Skip to main content

Thank you for visiting nature.com. You are using a browser version with limited support for CSS. To obtain the best experience, we recommend you use a more up to date browser (or turn off compatibility mode in Internet Explorer). In the meantime, to ensure continued support, we are displaying the site without styles and JavaScript.

Direct investigation of the reorientational dynamics of A-site cations in 2D organic-inorganic hybrid perovskite by solid-state NMR

Abstract

Limited methods are available for investigating the reorientational dynamics of A-site cations in two-dimensional organic–inorganic hybrid perovskites (2D OIHPs), which play a pivotal role in determining their physical properties. Here, we describe an approach to study the dynamics of A-site cations using solid-state NMR and stable isotope labelling. 2H NMR of 2D OIHPs incorporating methyl-d3-ammonium cations (d3-MA) reveals the existence of multiple modes of reorientational motions of MA. Rotational-echo double resonance (REDOR) NMR of 2D OIHPs incorporating 15N- and ¹³C-labeled methylammonium cations (13C,15N-MA) reflects the averaged dipolar coupling between the C and N nuclei undergoing different modes of motions. Our study reveals the interplay between the A-site cation dynamics and the structural rigidity of the organic spacers, so providing a molecular-level insight into the design of 2D OIHPs.

Introduction

Organic–inorganic hybrid perovskites (OIHPs) have attracted a significant amount of attention for photovoltaic applications since their power conversion efficiency (PCE) has reached over 25%1, which is already approaching the performance of commercial Si-based solar cells. The impressive PCE of OIHP photovoltaics is mainly attributed to their outstanding physical properties, such as a high optical absorption coefficient2, low exciton binding energy3 and long and balanced electron–hole diffusion length4,5. The chemical formula of OIHP is represented as ABX3 where A is an organic cation, such as methylammonium (MA+), B is a divalent metal cation, such as lead(II) ion (Pb2+) and X is a halide anion6,7. Although the electronic structure of OIHP near the band edges is mainly determined by the inorganic Pb and halide ions, A-site organic cations have also been reported to play an important role in affecting the device performance and stability, instead of only acting as a passive component for a charge compensation for the [PbI3] lattice8,9,10,11,12,13. For example, it has been proposed that the molecular rotations of A-site cations may cause distortion of the PbI6 octahedral unit, the consequent dynamical change of the band structure being at the origin of the slow carrier recombination and the superior conversion efficiency of CH3NH3PbI314. Several experimental techniques have revealed the dynamics of A-site cations, including solid-state nuclear magnetic resonance (ssNMR)10,15,16, neutron powder diffraction (NPD)17 and inelastic neutron scattering18,19. In particular, ssNMR has emerged as a useful tool for studying OIHP20 and the cation reorientational dynamics in OIHP. The interplay between the charge carrier lifetimes and the reorientational dynamics of A-site cations in OIHP photovoltaics has been providing evidence of the polaronic nature of charge carriers in perovskite photovoltaics10,15,21.

Recently, two-dimensional organic–inorganic hybrid perovskites (2D OIHPs) have attracted great attention owing to their superior ambient stability, and promising optoelectronic properties22,23,24,25. Ruddlesden–Popper perovskites are a typical example of layered 2D organic–inorganic hybrid perovskites having the generic chemical formula A′2An−1MnX3n+1. In this formula, A′ represents an organic spacer, such as long-chain alkylammonium cation (e.g. 1-butylammonium, BA+) or phenyl alkylammonium cation (e.g. 2-phenethylammonium, PEA+), A is an organic cation, M is a metal, X is a halide and n is the number of octahedral slabs per unit cell26,27,28,29. Layered 2D OIHP consists of a self-assembled periodic array of inorganic perovskite layers of corner-sharing PbX6 octahedral slabs, separated by the organic spacers in the lattice framework30,31. Accordingly, they exhibit a naturally formed “multiple quantum-well” (MQW) structure. The semiconducting inorganic PbX6 perovskites, with a smaller bandgap, act as potential “wells”, while the insulating organic layers, possessing a larger bandgap, act as potential “barriers”. The value of n is the number of inorganic octahedral slabs per unit cell that determines the width of the QW32,33,34. Layered 2D OIHPs have emerged as a new class of outstanding optoelectronic materials due to their unique tunable physical properties, and structural flexibility, achieved by controlling the value of n and the thickness of the perovskite slabs35,36,37. Because layered 2D OIHPs incorporate organic spacers between the flexible inorganic layers, they exhibit a greater structural versatility compared to their 3D OIHP counterparts38. It has been reported that the manipulations of the A-site cations and organic spacers may cause the structural rearrangement, or deformation, of the PbI6 octahedral unit in 2D OIHPs, which may further influence their electronic band structures near the band edges, and the corresponding optical and electronic behaviours39,40,41. Unlike their 3D OIHP counterparts consisting of only A-site cations, the detection of reorientation dynamics of A-site cations in 2D OIHPs with n ≥ 2 by ssNMR is a challenging task due to signal overlap with the additional organic spacers. Subsequently, the conventional 1H and 14N NMR relaxation methods for characterising the dynamics of cations in 3D OIHP10,15,16 are not applicable for studying the dynamics of A-site cations in 2D OIHPs. Until now, only the dynamics of the organic spacers at the 2D OIHP crystals have been analysed based on these ssNMR methods29,41,42,43,44. Here, we employed isotope labelling to distinguish A-site from spacer cations and avoid spectral overlap in 2D OIHPs with n = 2. Specifically, we employed 13C,15N-MA and CD3NH3+ as A-site cations, and investigated the dynamics of A-site molecular cations by REDOR NMR and 2H NMR, respectively.

To study the dynamics of MA, we first applied two-dimensional 13C–15N correlation double cross-polarisation magic-angle spinning spectroscopy45, 2D (13C,15N) DCP MAS, to observe the NMR signal of MA with a substantial sensitivity enhancement and without the interference of the signal of the spacer cations. REDOR NMR and 2H NMR were further employed to study the reorientational dynamics of MA in 2D OIHPs, which provides motional average to the dipolar coupling between the 13C and 15N nuclei of 13C,15N-MA and to the deuterium quadrupole coupling of CD3NH3+, respectively. Accordingly, both the environments and the dynamics of A-site molecular cations can be revealed. We further characterised the structural and optoelectronic properties of 2D OIHPs using powder X-ray diffraction spectroscopy (PXRD), absorption spectroscopy and photoluminescence spectroscopy (PL), in addition to 13C CPMAS NMR characterisation of the incorporated spacer molecules at the various temperatures. Our PXRD and PL results indicated that the choice of the spacer could influence the structures and the optoelectronic properties of 2D OIHPs, as mentioned in the literature33,39,41. We further showed that a 1-butylammonium spacer (BA+) is less rigid than a 2-phenethylammonium spacer (PEA+) according to our 13C CPMAS NMR results. Finally, the detection of the reorientational dynamics of MA by the two ssNMR methods reported here allows us to further examine the interplay between the rigidity of organic spacers and the dynamics of the A-site cations in 2D OIHPs. The present study complements previous NMR studies focusing on the spacer molecules or the frameworks29,41,42,43,44, and should provide insights into the future design of 2D OIHP materials.

