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. 2016 May 26;7:0. doi: 10.1038/ncomms11755

Electron–phonon coupling in hybrid lead halide perovskites

Adam D Wright 1, Carla Verdi 2, Rebecca L Milot 1, Giles E Eperon 1, Miguel A Pérez-Osorio 2, Henry J Snaith 1, Feliciano Giustino 2, Michael B Johnston 1, Laura M Herz 1,a
PMCID: PMC4894981  PMID: 27225329

Abstract

Phonon scattering limits charge-carrier mobilities and governs emission line broadening in hybrid metal halide perovskites. Establishing how charge carriers interact with phonons in these materials is therefore essential for the development of high-efficiency perovskite photovoltaics and low-cost lasers. Here we investigate the temperature dependence of emission line broadening in the four commonly studied formamidinium and methylammonium perovskites, HC(NH2)2PbI3, HC(NH2)2PbBr3, CH3NH3PbI3 and CH3NH3PbBr3, and discover that scattering from longitudinal optical phonons via the Fröhlich interaction is the dominant source of electron–phonon coupling near room temperature, with scattering off acoustic phonons negligible. We determine energies for the interacting longitudinal optical phonon modes to be 11.5 and 15.3 meV, and Fröhlich coupling constants of ∼40 and 60 meV for the lead iodide and bromide perovskites, respectively. Our findings correlate well with first-principles calculations based on many-body perturbation theory, which underlines the suitability of an electronic band-structure picture for describing charge carriers in hybrid perovskites.

Inline graphicPhonon scattering limits charge transport in perovskite solar cells, yet the interactions involved are still poorly understood. Here, Wright et al. show by photoluminescence measurements and first-principles calculations that longitudinal optical phonons dominate the electron-phonon coupling at room temperature.

Hybrid lead halide perovskites have attracted intense research activity following their first implementation as light absorbers in thin-film solar cells1 that now reach power conversion efficiencies (PCEs) in excess of 20% (refs 2, 3). These compounds are described by the general formula ABX3, where A is typically an organic cation such as methylammonium (CH3NHInline graphic or MA+) or formamidinium (HC(NH2)Inline graphic or FA+), B is a divalent metal cation (usually Pb2+) and X is a halide anion (I−, Br− or Cl−)4. Such hybrid organic–inorganic materials straddle the divide between organic and inorganic semiconductors, facilitating photovoltaic devices that combine the low processing costs of the former with the high PCEs of the latter2,3,5. In addition, their structural flexibility allows a wide compositional parameter space to be explored. Although MAPbI3 is the most commonly investigated perovskite, the currently most efficient perovskite solar cells replace all2 or most3 of the MA+ with FA+. FAPbI3 has the advantage of a smaller bandgap than MAPbI3 (1.48 versus 1.57 eV), making it more suited for use in single-junction solar cells6, and furthermore shows greater resistance to heat stress6. High-performing devices have used formulations containing both FA and MA cations, to counteract the thermodynamic instability of FAPbI3 in its perovskite phase at room temperature7,8,9. Meanwhile, mixed-halide perovskites incorporating both I− and Br− have been investigated for use in tandem solar cells5,6,10, as these systems allow for bandgap optimization across a wide tuning range.

The success of hybrid perovskites in photovoltaic applications has been widely attributed to their high absorption coefficients across the visible spectrum11, their low exciton binding energies4,12 facilitating charge formation and their long charge-carrier diffusion lengths enabling efficient charge extraction13,14. However, although much recent attention has been devoted towards unravelling the charge-carrier recombination mechanisms underlying these properties4,15, the interaction of charge carriers with lattice vibrations (phonons) is currently still a subject of intense debate16,17. Such electron–phonon interactions matter, because they set a fundamental intrinsic limit to charge-carrier mobilities in the absence of extrinsic scattering off impurities or interfaces18. In addition, charge-carrier cooling following non-resonant (above bandgap) photon absorption is governed by interactions between charges and phonons4. Slow charge-carrier cooling components (compared with GaAs) have been postulated for hybrid perovskites19, which may open the possibility for PCEs beyond the Shockley–Queisser limit. Furthermore, electron–phonon coupling has been shown to yield predominantly homogeneous emission line broadening in hybrid lead iodide perovskite at room temperature, making it suitable as a gain medium for short-pulse lasers20.

Despite the importance of electron–phonon interactions to the optoelectronic properties of these materials, currently no clear picture has emerged of which mechanisms are active. To address this issue, a number of studies have examined the temperature dependence of the charge-carrier mobility μ, which was found21,22,23,24 to scale with Tm with m in the range between −1.4 and −1.6. Several groups16,17,24 therefore proposed that electron–phonon coupling at room temperature is almost solely governed by deformation potential scattering with acoustic phonons, which is known18,25 to theoretically result in μ∝T−3/2. Although such behaviour may be adopted by non-polar inorganic semiconductors such as silicon or germanium18,26, it would be extremely unusual for perovskites that exhibit polar27,28 lead–iodide bonds. These findings have therefore raised the puzzling question of why such hybrid perovskites appear to evade the Fröhlich interactions between charge carriers and polar longitudinal optical (LO) phonon modes that normally govern polar inorganic semiconductors, such as GaAs18,29, at room temperature.

