Skip to main content

Thank you for visiting 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.

Multi Band Gap Electronic Structure in CH3NH3PbI3


Organo-lead halide perovskite solar cells represent a revolutionary shift in solar photovoltaics, introducing relatively soft defect containing semiconductors as materials with excellent charge collection for both electrons and holes. Although they are based on the nominally simple cubic perovskite structure, these compounds are in fact very complex. For example, in (CH3NH3)PbI3 the dynamics and ensuing structural fluctuations associated with the (CH3NH3)+ ions and the interplay with the electronic properties are still not fully understood, despite extensive study. Here, using ab-initio calculations, we show that at room and higher temperature, the rotation of CH3NH3 molecules can be viewed as effectively giving local structures that are cubic and tetragonal like from the point of view of the PbI3 framework, though in fact having lower symmetry. Both of these structures are locally polar, with sizable polarization, ~10 μC/cm2 due to the dipoles on the organic. They become energetically degenerate in the volume range, V ~ 250 Å3/f.u–265 Å3/f.u. We also find very significant dependence of the band gap on the local structure. This type of transition is analogous to a transition between two ferroelectric structures, where in-spite of strong electron phonon coupling, there is strong screening of charged defects which can lead to enhanced mobility and charge collection. The results provide insights into the enhanced light absorption near the band edge and good charge collection in this material.


The organic-inorganic hybrid perovskites (OIHP) have emerged as an important new class of photovoltaics, exemplified by methylammonium lead iodide CH3NH3PbI3 (MAPbI3), Laboratory devices based on these have reported efficiency exceeding 21%1 which is comparable to or even higher than the performance of existing solar cell technologies. The pace of research and ensuing progress is also impressive since first report2 on perovskite photovoltaic whose progress has outshined those of other solar cell types in photovoltaic research. Many efforts have made to increase the efficiency of OIHP by chemically and structurally adjusting the band gap and other properties3,4. In addition, the specific chemical bonding of divalent group IV elements with halides has been invoked as a possible explanation for the excellent charge collection in these materials. Specifically, the defect tolerance has been associated with high dielectric constants, and therefore defect tolerance4, as discussed in terms of high Born charges on the Pb and halogen atoms in these and related halides5,6,7. There is therefore a strong interplay between the lattice structure and bonding of the PbI3 part of the unit cell and the charge collection. This is complicated by the symmetry lowering but presumably electronically inactive organic cation on the perovskite A-site.

In addition to the dielectric properties, important for charge collection in these defected materials, light absorption beginning with optimized band gaps is crucial. The band gap can be tuned in various ways, but it is important that the successful approaches are ones that give not only optimal band gaps, but good absorption near the band edge, without degradation of the charge collection7,8,9. Rashba band splitting due to the spin - orbit coupling has been suggested as a possible cause for the reduced recombination rate10,11,12. For the I4/mcm structure, Zheng et al.10 have shown that the spin forbidden transition between conduction band and valence band reduced the recombination rate; a similar phenomenon has also been unveiled by Etienne et al.11 who studied the dynamical origin of the Rashba effect. Experimentally, Wang et al., proved that a weak indirect band gap presents in MPbI3 as a result of Rashba splitting of the conduction band due to the spin-orbit coupling12. However, it is to be emphasized that the Rashba splitting depends on symmetry lowering, closely related to polar order.

