Organic-inorganic hybrid perovskites such as methylammonium lead iodide (CH3NH3PbI3) are game-changing semiconductors for solar cells and light-emitting devices owing to their defect tolerance and exceptionally long carrier lifetimes and diffusion lengths. Determining whether the dynamically disordered organic cations with large dipole moment benefit the optoelectronic properties of CH3NH3PbI3 has been an outstanding challenge. Herein, via transient absorption measurements employing an infrared pump pulse tuned to a methylammonium vibration, we observe slow, nanosecond-long thermal dissipation from the selectively excited organic mode to the inorganic sublattice. The resulting transient electronic signatures, during the period of thermal-nonequilibrium when the induced thermal motions are mostly concentrated on the organic sublattice, reveal that the induced atomic motions of the organic cations do not alter the absorption or the photoluminescence response of CH3NH3PbI3, beyond thermal effects. Our results suggest that the attractive optoelectronic properties of CH3NH3PbI3 mainly derive from the inorganic lead-halide framework.
Metal-halide perovskites are emerging as low-cost, solution-processable semiconductors for applications involving the harvesting and emitting of light1,2. Recent spectroscopic measurements have demonstrated that the favorable optical and electronic properties of these materials likely arise from the strong electron–phonon interactions in these soft semiconductors, in conjunction with the large dynamic disorder of the lead-halide octahedral framework3,4,5,6. Hybrid organic–inorganic metal-halide perovskites, including the prototypical CH3NH3PbI3, present additional challenges in understanding the interplay between the structural and optoelectronic properties. This primarily stems from the significant structural fluctuations of the organic cations (e.g., CH3NH3+) with picosecond relaxation times observed from neutron scattering and millmeter-wave spectroscopic experiments7,8. Due to the potentially crucial importance for enhancing device efficiency9 and enabling additional functionalities10,11, the mutual interactions between the fluctuating dipolar organic cations and the charge carriers that reside on the inorganic Pb-I framework have been extensively investigated. Formation of (anti)ferroelectric domains arising from the orientational ordering of the polar organic cations was proposed to enhance carrier lifetimes12, but spectroscopic measurements did not support such a picture13,14,15. Dynamic bulk Rashba effect induced by the CH3NH3+ cations was also suggested16,17, yet recent theoretical and experimental results show that such an effect is negligible18. In fact, HC(NH2)2PbI3-based devices exhibit conversion efficiencies comparable to the CH3NH3PbI3 analog19, albeit the dipole moment of HC(NH2)2+ is much smaller than that of CH3NH3+ (ref. 12), and approaches that of the non-polar Cs+ cation. Although spectroscopy-based comparative studies between hybrid and all-inorganic perovskites have been attempted so as to evaluate the role of polar organic cations on material performance20,21,22, the properties of metal-halide perovskites are known to depend on synthetic conditions and material history23,24. For example, high-quality, vapor-deposited CsPbI3 thin films present impressively long carrier lifetime exceeding 10 µs that is comparable to the best CH3NH3PbI3 counterparts, whereas solution-processed CsPbI3 film showed significantly shorter lifetime25. Remarkable solar cell efficiencies derived from carefully prepared CsPbI3 have been reported26,27, and solar cells made from CH3NH3PbBr3 and CsPbBr3 exhibited comparable efficiencies21. These device characteristics hinted that the main role played by the organic cations is structural, with a different size than Cs+ as well as the additional electrostatic interactions and hydrogen bonding with the lead-halide framework28. While the black phase of CH3NH3PbI3 is stable at room temperature, it is known that the CsPbI3 counterpart is not stable at room temperature and special treatments are required to stabilize its black phase29, which makes a fair comparison between CH3NH3PbI3 and CsPbI3 difficult. As a result, experimental approaches permitting the direct probing of interactions between the organic and inorganic sublattices are important for the study of hybrid material systems30. Here, we employ infrared pump electronic-probe (IPEP) spectroscopy to excite the strongly absorbing vibrational modes of the organic sublattice and examine the corresponding optical response near the bandgap of CH3NH3PbI3. We found that the pump-induced motions of the CH3NH3+ cations do not change the subsequent absorption or the photoluminescence response of CH3NH3PbI3, but merely result in the heating of the inorganic sublattice in hundreds of picoseconds to nanosecond timescale.
