Abstract
The development of high efficiency perovskite solar cells has sparked a multitude of measurements on the optical properties of these materials. For the most studied methylammonium(MA)PbI_{3} perovskite, a large range (6–55 meV) of exciton binding energies has been reported by various experiments. The existence of excitons at room temperature is unclear. For the MAPbX_{3} perovskites we report on relativistic BetheSalpeter Equation calculations (GWBSE). This method is capable to directly calculate excitonic properties from firstprinciples. At low temperatures it predicts exciton binding energies in agreement with the reported ‘large’ values. For MAPbI_{3}, phonon modes present in this frequency range have a negligible contribution to the ionic screening. By calculating the polarization in time from finite temperature molecular dynamics, we show that at room temperature this does not change. We therefore exclude ionic screening as an explanation for the experimentally observed reduction of the exciton binding energy at room temperature and argue in favor of the formation of polarons.
Introduction
In the last three years metal halide perovskites have come up as very promising solar cell materials^{1,2,3}. Because of their relatively simple production procedure and high photovoltaic efficiency, they bear the potential of becoming competitive with current silicon based solar cells. The materials have an OMX_{3} perovskite structure (Organic(O), Metal(M), Halide(X)) and depending on the temperature up to three different crystal phases. The most frequently studied material is MAPbI_{3}. At temperatures above 333 K, the lead and iodine atoms form a cubic perovskite structure enclosing a methylammonium (MA) molecule^{4}. Combinations with the halogens Cl and Br can also be made and result in perovskite structures with different volumes and larger band gaps, not ideally suited for solar applications. According to early experimental measurements from the 1990s and 2000s, the MAPbX_{3} perovskites are semiconductors with optical band gaps (Δ_{opt}) ranging between ~1.6–3.1 eV^{5,6,7,8}. The optical gap is slightly lower than the fundamental electronic band gap (Δ), because of the electronhole (eh) interaction present in the excited system. With the emergence of very efficient perovskite solar cells, the mechanism behind the material’s good energy conversion rate has become a focus of research. In this regard, one important issue is the relatively large exciton binding energies (E_{xb}) reported for these materials, 6–55 meV for MAPbI_{3}^{5,7,9,10,11,12,13,14,15} and 76 meV^{7} for MAPbBr_{3}. Intriguingly, many reported values are higher than k_{B}T, which should make it difficult for electrons and holes to separate after excitation. It is then a mystery why these materials are so efficient in converting solar energy to power. As a solution to this puzzle, it has been proposed that ionic contributions from the PbI_{3} framework and the rotational freedom of MA molecules contribute to the screening properties, thereby reducing the exciton binding energy^{16,17,18,19}. Alternative explanations invoke the formation of polarons, quasiparticles dressed by the ionic lattice that might lower the band gap^{19} below the excitonic onset. Furthermore, recent experiments indicate that temperature also plays a role. Y. Yamada et al.^{9} measured a reduction of E_{xb} from ~30 meV at 13 K to ~6 meV at 300 K, and likewise, A. Miyata et al.^{10} measured a value of 16 ± 2 meV in the low temperature orthorhombic phase, but only a few meV at room temperature. Whether ionic screening does or does not affect E_{xb} is under debate^{20}. The large range of the reported E_{xb} values indicate the need for a theoretical description. In this work we report about first principles calculations on these ionic systems and address excitons in their interplay with polar phonons.
The theoretical modeling of metal halide perovskites is extremely challenging as it involves the treatment of several subtle, but important effects that are difficult to compute accurately. The first issue is the lattice structure to consider. Temperature dependent crystal structures have been determined^{4}, but uncertainties in the orientation of the organic part prevent an unequivocal structural resolution. The structural characteristics have been the subject of numerous studies based on different (Local Density, Generalized Gradient, van der Waals) DFT approximations^{21,22,23,24,25,26}. For the cubic phase of MAPbI_{3}, most calculations predict lattice constants in good to excellent agreement with experiment. However, differences in the orientation of the molecule and the resulting deformation of the unit cell have been reported. We address this issue here (i) by performing global search for minimum energy structures, (ii) calculating excitons for various unit cells, (iii) and finite temperature simulations. Second, the presence of heavy elements requires to consider relativistic effects including spinorbit coupling (SOC)^{27,28}. Furthermore, for a quantitative description of the electronic structure, it is essential to calculate manybody quasiparticle energies e.g. in the framework of the GW approximation^{27,29,30,31}. Finally, to evaluate E_{xb} and calculate accurate optical spectra, it is necessary to account for the eh interaction. This can be done by the BetheSalpeter equation (BSE) following GW calculations^{31,32}— a computationally exceedingly challenging endeavor if spinorbit coupling is taken into account. It is therefore not astonishing that previous work has often given unsatisfactory results. Several quasiparticle GW calculations have been reported recently^{27,29,30,31}, but a fully relativistic treatment including spinorbit interaction was only performed in refs 27 and 33. Although, BSE calculations have been reported, these often neglect relativistic effects^{31,32} and report much too large binding energies. Even if relativistic effects are accounted for, the binding energies (E_{xb} = 0.153 eV) are at least a factor 3 too large compared to any experimental values^{33}. As we will show here, we can entirely resolve this issue when sampling the Brillouin zone with sufficient accuracy.
