Abstract
ABO_{3} perovskite oxides with magnetic A and B cations offer a unique playground to explore interactions involving two spin sublattices and the emergent effects they may drive. Of particular interest is the possibility of having magnetically driven improper ferroelectricity, as in the much studied families of rareearth orthoferrites and orthochromites; yet, the mechanisms behind such effects remain to be understood in detail. Here we show that the strongest polar order corresponds to collinear spin configurations and is driven by nonrelativistic exchangestrictive mechanisms. Our firstprinciples simulations reveal the dominant magnetostructural couplings underlying the observed ferroelectricity, including a striking magnetically driven piezoelectric effect. Further, we derive phenomenological and atomistic theories that describe such couplings in a generic perovskite lattice. This allows us to predict how the observed effects can be enhanced, and even how similar ones can be obtained in other perovskite families.
Introduction
The RFeO_{3} and RCrO_{3} compounds, where R is a magnetic lanthanide, are usually called orthoferrites and orthochromites, respectively, as they all present the orthorhombic (Pbnm, GdFeO_{3}type) structure^{1,2} that is most common among perovskite oxides. These materials have received continued attention over decades because of their intriguing magnetic properties (see, for example, refs 3, 4, 5, 6, 7, 8, 9, 10, 11, 12, 13, 14, 15, 16 and references therein). More recently, they have regained interest in connection with prospect applications in magnetic devices, and because some of them have been shown to present ferroelectric order at low temperatures, which renders them multiferroic^{6,7,8,9,15}. More generally, the RFeO_{3} and RCrO_{3} materials constitute a unique playground to explore the novel physical effects potentially emerging from the presence of two interacting spin sublattices, and—thanks to their insulating character—the possibility of tuning such effects by the application of external electric fields.
In spite of the intense activity focused on these compounds, some of their key properties remain poorly understood at a fundamental, atomistic level. For example, in what regards their magnetism, a thorough characterization has been available for a long time^{3,4}; yet, the key role that certain magnetostructural couplings play in determining the ground state structure and other remarkable effects—as, for example, the presence of a magnetic compensation temperature at which the magnetizations of the rareearth ions and Fe/Cr sublattice cancel each other—has been discussed and highlighted only recently^{16}. Similarly, the onset of a ferroelectric polarization at low temperatures has so far been addressed mainly at an empirical level, and conflicting pictures (for example, as regards the alleged need of a nonzero canted magnetization in order to have ferroelectricity^{11,13}) can be found in the literature. Further, to the best of our knowledge only one firstprinciples work has discussed this problem^{10}, and that study was done under some simplifying assumptions (that is, adopting an Atype antiferromagnetic order for the Fe spins of DyFeO_{3}, while it is known that the actual arrangement is dominantly Gtype). Hence, while valuable, the existing works and discussions are hardly complete or conclusive, and there is a clear need for a systematic investigation of the origin of ferroelectricity in orthoferrites and orthochromites.
In this work we use firstprinciples methods to address this pending issue, adopting a general approach whose conclusions should, in fact, be relevant to all orthoferrites and orthochromites, and even all ABO_{3} perovskites with A and B magnetic sublattices. Our study shows there are two types of mechanisms leading to a ferroelectric polarization in these materials: a first type for which the effect is small and emerges from the symmetry breaking associated to a noncollinear spin structure; and a second type that leads to much larger polarizations and relies on exchangestrictive effects displayed by strictly collinear magnetic configurations. Here we mostly focus on the latter strongest effect and analyse the magnetic couplings responsible for the electric polarization, showing that they are mediated by up to four different structural distortions characteristic of all orthorhombic Pbnm perovskite phases. Most interestingly, we reveal a magnetically driven piezoelectric effect as one of the dominant sources of polarization. We discuss the atomistic models explaining the most interesting effects, and explain the implications of our results for other perovskite families and the engineering of new or optimized multiferroics.
Results
Conditions for ferroelectricity
Existing evidence clearly shows that ferroelectricity in orthoferrites and orthochromites is driven by the onset of magnetic order in both the rareearth and transitionmetal sublattices^{6,15}. This is thus a case of magnetically induced ferroelectricity, via symmetry breaking, which places these materials among the socalled Type II multiferroics^{17}. To understand the details of these symmetry breakings, our first task is to determine under which specific conditions—that is, for which particular spin arrangements—the electric polarization appears.