The NH3CH3 (MA) molecules have been theoretically shown to play important roles in MAPbI3. Theoretical reports by Ong et al.13,14 revealed how the rotation of molecule CH3NH3 couples to the PbI3 host leading to effective structural phase changes, at least locally. By using the Van der Waals corrected Density Functional Theory, Motta et al.15 revealed that the rotation of orientation of CH3NH3 molecule in cubic MAPbI3 from [111] direction to [110] direction distorts the PbI6 octahedral cage and results in indirect band gap. Such an effect has been also investigated by Gao, et al.16. On the opposite, under the hydrostatic pressure, Wang et al.12 reported that the Rashba splitting is reduced due to a pressure induced reduction in local electric field around the Pb atom. The role of molecule rotation is excluded in that report. Experimentally at finite temperature, the CH3NH3 molecule is reported to orient randomly17,18,19, giving a net overall cubic centrosymmetric state. In the cubic phase, the nuclear magnetic resonance (NMR)20 showed that the MA cations reorient themselves with picosecond scale dynamics at high temperature but freeze at low temperatures. Importantly, it has been shown that that there are sizable effects on the optical properties associated with the dynamics of the MA from experiments. In particular, Quarti and co-workers21 does not abruptly change at the cubic-tetragonal phase transition, but gradually changes from 270–400 K, in spite of the phase transition at 327 K22. The temperature dynamical correlations between MA molecules near the phase transition remain to be fully elucidated, but near the transition it is likely that there is substantial local correlation between the MA orientations, and therefore on the time scale of optical and electronic processes it is likely that the behavior is influenced by local structural effects associated with this dynamics. Therefore, the influence of the orientation of molecule to the properties of hybrid perovskite still needs further investigation. In the present work we examine the magnitudes of local structural effects on the electronic and optical properties, using first principles calculations for ordered structures (see Methods).

Considering the PbI3 part of the structure (for the discussion, but not in the calculations, which necessarily include the full atomic structure, including the dipoles associated with the organic A-site, we describe the structure of the PbI3 with space groups that describe to a close approximation this part of the cell), the tetragonal phase I4mcm is stable only at V < 252 Å/f.u theoretically14, at higher volume the cubic Pm-3m and tetragonal P4mm phase are more stable. The tetragonal P4mm is obtained from cubic Pm-3m by deforming only one lattice constant along the c-axis, c ≠ a) and the tetragonal I4/mcm is a further deformation from P4mm by the rotation of octahedral PbI6 anti-phase tilt around the c-axis. Since solar cell is working at room temperature and higher, therefore our research mainly focuses on Pm-3m and P4mm structures. In this report, we study the impact of MA molecules to the efficiency of hybrid perovskite based solar cell. Our results show that the MA units easily rotate in PbI6 cuboctahedral, consistent with experiment, and these rotations are coupled significantly to the PbI3 lattice inducing structural changes from cubic Pm-3m to tetragonal P4mm and vice versa. This causes a momentum dependent splitting of energy band by Rashba effect due to the spin-orbit coupling, prevents the electron recombination, and induces a multi band gap electronic structure.

Results and Discussion

To study the impact of molecule rotation on the properties of MAPbI3, we study the influence of volume change to the rotation. We start with the most stable structure of P4mm with a = b = 6.32 Å, c = 6.31 Å14 and volume of V = 252 Å3, which is close to experimental data a = b = 6.312 Å, c = 6.316 Å, and V = 251.6 Å317. The orientation of MA molecule is studied at three different directions: quasi-[111], quasi [001] and quasi-[110]. For the P4mm, at each of specific lattice constant a = b and specific orientation of MA molecule the lattice constant c is fully relaxed. Our study shows that the orientation of MA molecule along the quasi-[001] direction gives almost the same energy as the quasi-[110] direction, see Fig. 1.

Figure 1

The energy-volume phase diagram of Pm-3m and P4mm with different MA orientations [111], [110] and [001]. The insets are crystal structures of MAPbI3 at different points \({1}_{110}^{t}\), \({1}_{001}^{t}\), \({1}_{110}^{c}\), and \({1}_{111}^{c}\), see text for details.

The energy-volume phase diagram of structures P4mm and Pm-3m (for the PbI3 part of the cell) is given in Fig. 1. The result shows that at the same volume there is no preferred direction for MA molecules in tetragonal P4mm. On the other hand, the [110] and [001] directions are preferred directions for MA molecule in Pm-3m phase. We notice here that the P4mm structure was reported to be more stable than the Pm-3m (MA molecule lies along the [111] direction) with V ~ 250 Å3/f.u–260 Å3/f.u 14. We find that a rotation out of [111] direction of MA molecule further stabilizes the Pm-3m structure but the P4mm is still more stable than the Pm-3m structure (V < 256 Å3/f.u) with very small energy difference of 1–2 meV. Thus the preference for the MA orientation away from [111] plays an important role in selecting the structure.