Static optical response
Figure 1a maps the temperature-dependent static absorbance of a CH3NH3PbI3 thin film around its bandgap. The tetragonal-to-orthorhombic phase transition near 145 K is denoted by an abrupt change of the bandgap, and for each individual phase the bandgap increases with temperature. The near-bandgap, distinct absorption peak in the orthorhombic phase arises due to a comparatively stronger excitonic character. Figure 1b presents the temperature-dependent static absorbance arising from the N-H asymmetric stretching modes (abbreviated here as N-H-as modes) of the CH3NH3+ cation, which exhibit the strongest optical absorption cross-section among various vibrational modes of the molecular cation31. A dramatic increase of the N-H-as absorbance accompanying the phase transition is due to the formation of hydrogen bonding that suppresses the rotational motions of CH3NH3+ in the orthorhombic phase32. The pronounced mid-infrared absorbance, in conjunction with the near-bandgap optical response, facilitate IPEP measurements on the orthorhombic phase of CH3NH3PbI3.
In IPEP measurements, we selectively pumped the N-H-as modes (centered at 3120 cm−1; Fig. 1d and Supplementary Figure 1 show the pump profile) and probed the change of optical density (ΔOD) near the bandgap. The ΔOD spectral map acquired on CH3NH3PbI3 at 10 K is displayed in Fig. 1c. We observe a derivative-like transient spectral response, whose magnitude following the excitation starts from zero, grows with pump–probe time delay, and saturates on the nanosecond timescale. Positive ΔOD signal on the blue side of the static absorption peak and negative signal to the red conveys a spectral blueshift, consistent with transient lattice heating (Fig. 1a). Note that large bandgap shifts arising from the optical Stark effect were observed at zero delay time, when the pump and probe pulses temporally overlapped33 (Supplementary Fig. 2). As presented in Fig. 1d, sweeping the frequency of the infrared pump pulse shows that the obtained intensity of ΔOD is linearly proportional to the spectral overlap of the pump and the absorbance of the N-H-as modes. Furthermore, an off-resonance pump (centered at 2200 cm−1) results in negligible transient response (Supplementary Fig. 3), confirming that the response shown in Fig. 1c is due to vibrational excitation of the organic sublattice. The nanosecond timescale relates slow down-conversion of thermal energy from the high-energy N-H-as modes to the low-lying, cold phonon bath, with the latter encompassing all the CH3NH3+ modes except the N-H-as modes, and all the modes of the inorganic sublattice.
Probing the tetragonal phase at 205 K distills a comparably faster thermal equilibration with a timescale of hundreds of picoseconds (Supplementary Fig. 4). Measurement near the phase transition (near 145 K) reveals that the two coexisting phases respond independently to the pump (Fig. 2a), as no evidence of transient phase change is observed, which would otherwise lead to the transfer of spectral weight between the two phases. The ΔOD amplitude near the bandgap obtained for the tetragonal phase is, as expected, weaker than that for the orthorhombic counterpart, owing to a weaker vibrational absorption (Fig. 1b). The nearly identical timescales of ΔOD kinetics for the coexisting phases at 145 K (Supplementary Fig. 4d) indicate that the rotations of CH3NH3+, which are only present in the tetragonal phase, do not apparently influence the phonon–phonon coupling strength between the two sublattices. Temperature-dependent kinetics (Fig. 2b) reveal slower thermal equilibration at lower temperatures. Furthermore, the ΔOD amplitude increases with decreasing temperature (Fig. 2c), which results from the heat capacity that diminishes, and the absorption cross-section of the N-H-as modes that grows, with decreasing temperature. Fluence-dependent measurements (Fig. 2d) show that the ΔOD amplitude scales nearly linearly with the pump fluence, and the thermal equilibration time is not sensitive to pump fluence over the explored range, consistent with earlier work based on transient mid-infrared spectroscopy using electronic excitation and an infrared probe31.
