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. 2016 Feb 15;49(3):573–581. doi: 10.1021/acs.accounts.5b00540

Hybrid Organic–Inorganic Perovskites on the Move

David A Egger †,*, Andrew M Rappe ‡,*, Leeor Kronik †,*
PMCID: PMC4794706  PMID: 26878152

Conspectus

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Hybrid organic–inorganic perovskites (HOIPs) are crystals with the structural formula ABX3, where A, B, and X are organic and inorganic ions, respectively. While known for several decades, HOIPs have only in recent years emerged as extremely promising semiconducting materials for solar energy applications. In particular, power-conversion efficiencies of HOIP-based solar cells have improved at a record speed and, after only little more than 6 years of photovoltaics research, surpassed the 20% threshold, which is an outstanding result for a solution-processable material. It is thus of fundamental importance to reveal physical and chemical phenomena that contribute to, or limit, these impressive photovoltaic efficiencies.

To understand charge-transport and light-absorption properties of semiconducting materials, one often invokes a lattice of ions displaced from their static positions only by harmonic vibrations. However, a preponderance of recent studies suggests that this picture is not sufficient for HOIPs, where a variety of structurally dynamic effects, beyond small harmonic vibrations, arises already at room temperature.

In this Account, we focus on these effects. First, we review structure and bonding in HOIPs and relate them to the promising charge-transport and absorption properties of these materials, in terms of favorable electronic properties. We point out that HOIPs are much “softer” mechanically, compared to other efficient solar-cell materials, and that this can result in large ionic displacements at room temperature. We therefore focus next on dynamic structural effects in HOIPs, going beyond a static band-structure picture. Specifically, we discuss pertinent experimental and theoretical findings as to phase-transition behavior and molecular/octahedral rearrangements. We then discuss atomic diffusion phenomena in HOIPs, with an emphasis on the migration of intrinsic and extrinsic ionic species. From this combined perspective, HOIPs appear as highly dynamic materials, in which structural fluctuations and long-range ionic motion have an unusually strong impact on charge-transport and optical properties. We highlight the potential implications of these effects for several intriguing phenomenological observations, ranging from scattering mechanisms and lifetimes of charge carriers to light-induced structural effects and ionic conduction.

1. Introduction

Hybrid organic–inorganic perovskites (HOIPs), the structure of which is defined below, are materials which are solution processable, comprise earth-abundant elements, and yet exhibit outstanding semiconducting and light-absorption properties (see refs (1−3) for overviews). These features render HOIPs promising for (opto-) electronic applications in general and photovoltaic (PV) devices in particular,4−7 as power-conversion efficiencies surpassed 20% after some 6 years of PV research.8 The microscopic origin of this success lies partly in the electronic structure of HOIPs, which is well understood:9,10 it resembles that of a good inorganic semiconductor, with optical gaps that can be close to optimal for solar absorption, small exciton binding energies, and low effective masses. This combination allows for efficient charge-carrier generation, transport, and collection.

In this Account, we first review the static structural and electronic properties of HOIPs. We then show that the static band-structure picture, possibly with harmonically vibrating ions, still leaves important phenomena, for example, light-induced effects or hysteresis in the current–voltage curves of HOIP solar cells, unexplained. We therefore focus on dynamic structural effects in HOIPs, highlighting important molecular and octahedral rearrangements, as well as ion migration phenomena, discuss how those could explain some of the remaining mysteries of HOIPs, and suggest further routes for progress.

2. Crystal Structure, Bonding, and Phase Transitions of HOIPs

Perovskites possess the formula ABX3, where A, B, and X are ions that obey size restrictions quantified by the Goldschmidt tolerance factor:11

2.

where rA, rB, and rX denote the ionic radii. When t is close to unity, the “aristotype” ideal cubic perovskite structure can form. It consists of corner-shared BX6 octahedra and A-cations occupying the voids between them. When t significantly deviates from unity, perovskite motifs with edge- and face-sharing octahedra may be favored over the corner-sharing structure.12

Perovskites can adopt a wide variety of phases that typically involve small symmetry-breaking distortions of the aristotype,13 for example, octahedral tilts (characterized with Glazer’s notation14), A- and B-cation displacements, and their combinations. Many crystal structures and space groups are accessible from the aristotype, including polar space groups, that is, ferroelectric and antiferroelectric ones.15