Experimentally, the P4mm and Pm-3m structures are stable at room and higher temperature. On the other hand, our result at V < 265 Å3/f.u reveals that energy difference between P4mm and Pm-3m phases with different molecule orientations [111], [110], [001] is at maximum of 25 meV or equivalent to ~300 K. Such small energy differences easily allow the rotation of MA molecules in the cuboctahedral PbI6 by thermal excitation as is known. It is interesting to explore how the rotation of MA molecules will affect the properties of MAPbI3. Let start from cubic structure Pm-3m with a = b = c = 6.32 Å and MA molecule oriented along the [111] direction, point \({1}_{111}^{c}\), see Fig. 1. In principal, from the [111] direction MA molecule can rotate to any directions. To ease the study, we select two most symmetry directions: [110] and [001]. Our study shows that for the Pm-3m structure, the rotation of MA molecule from [111] direction to [110] or [001] will further stabilize the Pm-3m structure. It is noticed here that both Pm-3m structures with MA molecule oriented along [110] and [001] direction give almost the same total energy, EC[110] ~ EC[001], therefore we report only [110] direction. The conclusions for [001] case are the same for [110] direction. The rotation from point \({1}_{111}^{c}\) to point \({1}_{110}^{c}\) results in energy difference E(\({1}_{110}^{c}\)) − E(\({1}_{111}^{c}\)) = −16 meV ~ 186 °K. Our results show that at point \({1}_{110}^{c}\) the MAPbI3 structure is further stabilized from cubic Pm-3m to tetragonal P4mm structure by changing the lattice c-constant from 6.32 Å to 6.26 Å, point \({1}_{110}^{t}\), see Fig. 1, with E(\({1}_{110}^{t}\)) −E(\({1}_{110}^{c}\)) = −2 meV ~ 23 °K. If the MA molecule is in [001] direction then the Pm-3m structure is further stabilized to P4mm structure by reducing the lattice constant from 6.32 Å to 6.30 Å, point \({1}_{001}^{t}\) with energy difference E(\({1}_{001}^{t}\)) −E(\({1}_{001}^{c}\)) = − 1meV ~ 11.6 °K. In short, the rotation of MA molecule in different directions results in small energy differences in comparison to thermal energy at room temperature. Therefore MA molecules rotate in the cuboctahedral PbI3 under the thermal excitation near room temperature consistent with experiments. As discussed, such rotations are coupled to strain including volume, creating a breathing of the MAPbI3. In general, this type of coupling provides a local strain coupling that favors formatiion of regions or clusters of like orientation, and in the case of phase transitions, favors first order character with co-existence.

It is interesting to further explore the effect of such rotation on the electronic properties of MAPbI3. To investigate this effect we use the Tran-Blaha Modified Becke-Johnson (TB-MBJ) potential in general potential linearized augmented planewave (LAPW) method as implemented in the WIEN2k code23,24 to improve the value of band gap, which is under estimated by using the PBE25 or PBEsol26 GGA calculations. The TB-MBJ has been proved to give good band gap in comparison to GW method for s- and p –electron systems, which is applicable to MAPbI323. Our results, see Fig. 1, show that the [110] direction is the most stable direction for MA molecule in both Pm-3m and P4mm structure. The rotation of MA molecule causes a large difference in band gap and in general MAPbI3 gets (i) highest band gap with the tetragonal P4mm symmetry and MA molecule in [110] direction and (ii) lowest band gap with cubic Pm-3m symmetry and MA molecule in [111]. Figure 1 shows that at V < 265 Å3/f.u the maximum energy difference between phases is about 22 meV~255 0K which means that MA molecules are easy to rotate by thermal excitation at room temperature and higher. Such rotation not only changes the structure of MAPbI3 but also the energy band gap such as, at V = 252 Å3/f.u the rotation of MA molecule from [110] direction to [001] direction does not change much the energy band gap of MAPbI3, Egap ~ 1.22 eV, while the rotation from [110] direction to [111] direction reduces the energy band gap to Egap = 1.02 eV, 0.2 eV smaller. At higher volume the rotation of MA molecule results in larger band gap difference, larger shrinkage and expansion of volume. For example at V = 267 Å3/f.u the energy band gap of MAPbI3 is 1.2 eV in Pm-3m with molecule oriented in [111] direction. The rotation of molecule from [111] (Egap ([111]) = 1.02 eV) to [110] results in band gap of 1.32 eV. When MA molecule is in [110] direction, a further deformation from Pm-3m structure to P4mm by reducing the lattice constant c results in volume reducing from V~ 267 Å3/f.u to V~257 Å3/f.u and the band gap gets value of 1.4 eV, see Fig. 2.

