Abstract
Ruddlesden–Popper halide perovskites are 2D solutionprocessed quantum wells with a general formula A_{2}A’_{n1}M_{ n }X_{3n+1}, where optoelectronic properties can be tuned by varying the perovskite layer thickness (nvalue), and have recently emerged as efficient semiconductors with technologically relevant stability. However, fundamental questions concerning the nature of optical resonances (excitons or free carriers) and the exciton reduced mass, and their scaling with quantum well thickness, which are critical for designing efficient optoelectronic devices, remain unresolved. Here, using optical spectroscopy and 60Tesla magnetoabsorption supported by modeling, we unambiguously demonstrate that the optical resonances arise from tightly bound excitons with both exciton reduced masses and binding energies decreasing, respectively, from 0.221 m_{0} to 0.186 m_{0} and from 470 meV to 125 meV with increasing thickness from n equals 1 to 5. Based on this study we propose a general scaling law to determine the binding energy of excitons in perovskite quantum wells of any layer thickness.
Introduction
Ruddlesden–Popper halide perovskites^{1,2} (RPPs) are solutionprocessed quantum well structures formed by twodimensional (2D) layers of halide perovskite semiconductors separated by bulky organic spacer layers, whose stoichiometric ratios are defined by the general formula^{3} A_{2}A’_{n1}M_{ n }X_{3n+1} where A, A’ are cations, M is a metal, X is a halide and the integer value n determines the perovskite layer thickness (or quantum well thickness). Recent breakthrough in the synthesis of phasepure (a single nvalue) RPPs with higher values^{3,4,5} of n, up to n equals to 5, has inspired their use as lowcost semiconductors in optoelectronics^{5,6,7,8} as an alternative to threedimensional (3D) perovskites due to their technologically relevant intrinsic photo and chemicalstability^{5,6,7,8,9,10}. However, key fundamental questions remain unanswered in RPPs with n greater than 1, such as the nature of optical transitions, as well as the behavior of Coulomb interactions especially with increasing quantum well thickness. In fact there has been an intense ongoing debate^{6,7,8,11,12,13} regarding the exact nature of the optical transitions (excitons versus free carriers) in RPPs with large nvalues. RPPs with n equals to 1 (excitons at room temperature),^{14,15} and 3D perovskites^{16} (free carriers at room temperature) are representative of the two limiting regimes at room temperature, but the analysis of the crossover has not been performed. This issue originates from the lack of knowledge of the fundamental quantities such as the exciton reduced mass, dielectric constant and characteristics like the spatial extension of electron and hole wavefunctions, which play a crucial role in the determination of the exciton binding energy. In particular, contradictory reports of the value of the exciton reduced mass have significantly contributed to this uncertainty^{15,16} making it the most critical experimentally derived parameter required for the quantitative determination of the exciton characteristics in hybrid (organic–inorganic) perovskite systems. Moreover, unlike bulk inorganic semiconductors, heterostructures^{17} and 3D perovskites^{18,19}, it is nontrivial to determine the exciton reduced mass in layered hybrid perovskites using a symmetrybased (k.p) approach^{20} or using manybody ab initio calculations^{21}. Furthermore, ambiguity in the determination of the exciton binding energy in layered 2D perovskites has also been imposed by the limited understanding of the role of dielectric confinement versus quantum confinement with increasing quantum well thickness^{22,23}. More generally, phasepure RPPs with n greater than 1 present a unique opportunity to explore the physical properties of natural quantum well semiconducting crystals intermediate between monolayer 2D materials^{24,25} and 3D materials^{26}, a quasidimensional physics only accessible in synthetic inorganic semiconductor quantum well structures so far^{26}.
Here we present the study on using lowtemperature (4 K) magnetooptical spectroscopy to accurately determine the exciton reduced mass for (BA)_{2}(MA)_{n1}Pb_{ n }I_{3n+1} RPP crystals with perovskite layer thickness varying between 0.641 and 3.139 nm, corresponding to n varying between 1 and 5 (Fig. 1a, Supplementary Fig. 1, and Supplementary Table 1), where BA and MA stand for CH_{3}(CH_{2})_{3}NH_{3} and CH_{3}NH_{3}, respectively. The reduced mass is used to develop a generalized theoretical model for electron–hole interactions in RPPs and determine fundamental characteristics of the exciton states. In parallel, from lowtemperature optical spectroscopy we experimentally determine the exciton binding energy in the RPPs with n varying from 1 to 5. Finally, from these results we produce a general scaling behavior for the binding energy of Wannier–Mott exciton states in RPPs, which allows for prediction of the exciton binding energy for any given thickness. This study closes a longstanding scientific gap and will lead to the rational design of nextgeneration layered 2D perovskitebased optoelectronic devices.
