The most intriguing deviation from the initial MAPbI3 is represented by the mixed phase MAPbI3−xClx: here, a small part of the chlorine used in the PbCl2 precursor is supposed to become part of the final perovskite, thought it proves to be very difficult to observe. The difference in the two phases is evident in terms of charge recombination rate, sensibly lower in the mixed phase4,7,21. Initial studies indicated a co-existence of MAPbI3 and MAPbCl3 in a mixed phase, with a “chlorine rich” interface layer that facilitate the charge transfer between perovskite and TiO222,23. Subsequent studies, however, demonstrated that only extremely small amount of chlorine, or none at all, remains in the final perovskite24,25,26,27,28, suggesting that the different device performance between the pure MAPbI3 and MAPbI3−xClx is due to their film morphology, much more continuous in the latter case29,30.
Doping level, and hence band alignment, is an extremely important issue in organic-inorganic perovskite solar cells. Efficient devices need holes and electrons extracting layers with the correct energy level alignment31,32, therefore, understanding the details of the electronic structure of the perovskite absorber and the band alignment at the interfaces is of paramount importance. Initial experiments showed that both MAPbI3 and MAPbI3−xClx are extremely n-doped semiconductor, with the Fermi level very close to the conduction band minimum. However, depositing the perovskite material on p-doped semiconductor, like PEDOT:PSS or NiO, results in a reduced n-doping for perovskite33 and, more in general, it has been shown that the perovskite electronic structure may change depending on the substrate used34. Wang et al. showed that even a self-doping effect is possible by changing the relative ratio PbI2/MAI in the precursor solution35. Thus, understanding the origin of this doping, and the way to control it, is fundamental in the smart design of perovskite-based heterojunction devices, representing the key to improve the efficiency of future devices.
To address all these open issues, we report an accurate electronic property study of MAPbI3 and MAPbCl3, along with their lead halide precursors PbI2 and PbCl2. In order to understand the interface effects between MAPbI3 and MAPbCl3, a third sample composed by both the perovskites has been prepared. We used X-ray diffraction to confirm the high quality and phase purity of films, and photoemission spectroscopy to study their electronic properties. From Lead core-level photoemission we gain insight in the chemistry of the various compounds, while UV-excited valence bands provide information on band alignment and charge transfer mechanisms. Finally, photoemission spectra have been compared with first-principles GW calculations.
Results and Discussion
Lead halide samples have been evaporated in situ in high vacuum (P < 10−8 mbar) on a polycrystalline gold sample for photoemission experiments, while diffraction measurements have been performed on powder crystallized on a nylon loop. MAPbI3 sample has been prepared by spin-coating a pure iodine perovskite solution (CH3NH3I and PbI2 1:1 in DMF) on silicon < 100 > wafers (20 × 20 mm2) (2000 rpm for 60 seconds). Substrates were placed on a hot plate for 5 minutes at 85 °C to achieve complete evaporation of solvent and crystallization of the hybrid organic-inorganic material. MAPbCl3 sample for photoemission experiment has been prepared with a variation of the two-step method: PbCl2 was evaporated on a polycrystalline gold substrate, and a saturated methylammonium chloride (MACl) solution in ethanol was drop-casted on the obtained film. Diffraction measurement has been performed crystallizing a solution of MACl and PbCl2 1:1 in DMSO on a nylon loop without subsequent annealing. The mixed perovskite phase has been obtained evaporating PbI2 on polycrystalline gold (for the photoemission measurements) or silicon on a kapton tape (for the diffraction measurements) and drop-casting a solution of MACl and PbI2 1:1 5% in weight in DMF. All the drop-casting processes have been performed with the sample placed on a hot plate kept at 80 °C up to the complete evaporation of the solvent.