Figure 2

Energy band gap as a function of volume for Pm-3m and P4mm structure.

At lower volume V < 250 Å3/f.u the rotation of MA molecules in cuboctahedral PbI3 will transform the MAPbI3 from tetragonal P4mm to tetragonal I4/mcm14. Our calculations show that the transition results in big jump of energy band gap, such as at V = 252 Å3/f.u the P4mm has band gap of 1.22 eV while the I4/mcm at V = 251.02 Å3/f.u has energy band gap of 1.55 eV which is in agreement with experimental report1. Therefore at V ~ 251–252 Å3/f.u, the structure is sensitive with structural change and may co-exit three phases Pm-3m, P4mm and I4/mcm due to the rotation of molecules under thermal excitation. At lower volume V < 250 Å3/f.u the MAPbI3 is stabilized by I4/mcm structure due to larger energy difference between I4/mcm and P4mm phase and low thermal excitation energy.

The rotation of MA molecule varies the energy band gap of MAPbI3 with an average amount of 0.2 eV down to the redshifted spectra, which help to enhance the efficiency of solar absorber. It is more insightful to know how such rotation will affect the band structure of MAPbI3. The band structures of MAPbI3 at points \({1}_{111}^{c}\), \({1}_{110}^{c}\),(a = b = c = 6.32 Å), \({1}_{110}^{t}\) (a = b = 6.32 Å c = 6.26 Å) and \({1}_{001}^{t}\) (a = b = 6.32 Å, c = 6.30 Å) are given in Fig. 3. The results show that for cubic structure when the MA molecule is in the [111] direction then the energy band gap is direct band gap at A[½ ½ ½]. The rotation of MA molecule out of the [111] direction results in indirect bandgaps and higher energy band gap for both Pm-3m and P4mm structure, see Fig. 3. The rotation of molecules therefore not only changes the crystal structure, tunes the band gap of MAPbI3 but also tunes the nature of the band gap from direct to indirect and vice versa.

Figure 3

The band structure of MAPbI3 at: (a) points \({1}_{111}^{c}\), (b) \({1}_{110}^{c}\), (a = b = c = 6.32 Å), (c) \({1}_{110}^{t}\) (a = b = 6.32 Å c = 6.26 Å) and (d) \({1}_{001}^{t}\) (a = b = 6.32 Å, c = 6.30 Å) with X = [1/2 0 0] A [½ ½ ½], Γ [0 0 0], Z [0 0 ½] and M [½ ½ 0].

The nature of the band gap (indirect vs. direct) comes from the momentum dependent splitting of energy bands by Rashba effect due to the spin-orbit coupling. This effect has been mainly studied for the I4/mcm structure and much less studied for cubic Pm-3m and tetragonal P4mm. In principle the spin-orbit coupling causes the energy band splitting in cubic Pm-3m and tetragonal P4mm symmetry but there is no momentum dependent splitting of the energy band, the Rashba effect. The momentum dependent splitting of energy bands that occurs in these structures (Fig. 3) is due to the rotation of MA molecules in the PbI3 cuboctahedral. This rotation lowers the symmetry. However, the fast rotation of MA molecules in PbI3 cuboctahedral at room and higher temperature in a time average would make the MA molecule behave as a point like particle (Fig. S1, supporting information). The effect of spin-orbit coupling on the momentum dependent splitting of energy band due to the rotation of MA molecules in PbI3 cuboctahedral is reported in supporting information. The study reveals a strong dependence of Rashba interaction coefficient on the volume and the orientation of MA molecule in PbI3 cuboctahedral.