Results
Exciton reduced mass from magnetoabsorption measurements
Fig. 1 shows the RPP structure and results from magnetoabsorption spectroscopy, which was employed to probe the strength of the electron–hole interaction in RPPs and deduce the exciton reduced mass. These measurements were performed at 4 K in the Faraday geometry (magnetic field along the stacking direction of the layers, ĉaxis), and the optical spectra of the right and lefthanded circular polarization components (σ^{±}) of the transmitted white light were probed. Application of a high magnetic field on the RPP with n equals to 4 results in an energy shift of the optical resonance at about 1.9 eV (Fig. 1c, d). Similar results were obtained for the other RPPs (see Supplementary Fig. 2). This optical transition was identified as the exciton ground state and its energy shift under magnetic field in the Faraday configuration is expressed by^{26} ΔE = ±1/2 g_{0}μ_{B}B + c_{0}B^{2}, where the first term describes the Zeeman splitting of the σ^{+} and σ^{‒} exciton transitions (g_{0} is the gfactor in the perovskite plane, μ_{B} the Bohr magneton, B the magnetic field) and the second one the diamagnetic shift (c_{0} is the diamagnetic shift coefficient). Under magnetic field the competition between the Zeeman and diamagnetic effects explains the nonsymmetric, oppositesign energy shift of the σ^{+} and σ^{‒} exciton transitions with respect to the zero field exciton absorption energy (Fig. 1d and Supplementary Fig. 2). We note that this asymmetry becomes more pronounced for thicker perovskite layers (n approaching 5), which is a consequence of the strong increase of the diamagnetic coefficient with increasing nvalue. Fitting the exciton energy shifts for both σ^{+} and σ^{‒} polarizations using the model above yields the diamagnetic coefficients c_{0} of the RPPs (Fig. 1e). Here, c_{0} increases monotonically with the perovskite layer thickness, and it ranges from ~0.2 to ~1.1 µeV T^{−2} for the RPPs with n varying from 1 to 5, respectively. We note that due to relatively small signaltonoise ratio in the magnetoabsorption data for the RPP with n equals to 1 (Supplementary Fig. 2a), the diamagnetic coefficient for this compound was obtained from a combined experimental–theoretical approach which consisted in fitting the c_{0} value to be in best agreement with both the magnetoabsorption data and the experimental exciton binding energy discussed later in this paper. For comparison, we also included in Fig. 1e the value of c_{0} reported by Tanaka et al.^{15} (c_{0} = 0.26 µeV T^{−2}) for a RPP with n equals to 1 and with a slightly larger organic spacer (hexylammonium CH_{3}(CH_{2})_{5}NH_{3} instead of butylammonium CH_{3}(CH_{2})_{3}NH_{3} in our case). We note that our value of c_{0} for the RPP with n equals to 1 with BA as organic spacer is in agreement but slightly smaller than other reports of RPPs with n equals to 1 with longer organic spacers^{27,28,29}. Concomitant with the diamagnetic shift increase with nvalue, the gfactor presents a marked increase from 0.8 to 1.6 for the RPPs with n varying from 1 to 5, and a value of about 1.7 was derived from our 3D perovskites magnetoabsorption data (Supplementary Fig. 3) and is consistent with the literature^{30,31}.
The diamagnetic coefficient is directly connected to both the exciton reduced mass and the strength of the electron–hole Coulomb interaction. Although a simple relation exists for pure 2D systems where quantum confinement dominates^{22,26}, i.e., when confinement effects stem from the confinement of electron and hole wavefunctions in a 2D plane, this model does not apply to the RPPs due to the following reasons. First, the perovskite layer thickness is comparable to the spatial extent of the excitons^{15,16,27} and the exciton wavefunction cannot be strictly confined to a 2D plane (see also Supplementary Note 1 to 4). Second, the dielectric confinement plays a key role in the photophysics of RPPs^{15,23,27}. Dielectric confinement (also called image charge effect) manifests in a quantum well system provided that the thickness of the quantum wells is comparable to the exciton size, and the dielectric constant ratio between the quantum wells (perovskite layers with ε_{w}~4 or higher) and the barriers (organic spacing layers with ε_{b}~2.2) is larger than unity. This result leads to an enhancement of the Coulomb interaction between the electron and hole pair composing each exciton, which is a consequence of the reduced dielectric screening of the exciton electric field partially located outside the quantum well, i.e., in the surrounding barriers that have a lower dielectric constant.
Therefore, we developed a theoretical model (see details in the next section, Supplementary Note 1, and Supplementary Fig. 4), which describes the electron–hole Coulomb interaction in thin semiconductors and includes dielectric confinement (Keldysh theory^{22}). For this theoretical model to work, it requires an accurate determination of the exciton reduced mass (labeled µ). We evaluated the reduced mass for each RPP by adjusting the theoretical values of c_{0} to those measured experimentally (Fig. 1f and Supplementary Note 5). This yielded µ = 0.221 m_{0} (m_{0} is the free electron mass) for the RPP with n equals to 1, and 0.184 m_{0} for the RPP with n equals to 1 compound with longer organic spacers reported by Tanaka et al.^{15}. Then, we observe a monotonic decrease of the exciton reduced mass from 0.217 m_{0} for the RPP with n equals to 2 down to 0.196 m_{0} for the RPP with n equals to 4. Due to computational limitations, our model was not applied to the RPP with n equals to 5; however we estimated, to a first approximation, µ = 0.186 m_{0} from the extrapolation of the data for the RPPs with n equals 1 to 4.
The deduced values of exciton reduced mass in the RPPs up to n equals to 5 are significantly larger than those reported for 3D perovskites (Supplementary Fig. 3), even though the exciton states are well confined within the perovskite layer (see next section). This is surprising because a decrease of the exciton reduced mass is expected for increasing perovskite layer thickness, with limiting value of 0.104 m_{0} (3D perovskite), as the vicinity of the exciton approaches that of the 3D perovskites. However, the equivalent quantum well is still very thin even for the RPP with n equals to 5. Moreover, the reduced mass of the exciton ground state calculated by density functional theory (DFT) for each RPP (with n equals 1 to 4) yields a similar dependence on the nvalue as the experimental ones provided the underestimation of the bandgap computation by DFT is taken into account (Supplementary Fig. 5). We explain the higher values of exciton reduced mass in the RPPs studied as compared to their 3D counterpart by a progressive reduction of the energy bandgap^{26}. The limiting 3D value is thus expected to be reached for larger nvalue, i.e., when the RPP bandgap equals the 3D perovskite one. Furthermore, electronic band mixing and nonparabolicity effects have been known to induce changes in the exciton reduced mass in quantum well systems^{32,33,34,35}. These effects have also been discussed in classic inorganic semiconductors and agree with the nvalue dependence of the experimental bandgap, diamagnetic shift and gfactor (Figs. 1e and 3a, and Supplementary Fig. 6). In fact, the bandgap dependence of the exciton reduced mass was also reported recently in 3D hybrid perovskites^{31}. To conclude, the unambiguous determination of the reduced mass allows us to develop a predictive model for excitons in solutionprocessed quantum well systems and calculate the exciton binding energies of the RPP compounds.