XRD characterization has been performed to identify the phases present in all the synthesized samples. The lattice parameters of the perovskite phases have been refined and agree with literature data (Table S1). Figure 1 shows the powder diffraction pattern of all the investigated samples. Panels a) and b) show the diffraction pattern of tetragonal MAPbI3 and cubic MAPbCl3 perovskites, along with the diffraction patterns of the stock reagents used in the synthesis, respectively PbI2, MAI, PbCl2, and MACl. Upon formation of MAPbI3 perovskite by spin coating process no traces of residual of PbI2 or MAI can be detected, while panel b) shows that residual traces of MACl remains (peaks at 17.5, 22.9, 27.2, 29.5 degrees) in the MAPbCl3 formation process when deposition is not followed by an annealing. These data definitely support the importance of a mild annealing after the perovskite formation. The two-step process therefore does not ensure the formation of a pure perovskite sample, leaving a certain amount of unreacted precursor, mainly methylammonium compounds. An annealing performed in the temperature range 80–100 °C is enough to remove the metyhlammonium residual without ruining the perovskite film21,22.
Panel c) of Fig. 1 shows the diffraction pattern of the mixed perovskite sample once the background coming from the kapton tape has been removed. Majority of the diffraction signals can be associated to two perovskites, along with a certain amount of unreacted reagents (PbCl2, PbI2, MAI) and a mixed lead halide phase (PbClI). Curve fitting of the whole profile, reported in Supplementary Fig. S2, has been obtained using Le Bail refinement (Rwp of 1.3%). Inset shows the region 12–16°: here we can easily distinguish the contribution coming from PbI2 (12.7°), MAPbI3 (14.1°), and MAPbCl3 (15.6°). Supplementary Materials report crystallographic parameters of all the phases found (Table S2).
After a complete solid phase characterization of our samples have been obtained, photoemission spectroscopy has been exploited to determine their electronic structure. Figure 2b shows the Pb 4 f photoemission peaks of our reference compounds MAPbCl3, MAPbI3, PbCl2, and PbI2. All these spectra, besides the PbCl2 one, show a low energy component at 136.7 eV: this corresponds to interstitial elemental Pb10,24,36. It is worth noticing that the energy of the two lead salt peaks is remarkably different (1.5 eV) even if they are chemically very similar bearing formally the same lead oxidation state. The electron affinity of chlorine is in fact higher than the iodine one, controlling the charge transfer from lead atoms. In particular, an increase of the electron affinity of the halide corresponds to an increase of the binding energy of the lead peaks. Upon perovskite formation we can see that both MAPbCl3 and MaPbI3 show a lower Pb 4 f binding energy compared to their respective lead halide salts equivalents (less than 0.1 eV for PbI2 - MAPbI3, and 0.6 eV for PbCl2 - MAPbCl3), suggesting an effective total energy lowering induced by the perovskite formation, even more pronounced in the MAPbCl3 case.
The mixed perovskite shows much more broad and asymmetric lead peaks, indicating the presence of different and well-separated components. We fitted these peaks with three voigt components and a Shirley background (shown in Fig. 2a): the first component has been held at 136.7 eV to take in account for the elemental lead component, the other two left free to move. The fit result is reported in Table 1: the energy of the two free components shows an excellent similarity with the energy of lead peaks in pure MAPbCl3 and MAPbI3 perovskites. These results imply that little, or none, band bending occurs at the MAPbCl3/MAPbI3 interface. From this analysis the mixed perovskite sample results to be formed by 29% of MAPbCl3 and 71% of MaPbI3.
Since the binding energy of lead in PbI2 is very similar to the one in MAPbI3, it can be argued that the peak assigned to the perovskite could be a mixture of the two. This conclusion seems confirmed by XRD data, which show the presence of also lead halide. However, we have to consider the different probing depth of the two techniques: XRD is extremely bulk sensitive since it is a photon-in photon-out technique, while exactly the opposite holds for soft x-rays and UV photoemission. The kinetic energy of the analyzed electron in this experiment (both core levels and valence band) is in the range 50–150 eV, with an inelastic mean free path of less than 1 nm. For this reason, it is more consistent to compare core level with valence band data that, as we will discuss in the following, do not give us any evidence of PbI2 on the surface of the mixed sample. We can conclude that most of the PbI2 seen in the diffraction pattern comes from the substrate/perovskite interface, were a thick film of lead iodide has been evaporated.