To do that we consider all the spin configurations that are potentially relevant in these materials, following experimental evidence that: first, the dominant order in the Fe/Cr sublattice is antiferromagnetic Gtype (GAFM), with firstnearestneighboring spins antiparallel to each other, and second, the typical spin structures are commensurate with the 20atom crystallographic cell deduced from the atomic positions. More specifically, for the R spins we consider GAFM, CAFM, AAFM and ferromagnetic (FM) configurations (see the respective sketches in Fig. 1c). Note that for the CAFM and AAFM cases we consider the particular spin arrangement that is compatible with the crystallographic cell; this implies that the c axis of inphase rotations coincides with the socalled unique axis of these spin structures (that is, the direction of parallel spin alignment for the CAFM case, and antiparallel alignment for the AAFM order). We consider three possible orientations (along the orthorhombic axes indicated in Fig. 1b) of the vector describing the dominant AFM order, and allow the R and transitionmetal spin sublattices to orient differently; this results in a total of 36 different spin configurations.
We work with two model systems, GdFeO_{3} and GdCrO_{3}, which are particularly wellbehaved as regards noncollinear magnetic simulations performed with our computational tools (see Methods). Let us stress that this choice does not imply any loss of generality: We do not restrict our study to the specific magnetic ground state of the simulated gadolinium compounds, but rather consider all the spin configurations that are potentially relevant to the whole orthoferrite and orthochromite families. Further, the electric polarization that we expect to observe will be driven by the symmetry breaking imposed by the spin structure, possibly in combination with structural distortions that are qualitatively identical in all orthoferrites and orthochromites. Hence, consideration of GdFeO_{3} and GdCrO_{3} allows us to investigate all the qualitative effects that the Pbnm compounds can potentially display, and to draw general rules and conclusions. Needless to say, quantifying in detail the behaviour of particular compounds would require a specific investigation.
For each of the 36 considered spin arrangements, we proceed in the following way: we start the firstprinciples calculation with the atoms in the ideal (highsymmetry) positions of the Pbnm phase and the Gd and Fe/Cr magnetic moments initialized according to the specific spin arrangement. Then, we run a selfconsistent field density functional theory (DFT) calculation (allowing for noncollinear magnetism and including spin–orbit interactions; see Methods) in which the spins are free to optimize the energy. The selfconsistent field calculations are repeated along a full structural relaxation that stops when the forces on the atoms and stresses on the cell fall below a small threshold (see Methods). Finally, the resulting configuration is analysed, focusing on the optimized spin structure and the possible occurrence of an electric polarization (see Methods for details on the calculation of localized magnetic moments and polarization).
Table 1 summarizes the magnetic orders and polar distortions observed in the 36 cases considered, as obtained from our numerical simulations and verified by a symmetry analysis. Interestingly, only 13 cases, out of the 36 ones considered here, were numerically found to result in a polar solution. Table 2 details the spin arrangement obtained for two such polar cases.
The results for GdCrO_{3} regarding the existence or absence of an electrical polarization are qualitatively identical to those obtained for GdFeO_{3}, and are summarized in Table 3. This overall coincidence between the GdFeO_{3} and GdCrO_{3} results strongly supports our hypothesis that discussing these two specific compounds is relevant to understand the origin of electric polarization in all orthoferrites and orthochromites. For the sake of simplicity, in the following we will focus our discussion on the results for GdFeO_{3}.
Let us note that we also ran simulations in which the Gd^{3+} cations were treated as nonmagnetic (with their 4f electrons frozen at the ionic core), and explicitly checked that no polar distortion is obtained in absence of Gdmagnetism. This further demonstrates that the existence of a magnetic ordering at both the rareearth and Fe/Cr sublattices is necessary to obtain an electric polarization, and is in agreement with the symmetry analysis made by various authors^{18,19,20}.
Interestingly, the obtained polar solutions can be readily classified in two categories. First, we have those in which the rareearth spins have a dominant GAFM order parallel to the GAFM vector of the Fe sublattice. These three cases display a relatively large polarization. In addition, we have polar solutions in which the R spins present dominant GAFM (four cases) or AAFM (six cases) orders, with the corresponding AFM vectors being orthogonal to the GAFM vector for the Fe sublattice. As indicated in Table 1, in these situations we obtain very small polarization values (about 50–100 times smaller than those computed for the first category of polar solutions) that fall below the accuracy of our calculations. Let us first analyse in some detail the former category, which will be the focus of this paper; we will conclude this section with a brief discussion of the latter.
We get the largest polarization values for the cases sketched in Fig. 2. In all three cases the Gd and Fe spins exhibit a GAFM order and the corresponding AFM vectors are parallel to each other; more precisely, they both lie along the a direction in the case depicted in Fig. 2a, along b in the case of Fig. 2b, and along c in Fig. 2c. In all three cases the atomic symmetry is orthorhombic Pna2_{1}, with the polar axis being along the c direction. Note that this common symmetry only pertains to the atomic positions; obviously, the three different cases correspond to three different magnetic space groups, as detailed in Table 1. As also shown in the table, in all the cases the polarization is predicted to be around 0.4 μC cm^{−2}; this is of the same order of magnitude as the experimental value of 0.12 μC cm^{−2} reported in ref. 15 for GdFeO_{3} at 2 K, and therefore about two orders of magnitude smaller than those of classic ferroelectrics such as BaTiO_{3} or PbTiO_{3}. (We explicitly checked that the computed polarization value depends weakly on the HubbardU correction used in the simulations; more especifically, we obtain 0.37 μC cm^{−2} for U_{Gd}=5 eV and U_{Fe}=4 eV and 0.46 μC cm^{−2} when we use the smaller corrections U_{Gd}=3 eV and U_{Fe}=2 eV).