Here we clarify the relative activity of different charge-carrier scattering mechanisms in hybrid lead halide perovskites by investigating charge-carrier scattering through an analysis of the photoluminescence (PL) linewidth as a function of temperature between 10 and 370 K. By carefully examining the low-temperature regime in which thermal energies fall below those of high-energy LO phonon modes, we are able to clearly separate competing contributions from charge-carrier interactions with acoustic and optical phonons. We are therefore able to show unambiguously that Fröhlich coupling to LO phonons is the predominant cause of linewidth broadening in these materials at room temperature, with scattering from acoustic phonons and impurities being a minor component. We further demonstrate excellent agreement between the experimentally determined temperature dependence of the PL linewidth and theoretical values derived from ab initio calculations for MAPbI3. To elucidate how charge-carrier–phonon interaction strengths depend on perovskite composition, we examine FAPbI3, FAPbBr3, MAPbI3 and MAPbBr3, which represent a comprehensive set of the most commonly implemented organic and halide ingredients in hybrid perovskites. We show that although the choice of organic cation has relatively little effect on the Fröhlich interactions, bromide perovskites exhibit higher Fröhlich coupling than iodide perovskites as a result of their smaller high-frequency values of the dielectric function. Overall, our results conclusively demonstrate that electron–phonon coupling in hybrid lead halide perovskites follows a classic bandstructure picture for polar inorganic semiconductors, which are dominated by Fröhlich coupling between charge carriers and LO phonon modes in the high-temperature regime.

Results

Temperature-dependent PL spectra

To conduct our analysis of electron–phonon coupling in hybrid lead halide perovskites, we recorded steady-state PL spectra of solution-processed FAPbI3, FAPbBr3, MAPbI3 and MAPbBr3 thin films over temperatures from 10 to 370 K in increments of 5 K (Fig. 1). The observed PL peak positions at room temperature are consistent with those reported previously for these materials6,30,31,32,33. The colour plots in Fig. 1 exhibit abrupt shifts in PL peak energies at various temperatures that are associated with phase transitions commonly found in these relatively soft materials. For example, MAPbI3, MAPbBr3 and FAPbI3 have been reported to undergo a phase transition from an orthorhombic to a tetragonal structure between 130 and 160 K (refs 30, 33, 34). A further phase transition to the cubic phase follows at higher temperatures for the MA perovskites (at ∼330 K for MAPbI3 (refs 30, 34) and 240 K for MAPbBr3 (ref. 34)), whereas a transition to a trigonal phase occurs at around 200 K for FAPbI3 (ref. 30). The lower-temperature phase transition to the orthorhombic phase below 130–160 K is generally associated with larger energetic shifts as it marks a strong reduction in the extent of rotational freedom of the organic cation34,35,36. Higher-temperature structural changes are more subtle in this regard and therefore much harder to discern21. Apart from these discontinuities, the PL peak in all four materials shifts continuously towards higher energy with increasing temperature. This general trend is in contrast to that of typical semiconductors such as Si, Ge and GaAs, for which the bandgap decreases with temperature as a result of lattice dilation26,37. The atypical positive bandgap deformation potential of hybrid lead halide perovskites has been attributed to a stabilization of out-of-phase band-edge states as the lattice expands38.

Figure 1. Temperature dependence of steady-state PL.

Figure 1

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Colour plots of normalized steady-state photoluminescence spectra of (a) FAPbI3, (b) FAPbBr3, (c) MAPbI3 and (d) MAPbBr3 thin films at temperatures between 10 and 370 K.

In addition to these well-understood temperature trends, the PL spectra of MA-containing perovskites exhibit strong inhomogeneous broadening and multi-peak emission in the low-temperature orthorhombic phase. Such behaviour has been reported by ourselves21,39 and others24,31,40,41 on many occasions, yet a precise explanation is still outstanding. For example, the PL spectra of MAPbI3 develop additional peaks at temperatures below 150 K, as can be seen clearly in Supplementary Fig. 1, which shows spectra from the colour plots in Fig. 1 at selected temperatures. The emerging consensus is that these are caused by additional charge or exciton trap states that are only active in the low-temperature orthorhombic phase21,24,31,39,40,41. It has been proposed that these traps could derive from a small fraction of inclusions of the room-temperature tetragonal phase that are populated through charge or exciton transfer from the majority orthorhombic phase39. These inclusions could be a result of strain or the proposed impossibility of a continuous structural transition from the tetragonal to orthorhombic phase in MA perovskites, as reported by Baikie et al.35. We further note that as these complicating features do not appear in the PL spectra of the equivalent FA perovskites, they are probably not intrinsic to hybrid lead halide perovskites, which re-affirms the prevailing view that they originate from trap states. Importantly, the lack of uncomplicated low-temperature spectra has to date prevented proper analysis of the linewidth broadening of MA perovskites and the associated phonon coupling to charge carriers. As we show below, such analysis requires access to a low-temperature range over which PL spectra are dominated by intrinsic phonon broadening, rather than trap-related PL, for the contributions from acoustic and optical phonons to the clearly separated. Therefore, the discovery that the equivalent FA lead halide perovskites do not exhibit extrinsic defect-related PL in the low temperature range allows us to carry out such analysis unhindered.