In HOIPs, the A-site is occupied by a small organic cation (typically methylammonium, MA). Most HOIPs studied today have a divalent metallic atom (e.g., Pb or Sn) on the B-site and halogens (I, Br, Cl) on the X-sites. Figure 1a shows a schematic of the prototypical MAPbI3,16 described by Weber long ago,17 including the tetragonal and orthorhombic structures it adopts at lower temperatures (determined by X-ray diffraction, XRD).18 The molecular cation has a dipole moment and a symmetry lower than that of the (ideal) BX6 octahedron. Neighboring molecules in HOIPs can, in principle, align in different ways over various length scales. Therefore, while t can still be ≈1, one expects molecule-based symmetry breaking leading to a rich structural variety accessible at a given temperature. Indeed, density functional theory (DFT) calculations have shown that close to equilibrium many different structures are locally stable and differ in energy by only a few meV/formula unit.19−22 Phase diagrams and associated static and dynamic structural features of HOIPs can thus be particularly rich and interesting.

Figure 1.

Figure 1

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(a) Schematic representation of methylammonium lead iodide (MAPbI3) and its crystal structures at different temperatures.16 Upper (lower) panels show side (top) views. Dashed lines represent unit cell boundaries. Phase-transition temperatures were taken from ref (18). Adapted with permission from ref (16). Copyright 2015 American Physical Society. (b) Total and projected density of states of tetragonal MAPbI3, showing orbital-specific contributions.90 Reproduced with permission from ref (90). Copyright 2014 The Royal Society of Chemistry. (c) Graphical summary of pairwise dispersive energies, EvdWAB, between atomic sites A and B in the unit cell of MAPbI3 (left panel), MAPbBr3 (center panel), and MAPbCl3 (right panel).26 Reproduced with permission from ref (26). Copyright 2014 American Chemical Society.

This diversity can be linked to cohesion in HOIPs, for which ionic bonding is a major driving force. This manifests itself in the electronic structure of HOIPs (e.g., MAPbI3, see Figure 1b),23,90 characterized by an anionic (iodide) valence and cationic (lead) conduction band.9,10,23,90 The oxidation state of the X-ions in halide-based HOIPs is −1 (instead of −2 in oxide perovskites), and the Madelung potential is significantly less binding for HOIPs than for oxides.24 Again using MAPbI3 as an example, Pb and I also interact covalently to some extent, especially due to interaction of lone-pair Pb 6s with I 5p electrons, contributing to the top of the valence band (Figure 1b).9,10,23,90 The species in HOIPs have large polarizabilities and can support significant dispersive interactions. Therefore, ordinarily weak interactions, notably van der Waals (vdW) interactions, and hydrogen bonding supported by the organic cation, also play an important role for the structure of HOIPs, especially given relatively weak electrostatic binding.25−27 Accordingly, first-principles calculations demonstrated the importance of vdW-interactions among the inorganic atoms25−27 and H-bonding between the organic moieties and inorganic octahedra (Figure 1c).26

Significant contributions of the organic cation to the HOIP band structure are found only at several eV below the valence band maximum (Figure 1b),9,10,23,90 that is, beyond H-bonding there is essentially no hybridization between the organic and inorganic part of HOIPs. Instead, the molecule acts as a scaffold, big enough so that lead-halide perovskites can form (with favorable t) close to room temperature. The large size of MA is important, because the analogous all-inorganic, CsPbI3, adopts the edge-sharing NH4CdCl3 structure at ambient conditions rather than the cubic perovskite one, with a significantly different electronic structure that is less favorable for photovoltaics.3

The above considerations suggest that chemical bonds are not stiff in HOIPs. Indeed, lattice constants of ideal cubic MAPbX3 span 5.7–6.3 Å, significantly larger than the 3.8–4.2 Å common for oxide perovskites.13 Furthermore, experimental and theoretical Young and bulk moduli of different HOIPs26,28−31 are between ≈10 and 25 GPa, that is, at least tens of GPa smaller than values for typical oxide perovskites or inorganic semiconductors. This means that HOIPs easily accept changes to their equilibrium bond lengths, providing for large conformational freedom compared to other semiconductors with similar electronic properties.