In the case of GdCrO_{3}, the predicted polarization is of the order of tenths of μC cm^{−2}, as well (Table 3), which is consistent with the experimental result of 0.6 μC cm^{−2} reported in ref. 13. We should be cautious about this interpretation of the experimental data for GdCrO_{3}, though, as it is not clear whether the polarization measured in ref. 13 at relatively hightemperatures is a result of the simultaneous order of both spin sublattices or some other effect.
Table 1 further shows that when the GAFMordered spins of both Gd and Fe sublattices lie parallel to the a axis, we also obtain a weak magnetization along c, which is consistent with the experimental observation of ref. 15 for GdFeO_{3}. In contrast, when the Gd and Fe spins lie parallel to the b axis, no weak magnetization is observed. Finally, when the spins lie along c, the weak magnetization appears again, but is now antiparallel to the a axis. Hence, we find that the presence of a polar distortion (always along c) is independent from the existence or absence of a net magnetization, which is at odds with the picture proposed in refs 11, 13. Further, in the cases in which a weak magnetization exists, the spins may cant parallel or perpendicular to the polarization axis. Note that a discussion of the canted spin orders in orthorhombic perovskites is given in refs 16, 21.
It is thus clear that a sizable electric polarization appears in orthoferrites and orthochromites when both the R and Fe/Cr spin sublattices adopt a dominant GAFM arrangment, with the AFM vectors being parallel to each other. The presence or absence of a weak magnetization is irrelevant as it regards the occurrence of the electric polarization. Further, the resulting polarization is largely independent from the direction along which the spins lie, which strongly suggests that it will occur even if we run our structural relaxations assuming that magnetization is described by a scalar field (that is, as in the standard nonrelativistic calculations based on the local spindensity approximation or the socalled σgeneralized gradient approximation). Indeed, we explicitly verified this conjecture, obtaining coriented polarizations of about 0.40 and 0.16 μC cm^{−2} for GdFeO_{3} and GdCrO_{3}, respectively, which are essentially identical to those of Tables 1 and 3.
Let us now comment on the second category of polar solutions for which we found negligibly small polarization values. These occur when we have a dominant GAFM or AAFM order of the Gd spins, the corresponding AFM vector being orthogonal to that characterizing the GAFM arrangement of the Fe sublattice. Hence, in this case the magnetically driven ferroelectricity fundamentally relies on having a noncollinear spin arrangement. Indeed, we explicitly checked that, for the case of Gd spins with AAFM order, the effect disappears if we treat magnetism at the scalar level. (For Gd spins with GAFM order, the scalarmagnetism calculation reduces to the one discussed above and yields a relatively large polarization). The reliance on a noncollinear spin structure, and the likely importance of spin–orbit interactions in many of these cases, probably explains the very small magnitude of the effect.
Hence, this initial exercise has shown that there are two possible routes to obtain a magnetically driven polar distortion in orthoferrites and orthochromites. The first one relies on a mechanism that is active at the scalarmagnetism level and in the absence of relativistic interactions; this mechanism leads to relatively large polarizations. The second one fundamentally relies on having a noncollinear magnetic configuration, and leads to much smaller effects. In the following we focus our discussion on the first mechanism, which is most likely to explain the experimental data on GdFeO_{3} and GdCrO_{3} and, because it is stronger, can be expected to offer more interesting possibilities as regards the design or optimization of magnetoelectric multiferroics.
Structural underpinnings
To identify the origin of ferroelectricity in these materials, let us first indicate that the induced polar distortions mainly involve the rareearth cations, which spontaneously move out of their positions in the centrosymmetric Pbnm state as the Gd and Fe/Cr spins order in collinear GAFM patterns. Further, it can be checked numerically that the spin order by itself is not enough to explain the onset of ferroelectricity. Indeed, when we run a simulation with GAFMordered Gd and Fe/Cr spins, while maintaining the atoms at the positions corresponding to the ideal cubic perovskite structure, we obtain no indication that a ferroelectric distortion will appear. (One such indication would be, for example, forces of the appropriate (polar) symmetry acting on the atoms. This kind of signature is further discussed and used below). It is thus clear that the spin arrangement somehow cooperates with the structural distortions characterizing the orthorhombic structure to produce the symmetry breaking that leads to the electric polarization. Further, the strength of the corresponding magnetostructural couplings will determine the magnitude of the induced ferroelectric distortion. Note that such couplings will be of the socalled exchangestrictive type, as our simulations indicate that they occur even in absence of relativistic spin–orbit interaction.
