Abstract
Ferroelectric Rashba semiconductors (FERSCs) have recently emerged as a promising class of spintronics materials. The peculiar coupling between spin and polar degrees of freedom responsible for several exceptional properties, including ferroelectric switching of Rashba spin texture, suggests that the electron’s spin could be controlled by using only electric fields. In this regard, recent experimental studies revealing chargetospin interconversion phenomena in two prototypical FERSCs, GeTe and SnTe, appear extremely relevant. Here, by employing density functional theory calculations, we investigate spin Hall effect (SHE) in these materials and show that it can be large either in ferroelectric or paraelectric structure. We further explore the compatibility between doping required for the practical realization of SHE in semiconductors and polar distortions which determine Rashbarelated phenomena in FERSCs, but which could be suppressed by free charge carriers. Based on the analysis of the lone pairs which drive ferroelectricity in these materials, we have found that the polar displacements in GeTe can be sustained up to a critical hole concentration of over ~10^{21}/cm^{3}, while the tiny distortions in SnTe vanish at a minimal level of doping. Finally, we have estimated spin Hall angles for doped structures and demonstrated that the spin Hall effect could be indeed achieved in a polar phase. We believe that the confirmation of spin Hall effect, Rashba spin textures and ferroelectricity coexisting in one material will be helpful for design of novel allinone spintronics devices operating without magnetic fields.
Introduction
Employing electron’s spin for information processing is one of the main goals of semiconductor spintronics.^{1,2} The electric and nonvolatile control of spins in recently discovered ferroelectric Rashba semiconductors (FERSCs) holds a promise to combine storage, memory and computing functionalities.^{3,4} The exceptional properties of these novel materials arise from the unique property that the spin degrees of freedom are coupled to the electric polarization, whereby the polar axis intrinsically breaks the inversion symmetry (IS). The giant Rashba spinsplitting of the bulk electronic states can be then switched with the ferroelectric orientation and controlled by an electric field. On the other hand, the large spin–orbit coupling (SOC) required in these materials could also give rise to chargetospin interconversion phenomena, such as spin Hall effect (SHE),^{5,6,7,8} Edelstein–Rashba effect^{9} or spin galvanic effect^{10} allowing the electric control of spin currents.^{11} In this paper, we have theoretically studied the intrinsic SHE in two prototype FERSC compounds, GeTe and SnTe, and explored its compatibility with the polar distortion, a fundamental property in these materials.
The ferroelectric XTe (X = Ge, Sn) monochalcogenides share rhombohedrally distorted rocksalt structure (space group R3m, Fig. 1). Both possess spontaneous electric polarization \(\overrightarrow{P}\) parallel to [111] direction, but the high Curie temperature of GeTe (T_{C} = 700 K)^{12,13} allowed indepth experimental studies of the ferroelectric phase, which proved the polarization switching,^{14} electronic structures^{15,16,17} and reversible Rashba spin textures.^{18} Importantly, spintocharge conversion has been recently measured via spin pumping experiments in Fe/GeTe bilayers demonstrating high potential of such interfaces for multifunctional spintronics applications.^{19,20,21} On the other hand, ferroelectric phase of SnTe (T_{C} = 100 K)^{22} has been known mainly from the theoretical side.^{23} Although the intermediate topological phases predicted at the phase transition still await an experimental confirmation, even the room temperature cubic crystal is intriguing, as it represents a prototypical example of a topological crystalline insulator.^{24} Finally, recent spin pumping experiments performed for the highsymmetry paraelectric bulk revealed strong SHE whose origin remains elusive.^{25}
Our calculations based on density functional theory (DFT) allowed us to quantitatively estimate spin Hall conductivities (SHCs) for low and highsymmetry structures of both materials. First, we have unveiled that the ferroelectric phase could indeed enhance the SHE as compared with the paraelectric structure. We have interpreted this effect in terms of additional contributions to spin Berry curvature, originating from spinsplitted electronic states in the polar phase. Second, since the realization of SHE in semiconductors requires doping, we have studied the evolution of polar distortion with respect to the charge carrier concentration and estimated critical levels of doping that can sustain the lowsymmetry phase. Finally, we have calculated spin Hall angles for doped structures and explored their potential for practical realization of SHE and electric control of Rashba effect (RE) at the same time.
Results and discussion
Electronic properties and SHE
Spin Hall materials are usually found either among elemental metals with strong SOC^{26,27,28} or novel topological phases, such as Weyl and Dirac nodal line semimetals where spin–orbitprotected gaps between the electronic bands are crossed by the Fermi level.^{29,30,31} It has also been known that a giant RE could induce large SHC as long as the Fermi level can be tuned and brought between lower and upper Rashba bands.^{32} In a polar material, the IS breaking gives rise to giant Rashba spin–orbitderived spin splittings of the electronic states. Therefore, we expect that the ferroelectric structure could, in principle, enhance the SHC over the paraelectric phase at specific values of the chemical potential.