The rich structural diversity, together with the material flexibility of HOIPs, may lead to different phases being present locally (i.e., multiple variants of the aristotype coexist) in HOIP films and surfaces. Indeed, theoretical work showed that XRD patterns are compatible with different coexisting phases32 and that on a sub-ps time scale systems can deviate from the ideal structure.33 Moreover, the thermodynamic stability of HOIPs, quantified by the segregation energy of ABX3 → AX + BX2, is very low.34 Therefore, regions containing a fraction of the binary components (BX2 and/or AX) and other complexes are another possibility discussed in the literature.35 Practically, the local presence of secondary phases is especially relevant to HOIPs in which phase transitions can occur around room temperature, notably MAPbI3 (Figure 1a).

3. Molecular Rotations and Octahedral Distortions

A peculiar aspect of HOIPs, compared to traditional semiconductors, is that the organic molecule may undergo significant rearrangements in the ideal crystal. This phenomenon was invoked for MAPbX3 by Weber already in 1978:17 the nonspherical MA apparently does not distort the lead halide octahedra and significant MA motion explains the MA appearing to be spherical on average.17

To understand molecular rearrangements microscopically, recall that the potential energy surface of the molecule is influenced by interactions with neighboring BX6 octahedra and molecule–molecule coupling. Dipole–dipole interactions of molecules with distorted metal-halide octahedra could also play a role for lower-symmetry HOIP structures, with molecule–molecule coupling expected to be largely due to (screened) dipole–dipole interactions. Typical organic cations, notably MA, allow for several low-energy orientations as part of the perovskite structure, for example, aligned with corners, edges, or faces of the inorganic cages (Figure 2a).36,37 Theoretically, energy barriers for molecular rotation can be as low as several meV,10,19,20 suggesting significant movement of molecules at finite temperatures. Indeed, dielectric response and Raman spectroscopy results were interpreted by light exposure inducing or enhancing molecular rearrangements.38,39 Specific experimental evidence for molecular rearrangements is strong. Early measurements of 2H and 14N solid-state nuclear magnetic resonance spectra indicated rapid (sub-ps correlation times) molecular reorientations for the high-temperature phases of deuterated MAPbX3, essentially independent of anion identity,40 as confirmed recently.41 Temperature-dependent dielectric response measurements of MAPbX3, analyzed using the Debye model, suggested dynamic disorder of MA dipoles involving ps relaxation.18 Dynamic disorder was also found in Cs-based all-inorganic crystals, suggesting that in lead-halide perovskites dynamic disorder is relevant irrespectively of the A-site cation.42

Figure 2.

Figure 2

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(a) Possible minimum-energy orientations and associated reorientation pathways, indexed from (i) to (v), for MA+ in MAPbI3, based on rotation (2) in panel (b). (b) Two modes of rotation of MA+: (1) rotation of CH3 or NH3; (2) rotation of MA+, swapping locations of C and N. Reproduced with permission from ref (37). Copyright 2015 Macmillan Publishers Ltd.: Nature Communications. (c) Temperature-dependent mean-squared displacement of hydrogen atoms in MAPbBr3 from neutron scattering. Reproduced with permission from ref (47). Copyright 2015 American Physical Society.

Combining quasi-elastic neutron scattering measurements with Monte Carlo simulations for MAPbI3, Leguy et al. suggested two primary molecular motions dominant at room temperature (Figure 2b):37 Motion of CH3 and NH3 about the C–N axis, or of the entire MA unit by rotation perpendicular to the C–N axis, which can occur via several possible pathways (Figure 2a). These two processes have different activation energies and thus occur at somewhat different time scales: the CH3- or NH3-related events occur at a possibly sub-ps time scale, whereas the realignment of the entire molecular unit is slower (3–14 ps), of similar magnitude to that deduced from molecular dynamics (MD)43,44 and recent experiments.45,46 One can therefore conclude that at room and higher temperatures, molecules in HOIPs have large conformational freedom. This agrees with Weber’s analysis:17through extensive rotational dynamics of the molecular unit, the overall symmetry of HOIP crystals is increased. More restricted molecular rotations correspond to a lower overall symmetry of the molecular unit and can be interpreted as symmetry-breaking distortions from the ideal thermally symmetrized A-site.