Having established the transient electronic response around the bandgap following infrared molecular vibrational excitation, we then turn to investigating whether perturbatively induced motions of the organic sublattice influence the near-bandgap optical properties of CH3NH3PbI3. As illustrated in Fig. 3a, following the selective excitation of N-H-as modes, phonon–phonon scattering leads to the sequential population of various lower-energy CH3NH3+ vibrational modes, and ultimately the population of inorganic phonon modes. Note that thermal equilibration within the inorganic sublattice itself requires only 10 to 20 ps, as shown by ultrafast electron diffraction measurements4. Therefore, the nanosecond timescale is mainly attributed to the following two consecutive processes: (i) intramolecular vibrational relaxation (IVR) within the CH3NH3+ cations34, and (ii) non-equilibrium thermal energy transfer from CH3NH3+ to the inorganic framework31. The IVR process of the CH3NH3+ cations involves a succession of energy down-conversion through all the intermediate phonon modes starting from the selectively excited organic mode to the lowest-lying modes, which is expected to take longer than the lifetime of any specific organic vibrational mode. Indeed, several two-dimensional infrared spectroscopic studies demonstrated a few-picosecond timescale for the reorientational motions of the organic cations, as well as a significantly longer timescale (tens to hundreds of picoseconds) that was attributed to thermal response of the lattice13,14,15. Although the longer timescale has not been further pursed in those studies, we speculate that it is of similar origin as what we observed here. We note that the slow timescale can also be contributed by an ineffective (i.e., slow) heat energy transfer from the organic vibrational modes to the inorganic phonon modes, evident from the low thermal conductivities of organic–inorganic hybrid material systems35,36. We also note that the coupling between the high-energy vibrations and the electronic states during the first 10 ps cannot be carefully addressed due to the excitation of optical phonon modes of the lead iodide framework (as discussed in the Time-resolved photoluminescence measurements section).
To gain more insights into the vibrational evolution, we performed ab initio molecular dynamics simulations on the orthorhombic structure with selective excitation of the N-H-as modes based on the phonon calculations, from which we extracted atomic trajectories up to 130 ps. As shown in Fig. 3b, selective excitation of the N-H-as modes results in the population of various stretching modes as represented by the variation of bond lengths of N-H, C-H, and C-N. The C-N bond-length variation decays more slowly in comparison to the C-H and N-H bonds, as the latter two are associated with vibrational modes of the highest frequencies and depopulate most rapidly via IVR. Note that librational motions, captured by the orientational variation of the C-N bond (Fig. 3c), can also be induced. The simulated timescale is furthermore not strongly dependent on the total imparted energy in the simulations (Fig. 3c), which is consistent with the experimental results (Fig. 2d).
The change of the ΔOD amplitude can act as a proxy for how much thermal energy has been transferred to the inorganic framework (that in turn determines the bandgap). The transient response at long delay time (later than 1000 ps), when the sample has reached thermal equilibrium (Fig. 2b), results from the change of the bandgap with temperature. Transient spectra plotted for representative delay times (Fig. 3d) during the thermal relaxation closely overlap with a simple scaling of the amplitude. Such spectral similarity suggests that no net increase or decrease of optical absorption coefficient, other than that caused by lattice heating, occurs upon this perturbation when CH3NH3PbI3 is at thermal non-equilibrium (i.e., 0 to 1000 ps). Because optical absorption can be viewed as an inverse process of bimolecular recombination37, the data shown in Fig. 3d implicitly suggest that the pump-induced CH3NH3+ motions do not impact bimolecular recombination in CH3NH3PbI3.
IPEP measurements on CH3NH3PbBr3 and CH3NH3PbCl3 single crystals reveal similar transient optical response (Supplementary Fig. 5) compared to CH3NH3PbI3 due to their structural similarity. However, in contrast to CH3NH3PbX3 (X = I, Br, Cl), which are three-dimensional (3D) perovskites, the impact of artificially induced organic cation motion is observed for the two-dimensional perovskite, (CH3(CH2)3NH3)2PbI4. For this compound38, the CH3(CH2)3NH3+ cations situated between the perovskite layers strongly impact the electronic properties through both quantum and dielectric confinement effects. Following selective vibrational excitation near 3100 cm−1 (Supplementary Fig. 6), a much faster transient optical response, relative to the 3D counterparts, was observed for (CH3(CH2)3NH3)2PbI4 near the exciton transition energy (Supplementary Fig. 5), owing to the internal IVR processes of the CH3(CH2)3NH3+ cations that alter the strength of quantum confinement of the electron–hole pairs (i.e., excitons) residing on the Pb-I framework.
