The striking range of experimentally observed low-temperature (LT) and high-temperature (HT) magnetic, electronic, and structural properties across the 3d ABO3 perovskites family have held the condensed matter physics community in constant fascination for many years1,2,3,4. Regarding magnetism, the LT phases are generally spin-ordered, either ferromagnetic (FM) (e.g., YTiO35) or antiferromagnetic (AFM) (e.g., LaVO36, CaMnO37, LaMnO38, CaFeO39, LaFeO38, or YNiO310), whereas the HT phases exhibit spin-disordered paramagnetism (PM). Regarding the electronic metal vs. insulator bandgap characteristics, these compounds show three modalities: (i) most LT and HT phases are insulating, except (ii) CaVO3 and SrVO3 that are PM metals at all temperatures11, whereas (iii) CaFeO39 or YNiO310,12 display both PM metal and PM insulator HT phases. Regarding structural aspects, these perovskites show a range of crystal structure types (cubic, monoclinic, and orthorhombic) as well as structural distortions within such space groups (including octahedral rotations, anti-polar displacements), as well as Jahn–Teller (LaVO3, LaMnO3) or breathing distortion (CaFeO3 and YNiO3) types (see Supplementary Fig. 1). The HT PM phases usually inherit the LT structure, although they can also transform to their own, distinct structure type (as in LaVO3, CaFeO3, and YNiO3).

The enormous number of publications in this field typically focus on one or just few selected ABO3 compound(s) and one or two of the effects noted above. This makes it difficult to assess the key question: what is the minimal physical description needed to capture the basic magnetic, transport, and structural ground-state properties, and can one define a single, overarching theoretical framework that works essentially across the board? This question is highly consequential because the ABO3 system of compounds is in constant demand for theoretical support in the areas of applications that depend on gapping, such as catalysis, water splitting, transparent conductors, thermoelectricity, piezoelectricity, ferroelectricity, and heterostructures showing two-dimensional electron gases (2DEG)13.

The question of the origin of Mott bandgaps is central to this field: Perhaps the most celebrated issue in this regard, raised by Peierls and Mott3,4, concerns the way in which a bandgap can form in the presence of an odd number of electrons, when the Fermi energy EF would intersect what in basic band theory would appear to be a partially occupied, gapless band3. The classic Mott–Hubbard “strongly correlated” symmetry-conserving view has formed a central paradigm to resolve this apparent inconsistency and for teaching and explaining the known phenomenology14,15,16. This viewpoint was motivated by the fact that in the extreme ionic limit (where the 3d ion carries all of the active electrons, while O2− is a rigid, closed shell), the energy levels near EF are degenerate with partial occupancy (such as the triply degenerate t2g occupied by just two electrons, or the doubly degenerate eg occupied by just a single electron). The question that arose was whether lifting such degeneracies, as needed for gapping, would require specialized correlated methodologies that go beyond what band theory would accommodate. The Mott–Hubbard mechanism for gap formation and magnetism in such d-electron oxides (Fig. 1a) envisions electrons moving across the lattice, forming atomic-like states on certain 3d atomic sites with doubly occupied d orbitals (“upper Hubbard band”) and empty d orbitals on other sites (“lower Hubbard band”). In this picture, the bandgap of the AFM and PM phases of these oxides therefore emerges due to this correlation-induced electron–electron repulsion (Fig. 1b top panel), without spatial symmetry breaking (such as structural distortions or magnetic order that would lower the symmetry of the degenerate states). In this view, symmetry can break afterward, but is nonessential for gapping. From this point of view, the minimal theoretical description needed would entail multi-determinant dynamically correlated methodologies capable of treating open-shell degenerate configurations. Band theory (depicted schematically in the lower part of Fig. 1b) was imagined to fail in producing the observed gaps and structures. Note that in most dynamically correlated calculations, the crystal structure and its subtle distortions were not predicted from the underlying electronic structure (with the exception of the works of Marianetti et al.17 and Leonov et al.18 for instance) but rather copied from experimentally observed structures. Thus, these simulations are not a proof of the dominant role of dynamical electron correlations over structural symmetry breaking modes for the gap opening. This question is open.