Results

Dynamics of A-site cations of 2D OIHPs

We compared two types of 2D OIHP, one containing the 1-butylammonium spacer (2D (BA)2MAPb2I7 (n = 2)) and one containing the 2-phenethylamine spacer (2D (PEA)2MAPb2I7 (n = 2)). Both were synthesised using the slow evaporation at a constant-temperature (SECT) growth method28. For comparison, we also synthesised 3D MAPbI3, in which no organic spacer is present. The perovskites were synthesised using methylammonium iodide (MAI) that was 13C,15N-labeled, methyl-d3-labeled or natural abundance.

13CH315NH3I (13C,15N-MAI) was synthesised from commercially available 13CH3I and 15N-phthalimide following the classic Gabriel synthesis (Supplementary Methods). The 2D (13C,15N) DCP MAS NMR of the 2D OIHP crystals synthesised with 13C,15N-methylammonium iodide exhibited signal solely from the dipolar-coupled 13C–15N spin pair, which is practically absent (comprising 0.004%) from a natural-abundance sample. The purity of the 2D OIHP samples was examined by PXRD spectroscopy, which confirmed the single-crystal structure of 2D OIHP (Supplementary Fig. 1). The PL spectra of the natural-abundance and 13C,15N materials were nearly identical as shown in Supplementary Fig. 2. Thus, the structural and the physical properties of 2D OIHPs were not noticeably altered by the 13C and 15N nuclei. As shown in Fig. 1b, the natural-abundance methylamine (MA) signal is poor and largely overlapped with the C2 signal of BA. In contrast, the 2D (13C,15N) DCP MAS spectra of the 13C,15N-labeled 2D OIHP allow observation of the 13C–15N spin pair free of interference from the signals of the spacer cations (Fig. 1c). This also enabled the unambiguous assignment of the resonance peaks of the unlabeled MA in Fig. 1b. Notably, the 2D (13C,15N) DCP MAS spectrum of 2D (BA)2(13C,15N-MA)Pb2I7 (n = 2) contains two cross-peaks (Fig. 1c), suggesting the existence of the two different local environments of the A-site MA. The major component corresponds to a 31.4 ppm peak, while the minor component is associated with a 27.2 ppm peak in the 13C direct excitation MAS spectrum (Fig. 1b). Comparison of the 13C NMR spectra of the 13C,15N-perovskite and the 13C,15N-methylammonium iodide precursor (Supplementary Fig. 3) ruled out the possibility of the minor MA component being the unreacted 13C,15N-methylammonium iodide precursor. Moreover, the PXRD and UV data (Supplementary Figs. 1 and 2) showed one series of periodic repetitions of Miller planes and one excitonic absorption peak in both the 13C,15N-labeled and the unlabeled 2D (BA)2MAPb2I7 (n = 2). Thus, the minor MA spectral component indicates the presence of minor structural impurity, as suggested in a recent work46. The amount of the minor MA component was estimated to be roughly 3% of the total amount of MA based on the ratio of the peak intensities of the 13C direct excitation MAS spectrum. In contrast, only one local environment of MA in 2D (PEA)2(13C,15N-MA)Pb2I7 (n = 2) was observed in Fig. 1c. Interestingly, the intensity of the cross peak of the major MA component of 2D (BA)2(13C,15N-MA)Pb2I7 (n = 2) is less than that of the minor MA component, suggesting that the major MA component is associated with the lower transfer efficiency of double cross-polarisation (DCP). The reason for the lower DCP transfer efficiency is attributed to the presence of the reorientational motion of the C–N bond of MA. In summary, different local environments and the dynamics of the A-site cations were observed in 2D OIHP crystals incorporated with different organic spacers.

Fig. 1: 13C NMR spectral characterisation of 2D OIHP crystals (n = 2).
figure 1

a The structural models of 2D (BA)2(MA)Pb2I7 (n = 2) and 2D (PEA)2(MA)Pb2I7 (n = 2). b The 13C CPMAS spectra of 2D (BA)2(MA)Pb2I7 (n = 2) and 2D (PEA)2(MA)Pb2I7 (n = 2) synthesised with 13C,15N-MA, respectively. The spectra with ×20 magnification are shown on the top, overlayed with the spectra of the materials synthesised with natural-abundance MA. The two sets of spectra have been normalised by the height of the C1 carbon peak of BA and the aromatic carbon peak at 130.7 ppm, respectively. c 2D DCP MAS (13C,15N) correlation spectra of 2D (BA)2(13C,15N-MA)Pb2I7 (n = 2) and 2D (PEA)2(13C,15N-MA)Pb2I7 (n = 2), respectively. The 13C direct excitation MAS NMR spectra are overlayed on the top.

The reorientation dynamics of the MA cation can be studied in a quantitative manner by 13C{15N}REDOR NMR, which measures the time evolution of the internuclear dipolar interaction. The pulse sequence is shown in Fig. 2a, where 13C is the observed spin and 15N is the dephasing spin. Two sets of the interleaved experimental REDOR signals were recorded. The full echo signal, denoted as S0, was recorded without the dephasing pulses and the reduced echo signal, denoted as S, was recorded with the dephasing pulses switched on to recouple the dipolar interaction of the 13C–15N spin pairs. The data were plotted as a REDOR dephasing curve of ΔS/S0 versus different dephasing times N × Tr, where Tr is the rotor period and N is 2(n + 1). In a typical solid-state powder, in the absence of reorientational motion, the distance-dependent nature of the REDOR dephasing curve allows for the extraction of internuclear distances at angstrom resolution47. A powder sample of 13C,15N-MAI crystals was used as a reference, where the reorientational motion of the 13C–15N vector is absent. Fitting the experimental 13C{15N}REDOR results (orange open circles) to a simulated dephasing curve (orange dashed line) indicate a C–N bond length of 1.51 Å, consistent with published single-crystal X-ray crystallography bond lengths of 1.469–1.516 Å33,48,49,50,51.

Fig. 2: 13C{15N}REDOR NMR characterisation.
figure 2

a 13C{15N}REDOR NMR pulse sequence. b The experimental {13C}15N REDOR dephasing curve of the precursor 13C,15N-MAI powder. The dashed line is the REDOR curves simulated using the length of carbon-nitrogen bond of MA molecule reported in X-ray crystallography research33, 48,49,50,51. c The {13C}15N REDOR spectra at the 2.4 ms dephasing time of 13C,15N-MAI powder, 2D (PEA)2(13C,15N-MA)Pb2I7 (n = 2), 2D (BA)2(13C,15N-MA)Pb2I7 (n = 2) and 3D (13C,15N-MA)PbI3.