Analysis of PL linewidth broadening

Analysis of temperature-dependent emission broadening has long been used to assess the mechanisms of electron–phonon coupling in a wide range of inorganic semiconductors42 (see Supplementary Table 1 for a literature overview of the results). We here apply these methods to hybrid lead halide perovskites by first extracting the full width at half-maximum (FWHM) of the PL spectra shown in Fig. 1 and then analysing its temperature dependence (plotted in Fig. 2). For most inorganic semiconductors, different mechanisms of scattering between charge carriers and phonons or impurities are associated with different functional dependencies of the PL linewidth Г(T) on temperature, which can be expressed as the sum over the various contributions42,43:

Figure 2. Temperature dependence of linewidth.

Figure 2

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FWHM of the steady-state PL spectra as a function of temperature for (a) FAPbI3, (b) FAPbBr3, (c) MAPbI3 and (d) MAPbBr3 thin films plotted as black dots. The solid red lines are fits of Г(T)=Г0+ГLO, which account for contributions from inhomogeneous broadening and Fröhlich coupling with LO phonons. For the perovskites containing MA, the fits are extrapolated into the low-temperature region in which the model does not hold, as indicated by dashed red lines (actual fits were carried out between 150 and 370 K for MAPbI3, and between 100 and 370 K for MAPbBr3). The inset shows the functional form of the temperature dependence of the contributions to PL linewidth in semiconductors from inhomogeneous broadening (Г0, magenta), Fröhlich coupling between charge carriers and LO phonons (ГLO, red) and acoustic phonons (Гac, blue), and scattering from ionized impurities (Гimp, green), as given by the terms of equation (1). An alternative presentation of the linewidths as a mutliple of the thermal energy is given in Supplementary Fig. 2.

graphic file with name ncomms11755-m3.jpg

Here, Г0 is a temperature-independent inhomogeneous broadening term, which arises from scattering due to disorder and imperfections42,44. The second and third terms (Гac and ГLO) are homogeneous broadening terms, which result from acoustic and LO phonon (Fröhlich) scattering28,42,44 with charge-carrier–phonon coupling strengths of γac and γLO, respectively. Electron–phonon coupling is in general proportional to the occupation numbers of the respective phonons, as given by the Bose–Einstein distribution function45,46, taken as Inline graphic for LO phonons, where ELO is an energy representative of the frequency for the weakly dispersive LO phonon branch18,47. For acoustic phonons whose energy is much smaller than kBT over the typical observation range, a linear dependence on temperature is generally assumed46,48. Ab initio calculations of the relevant phonon energies and occupation numbers are shown in Supplementary Fig. 4, which confirms that the linear approximation to the acoustic phonon population used in equation (1) is appropriate. The final term, Гimp, phenomenologically accounts for scattering from ionized impurities with an average binding energy Eb (ref. 43). These impurities contribute γimp of inhomogeneous broadening to the width when fully ionized43,45.

In general, the two major mechanisms governing the electron–phonon coupling in inorganic semiconductors are deformation potential scattering, in which distortions of the lattice change the electronic band structure, and electromechanical or piezoelectric interactions, in which lattice-related electric fields modify the electronic Hamiltonian18. Specifically, the LO phonon term in equation (1) accounts for the Fröhlich interaction between LO phonons and electrons, which arises from the Coulomb interaction between the electrons and the macroscopic electric field induced by the out-of-phase displacements of oppositely charged atoms caused by the LO phonon mode18. Although both transverse optical and LO phonons interact with electrons via non-polar deformation potentials, equation (1) only accounts for LO phonons because of the dominant influence of their Fröhlich interaction with electrons in polar crystals at higher temperatures49. As optical phonons in semiconductors typically have energies of the order of tens of meV (ref. 18), their population at low temperatures (T<100 K) is very small; thus, homogeneous broadening in this regime predominantly results from acoustic phonons18,49. Therefore, careful examination of the low-temperature regime allows separation of the contributions from optical and acoustic modes. Long-wavelength acoustic phonons induce atomic displacements, which can correspond to macroscopic crystal deformation, affecting electronic energies via either the resultant deformation potential or a piezoelectrically induced electric field18.

To establish qualitatively which electron–phonon scattering mechanisms contribute in hybrid lead halide perovskites, we compare the temperature-dependent PL linewidth plotted in Fig. 2 with the functional form of the terms in equation (1). To aid comparison, the inset to Fig. 2a shows example functions for the separate components. First, we assess the possibility of electron scattering with ionized impurities playing a significant role. Comparison of the curves in the inset with the data in the main Fig. 2 makes it apparent that the shape of the ionized impurity scattering term Гimp could not produce the observed linear variation with T of the linewidths at high temperatures. Therefore, we conclude that scattering with ionized impurities does not play any major role here, in agreement with findings based on recent analyses of the temperature-dependence of the charge-carrier mobility in this regime21,22,23,24. We therefore assume Гimp≈0 for the rest of the analysis.