Finally, Fig. 3 shows the valence band of the two perovskites (panels a and b) along with lead iodide and chloride salts (panel c). These spectra are acquired with low energy photons (55 eV), differently from most of the other perovskite valence bands published up to now10,24,33,36,37. The low photon energy we used ensures a comparable photoemission cross section for lead/iodine and carbon/nitrogen derived states, permitting us to highlight the structure in the 6–12 eV binding energy range. Considering that the calculated DOS does not take into account the different cross section of the different element-derived states, we can conclude that accordance between experimental data and calculations is fairly good. This remarks once again the excellent quality of our samples, comparable with in-situ cleaved ones38, that permits us to determine with a high degree of reliability the energy level alignment of the perovskites films.
Samples with such high-quality surface do not need the more bulk sensitive high-energy photons for a clear determination of the valence band maximum, with the advantage of gaining energy resolution. Moreover, it is worth noting that none of our valence bands show an appreciable Fermi level, regardless the amount of metallic lead appearing in XPS spectra.
Figure 4 shows an enlarged view of the photoemission spectra near the valence band maximum plotted in a logarithmic scale graph, used to extract the value of the valence band maximum (in Supporting Information the same procedure using linear scale graphs). The measured value of 1.15 eV for the valence band maximum of MAPbI3 is in fair accordance with the previously reported values, confirming that this compound is a n-doped semiconductor. The MAPbCl3: looks instead an intrinsic semiconductor, with its band gap of 2.9 eV, and its valence band maximum placed at 1.46 eV.
Panel b of Fig. 5 summarizes the energy level position derived from our data, joined with band gap values found in literature2,22,30,37,39,40. In this scheme bands are aligned to the Fermi level, as it would be in the case of an interface, but far enough from it not to take into account any band bending effect. From this scheme it is evident that the only interface capable of promoting the charge transfer from the MAPbI3 is the MAPbI3/PbI2 one. In fact, at this interface holes can be transferred from MAPbI3 to PbI2, but not electrons. While valence band maximum of PbI2 is approximately 0.3 eV closer to the Fermi level with respect to the MAPbI3 one, and hence capable of accepting holes, its conduction band is 1 eV further away from Fermi, forbidding any electron transfer from MAPbI3 to PbI2. This scheme is consistent with some others presented in the literature41,42, but differs from the one presented by Chen et al.43. In the latter, the authors claim that the presence of PbI2 between the perovskite absorber and the electron transfer material TiO2 helps to avoid recombination between the electron injected in the scaffold and the remaining hole in the perovskite, but on the basis of our data we can exclude that any electron transfer from the perovskite to TiO2 (or any other electron transporting material) occurs via a PbI2 layer. From our scheme it results also clear that no charge transfer, neither of electrons nor of holes, is possible from MAPbI3 to MAPbCl3.
The valence band of the mixed perovskite shows a peculiar behavior. Figure 6 shows the experimental UPS spectrum (purple circles) acquired with a photon energy of 21.22 eV (He I emission line), along with two differently displaced calculated spectra. It is worth noticing that the photon energy used to acquire this valence band spectrum is different from the previous one (21.22 vs 55 eV), however, the change in probing depth and difference in photoionization cross section do not affect the value of the quantity we are mostly interested in, i.e. the valence band maximum. In both panels, the experimental spectrum is compared with a total DOS formed by simply adding the calculated DOSs of MAPbI3 and MAPbCl3. Once again accordance between the experimental spectrum and the calculated DOS is reasonable, meaning that basically MAPbI3 and MAPbCl3 form two distinct phases in the sample, with no interplay between them.
In panel a, each single calculated DOS has been placed at the same binding energies of the calculated DOSs in panels a and b of Fig. 3. This choice ensures a perfect energy matching between total DOS and experimental spectrum for the peak at 5.5 eV of binding energy, whose major contribution comes from the MAPbCl3 DOS. However, the same does not hold for the structures between 1 and 3 eV and at 8 eV of binding energy, mainly due to MAPbI3 DOS. Moreover, the valence band onset is not well matched in this condition, as highlighted in the inset of Fig. 6: calculated DOS (bronze continuous line) is shifted 0.3 eV toward higher binding energies with respect to the experimental spectrum (violet circles). To overcome these problems a new total DOS has been shaped: in panel b of Fig. 6 it is shown as a green continuous line. This new total DOS is again the sum of the single MAPbI3 and MAPbCl3 DOSs, but in this case the MAPbI3 DOS has been shifted by 0.3 eV towards lower binding energies with respect to its original position. This new total DOS still matches the peak at 5.5 eV, but now is capable of matching well also the region at 8 eV and the valence band onset, as shown in the inset of Fig. 6. The shift of the MAPbI3 component of the valence band is also reflected by the valence band maximum: in this mixed sample it is 0.86 eV as extrapolated once again from a logarithmic plot, i.e. 0.3 eV closer to the Fermi level with respect to the pure MAPbI3 perovskite.