While REDOR NMR is a popular method for measuring the internuclear distance at atomic resolution, it can also be applied to study the molecular motion of a dipolar-coupled nuclear spin pair52,53. Using a model-free approach54,55, the theoretical analysis of REDOR dephasing for a 13C–15N spin pair undergoing reorientational motion of the 13C-15N vector is described in Supplementary Methods. An order parameter \({{{{{\mathscr{S}}}}}}\) is used to describe the motional modulation of the effective dipolar interaction54,55. For the case of a rigid 13C–15N vector, in the absence of reorientational motion, \({{{{{\mathscr{S}}}}}}=1\) and the REDOR dephasing maximum appears around 2 ms of the dephasing time. In contrast, no REDOR dephasing will be observed if the 13C–15N vector is undergoing completely random reorientational motion (\({{{{{\mathscr{S}}}}}}=0\)). In the case of \(0 \, < \, {{{{{\mathscr{S}}}}}} \, < \, 1\), a reduced REDOR dephasing value around 2 ms of the dephasing time will be obtained, as indicated in Supplementary Fig. 4. Experimentally, we chose to compare the 13C{15N}REDOR dephasing values (ΔS/S0) at 2.4 ms of the dephasing time, denoted as (ΔS/S0)2.4ms, of the various samples so that the xy-8 phasing cycling could be applied to the dephasing pulses. Given that 10 kHz of the MAS frequency was used in this series of REDOR experiments, a reduced 13C{15N} REDOR (ΔS/S0)2.4ms value indicated that the presence of the reorientational motion of the C–N vector partially averaged out the 13C–15N dipole-dipole interaction over the period of 100 μs. In summary, the degree of the motional averaging caused by the reorientational motion of the C–N vectors can be characterised by an order parameter \({{{{{\mathscr{S}}}}}}\) and can be directly associated with the reduction of the 13C{15N} REDOR (ΔS/S0)2.4ms values.

We systematically studied the reorientational dynamics of 13C,15N-MA incorporated in three different perovskite crystals by measuring the effective 13C–15N dipolar interactions of 13C,15N-MA using 13C{15N}REDOR NMR. While the (ΔS/S0)2.4ms value of the powder sample of 13C,15N-MAI crystals (rigid 13C-15N vector, \({{{{{\mathscr{S}}}}}}=1\)), was around the maximum value of 1, reduced (ΔS/S0)2.4ms values were observed for the three perovskite samples: 2D (PEA)2(13C,15N-MA)Pb2I7 (n = 2), 2D (BA)2(13C,15N-MA)Pb2I7 (n = 2), and 3D (13C,15N-MA)PbI3 (Fig. 2(c)–(f)). No organic spacer is present in the 3D (13C,15N-MA)PbI3 which was included for comparison. The minor MA peak of 2D (BA)2(13C,15N-MA)Pb2I7 (n = 2) was fully dephased at 2.4 ms indicating the absence of the reorientational motion of MA. In contrast, the (ΔS/S0)2.4ms values observed for 3D (13C,15N-MA)PbI3 and the major MA peak in 2D (BA)2(13C,15N-MA)Pb2I7 (n = 2) were less than 10%, indicating that MA cations in these two samples underwent reorientational motion. Interestingly, the (ΔS/S0)2.4ms value measured for the 2D (PEA)2(13C,15N-MA)Pb2I7 sample was greater than the (ΔS/S0)2.4ms values for 2D (BA)2(13C,15N-MA)Pb2I7 by more than 10%. Thus, the A-site cations undergo more restricted reorientational motion in 2D (PEA)2(13C,15N-MA)Pb2I7 than in (BA)2(13C,15N-MA)Pb2I7.

To explore the spacer-dependent dynamics of the A-site cation, the REDOR (ΔS/S0)2.4ms values of 13C{15N}REDOR experiments were recorded at various temperatures. As plotted in Fig. 3, only minor change of the REDOR (ΔS/S0)2.4ms values were measured for 3D (13C,15N-MA)PbI3 during the cooling process from 308 to 243 K, indicating that the reorientational motion of the A-site MA did not change significantly in this temperature range. By contrast, there was an obvious change of the REDOR (ΔS/S0)2.4ms values of 2D (BA)2(13C,15N-MA)Pb2I7 (n = 2) which were found to increase from 0.06 at 308 K, to 0.43 at 243 K, implying that the reorientational motion of MA becomes more restricted as the temperature decreases. In contrast, the reorientational motion of MA in 2D (PEA)2(13C,15N-MA)Pb2I7 (n = 2) changed only slightly during cooling, as seen from the slightly increased REDOR (ΔS/S0)2.4ms value.

Fig. 3: The temperature-dependent 13C{15N}REDOR dephasing (ΔS/S0) of 13C,15N-MA incorporated in different materials.
figure 3

The ΔS/S0 of MA peak in 2D (PEA)2(13C,15N-MA)Pb2I7 (n = 2) (blue solid squares), 2D (BA)2(13C,15N-MA)Pb2I7 (n = 2) (red open triangles)* and 3D (13C,15N-MA)PbI3 (black solid squares) at the dephasing time of 2.4 ms. *The data were obtained from the major MA peak of 2D (BA)2(13C,15N-MA)Pb2I7 (n = 2).