To separate the contributions from acoustic and optical phonon modes, we first focus on an analysis of the PL linewidth for perovskites containing FA as the organic cation. As Fig. 2a,b show, these materials exhibit smooth variation of the linewidth, whereas for MA-containing perovskites the presence of the impurity emission discussed above leads to additional emission broadening in the low-temperature phase (Fig. 2c,d). Both FAPbI3 and FAPbBr3 approach a PL linewidth of the order of 20 meV towards T=0, which can therefore be identified as the temperature-independent inhomogeneous broadening term Г0 arising from disorder. To qualitatively assess the relative importance of acoustic versus optical phonon contributions, an inspection of the gradient of these curves in the low-temperature regime is essential. Although the optical phonon terms lead to a gradient of zero in the regime for which ELO<kBT, the smaller energies of acoustic phonons should result in a non-zero gradient given by γac here. However, visual inspection of the graphs in Fig. 2a,b shows that the gradient of the FWHM versus temperature approaches zero at low temperature, suggesting negligible acoustic phonon contribution (γac≈0). Indeed, we find that fits of equation (1) to these curves converge with γac→0. This result is not surprising, given that in polar inorganic semiconductors the contribution of acoustic phonons to the broadening at room temperature is typically dwarfed by that of the LO phonons and indeed several studies ignore the contribution of acoustic phonons in such systems49. However, we may obtain an upper limit to γac by careful examination of the data in the low-temperature regime in which acoustic phonons are still expected to contribute significantly. Here we may fit Г(T)=Г0+γacT to the data in the low-temperature (T<60 K) region50 or, as an alternative method, obtain the gradient of the data near T=0 K from differentiation. Both methods yield upper limits around γac=60±20 μeV K−1 for FAPbI3 and FAPbBr3; therefore, acoustic phonons will only contribute up to ∼18 meV to the linewidth broadening at 300 K. Hence, our analysis illustrates that the majority of broadening in the room-temperature regime arises from charge-carrier interactions with optical phonons, as would be expected for a polar semiconductor.

To further quantify the dominant Fröhlich coupling in these systems, we proceed by fitting all data including only the mechanisms based on temperature-independent inhomogeneous broadening and Fröhlich coupling to LO phonon modes. For perovskites containing FA cations, fits of Г(T)=Г0+ГLO to the PL linewidth data are plotted in Fig. 2a,b (red lines) and the extracted fitting parameters are presented in Table 1. Apart from Fröhlich coupling strengths, we are also able to determine the energy of LO phonon modes that play the dominant role in electron–LO-phonon coupling. We find ELO=11.5 meV for FAPbI3, with the value for FAPbBr3 (15.3 meV) being 1.3 times larger, which is only slightly greater than the factor of 1.2 expected from a crude model of the frequency of a diatomic harmonic oscillator. These LO phonon energies of hybrid lead halide perovskites are somewhat lower than those typically measured for a range of inorganic semiconductors (see Supplementary Table 1 for an overview); however, they agree well with a recent combined experimental and density functional theory (DFT) study assigning LO phonon modes of the Pb-I lattice in MAPbI3 with energies near 10 meV (ref. 51) and with our present calculations (see next section).

Table 1. Extracted linewidth parameters.

Sample Г0/meV γLO/meV ELO/meV
FAPbI3 19±1 40±5 11.5±1.2
FAPbBr3 20±1 61±7 15.3±1.4
MAPbI3 26±2 40±2 [11.5]
MAPbBr3 32±2 58±2 [15.3]
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FA, formamidinium; LO, longitudinal optical; MA, methylammonium.

Linewidth broadening parameters extracted from fits of Г(T)=Г0+ГLO to the PL linewidth data for the four hybrid perovskite films. Г0 is the inhomogeneous broadening (the linewidth at 0 K), γLO is the strength of the LO phonon–charge-carrier Fröhlich coupling and ELO is the relevant LO phonon energy. For fits to the data from MA-containing perovskites, the values of ELO extracted previously for the FA-containing perovskites were used (hence, they are italicized and enclosed in square brackets). Because of the additional defect luminescence present in the orthorhombic phase of the MA-containing perovskites, fits were only carried out between 150 and 370 K for MAPbI3, and between 100 and 370 K for MAPbBr3 (see solid lines in Fig. 2c,d Therefore, the extracted parameters do not reflect the lineshape broadening in the low-temperature phase of the MA-containing perovskites.