Since the rotational dynamics of the MA molecules may be correlated through strain coupling, [11] it may be useful to consider a new band structure, which is a combination of band structures of MAPbI3 with MA molecules in different directions. There are four structures in our cases: Pm-3m structure with MA molecule in [111] and [110]/[001] direction, P4mm structure with MA molecule in [110] and [001] direction, see Fig. 4. This is germane to the case where the correlation length for MA rotation is significantly longer than the unit cell dimension, so that local band structures are important. The new energy band structure has features of good solar absorber materials with (1) multi energy bandgaps and (2) indirect energy bandgaps. The most extension of energy band gap to the lower value comes from the rotation of MA molecule to the [111] direction. The multi energy band gap structure (1) allows more photons with different wavelengths are absorbed. The indirect energy band gap (2) prevents the recombination of electrons in the conduction band with holes in the valence band. This mechanism enhances the electron density in the conduction band of MAPbI3 and their lifetime.

Figure 4

The new band structure of MAPbI3 which is the combination of 4 band structures in Fig. 3 (a) at a = b = 6.32 Å, see text for c-parameters. (b) The band structure with a = b = 6.438 Å and c = 6.438 Å(Pm-3m), c = 6.21 Å [110] (P4mm), c = 6.242 Å [001] (P4mm). The color lines/circles match with report in Fig. 3.

The rotation of MA molecule in the cuboctaheral PbI3 causes an electronic polarization. The momentum dependent splitting of energy band only appears in case of anisotropy. To investigate this effect, we calculate the volume evolution of electronic polarization when the MA molecules are in different orientations. The results are shown in Fig. 5. The result clearly shows that for cubic structure when the MA molecule is in [111] direction then the polarizations in three different directions are almost the same. Such effect results in a very weak energy band splitting as shown in Fig. 3a. When MA molecule is in [110] or [001] direction, the electronic polarizations in different directions are very much different, see Fig. 5(b–d), causing a strong energy band splitting as shown in Fig. 3(b–d).

Figure 5

The Volume evolution of electron polarization of MAPbI3 with different MA orientations (a) cubic [111]; (b) cubic [110]; (c) P4mm [001]; and (d) P4mm [110].

The rotation of MA molecule changes the lattice constants continuously in three directions from a to a-δ and vice versa with δ is the lattice constant difference between cubic Pm-3m and tetragonal P4mm when MA molecule is in the [110] direction. Since we are studying the MAPbI3 by using density functional theory i.e., one unit cell with periodic conditions, therefore this phenomenon is only valid when all molecules rotate at the same direction. In general, without any external constrain, at the same time all MA molecules in MAPbI3 rotate non-orientation. Such free rotation induces a continuous change of PbI3 cuboctahedral, shrink and expand in all directions. Therefore the lattice constant may be effectively considered as the quasi-cubic Pm-3m structure or quasi-tetragonal P4mm structure with lattice constants a = b~c.


In summary, we have studied the impact of correlated orientations of MA molecules on the evolution of crystal structures, energy band structures and energy band splitting of MAPbI3 focusing on Pm-3m and P4mm structure. The results showed that at V = 250 Å3/f.u three structures I4/mcm, P4mm and Pm-3m coexist. The energy band gap of I4/mcm structure is 1.55 eV which is in perfect agreement with experimental report but it is about 1.2 eV for Pm-3m and P4mm structure when MA molecule is in the [001] and [110] direction. When MA molecule is in the [111] direction, the MAPbI3 is stabilized with Pm-3m structure with energy band gap of 1.02 eV. At higher volume the P4mm and Pm-3m is more stable than I4/mcm. Although the MAPbI3 is stable with Pm-3m structure and MA molecule is in [110] direction, the rotations of MA molecules induce the change of local lattice constants. Therefore MAPbI3 can exist in both Pm-3m and P4mm structures. The volume evolution of band structure shows an increasing trend of energy band gap with volume. The rotation of MA molecule defines the direct and indirect nature of energy band gap with an extension 0.2 eV of energy band gap down to redshifted region when MA molecule is in [111] direction. A new band structure has been proposed with new features (1) multi energy bandgaps and (2) indirect energy bandgaps. Study on the spin-orbit induced band splitting effect shows strong dependence of Rashba interaction coefficient on the volume and the orientation of MA molecule in cuboctahedral PbI3.