Lineshape analysis of 2H NMR spectra can yield useful information about the motion of the deuterium quadrupole in solid. 2H NMR spectra of 2D (PEA)2(d3-MA)Pb2I7 (n = 2) and 2D (BA)2(d3-MA)Pb2I7 (n = 2) were acquired at 11.7 T in the 243–298 K range. For a non-rotating CD3 group, the quadrupole splitting (νQ), measured cusp to cusp of the 2H spectrum, would be ~120 kHz. Rapid C3 rotation would reduce this νQ value three-fold to ~40 kHz. The existence of additional reorientational motion of the C3 axis would result in a narrower spectral lineshape11. Interestingly, multiple νQ values were observed from the 2H NMR spectra of both 2D OIHPs (Fig. 4), suggesting the existence of multiple modes of reorientational motions. It worth mentioning that there was only one chemical environment observed for the MA in 2D (PEA)2(13C,15N-MA)Pb2I7 (n = 2) as indicated in Fig. 1c. The existence of multiple modes of the C–N reorientational motion was also suggested previously in 3D MAPbI3 perovskite crystals using neutron powder diffraction17, quasielastic neutron scattering measurement18 and first-principle calculations56. The orientation of the C–N vector and the geometry of its motion with respect to the molecular frame of 2D perovskite crystals are needed to construct a detailed model for quantitative analysis of the 2H NMR spectra. However, these parameters are not currently available in the literature. Nonetheless, we can still learn about the reorientational motion of the C–N vector based on qualitative analysis. The 2H NMR spectral lineshape of 2D (BA)2(d3-MA)Pb2I7 (n = 2) was shown to widen significantly as the temperature was decreased from 298 to 243 K, indicating that the reorientational motion of the C–N vector changed significantly as the temperature was decreased. This result is consistent with our REDOR result, showing the significant change of the 13C{15N} REDOR (ΔS/S0)2.4ms values of 2D (BA)2(13C,15N-MA)Pb2I7 during cooling. In contrast, no obvious change of the 2H NMR spectral lineshape of 2D (PEA)2(d3-MA)Pb2I7 was observed during cooling. This finding echoes the REDOR data for 2D (PEA)2(13C,15N-MA)Pb2I7. Overall, we observed that the choice of the spacer cation in 2D perovskite affects the temperature dependence of the reorientational motional of MA. It is worth mentioning that full REDOR dephasing at 2.4 ms was observed for 3% (the minor component) of MA in 2D (BA)2(d3-MA)Pb2I7, indicating the absence of the reorientational motion of the C–N vector. The quadrupole splitting (νQ) associated with the minor MA component in 2D (BA)2(d3-MA)Pb2I7 should therefore be equal or greater than 40 kHz, which was not observed (Fig. 3a). This discrepancy may be due to the low sensitivity of the deuterium spectra, compared to that of the 13C spectra of 13C,15N-MA.

Fig. 4: 2H NMR spectra of 2D OIHP crystals (n = 2).
figure 4

The full-scale 2H spectra of a 2D (BA)2(d3-MA)Pb2I7 (n = 2) and b 2D (PEA)2(d3-MA)Pb2I7 (n = 2) recorded at various temperatures, ranging from 298 to 243 K.

13C CPMAS NMR, PXRD and DSC Characterisations

To further investigate the response of the spacer cations during cooling, the 13C CPMAS NMR spectra of 2D OIHPs were recorded at various temperatures. Figure 5a, b presents the magnified 13C CPMAS NMR spectra, highlighting the resonance peaks of the spacer cations of the two 2D OIHPs. An obvious conformational change of the 1-butylammonium (BA+) cation spacer in 2D (BA)2(13C,15N-MA)Pb2I7 (n = 2) was observed, where the 13C resonances of C3 and C4 of BA are split into two peaks, during the cooling process from 268 to 243 K. The peak splitting shows the existence of two BA conformations in this temperature range, indicating the packing geometry of the BA molecules was altered during cooling. In contrast, neither peak splitting nor peak position changes were found in the 13C CPMAS NMR spectrum of 2D (PEA)2(13C,15N-MA)Pb2I7 (n = 2) during the cooling process, indicating no change in the conformation and the chemical environment of PEA. A signal reduction of a phenyl carbon resonance peak at 130 ppm with increasing temperature may be due to the flipping of the phenyl ring. The full-scale 13C CPMAS NMR spectra which highlight the resonance peaks of the molecular cation MA, are also shown in Supplementary Fig. 5. There is no obvious change of the peak position nor intensity for the 13C resonance peak of MA for the PEA-based 2D OIHPs. In contrast, the major peak of MA in 2D (BA)2(13C,15N-MA)Pb2I7 (n = 2) displays a clear up-field shift and significant intensity increase on cooling from 298 to 268 K, suggesting that a change in the MA chemical environment accompanied the change of the packing geometry of the BA ions. Differential scanning calorimetry (DSC) and PXRD were further used to study the structural response of 2D (BA)2(MA)Pb2I7 (n = 2) and 2D (PEA)2(MA)Pb2I7 (n = 2) during the cooling process. The endothermic peak observed in the DSC measurement of 2D (BA)2(MA)Pb2I7 (n = 2) indicated a clear phase change occurring at ~280 K (Supplementary Fig. 6). This echoes the finding in a recent study33, showing the associated phase change was from Cmcm to P-1 space group. In contrast, no evidence of phase change was found in the DSC measurement of (PEA)2(MA)Pb2I7 (n = 2). Moreover, based on the comparison of PXRD patterns recorded at 300 K and 250 K (Fig. 5c, d) a clear structural change for (BA)2(MA)Pb2I7 (n = 2) was observed with cooling from 300 to 250 K, while no change was observed for the (PEA)2(MA)Pb2I7 (n = 2).

Fig. 5: The 13C CPMAS spectra and PXRD spectra of 2D OIHP crystals (n = 2).
figure 5

The 13C CPMAS spectra of a 2D (BA)2(13C,15N-MA)Pb2I7 (n = 2) and b 2D (PEA)2(13C,15N-MA)Pb2I7 (n = 2) recorded at various temperatures, ranging from 308 to 243 K. The PXRD patterns of c 2D (BA)2MAPb2I7 (n = 2) and d 2D (PEA)2MAPb2I7 (n = 2) measured at 300 K (black colour) and 250 K (blue colour). The red dashed boxes highlight the obvious changes of the 13C CPMAS and PXRD spectra during cooling.

PL characterisation

It is well-known that the structural deformation of the octahedral layers, induced by changing the packing geometry of the organic spacers, may strongly affect the optical and electronic properties of 2D OIHPs33,39,41. Photoluminescence spectroscopy (PL) during the cooling from 300 to 250 K revealed a significant blue shift from 581 to 574 nm in 2D (BA)2(13C,15N-MA)Pb2I7 (n = 2), as shown in Supplementary Fig. 7. The corresponding PL emission peak of 2D (PEA)2(13C,15N-MA)Pb2I7 (n = 2) remained unshifted. The results suggest that the phase change or structural deformation of 2D OIHPs induced by changing the packing geometry of the organic spacers, may strongly affect the optical properties of 2D OIHPs.

The role of the rigidity of spacer cation in 2D OIHPs

These results may help to elucidate the important role of the organic spacers in determining the structure and properties of 2D OIHPs. Flexible alkyl-chain cations such as 1-butylammonium (BA) produce a more fluctuating structure at ambient conditions compared to 2D OIHPs based on 2-phenethylammonium (PEA) cations, consistent with recent theoretical results38. The CH-π stacking between the aromatic rings of the PEA spacer may restrict thermal motions between two inorganic perovskite layers. By contrast, there is no such interaction among the alkyl BA cations, which may result in more flexibility and more structural dynamics in the inorganic perovskite layers. Accordingly, the 2D OIHP crystal, consisting of PEA organic spacers, exhibits a relatively rigid structure with lower conformational freedom of the crystal structure, as compared to its BA counterpart. That temperature-induced structural change of 2D OIHPs with cooling is mainly attributed to the influence of the organic spacers can also be concluded from the 13C CPMAS NMR spectra of 2D OIHP (n = 1), which lack A-site cations (Supplementary Fig. 8). For 2D OIHPs consisting of BA spacers, the structural deformation of the inorganic PbI6 octahedral layers with cooling was induced by changing the packing geometry of BA, as seen from the ssNMR, PXRD and DSC data. In contrast, there was no such structural deformation of the inorganic octahedral layers in the 2D OIHPs consisting of PEA spacers with cooling in this temperature range.