As noted above, the situation is more complex for MA perovskites, owing to the additional trap-related emission in the low-temperature orthorhombic phase that gives rise to sizeable (>100 meV) additional broadening (see Fig. 2c,d). However, in the high-temperature regime, PL linewidths of the MA perovskites vary much in the same manner as that of their FA counterparts, suggesting very similar mechanisms. This may be expected, as the organic cation has relatively little influence on the vibrations of the lead-halide lattice. Hence, we model the linewidth broadening of MA perovskites in the high-temperature regime again using Г(T)=Г0+ГLO (solid red lines in Fig. 2c,d), using the LO phonon energies determined previously for FA perovskites. The resultant γLO values are, as expected, very similar to those for the corresponding FA perovskites (Table 1). We may also extrapolate these fits down through the low-temperature regime (dashed red lines), where they do not reflect experimental reality but rather show the broadening that would be present if the additional defects in the orthorhombic phase were absent. As such, values extracted for the parameter Г0 here mostly reflect inhomogeneous disorder present in the high-temperature phases of MAPbI3 and MAPbBr3 at temperatures above 150 and 100 K, respectively.

Finally, we comment on the extent to which excitonic effects may influence the coupling between charge carriers and phonons. Although the exact values for the exciton-binding energies in these systems are still a matter of debate, most reported values fall into the range of a few to a few tens of milli-electronvolts (see ref. 4 for a review). These values are compatible with numerous studies demonstrating that at room temperature, following non-resonant excitation, hybrid lead halide perovskites sustain free charge carriers as the predominant species13,14,52. Excitonic effects in the generated charge-carrier population are expected to increase as the temperature is lowered. However, we have recently examined infrared photoinduced transmission spectra for methylammonium lead iodide perovskite21 and found these to be predominantly governed by free-charge (Drude-like) features, with localization effects (for example, from excitons) only contributing at low temperature and not more than around 23% even at 8 K. This suggests that over the temperature window we examine here, emission broadening is mostly governed by interactions between phonons and free charge carriers rather than excitons. Such predominantly free-charge behaviour of the photogenerated species may be understood, for example, in terms of the Saha equation or a low Mott density for these systems, and considering that the initial highly non-resonant excitation generates predominantly free electron–hole pairs12. We may further inspect in more detail the temperature-dependent line shapes of the emission spectra and find these to exhibit high-energy Boltzmann tails corresponding to a thermalized electron–hole density near the lattice temperature (see Supplementary Fig. 3). These overall observations are therefore compatible with the presence of a thermalized free electron–hole charge-carrier density that scatters off mostly LO phonons whose occupancy is governed by the Bose–Einstein distribution function. Analysis of how the energies of such thermalized free electrons and holes influence the precise lineshape of the PL spectra as a function of temperature could provide additional insight into the scattering mechanisms for free charge carriers. Such additional analysis is however beyond the scope of the present investigation, which is limited to considering only the extent of linewidth broadening.

First-principles calculations

We further corroborate our analysis with first-principles calculations of the electron–phonon coupling in MAPbI3 (see details in Methods section and in the Supplementary Note 1). In accordance with the above discussion, we separately consider the broadening arising from the interaction of phonons with free conduction-band electrons and free valence-band holes53. The combined broadening arising from both types of charge carrier is then compared with the experimentally determined emission broadening. In Fig. 3a, we present a heat-map of the imaginary part of the electron–phonon self-energy, Im(Σ), projected on the quasiparticle band structure of MAPbI3; 2 Im(Σ) represents the linewidth of electrons and holes arising from the electron–phonon interaction before accounting for many-body effects (see Methods) and is therefore directly comparable to the experimentally determined FWHM of the PL emission linewidth. Figure 3b shows Im(Σ) as a function of electron energy, together with the density of electronic states. This figure indicates that the increase in the linewidth is linked to the phase-space availability for electronic transitions, that is, Im(Σ) increases with increasing density of electronic states, because each state can scatter into a higher number of states by absorbing or emitting a phonon. Our calculations show that the dominant contribution to the electron–phonon self-energy arises from the coupling with the LO mode at Inline graphic, which is shown schematically in Fig. 3c. This observation is compatible with the analysis of the temperature dependence of the PL broadening, as presented in Fig. 2, yielding similar energy for the predominantly coupling LO phonon mode in MAPbI3.

Figure 3. Ab initio calculations of electron–phonon coupling and PL broadening in MAPbI3.

Figure 3

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(a) Electronic band structure of orthorhombic MAPbI3, calculated within the GW approximation as in ref. 55, combined with a heat map of the imaginary part of the electron–phonon self-energy (Im(Σ)) at T=200 K. The zero of the energy is placed in the middle of the bandgap. In b, the imaginary part of the electron–phonon self-energy is shown together with the electronic density of states (DOS). 2 Im(Σ) corresponds to the electron/hole linewidth arising from electron–phonon coupling (apart from the quasiparticle renormalization factor Z). (c) Ball-and-stick representation of the LO vibration responsible for the broadening of the PL peaks. The blue arrows indicate the displacements of Pb and I atoms, for the phonon wavevector q→0 along the [100] direction. This is a Pb–I stretching mode with B3u symmetry51. (d) Temperature dependence of the FWHM of the PL peak in MAPbI3: fit to the experimental data (dashed black line) and theoretical calculations using Fermi's golden rule (blue triangles) and the more accurate Brillouin–Wigner perturbation theory (red triangles). The theoretical broadening is obtained as the sum of 2 lm(Σ) at the valence and conduction band edges in the case of Fermi's golden rule, and the sum of 2 Z lm(Σ) when including many-body quasiparticle renormalization, rigidly shifted by the FWHM at T=0 K (25.72 meV), to account for inhomogenous broadening. The lines are guides to the eye.