Fig. 1
figure 1

Role of the interelectronic U parameter. a Mott–Hubbard mechanism with one d electron per site having either a spin up or a spin down. Assuming no symmetry breaking, electrons are hopping on the lattice with a probability t and produce doubly occupied (upper Hubbard band) and empty (lower Hubbard band) orbitals on the sites. Double occupancy causes energy penalty U. b The naive density functional theory (N-DFT, lower panel) also assuming no symmetry breaking would have instead an ungapped, metallic band

However, the failure of naive DFT models does not disqualify DFT. The question is: what type of band theory fails so dramatically to describe gapping in 3d compounds (lower part of Fig. 1b). A natural adoption of this symmetry-conserving principle within band theory for PM phases is to assume a structure where all 3d ions are symmetry-equivalent, having identical local environments (a monomorphous representation). However, since the total magnetic moment in the PM phase must be zero, such a nonmagnetic description forces zero moment on an atom-by-atom basis. This is bound to produce zero gap in a band-theoretic description for systems with an odd number of electrons, in stark contrast with experiments for most AFM and PM phases (Fig. 2).

Fig. 2
figure 2

Summary of the properties (electronic configurations, space group symmetry, metal vs. insulator behavior, spin order, Goldschmidt tolerance factor, mode of gapping, energy differences between the different magnetic solutions, bandgap, and magnetic moments) of oxide perovskites with unpaired electronic d shell configurations tested in our simulations. Green (red) tick marks refer to DFT success (failure) to reproduce the experimental observations available in the literature. For the high-temperature phase, the results of the nonmagnetic approximation to PM are provided in parenthesis

A common-sense examination of the reasonableness of this approach, apparently missed earlier, is to compare the total energy of this nonmagnetic (NM) approximation with the total energy of the same DFT, but using a proper spin-polarized ground state. We find that the naive DFT has a higher total energy of 452, 1167, 935, 4313, and 1925 meV/f.u for YTiO3, LaVO3, CaMnO3, LaMnO3, and CaFeO3, respectively (see Fig. 2 and Supplementary Note 2 for further details). In other words, the ansatz of a NM state is a highly unlikely scenario.

Even though naive DFT approximations correspond to extremely high-energy solutions, they were often used in the literature to suggest that DFT band theory fails to explain gapping of Mott insulators, the latter being argued to require instead an explicitly correlated approach18,19,20,21,22. In the specific case of rare-earth nickelates, it was stated that “Standard DFT and DFT + U methods fail to describe the phase diagram, with DFT predicting that all compounds remain metallic and undisproportionated…. These results establish that strong electronic correlations are crucial to structural phase stability and methods beyond DFT and DFT + U are required to properly describe them” in ref. 23, “spin polarized DFT shows metallic behaviour with neither magnetism nor bond disproportionation…: This qualitative structural error ….signals the importance of correlations” in ref. 17, or “While density functional band theory (DFT) is the workhorse of materials science, it does not capture the physics of the Mott/charge-transfer insulator transition” in ref. 19. Moreover, gapping (and the related structural distortions) in the paramagnetic phases of oxides is often claimed to be unreachable by DFT simulations: “However, these methods (i.e., LDA, GGA, and LDA + U) usually fail to describe the correct electronic and structural properties of electronically correlated paramagnetic materials” and “Therefore, LDA + U cannot describe the properties of LaMnO3 at T > TN and, in particular, at room temperature, where LaMnO3 is a correlated paramagnetic insulator with a robust JT distortion” in ref. 18 or “Although they cannot represent the paramagnetic insulating state, static mean-field theories such as DFT, DFT + U, and hybrid functional approaches may capture some of the physics of the AFM insulating ground state” in ref. 17. Many similar claims about the failure of DFT abound in the correlated literature.

However, naive DFT does not represent what DFT can do. There are certainly a number of papers over the years that have shown gapping in 3d oxides using appropriate DFT and taking into account the structural, electronic, and magnetic degrees of freedom appearing in oxides (i.e., allowing spin polarization, lower energy phase searches for instance)24,25,26,27,28,29,30,31,32,33. With the exception of ref. 25, many of these studies focused on the low-temperature spin-ordered phase, even though the gapping usually appears in the paramagnetic (PM) spin-disordered phase. In ref. 25, Trimarchi et al. have proposed a strategy to model PM phases of simple binary oxides, identifying mechanisms to explain gapping in binaries such as MnO and NiO. This paper focuses on ternary compounds such as ABO3 that possess strongly entangled structural, electronic, and magnetic degrees of freedom, yielding far more complex physical behavior and a large range of functionalities encompassing ferroelectricity, magnetism, and thermoelectricity for instance. So far, DFT studies have neither addressed the PM phases of 3d transition metal ABO3 materials, nor elaborate the specific modalities of DFT required to produce gapping, nor have they systematically described the “Periodic Table of gapping” by considering the whole range of trends for the chemical series ABO3 with different A and B atoms. The continuing impression is that DFT itself is failing. It thus seems that the question of what is the minimal theory that describes the basic ground-state phenomenology across the ABO3 series—symmetry broken or symmetry conserving, statically (mean-field treatment of electron–electron repulsion as in DFT) or dynamically correlated—is still unsettled.