Calculating the exciton binding energy in 2D perovskites
The binding energy of the exciton ground state was calculated for each RPP (with n equals 1 to 4) by inputting each respective value of the exciton reduced mass into our theoretical model and semiempirically solving the Bethe–Salpeter equation based on the effective mass Green’s function approach^{23}. This approach includes: calculating the electronic structures of the RPPs to extract exciton wavefunctions and dielectric constant profiles using DFT, generalizing the Keldysh theory for 2D perovskites and combining both of the above by building a semiempirical model to simulate the Wannier–Mott exciton characteristics (Fig. 2 and Supplementary Note 1, 2, and 6). In our model, the potential function describing the Coulomb interaction between the electron and hole forming the exciton states is based on Keldysh theory^{22} generalized to a semiconducting dielectric quantum well (Fig. 2a), i.e., a dielectric well (perovskite layer) with thickness d and dielectric constant ε_{w} sandwiched between well barriers (organic spacing layers) with dielectric constant ε_{b}. The nonlocal, screened electron–hole pair interaction potential is given by:
in reciprocal space and in the inplane \(\left( {{\hat{\mathbf a,}}{\hat{\mathbf b}}} \right)\) direction. In Eq. (1), the difference of electron and hole transverse (inplane) wavevectors is q_{t}, \({\mathrm{\Delta }} = \left( {1  \chi ^2e^{  2q_{\mathrm{t}}d}} \right)^{  1}\), and \(\chi = \frac{{\varepsilon _{\mathrm{w}}  \varepsilon _{\mathrm{b}}}}{{\varepsilon _{\mathrm{w}} + \varepsilon _{\mathrm{b}}}}\). Here, the dielectric constants are inputs from our DFT results and were taken at optical frequency because the values of binding energy measured in RPPs (see next section) are one order of magnitude larger than the highest energy value reported for the lattice optical phonon modes^{36}. The electron (ρ_{e}) and hole (ρ_{h}) probability density profiles along the stacking axis ĉ (z_{e,h} are realspace coordinates along this direction) were also obtained from our DFT results. This method is equivalent to the realspace computation of the screening effect using the image charge method^{37}. We also note that the general expression (1) of the electron–hole interaction potential corresponds to the general Keldysh potential in real space^{22}. Upon different degrees of approximation (as discussed in Supplementary Note 3), the electron–hole interaction potential used in the literature in the limit of monolayer 2D transition metal dichalcogenides^{38,39,40,41,42} can be retrieved. However, these approximations are not valid in RPPs (Supplementary Note 4) and the general expression (1) needs to be used.
Overall, theoretical solution to the exciton binding energy in each RPP requires the knowledge of: the electron and hole probability density distributions, the dielectric constant profile along the stacking direction, and the exciton reduced mass. In RPPs, the density profiles and dielectric constants along the stacking direction (Fig. 2c and Supplementary Fig. 4b), along with the electronic band structure (Fig. 2b), were derived from the electron and hole wavefunctions calculated by DFT (Supplementary Note 6). A representative example of the electron and hole probability density profiles is sketched in Fig. 2c for the RPPs with n equals to 4. Our calculations reveal that the charge wavefunctions stay confined into the perovskite layers and exhibit little leakage into the organic spacing layers, which is consistent with uncoupled quantum well systems. Moreover, the results reveal maximum values of dielectric constant in the range of 4 to 5.2 for the perovskite layers in RPPs with n equals 1 to 5, and a minimum value of about 2.2 for the organic spacing layers, consistent with previous estimations^{43,44}. The contrast of dielectric constants between the perovskite and organic spacers is at the origin of the strong dielectric confinement effects observed in RPPs, as discussed in the next section.
Gathering all these information, our general model was then applied to the calculation of the exciton binding energy in RPPs, yielding a value of 467 meV for the RPP with n equals to 1 (435 meV for the case of longer organic spacers from Tanaka et al.^{15}), and which decreases monotonically to ~135 meV for the RPP with n equals to 4 as illustrated in Fig. 2d (see also Supplementary Fig. 7 and Supplementary Table 2). We observe a radical difference of the exciton binding energies calculated using our general approach as compared to those obtained under various degrees of approximation usually suited to 2D materials such as transition metal dichalcogenides^{38,39,40,41,42}, i.e., in the case the charges are strictly restricted to a 2D plane and including or not dielectric confinement (see details in Supplementary Note 3). The accuracy of our model to predict the binding energies of excitons in 2D perovskites was then verified by directly measuring these values using optical spectroscopy techniques.
Direct measurement of the exciton binding energy
We directly measured the exciton binding energy in each RPP using optical absorption, photoluminescence (PL) and photoluminescence excitation (PLE) spectroscopy (Fig. 3). The optical bandgap was tuned over the visible spectral range from 2.540 ± 0.004 eV (488 nm) in the RPP with n equals to 1 down to 1.846 ± 0.004 eV (672 nm) in the RPP with n equals to 5 (Fig. 3a). We note that the RPPs with n greater than 1 retained their optical bandgap from 290 K down to 4 K. This observation implies that our study conducted at low temperature is directly transposable to room temperature and provides direct insights into the photophysics of materials used in practical devices.