Discussion

Here, we used two different ssNMR methods to study the reorientational motions of the A-site cation MA incorporated in 2D OIHPs with n ≥ 2. The reorientational motion of the C–N bond of MA modulates the effective dipolar coupling between the 13C and 15N nuclei of 13C,15N-MA, which can be studied using REDOR NMR. The same reorientational motion of the C–N bond of MA also modulates the quadrupolar splitting (νQ) of the 2H NMR spectra of CD3NH3+ incorporated in 2D OIHPs. Thus, the 2H NMR lineshape also reflects the reorientational dynamics of the C–N vector.

REDOR NMR analyses were performed on 13C,15N-MAI crystal powder, 2D (BA)2(13C,15N-MA)Pb2I7 (n = 2), 2D (PEA)2(13C,15N-MA)Pb2I7 (n = 2) and 3D (13C,15N-MA)PbI3, to compare the reorientational dynamics of 13C,15N-MA incorporated in different materials. The reorientational motion of MA is absent for the 13C,15N-MAI crystal powder sample, evident from the consistency between the experimental REDOR curve and the simulated REDOR curve using the carbon-nitrogen bond length obtained in single-crystal X-ray studies. The 13C,15N-MA in 2D (PEA)2(13C,15N-MA)Pb2I7 (n = 2) was found to undergo a more restricted reorientational motion at room temperature when compared to 2D (BA)2(13C,15N-MA)Pb2I7 (n = 2) and 3D (13C,15N-MA)PbI3. Moreover, an obvious change of the reorientational dynamics of 13C,15N-MA in 2D (BA)2(13C,15N-MA)Pb2I7 (n = 2) occurred during cooling from 298 to 268 K, evident from an obvious increase in the 13C{15N} REDOR (ΔS/S0)2.4ms value. It is worth mentioning that the significant change in the reorientational dynamics can also be correlated to the significant change of the chemical environment of MA, evident from the clear up-field shift and a significant increase in the intensity of the 13C CPMAS resonance peak of MA during cooling from 298 to 268 K. In contrast, only slight changes of MA reorientational dynamics were observed in 2D (PEA)2(13C,15N-MA)Pb2I7 (n = 2) and 3D (13C,15N-MA)PbI3 with cooling. Accordingly, the change of the dynamics of the A-site cations in response to temperature change depends on the choice of the spacer cations of 2D OIHPs. The results of the temperature variation 2H NMR lineshape analyses of d3-MA incorporated in 2D OIHPs are consistent with the REDOR NMR results, showing that the choice of the spacer cations in 2D OIHPs may affect the reorientational dynamics of the A-site cations. It is important to note that 2H NMR lineshape analyses further revealed the existence of the multiple modes of the reorientational motions of MA. Thus, we should interpret the dipolar coupling measured in our REDOR measurements as the average dipolar coupling between the 13C and 15N nuclei of MA undergoing different modes of motions, which are characterised by different values of the order parameters. We recorded both 13C CPMAS NMR and PXRD at different temperatures to investigate the structural changes of the organic spacer cations and of the inorganic frameworks of 2D OIHPs with cooling, respectively. 2D BA-based OIHP exhibits less structural rigidity than 2D PEA-based OIHP. The structural deformation of the octahedral perovskite layers induced by the conformational change of the alkyl BA spacers in the 2D BA-based OIHPs occurs with cooling33. In contrast, there is no such structural change in both the inorganic framework of perovskites and the conformation of organic spacers in the 2D PEA-based OIHPs, evident from the ssNMR and PXRD analyses, respectively. Consequently, the structural deformation of the inorganic octahedral layers induced by changing the packing geometry of the BA organic spacers occurs on cooling, resulting in the change of the reorientational motion of the A-site cations and the change of optoelectronic property indicated by the shift in the PL spectrum. When the rigid spacer cation PEA was incorporated in 2D OIHP crystals, there is no such significant change neither in the conformation of the spacer cation nor in the inorganic frameworks with cooling. Consequently, the reorientational dynamics of the A-site cation were found to stay relatively unchanged in the PEA-containing 2D OIHPs. In conclusion, the ssNMR study provides information on the reorientational dynamics of the A-site cation in 2D OIHP crystals. The study further unveiled that the dynamics of the A-site cation in 2D OIHP is affected by the crystal structures, which are influenced by the choice of the organic spacers. The interplay between the rigidity of the organic spacers and the A-site cations dynamics of 2D OIHPs is clearly unveiled, even though there is no direct bonding between the A-site cations and the organic spacers. Our results may provide a deep insight into the future design of 2D OIHPs at a molecular level.

Methods

Synthesis of 2D organic–inorganic hybrid perovskite

The chemicals, including lead(II) oxide (PbO, ≥99.9%), 57% aqueous hydriodic acid (HI) in H2O, 50% aqueous hypophosphorous acid (H3PO2) in H2O, 99.5% 1-butylamine (BA), 99% 2-phenethylamine (PEA), 99% methyl-d3-amine hydrochloride and ≥99% natural-abundance methylamine hydroiodide (MAI), were purchased from Sigma-Aldrich (St. Louis). The synthesis of 13C-methyl-15N-ammonium iodide, 13C,15N-MAI is described in the Supplementary Methods. The 2D OIHP crystals were synthesised according to Chen et al.28. Briefly, a mixed solution containing 10 ml of hydriodic acid, 57 wt.% in H2O and 1.7 mL of hypophosphorous acid solution, 50 wt.% in H2O, was prepared to dissolve 10 mmol PbO at 80 °C and stirred continuously at 600 rpm to obtain a yellow coloured PbI2 solution. BAI was obtained by adding 10 mmol BA in 5 mL HI solution incubated in an ice bath. The BAI solution was slowly added into the PbI2 solution at 80 °C to obtain orange-colour precipitates, and then the mixed solution was heated up to 100 °C to dissolve the reprecipitates. The solution was cooled down to room temperature to obtain orange flakes of 2D (BA)2PbI4 (n = 1) compound. For the synthesis of 2D (BA)2(MA)Pb2I7 (n = 2), a stoichiometric quantity of the 5 mmol MAI was first dissolved into the PbI2 solution to produce black precipitates of MAPbI3, and then re-dissolved by heating up to 110 °C to obtain a clear yellow solution. BAI solution was obtained by adding 7 mmol BA in 5 mL HI solution incubated in an ice bath. The BAI solution was then added dropwise into the clear yellow solution at 110 °C. Finally, the solution was cooled down to room temperature to obtain red flakes of 2D (BA)2MAPb2I7 (n = 2) compound. Similar procedures were followed for preparing 2D (PEA)2(MA)n-1PbnI3n+1 crystals with n = 1 and n = 2, except that the different molar ratios of the precursors were used. The molar ratios of the precursors, PbO:MAI:PEA, were 1.72:0:3.45 and 6:18:1, for preparing the crystals with n = 1 and n = 2, respectively. Methyl-d3-amine hydrochloride was used to replace the nature-abundance MA for the synthesis of 2D(BA)2(d3-MA)Pb2I7 (n = 2). 13C-methyl-15N-ammonium iodide, abbreviated as 13C,15N-MAI, was used to replace the natural-abundance MA for the synthesis of 2D (BA)2(13C,15N-MA)Pb2I7 (n = 2) and (PEA)2(13C,15N-MA)Pb2I7 (n = 2).