Time-resolved photoluminescence measurements
We further explored if the infrared pump-induced CH3NH3+ motions can directly impact photoluminescence (PL) of CH3NH3PbI3, using infrared pump PL-probe measurements based on the schematic shown in Supplementary Fig. 7. Here, the pump pulse was followed by a time-delayed (denoted as Δt), low-intensity, 400 nm PL-probe pulse that generates electron–hole pairs (positive Δt is defined if the infrared pump hits the sample first). The emitted photons were either detected by a charge-coupled device (CCD) camera or spectrally and temporally resolved by a streak camera. Figure 4a presents a representative, spectrally resolved PL map measured at 50 K without using the infrared pump. Figure 4b shows the spectrally integrated PL decay kinetics measured under various negative values of Δt, with the infrared pump turned on. The dip in the PL decay trace, which exhibits an instrument-response-time-limited timescale, is also observed by using an off-resonant mid-infrared pump (Supplementary Fig. 8), and therefore attributed to the electric-field-driven dissociation of electron–hole pairs, or the optical Stark effect. We then focused on measurements under positive Δt values. Figure 4c presents PL decays measured using different positive Δt values that traverse the duration of sublattice thermal equilibration. We find that optically pumping the organic vibrational modes of CH3NH3PbI3 does not apparently alter the carrier recombination rate.
While streak camera measurements only detect PL over specific time windows, time-integrated PL measurements with higher signal-to-noise ratio can reveal whether the infrared pump-induced CH3NH3+ motions can enhance (by suppressing defect scattering of charge carriers) or suppress (by slowing down the recombination rate of carriers so that more trapping events can take place) the brightness of CH3NH3PbI3. Static, temperature-dependent PL intensity (Fig. 4d) suggests that a substantial portion of photo-generated carriers are lost through non-radiative decay pathways at 50 K. The time-integrated PL spectra measured at 10 K and 50 K are shown in Fig. 4e; note that the dramatic change in PL linewidth upon temperature reduction has been observed previously39. For both temperatures, the infrared pump (Δt = 2000 ps) yields a blueshift of the PL spectrum, stemming from a bandgap increase due to lattice heating. We ran measurements at these two temperatures because the fast PL decay component due to bimolecular recombination40 is commensurate with the thermal equilibration time, and hence the impact of non-equilibrium CH3NH3+ motions, if there are any, can be more pronounced. Based on the PL spectral shift at 50 K (in conjunction with data in Fig. 1a and heat capacity41), we estimate that 0.06 photons are absorbed per orthorhombic unit cell by CH3NH3+, with a photon energy of 386 meV (corresponding to 3120 cm−1). We denote the change of PL counts at each wavelength as ΔN = Non − Noff, where Non (Noff) designates PL counts obtained with (without) the infrared pump. The spectra of ΔN/Itot measured at 10 K and 50 K using variable positive Δt values are presented in Fig. 4f, g, respectively, where Itot is the spectrally integrated, total PL counts measured without the infrared pump. At 10 K, infrared pumping yields a PL blueshift, the magnitude of which increases with Δt. This arises because a larger Δt results in a more substantial sample heating (which causes a larger bandgap increase) before the photoluminescence event takes place. A similar PL blueshift is observed also at 50 K, although an additional increase of the PL intensity, implied by an asymmetric line shape, is observed especially for small Δt values. To explore the origin of such PL enhancement, we ran control experiments with an off-resonance infrared pump centered at 2200 cm−1. As shown in Fig. 4h, although the PL blueshift is no longer present due to the lack of lattice heating, a PL intensity enhancement is still recovered. The observed PL enhancement retained using both pumping wavelengths is likely attributable to polaron formation arising from below-bandgap excitation of various phonon modes of the inorganic sublattice (evident from Supplementary Fig. 9)6 that may contribute to the protection of charge carriers from defect scattering. This effect is not clearly observable at 10 K since the ΔN/Itot intensity arising from bandgap blueshift is an order of magnitude larger than in the 50 K measurement. Importantly, comparison of Fig. 4g, h reveals that the induced CH3NH3+ motions alone lead to negligible variation of the integrated PL intensity.
Our transient absorption and PL measurements both suggest that infrared pump-induced CH3NH3+ motions do not lead to noticeable changes of the near-bandgap absorption and PL properties, beyond effects due to lattice heating. Such an observation implies that photo-generated carriers residing on the inorganic sublattice are essentially decoupled from the dynamically disordered organic cations. The transient spectroscopic technique reported here, complementary to fully electronic pump–probe, or fully infrared (vibrational) pump–probe measurements14,42,43, can be generalized for studying organic semiconductors, organic–inorganic interfaces, and other organic–inorganic hybrid materials such as superatomic solids35 and two-dimensional hybrid perovskites44.