Figure 3b shows a single sharp peak in the PL spectra, indicating the emission of the exciton ground state^{14,45}. The lowenergy shoulder observed more than tens of meV below the exciton peak in all RPPs was recently assigned in the RPP with n equals to 1 to a phonon replica^{46} and selftrapped excitons^{47}. Based on power dependence measurements of the PL (Supplementary Fig. 8), we hypothesize a similar origin for the resonances in the RPPs with n greater than 1, but we only focus on investigating the ground state exciton transition in this study.
All the presented absorption spectra show similar features (Fig. 3d), which includes a single absorption peak at low energy corresponding to the exciton ground state resonance. Moreover, a steady increase of absorption at higher energies modulated by energy optical transitions is well reproduced in the PLE measurements (Fig. 3e). These spectral features were assigned to the Rydberg series of the Wannier–Mott exciton (1s, 2s, 3s, 4s noted as Ns, with N equals to 1, 2, 3 and 4 and having energies E_{ Ns }) and are illustrated in Fig. 3c. The onset of the continuum E_{G} corresponds to electron and hole free carrier states (Fig. 3c), as previously reported in the RPP with n equals to 1 perovskites^{15,45}, other 2D nanomaterials^{39,48} and quantum well semiconductors^{26,49}. Absorption transition features, marked as A, B and C, are observed in both the absorption and PLE spectra for energy higher than E_{G}, and are apparently common to all the RPPs given an energy scaling with the nvalue proportional to the bandgap scaling (Fig. 3d, e). Close to the continuum onset and in our experimental energy range, the optical transitions in RPPs at energies above E_{G} have been assigned^{11,14,50} to transitions between the Pb(6s)I(5p) states in the valence band and Pb(6p) states in the conduction band^{20,51}. The absorption features A, B and C can be understood as transitions between valence and conduction bands overlapping with the continuum of states from the bandedge exciton. For example, from the calculated RPP band structures (Fig. 2b and Supplementary Fig. 4a), one can assume that the high energy optical transitions involve the series of the minibands directly below the highest valence band and above the lowest conduction band at the Γ high symmetry point in the Brillouin zone. Calculation of the broadband optical spectra in the RPPs, including dipole allowed transitions from group theory and joint density of states, should be performed in future theoretical studies in order to understand the details of the experimental absorption spectra at energies higher than the continuum E_{G}.^{20,51}
The exciton binding energies in RPPs were derived from the study of the optical transitions corresponding to the exciton Rydberg series and the continuum. We present a representative example for the RPP with n equals to 4 in Fig. 4a, b. Dielectric confinement (or image charge effect) has been shown^{15,27,44,45} to mainly influence the 1s excitons in RPPs with n equals 1. Therefore, the 2s and 3s exciton states were fitted using the classic 2D hydrogen Rydberg series with energies^{26} E_{ Ns } = E_{G} − R_{y} /(N − 1/2)^{2}, where R_{y} is the Rydberg energy. This yields E_{G} = 2.078 ± 0.012 eV and R_{y} = 0.11 ± 0.04 eV for the RPP with n equals to 4 (Fig. 4b, dashed red line). This procedure is similar to the one used in transition metal dichalcogenides^{39,52} and 2D perovskites^{15,45,53}. It was also applied to the RPPs with n equals to 1, 2, 3 and 5 (Supplementary Fig. 9), i.e., the 1s, 2s and 3s exciton states were identified from the analysis of the experimental spectra and the 2s, 3s Rydberg series were fitted with the 2D hydrogen model to derive the continuum energy E_{G}. The binding energy of the 1s exciton ground state was derived from the difference E_{1s} − E_{G}, which ranges from about 470 meV for the RPP with n equals to 1 down to 125 meV for the RPP with n equals to 5 (Fig. 4c, d, Supplementary Table 1). We note that the lower limit of the exciton binding energy is given by the energy difference between the (1s) exciton ground state and (2s) first excited state (Fig. 4d). We emphasize that the predicted theoretical and experimentally determined values are in excellent agreement (Fig. 4d and Supplementary Fig. 7), thus validating the accuracy of our developed theoretical model for Wannier–Mott excitons in RPPs. These results emphasize the need for an accurate determination of the exciton reduced mass and taking into account the contributions of quantum and dielectric confinements as well as hole and electron density profiles in order to develop an accurate and robust theoretical model for the 2D perovskite systems.
After validating the model, we can further extract pertinent details on the specific role of dielectric confinement on the exciton characteristics and the scaling of the exciton binding energy with perovskite layer thickness. The model elucidates that the overlap of the electron and hole wavefunctions, whose convolution forms the exciton ground state, becomes more pronounced towards the center of the perovskite layer for the highest nvalue (Fig. 2c and Supplementary Fig. 4c). This suggests that the electric field lines for the exciton ground state are significantly more localized within the perovskite layer for larger nvalues than for the RPP with n equals to 1 and 2. This is consistent with the fact that with increasing perovskite layer thickness the strength of dielectric confinement decreases with respect to quantum confinement (Fig. 2d). Furthermore, the calculated probability densities of the electron and hole wavefunctions exhibit negligible intensity outside of the perovskite layer (i.e., into the organic spacer layer) as displayed in Fig. 2c and Supplementary Fig. 4c, which is comparable to a technologically relevant multi quantum well system. In summary, our theoretical model demonstrates that the strong exciton binding energy in thin 2D perovskite layers (n approaching 1) stems from strong dielectric confinement effects, which wane progressively for larger perovskite layer thicknesses (n approaching 5 or greater).