Single crystals growth

A saturated 2D OIHP solution was prepared by dissolving 2D OIHP compounds in a mixed solution containing 10 ml of hydriodic acid, 57 wt.% in H2O, and 1.7 ml of hypophosphorous acid solution, 50 wt.% in H2O, under stirring at a constant temperature of 60 °C in an oil bath. The well-stabilised 2D OIHP saturated solution was allowed to evaporate at a constant temperature of 62 °C for several days to obtain the high-quality 2D OIHP crystals. The crystals were carefully stored in a glove box to avoid moisture.

Solid-state NMR experiments

REDOR experiments were carried out on a wide-bore 14.1-T Bruker AVIII spectrometer equipped with a 3.2-mm triple-resonance magic-angle-spinning (MAS) probe head. The Larmor frequencies for 1H, 13C and 15N are 600.21, 150.92 and 60.81 MHz, respectively. The sample spinning rate was 10 kHz. The 13C polarisation was built up by the cross-polarisation (CP) scheme with a π/2 pulse of 5 μs, and a CP contact of 1.5 ms. The π pulse durations for 13C and 15N were 10 and 12 μs, respectively. During the REDOR sequence, the 1H CW decoupling scheme with a 100-kHz rf field was adopted, while the 1H TPPM decoupling with a 70 kHz rf field as used during signal acquisition. Static 2H spectra were acquired on a wide-bore 11.7-T Bruker AVIII spectrometer equipped with a 3.2 mm MAS probehead. The Larmor frequency for 2H is 76.75 MHz and the spectra were acquired by a solid echo sequence with two π/2 pulses of 6 μs and an interpulse delay of 50 μs, while the recycle delay was 1 s. 1H CW decoupling of 50 kHz of field strength was applied during the signal acquisition.

Data availability

The raw data collected in this study have been deposited in the figshare archive under accession code 19245843.v2.

Code availability

The Mathematica codes used for the data fitting in Fig. 2b and for simulating the Supplementary Fig. 4 in this study have been deposited in the figshare archive under accession code 19245843.v2.

References

  1. Bush, K. A. et al. Minimizing current and voltage losses to reach 25% efficient monolithic two-terminal perovskite–silicon tandem solar cells. ACS Energy Lett. 3, 2173–2180 (2018).

    CAS  Google Scholar 

  2. Miyata, A. et al. Direct measurement of the exciton binding energy and effective masses for charge carriers in organic–inorganic tri-halide perovskites. Nat. Phys. 11, 582–587 (2015).

    CAS  Google Scholar 

  3. Galkowski, K. et al. Determination of the exciton binding energy and effective masses for methylammonium and formamidinium lead tri-halide perovskite semiconductors. Energy Environ. Sci. 9, 962–970 (2016).

    CAS  Google Scholar 

  4. Dong, Q. et al. Electron-hole diffusion lengths > 175 mm in solution-grown CH3NH3PbI3 single crystals. Science 347, 967–970 (2015).

    ADS  CAS  PubMed  Google Scholar 

  5. Lim, J. et al. Elucidating the long-range charge carrier mobility in metal halide perovskite thin films. Energy Environ. Sci. 12, 169–176 (2019).

    CAS  Google Scholar 

  6. Park, N.-G. & Zhu, K. Scalable fabrication and coating methods for perovskite solar cells and solar modules. Nat. Rev. Mater. 5, 333–350 (2020).

    ADS  CAS  Google Scholar 

  7. Chen, T.-P. et al. Self-assembly atomic stacking transport layer of 2D layered titania for perovskite solar cells with extended UV stability. Adv. Energy Mater. 8, 1701722 (2018).

  8. Kubicki, D. J. et al. Formation of stable mixed guanidinium-methylammonium phases with exceptionally long carrier lifetimes for high-efficiency lead iodide-based perovskite photovoltaics. J. Am. Chem. Soc. 140, 3345–3351 (2018).

    CAS  PubMed  Google Scholar 

  9. Gong, J. et al. Electron-rotor interaction in organic-inorganic lead iodide perovskites discovered by isotope effects. J. Phys. Chem. Lett. 7, 2879–2887 (2016).

    CAS  PubMed  Google Scholar 

  10. Kubicki, D. J. et al. Cation dynamics in mixed-cation (MA)x(FA)1-xPbI3 hybrid perovskites from solid-state NMR. J. Am. Chem. Soc. 139, 10055–10061 (2017).

    CAS  PubMed  Google Scholar 

  11. Bernard, G. M. et al. Methylammonium cation dynamics in methylammonium lead halide perovskites: a solid-state NMR perspective. J. Phys. Chem. A 122, 1560–1573 (2018).

    CAS  PubMed  Google Scholar 

  12. Selig, O. et al. Organic cation rotation and immobiliszation in pure and mixed methylammonium lead-halide perovskites. J. Am. Chem. Soc. 139, 4068–4074 (2017).

    CAS  PubMed  Google Scholar 

  13. Kubicki, D. J. et al. Phase segregation in potassium-doped lead halide perovskites from (39)K solid-state NMR at 21.1 T. J. Am. Chem. Soc. 140, 7232–7238 (2018).

    CAS  PubMed  Google Scholar 

  14. Motta, C. et al. Revealing the role of organic cations in hybrid halide perovskite CH3NH3PbI3. Nat. Commun. 6, 7026 (2015).

    ADS  CAS  PubMed  Google Scholar 

  15. Fabini, D. H. et al. Universal dynamics of molecular reorientation in hybrid lead iodide perovskites. J. Am. Chem. Soc. 139, 16875–16884 (2017).