Chemicals and the synthesis of CH3NH3I
Methylamine solution (CH3NH2, 40 wt.% in H2O), N-methyl-2-pyrrolidinone (NMP), and γ-Butyrolactone (GBL, ≥99%) were purchased from Aldrich. Hydriodic acid (HI, 57 wt.% in H2O) and lead(II) iodide (PbI2, 99.9985% metal basis) were purchased from Alfa Aesar. Ethyl ether (anhydrous) and acetone were obtained from Fisher Chemical. All chemicals were used as received without further purification. Equimolar of HI was dropwise added to CH3NH2 with stirring in a 50 mL round bottom flask immersed in ice bath, followed by rotary evaporation at 60 °C to dry off the solvent. Next, the white solid was obtained and washed with excessive ethyl ether on a filter paper, accompanied with vacuum filtration. The washed CH3NH3I powder was then dried in a vacuum oven at 60 °C overnight to yield the final product.
CH3NH3PbI3 thin film fabrication
The preparation of CH3NH3PbI3 thin film follows method reported previously with slight modification45. The 1.2:1 molar ratio of CH3NH3I/PbI2 was dissolved in 1:1 volume ratio of NMP/GBL to make a 40 wt.% precursor solution. Then, the precursor solution was spun-coated on an acetone-cleaned sapphire substrate with a speed of 3000 rpm for 30 s. Next, the as-formed wet film was quickly transferred into an ethyl ether bath (50 mL) for 90 s. Finally, the developed film was dried in air, covered by a Petri dish, and followed by annealing at 150 °C for 15 min on a hot plate in a humidity-controlled environment.
Static optical characterization
Static infrared absorbance spectra were captured with Fourier transform infrared (FTIR; Thermo Nicolet 6700). Static visible absorbance spectra were obtained with a customized setup. In all the optical measurements (both static and transient), the samples were mounted in a 4 K closed-cycle cold-finger cryostat under with a base pressure below 1 × 10−7 Torr.
Transient absorption measurements
Transient absorption (i.e., IPEP) measurements were performed using a 35 fs amplified titanium/sapphire laser operating at 800 nm at a repetition rate of 2 kHz. Broadband visible probe pulses were generated by focusing a portion of the amplifier output onto an Al2O3 window. Infrared pump pulses were generated by difference frequency mixing of signal and idler beams using an optical parametric amplifier and were reduced in repetition rate to 1 kHz. The probe pulses were mechanically time delayed using a translation stage and retroreflector. Full transient spectral maps are shown in Supplementary Figs. 10 and Fig. 11.
Infrared pump PL-probe measurements
Generation of the infrared pump pulse was identical to that employed in the transient absorption measurements. The 400 nm PL excitation pulses were produced by frequency-doubling of the 800 nm amplifier output with a BBO crystal and underwent similar beam path as the visible probe pulses in the IPEP measurements. Both the infrared pump pulses and the 400 nm PL excitation pulses were maintained at 2 kHz. Temporally and spectrally resolved PL data were collected with a streak camera. Time-integrated PL data were captured with a CCD camera. The spot size of the 400-nm PL excitation pulses was adjusted to be smaller than that of the infrared pump pulses. The fluence of 400 nm PL excitation pulse was kept below 1 µJ cm−2.
Calculations of the phonon spectrum and phonon–phonon scattering phase space
Vienna Ab initio Simulation Package (VASP) was used to perform structure relaxation and self-consistent density functional theory (DFT) calculations46,47,48,49. The projector augmented wave (PAW) method50 was used in conjunction with the generalized gradient approximation (GGA)51 for the exchange-correlation (xc) functional52. We used the van der Waals density functional (vdW-DF) method to treat the dispersion forces from non-local electron–electron interactions, particularly, the optB86b-vdW functional53. DFT calculations of primitive cell of CH3NH3PbI3 in the orthorhombic phase with space group of Pnma (No. 62) were performed using a 4 × 4 × 4 Γ-centered k-point mesh and a kinetic energy cutoff of 550 eV. The force and energy convergence thresholds were set to be 5 × 10−3 eV Å−1 and 10−8 eV, respectively. Phonon calculations were performed using Phonopy package54, wherein 1 × 1 × 1 supercell structures were constructed to extract harmonic interatomic force constants which were used to construct dynamical matrix and obtain phonon dispersion relation along high-symmetry paths in the Brillouin zone. Phonon scattering phase space accounting for three-phonon interactions was calculated using ShengBTE package55.