Simple analytical expression of the exciton binding energy scaling law
Finally, based on our understanding of the exciton behavior with varying perovskite layer thickness, we developed a general empirical scaling law of the exciton binding energies based on a classical model for low dimensional systems^{54} as described in Eq. (1):
In this expression for the exciton ground state binding energy, E_{0} (=16 meV) and a_{0} (=4.6 nm) are the 3D Rydberg energy and Bohr radius of 3D perovskites^{16}, respectively, and L_{w} is the physical width of the quantum well (Supplementary Table 1) for an infinite quantum well potential barrier^{55}. In the model (2), the exciton is considered isotropic in a αdimensional space (α strictly greater than 1 and smaller than 3) and we introduce an empirical correction factor γ. The factor γ is a simple way to empirically account for the deviations from the pure quantum confinement regime, including electron and holes densities and dielectric confinement effects. In a purely quantum confined regime γ equals to 1 in the expression of α, but experimentally derived α−value in RPPs can only be fitted with a larger γ value, i.e., γ equals to 1.76 (Fig. 5a). The corresponding decrease in the value of α highlights additional compression of the exciton wavefunction in the quantum well due to dielectric confinement, which results in enhanced values of exciton binding energy as compared to merely including the quantum confinement effect (Fig. 5b). The surprisingly good agreement of the expression (2) with experimental results, only using a γ correction factor independent of the nvalue to take into account dielectric effects, will be understood in future studies involving different RPP compositions (Br and Snbased 2D perovskites, various organic spacing layers, etc.). We also note that in the simplistic approximation of Hydrogen exciton model, the changes of exciton confinement with perovskite layer thickness can be understood as changes of both the effective dielectric constant value and the exciton Bohr radius as a function of nvalue (Supplementary Fig. 10).
Applying our model (2) for large nvalues, we predict that the exciton binding energy in RPPs is larger than room temperature thermal fluctuations (k_{B}T) up to n about 20 (perovskite layer thickness of 12.6 nm). This demonstrates the surprising robustness of exciton states in RPPs, in spite of the small spatial extension of the exciton as compared to the perovskite layer thickness. In other words, a more abrupt reduction of the exciton binding energy with increasing perovskite layer thickness was expected given the strong screening of the electron–hole Coulomb interaction reported in 3D perovskites^{16}, a situation approached by RPPs with perovskite layer thickness of a few nanometers. Again, this underlines the unusual nature of photoexcited states in RPPs, and to more extent in solutionprocessed quantum well systems as a template for exploring quasi2D semiconductors.
In summary, we demonstrate the importance of Coulomb interactions in 2D layered perovskites and experimentally elucidate properties of unexpectedly strongly bound excitons (>120 meV) in RPPs with thickness up to 3.1 nm (corresponding to n equals to 5). We propose a generic formulation of the scaling of the exciton binding energy with the perovskite layer thickness from the single layer (n equals to 1) to 3D crystals (n tends to infinity), further predicting the nature of optical transitions at room temperature to change from excitonic to free carrier like only in RPPs with thickness larger than ~12 nm (n about 20). These results mark a fundamental step towards the design of new 2D perovskitebased semiconductor materials for nextgeneration optoelectronic and photonic technologies such as solar cells, lightemitting diodes, photodetectors, polariton and electrically driven lasers.
Methods
RPP crystal synthesis and preparation
The crystal structures of the RPPs, (BA)_{2}(MA)_{n1}Pb_{ n }I_{3n+1}, is composed of an anionic layer {(MA)_{n1}Pb_{ n }I_{3n+1}}^{2−}, derived from bulk methylammonium lead triiodide perovskites (MAPbI_{3}), which is sandwiched between nbutylammonium (BA) spacer cations (Fig. 1a). BA and MA stand for CH_{3}(CH_{2})_{3}NH_{3} and CH_{3}NH_{3}, respectively. RPPs with n ranging from 1 to 5, corresponding to perovskite layer thickness between 0.641 and 3.139 nm, were synthetized and purified following previously reported method^{3,4,5}. More precisely, the raw crystals were prepared by combining PbO, MACl and BA in appropriate molar ratios in a HI/H_{3}PO_{2} solvent mixture. The precursor solutions were prepared with 0.225 M of Pb^{2+} concentration and stirred at room temperature overnight. Phase purity and crystalline quality of each crystal sample was established by monitoring Xray diffraction (Supplementary Fig. 1). In addition, the small Stokes shifts and relatively sharp linewidths of the exciton resonances (Fig. 3) were another indication of the homogeneity and low disorder in the RPP crystals. Thin RPP crystals were mechanically exfoliated onto either the 3.5 μm core of a singlemode optical fiber for magnetoabsorption spectroscopy or transparent quartz substrates for optical absorption, PL, and PLE spectroscopy experiments.
The 3D perovskite MAPbI_{3} (n tends to infinity) samples for magnetoabsorption spectroscopy were prepared as thin films on transparent substrates using the hotcasting method previously reported^{56}.
Magnetoabsorption spectroscopy
A single RPP crystal was affixed over the core of a 3.5 µm diameter singlemode optical fiber to ensure rigid optical alignment of the light path during the magnetic field pulse. The fibersample assembly was mounted in a custom optical probe that was fitted in the 4 K bore of a 65 T capacitordriven pulsed magnet. The sample was in a helium exchange gas environment to ensure thermal anchoring at 4 K. White light from a Xe lamp transmits the sample via the singlemode fiber and was retroreflected and dispersed in a 300 mm spectrometer with a 300 groove/mm grating. Broadband spectra were recorded every 2.3 ms throughout the magnet pulse. Access to σ^{+} and σ^{−} circular polarization was achieved via a thinfilm circular polarizer mounted directly after the sample and by reversing the direction of the magnetic field. Details of the setup can be found elsewhere^{57}.