Consistent with this interpretation, molecular rotation in HOIPs was found to be strongly temperature-dependent, as deduced from the mean-squared displacement of the hydrogen atoms extracted from temperature-dependent neutron scattering (Figure 2c).47 Once HOIPs are cooled and undergo phase transitions into tetragonal and orthorhombic structures, hydrogen displacements become smaller, indicating that rotations are restricted: experimental and theoretical results have shown that at lower temperatures molecular orientations are confined to high-symmetry directions of the crystal40,44 and reorientation energy barriers are enhanced.21

As T is lowered, the AX12 cuboctahedra shrink (due to BX6 octahedral rotations), so there is less space for molecular rearrangements. It is therefore reasonable that molecular and octahedral rearrangements are acting in concert: molecules reorient over short times and, because BX6 distortions and molecular rotations are coupled, bond lengths and angles of the BX6 octahedra also change significantly.20,32,37 In this context, consider the related HOIP MAPbBr3, for which molecular rotations have been described as coupled to BX6 octahedral distortions, resulting in coupling of order–disorder and displacive phase-transitions.47 Interestingly, for MAPbI3, phonon spectra also indicate significant coupling between molecular and PbI6-related modes.16

Such cooperative action of molecular rotations and octahedral distortions suggests that HOIPs are dynamic materials: a snapshot of a single structure cannot account for important dynamical effects and, thus, does not provide sufficient insight into their properties. For example, first-principles calculations showed that the band gap magnitude, and even whether it is direct or slightly indirect, can change with molecular rotation.20 This is interesting, given that the molecular electronic states do not contribute to the frontier levels in HOIPs (vide supra). However, consider that for a related Sn-based HOIP, molecular rearrangements influence the band structure48 through electrostatic and hydrogen-bonding effects on the inorganic ions, which are primarily responsible for the band-edge electronic structure.9,10,23,90 Therefore, structural fluctuations at room temperature can induce dynamical changes in important electronic-structure parameters, for example, band gap, effective masses, and possibly carrier lifetimes. Such effects have been reported also for Pb-based HOIPs based on MD, which at 320 K predict time-dependent band gap changes of 0.1–0.2 eV.32,33

We speculate that the interplay of electronic and structural dynamical phenomena can result in a number of interesting electron–lattice coupling effects in HOIPs.49 For example, scattering of charge-carriers by acoustic phonons may help understand some as-yet unexplained results for modest carrier mobilities of HOIPs.49,50 Polaronic effects in HOIPs could also be important and were invoked to explain low mobilities,49,51,52 light-induced changes of the low-frequency dielectric response,39 and photostability due to coupling of light-generated carriers to polar fluctuations in the lattice.53

Molecular rotations, octahedral distortions, and phase transitions are closely related to ferroelectricity, which for HOIPs is possible in principle because lower-temperature phases can crystallize in polar space groups.2 Ferroelectricity in HOIPs has been studied based on Berry phase calculations, predicting polarization of ≈4–12 μC/cm2 for the lower-temperature phases of MAPbX3 (X = I, Br, Cl),22,54,55 significantly lower than values reported for ferroelectric oxides, for example, BaTiO3. Measuring ferroelectric hysteresis in HOIPs is challenging, given their small band gap and relatively large number of mobile carriers, which can result in leakage currents.13,22 The ferroelectric nature of HOIPs is therefore currently disputed, with reports claiming either presence56 or absence22,57 of ferroelectricity. Interestingly, Zhou et al.21 predict that in MAPbI3 different molecular orientations have a larger impact on the polarization than lead displacements.

Given the molecular flexibility and rich structural diversity of HOIPs, large ferroelectric domains in HOIPs could indeed be difficult to stabilize over a sufficiently long time at room temperature. But one could also consider short-lived ferroelectric domains in HOIPs.24,36 Interestingly, long-range electrostatic interactions of molecular dipoles can induce polar domains via regions of (partially) aligned dipoles.36,58 Such domains can alter the HOIP band gap,54 separate electron and hole wave functions (Figure 3a),58 and suppress carrier recombination.59,60 Polar domains can also serve as channels for segregated transfer of electrons and holes, for example, by domain-wall formation (Figure 3b),24,36,54 which could partly explain the long carrier lifetimes of HOIPs. Ferroelectric phenomena in principle could also help explain the hysteresis observed in HOIP solar cells,61 although recent results put this into question.37 Furthermore, ferroelectricity can give rise to a bulk PV effect, also discussed for HOIPs.62,63 The possibly strong impact of ferroelectricity and polar domains on charge-transport calls for establishing more definitive experimental evidence for its absence or presence in HOIPs, at best combined with advanced theory that can account for the structural fluctuations.

Figure 3.