To identify which structural distortions mediate the occurrence of a magnetically driven polarization in orthoferrites and orthochromites, we run the following computational experiments. In what follows the Gd and Fe spins are always GAFMordered and we treat magnetism at the scalar level. Let us focus on the calculations done for GdFeO_{3}, the results for GdCrO_{3} being qualitatively identical. First, we consider GdFeO_{3} in the ideal cubic perovskite structure, assuming a cubic lattice constant obtained by averaging the experimental values for the orthorhombic phase. Because of the cubic symmetry, the forces on the atoms are strictly null in this configuration. Then, we distort this reference state following each of the symmetryinequivalent atomic distortions that characterize the Pbnm ground state. We compute the forces induced on the Gd and Fe atoms as we condense the different distortion modes, and then calculate the average force on the Gd and Fe sublattices; note that these polar forces act as (that is, have the symmetry of) an effective electric field and drive the onset of the improper ferroelectric polarization. Our result for the evolution of the Gd and Fe polar forces as a function of the various distortion modes is shown in Fig. 3.
Figure 3a shows the results for the dominant distortions characterizing the orthoferrite and orthochromite compounds, that is, the antiphase (about the a axis) and inphase (about c) O_{6}octahedra rotations that determine the symmetry breaking from cubic to orthorhombic and constitute the primary order parameters of the structural transition (Fig. 1d,e). Such a O_{6}rotational pattern is termed a^{−}a^{−}c^{+} in the notation introduced by Glazer^{22}. Our results show that the antiphase rotations create a considerable polar force on the Gd atoms, while the inphase rotations do not induce any force at all. Interestingly, the dependence of the polar force on the antiphase rotation amplitude is quadratic, with a quartic behaviour appearing for large distortions. For reference, the amplitude of the various distortions in the equilibrium orthorhombic phase of GdFeO_{3} is indicated in the caption of Fig. 3.
Then, we have large and very important secondary distortions involving antipolar displacements of the rareearth cations in the ab plane (Fig. 1f). There are two such antipolar modes, corresponding respectively to the X (2π/a_{pc}(0, 0, 1/2)) and R (2π/a_{pc}(1/2, 1/2, 1/2)) qpoints of the first Brillouin zone of the ideal cubic perovskite phase, where a_{pc} is the pseudocubic lattice parameter. The polar forces associated to these modes are shown in Fig. 3b. The dependence of the force on the distortion amplitude is quadratic for both antipolar patterns.
Finally, the cell strains in the cubic to orthorhombic transformation, the most important effect being associated to the η_{6} shear controlling the angle formed by the a_{pc} and b_{pc} pseudocubic lattice vectors (defined in Fig. 1b). Figure 3c shows the corresponding polar forces, which have a linear dependence with the shear strain amplitude.
We thus find a remarkable result, namely, that several (namely, four) distortions of the Pbnm structure contribute to the onset of the magnetically driven electric polarization in these orthoferrites and orthochromites.
Key magnetostructural couplings
To gain further insight into the atomistic underpinnings of these couplings, it is most convenient to start with the last one of the cases mentioned above, that is, the linear dependence of the polar force (and, hence, of the induced polarization) with a shear deformation of the cell. This is a striking result with very broad implications: It tells us that any cubic ABO_{3} perovskite with magnetic A and B sublattices will behave as a piezoelectric (that is, a material in which elastic strain induces an electric polarization) if the A and B spins acquire a (collinear) Gtype AFM order.
Figure 4 sketches the symmetry breaking that drives such an interesting effect. Indeed, it is immediate to realize that, when magnetically disordered, the cubic perovskite phase is centrosymmetric and, in particular, the Gd and Fe/Cr cations are sitting at inversion centres of the lattice. Further, if only the Fe/Cr spins order (Fig. 4a), the structure is still centrosymmetric (point group mm). More precisely, assuming that spatial inversion does not change the sign of the atomic magnetic moments, from Fig. 4a we can see that the Fe/Cr atoms continue to occupy inversion centres, while at Gd sites the inversion symmetry is recovered when combined with a time reversal transformation. (The time reversal operation changes the sign of all the spins, but has no effect on the atomic structure). In contrast, when both the Gd and Fe/Cr spins are GAFMordered (Fig. 4b), all the inversionsymmetry points are lost, and cannot be recovered even if we combine the spatialinversion operation with time reversal. Hence, in this case the cubic phase is noncentrosymmetric (point group 3m) and will present a piezoelectric response, even if it is nonpolar. Indeed, as shown in Fig. 4c, when we apply a shear strain in the ab plane of such a structure, the environment of the Fe cations becomes asymmetric along the c direction, which guarantees that coriented forces acting on the Fe atoms will appear. This is a typical exchangestrictive effect: the spinup Fe atom in Fig. 4 will surely have a preference between bonding to the two spinup Gd atoms that approach it from above, or with the two spindown Gd’s that come closer from below; thus the polar force appears. As sketched in the figure, it is easy to demonstrate that this symmetry breaking occurs in exactly the same way everywhere in the lattice, thus resulting in an homogeneous force field that gives rise to an homogeneous effective electric field. This is thus the origin of the strain η_{6}driven polar force of Fig. 3c.