Ab initio molecular dynamics (AIMD) simulations
The starting structures for AIMD were obtained by exciting all the CH3NH3+ cations by a certain fraction of the phonon eigenvectors for the highest energy mode (the N-H-as mode). To study the effect of fluence on the perovskite dynamics, the atoms in the CH3NH3+ cations were displaced from their equilibrium positions by a fraction of 0.10 and 0.07, which correspond to an energy imparted of 164 meV and 72 meV, respectively. AIMD simulations were performed as implemented in the VASP package, using PAW pseudopotentials and the GGA functional with vdW-DF correction. Because of computational expense, spin–orbit coupling was not considered. An energy cutoff of 500 eV was used for the plane wave basis. The atoms were relaxed until forces on the atoms were less than 0.0001 eV Å−1, and gamma point sampling was used for the Brillouin zone. A time step of 0.5 fs was applied for the AIMD calculations. Standard molecular dynamics was performed using a microcanonical ensemble by applying the IBRION = 0 and the SMASS = −3 tags. The AIMD trajectories and structure snapshots were visualized with VESTA and VMD softwares56,57. The structure of the CH3NH3PbI3 used in the calculation was obtained from ref. 58.
All relevant data used in the article are available from the authors.
Lee, M. M., Teuscher, J., Miyasaka, T., Murakami, T. N. & Snaith, H. Efficient hybrid solar cells based on meso-superstructured organometal halide perovskites. Science 338, 643–647 (2012).
Jia, Y., Kerner, R. A., Grede, A. J., Rand, B. P. & Giebink, N. C. Continuous-wave lasing in an organic–inorganic lead halide perovskite semiconductor. Nat. Photonics 11, 784–788 (2017).
Xing, G. et al. Long-range balanced electron- and hole-transport lengths in organic-inorganic CH3NH3PbI3. Science 342, 344–347 (2013).
Wu, X. et al. Light-induced picosecond rotational disordering of the inorganic sublattice in hybrid perovskites. Sci. Adv. 3, e1602388 (2017).
Yaffe, O. et al. Local polar fluctuations in lead halide perovskite crystals. Phys. Rev. Lett. 118, 136001 (2017).
Miyata, K. et al. Large polarons in lead halide perovskites. Sci. Adv. 3, e1701217 (2017).
Leguy, A. M. A. et al. The dynamics of methylammonium ions in hybrid organic–inorganic perovskite solar cells. Nat. Commun. 6, 7124 (2015).
Poglitsch, A. & Weber, D. Dynamic disorder in methylammoniumtrihalogenoplumbates (II) observed by millimeter-wave spectroscopy. J. Chem. Phys. 87, 6373–6378 (1987).
Wang, L., McCleese, C., Kovalsky, A., Zhao, Y. & Burda, C. Femtosecond time-resolved transient absorption spectroscopy of CH3NH3PbI3 perovskite films: evidence for passivation effect of PbI2. J. Am. Chem. Soc. 136, 12205–12208 (2014).
Odenthal, P. et al. Spin-polarized exciton quantum beating in hybrid organic–inorganic perovskites. Nat. Phys. 13, 894–899 (2017).
Ye, H.-Y. et al. Metal-free three-dimensional perovskite ferroelectrics. Science 361, 151–155 (2018).
Frost, J. M. et al. Atomistic origins of high-performance in hybrid halide perovskite solar cells. Nano Lett. 14, 2584–2590 (2014).
Taylor, V. C. A. et al. Investigating the role of the organic cation in formamidinium lead iodide perovskite using ultrafast spectroscopy. J. Phys. Chem. Lett. 9, 895–901 (2018).
Bakulin, A. A. et al. Real-time observation of organic cation reorientation in methylammonium lead iodide perovskites. J. Phys. Chem. Lett. 6, 3663–3669 (2015).
Selig, O. et al. Organic cation rotation and immobilization in pure and mixed methylammonium lead-halide perovskites. J. Am. Chem. Soc. 139, 4068–4074 (2017).
Motta, C. et al. Revealing the role of organic cations in hybrid halide perovskite CH3NH3PbI3. Nat. Commun. 6, 7026 (2015).