Following the standard E. Wigner definition34, correlations are considered to be all physical effects beyond mean-field Hartree–Fock methods35. An often voiced popular (but incomplete) analogous view applied to DFT is that correlation is everything that DFT does not get right. According to this paradigm, the success of (a more general) DFT in describing the trends in the properties of ABO3 d-electron perovskites, described in this paper, would suggest that whereas ABO3 oxides may be complicated, they are not necessarily strongly correlated. In fact, DFT is an exact formal theory for the ground-state properties for the exact exchange-correlation energy functional36, so there is no reason in principle why the properties noted above could not be captured by an ultimate DFT. The paradigm that correlation is what DFT does not get right is, therefore, most likely, a diminishing domain.

In this paper, we show that minimizing the total energy of the AFM and PM phases in supercell representations that allow symmetry breaking, produces atomic displacements and other symmetry-lowering modes that closely follow experiments, and that the same symmetry-breaking modes also predict the correct trends in bandgaps and moments. This is achieved in a single-determinant, mean-field-like band structure approach. This suggests that dynamic correlations outside current DFT implementations and the view that symmetry-conserving physics applies across the board for all AB(d)O3 d-electron systems are not forced upon us by the data, as suggested in previous literature, but represent instead a viewpoint of that literature. We find therefore that the ground-state properties of 3d ABO3 oxides are not good examples of the failure of DFT or the need for special effects outside current DFT. Achieving this requires (a) allowing sufficient structural flexibility (a polymorphous description) in the description of the various phases, so that symmetry breaking reduced crystal symmetries that could lift degeneracies (octahedral rotations, Jahn–Teller, and bond disproportionation effects) and electronic instabilities could occur, should they lower the total energy, and (b) using an exchange-correlation functional in the Kohn-Sham DFT (KS-DFT) that distinguishes occupied from unoccupied states (such as DFT + U; self-interaction corrected functionals) and minimizes the delocalization error37. We are neither claiming that all current and future d or f-electron compounds can be fully explained by DFT with currently known exchange-correlation (XC) functionals, nor that properties other than the basic trends in gapping, moments, and structural displacements can be always predicted. These questions are left for future research. Such failures, if and when found, would provide legitimate challenges for explicitly correlated methodologies to explain. This is a consequential result because it suggests that a rather simple tool such as DFT (requiring a low computational effort with respect to heavier machineries treating dynamical correlations) offers a single platform to study reliably and with sufficient precision not only bandgap formation, structure, and magnetism in ABO3, but also—in the future—other ground-state issues such as doping, defect physics, and interface effects.


The DFT format used

The dual input to this (or other) theories is: (a) a framework for interelectronic interaction (DFT exchange and correlation functional) and (b) a representation of the structural/geometrical degrees of freedom that could be optimized in seeking minimum total energy. Previously, technical shortcomings in (b) within a naive DFT approach (summarized in Supplementary Note 2) were often attributed to theoretical failures in describing the underlying interelectronic interactions (a).

The DFT features that are needed beyond the N-DFT are: (a) functionals that distinguish occupied from unoccupied states. Since we are interested in determining what are the minimum theoretical ingredients needed to explain the ground-state properties observed in the ABO3 series, we deliberately adopt for (a) a mean-field, single-determinant, Bloch periodic band structure approach, with an electron-gas-based description of exchange and correlation. XC functional represents a hierarchy of approximations38,39 (“rungs”). The first three rungs correspond to an XC potential depending on the local density (LDA) and its first (GGA) and second derivative (meta GGA), being local or semi-local functionals of the noninteracting density matrix, with no distinction between occupied and unoccupied levels. The first rung that distinguishes occupied from unoccupied states is rung 4 being a nonlocal functional of the noninteracting density matrix. While ideally this would be a fully self-interaction corrected functional, this functional does not exist as yet, so we use a simple approximation to it in the form of the DFT + U method.