Before we start a more detailed analysis of the relationship between electronic structures and SHCs in polar and nonpolar phases, let us briefly comment on the accuracy of our calculations, essential for realistic evaluation of the SHC. Figure 2a shows the band structure calculated for the ferroelectric GeTe (blue line) along the highsymmetry directions defined in Fig. 1b. The ferroelectric distortion of the rhombohedral structure gives rise to inequivalent hexagonal faces in the Brillouin zone (BZ), two of them perpendicular to the polar axis and centered at Z points, and six corresponding to other hexagons centered at L, as marked in the scheme. The band structure agrees perfectly with earlier theoretical predictions and experimental results. In particular, our band gap E_{g} = 0.65 eV is very close to the experimental one (0.61 eV)^{33} and coincides exactly with the value obtained previously with Heyd–Scuseria–Ernzerhof (HSE) hybrid functional.^{3} We note that a simple PBE calculation yields an incorrect energy gap of only 0.3 eV. Importantly, the reliable value of the band gap is relevant for the estimation of Rashba spin splittings. They can be easily noticed in Fig. 2a, especially close to the valence band maximum (VBM) and highest conduction band minimum (HBM) along the ZU direction. Their values, 250 meV and 100 meV for valence and conduction bands, respectively, are again in excellent agreement with the HSE calculations and with experimental results reporting giant RE in bulk electronic states of GeTe.^{3,17,18} The corresponding Rashba parameters (6.4 and 2.4 eVÅ) are comparable with the values in different polar materials, such as BiTeI.^{34}
Surprisingly, despite much smaller polar displacement, the electronic properties of the ferroelectric SnTe are quite similar to those described above. The strong SOC combined with the small band gap (0.33 eV) induces giant Rashba splittings (parameters) of the valence and conduction bands along ZU path, estimated to approximately 180 and 290 meV (4.0 and 8.3 eVÅ), respectively, again in good agreement with earlier hybrid functional calculations.^{23}
As a next step, we will analyze the intrinsic SHE in both compounds. By using Bilbao Crystallographic Server,^{35,36} we have determined nonzero elements of \({\sigma }_{ij}^{k}\) and expressed them in terms of four independent components identified in the ferroelectric phase (space group no. 160). The third rank tensor of SHC can be written by treating different spin polarizations as separate matrices in the following form:
We have also performed an analogous symmetry analysis for the paraelectric phase (space group no. 225) and found only one independent component of the SHC tensor; more specifically, the elements of the matrices above are all identical, except for \({\sigma }_{xx}^{x}\) which vanishes in such a case.
Figure 2c–c′ shows SHC components \({\sigma }_{xy}^{z}\), \({\sigma }_{yz}^{x}\) and \({\sigma }_{zx}^{y}\) representing typical experimental geometries. We note that the elements \({\sigma }_{yx}^{y}={\sigma }_{xy}^{y}={\sigma }_{yy}^{x}={\sigma }_{xx}^{x}\) describe either rarely occuring configurations with spin polarizations aligned along spin/charge current or socalled longitudinal spin currents flowing in the direction of charge current. Because it is not yet clear whether they should be classified as SHEs,^{37} we have omitted them in the discussion below (\({\sigma }_{xx}^{x}\) is reported in the Supplementary Fig. 1). The plotted SHCs strongly suggest a sizable SHE in either ferroelectric (blue) or centrosymmetric (red) configuration. It emerges due to the significant impact of SOC on the electronic states, as deduced from the comparison between fullyrelativistic and scalarrelativistic electronic structures. Nevertheless, it is evident that the magnitudes of SHCs are not identical in the two phases. Although the difference could arise either from the unit cell deformation or the polar displacement itself, a closer analysis revealed that the component \({\sigma }_{yz}^{x}\) changes mostly because of the deviation from the cubic unit cell, while the modifications in \({\sigma }_{xy}^{z}\) and \({\sigma }_{zx}^{y}\) arise predominantly from differences in the internal positions. As the latter leads to the IS breaking and Rashba spinsplitting in several regions of the BZ, we are convinced that it must be also a cause of a slight change in the magnitudes of SHC.