Zheng, F., Tan, L. Z., Liu, S. & Rappe, A. M. Rashba spin–orbit coupling enhanced carrier lifetime in CH3NH3PbI3. Nano Lett. 15, 7794–7800 (2015).
Frohna, K. et al. Inversion symmetry and bulk Rashba effect in methylammonium lead iodide perovskite single crystals. Nat. Commun. 9, 1829 (2018).
Yang, W. S. et al. High-performance photovoltaic perovskite layers fabricated through intramolecular exchange. Science 348, 1234–1237 (2015).
Zhu, H. et al. Organic cations might not be essential to the remarkable properties of band edge carriers in lead halide perovskites. Adv. Mater. 29, 1603072 (2017).
Kulbak, M., Cahen, D. & Hodes, G. How important is the organic part of lead halide perovskite photovoltaic cells? Efficient CsPbBr3 cells. J. Phys. Chem. Lett. 6, 2452–2456 (2015).
Zhu, H. et al. Screening in crystalline liquids protects energetic carriers in hybrid perovskites. Science 353, 1409–1413 (2016).
Wu, X. et al. Trap states in lead iodide perovskites. J. Am. Chem. Soc. 137, 2089–2096 (2015).
Stoumpos, C. C. & Kanatzidis, M. G. The renaissance of halide perovskites and their evolution as emerging semiconductors. Acc. Chem. Res. 48, 2791–2802 (2015).
Hutter, E. M. et al. Vapour-deposited cesium lead iodide perovskites: microsecond charge carrier lifetimes and enhanced photovoltaic performance. ACS Energy Lett. 2, 1901–1908 (2017).
Wang, P. et al. Solvent-controlled growth of inorganic perovskite films in dry environment for efficient and stable solar cells. Nat. Commun. 9, 2225 (2018).
Sanehira, E. M. et al. Enhanced mobility CsPbI3 quantum dot arrays for record-efficiency, high-voltage photovoltaic cells. Sci. Adv. 3, eaao4204 (2017).
Egger, D. A. et al. What remains unexplained about the properties of halide perovskites? Adv. Mater. 30, 1800691 (2018).
Fu, Y. et al. Selective stabilization and photophysical properties of metastable perovskite polymorphs of CsPbI3 in thin films. Chem. Mater. 29, 8385–8394 (2017).
Grechko, M., Bretschneider, S. A., Vietze, L., Kim, H. & Bonn, M. Vibrational coupling between organic and inorganic sublattices of hybrid perovskites. Angew. Chem. Int. Ed. 57, 13657–13661 (2018).
Guo, P. et al. Slow thermal equilibration in methylammonium lead iodide revealed by transient mid-infrared spectroscopy. Nat. Commun. 9, 2792 (2018).
Whitfield, P. S. et al. Structures, phase transitions and tricritical behavior of the hybrid perovskite methyl ammonium lead iodide. Sci. Rep. 6, 35685 (2016).
Yang, Y. et al. Large polarization-dependent exciton optical Stark effect in lead iodide perovskites. Nat. Commun. 7, 12613 (2016).
Elles, C. G., Cox, M. J. & Crim, F. F. Vibrational relaxation of CH3I in the gas phase and in solution. J. Chem. Phys. 120, 6973–6979 (2004).
Ong, W.-L. et al. Orientational order controls crystalline and amorphous thermal transport in superatomic crystals. Nat. Mater. 16, 83–88 (2016).
Ong, W.-L., Rupich, S. M., Talapin, D. V., McGaughey, A. J. H. & Malen, J. A. Surface chemistry mediates thermal transport in three-dimensional nanocrystal arrays. Nat. Mater. 12, 410–415 (2013).
Davies, C. L. et al. Bimolecular recombination in methylammonium lead triiodide perovskite is an inverse absorption process. Nat. Commun. 9, 293 (2018).
Stoumpos, C. C. et al. Ruddlesden–Popper hybrid lead iodide perovskite 2D homologous semiconductors. Chem. Mater. 28, 2852–2867 (2016).
Wright, A. D. et al. Electron–phonon coupling in hybrid lead halide perovskites. Nat. Commun. 7, 11755 (2016).
Milot, R. L., Eperon, G. E., Snaith, H. J., Johnston, M. B. & Herz, L. M. Temperature-dependent charge-carrier dynamics in CH3NH3PbI3 perovskite thin films. Adv. Funct. Mater. 25, 6218–6227 (2015).