For the calculations of electronic structures and related properties of MAPbI3 we use the projector augmented wave (PAW) method27 with the Perdew-Burke-Ernzerhof (PBE)25 and the PBE revised for solids (PBEsol)26 generalized gradient approximation (GGA) exchange correlation potentials as implemented in the VASP code28. The cut-off energy for the plane wave expansion of the wave functions is 500 eV, and all atoms in the unit cell are fully relaxed till the Hellman-Feynman forces are less than 0.005 eV/Å. The 6 × 6 × 6 Monkhorst-Pack grid of k-points29 for Brillouin zone integration was used in calculations for Pm-3m and P4mm structures. The semicore states of the Pb atoms are treated as valence electrons; i.e., 14 valence electrons for Pb (5d106s2 6p2). The I-5s25p5, C-2s22p2, N-2s22p3 and H-1s were considered as valence electrons.

The symmetry of Pm-3m and P4mm is built based on the PbI3 frame without the presence of molecule CH3NH3. After the frame is built then the molecule CH3NH3 is added to the center of the PbI3 frame at different orientations [001], [110] and [111]. At each of specific orientation the MAPbI3 crystal structure is fully relaxed without any constrain on the symmetry. The obtained structures are therefore at P1 symmetry in general due to the presence of CH3NH3 molecule and they are very close to the Pm-3m or P4mm symmetry. Therefore they are called a pseudo-cubic Pm-3m or a pseudo-tetragonal P4mm.

We applied the Van der Waals correction force (vdW-DF2 or D2)30, which is proved to be the best in comparison the lattice constant of CH3NH3PbI3 with experimental data31, in our calculation and find that the PBEsol and PBE + vdWDF2 give the same results as reported by Menendex, ref.31. On the other hand, our results based on the vdW-D3 correction method by Grimme et al.32, which is reported by Thind et al.33, underestimate the lattice constant of the cubic structure Pm-3m in comparison to experimental data, see the table S1. Because of this we preferred to use PBEsol method instead of PBE-vdW-D3.

To calculate the energy band structure of MAPbI3 we use the WIEN2k software package23. This program allows to compute the electronic structure of MAPbI3 within DFT utilizing the full potential (linear) augmented plane wave + local orbitals (APW + lo) method and applying the MBJ method24. The atomic sphere radii of MAPbI3 are chosen as 2.5 a.u for Pb and I; 1.28 a.u for N, 1.34 a.u for C and 0.69 a.u for H. Inside the atomic spheres, the partial waves were expanded up to lmax = 10 and the number of plane waves was limited by a cut off Kmax = 4.64 (a.u−1). The charge density was Fourier-expanded with Gmax = 20 Ry. A k-mesh of 10 × 10 × 10 in the full Brillouin zone was used. In addition to the usual valence states, also extra local orbitals for “semi-core” states (Pb- 5b, 5d, 6 s, 6p; I-4d, 5 s, 5p; N: 2p, and C:2p) were added and considered as band states.


  1. 1.

    Zhou, H. et al. Interface engineering of highly efficient perovskite solar cells. Science 345, 542–546 (2014).

    ADS  CAS  Article  Google Scholar 

  2. 2.

    Kojima, A., Teshima, K., Shirai, Y. & Miyasaka, T. Organometal halide perovskites as visible-light sensitizers for photovoltaic cells. J. Am. Chem. Soc. 131, 6050–6051 (2009).

    CAS  Article  Google Scholar 

  3. 3.

    Deschler, F. et al. High photoluminescence efficiency and optically pumped lasing in solution-processed mixed halide perovskite semiconductors. J. Phys. Chem. Lett. 5, 1421–1426 (2014).

    CAS  Article  Google Scholar 

  4. 4.

    Chattopadhyay, D. & Queisser, H. J. Electron scattering by ionized impurities in semiconductors. Rev. Mod. Phys. 53, 745–768 (1981).

    ADS  CAS  Article  Google Scholar 

  5. 5.

    Du, M. H. Efficient carrier transport in halide perovskites: theoretical perspectives. J. Mater. Chem. A 2, 9091–9098 (2014).