Computational method
The firstprinciples calculations use a planewave basis and the projector augmented wave (PAW) method^{34} as implemented in the vasp code^{35,36,37}. For structure determination, the PBEsol (Perdew, Burke, Ernzerhof modified for solids)^{38} functional was used, if not otherwise noted. Cross checks were also performed using van der Waals corrected functionals, specifically, the PBED3 method of Grimme^{39} finding no relevant differences for the properties reported here. The MAPbX_{3} cubic perovskite unit cells (12 atoms per cell) were constructed starting from the cubicphase of MAPbI_{3} determined by Xray diffraction^{4} and seeking the global energy minimum by simulated annealing. To determine candidate structures, molecular dynamics simulations were performed with a linear decrease of the temperature from 800 K to 500 K in 50000 steps of 1.5 fs. Approximately every ~1000 steps a snapshot was taken and fully relaxed. This process was repeated from the lowest energy structure yet found. A unique global minimum was found for all considered materials (See Supplementary Materials). In the subsequent electronic structure calculations (GW and BSE), SOC was fully included, and for Pb the 5s^{2}5p^{6}5d^{10} orbitals were included in the valence^{27}. Gaussian smearing with σ = 0.05 eV was used to broaden the oneelectron levels. Manybody effects were accounted for by first calculating PBE orbitals, and then determining the quasiparticle energies and fundamental gaps in the GW_{0} approximation^{40,41}. Here the one electron energies in G were iterated until the quasiparticle energies are converged, while keeping W_{0} fixed at the DFTRPA level^{42}. About 2100 empty bands on a 4 × 4 × 4 Γcentered kpoint grid and 128 points on the frequency grid are needed to obtain well converged band gaps.
To determine the optical properties, the BetheSalpeter equation for the polarizability^{43,44,45} was solved. The common TammDancoff approximation^{46}, 32 occupied and unoccupied KS orbitals, the W_{0} of the preceding GW_{0} calculations, and 6 × 6 × 6 kpoints centered on a low symmetry kpoint were used.
To obtain kpoint converged values for the exciton binding energy E_{xb} at least 20 × 20 × 20 kpoints are, however, required. These BSE calculations, were performed using only 2 (un)occupied orbitals and fitting W_{0} to a model dielectric function^{47} that depends parametrically on the macroscopic dielectric constant determined in the previous BSE calculations with few kpoints. Since even GW calculations are prohibitive for so many kpoints, we use PBE calculations and applied a scissor technique to raise the unoccupied KS eigenvalues (compare Fig. 1). At these dense kpoint grids, the E_{xb} becomes linearly dependent on the inverse of the total number of kpoints^{48}. The E_{xb} values reported in this work are therefore obtained by linear extrapolation to obtain the limit of the infinitely dense kpoint grid (See Supplementary Materials).
The effect of different molecular orientations on the exciton binding energy have been assessed by BSE calculations on low energy configurations of the FASnI_{3} and MAPbI_{3} super cells. In addition, we have constructed a super cell for FASnI_{3}. These structures were acquired by taking snap shots from Parallel Tempering Molecular Dynamics (PTMD) calculations at 300 K. The structures are the lowest energy configurations from the PTMD trajectory and were relaxed into their instantaneous ground state, while keeping the volume and cell shape fixed to the experiment. The structure is a randomly picked configuration at 300 K from a separate PTMD calculation and was not relaxed. In the structures the molecular dipoles are orthogonally orientated w.r.t. each other and in the structures all the molecular dipoles have a different orientation. The same BSE calculation procedure was used as before, but the screening parameters and GW_{0} gap were not calculated; the values for the unit cell were used instead. This is a reasonable approximation, since calculation of the screening in the computationally more efficient random phase approximation shows little difference in electronic screening for different unit cells and different molecular orientations.
Details of the finite temperature dielectric function calculations are presented in the results section.