A number of calculations have used this “DFT + U” approach, where DFT is amended by an on-site potential that removes part of the spurious self-interaction error and thereby creates a distinction between occupied and empty states producing at times gapped states25,27,28,29,30,32,40,41,42. DFT + U successfully obtained gapping in simple binary oxides such as MnO, FeO, CoO, or NiO25, dioxides such as UO226, and in the spin-ordered phases of the much more complex 3d transition metal ABO3 compounds27,28,29,30,31,32,41,43,44. These successes have, in part, propagated the view that it is the interelectronic repulsion akin to the Hubbard Hamiltonian that produces gapping in DFT + U. In fact, the role of the on-site potential U in DFT + U, where U is a one-body on-site potential shifting the d orbital to deeper energies, is distinct from the Hubbard Hamiltonian, where it truly represents interelectronic repulsion. Furthermore, U in DFT is actually not required to produce gapping, as illustrated by U-free calculations for the spin-ordered state of several ABO3 compounds28,45,46,47,48,49,50,51,52 as well as for other complex oxides such as VO224 and La2CuO453 for instance. Further details on the DFT calculations and on the choice of U parameters are provided in Supplementary Note 3.

(b) The polymorphous representation of structural degrees of freedom: A primitive unit cell containing a single formula unit of ABO3 cannot break the symmetry in band theory, as there is but a single 3d atom in the crystal. In order to provide a real test to the ability of the DFT XC functional to describe the basic trio of properties—spin arrangement, gapping, and structure—it is necessary to provide in (b) sufficient electronic and structural generality and flexibility in the way the system is represented, so that symmetry-breaking events requiring such flexibility could be captured insofar as they lower the total energy. Here, instead of restricting the unit cell representation of PM (and for AFM) magnetic structures to a single, primitive cell having but a single, symmetry-unique BO6 motif (monomorphous representation), we allow supercells that can develop a set of symmetry-independent BO6 motifs (polymorphous representation), subject to the constraint that the total supercell represents the macroscopic crystal and spin structures (e.g., zero moment in the PM). We use the Special Quasi Random (SQS)54 construct that selects supercells of a given crystalline space group symmetry, such that the occupation of sites by spins follows a random pair and multibody correlation functions (appropriate to the HT limit) with a total moment of zero. The method is described in detail in refs. 25,54. We have tested the convergence of the results with respect to energy, magnetic moment, and bandgaps on two “limit” compounds (namely YTiO3, i.e., d1, and YNiO3, i.e., d7). We have found that a 160-atom unit cell is sufficiently large to produce converged results (see Supplementary Note 4 for details on SQS and the generated supercells). This polymorphous representation25 provides an opportunity to break spatial symmetry, should the total energy be lowered in doing so.

To explore the opportunities for symmetry breaking allowed, in principle, by the polymorphous approach, one has to exercise a few symmetry-breaking “nudges”:

  1. (1)

    Allowing different local environments for the various chemically identical 3d atoms in the lattice. Specifically, a different number of spin-up vs. spin-down sites can exist around each 3d site subject to the SQS constraint that all pair interactions are purely random (i.e., no short-range order) and the total spin is zero.

  2. (2)

    Occupation number fluctuations whereby atomic sites with partial occupation of initially degenerate levels can have different assignments of the electrons to the degenerate partners [such as (1, 0, 1) for two electrons in the three partners of t2g, rather than using fractional and equal occupation such as (2/3, 2/3, 2/3)]55. The problem of finding the site occupations that lead to minimum energy is, in general, a nontrivial optimization problem26, especially when done for the artificial case of (i) a high- symmetry unit cell and (ii) a rigid lattice. However, here we (i) use a supercell that already has a low symmetry (3d atoms have their own local environment) and (ii) allow the lattice to respond to site fluctuations in occupation numbers. In addition, as we will show below, most of the structural distortions (O6 rotations and anti-polar motions of ions) appearing in the ABO3 perovskites mix the “cubic” orbitals removing orbital degeneracies present in the initial cubic phase. Thus, the existence of metastable phases in the cubic cell is not so crucial for our study and these orbital broken symmetries are there to probe the mechanism yielding the bandgap (Jahn–Teller motion or disproportionation for instance). We have tested few initial guesses and only the most stable phase reached after the self-consistency is kept. Finally, for disproportionating materials (e.g., YNiO3 or CaFeO3), different types of initial nudging were performed, such as (1, 0) eg partner occupancies on all B sites or (1, 1) and (0, 0) eg partner occupancies between neighboring B sites.