In both cases the total DOS has been composed with 30% of MAPbCl3 and 70% of MaPbI3 calculated DOSs, consistently with the amount deduced by the XPS data. The accordance between experimental data and calculations is good even without adding PbI2 derived features, confirming that PbI2 is underneath the perovskite film as discussed for XPS data, too deep to be detected by photoemission. To corroborate this hypothesis, we can notice that the valence band offset for this mixed phase (inset of Fig. 6) is around 100 meV shifted toward higher binding energy with respect to the PbI2 onset (Fig. 4c), excluding definitely the possibility that photoemission spectra for this sample show any PbI2 related features.
The shift of the MAPbI3 valence band looks really similar to what observed by Wang et al., where a perovskite self-doping is observed just due to a growth procedure that uses an excess of MAI29. This is also supported by the electron secondary cuts reported in panel (a) of Fig. 5. Here, we find the work function values for MAPbI3 and MAPbCl3 perovskites, which are in good accordance with the already known value, and for the mixed perovskite we prepared. We can see that, the while valence band is the superposition of the two contributions of MAPbI3 and MAPbCl3, the work function neither is intermediate between the two, nor the lowest one. Exactly as in the case of a MAPbI3 perovskite growth with an excess of MAI, the work function of our mixed perovskite is higher than the stoichiometric one. However, in our growth process there is no excess of MAI, but rather a lack. We drop casted a solution 1/1 PbI2:MAI, i.e. a stoichiometric solution, on a PbI2 film, and XRD patterns and photoemission spectroscopy spectra suggest that our sample is essentially a stoichiometric (even if mixed) perovskite deposited on PbI2 film. On the other hand, panel b of Fig. 5 shows clearly that the Fermi level of PbI2 is not in the center of its band gap, but rather closer to the valence band maximum, as the case of a p-type semiconductor. This picture is closer to the one described by Miller et al., where MAPbI3 deposited on different p and n-type semiconductor shows a different doping level33. Finally, it is worth noting that the MAPbCl3 valence band is perfectly aligned between the pure and the mixed phase, meaning that whatever is the origin of doping in MAPbI3, this does not affect the MAPbCl3 perovskite.
In this paper we have investigated the electronic structure of MAPbI3, MAPbCl3, and their lead halide precursors PbI2 and PbCl2. High resolution photoemission spectra have been compared with accurate GW calculations. The good accordance between experimental spectra and calculations, along with XRD, confirm the high reliability of our data, allowing us to be highly confident on the correctness of the extracted information.
Valence band alignment between perovskites and lead halide precursors clearly indicates that no charge transfer between them is possible, except for a hole transfer process from MAPbI3 to PbI2.
A third perovskite sample, composed by both MAPbI3 and MAPbCl3 has also been investigated by means of X-ray diffraction and photoemission. Here a different doping level for the MAPbI3 component has been found, possibly related to the p-type nature of the PbI2 film forming the substrate of the perovskite.
Best efficiency performances have been obtained by a smart design of the heterojunctions for charge transfer44, demonstrating the importance of a precise knowledge of the electronic structure of all the components. The high accuracy electronic structure determination we performed will therefore provide robust basis for further boosting of devices performance. Always in this framework, however, future studies on the doping origin of perovskite are required, as the ability of tuning this doping level can add a new parameter in devices design.
Photoemission experiment has been performed in a modified VG Escalab MKII (secondary cut-off electrons and valence bands at 21.22 eV) and on BEAR beamline at Elettra45 (core levels and valence bands at 55 eV). The overall resolution is 200 meV for valence band spectra and 800 meV for core level spectra. All binding energies are referred to the Fermi level of the spectrometer. Binding energy calibration has been performed using the elemental Pb4f7/2 (Pb0) component present in all the spectra for core levels, while valence bands have been aligned using a gold foil placed in the vicinity of the sample.