The 3D perovskite MAPbI_{3} thin films were measured in the same manner as described above by placing film sample in front of the core of the optical fiber used for illumination.
Optical absorption, PL and PLE
Optical spectroscopies were performed with an inlabbuilt confocal microscopy system focusing close to the diffraction limit (about 1 μm resolution), a monochromatic laser tunable over the visible and nearinfrared spectral ranges. PL spectral responses were obtained through a spectrograph (SpectraPro 2300i) and a CCD camera (EMCCD 1024B) yielding an error of less than 2 nm. PL data in the main text were measured for light excitation at 440 nm (if not mentioned otherwise) and the excitation intensity was typically of the order of or below 10^{3} mW cm^{−2}. PLE spectra were obtained by measuring the PL integrated intensity while scanning with a 2 nm step the excitation light wavelength at wavelengths smaller than the one of the PL emission peak. Absorption spectra were measured either via a balanced photodiode by tuning the laser excitation wavelength or by detecting the spectral transmission/reflection of the samples exposed to white light. Samples were measured under vacuum (between 10^{−5} and 10^{−6} Torr) and cooled at 4 K if not mentioned otherwise.
Theory
A momentum space representation of the exciton Green’s function developed previously for classic quantum wells^{58} was used to solve the Bethe–Salpeter equation in the effective mass approximation. This method was adapted for RPPs to include the screening of the electron–hole interaction related to the dielectric confinement and the electron and hole wavefunctions overlap. These latter effects were evaluated at the DFT level. The Wannier–Mott exciton Rydberg states appear as the bound states in the absorption spectrum and can also be determined from the corresponding Schrödinger equation for the two particle wave functions (see details in Supplementary Note 1, 2, and 6).
Data availability
The data that support the findings of this study are available from the corresponding authors upon reasonable request.
References
 1.
Ruddlesden, S. N. & Popper, P. New compounds of the K_{2}NIF_{4} type. Acta. Crystallogr. 10, 538–539 (1957).
 2.
Mitzi, D. B., Feild, C. A., Harrison, W. T. A. & Guloy, A. M. Conducting tin halides with a layered organicbased perovskite structure. Nature 369, 467–469 (1994).
 3.
Stoumpos, C. C. et al. Ruddlesden–Popper hybrid lead iodide perovskite 2D homologous semiconductors. Chem. Mater. 28, 2852–2867 (2016).
 4.
Stoumpos, C. C. et al. High members of the 2D RuddlesdenPopper halide perovskites: synthesis, optical properties, and solar cells of (CH_{3}(CH_{2})_{3}NH_{3})_{2}(CH_{3}NH_{3})_{4}Pb_{5}I_{16}. Chem 2, 427–440 (2017).
 5.
Cao, D. H., Stoumpos, C. C., Farha, O. K., Hupp, J. T. & Kanatzidis, M. G. 2D homologous perovskites as lightabsorbing materials for solar cell applications. J. Am. Chem. Soc. 137, 7843–7850 (2015).
 6.
Tsai, H. et al. Highefficiency twodimensional Ruddlesden–Popper perovskite solar cells. Nature 536, 312–316 (2016).
 7.
Blancon, J.C. et al. Extremely efficient internal exciton dissociation through edge states in layered 2D perovskites. Science 355, 1288–1292 (2017).
 8.
Yuan, M. et al. Perovskite energy funnels for efficient lightemitting diodes. Nat. Nanotechnol. 11, 872–877 (2016).
 9.
Smith, I. C., Hoke, E. T., SolisIbarra, D., McGehee, M. D. & Karunadasa, H. I. A layered hybrid perovskite solarcell absorber with enhanced moisture stability. Angew. Chem. Int. Ed. 53, 11232–11235 (2014).
 10.
Cao, D. H. et al. Thin films and solar cells based on semiconducting twodimensional Ruddlesden–Popper (CH_{3}(CH_{2})_{3}NH_{3})_{2}(CH_{3}NH_{3})_{n−1}S_{n}I_{3n+1} perovskites. ACS Energy Lett. 2, 982–990 (2017).
 11.
Tanaka, K. & Kondo, T. Bandgap and exciton binding energies in leadiodidebased natural quantumwell crystals. Sci. Technol. Adv. Mater. 4, 599–604 (2003).
 12.
Wu, X., Trinh, M. T. & Zhu, X.Y. Excitonic manybody interactions in twodimensional lead iodide perovskite quantum wells. J. Phys. Chem. C 119, 14714–14721 (2015).
 13.
GélvezRueda, M. C. et al. Interconversion between free charges and bound excitons in 2D hybrid lead halide perovskites. J. Phys. Chem. C 121, 26566–26574 (2017).
 14.
Ishihara, T., Takahashi, J. & Goto, T. Optical properties due to electronic transitions in twodimensional semiconductors (C_{n}H_{2n+1}NH_{3})_{2}PbI_{4}. Phys. Rev. B 42, 11099–11107 (1990).
 15.
Tanaka, K. et al. Image charge effect on twodimensional excitons in an inorganicorganic quantumwell crystal. Phys. Rev. B 71, 045312 (2005).
 16.
Miyata, A. et al. Direct measurement of the exciton binding energy and effective masses for charge carriers in organicinorganic trihalide perovskites. Nat. Phys. 11, 582–587 (2015).