Finally, we note that in both materials the enhancement in the ferroelectric phase is rather small; for example, the feature that may really contribute to SHE in polar GeTe is a small peak of \({\sigma }_{xy}^{z}\) just below the Fermi level achievable in the presence of moderate doping. The difference is even more difficult to notice in SnTe, as all SHC components have comparable magnitudes, similar to the cubic phase (Fig. 2c′). We also emphasize that the band structures might change significantly upon the charge injection, thus the analysis based on the rigid shift of the chemical potential in Fig. 2c–c′ anyway provides only a rough approximation of SHC in doped materials. In order to obtain more realistic predictions, we have performed additional calculations which explicitly takes charge carriers into account.
Dopinginduced evolution of polar displacements
The idea of realizing SHE in a device based on FERSC raises the question whether ferroelectricity, the key property of these materials, can be sustained upon doping which is required to achieve a nonzero SHC. In fact, the existence of ferroelectric metals has been debated for several years,^{38,39} as not only do the conduction charges screen the external electric fields, but they also suppress the Coulomb interactions that give rise to polar distortions. Although true ferroelectric metals are rare,^{40,41,42} it has been shown that the polar phase can survive in some materials upon doping. For example, ferroelectric distortions in BaTiO_{3} are sustained up to a critical concentration of 0.11e per unit cell volume (u.c.),^{43,44} whereas in BiFeO_{3}, PbTiO_{3} and other lonepairdriven ferroelectrics the charge injection even enhances the polar structures.^{45,46} Since the response to doping will depend, in general, on the origin of ferroelectricity (e.g. shortrange vs longrange interactions among other factors),^{47,48} a careful analysis is needed to confirm the compatibility between SHE and the polar phase.
The ferroelectric displacement in both GeTe and SnTe is driven by the lone pair of the cation. As it has been shown in detail by Waghmare et al., the stereochemical activity of the latter is determined by the interacting s and p states of the cation mediated by the mixing with the anion p states.^{49} The strictly chemical origin of the ferroelectricity suggests that the displacement might be sustained even in the presence of free charges screening the Coulomb interaction. We note, however, that the previous studies demonstrating the persistence of polar distortion in lonepairdriven ferroelectrics were focused on electron doping, while GeTe and SnTe are always ptype doped due to the vacancies that naturally form in these materials.^{50} In the analysis below, we consider both signs of charge in order to provide a complete picture of the physics behind.
Figure 3a shows the evolution of polar displacement in GeTe as a function of charge carrier concentration. We can immediately notice that n and ptype doping yield two completely different structural scenarios. In case of the former, the displacements are indeed enhanced, similarly as in the previous studies of lonepairdriven ferroelectrics. In contrast, ptype doped structures reveal a rather fast decay of polar distortions which vanish above the critical hole concentration of n = 0.13∣e∣/u.c. corresponding to about 2.2 × 10^{21}/cm^{3}, closely resembling the behavior of BaTiO_{3} with ferroelectric instability ensured by the Coulomb force.^{43} This indicates that the lone pairs in GeTe might become less active upon ptype doping. We also notice that the volumes of the unit cell, Fig. 3b, follow quite similar trend, i.e. a larger displacement tends to increase the volume, while paraelectric structures favor smaller unit cells. Finally, ferroelectric to paraelectric transition in ptype doped regime is further confirmed by the phonon calculations of the doped cubic cells shown in Fig. 3c. Ferroelectric instabilities manifest as the imaginary frequencies of phonons that soften close to the point of phase transition.
In order to shed more light on these intriguing findings, we have calculated the electron localization function (ELF) which helps to identify regions associated with electron pairs. Figure 3d compares ELF plotted for selected configurations from Fig. 3a–c as well as for an undistorted structure. The lone pairs are seen as pronounced red regions around the Ge atoms, rather spherical in the centrosymmetric configuration (upper left) and distorted in the ferroelectric structure (upper right). The asymmetric lobe confirms the activity of the lone pair in the polar phase and demonstrates dominant role that it plays in the mechanism of ferroelectricity. Furthermore, the comparison of the heavily p and ntype ‘ferroelectrics’ (bottom right and left, respectively) clearly shows that in the former the lobes resemble those observed in the centrosymmetric structure. In contrast, the asymmetric lobe in the electrondoped configuration is even more enhanced with respect to the undoped ferroelectric, which indicates a stronger stereochemical activity of Ge.
The reason of the distinct evolution of the hole and electron doped structures can be further rationalized by the analysis of the projected density of states (PDOS) calculated for the corresponding cubic cells (Fig. 4). As discussed in ref. ^{49}, the primary cause of the distortion is mixing between s and p states of the cation (dark and light blue, respectively) resulting from a delicate balance of their bonding/antibonding with the anion p states (orange lines). Since this effect occurs predominantly at the top of valence bands, it is thus not surprising that the lone pair remains unaffected by ntype doping which shifts the Fermi level in opposite direction (Fig. 4a). On the other hand, in the presence of holes as shown in Fig. 4c, all the involved states reconstruct, slightly hybridizing with conduction bands which in turn suppresses the distortion.