Results
In Fig. 1 (left), the calculated GW_{0} quasiparticle band structures of the three MAPbX_{3} structures are shown. The band gap at the R points is indicated and is in excellent agreement with experiment^{5,6,7,8}. SOC shifts the band gap minimum to R′ making it slightly indirect^{30}. The exciton wave function is expressed in an electronhole product basis, . The first eigenstate of the generalized BSE eigenvalue problem^{45} is visualized by plotting as a fat band structure. On the right hand side of Fig. 1 a zoomin of the region close to R is made. It shows that the exciton is very localized in kspace, primarily consisting of states at the band extrema. Going from iodine to chlorine, the dispersion flattens (effective electron/hole masses increase), the band gap increases and, as a result, the extent of the exciton in kspace increases. The corresponding parameters are tabulated in Table 1. We have calculated the corresponding exciton binding energies also in the WannierMott (WM) model for screened Coulomb interacting eh pairs in parabolic bands: , with the effective mass of the eh pair, ε_{∞} the high freq. dielectric constant and R_{∞} the Rydberg constant. Since we use the SOC split “RashbaDresselhaus”^{49} band structure in the BSE method, we can test the validity of the simple parabolic dispersion assumed in the WM model. We see (Table 1) that WM gives the correct order of the eh interaction, however it results in a different ratio between I:Br and Br:Cl, which can not be trivially explained by small errors in μ or ε_{∞}.
An important question is, whether the ionic contributions to the screening can be disregarded in the BSE calculations. To explore this point, Fig. 2 shows the sum of the ionic and electronic contribution to the dielectric function at 0 K, ε(ω), with the ionic contribution calculated using density functional perturbation theory (DFPT)^{50,51,52}. A sizable increase of the static dielectric constant (ε_{0}) compared to the ‘ionclamped’ high frequency dielectric constant (ε_{∞}) is found. The increase comes from optically active phonon modes below 20 meV (see Im ε_{p}(ω)), clearly displaying the ionic nature of this material. However, the phonon modes present in the relevant energy window around E_{xb} ≈ 45 meV (see inset) are practically not active.
Since the exciton binding seems to change with temperature, the second intriguing question is whether the screening changes at finite temperature. To explore this, we have developed a novel scheme to evaluate the dielectric ionic response at finite temperature that we briefly describe in this section (a more detailed description will be presented in a future work). The idea is inspired by methods usually used to determine the electronic contributions to the screening in timedependent DFT^{53}. Well equilibrated finite temperature ensembles are subjected to a short constant electric field in time Eδ(t) acting on the ions. The δpulse is a natural way of exciting all possible frequencies in the system. The force exerted by this field onto the ions is proportional to , where Z_{α,β} are the Born effective charges evaluated by density functional perturbation theory, and α and β are Cartesian indices^{50}. In the first time step, these forces are added, thereby exciting the ionic system. The issue is to find a suitable way to calculate the induced ionic polarization P(t) caused by the delta peak. Here, we calculate the induced polarization as δP(t) = (P_{+}(t) − P_{−}(t))/2, where P_{+}(t) is the time evolution of the polarization for a positive delta peak Eδ(t), and P_{−}(t) the time evolution of the polarization after a negative delta peak −Eδ(t). The evolving P(t) can in principle be evaluated using the Berry curvature^{54}, but the Berry curvature often jumps discontinuously as the ions move. Hence, we evaluate the change of the polarization from the velocities v_{α}(t) and the Born effective charges Z_{αβ}(t) as . The additional cost is small, since Z(t) varies very slowly and needs to be recalculated only about every 50 time steps. The Fourier transformation of δP(t) is directly related to the ionic polarizability^{55}. We first tested this approach at T = 0 K and found exact agreement with perturbation theory. To obtain reasonably noisefree data at finite temperature, we use a 2 × 2 × 2 super cell and average over 80 starting configurations in order to converge the spectrum. After the δpulse, the system is allowed to evolve in the microcanonical ensemble unperturbed for 3 ps, the short time somewhat limiting the spectral resolution. However, the 80 starting configurations were obtained by a taking independent snapshots every 0.7 ps from a well equilibrated 60 ps long finite temperature MD trajectory. Therefore, we expect most of the dynamics to be sampled. The PBED3 method of Grimme^{39} was used here (although PBEsol results are very similar) and the deuterium mass was used for the hydrogen atoms. This replacement only changes the hydrogen related modes above 100 meV and allows to increase the time step during the simulation.
Clearly, the 300 K finite temperature polarizability (solid red line in Fig. 2) above 20 meV is very similar to the one at T = 0 K (dashed blue line in Fig. 2). The modes are at the same positions but broadened by fluctuations in the cage structure, as well as rotations of the molecules. Below 20 meV some differences are visible, however, in both methods the calculated ε_{0} is close to 30, in excellent agreement with the measured value of 28.8^{56}.