Mathematically, we can model this effect by deriving the invariant coupling that appears in a Landau potential describing the energetics of the material around the reference cubic phase as a function of the relevant macroscopic order parameters. Such order parameters are the two GAFM orders in the system as quantified by scalars G_{Gd} and G_{Fe}, the polarization P_{α}, and the shear strain η_{αβ}; here, α and β label the Cartesian directions that we assume coincide with the pseudocubic lattice vectors of the perovskite structure. Then, the magnetostructural (ms) coupling leading to the effect in Fig. 3c is given by
where is the LeviCivita symbol, which equals +1 when the ordered triad αβγ forms a righthanded system, −1 when lefthanded, and 0 when there are repeated indexes. In addition, η_{αβ} (for α≠β) denotes the symmetric part of a shear strain; in particular we have 2η_{xy}=η_{6} in Voigt notation. Finally, note that we can replace the product G_{Gd}G_{Fe} by the dot product G_{Gd}·G_{Fe} if we want to recover a threedimensional representation of the magnetism.
Let us note a subtlety concerning the invariance of such a coupling term with respect to the symmetry operations of the cubic reference phase. If we think of the action of space inversion on such a term, for the structural order parameters we trivially have P_{α}→−P_{α} and η_{αβ} → η_{αβ}, without any ambiguity. In contrast, the transformation of the magnetic order parameters depends on the precise location of the inversion centre that we consider. Thus, for example, if we consider a Fecentred inversion point, we have G_{Gd}→−G_{Gd} and G_{Fe}→G_{Fe}; in contrast, if we consider inversion points at the Gd or oxygen sites, we get G_{Gd}→G_{Gd} and G_{Fe}→−G_{Fe}. Nevertheless, in all cases it is true that the product G_{Gd}G_{Fe} changes sign upon spatial inversion, as needed for the term to be invariant. Note that this dependence on the location of the inversion point is not related to the magnetic character of the G_{Fe} and G_{Gd} order parameters, but to the fact that they are associated to a qpoint different from Γ. In fact, similar considerations apply to the O_{6}rotational order parameters discussed below.
Note that the coupling just described is linear in the polarization, and will thus lead to an effective electric field of the form:
In particular, this implies that the η_{6}=2η_{xy} shear will induce an effective field, and thus an improper polarization, along c, in agreement with our DFT results. (Note that such an effective field will induce proportional polar forces acting on the various atomic sublattices). In addition, in agreement with our results for the polar forces of Fig. 3c, both the effective field and the induced polarization will be linear in η_{6}.
Similarly, it is possible to identify the symmetryinvariant couplings responsible for the other effects shown in Fig. 3a,b. More precisely, we have
and
where ω_{Rα} denotes the amplitude of antiphase O_{6} rotations about the pseudocubic axis α; A_{Rα} and denote antipolar distortions along α and modulated according to R and Xtype qpoints of the Brillouin zone, respectively; in the case of , the Xtype point is 2π/a_{pc}(1/2, 0, 0) for γ=x, 2π/a_{pc}(0, 1/2, 0) for γ=y and 2π/a_{pc}(0, 0, 1/2) for γ=z. All these terms yield effective electric fields that are quadratic in the amplitude of the structural distortions, in agreement with our numerical results for the polar forces of Fig. 3a,b. As an illustrative example, Fig. 4d illustrates the occurrence of homogeneous polar forces caused by the interactions captured by equation (5). Note also that couplings with a quartic dependence of these structural distortions can be similarly deduced.
It is also possible to demonstrate that, in contrast, symmetry precludes the existence of couplings that would lead to a linear dependence of the polar forces on the antiphase rotational or antipolar order parameters. For example, a coupling of the form is incompatible with translational symmetry (among others) and cannot exist. Again, this is compatible with our numerical findings. Similarly, symmetry precludes the onset of polar forces as inphase rotations condense on their own, as consistent with the null result shown in Fig. 3a.