In SnTe, the calculations of structural parameters with varying carrier concentration revealed trends very similar to those observed in GeTe. We emphasize that the polar displacement, even without doping, is very tiny (τ ~ 0.01). Moreover, as can be observed in Fig. 5a, τ decays much faster than in GeTe; the polar phase is completely suppressed at the carrier concentration of n = 0.03∣e∣/u.c. equivalent to around 4.0 × 10^{20}/cm^{3}, a doping commonly observed in experiments. We believe that the weaker ferroelectricity in this material can be assigned to a smaller and less active lone pair, resulting in a decreased tendency to a covalent bond formation.
Finally, let us comment on the practical realization of polarization reversal, which can be challenging in a doped semiconductor. Recent experimental study by Kolobov et al. based on piezoresponse force microscopy have demonstrated that the ferroelectric switching is possible in ptype doped epitaxial GeTe films.^{14} As estimated above, the polar displacements should survive even at the high doping level of over 10^{21} e/cm^{3} above the typically measured values,^{51,52} but the applied electric field might still be screened by free carriers induced by the vacancies. We believe that the successful realization of ferroelectric switching in GeTe samples could be related to a strong electric field applied locally with the PFM tip which allows to switch the domains. As pointed out by Kolobov et al., the reduced thickness of the film might also play a role in the overall mechanism of the switching. These indicate that the ferroelectric switching in this material has to be further explored from both fundamental and practical sides; ideally, the polarization reversal should be achieved by applying an opposite voltage with the electrode contacts. On the other hand, the ferroelectric switching has never been reported in a similar rhombohedral SnTe, most likely due to the weak ferroelectricity and low temperature of phase transition, which also impedes the realization of FERSC in this material.
SHE in doped FERSCs
Finally, we will focus on the SHE in the doped structures discussed in the previous section. Figure 6 reports the values of spin Hall angle, defined as a ratio of spin and charge conductivity. We have compared the values estimated for XTe at moderate and high concentrations of holes with the calculations for known spin Hall materials. The highest SHCs in GeTe within the considered range of carrier concentrations are ~30–80 (\(\hbar\)/e)(Ω × cm)^{−1} with the maximum value found at n = 0.1∣e∣/u.c. = 2.0 × 10^{21}∣e∣/cm^{3} for \({\sigma }_{yz}^{x}\). The calculated spin Hall angle θ_{SH} ~ 0.01 (green circle) is lower than in case of Pt and much below the value estimated for (nodal line) semimetal IrO_{2}.^{30,31} It can be assigned to the large charge conductivity in doped GeTe. On the other hand, θ_{SH} is higher at n = 0.02∣e∣/u.c. ≈ 3 × 10^{20}/cm^{3} (green square), as the charge conductivity changes faster than the SHC. This confirms that the sizable SHE could be explored in GeTe at hole concentrations of 10^{20}–10^{21}/cm^{3}, which genuinely sustains the polar phase and is typically observed in experiments. In fact, recent results based on unidirectional spin Hall magnetoresistance in Fe/GeTe bilayer seem to be in good agreement with the above estimation.^{21} In those experiments, the SHE was observed in GeTe with holes concentration of ~2.2 × 10^{20}/cm^{3}.
Analogous trends can be noticed for SnTe displayed as blue square and circle in Fig. 6. We have found that the SHCs are much above those estimated for GeTe, similarly as in case of previously reported 2DXTe.^{53} Notably, the values of SHCs continuously grow with doping, achieving 170–250 (\(\hbar\)/e)(Ω × cm)^{−1} for hole concentrations of 0.02–0.1∣e∣/u.c., which results in very high spin Hall angles of 0.03–0.15. Because the polar distortions of SnTe are suppressed already at 0.02∣e∣/u.c., the giant SHE should rather be attributed to the paraelectric phase. In fact, the estimated spin Hall angle is in good agreement with the experimental value of 0.01 measured in the hightemperature rocksalt structure by Ohya et al.^{25} Although it has been suggested that the topological surface states could enhance the efficiency of SHE, our analysis shows that the large spin Hall angle can be entirely assigned to the strong SOC of bulk electronic states in the cubic structure. Thus, despite the realization of FERSC seems difficult in this material, it is extremely promising for spintronics applications based on SHE.