We now discuss the question whether ionic screening should be included in the calculation of the exciton binding energy. The values reported in Table 1 assume a fixed lattice, i.e. a vertical transition. It is well established from the FranckCondon energy diagram that lattice relaxation in the excited state can only decrease the transition energy, i.e. thermal or adiabatic transition energies including relaxation are always below vertical transition energies^{57}. Lattice relaxation therefore can only increase the exciton binding energy, since the fundamental gap minus the transition energy is defined as the exciton binding energy E_{xb}. Whether relaxation needs to be included, i.e. whether the vertical or thermal transition energy is measured experimentally can be disputed, although common wisdom is that optical absorption virtually always measures vertical excitation energies. One argument is that the position of the (dominant) longitudinal optical phonon mode (ω_{LO}) compared to the typical energy scales of the optical absorption determines whether ionic relaxation should be considered. In the effective mass approximation this leads to two extreme cases, , and (ionic relaxation needs to be included)^{58,59}. Since the dominant active phonon modes for MAPbI_{3} are all below 10 meV, we have and the use of an ε_{eff} ≈ ε_{∞} ≈ 6.8 is entirely justified (see Fig. 2 for energies larger than 40 meV). The temperature independence of the ionic screening, furthermore, implies that the observed lowering of the exciton binding energy at elevated temperatures must have a different origin than changes in the ionic screening. In agreement with theory, recent room temperature timeresolved terahertz spectroscopy experiments, indicate a near constant screening ε(ω) = 5.5 in the frequency range of ω = 40–100 meV and E_{xb} = 49 ± 3 meV^{60}.
However, if the exciton binding energy E_{xb} is not lowered by ionic screening, what mechanism then leads to carrier separation at higher temperatures? Our calculations also shed light on this. Individual electrons e^{−} and holes h^{+} can be screened by the lattice, thereby forming ‘dressed’ quasiparticles (QP) known as polarons. Since the mesoscopic WannierMott model was so precise, we again resort to a mesosocopic model, namely, Fröhlich’s theory for large polarons. In this model, polaron formation lowers the QP energy by , with a coupling constant . Using the data from Table 1, a screening of ε_{0} = 30, ε_{∞} = 6, and meV from Fig. 2 we obtain an α of 2.3/2.8. This lowers the QP energy of the electron and hole by 19 and 23 meV, respectively, and hence reduces the QP gap by 42 meV. This means that the charge separated polaronic state is only slightly less stable than the bound exciton. If we further recall that after excitation the electrons and holes are not yet close to the conduction or valence band edges, and that they are both individually scattered by lattice phonons loosing energy but possibly gaining momentum^{61}, it is likely that they will rapidly separate in space and never reach their global groundstate, the bound exciton. Charge separation after optical excitation will be further eased by nonregularities in the electrostatic potential. And nonregularities exist aplenty in MAPbI_{3} at elevated temperatures: the polar MA molecules seem to prefer a short range ferroelectric order causing ferroelectric domains and a strong corrugation of the electrostatic potential^{17}. A possible way to experimentally disentangle polaron formation and such molecular contributions and related corrugations in the potential is to perform control measurements on an OPbI_{3} perovskite with O cations that are non polar, for instance Cs.
We like to comment briefly on the performance of a wider class of perovskites (OMX_{3}). Specifically, we have replaced MA by formamidinium (FA) and Pb by Sn, thereby constructing twelve different perovskites. Their global lowest energy structure was calculated as before by simulated annealing and subsequent relaxation. FA is larger than MA and thereby changes the band gap of the perovskite. FASnI_{3} is a particular interesting candidate, previous work suggests that this is possibly a ferroelectric leadfree alternative for MAPbI_{3}^{49}. In Fig. 3 we show the trend in the exciton binding energies w.r.t. the GW_{0} band gap. Clearly, the halogen species predominantly determines the gap. For each halogen, the strength of the exciton binding energy and the optical gap can be finetuned by varying the molecule or the metal atom. Nevertheless, only iodine based perovskites seem to posses sufficiently small band gaps and exciton binding energies to be suitable for solar cells. An overview of the band gaps calculated at the various level of theory and available experimental data has been presented in Table 2. Over the whole range a good agreement is found between the GWBSE calculations on these small unit cell structures and experimentally observed band gaps. Small discrepancies can be caused by the unit cell approach taken in this work. For those structures, which have not yet been synthesized or for which the band gap has not yet been measured, we put these number forward as predictions.