Onoda-Yamamuro, N., Matsuo, T. & Suga, H. Calorimetric and IR spectroscopic studies of phase transitions in methylammonium trihalogenoplumbates (II)†. J. Phys. Chem. Solids 51, 1383–1395 (1990).
Guo, Z. et al. Long-range hot-carrier transport in hybrid perovskites visualized by ultrafast microscopy. Science 356, 59–62 (2017).
Guo, P. et al. Cross-plane coherent acoustic phonons in two-dimensional organic-inorganic hybrid perovskites. Nat. Commun. 9, 2019 (2018).
Smith, M. D. & Karunadasa, H. I. White-light emission from layered halide perovskites. ACC Chem. Res. 51, 619–627 (2018).
Yang, M. et al. Square-centimeter solution-processed planar CH3NH3PbI3 perovskite solar cells with efficiency exceeding 15%. Adv. Mater. 27, 6363–6370 (2015).
Kresse, G. & Hafner, J. Ab initio molecular dynamics for liquid metals. Phys. Rev. B 47, 558–561 (1993).
Kresse, G. & Hafner, J. Ab initio molecular-dynamics simulation of the liquid-metal--amorphous-semiconductor transition in germanium. Phys. Rev. B 49, 14251–14269 (1994).
Kresse, G. & Furthmüller, J. Efficiency of ab-initio total energy calculations for metals and semiconductors using a plane-wave basis set. Comput. Mater. Sci. 6, 15–50 (1996).
Kresse, G. & Furthmüller, J. Efficient iterative schemes for ab initio total-energy calculations using a plane-wave basis set. Phys. Rev. B 54, 11169–11186 (1996).
Blöchl, P. E. Projector augmented-wave method. Phys. Rev. B 50, 17953–17979 (1994).
Perdew, J. P., Burke, K. & Wang, Y. Generalized gradient approximation for the exchange-correlation hole of a many-electron system. Phys. Rev. B 54, 16533–16539 (1996).
Hohenberg, P. & Kohn, W. Inhomogeneous electron gas. Phys. Rev. 136, B864–B871 (1964).
Klimeš, J., Bowler, D. R. & Michaelides, A. Van der Waals density functionals applied to solids. Phys. Rev. B 83, 195131 (2011).
Togo, A. & Tanaka, I. First principles phonon calculations in materials science. Scr. Mater. 108, 1–5 (2015).
Li, W., Carrete, J., A. Katcho, N. & Mingo, N. ShengBTE: a solver of the Boltzmann transport equation for phonons. Comput. Phys. Commun. 185, 1747–1758 (2014).
Momma, K. & Izumi, F. VESTA 3 for three-dimensional visualization of crystal, volumetric and morphology data. J. Appl. Crystallogr. 44, 1272–1276 (2011).
Humphrey, W., Dalke, A. & Schulten, K. VMD: Visual molecular dynamics. J. Mol. Graph. 14, 33–38 (1996).
Brivio, F. et al. Lattice dynamics and vibrational spectra of the orthorhombic, tetragonal, and cubic phases of methylammonium lead iodide. Phys. Rev. B 92, 144308 (2015).
The work was performed, in part, at the Center for Nanoscale Materials, a U.S. Department of Energy Office of Science User Facility, and supported by the U.S. Department of Energy, Office of Science, under Contract No. DE-AC02-06CH11357. This material is based upon work supported by Laboratory Directed Research and Development (LDRD) funding from Argonne National Laboratory, provided by the Director, Office of Science, of the U.S. Department of Energy under contract DE-AC02-06CH11357. Work at Northwestern University was supported by grant SC0012541 from the US Department of Energy, Office of Science (sample preparation). T.X. acknowledges the financial support from National Science Foundation (DMR-1806152). We thank Dr. A. B. F. Martinson for comments on the paper.
The authors declare no competing interests.
Journal peer review information: Nature Communications thanks Daniel Vanmaekelbergh and the other anonymous reviewer(s) for their contribution to the peer review of this work.
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Guo, P., Mannodi-Kanakkithodi, A., Gong, J. et al. Infrared-pump electronic-probe of methylammonium lead iodide reveals electronically decoupled organic and inorganic sublattices. Nat Commun 10, 482 (2019). https://doi.org/10.1038/s41467-019-08363-2