Summary
In summary, we have studied SHE in prototype Rashba ferroelectrics GeTe and SnTe. Although such an idea might appear contradictory, we have demonstrated that the SHE could be indeed observed in a doped polar (or ferroelectric) material. We have explored several aspects related to the realization of SHE in polar structures. First, we have noticed that the Rashba splittings of the electronic bands can enhance SHC, but they play a minor role at the hole concentrations usually observed in the considered materials. Second, we have investigated the evolution of polar distortions under carrier doping and found that the lone pair driven ferroelectricity is robust against electron injection, whereas in the presence of holes the polar displacements can be sustained up to ~0.13 (0.03) ∣e∣/u.c. in GeTe (SnTe). Finally, we have reported spin Hall angles for both materials at the typical concentrations of holes 10^{20}–10^{21}/cm^{3}. The values in GeTe are close to 0.01 and refer to the polar phase, while giant SHE in SnTe characterized by the angles of ~0.1 is likely to be found in paraelectric structures. In conclusion, our results indicate that the SHE could be realized in FERSCs. This opens a new perspective to integrate different functionalities within one material, and combine spin injection/detection with electric spin manipulation in a device similar to recently presented allelectric spin transistor.^{54} We believe that our study will stimulate further search of FERSCs with complementary spindependent electronic properties, whereby the interplay of chargetospin conversion, Rashbarelated physics and ferroelectricity could bring novel spintronics applications.
Methods
Firstprinciples calculations based on DFT were performed using QUANTUM ESPRESSO package^{55,56} interfaced with the AFLOWπ infrastructure.^{57} We treated the exchange and correlation interaction within the generalized gradient approximation (GGA),^{58} and the ion–electron interaction with the projector augmentedwave fullyrelativistic pseudopotentials^{59} from the pslibrary database.^{60} The electron wave functions were expanded in a plane wave basis set with the cutoff of 85 Ry. The electronic properties were calculated using the pseudohybrid Hubbard density functional ACBN0.^{61} We remark that this parameterfree alternative of traditional DFT+U methods was proven to yield extremely accurate values of energy gaps and relative positions of different bands in widegap semiconductors or perovskite oxides,^{62,63} in good agreement with more demanding beyondDFT approaches,^{64} such as hybrid functionals or GW approximation.
The rhombohedral unit cells were fully relaxed until the forces on each atom became smaller than 10^{−3} Ry/bohr; the optimized lattice constants of the groundstate ferroelectric GeTe (SnTe) are equal to 4.37 Å (4.57 Å), respectively. The BZ sampling at the level of DFT was performed following the MonkhorstPack scheme using a 16 × 16 × 16 kpoints grid. The electron/hole doping was simulated by adding extra charge to the system with the compensating amount of opposite charge in the background.
The intrinsic SHCs were calculated as implemented in the PAOFLOW code^{65} following the Kubo’s formula:^{66,67}
where \({\Omega }_{n,ij}^{k}\) is the spin Berry curvature of nth band assuming spin polarization along k and spin (charge) current along i (j), \({f}_{n}(\overrightarrow{k})\) is the FermiDirac distribution function and \({j}_{i}^{k}=\{{s}_{k},{v}_{i}\}\) is the spin current operator, where s and v stand for spin and velocity operators, respectively. In order to properly resolve the rapid variation of spin Berry curvatures, we have interpolated the kpoints mesh to 48 × 48 × 48 using the adaptive smearing in the final SHC calculations. The corresponding convergence test is reported in the Supplementary Information.
Data availability
Data are available from the authors upon reasonable request.
Code availability
The PAOFLOW code can be downloaded from http://aflowlib.org/src/paoflow/.
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Acknowledgements
We are grateful to Naiwrit Karmodak, Christian Rinaldi, Riccardo Bertacco, Marcio Costa and Frank Cerasoli for valuable discussions. The members of the AFLOW Consortium (http://www.aflow.org) acknowledge the grant ONRMURI N000141310635. Finally, we acknowledge the High Performance Computing Center at the University of North Texas and the Texas Advanced Computing Center at the University of Texas, Austin.
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J.S. coordinated the project, providing calculations, data analysis and writing the manuscript; H.W. initiated the project and performed the calculations; P.G. performed the calculations; M.B.N. and S.C. analyzed the results; S.P. and M.B.N. conceived the idea of spin Hall effect in Rashba ferroelectrics. All the authors contributed to the discussion of the results.
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Wang, H., Gopal, P., Picozzi, S. et al. Spin Hall effect in prototype Rashba ferroelectrics GeTe and SnTe. npj Comput Mater 6, 7 (2020). https://doi.org/10.1038/s4152402002740
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DOI: https://doi.org/10.1038/s4152402002740
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