    CAS  PubMed  Google Scholar 

  16. Senocrate, A., Moudrakovski, I. & Maier, J. Short-range ion dynamics in methylammonium lead iodide by multinuclear solid state NMR and (127)I NQR. Phys. Chem. Chem. Phys. 20, 20043–20055 (2018).

    CAS  PubMed  Google Scholar 

  17. Weller, M. T., Weber, O. J., Henry, P. F., Pumpo, A. M. & Hansen, T. C. Complete structure and cation orientation in the perovskite photovoltaic methylammonium lead iodide between 100 and 352 K. Chem. Commun. 51, 4180–4183 (2015).

    CAS  Google Scholar 

  18. Leguy, A. M. et al. The dynamics of methylammonium ions in hybrid organic-inorganic perovskite solar cells. Nat. Commun. 6, 7124 (2015).

    ADS  PubMed  Google Scholar 

  19. Chen, T. et al. Rotational dynamics of organic cations in the CH3NH3PbI3 perovskite. Phys. Chem. Chem. Phys. 17, 31278–31286 (2015).

    CAS  PubMed  Google Scholar 

  20. Kubicki, D. J., Stranks, S. D., Grey, C. P. & Emsley, L. NMR spectroscopy probes microstructure, dynamics and doping of metal halide perovskites. Nat. Rev. Chem. 5, 624–645 (2021).

    CAS  Google Scholar 

  21. Gallop, N. P. et al. Rotational cation dynamics in metal halide perovskites: effect on phonons and material properties. J. Phys. Chem. Lett. 9, 5987–5997 (2018).

    CAS  PubMed  Google Scholar 

  22. Mitzi, D. B., Feild, C. A., Harrison, W. T. A. & Guloy, A. M. Conducting tin halides with a layered organic-based perovskite structure. Nature 369, 467–469 (1994).

    ADS  CAS  Google Scholar 

  23. Alanazi, A. Q. et al. Atomic-level microstructure of efficient formamidinium-based perovskite solar cells stabilised by 5-ammonium valeric acid iodide revealed by multinuclear and two-dimensional solid-state NMR. J. Am. Chem. Soc. 141, 17659–17669 (2019).

    CAS  PubMed  Google Scholar 

  24. Dong, Y., Lu, D., Xu, Z., Lai, H. & Liu, Y. 2‐Thiopheneformamidinium‐based 2D Ruddlesden–Popper perovskite solar cells with efficiency of 16.72% and negligible hysteresis. Adv. Energy Mater. 10, 2000694 (2020).

    CAS  Google Scholar 

  25. Hope, M. A. et al. Nanoscale phase segregation in supramolecular π-templating for hybrid perovskite photovoltaics from NMR crystallography. J. Am. Chem. Soc. 143, 1529–1538 (2021).

    CAS  PubMed  Google Scholar 

  26. Mao, L., Stoumpos, C. C. & Kanatzidis, M. G. Two-dimensional hybrid halide perovskites: principles and promises. J. Am. Chem. Soc. 141, 1171–1190 (2019).

    CAS  PubMed  Google Scholar 

  27. Saparov, B. & Mitzi, D. B. Organic-inorganic perovskites: structural versatility for functional materials design. Chem. Rev. 116, 4558–4596 (2016).

    CAS  PubMed  Google Scholar 

  28. Raghavan, C. M. et al. Low-threshold lasing from 2D homologous organic-inorganic hybrid Ruddlesden-Popper perovskite single crystals. Nano Lett. 18, 3221–3228 (2018).

    ADS  CAS  PubMed  Google Scholar 

  29. Milić, J. V. et al. Supramolecular engineering for formamidinium‐based layered 2D perovskite solar cells: structural complexity and dynamics revealed by solid‐state NMR spectroscopy. Adv. Energy Mater. 9, 1900284 (2019).

    Google Scholar 

  30. Blancon, J. C. et al. Extremely efficient internal exciton dissociation through edge states in layered 2D perovskites. Science 355, 1288–1292 (2017).

    ADS  CAS  PubMed  Google Scholar 

  31. Tsai, H. et al. High-efficiency two-dimensional Ruddlesden-Popper perovskite solar cells. Nature 536, 312–316 (2016).

    ADS  CAS  PubMed  Google Scholar 

  32. Li, M. K. et al. Intrinsic carrier transport of phase-pure homologous 2D organolead halide hybrid perovskite single crystals. Small 14, 1803763 (2018).

    ADS  Google Scholar 

  33. Paritmongkol, W. et al. Synthetic variation and structural trends in layered two-dimensional alkylammonium lead halide perovskites. Chem. Mater. 31, 5592–5607 (2019).

    CAS  Google Scholar 

  34. Zheng, K. & Pullerits, T. Two dimensions are better for perovskites. J. Phys. Chem. Lett. 10, 5881–5885 (2019).

    CAS  PubMed  Google Scholar 

  35. Mitzi, D. B., Chondroudis, K. & Kagan, C. R. Organic-inorganic electronics. IBM J. Res. Dev. 45, 29–45 (2001).

    CAS  Google Scholar 

  36. Spanopoulos, I. et al. Uniaxial expansion of the 2D Ruddlesden-Popper perovskite family for improved environmental stability. J. Am. Chem. Soc. 141, 5518–5534 (2019).

    CAS  PubMed  Google Scholar 

  37. Gao, Y. et al. Molecular engineering of organic-inorganic hybrid perovskites quantum wells. Nat. Chem. 11, 1151–1157 (2019).

    CAS  PubMed  Google Scholar 

  38. Ghosh, D., Neukirch, A. J. & Tretiak, S. Optoelectronic properties of two-dimensional bromide perovskites: influences of spacer cations. J. Phys. Chem. Lett. 11, 2955–2964 (2020).

    CAS  PubMed  Google Scholar 

  39. Dahod, N. S. et al. Melting transitions of the organic subphase in layered two-dimensional halide perovskites. J. Phys. Chem. Lett. 10, 2924–2930 (2019).

    CAS  PubMed  Google Scholar 

  40. Gong, X. et al. Electron-phonon interaction in efficient perovskite blue emitters. Nat. Mater. 17, 550–556 (2018).

    ADS  CAS  PubMed  Google Scholar 

  41. Tremblay, M. H. et al. (4NPEA)2PbI4 (4NPEA = 4-nitrophenylethylammonium): structural, NMR, and optical properties of a 3 x 3 corrugated 2D hybrid perovskite. J. Am. Chem. Soc. 141, 4521–4525 (2019).

  42. Ueda, T., Shimizu, k, Ohki, H. & Okuda, T. 13C CP/MAS NMR study of the layered compounds [C6H5CH2CH2NH3]2[CH3NH3]n-1Pbnl3n+1 (n = 1, 2). Z. f.ür. Naturforsch. A 51, 910–914 (1996).