Figure 3d shows that our calculated temperature dependence of the PL broadening is in good agreement with experiment. In this figure we compared our calculations with the experimental trends obtained from the fit shown in Fig. 2 (which does not account for the anomalous broadening below 150 K, as discussed above). The blue triangles represent the data calculated based on Fermi's golden rule, which is equivalent to using the imaginary part of the electron–phonon self-energy, 2 Im(Σ), whereas the red triangles were obtained by using Brillouin–Wigner perturbation theory54, which corresponds to scaling the self-energy by the quasiparticle renormalization factor Z, that is 2 Z Im(Σ) (see Methods). The comparison between calculations and experiments shows that the experimental data are most accurately described by fully taking into account the many-body renormalization of the electron lifetime. Taken together, the impressive agreement between (1) our measured and calculated characteristic phonon energy scale (11.5 and 13 meV, respectively), (2) the magnitude of our measured and calculated linewidth broadening at room temperature (90 and 75 meV, respectively), and (3) the phonon energy scale identified here and the LO phonon identified between 10 and 13 meV in our previous study51, strongly support the notion that the broadening of the PL spectra reflects the interaction between free carriers and LO phonons.

In addition, we may use first-principle calculations to elucidate why the lead bromide perovskites exhibit Fröhlich coupling constants that are larger than those of the lead iodide system by a factor of 1.5. To investigate this trend, we performed DFT calculations for MAPbBr3 (see Supplementary Note 1) to compare the associated Born effective charges between the two systems. Our results indicate that the electron–phonon coupling in the bromide perovskite is 40% stronger than in the iodide perovskite, in excellent agreement with our measurements. We find that the increased Fröhlich coupling in MAPbBr3 is primarily connected with the smaller high-frequency value of the dielectric function compared with MAPbI3.

Discussion

Our analysis of the experimentally determined emission linewidth broadening and our first-principles calculations strongly support the notion that Fröhlich coupling to LO phonons is the predominant charge-carrier scattering mechanism in hybrid lead halide perovskites. As already discussed above, such behaviour is in many ways to be expected for these materials, because the lead-halide bond is sufficiently polar (see our calculated Born effective charges in Supplementary Table 2) to lead to macroscopic polarizations from LO phonon modes that modify the electronic energies, causing electron–phonon scattering. Coupling of charge carriers to phonons with energies in the meV range has also been postulated from the signature of such modes in the room- and low-temperature photoconductivity spectra21,56. However, the predominance of Fröhlich coupling appears at first sight to contradict the measured21,22,23,24 temperature dependence of the charge-carrier mobility, which has been stated16,17,24 to approach the expected form for acoustic deformation potential scattering (μ∝T−3/2). We note, however, that although electron–phonon coupling generally leads to charge-carrier mobilities that increase with decreasing temperature, the exact functional dependence is usually a composite of many different scattering mechanisms that can be hard to attribute uniquely18. Charge-carrier scattering with low-energy acoustic phonons can relatively easily be quantified by considering the distribution function of a nondegenerate electron gas approximated by a Boltzmann distribution, which gives the probability that a particular state with energy Ek is occupied at any temperature T. Such calculations result in predicted variations in mobility following μ∝T−3/2 for acoustic phonon deformation potential scattering25,26 and μ∝T−1/2 for acoustic phonon piezoelectric scattering18. For Fröhlich interactions between charges and LO phonons, analytical solutions are harder to establish57, but the reduction in LO phonon occupancy with decreasing temperature similarly leads to an increase in charge-carrier mobility in polar semiconductors18. Even for non-polar semiconductors such as silicon, electron–phonon interactions are found to be complex, for example, involving higher-order phonon terms and intervalley scattering58. Therefore, we conclude that although acoustic phonon deformation potential scattering may result in μ∝T−3/2, the converse may not necessarily also hold. In addition, the rapid energy loss of electrons observed following non-resonant excitation19,59 can only sensibly be explained by a succession of high-energy optical phonon emissions60, as is typically observed in inorganic semiconductors4,61. Therefore, we conclude that Fröhlich coupling to LO phonons, rather than acoustic phonon deformation potential coupling, is the dominant charge-carrier scattering mechanism at room temperature in these hybrid lead halide perovskites. Although our findings themselves do not explain the temperature dependence of the charge-carrier mobility in these materials, they support the hypothesis that the observed μ∝T−3/2 relationship is not wholly attributable to acoustic deformation potential scattering. It is also clear that for these high-quality materials, scattering from ionized impurities is a negligible component at room temperature, with both our PL linewidth data and earlier charge-carrier mobility measurements21,22,23, indicating a complete absence of such contributions.