To finish this part, let us note that the above energy couplings, which involve macroscopic order parameters, can ultimately be deduced from atomistic interactions, that is, interactions involving atomic spins, offcentring displacements of specific Gd and Fe cations, rotations of individual O_{6} octahedra, and so on. There are recent examples of such an atomistic approach to investigate these and similar perovskite materials, for example, in what regards the interplay between rotational and antipolar distortions^{23} or the coupled magnetic orders and origin of weak magnetization in orthoferrites and orthochromites^{16,21}. Working with atomistic couplings is also a necessary step towards the development of effective models—for example, of the socalled effective Hamiltonian type^{24,25,26}—that can eventually permit largescale statistical simulations of these multiferroic effects. Here, to illustrate such an approach, we describe the simplest atomistic coupling that leads to the energy discussed above.
As sketched in Fig. 5, let u_{iα} denote the offcentring displacement of the Gd cation at cell i along Cartesian direction α, and let m_{Gd,i} be the (scalar) magnetic moment associated to the same Gd cation. Also, let m_{Fe,ilmn} be the magnetic moment of the Fe cation located at the cell defined by R_{i}+l a_{pc}+m b_{pc}+n c_{pc}, where R_{i} is the lattice vector corresponding to cell i; a_{pc}, b_{pc}, and c_{pc} are the lattice vectors corresponding to the fiveatom pseudocubic perovskite cell; and l, m and n are integers. Finally, let η_{αβ}, for α≠β, be the symmetric part of the homogeneous strain tensor, which we use to represent the strain state of individual cells, as shown in Fig. 5. Then, if we search for the simplest symmetryallowed coupling involving the Gd and Fe spins, as well as the Gd offcentring distortion and cell shear strains, we obtain
where is a materialdependentcoupling constant. Now, let us consider the particular case in which both the Gd and Fe spin sublattices adopt a Gtype AFM order, so that and , where . Let us also imagine that the Gd offcentrings are homogeneous throughout the lattice, so that u_{iα}=u_{α} i; such distortions generate a polarization , where is the relevant effective charge of the Gd cation and Ω is the volume of the fiveatom perovskite cell. It is thus trivial to verify that the atomistic coupling in equation (6) leads to the macroscopic interaction of equation (1), with .
Discussion
Let us now discuss the implications of our results from two perspectives, a general one that concerns multiferroic perovskites at large, and one focused on previous and current work on multiferroic orthoferrites and orthochromites.
In a generic way, our results can be described as examples of improper ferroelectricity driven by spin ordering. The magnitude of the induced electric polarization depends on magnetostructural couplings, with the strongest (exchangestrictive) effects corresponding to collinear spin configurations and present in the absence of relativistic interactions. Our findings support the essential correctness of previous discussions of magnetically induced polarization in these materials^{6,10}, which were based on empirically deduced models or simplified firstprinciples studies. Note that, at variance with the present work, the previous studies did not consider all the existing magnetostructural couplings, nor did they explain the effects with a detailed theory. Interestingly, let us mention that the collinear AAFM orders hypothesized for both R and M spin sublattices in these references actually occur, as a weakcanted orders, in many of the spin configurations considered in our work (Table 1). From the point of view of a polarization induced by symmetry breaking, such cases are thus essentially identical.
Our results and analysis go one step further, as they offer valuable insights into the atomistic underpinnings of the magnetically driven ferroelectricity, as well as hints at how to optimize these effects or obtain related ones in similar situations. For example, let us recall the mechanism described by equation (1), by which a shear–strain mediates the occurrence of the magnetically driven polarization. The presence of such an interaction implies that it is possible to enhance the electric polarization of orthoferrites and orthochromites by growing them as thin films on orthorhombic substrates presenting a large shear strain. One example of such substrates is the commonly used DyScO_{3} system for which η_{6}≈5.0% (ref. 27).
Similarly, the magnetostructural coupling given by equation (3) should yield an improper polarization for other O_{6}rotational patterns; in other words, its action is by no means exclusive to the a^{−}a^{−}c^{+} structure typical of Pbnm phases. We explicitly checked this by simulating a a^{−}a^{−}a^{−} polymorph of GdFeO_{3} with our firstprinciples methods. Typically, this rotational pattern results in the nonpolar Rc space group. However, because of the combination of the rotational distortion and GAFM order for both Gd and Fe spin sublattices, the atomic symmetry of such a structure is polar with the rhombohedral R3c space group. This is precisely the effect reflected in equation (3), and it results in a polarization of about 0.2 μC cm^{−2} when we fully relax GdFeO_{3} in this hypothetical rhombohedral phase. We explicitly checked that, if we suppress the Gd spins, by freezing them into the ionic core, we obtain the nonpolar Rc symmetry and a null polarization. Hence, this polar distortion is genuinely driven by the simultaneous magnetic order of the Gd and Fe spin sublattices. Hence, knowledge of the atomistic couplings responsible for the polarization in orthoferrites and orthochromites allows us to identify alternative possibilities, corresponding to completely different crystallographic symmetries, in which the same sort of magnetically driven polarization can exist.