    ADS  CAS  Google Scholar 

  43. Dahlman, C. J. et al. Dynamic motion of organic spacer cations in Ruddlesden–Popper lead iodide perovskites probed by solid-state NMR spectroscopy. Chem. Mater. 33, 642–656 (2021).

    CAS  Google Scholar 

  44. Lee, J., Lee, W., Kang, K., Lee, T. & Lee, S. K. Layer-by-layer structural identification of 2D Ruddlesden–Popper hybrid lead iodide perovskites by solid-state NMR spectroscopy. Chem. Mater. 33, 370–377 (2021).

    CAS  Google Scholar 

  45. Schaefer, J., McKay, R. A. & Stejskal, E. O. Double-cross-polarization NMR of solids. J. Magn. Reson. 34, 443–447 (1979).

    ADS  CAS  Google Scholar 

  46. Blancon, J.-C., Even, J., Stoumpos, C. C., Kanatzidis, M. G. & Mohite, A. D. Semiconductor physics of organic–inorganic 2D halide perovskites. Nat. Nanotechnol. 15, 969–985 (2020).

    ADS  CAS  PubMed  Google Scholar 

  47. Gullion, T. & Schaefer, J. Rotational-echo, double-resonance NMR. J. Magn. Reson. 81, 196–200 (1989).

    ADS  CAS  Google Scholar 

  48. Stoumpos, C. C. et al. Ruddlesden–Popper hybrid lead iodide perovskite 2D homologous semiconductors. Chem. Mater. 28, 2852–2867 (2016).

    CAS  Google Scholar 

  49. Cortecchia, D. et al. Structure-controlled optical thermoresponse in Ruddlesden-Popper layered perovskites. APL Mater. 6, 114207 (2018).

    ADS  Google Scholar 

  50. Morrow, D. J. et al. Disentangling second harmonic generation from multiphoton photoluminescence in halide perovskites using multidimensional harmonic generation. J. Phys. Chem. Lett. 11, 6551–6559 (2020).

    CAS  PubMed  Google Scholar 

  51. Calabrese, J. et al. Preparation and characterization of layered lead halide compounds. J. Am. Chem. Soc. 113, 2328–2330 (1991).

    CAS  Google Scholar 

  52. Goetz, J. M. & Schaefer, J. REDOR dephasing by multiple spins in the presence of molecular motion. J. Magn. Reson. 127, 147–154 (1997).

    ADS  CAS  PubMed  Google Scholar 

  53. Goetz, J. M., Wu, J. H., Yee, A. F. & Schaefer, J. Two-dimensional transferred-echo double resonance study of molecular motion in a fluorinated polycarbonate. Solid State Nucl. Magn. Reson. 12, 87–95 (1998).

    CAS  PubMed  Google Scholar 

  54. Lipari, G. & Szabo, A. Model-free approach to the interpretation of nuclear magnetic resonance relaxation in macromolecules. 1. theory and range of validity. J. Am. Chem. Soc. 104, 4546–4559 (1982).

    CAS  Google Scholar 

  55. Haller, J. D. & Schanda, P. Amplitudes and time scales of picosecond-to-microsecond motion in proteins studied by solid-state NMR: a critical evaluation of experimental approaches and application to crystalline ubiquitin. J. Biomol. NMR 57, 263–280 (2013).

    CAS  PubMed  PubMed Central  Google Scholar 

  56. Tong, C.-J., Geng, W., Prezhdo, O. V. & Liu, L.-M. Role of methylammonium orientation in ion diffusion and current–voltage hysteresis in the CH3NH3PbI3 perovskite. ACS Energy Lett. 2, 1997–2004 (2017).

    CAS  Google Scholar 

Download references

Acknowledgements

This work is supported by Ministry of Science and Technology (MOST) (Taiwan), Academia Sinica iMate Program  (AS-iMATE-111-33) and Career Development Award (AS-CDA-109-M03) for the funding. We thank Prof. Mark S. Conradi, Dr. Michitoshi Hayashi, Dr. Liang-Yan Hsu and Dr. Ching-Ming Wei for the valuable discussions and thank Mr. Boyan Andreychin for technical assistance.

Author information

Authors and Affiliations

Authors

Contributions

T.Y.Y. and C.W.C. conceived the idea and supervised this work; C.C.L. performed the synthesis of 2D OIHP crystals, PXRD, PL and the absorption experiments; C.Y.H. and Y.C.W. performed the synthesis of 3D MAPbI3 crystals; T.Y.Y., S.J.H. and P.H.W. performed NMR experiments; T.P.C. performed temperature-dependent PXRD and DSC; T.P.C. and C.C.C. performed temperature-dependent PL; V.M.G., D.R. and O.P. performed the synthesis of 13C-methyl-15N-ammonium iodide and discussed the results; T.Y.Y., C.W.C., P.T.C., R.S. and C.C.L. discussed and analysed the results; T.Y.Y., C.W.C., V.M.G. and C.C.L. wrote the manuscript together.

Corresponding authors

Correspondence to Chun-Wei Chen or Tsyr-Yan Yu.

Ethics declarations

Competing interests

The authors declare no competing interests.

Peer review

Peer review information

Nature Communications thanks John Grey, Dominik Kubicki and John Ripmeester for their contribution to the peer review of this work. Peer reviewer reports are available.

Additional information

Publisher’s note Springer Nature remains neutral with regard to jurisdictional claims in published maps and institutional affiliations.

Supplementary information

Rights and permissions

Open Access This article is licensed under a Creative Commons Attribution 4.0 International License, which permits use, sharing, adaptation, distribution and reproduction in any medium or format, as long as you give appropriate credit to the original author(s) and the source, provide a link to the Creative Commons license, and indicate if changes were made. The images or other third party material in this article are included in the article’s Creative Commons license, unless indicated otherwise in a credit line to the material. If material is not included in the article’s Creative Commons license and your intended use is not permitted by statutory regulation or exceeds the permitted use, you will need to obtain permission directly from the copyright holder. To view a copy of this license, visit http://creativecommons.org/licenses/by/4.0/.

Reprints and Permissions

About this article

Verify currency and authenticity via CrossMark

Cite this article

Lin, CC., Huang, SJ., Wu, PH. et al. Direct investigation of the reorientational dynamics of A-site cations in 2D organic-inorganic hybrid perovskite by solid-state NMR. Nat Commun 13, 1513 (2022). https://doi.org/10.1038/s41467-022-29207-6

Download citation

  • Received:

  • Accepted:

  • Published:

  • DOI: https://doi.org/10.1038/s41467-022-29207-6

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.

Search

Quick links

Nature Briefing

Sign up for the Nature Briefing newsletter — what matters in science, free to your inbox daily.

Get the most important science stories of the day, free in your inbox. Sign up for Nature Briefing