  3. (3)

    Displacement fluctuations (i.e., atomic relaxation requiring cells larger than the primitive cell), including local Jahn–Teller distortions as well as octahedral mode deformations, such as breathing, tilting, rotation, and anti-polar displacements described in detail in Supplementary Note 1.

Predictions for low-temperature magnetically ordered AFM/FM phases

Figure 2 summarizes our results for the lowest energy phase considering spin-ordered phases (energy differences between all tested magnetic configurations and initial symmetries are given in Supplementary Table 6). Consistent with experiments and previous DFT theoretical literature27,28,29,30,32,40,41,56, for all explored compounds, we find (i) the correct low T crystal structure— orthorhombic for CaVO3, CaMnO3, LaMnO3, and LaFeO3; monoclinic for LaVO3, CaFeO3, and YNiO3; cubic for SrVO3; (ii) the correct low T spin-ordered phase, including AFM (for YTiO3, LaVO3, CaMnO3, LaMnO3, LaFeO3, and YNiO3) or FM (for YTiO3) (except for CaFeO3 that exhibits an incommensurate antiferromagnetic spin spiral order at low temperature9 not included in our modeling); (iii) all compounds adopting a spin-ordered ground state (YTiO3, LaVO3, CaMnO3, LaMnO3, CaFeO3, LaFeO3, and YNiO3) are predicted insulating. Furthermore, (iv) the key cell-internal lattice distortions (O6 group rotations, Jahn–Teller distortions, and bond disproportionation) observed experimentally, are reproduced by theory with mode amplitudes in excellent agreement with experiments (see Supplementary Table 7).

Predictions for high-T paramagnetic phases

Predicted structure types and sublattice distortions: Using the polymorphous representation, the DFT + SQS reproduces the experimentally observed structure for PM phases (YTiO3, CaVO3, SrVO3, LaVO3, CaMnO3, LaMnO3, CaFeO3, LaFeO3, and YNiO3) as summarized in Fig. 2. Interestingly, the relaxed HT structures share key similarities with the LT phases (O6 rotations, bond disproportionation), as inferred by our symmetry-adapted mode analysis (Supplementary Table 7), i.e., the LT phases generally inherit the properties of the PM phases. Only LaVO3 exhibits a PM phase that undergoes an alternative Jahn–Teller motion pattern with respect to the LT phase, yielding an orthorhombic symmetry instead of a monoclinic symmetry (Supplementary Table 7 and Supplementary Fig. 1).

Predicted metal versus insulating characteristics: The present approach correctly reproduces the experimentally observed insulating or metallic behaviors for all materials (Fig. 2). We note, however, that just as is the case in the highly uncorrelated compounds Si and GaAs, DFT often does not give accurate absolute bandgaps (and hence, effective masses), and a GW correction is needed57. The 3d oxides of ABO3 are no exception; we expect that more quantitative gap values and (renormalized) masses will be available as GW is applied to our SQS–DFT.

Surprisingly, the approach also correctly reproduces the two experimentally observed paramagnetic phases of CaFeO3 and YNiO3, with an insulating phase slightly more stable than the metallic phase (Fig. 2; Supplementary Table 6). Finally, we note that ABO3 with early 3d elements B = Ti, V shows band edges that are d-like (upper Hubbard and lower Hubbard bands (c.f. Fig. 1b, top), whereas those with later 3d elements (B = Mn, Fe, and Ni) display oxygen-like band edges (see Figs. 36).