Diffraction experiments have been performed at room temperature at the XRD1 beamline at Elettra46. The powder diffraction patterns of MAPbI3 and mixed perovskites sample (both grown on thick substrates) have been collected in transmission mode using a monochromatic wavelength of 0.7 Å with an exposure time of 30 seconds, while the perovskite sample MAPbCl3 (mounted on nylon loop) has been collected using a monochromatic wavelength of 1 Å for 60 seconds (to improve count statistics). Bidimensional diffraction patterns were recorded on a PILATUS 2 M hybrid pixel area detector (pixel dimension 172 μm - Dectris Ltd., Baden-Daettwil, Switzerland) at a distance of 200 mm for MAPbCl3 and 85 mm for MAPbI3 and mixed perovskite phase. One-dimensional diffraction patterns (Fig. S2a–c) were obtained in the 2θ range 5−25° for both MAPbI3 and mixed MAPbI3/MAPbCl3 samples and in the 2θ range 7−47° for MAPbCl3 sample by integrating the two-dimensional images with the program FIT2D. Standard experimental calibration has been followed using a 0.3 mm borosilicate capillary filled with NIST LaB6 660a standard powder (SRM660), to define the beam centre, adjust detector distance and tilting. Monochromator energy has been calibrated using a fluorescence scan at selenium K absorption edge. All the experimental patterns have been analyzed using a whole powder pattern fitting (Le Bail method) using the GSAS Package with the EXPGUI interface. All the phases used to model the synthetized compounds are listed in the Table S2 of the SI.
DOSs have been obtained using the GW approximation in which the electron self-energy is expressed as the product of the electron one-body Green’s function (G), evaluated at the Density Functional Theory (DFT) level, with the screened Coulomb interaction (W) which in turn is evaluated within the random phase approximation47,48. Spin-orbit coupling (SOC) is pivotal for the correct assessment of electronic properties49. Calculations were performed using the Quantum-Espresso50,51 suite of DFT packages. The generalized gradient approximation (GGA) for the exchange and correlation energy described in ref.52 is used in the DFT calculations. We investigated the room-temperature tetrahedral phases of MAPbI3 and MAPbCl3 involving a primitive cell comprising 48 atoms, which is described through periodic boundary conditions and discrete sampling of the Brillouin zone. Both lattice parameters and atomic positions have been optimized at the DFT level. A thorough description of the technical details required by our SOC-GW calculations is reported in refs49.
Data are available upon request to the corresponding authors.
Kojima, A., Teshima, K., Shirai, Y. & Miyasaka, T. Organometal halide perovskites as visible-light sensitizers for photovoltaic cells. J. Am. Chem. Soc. 131, 6050–6051 (2009).
Lee, M. M., Teuscher, J., Miyasaka, T., Murakami, T. N. & Snaith, H. J. Efficient Hybrid solar cells based on meso-superstructured organometal halide perovskites. Science 338, 643–647 (2012).
Burschka, J. et al. Sequential deposition as a route to high-performance perovskite-sensitized solar cells. Nature 499, 316–319 (2013).
Wehrenfennig, C., Eperon, G. E., Johnston, M. B., Snaith, H. J. & Herz, L. M. High charge carrier mobilities and lifetimes in organolead trihalide perovskites. Adv. Mater. 26, 1584–1589 (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, 1764–1769 (2013).
Xing, G. et al. Long-range balanced electron- and hole-transport lengths in organic-inorganic CH3NH3PbI3. Science 342, 344–347 (2013).
Stranks, S. D. et al. Electron-hole diffusion lengths exceeding 1 micrometer in an organometal trihalide perovskite absorber. Science 342, 341–344 (2013).
Yang, J. P. et al. Band dispersion and hole effective mass of methylammonium lead iodide perovskite. Solar-RLL 2, 1800132 (2018).
Lee, M.-I. et al. First determination of the valence band dispersion of CH3NH3PbI3 hybrid organic–inorganic perovskite. J. Phys. D: Appl. Phys. 50, 26LT02 (2017).
Conings, B. et al. Perovskite-based hybrid solar cells exceeding 10% efficiency with high reproducibility using a thin film sandwich approach. Adv. Mater. 26, 2041–2046 (2014).