In addition, our findings give early answers to the question of how perovskite composition affects Fröhlich interactions between charge carriers and phonons. Such interactions determine the maximum charge-carrier mobilities intrinsically attainable, which in turn affects charge-carrier extraction in solar cells. We show that Fröhlich coupling in hybrid lead bromide perovskites appears to be stronger because of the lower dielectric function in the high-frequency regime. Indeed, the THz charge-carrier mobility for FAPbBr3 thin films has recently been shown to be somewhat lower than that for FAPbI3 films10, which could be related to decreased momentum scattering time resulting from increased scattering with LO phonons. However, it may also be partly related to a higher propensity towards disorder in the bromide perovskites, as the inhomogeneous broadening parameter Г0 appears to be somewhat higher for bromide than iodide perovskites here. Similarly, higher Urbach energies have previously been reported for MAPbBr3 compared with MAPbI3, in accordance with larger energetic disorder in the former62. We also find that Г0 tends to be lower for the perovskites containing FA as the organic cation, which points to larger material uniformity as one reason behind this material's recent success in the highest efficiency perovskite solar cells2,7.

We may also compare these findings with those of other polar inorganic semiconductors for which Fröhlich coupling is known to be active. Supplementary Table 1 provides a detailed literature survey of values established for γLO in other inorganic semiconductors. It has been pointed out17 that charge-carrier mobilities established for lead halide perovskites (typically ≤100 cm2 (V s)−1)15,17 are relatively modest compared with those achieved in high-quality GaAs despite the effective charge-carrier masses in perovskites being only slightly elevated above those in GaAs. The values of γLO≈40 meV and γLO≈60 meV we extract from our data for the respective iodide and bromide perovskites (see Table 1) are somewhat higher than the range reported for GaAs (see comparison in Supplementary Table 1), which may partly explain these discrepancies. However, they are significantly lower than those typically found in highly polar materials such as GaN and ZnO where they can be over an order of magnitude higher28. Further theoretical modelling of charge-carrier mobility in these systems based on our findings will most probably allow more quantitative explanations and predictions to be made.

In summary, we have conducted an in-depth analysis of charge-carrier–phonon interactions in hybrid lead halide perovskites, considering the four currently most implemented organic and halide components in hybrid perovskite photovoltaics, which are FAPbI3, FAPbBr3, MAPbI3 and MAPbBr3. Our analysis of the temperature-dependent emission linewidth of FAPbI3 and FAPbBr3 allowed us to establish that the Fröhlich interaction between charge carriers and LO phonons provides the dominant contribution to the predominantly homogeneous linewidth broadening in these hybrid perovskites at room temperature. We successfully corroborated our findings with DFT and many-body perturbation theory calculations, which underline the suitability of an electronic bandstructure picture for describing charge carriers in perovskites. We furthermore obtained experimentally measured energies of LO phonon modes responsible for Fröhlich interactions in these materials and showed that Fröhlich interactions are higher for bromide perovskites than iodide perovskites, providing a link between composition and electron–phonon scattering that fundamentally limits charge-carrier motion. These results lay the groundwork for more quantitative models of charge-carrier mobility values and cooling dynamics that underpin photovoltaic device operation.

Methods

Sample preparation

All materials, unless otherwise stated, were purchased from Sigma-Aldrich and were used as received. Methylammonium iodide, methylammonium bromide, formamidinium iodide and formamidinium bromide were purchased from Dyesol. Thin films were prepared on Z-cut quartz substrates. These were initially cleaned sequentially with acetone followed by propan-2-ol, then treated with oxygen plasma for 10 min.

MA perovskite films were deposited in a nitrogen-filled glovebox using a solvent quenching method wherein an excess of antisolvent is deposited onto the wet substrate while spin-coating63. A 1:1 molar ratio solution of MAX and PbX2 (X=I, Br) was dissolved in anhydrous N,N-dimethylformamide at 1 M. This was then spin-coated onto the quartz substrates at 5,000 r.p.m. for 25 s. During spin coating, after 7 s an excess of anhydrous chlorobenzene was rapidly deposited onto the spinning film. After spin-coating, films were annealed at 100 °C for 10 min.

FA perovskite films were deposited using an acid-addition method to produce smooth and uniform pinhole-free films6. FAX and PbX2 (X=I, Br) were dissolved in anhydrous N,N-dimethylformamide in a 1:1 molar ratio at 0.55 M. Immediately before film formation, small amounts of acid were added to the precursor solutions, to enhance the solubility of the precursors and allow smooth and uniform film formation. Thirty-eight microlitres of hydroiodic acid (57% mass/mass) was added to 1 ml of the 0.55 M FAPbI3 precursor solution and 32 μl of hydrobromic acid (48% mass/mass) was added to 1 ml of the 0.55 M FAPbBr3 precursor solution. Films were then spin coated from the precursor plus acid solution on warm (85 °C) oxygen plasma-cleaned substrates at 2,000 r.p.m. in a nitrogen-filled glovebox and subsequently annealed in air at 170 °C for 10 min.