The last example emphasizes the generality of our results: Because the newly identified couplings are active in any perovskite structure with A and B magnetic sublattices, they apply to (and can be used to our advantage in) a large variety of compounds beyond the ferrites and chromites. Indeed, such couplings can potentially play an active role, and lead to multiferroic phases, in other orthorhombic perovskites, the nickelate (RNiO_{3}), manganite (RMnO_{3}) and titanate (RTiO_{3}) families being obvious candidates. Further, the couplings unveiled in this work should also be relevant to essentilly all perovskite phases hosting two spin sublattices, as perovskites are all but guaranteed to present shear, O_{6}rotational and/or antipolar distortions of some form. Further, such structural distortions can often be induced or controlled by a variety of means, chemical substitution and strain engineering being the most usual ones. Hence, the possibilities to find or induce ferroelectric order in perovskites with two magnetic sublattices, thanks to the couplings here described, seem essentially endless.
Interestingly, the magnetically driven piezoelectric response, and ensuing improper polarization, revealed in this work can be viewed as an example of a broader family of effects. Thus, for instance, it has been recently shown that spin order may result in a contribution to the polarization of a ferroelectric via a combination of magnetoelastic and piezoelectric couplings^{28}. Similarly, it is possible to obtain a linear magnetoelectric response in materials that are both piezomagnetic and piezoelectric^{29}. Nevertheless, while they involve similar ingredients, there is a critical difference between such effects and the one that we have introduced in this work: in the present case the material is not piezoelectric in absence of magnetic order; instead, piezoelectricity is magneticallydriven. Hence, we could say that the mechanisms discussed in refs 28, 29 are typical of the socalled type I multiferroics^{17}, where ferroelectricity is a proper order, while the mechanisms discussed here would generally correspond to type II materials with an improper (magnetically induced) polar order.
Our present results are somewhat reminiscent of recent observations on materials like LaMn_{3}Cr_{4}O_{12} (refs 30, 31, 32), which presents a dual Gtype collinear antiferrmagnetism that results in an electric polarization^{30}. However, beyond obvious structural and stoichiometric differences, it should be noted that in LaMn_{3}Cr_{4}O_{12} the magnetically driven polar distortion relies on the spin–orbit couplings, at variance with the main effects discussed here.
Let us conclude by discussing the implications of our results as regards previous works on RFeO_{3} and RCrO_{3}. As already mentioned, the reasonable numerical agreement between our computed polarizations and those experimentally measured for some orthoferrites and orthochromites suggests that the polar order in those compounds emerges from having nearlycollinear GAFM arrangments in both the rareearth and transitionmetal sublattices. Further, as already mentioned above, our results clearly show that the occurrence of a ferroelectric polarization is unrelated to the presence or absence of a net (weak) magnetization, at variance from the picture proposed in refs 11, 13. More specifically, in refs 11, 13 both the electric polarization and weak magnetization are observed to simultaneously disappear at a spin reorientation transition, which seems to imply a causal connection between them. Our results, though, indicate that, while there may be a common cause for these two effects, it is not the case that one is necessary for the other to occur.
Also, let us note that various works on ferrites (like, for example, SmFeO_{3} (ref. 12)) and chromites (like, for example, ErCrO_{3} (ref. 13)) have reported electric polarizations occurring at temperatures well above the ordering transition for the rareearth spins. However, according to our present results and to the symmetry analysis made by others^{18,19,20}, a simple AFM order of the Fe/Cr spins cannot produce such polarizations in absence of rareearth magnetism; instead, a cycloidal arrangement—as, for example, the one occurring in prototypic compound TbMnO_{3} (ref. 33)—is needed for a polarization to appear.
In summary, we have conducted a systematic theoretical investigation on the sources of improper magnetically driven ferroelectricity in rareearth orthoferrite and orthochromite perovskites. Our work has confirmed that both the rareearth and transitionmetal spin sublattices need to order for the multiferroic effects to occur. Further, our calculations reveal several possible scenarios leading to the improper polar order; in particular, we find that the largest polarizations are driven by exchangestrictive mechanisms and correspond to simple colinear spin arrrangments. Our results are in reasonable agreement with (and explain) available experimental data.