Liu, M., Johnston, M. B. & Snaith, H. J. Efficient planar heterojunction perovskite solar cells by vapour deposition. Nature 501, 395–398 (2013).
Malinkiewicz, O. et al. Perovskite solar cells employing organic charge-transport layers. Nat. Photonics 8, 128–132 (2014).
Sutter-Fella, C. M. et al. Cation-dependent light-induced halide demixing in hybrid organic–inorganic perovskites. Nano Lett. 18, 3473–3480 (2018).
Ono, L. K., Juarez-Perez, E. J. & Qi, Y. Progress on perovskite materials and solar cells with mixed cations and halide anions. ACS Appl. Mater. Interfaces 9, 30197–30246 (2017).
Li, W. et al. Chemically diverse and multifunctional hybrid organic–inorganic perovskites. Nature Rev. Mater. 2, 16099 (2017).
Chen, Y., Zhang, L., Zhang, Y., Gaoa, H. & Yan, H. Large-area perovskite solar cells–a review of recent progress and issues. RSC Adv. 8, 10489–10508 (2018).
Hao, F., Stoumpos, C. C., Cao, D. H., Chang, R. P. H. & Kanatzidis, M. G. Lead-free solid-state organic–inorganic halide perovskite solar cells. Nat. Photonics 8, 489–494 (2014).
Pang, S. et al. NH2CH=NH2PbI3: An alternative organolead iodide perovskite sensitizer for mesoscopic solar cells. Chem. Mater. 26, 1485–1491 (2014).
Li, C. et al. Halide-substituted electronic properties of organometal halide perovskite films: direct and inverse photoemission studies. ACS Appl. Mater. Interfaces 8, 11526–11531 (2016).
Hieulle, J. et al. Unraveling the impact of halide mixing on perovskite stability. Jour. Amer. Chem. Soc. 141, 3515–3523 (2019).
Suarez, B. et al. Recombination study of combined halides (Cl, Br, I) perovskite solar cells. J. Phys. Chem. Lett. 5, 1628–1635 (2014).
Colella, S. et al. MAPbI3−xClx Mixed halide perovskite for hybrid solar cells: the role of chloride as dopant on the transport and structural properties. Chem. Mater. 25, 4613–4618 (2013).
Colella, S. et al. Elusive presence of chloride in mixed halide perovskite solar cells. J. Phys. Chem. Lett. 5, 3532–3538 (2014).
Philippe, B. et al. Chemical and electronic structure characterization of lead halide perovskites and stability behavior under different exposures - a photoelectron spectroscopy investigation. Chem. Mater. 27, 1720–1731 (2015).
Dualeh, A. et al. Effect of annealing temperature on film morphology of organic-inorganic hybrid pervoskite solid‐state solar cells. Adv. Funct. Mater. 24, 3250–3258 (2014).
Raga, S. R. et al. Influence of air annealing on high efficiency planar structure perovskite solar cells. Chem. Mater. 27, 1597–1603 (2015).
Yu, H. et al. The role of chlorine in the formation process of CH3NH3PbI3−xClx perovskite. Adv. Funct.Mater. 24, 7102–7108 (2014).
Unger, E. L. et al. Chloride in lead chloride-derived organo-metal halides for perovskite-absorber solar cells. Chem. Mater. 26, 7158–7165 (2014).
Tidhar, Y. et al. Crystallization of methyl ammonium lead halide perovskites: implications for photovoltaic applications. J. Am. Chem. Soc. 136, 13249–13256 (2014).
Edri, E., Kirmayer, S., Kulbak, M., Hodes, G. & Cahen, D. Chloride inclusion and hole transport material doping to improve methyl ammonium lead bromide perovskite-based high open-circuit voltage solar cells. J. Phys. Chem. Lett. 5, 429–433 (2014).
Schulz, P. et al. Interface energetics in organo-metal halide perovskite-based photovoltaic cells. Energy Environ. Sci. 7, 1377–1381 (2014).
Park, S. M. et al. Processing dependent influence of the hole transport layer ionization energy on methylammonium lead iodide perovskite photovoltaics. ACS Appl. Mater. Interfaces 10, 15548–15557 (2018).