Discussion
The last point we need to consider is how different molecular orientations influence the results. In a real (super)structure the exciton wave function will span many unit cells with molecules that have different orientations. It has been suggested that the ordering and orientation of the molecules in the lattice aids the eh dissociation process^{17,18,62}. Both the MA and FA molecules have an intrinsic dipole moment and are only weakly bonded to the MX_{3} cage. It is known from Nuclear Magnetic Resonance Spectroscopy measurements that the MA molecules in MAPbX_{3} have the full rotational degree of freedom at room temperature and that reorientation is a fairly rapid process^{63}. However, with a typical reorientation time in the picosecond time scale, it is the slowest screening mechanism present in the OMX_{3} perovskites. To asses the effect of different molecular orientations, BSE calculations have been performed on and cells containing 2 and 4 molecules, respectively. For the and the larger FASnI_{3} cell, the calculated exciton binding energies are 33 and 31 meV, respectively. Compared to the 31 meV predicted for the unit cell, the super cell approach does not give significantly different results for the exciton binding energy. The same holds for MAPbI_{3}, where the cell results in an exciton binding energy of 51 meV, which is only slightly larger than the 45 meV predicted for the unit cell.
Conclusion
Accurate first principles calculations predict exciton binding energies of the order of 50, 70 and 110 meV for MAPbI_{3}, MAPbBr_{3} and MAPbCl_{3}, respectively. The agreement of the WannierMott model with our high level calculations is good, provided that the model parameters are taken from accurate first principles calculations. The large exciton binding energy is clearly at variance with the observed high efficiency of solar cells, but in excellent agreement with most low temperature measurements. The much discussed ionic screening is almost temperature independent and substantially increases ε_{0} from around 6 to 30. However, the optically active modes are too slow (<10 meV) to effectively screen the excitons. For certain, we can rule out that a change of the ionic screening is responsible for the experimentally observed reduction of the exciton binding energy at room temperature. Instead, our calculations predict a different scenario: electrons and holes separate after optical excitation forming two individual polarons, lowering the fundamental gap by 42 meV. This scenario should now be carefully evaluated by experiments, and if validated, offers an intriguing option for the design of novel polaronic solar cell materials.
Additional Information
How to cite this article: Bokdam, M. et al. Role of Polar Phonons in the Photo Excited State of Metal Halide Perovskites. Sci. Rep. 6, 28618; doi: 10.1038/srep28618 (2016).
References
 1.
Green, M. A., HoBaillie, A. & Snaith, H. J. The emergence of perovskite solar cells. Nature Phot. 8, 506–514 (2014).
 2.
Grätzel, M. The light and shade of perovskite solar cells. Nature Mater. 13, 838–842 (2014).
 3.
Kim, H.S., Im, S. H. & Park, N.G. Organolead halide perovskite: New horizons in solar cell research. J. Phys. Chem. C 118, 5615–5625 (2014).
 4.
Stoumpos, C. C., Malliakas, C. D. & Kanatzidis, M. G. Semiconducting tin and lead iodide perovskites with organic cations: Phase transitions, high mobilities, and nearinfrared photoluminescent properties. Inorg. Chem. 52, 9019–9038 (2013).
 5.
Hirasawa, M., Ishihara, T. & Goto, T. Exciton features in 0, 2, and 3dimensional networks of [pbi6]4 octahedra. J. Phys. Soc. Jpn. 63, 3870–3879 (1994).
 6.
Papavassiliou, G. & Koutselas, I. Structural, optical and related properties of some natural three and lowerdimensional semiconductor systems. Synthetic Metals 71, 1713–1714 (1995).
 7.
Tanaka, K. et al. Comparative study on the excitons in leadhalidebased perovskitetype crystals {CH3NH3PbBr3} {CH3NH3PbI3}. Sol. State Comm. 127, 619–623 (2003).
 8.
Kitazawa, N., Watanabe, Y. & Nakamura, Y. Optical properties of ch3nh3pbx3 (x = halogen) and their mixedhalide crystals. J. Mater. Sci. 37, 3585–3587 (2002).
 9.
Yamada, Y., Nakamura, T., Endo, M., Wakamiya, A. & Kanemitsu, Y. Photoelectronic responses in solutionprocessed perovskite ch3nh3pbi3 solar cells studied by photoluminescence and photoabsorption spectroscopy. IEEE J. Photovolt. 5, 401–405 (2015).
 10.
Miyata, A. et al. Direct measurement of the exciton binding energy and effective masses for charge carriers in organicinorganic trihalide perovskites. Nature Phys. 11, 582–587 (2015).
 11.
Sun, S. et al. The origin of high efficiency in lowtemperature solutionprocessable bilayer organometal halide hybrid solar cells. Energy Environ. Sci. 7, 399–407 (2014).