Fig. 3
figure 3

Electronic properties of compounds with closed subshells. Averaged projected density of states on B d levels (gray) and O p levels (red) in CaMnO3 (a) and LaFeO3 (b) in a hypothetical cubic phase within the PM order. The averaged density of states is extracted by summing all contributions coming from all atoms in the PM cells, in each of the spin channels, for p (O, in red) and d (B, in gray) orbitals. Positive (negative) values stand for spin up (down). Orbital resolved DOS on t2g (blue) and eg (green) level is also provided, but for a given B-site cation in the supercell

Fig. 4
figure 4

Electronic properties of compounds lifting electronic degeneracies through octahedra rotations. a, c, d Averaged projected density of states on B d levels (gray) and O p levels (red) in YTiO3 (B = Ti, upper panel) and LaMnO3 (B = Mn, lower panel) in the PM phase. Projected density of states on t2g (blue) and eg (green) levels for a specific B cation within the supercell are also reported. b, e Partial charge-density maps in the (ab) plane of levels located near the Fermi level reported in a and d

Fig. 5
figure 5

Electronic properties of compounds with an unstable electronic structure. ac Averaged projected density of states on V d levels (gray) and O p levels (red) in LaVO3 in the PM phase with different symmetries, lattice distortions, or orbital broken symmetries (OBS). Projected density of states on t2g (blue) and eg (green) levels for a specific V cation within the supercell are also reported. d Partial charge-density plot in the (xz) plane of the last two occupied bands in the AFM-C phase of LaVO3

Fig. 6
figure 6

Electronic properties of compounds undergoing disproportionation effects. a, b Averaged projected density of states on Ni d levels (gray) and O p levels (red) in YNiO3 in the cubic (a) and monoclinic (b) PM phase. c, d Projected density of states on t2g (blue) and eg (green) levels for a couple of NiL (upper panel) and NiS (lower panel) cations within the supercells. e Partial charge-density maps in the (a, b) plane of levels located near the Fermi level (the energy window is reported in b). f Energy difference (in meV/f.u) between the AFM ground state and PM solutions using the orthorhombic (blue diamond) and monoclinic (red squares) symmetries as a function of the tolerance factor. g Bandgap Eg (in eV) associated with the lowest PM phase as a function of the tolerance factor

Gapping mechanisms

Having now established that the methodology used correctly captures the basic physical properties observed experimentally for the different compounds presented in Fig. 2, we next study the triggering mechanism of the gap formation, i.e., the factors causing gapping, providing a classification of gapping mechanisms for the different ABO3 perovskites.

The methodology used to identify the leading gapping mechanism is to start from an assumed high-symmetry cubic perovskite phase (Pm-3m symmetry), and slightly “nudge” (in the linear response sense) this structure with respect to potential symmetry- breaking modes, looking for energy lowering and gap formation. The perturbing modes are (a) allowing different local environments, (b) occupation number fluctuation, and (c) displacement fluctuations, including local Jahn–Teller distortions as well as octahedral mode deformations, such as breathing, tilting, rotation, and anti-polar displacements. Once the leading symmetry- breaking mechanism is found (with respect to cubic), we proceed to perform the complete gapping and magnetism calculation using the actual crystal structure (orthorhombic, cubic, and monoclinic) looking for minimum energy. We group the ABO3 compounds into four categories in terms of the gapping mechanisms.

Gapping mechanism 1: compounds forming closed subshells by octahedral breaking of atomic symmetry

The free ions Mn4+ (d3) and Fe3+ (d5) with an odd number of electrons would simplistically lead to partially filled degenerate states and hence candidate for ungapped “metallic bands”. But the solid-state octahedral symmetry breaks the continuous rotational atomic d symmetry: starting from an assumed cubic phase, CaMnO3 and LaFeO3 are already found to be insulators with bandgaps of 0.10 eV (CaMnO3, t2g3) and 0.85 eV (LaFeO3, t2g3eg2) and sizable magnetic moments of 2.46 µB and 4.20 µB, respectively (Fig. 3a, b). Consequently, in this group, the bandgap originates from lowering the atomic symmetry by the octahedral field and Hund’s rule, driving half-filling of the degenerate partners and an ensuing gap already at the cubic level (such an observation was already raised for CaMnO331). Because of the relative A-to-B atomic size mismatch in ABO3 (as reflected by the 1926 Goldschmidt tolerance factor t58 reported in Fig. 2, being less than 1), these compounds do not prefer the ideal cubic structure and could distort by O6 rotations, as indeed obtained by DFT energy minimization. This additional symmetry lowering produces energy gains of 315 and 378 meV/f.u in CaMnO3 and LaFeO3, respectively, further increasing their bandgaps to 0.64 and 1.31 eV without altering the B cation magnetic moment (Fig. 2).