    CAS  Article  Google Scholar 

  6. 6.

    Brivio, F., Walker, A. B. & Walsh, A. Structural and electronic properties of hybrid perovskites for high-efficiency thin-film photovoltaics from first principles. APL Mater. 1, 042111-1-5 (2013).

    ADS  Article  Google Scholar 

  7. 7.

    Du, M. H. & Singh, D. J. Enhanced Born charge and proximity to ferroelectricity in thallium halides. Phys. Rev. B 81, 144114-1-5 (2010).

    ADS  Google Scholar 

  8. 8.

    Mosconi, E., Amat, A., Nazeeruddin, M. K., Grätzel, M. & De Angelis, F. First principles modeling of mixed halide organometal perovskites for photovoltaic applications. J. Phys. Chem. C 117, 13902–13913 (2013).

    CAS  Article  Google Scholar 

  9. 9.

    Wehrenfennig, C., Eperon, G. E., Johnston, M. B., Snaith, H. J. & Herz, L. M. High charge carrier mobilities and lifetimes in organolead trihalide perovskites. Adv. Mater. 26, 1584–1589 (2014).

    CAS  Article  Google Scholar 

  10. 10.

    Zheng, F., Tan, L. Z. & Rappe, A. M. Rashba spin-orbit splitting enhanced carrier lifetime in CH3NH3PbI3. Nano. Lett. 15, 7794–7800 (2015).

    ADS  CAS  Article  Google Scholar 

  11. 11.

    Etienne, T., Mosconi, E. & Angelis, F. D. Dynamical origin of the Rashba effect in organohalide lead perovskites: A key to suppressed carrier recombination on perovskite solar cells. J. Phys. Chem. Lett. 7, 1638–1645 (2016).

    CAS  Article  Google Scholar 

  12. 12.

    Wang, T. et al. Indirect to direct band gap transition in methylammonium lead halide perovskte. Energy Environ. Sci. 10, 509–515 (2017).

    CAS  Article  Google Scholar 

  13. 13.

    Ong, K. P., Goh, T. W., Xu, Q. & Huan, A. Mechanical origin of the structural phase transition in methylammonium lead iodide CH3NH3PbI3. J. Phys. Chem. Lett. 6, 681–685 (2015).

    CAS  Article  Google Scholar 

  14. 14.

    Ong, K. P., Goh, T. W., Xu, Q. & Huan, A. Structural evolution in methylammonium lead iodine CH3NH3PbI3. J. Phys. Chem. A 19, 11033–11038 (2015).

    Article  Google Scholar 

  15. 15.

    Motta, C. et al. Revealing the role of organic cations in hybrid halide perovskite CH3NH3PbI3. Nat. Commun. 6, 1–7 (2015).

    ADS  Article  Google Scholar 

  16. 16.

    Gao, W. W. et al. Quasiparticle band gap of organic-inorganic hybrid perovskites: Crystal structure, spin-orbit coupling, and self-energy effects. Phys. Rev. B 93, 085202 (2016).

    ADS  Article  Google Scholar 

  17. 17.

    Baikie, T. et al. Synthesis and crystal chemistry of the hybrid perovskite (CH3NH3)PbI3 for solid-state sensitised solar cell applications. J. Mater. Chem. A 1, 5628–5641 (2013).

    CAS  Article  Google Scholar 

  18. 18.

    Onoda-Yamamuro, N., Matsuo, T. & Suga, H. Calorimetric and IR spectroscopic studies of phase transitions in methylammonium trihalogenoplumbates. J. Phys. Chem. Solids 51, 1383–1395 (1990).

    ADS  CAS  Article  Google Scholar 

  19. 19.

    Weller, M. T. et al. Complete structure and cation orientation in the perovskite photovoltaic methylammonium lead iodide between 100 and 352 K. Chem. Commun. 51, 4180–4183 (2015).

    CAS  Article  Google Scholar 

  20. 20.

    Wasylishen, R., Knop, O. & Macdonald, J. Cation rotation in methylammonium lead halides. Solid State Commun. 56, 581–582 (1985).

    ADS  CAS  Article  Google Scholar 

  21. 21.