 12.
Saba, M. et al. Correlated electronhole plasma in organometal perovskites. Nature Comm. 5, 5049 (2014).
 13.
Savenije, T. J. et al. Thermally activated exciton dissociation and recombination control the carrier dynamics in organometal halide perovskite. J. Phys. Chem. Lett. 5, 2189–2194 (2014).
 14.
Zhang, Q., Ha, S. T., Liu, X., Sum, T. C. & Xiong, Q. Roomtemperature nearinfrared highq perovskite whisperinggallery planar nanolasers. Nano Lett. 14, 5995–6001 (2014).
 15.
D’Innocenzo, V. et al. Excitons versus free charges in organolead trihalide perovskites. Nature Comm. 5, 3586 (2014).
 16.
Huang, L.y. & Lambrecht, W. R. L. Electronic band structure, phonons, and exciton binding energies of halide perovskites cssncl_{3}, cssnbr_{3}, and cssni_{3}. Phys. Rev. B 88, 165203 (2013).
 17.
Frost, J. M. et al. Atomistic origins of highperformance in hybrid halide perovskite solar cells. Nano Lett. 14, 2584–2590 (2014).
 18.
Even, J., Pedesseau, L. & Katan, C. Analysis of multivalley and multibandgap absorption and enhancement of free carriers related to exciton screening in hybrid perovskites. J. Phys. Chem. C 118, 11566–11572 (2014).
 19.
MenéndezProupin, E., Beltrán Ros, C. L. & Wahnn, P. Nonhydrogenic excitons in perovskite ch3nh3pbi3. arXiv: 1507.00404v1 (2015).
 20.
Filippetti, A., Delugas, P., Saba, M. I. & Mattoni, A. Entropysuppressed ferroelectricity in hybrid leadiodide perovskites. J. Phys. Chem. Lett. 6, 4909–4915 (2015).
 21.
Borriello, I., Cantele, G. & Ninno, D. Ab initio investigation of hybrid organicinorganic perovskites based on tin halides. Phys. Rev. B 77, 235214 (2008).
 22.
Mosconi, E., Amat, A., Nazeeruddin, M. K., Grätzel, M. & De Angelis, F. Firstprinciples modeling of mixed halide organometal perovskites for photovoltaic applications. J. Phys. Chem. C 117, 13902–13913 (2013).
 23.
Brivio, F., Walker, A. B. & Walsh, A. Structural and electronic properties of hybrid perovskites for highefficiency thinfilm photovoltaics from firstprinciples. APL Materials 1, 042111 (2013).
 24.
Feng, J. & Xiao, B. Crystal structures, optical properties, and effective mass tensors of ch3nh3pbx3 (x = i and br) phases predicted from hse06. J. Phys. Chem. Lett. 5, 1278–1282 (2014).
 25.
Egger, D. A. & Kronik, L. Role of dispersive interactions in determining structural properties of organicinorganic halide perovskites: Insights from firstprinciples calculations. J. Phys. Chem. Lett. 5, 2728–2733 (2014).
 26.
Motta, C. et al. Revealing the role of organic cations in hybrid halide perovskite ch3nh3pbi3. Nature Comm. 6, 7026 (2015).
 27.
Filip, M. R. & Giustino, F. gw quasiparticle band gap of the hybrid organicinorganic perovskite ch_{3}nh_{3}pbi_{3}: Effect of spinorbit interaction, semicore electrons, and selfconsistency. Phys. Rev. B 90, 245145 (2014).
 28.
MenéndezProupin, E., Palacios, P., Wahnón, P. & Conesa, J. C. Selfconsistent relativistic band structure of the CH_{3}NH_{3}PBI_{3} perovskite. Phys. Rev. B 90, 045207 (2014).
 29.
Umari, P., Mosconi, E. & Angelis, F. D. Relativistic gw calculations on ch3nh3pbi3 and ch3nh3sni3 perovskites for solar cell applications. Sci. Rep. 4, 4467 (2014).
 30.
Brivio, F., Butler, K. T., Walsh, A. & van Schilfgaarde, M. Relativistic quasiparticle selfconsistent electronic structure of hybrid halide perovskite photovoltaic absorbers. Phys. Rev. B 89, 155204 (2014).
 31.
Castelli, I. E., GarcaLastra, J. M., Thygesen, K. S. & Jacobsen, K. W. Bandgap calculations and trends of organometal halide perovskites. APL Materials 2, 081514 (2014).
 32.
Even, J., Pedesseau, L., Jancu, J.M. & Katan, C. Dft and k.p modelling of the phase transitions of lead and tin halide perovskites for photovoltaic cells. Phys. Stat. Sol. RRL 8, 31–35 (2014).