 17.
Bastard, G. Wave Mechanics Applied to Semiconductor Heterostructures (Les Éditions de Physique, Les Ulis, 1988).
 18.
Yu, Z. G. Effectivemass model and magnetooptical properties in hybrid perovskites. Sci. Rep. 6, 28576 (2016).
 19.
Filip, M. R., Verdi, C. & Giustino, F. GW band structures and carrier effective masses of CH_{3}NH_{3}PbI_{3} and hypothetical perovskites of the type APbI_{3}: A=NH_{4}, PH_{4}, AsH_{4} and SbH_{4}. J. Phys. Chem. C 119, 25209–25219 (2015).
 20.
Even, J., Pedesseau, L., Dupertuis, M.A., Jancu, J.M. & Katan, C. Electronic model for selfassembled hybrid organic/perovskite semiconductors: reverse band edge electronic states ordering and spinorbit coupling. Phys. Rev. B 86, 205301 (2012).
 21.
Xiao, Z. et al. Photovoltaic properties of twodimensional (CH_{3}NH_{3})_{2}Pb(SCN)_{2}I_{2} perovskite: a combined experimental and density functional theory study. J. Phys. Chem. Lett. 7, 1213–1218 (2016).
 22.
Keldysh, L. V. Coulomb interaction in thin semiconductor and semimetal films. Sov. J. Exp. Theor. Phys. Lett. 29, 658 (1979).
 23.
Pedesseau, L. et al. Advances and promises of layered halide hybrid perovskite semiconductors. ACS Nano 10, 9776–9786 (2016).
 24.
Mak, K. F. & Shan, J. Photonics and optoelectronics of 2D semiconductor transition metal dichalcogenides. Nat. Photonics 10, 216–226 (2016).
 25.
Li, L. et al. Direct observation of the layerdependent electronic structure in phosphorene. Nat. Nanotechnol. 12, 21–25 (2017).
 26.
Klingshirn, P. C. F. Semiconductor Optics (Springer, Berlin Heidelberg, 2012).
 27.
Kataoka, T. et al. Magnetooptical study on excitonic spectra in (C_{6}H_{13}NH_{3})_{2}PbI_{4}. Phys. Rev. B 47, 2010–2018 (1993).
 28.
Hirasawa, M., Ishihara, T., Goto, T., Uchida, K. & Miura, N. Magnetoabsorption of the lowest exciton in perovskitetype compound (CH_{3}NH_{3})PbI_{3}. Phys. B Condens. Matter 201, 427–430 (1994).
 29.
Ishihara, T. Optical properties of PbIbased perovskite structures. J. Lumin. 60, 269–274 (1994).
 30.
Tanaka, K. et al. Comparative study on the excitons in leadhalidebased perovskitetype crystals CH_{3}NH_{3}PbBr_{3} CH_{3}NH_{3}PbI_{3}. Solid State Commun. 127, 619–623 (2003).
 31.
Galkowski, K. et al. Determination of the exciton binding energy and effective masses for methylammonium and formamidinium lead trihalide perovskite semiconductors. Energy Environ. Sci. 9, 962–970 (2016).
 32.
Haldar, S. et al. Effect of carrier confinement on effective mass of excitons and estimation of ultralow disorder in Al_{x}Ga_{1}−_{x}As/GaAs quantum wells by magnetophotoluminescence. Sci. Rep. 7, 4905 (2017).
 33.
Tomić, S. et al. Influence of conductionband nonparabolicity on electron confinement and effective mass in GaN_{x}As_{1x}∕GaAs quantum wells. Phys. Rev. B 69, 245305 (2004).
 34.
Nelson, D. F., Miller, R. C. & Kleinman, D. A. Band nonparabolicity effects in semiconductor quantum wells. Phys. Rev. B 35, 7770–7773 (1987).
 35.
Lee, K.S. & Lee, E.H. Optical determination of the heavyhole effective mass of (In, Ga)As/GaAs quantum wells. ETRI J. 17, 13–24 (1996).
 36.
Cortecchia, D. et al. Broadband emission in twodimensional hybrid perovskites: the role of structural deformation. J. Am. Chem. Soc. 139, 39–42 (2017).
 37.
Kumagai, M. & Takagahara, T. Excitonic and nonlinearoptical properties of dielectric quantumwell structures. Phys. Rev. B 40, 12359–12381 (1989).
 38.
Cudazzo, P., Tokatly, I. V. & Rubio, A. Dielectric screening in twodimensional insulators: implications for excitonic and impurity states in graphane. Phys. Rev. B 84, 085406 (2011).
 39.
Chernikov, A. et al. Exciton binding energy and nonhydrogenic Rydberg series in monolayer WS_{2}. Phys. Rev. Lett. 113, 076802 (2014).
 40.
Berkelbach, T. C., Hybertsen, M. S. & Reichman, D. R. Theory of neutral and charged excitons in monolayer transition metal dichalcogenides. Phys. Rev. B 88, 045318 (2013).
 41.
Latini, S., Olsen, T. & Thygesen, K. S. Excitons in van der Waals heterostructures: the important role of dielectric screening. Phys. Rev. B 92, 245123 (2015).
 42.
Olsen, T., Latini, S., Rasmussen, F. & Thygesen, K. S. Simple screened hydrogen model of excitons in twodimensional materials. Phys. Rev. Lett. 116, 056401 (2016).
 43.
Sapori, D., Kepenekian, M., Pedesseau, L., Katan, C. & Even, J. Quantum confinement and dielectric profiles of colloidal nanoplatelets of halide inorganic and hybrid organic–inorganic perovskites. Nanoscale 8, 6369–6378 (2016).