PL spectroscopy

Each sample was photoexcited by a 398-nm picosecond pulsed diode laser (PicoHarp, LDH-D-C-405M) with a repetition rate of 10 kHz and a fluence of 490 nJ cm−2. The resultant PL was collected and focused into a grating spectrometer (Princeton Instruments, SP-2558), which directed the spectrally dispersed PL onto an iCCD (PI-MAX4, Princeton Instruments). The sample was mounted under vacuum (P<10−6 mbar) in a cold-finger liquid helium cryostat (Oxford Instruments, MicrostatHe). An associated temperature controller (Oxford Instruments, ITC503) monitored the temperature at two sensors mounted on the heat exchanger of the cryostat and the end of the sample holder, respectively; the reading from the latter was taken as the sample temperature. PL measurements were taken as the sample was heated in increments of 5 K between 10 and 370 K.

Computational methods

We carried out ab initio calculations on MAPbI3 in the orthorhombic phase using the crystallographic data in ref. 35. The ground-state electronic structure was computed within the local density approximation to DFT including spin–orbit coupling, as implemented in the Quantum ESPRESSO package64. We used norm-conserving pseudopotentials to describe the core–valence interaction, with the semicore d states taken explicitly into account in the case of Pb and I. Ground-state calculations were converged with a plane-wave cutoff of 100 Ry and a 6 × 6 × 6 unshifted Brillouin-zone grid. The electronic quasiparticle energies were calculated with the SS-GW method described in ref. 65 using the Yambo code66 and interpolated by means of Wannier functions as in ref. 55, using wannier90 (ref. 67). This yields bandgap and effective masses in good agreement with experiment (see Supplementary Note 1). The lattice dynamical properties were computed within density functional perturbation theory at the Г point, as in ref. 51). The LO–TO splitting was included through the evaluation of the non-analytic contribution to the dynamical matrix. The electron–phonon coupling was calculated using the EPW code68,69, v.4. The electron–phonon self-energy, Σnk, was calculated as:

graphic file with name ncomms11755-m6.jpg

Here, Inline graphic and nqv are the Fermi–Dirac and the Bose–Einstein occupations, respectively, ɛnk and ɛmk+q are electron energies, ℏωqv is the energy of a phonon with wavevector q and polarization ν, and η is a small broadening (10 meV in Fig. 3a,b; 1 meV in Fig. 3d). Only the interaction with the LO phonons was taken into account, by calculating the electron–phonon matrix element Inline graphic as in ref. 70 (see Supplementary equation (1)). The self-energy in equation (2) was converged by using up to two million random q points in the Brillouin zone. The quasiparticle renormalization factor Z is defined as the frequency derivative:

graphic file with name ncomms11755-m9.jpg

and is evaluated at the band edges. In the case of the conduction band edge, we find Z=0.54 at zero temperature.

Data availability

The data that support the findings of this study are available from the corresponding author on request, as is the custom Matlab code used to analyse the PL data. The Quantum ESPRESSO64, Yambo66, wannier90 (ref. 67) and EPW v.4 (ref. 69) software used to perform the first-principles calculations are open source and are accessible online.

Additional information

How to cite this article: Wright, A. D. et al. Electron–phonon coupling in hybrid lead halide perovskites. Nat. Commun. 7:11755 doi: 10.1038/ncomms11755 (2016).

Supplementary Material

Supplementary Information

Supplementary Figures 1-4, Supplementary Tables 1-2, Supplementary Note 1, Supplementary Equation 1 and Supplementary References

ncomms11755-s1.pdf (872.1KB, pdf)

Acknowledgments

This work was supported by the Leverhulme Trust (Grant RL-2012-001), the UK Engineering and Physical Sciences Research Council (grant numbers EP/J009857/1, EP/L024667, EP/L016702/1 and EP/M020517/1) and the Graphene Flagship (EU FP7 grant number 604391). This work used the ARCHER UK National Supercomputing Service via the AMSEC Leadership project and the Advanced Research Computing (ARC) facility of the University of Oxford.

Footnotes

Author contributions A.D.W. performed the PL experiments, did the data analysis and participated in the experimental planning. C.V. carried out the first-principles calculations. R.L.M. gave guidance for the PL experiments. G.E.E. prepared the samples. H.J.S. gave guidance on sample preparation. M.A.P.-O. provided support with the first-principles calculations. The project was conceived, planned and supervised by F.G., M.B.J. and L.M.H. A.D.W. wrote the first version of the manuscript. All authors contributed to the discussion and preparation of the final version of the paper.

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Associated Data

This section collects any data citations, data availability statements, or supplementary materials included in this article.

Supplementary Materials

Supplementary Information

Supplementary Figures 1-4, Supplementary Tables 1-2, Supplementary Note 1, Supplementary Equation 1 and Supplementary References

ncomms11755-s1.pdf (872.1KB, pdf)

Data Availability Statement

The data that support the findings of this study are available from the corresponding author on request, as is the custom Matlab code used to analyse the PL data. The Quantum ESPRESSO64, Yambo66, wannier90 (ref. 67) and EPW v.4 (ref. 69) software used to perform the first-principles calculations are open source and are accessible online.

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