    Quarti, C. et al. Structural and optical properties of methylammonium lead iodide across the tetragonal to cubic phase transition: implications for perovskite solar cells. Energy Environ. Sci. 9, 155–163 (2016).

    CAS  Article  Google Scholar 

  22. 22.

    Poglitisch, A. & Weber, D. Dynamic disorder in methylammoiuntrihalogenoplumbates (II) observed by millimeter-wave spectroscopy. J. Chem. Phys. 87, 6373–6378 (1987).

    ADS  Article  Google Scholar 

  23. 23.

    Blaha, P., Schwarz, K., Madsen, G. K. H., Kvasnicka, D. & Luitz, J. WIEN2k, an augmented plane wave + local orbitals program for calculating crystal properties. (Techn. Universität Wien, Austria, 2009).

  24. 24.

    Tran, F. & Blaha, P. Accurate band gaps of semiconductors and insulators with a semilocal exchange-correlation potential. Phys. Rev. Lett. 102, 226401 (2009).

    ADS  Article  Google Scholar 

  25. 25.

    Perdew, J. P., Burke, S. & Ernzerhof, M. Generalized gradient approximation made simple. Phys. Rev. Lett. 77, 3865 (1996).

    ADS  CAS  Article  Google Scholar 

  26. 26.

    Perdew, J. P. et al. Restoring the density –gradient expansion for exchange in solids and surfaces. Phys. Rev. Lett. 100, 136406 (2008).

    ADS  Article  Google Scholar 

  27. 27.

    Blochl, P. E. Projector Augmented-Wave Method. Phys. Rev. B 50, 17953 (1994).

    ADS  CAS  Article  Google Scholar 

  28. 28.

    Kresse, G. & Furthmuller, J. Efficient Iterative Schemes for Ab Initio Total-Energy Calculations Using a Plane-Wave Basis Set. Phys. Rev. B 54, 11169 (1996).

    ADS  CAS  Article  Google Scholar 

  29. 29.

    Monkhorst, H. J. & Pack, J. D. Special Points for Brillouin-Zone Integrations. Phys. Rev. B 13, 5188 (1976).

    ADS  MathSciNet  Article  Google Scholar 

  30. 30.

    Lee, K., Murray, E. D., Kong, L., Lundqvist, B. I. & Langreth, D. C. Phys. Rev. B 82, 081101 (2010).

    ADS  Article  Google Scholar 

  31. 31.

    Menendex-Proupin, E., Palacious, P., Wahnon, P. & Conesa, J. C. Phys. Rev. B 90, 045207 (2014).

    ADS  Article  Google Scholar 

  32. 32.

    Grimme, S., Antony, J., Ehrlich, S. & Krieg, S. H. A consistent and accurate ab initio parametrization of density functional dispersion correction (DFT-D) for the 94 elements H-Pu. J. Chem. Phys. 132, 154104 (2010).

    ADS  Article  Google Scholar 

  33. 33.

    Thind, A. S., Huang, X., Sun, J. & Mishra, R. First Principles Prediction of a stable Hexagonal Phase of CH3NH3PbI3. Chem. Mat. 29, 6003 (2017).

    CAS  Article  Google Scholar 

Download references


This work was supported by Institute of High Performance Computing, Agency of Science, Technology, And Research (A*STAR). Work at Nanyang Technological University (NTU) was supported by Singapore Ministry of Education through AcRF Tier1 grant MOE2017-T1-002-142.

Author information




Theoretical calculations were carried out by K.P.O., S.W., Z.F. and M.B.S. All authors contributed to interpretation of the results. The manuscript was prepared by K.P.O., S.W., D.J.S., Z.F., T.H.N., M.S. and C.D.

Corresponding authors

Correspondence to Khuong P. Ong or Cuong Dang.

Ethics declarations

Competing Interests

The authors declare no competing interests.

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

Reprints and Permissions

About this article

Verify currency and authenticity via CrossMark

Cite this article

Ong, K.P., Wu, S., Nguyen, T.H. et al. Multi Band Gap Electronic Structure in CH3NH3PbI3. Sci Rep 9, 2144 (2019).

Download citation

Further reading


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.


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