 33.
Ahmed, T. et al. Optical properties of organometallic perovskite: An ab initio study using relativistic gw correction and bethesalpeter equation. Europhys. Lett. 108, 67015 (2014).
 34.
Blöchl, P. E. Projector augmentedwave method. Phys. Rev. B 50, 17953–17979 (1994).
 35.
Kresse, G. & Hafner, J. Abinitio moleculardynamics for liquidmetals. Phys. Rev. B 47, 558–561 (1993).
 36.
Kresse, G. & Furthmüller, J. Efficient iterative schemes for ab initio totalenergy calculations using a planewave basis set. Phys. Rev. B 54, 11169–11186 (1996).
 37.
Kresse, G. & Joubert, D. From ultrasoft pseudopotentials to the projector augmentedwave method. Phys. Rev. B 59, 1758–1775 (1999).
 38.
Perdew, J. P. et al. Restoring the densitygradient expansion for exchange in solids and surfaces. Phys. Rev. Lett. 100, 136406 (2008).
 39.
Grimme, S., Antony, J., Ehrlich, S. & Krieg, H. A consistent and accurate ab initio parametrization of density functional dispersion correction (dftd) for the 94 elements hpu. J. Chem. Phys. 132, 154104 (2010).
 40.
Hedin, L. New method for calculating the oneparticle green’s function with application to the electrongas problem. Phys. Rev. 139, A796–A823 (1965).
 41.
Hybertsen, M. S. & Louie, S. G. Electron correlation in semiconductors and insulators: Band gaps and quasiparticle energies. Phys. Rev. B 34, 5390–5413 (1986).
 42.
Shishkin, M. & Kresse, G. Implementation and performance of the frequencydependent gw method within the paw framework. Phys. Rev. B 74, 035101 (2006).
 43.
Hanke, W. & Sham, L. J. Manyparticle effects in the optical spectrum of a semiconductor. Phys. Rev. B 21, 4656–4673 (1980).
 44.
Onida, G., Reining, L. & Rubio, A. Electronic excitations: densityfunctional versus manybody green’sfunction approaches. Rev. Mod. Phys. 74, 601–659 (2002).
 45.
Sander, T., Maggio, E. & Kresse, G. Beyond the tammdancoff approximation for extended systems using exact diagonalization. Phys. Rev. B 92, 045209 (2015).
 46.
Dancoff, S. M. Nonadiabatic meson theory of nuclear forces. Phys. Rev. 78, 382–385 (1950).
 47.
Bechstedt, F., Sole, R. D., Cappellini, G. & Reining, L. An efficient method for calculating quasiparticle energies in semiconductors. Sol. State Comm. 84, 765–770 (1992).
 48.
Fuchs, F., Rödl, C., Schleife, A. & Bechstedt, F. Efficient approach to solve the bethesalpeter equation for excitonic bound states. Phys. Rev. B 78, 085103 (2008).
 49.
Stroppa, A. et al. Tunable ferroelectric polarization and its interplay with spinorbit coupling in tin iodide perovskites. Nature Comm. 5, 5900 (2014).
 50.
Wu, X., Vanderbilt, D. & Hamann, D. R. Systematic treatment of displacements, strains, and electric fields in densityfunctional perturbation theory. Phys. Rev. B 72, 035105 (2005).
 51.
Gajdoš, M., Hummer, K., Kresse, G., Furthmüller, J. & Bechstedt, F. Linear optical properties in the projectoraugmented wave methodology. Phys. Rev. B 73, 045112 (2006).
 52.
PérezOsorio, M. A. et al. Vibrational properties of the organicinorganic halide perovskite ch3nh3pbi3 from theory and experiment: Factor group analysis, firstprinciples calculations, and lowtemperature infrared spectra. J. Phys. Chem. C 119, 25703–25718 (2015).
 53.
Walter, M. et al. Timedependent densityfunctional theory in the projector augmentedwave method. J. Chem. Phys. 128, 244101 (2008).
 54.
Resta, R. Macroscopic polarization in crystalline dielectrics: the geometric phase approach. Rev. Mod. Phys. 66, 899–915 (1994).
 55.
Thomas, M., Brehm, M., Fligg, R., Vöhringer, P. & Kirchner, B. Computing vibrational spectra from ab initio molecular dynamics. Phys. Chem. Chem. Phys. 15, 6608–6622 (2013).
 56.
Poglitsch, A. & Weber, D. Dynamic disorder in methylammoniumtrihalogenoplumbates (ii) observed by millimeterwave spectroscopy. J. Chem. Phys. 87, 6373–6378 (1987).