We have identified in detail the magnetostructural couplings responsible for the largest polarizations found. Interestingly, four structural distortions of the ideal cubic perovskite contribute: one shear strain, one antiphase O_{6}rotational mode, and two antipolar modes. The dependence is linear for the shear strain (an effect that can be seen as a magnetically induced piezoelectricity of the cubic perovskite structure) and quadratic for the other distortions. We have modelled these couplings in the framework of a general Landaulike potential that applies to any ABO_{3} perovskite with two magnetic sublattices, and confirmed explicitly that similar effects can be obtained (and enhanced) in compounds belonging to other families and presenting other symmetries. In particular, our DFT simulations showed that our discovered magnetostructural coupling involving antiphase O_{6} rotations can drive improper ferroelectricity in rhombohedral (a^{−}a^{−}a^{−}) perovskites (the transition is Rc→R3c). Indeed, because the most relevant nonpolar distortions of the perovskite structure are present in orthoferrites and orthochromites, our study has allowed us to map out essentially all the possibilities to obtain effects of this kind in these compounds, its conclusions being general and virtually exhaustive. Our work thus highlights perovskites with two magnetic sublattices as a rich playground for novel magnetoelectric effects, and provides the basic cartography of the field.
Methods
Firstprinciples calculations
For the simulations we use DFT as implemented in the Vienna abinitio Simulation Package within the framework of the projected augmented wave method^{34,35}. The generalized gradient approximation with the Perdew and Wang parameterization^{36} was employed, using a ‘Hubbard U’ correction^{37} for a better treatment of Fe and Cr’s 3d electrons and Gd’s 4f electrons. The U’s are chosen to be 4.0, 3.0 and 3.0 eV for Gd, Fe and Cr, respectively, in line with previous works^{10}. We solved explicitly for the following electrons: 4f^{7}5s^{2}5p^{6}5d^{1}6s^{2} for Gd, 3d^{7}4s^{1} for Fe, 3d^{5}4s^{1} for Cr, and 2s^{2}2p^{4} for O. Note that the Gd atoms are allowed to order magnetically, since their 4f electrons are explicitly treated in the simulations; alternatively, one can assume a 3+ ionization state and consider the 4f electrons frozen in the ionic core, an approximation that we adopt to run some tests described in the text. The electronic wave functions were represented in a planewave basis cut off at 500 eV. The reciprocal space integrals were computed using a Monkhorst–Pack kpoint mesh of 6 × 6 × 4, corresponding to the 20atom orthorhombic cell which can be viewed as a × × 2 multiple of the elemental fiveatom perovskite unit. Note that this is the primitive cell for a a^{−}a^{−}c^{+} pattern of oxygen octahedra rotations, as expressed in Glazer’s notation^{22}. Note also that the shear strain η_{6} in the pseudocubic representation can be obtained from the lattice constants of the orthorhombic cell as η_{6}=2(b−a)/(b+a).
Spin–orbit couplings and noncollinear magnetic states are both considered in the calculations, unless otherwise specified. The structural optimizations are carried out until the forces acting on the atoms go below 0.005 eV Å^{−1}; we checked this is sufficient by running relaxations down to 0.001 eV Å^{−1} in a few representative cases.
Symmetry analysis
The space groups of various configurations are identified using the FINDSYM code, which is able to tackle magnetic symmetries^{38} (http://iso.byu.edu/iso/findsym.php). The Berry phase method^{39} is used to calculate electric polarizations. We typically run the Berry phase calculations at the scalarmagnetism level, but using the structures obtained from noncollinear calculations including spin–orbit couplings; the polarizations thus computed were checked to be correct in a few representative cases for which we ran the Berry phase calculation at the noncollinear level with spin–orbit. We use the VESTA code^{40} to draw most of the sketches that appear in the present work, and the tools in the Bilbao Crystallographic Server to conduct some structural and symmetry analyses (http://www.cryst.ehu.es).
Finally, for the benefit of the interested reader, we list in Table 4 the transformations of the order parameters appearing in our energy terms (equations (1, 2, 3, 4, 5)) under the generators of the full cubic point group (mm) and time reversal. With this information at hand, the symmetryallowed invariants can be deduced.
Data availability
The original data of this study can be obtained from the corresponding author upon request.
Additional information
How to cite this article: Zhao, H. J. et al. Improper electric polarization in simple perovskite oxides with two magnetic sublattices. Nat. Commun. 8, 14025 doi: 10.1038/ncomms14025 (2017).
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Acknowledgements
This work was supported by FNR Luxembourg Grants FNR/P12/4853155/Kreisel (H.J.Z. and J.Í.) and INTER/MOBILITY/15/9890527 GREENOX (L.B. and J.Í.). L.B. also thanks the support of the Office of Basic Energy Sciences, under contract ER46612. X.M.C. also thanks support from the National Natural Science Foundation of China (grant number 51332006) and the National Basic Research Program of China (grant number 2016YFA0300101). Most of the calculations were run at the Arkansas High Performance Computing Center.
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Zhao, H., Bellaiche, L., Chen, X. et al. Improper electric polarization in simple perovskite oxides with two magnetic sublattices. Nat Commun 8, 14025 (2017). https://doi.org/10.1038/ncomms14025
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DOI: https://doi.org/10.1038/ncomms14025
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