Miller, E. M. et al. Substrate-controlled band positions in CH3NH3PbI3 perovskite films. Phys. Chem. Chem. Phys. 16, 22122–22130 (2014).
Olthof, S. & Meerholzm, K. Substrate-dependent electronic structure and film formation of MAPbI3 perovskites. Sci. Rep. 7, 40267, https://doi.org/10.1038/srep40267 (2017).
Wang, Q. et al. J. Huang, Qualifying composition dependent p and n self-doping in CH3NH3PbI3. Appl. Phys. Lett. 105, 163508 (2014).
Lindblad, R. et al. Electronic structure of TiO2/CH3NH3PbI3 perovskite solar cell interfaces. J. Phys. Chem. Lett. 5, 648–653 (2014).
You, J. et al. Low-temperature solution-processed perovskite solar cells with high efficiency and flexibility. ACS Nano 8, 1674–1680 (2014).
Kollár, M. et al. Clean, cleaved surfaces of the photovoltaic perovskite. Sci. Rep. 7, 695, https://doi.org/10.1038/s41598-017-00799-0 (2017).
Park, B. W. et al. Enhanced crystallinity in organic-inorganic lead halide perovskites on mesoporous TiO2 via disorder-order phase transition. Chem. Mater. 26, 4466–4471 (2014).
Mosconi, E., Amat, A., Nazeeruddin, M. K., Grätzel, M. & De Angelis, F. First-principles modeling of mixed halide organometal perovskites for photovoltaic applications. J. Phys. Chem. C 117, 13902–13913 (2013).
Calloni, A. et al. Stability of organic cations in solution-processed CH3NH3PbI3 perovskites: formation of modified surface layers. J. Phys. Chem. C 119, 21329–21335 (2015).
Zhou, X., Li, X., Liu, Y., Huang, F. & Zhong, D. Interface electronic properties of co-evaporated MAPbI3 on ZnO(0001): In situ X-ray photoelectron spectroscopy and ultraviolet photoelectron spectroscopy study. App. Phys. Lett. 108, 121601 (2016).
Chen, Q. et al. Controllable self-induced passivation of hybrid lead iodide perovskites toward high performance solar cells. Nano Lett. 14, 4158–4163 (2014).
Zhou, H. et al. Interface engineering of highly efficient perovskite solar cells. Science 345, 542–546 (2014).
Nannarone, S. et al. The BEAR Beamline at Elettra. AIP Conf. Proc. 705, 450–453 (2004).
Lausi, A. et al. Status of the crystallography beamlines at Elettra. European Physical Journal Plus 130, 43 (2015).
Hedin, L. New Method for Calculating the One-Particle Green’s Function with Application to the Electron-Gas Problem. Phys. Rev. 139, A796–A823 (1965).
Hybertsen, M. S. & Louie, S. G. Electron correlation in semiconductors and insulators: Band gaps and quasiparticle energies. Phys. Rev. B 34, 5390–5413 (1986).
Umari, P., Mosconi, E. & De Angelis, F. Relativistic GW calculations on CH3NH3PbI3 and CH3NH3SnI3 Perovskites for Solar Cell Applications. Sci. Rep. 4, 4467, https://doi.org/10.1038/srep04467 (2014).
Giannozzi, P. et al. QUANTUM ESPRESSO: a modular and open-source software project for quantum simulations of materials. J. Phys. Condens. Matter 21, 395502 (2009).
Giannozzi, P. et al. Advanced capabilities for materials modelling with Quantum ESPRESSO. J. Phys. Condens. Matter 29, 465901 (2017).
Perdew, J., Burke, K. & Ernzerhof, M. Generalized Gradient Approximation Made Simple. Phys. Rev. Lett. 77, 3865–3868 (1996).
A.G. thanks MIUR support within the FIRB “Nanosolar” (RBAP11C58Y) and “Advanced Nanotechnologies For Multivariate Sensor Fabrication” by NATO Emerging Security Challenges Division. Measurements on BEAR beamline in Elettra have been performed under the proposal No. 20140068.
The authors declare no competing interests.
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Caputo, M., Cefarin, N., Radivo, A. et al. Electronic structure of MAPbI3 and MAPbCl3: importance of band alignment. Sci Rep 9, 15159 (2019). https://doi.org/10.1038/s41598-019-50108-0
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