 57.
Freysoldt, C. et al. Firstprinciples calculations for point defects in solids. Rev. Mod. Phys. 86, 253–305.
 58.
Bechstedt, F., Seino, K., Hahn, P. H. & Schmidt, W. G. Quasiparticle bands and optical spectra of highly ionic crystals: Aln and nacl. Phys. Rev. B 72, 245114 (2005).
 59.
Bechstedt, F. ManyBody Approach to Electronic Excitations 1 edn. (SpringerVerlag Berlin Heidelberg, 2015).
 60.
ValverdeChávez, D. et al. Intrinsic femtosecond charge generation dynamics in single crystal ch3nh3pbi3. Energy Environ. Sci. 8, 3700–3707 (2015).
 61.
Bernardi, M., VigilFowler, D., Lischner, J., Neaton, J. B. & Louie, S. G. Ab Initio study of hot carriers in the first picosecond after sunlight absorption in silicon. Phys. Rev. Lett. 112, 257402 (2014).
 62.
Ma, J. & Wang, L.W. Nanoscale charge localization induced by random orientations of organic molecules in hybrid perovskite ch3nh3pbi3. Nano Lett. 15, 248–253 (2015).
 63.
Wasylishen, R., Knop, O. & Macdonald, J. Cation rotation in methylammonium lead halides. Sol. State Comm. 56, 581–582 (1985).
 64.
Mostofi, A. A. et al. wannier90: A tool for obtaining maximallylocalised wannier functions. Comp. Phys. Comm. 178, 685–699 (2008).
 65.
Pang, S. et al. Nh2chnh2pbi3: An alternative organolead iodide perovskite sensitizer for mesoscopic solar cells. Chem. Mat. 26, 1485–1491 (2014).
 66.
Eperon, G. E. et al. Formamidinium lead trihalide: a broadly tunable perovskite for efficient planar heterojunction solar cells. Energy Environ. Sci. 7, 982–988 (2014).
Acknowledgements
M.B., C.F. and D.D.S. acknowledge funding by the joint Austrian Science Fund  Indian Department of Science and Technology (DST) project INDOX (Grant No. I1490N19). G.K. and C.F. acknowledge funding by Austrian Science Fund (FWF): F41 SFB ViCoM. The calculations were partly performed at the Vienna Scientific Cluster (VSC3).
Author information
Affiliations
University of Vienna, Faculty of Physics and Center for Computational Materials Science, Sensengasse 8/12, 1090 Vienna, Austria
 Menno Bokdam
 , Tobias Sander
 , Cesare Franchini
 & Georg Kresse
Consiglio Nazionale delle Ricerche  CNRSPIN, I67100 L’ Aquila, Italy
 Alessandro Stroppa
 & Silvia Picozzi
Solid State and Structural Chemistry Unit, Indian Institute of Science, 560012 Bengaluru, India
 D. D. Sarma
Authors
Search for Menno Bokdam in:
Search for Tobias Sander in:
Search for Alessandro Stroppa in:
Search for Silvia Picozzi in:
Search for D. D. Sarma in:
Search for Cesare Franchini in:
Search for Georg Kresse in:
Contributions
G.K., C.F., M.B and A.S. conceived the project; M.B. and G.K. proposed and implemented the new method to calculate the finite temperature dielectric function, and performed all DFT and GWBSE calculations. D.D.S. and S.P. included insight from the experimental and theoretical standing of the perovskite field. All the authors contributed with discussions and writing of the manuscript.
Competing interests
The authors declare no competing financial interests.
Corresponding author
Correspondence to Menno Bokdam.
Supplementary information
PDF files
Rights and permissions
This work is licensed under a Creative Commons Attribution 4.0 International License. The images or other third party material in this article are included in the article’s Creative Commons license, unless indicated otherwise in the credit line; if the material is not included under the Creative Commons license, users will need to obtain permission from the license holder to reproduce the material. To view a copy of this license, visit http://creativecommons.org/licenses/by/4.0/
About this article
Further reading

Longlived hotcarrier light emission and large blue shift in formamidinium tin triiodide perovskites
Nature Communications (2018)

Chemically diverse and multifunctional hybrid organic–inorganic perovskites
Nature Reviews Materials (2017)

A hybrid organicinorganic perovskite dataset
Scientific Data (2017)

Accurate and efficient band gap predictions of metal halide perovskites using the DFT1/2 method: GW accuracy with DFT expense
Scientific Reports (2017)
Comments
By submitting a comment you agree to abide by our Terms and Community Guidelines. If you find something abusive or that does not comply with our terms or guidelines please flag it as inappropriate.