 44.
Muljarov, E. A., Tikhodeev, S. G., Gippius, N. A. & Ishihara, T. Excitons in selforganized semiconductor/insulator superlattices: PbIbased perovskite compounds. Phys. Rev. B Condens. Matter 51, 14370–14378 (1995).
 45.
Yaffe, O. et al. Excitons in ultrathin organicinorganic perovskite crystals. Phys. Rev. B 92, 045414 (2015).
 46.
Gauthron, K. et al. Optical spectroscopy of twodimensional layered (C_{6}H_{5}C_{2}H_{4}NH_{3})_{2}PbI_{4} perovskite. Opt. Express 18, 5912–5919 (2010).
 47.
Dohner, E. R., Jaffe, A., Bradshaw, L. R. & Karunadasa, H. I. Intrinsic whitelight emission from layered hybrid perovskites. J. Am. Chem. Soc. 136, 13154–13157 (2014).
 48.
Meckbach, L., Stroucken, T. & Koch, S. W. Giant excitation induced bandgap renormalization in TMDC monolayers. Appl. Phys. Lett. 112, 061104 (2018).
 49.
Haug, H. & Koch, S. W. Quantum Theory of the Optical and Electronic Properties of Semiconductors: Fifth Edition (World Scientific Publishing Company, Singapore, New Jersey, London, 2009).
 50.
Kitazawa, N., Yaemponga, D., Aono, M. & Watanabe, Y. Optical properties of organic–inorganic hybrid films prepared by the twostep growth process. J. Lumin. 129, 1036–1041 (2009).
 51.
Even, J., Pedesseau, L. & Katan, C. Analysis of multivalley and multibandgap absorption and enhancement of free carriers related to exciton screening in hybrid perovskites. J. Phys. Chem. C 118, 11566–11572 (2014).
 52.
Hill, H. M. et al. Observation of excitonic Rydberg states in monolayer MoS_{2} and WS_{2} by photoluminescence excitation spectroscopy. Nano Lett. 15, 2992–2997 (2015).
 53.
Takagi, H., Sato, M., Takeoka, Y., Kunugita, H. & Ema, K. Influence of image charge effect on exciton fine structure in an organicinorganic quantum well material. AIP Conf. Proc. 1566, 435–436 (2013).
 54.
Christol, P., Lefebvre, P. & Mathieu, H. Fractional‐dimensional calculation of exciton binding energies in semiconductor quantum wells and quantum‐well wires. J. Appl. Phys. 74, 5626–5637 (1993).
 55.
Even, J., Pedesseau, L. & Katan, C. Understanding quantum confinement of charge carriers in layered 2D hybrid perovskites. ChemPhysChem 15, 3733–3741 (2014).
 56.
Nie, W. et al. Highefficiency solutionprocessed perovskite solar cells with millimeterscale grains. Science 347, 522–525 (2015).
 57.
Stier, A. V., Wilson, N. P., Clark, G., Xu, X. & Crooker, S. A. Probing the influence of dielectric environment on excitons in monolayer WSe_{2}: insight from high magnetic fields. Nano Lett. 16, 7054–7060 (2016).
 58.
Chuang, S.L., SchmittRink, S., Miller, D. A. B. & Chemla, D. S. Exciton Green’sfunction approach to optical absorption in a quantum well with an applied electric field. Phys. Rev. B 43, 1500–1509 (1991).
Acknowledgements
The work at Los Alamos National Laboratory (LANL) was supported by LDRD program (to J.C.B., W.N., S.T., A.D.M.) and was partially performed at the Center for Nonlinear Studies. J.C.B. and A.D.M. acknowledge support from the DOE (EERE 16471544). The work was conducted, in part, at the Center for Integrated Nanotechnologies (CINT), a U.S. Department of Energy, Office of Science user facility. Part of this work was performed at the National High Magnetic Field Laboratory, which is supported by NSF DMR1157490, NSF DMR1644779 and the State of Florida. S.A.C. acknowledges support from the DOE Basic Energy Sciences “Science of 100 T” program. Work at Northwestern University was supported by ONR grant N000141712231. The work in France was supported by Agence Nationale pour la Recherche (TRANSHYPERO project). This work was granted access to the HPC resources of (TGCC/CINES/IDRIS) under the allocation 2017A0010907682 made by GENCI. The work at Rice University (to F.K., G.T.N., J.K.) was supported by the NSF (Grant No. DMR1310138), the Robert A. Welch Foundation (Grant No. C1509) and the Air Force Office of Science Research (Grant No. FA95501410268).
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J.C.B. and A.D.M. conceived the idea, designed the experiments and wrote the manuscript. J.C.B. made the samples, performed the optical spectroscopy measurements, analyzed the data and provided insights into the mechanisms with support from J.J.C. A.V.S. performed the magnetoabsorption measurements and analyzed the data under the supervision of S.A.C. F.K. and G.T.N. performed magnetoabsorption measurements on the RPP with n equals to 1 under the supervision of J.K. J.E. developed the theoretical models. B.T. performed the DFT calculations with support from C.K., L.P. and M.K. M.G.K. and C.C.S. developed the chemistry for the synthesis of phasepure crystals with support from H.T. and W.N. All authors contributed to this work, read the manuscript and agree to its contents and all data are reported in the main text and supplemental information.
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Blancon, J., Stier, A.V., Tsai, H. et al. Scaling law for excitons in 2D perovskite quantum wells. Nat Commun 9, 2254 (2018). https://doi.org/10.1038/s4146701804659x
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