Figure 3

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(a) Isosurface representation of the charge densities associated with the conduction band minimum (CBM) and valence band maximum (VBM) in a 20736-atom supercell of MAPbI3 with MA randomly oriented along the eight ⟨111⟩ directions.58 Reproduced with permission from ref (58). Copyright 2015 American Chemical Society. (b) Schematic illustration of steps in the electrostatic potential, causing electron–hole separations in an array of uncharged domain walls (UCDWs).54 Reproduced with permission from ref (54). Copyright 2015 American Chemical Society.

4. The Role of Ion Migration

For HOIPs, as for any semiconductor, knowledge of defects is crucial for understanding the electrical properties. Several defect-related observations have been reported, including very long charge-carrier diffusion lengths and low trap densities.64−66 Here, we focus on migration of ionic defects, invoked to explain phenomenological observations including hysteresis61,67,68 (via ion-blocking contacts), switchable PV effects,69,70 and light-induced changes in structural38,69−72 and dielectric properties.39 Whether (intrinsic or extrinsic) ions can diffuse at room temperature is, naturally, also relevant for material stability.

For some inorganic lead-halide perovskites73 and lead dihalides,74 ion migration has been investigated decades ago. These conduct anions through vacancies, with activation energies of ≈0.2–0.4 eV. For HOIPs, ionic conduction was proposed by Dualeh et al. based on impedance spectroscopy.75 Recently, several experimental and theoretical studies presented more detailed evidence for migration of intrinsic ionic defects in HOIPs. Yang et al. measured temperature-dependent conductivities of MAPbI3, showing an activation energy of ≈0.4 eV.76 Using impedance spectroscopy and galvanostatic DC-measurements, they argued that MAPbI3 is a mixed ionic-electronic conductor, with surprisingly large ionic conductivities in the dark, even surpassing the electronic ones.76 Yuan et al. reported that the MAPbI3 conductivity in the dark consists of two regions (Figure 4a):77 the first (100–270 K) exhibits activation energies of ≈40 meV, assigned to electronic carriers, and the second (290–350 K) 10-fold larger ones (≈0.4 eV), assigned to ionic migration.77

Figure 4.

Figure 4

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(a) Arrhenius plot of the electrical conductivity of MAPbI3 in the dark (blue) and under illumination (red).77 Reproduced with permission from ref (77). Copyright 2015 Wiley-VCH Verlag GmbH & Co. (b–d) Schematics of ionic diffusion mechanisms in MAPbI3: migration of I vacancies (b),78 MA vacancies (c),78 and hydrogen interstitials (d).83 Panels (b) and (d) show pathways with several geometries. Reproduced with permission from ref (78). Copyright 2015 Macmillan Publishers Ltd.: Nature Communications. Adapted from ref (83). Copyright 2015 Wiley-VCH Verlag GmbH & Co.

While these two studies present independent experimental evidence for ion migration with similar activation energies, they disagree on the diffusion constant (by some 3 orders of magnitude) and over which ion moves. Yang et al. used a solid-state Pb|MAPbI3|AgI|Ag electrochemical cell and observed PbI2 formation at the Pb|MAPbI3 interface under bias, indicating that I– is the fastest intrinsic defect (Figure 4b).76,78 In contrast, using photothermal induced resonance microscopy, Yuan et al. concluded that MA+ migrates (see Figure 4c)78 when the device is electrically poled.77 They recently reported evidence for iodide vacancy migration at elevated temperatures, relevant in the decomposition of MAPbI3 under small electric fields.79

Further results supporting either migration model have been found. It was argued that under illumination of mixed iodide-bromide films, halides can segregate into regions that are structurally different from the rest of the film (cf. section 2), influencing its optical properties.72 However, it was recently found that the organic cations (MA and formamidinium) can be rapidly exchanged, implying that organic cations may also be mobile.80 Because HOIPs can easily deviate from their ideal bulk structure, as emphasized throughout, dynamical disorder, grain boundaries, and other nonidealities can also affect ion migration.

Recently, ion diffusion has been examined theoretically, allowing the identification of minimum energy paths and barriers for ideal structures. Calculations of defects and their diffusion are highly sensitive to the underlying theoretical and numerical framework. For HOIPs, migration barriers of 0.1–0.6 eV are found for iodide vacancies and of 0.5–0.9 eV for MA+ migration,78,81,82 which are quite large deviations. Thus, theoretically there is still significant uncertainty over which ions actually migrate.

We recently suggested an additional mechanism for ion migration: diffusion of hydrogen impurities, for example, protons (Figure 4d).83 Hydrogen is an important extrinsic defect in inorganic semiconductors and some oxide perovskites are well-known proton conductors.84 In HOIPs, hydrogen could therefore exist as extrinsic (introduced, e.g., via H2O-induced partial decomposition of the HOIP, as speculated in ref (24)) or as intrinsic defects (through the organic unit). Our calculations predicted low migration barriers (∼0.1–0.2 eV) for H+ in MAPbI3 and showed that diffusion mechanisms resemble those discussed for oxide proton conductors, involving transient H-bonds (Figure 4d).83 We showed that differently charged defects prefer different sites (to be near ions of opposite charge), allowing for ionization-enhanced defect migration. This may be relevant for other defects and charging scenarios and has been supported by recent experiments.85 Given that hydrogen impurities are difficult to control, H migration can complicate the interpretation of conductivity measurements, especially in light of recent findings on H2O adsorption and associated degradation mechanisms.85−89

5. Summary and Conclusions

In this Account, we provided an overview of structural dynamics of hybrid organic–inorganic perovskites (HOIPs), a family of materials that is highly interesting for applications in (opto)electronics and also puzzling from a scientific perspective. This is especially so considering a number of experimental observations that are atypical in the context of other highly efficient materials for PV.

We discussed crystal cohesion and bonding, showing that it is relatively weak, based on the mechanical properties of HOIPs and on first-principles calculations. This is especially relevant given that perovskites can access many lower-symmetry structures from an aristotype, which for HOIPs implies a large pool of structural motifs accessible at room temperature. In thin films, secondary structural phases could therefore exist. We discussed several findings on rotational dynamics of molecular cations in HOIPs, highlighting their strong connection with octahedral distortions, which can influence the electronic properties of HOIPs. Together with the notion of locally fluctuating regions bearing secondary phases, one may envision domains that can locally facilitate (or hinder) charge-carrier transport and/or separation.

Finally, more and more evidence points toward significant migration of ionic species in HOIPs. It is unclear which species is/are moving, but experimental and theoretical studies proposed several different defect models, including halide and molecular vacancies, as well as hydrogen impurities.

From this perspective, HOIPs emerge as materials that are highly flexible mechanically and structurally dynamic. Given the potentially strong impact of structural fluctuations on charge-transport and optical properties, it appears necessary to call for a change in the perception of HOIPs: Envisioning them in one specific structure at a given temperature, distorted only by small and harmonic changes, clearly falls short of recognizing dynamical phenomena as an outstanding characteristic of these materials.

We conclude that HOIPs are “on the move” and hope that our emphasis on this issue will trigger further experimental and theoretical work to establish a microscopic understanding of their structural dynamics. We believe that this will be relevant to open questions in the field, some of which we have outlined throughout this Account. It may furthermore shine light on an important and curious property: that a high-quality semiconductor can be processed from solution by simple means.

Acknowledgments

D.A.E. and L.K. were supported by a research grant from Dana and Yossie Hollander and by the Austrian Science Fund (FWF):J3608-N20. A.M.R. was supported by the US Office of Naval Research, Grant N00014-14-1-0761.

Biographies

David A. Egger received his Ph.D. in Physics in 2013 from Graz University of Technology, Austria. Currently, he is a Postdoctoral Fellow at the Department of Materials and Interfaces at the Weizmann Institute of Science, supported by a Schrödinger Fellowship of the Austrian Science Fund. In 2014, he received the Koshland Prize of the Weizmann Institute of Science.

Andrew M. Rappe received his Ph.D. in Physics and Chemistry in 1992 from MIT. He is Professor of Chemistry and Professor of Materials Science and Engineering at the University of Pennsylvania, as well as founding co-director of the VIPER Program. He is a Fellow of the American Physical Society, a Sloan Fellow, and a Dreyfus Teacher-Scholar. He was awarded a Weston Visiting Professorship at the Weizmann Institute of Science in 2014.

Leeor Kronik obtained his Ph.D. in Physical Electronics in 1996 at Tel Aviv University. Presently, he leads a group devoted to the quantum theory of real materials at the Department of Materials and Interfaces, Weizmann Institute of Science. He is a Fellow of the American Physical Society and a Member of the Israeli Young National Academy and has received the Young Scientist Award of the Israel Chemical Society (2010) and the Young Scientist Krill Prize of the Wolf Foundation (2006).

The authors declare no competing financial interest.

Special Issue

Published as part of the Accounts of Chemical Research special issue “Lead Halide Perovskites for Solar Energy Conversion”.

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