Gapping mechanism 2: compounds lifting electronic degeneracies due to octahedral rotations and those retaining electronic degeneracies due to small or absent octahedral rotations

Unlike CaMnO3 and LaFeO3, the cubic symmetry alone does not create half-filling in CaVO3, SrVO3, YTiO3 (d1), and LaMnO3 (d4) that continues to exhibit electronic degeneracies of either t2g or eg levels. CaVO3 and SrVO3 are metals, whereas YTiO3 and LaMnO3 are insulators in both PM and LT phases. These can be classified in terms of the strength of the octahedral tilting effects.

YTiO3 and LaMnO3 are gapped insulators due to octahedral rotation in the absence of electronic instability: We first probed the d1 orbital degeneracy of Ti3+ in YTiO3 and of d4 of Mn3+ in LaMnO3 by nudging the occupancy to a specific degenerate partner within the cubic phase (e.g., occupation of the t2g triplet by (1, 0, 0) rather than (1/3, 1/3, 1/3)). We find that the imposed orbital broken symmetry (OBS) is unstable and decays back to a metallic solution with equal occupations of degenerate partners. Thus, in the ideal cubic symmetry, these compounds do not develop any electronic instability that would break the d orbital degeneracy, thereby leading to gap formation.

Permitting the next non-cubic symmetry breaking reveals the gapping mechanism here. Due to a large A-to-B cation size mismatch in ABO3, reflected by their tolerance factor (Fig. 2), YTiO3 and LaMnO3 are expected to be unstable in their cubic structures and to develop O6 rotations, lowering the symmetry from cubic Pm-3m to orthorhombic Pbnm, as indeed found in DFT energy minimization. This results in large total energy lowering (∆E = −1898 and −632 meV/f.u in YTiO3 and LaMnO3, respectively) and in insulating phases with a bandgap created between d levels (Fig. 4a, c). Due to the symmetry lowering, the point group symmetry is reduced from Oh to D2h and a new basis of d orbitals is produced locally on each of the transition metal sites. In YTiO3, it results in a split-off d band below the Fermi level (Fig. 4a) and the Ti d electron is localized in an orbital corresponding to a linear combination of the “cubic-t2g” levels (Fig. 4b) of the form αdxy + βdxz + γdyz (α2 + β2 + γ2 =1), whose coefficients α, β, and γ are triggered by combinations of octahedra rotations and A cations anti-polar motions27 (no Jahn–Teller (JT) motions are observed in the structure on the basis of our symmetry-adapted modes presented in Supplementary Table 7). This results in “orbital ordering” that is clearly a DFT band structure effect triggered by lowering the site symmetry, not a dynamical correlation effect. The characteristic shape of the orbital (reflected in the charge-density map of Fig. 4b) then drives the FM interactions at low temperature27.

A similar mechanism applies for LaMnO3, although the material displays a large in-phase JT distortion (Supplementary Table 7). This produces a gap located between eg levels (Fig. 4c). To settle the importance of the additional JT motion with respect to YTiO3, we calculate the very same Pbnm phase but remove the JT mode. We observe that the material is already an insulator and the averaged Mn3+ magnetic moments are mostly unaltered (Fig. 4d) (even though relying on standard LDA calculations, rotations were previously shown to open pseudo gaps, irrespective of the presence of a Jahn–Teller motion in ref. 59). Therefore, O6 rotations are sufficiently large to split the new basis of eg levels and the Mn3+ electrons are localized in an orbital pointing either along x or y directions on Mn neighboring sites in the (ab) plane (Fig. 4e). These orbitals correspond to linear combinations of the “cubic eg” levels of the form \(\xi d_{z^2} + \eta d_{x^2 - y^2}\) (ξ 2+η2 = 1, \(\left| \xi \right| \approx \left| \eta \right|\)). The specific orbital pattern stabilizes an AFM-A order at low temperature, without changing substantially the bandgap and the averaged magnetic moments (Fig. 2).

CaVO3 and SrVO3 are metals because of insufficiently large O6 rotations: because of their closer-to-1 tolerance factor (Fig. 2), CaVO3 and SrVO3 are not developing large O6 rotations (Supplementary Table 7), as found in DFT energy minimization, and thus the orbitals are not sufficiently split to render an insulating phase. Note that the metallic state is not due to some strongly correlated effect but rather due to a trivial, semiclassical mechanism captured by the 1926 Goldschmidt tolerance factor58. The mechanism was validated by artificially imposing the YTiO3-type O6 rotations onto CaVO3, finding in our variational self-consistency, an insulator with a bandgap of 0.14 eV. In agreement with this result, Pavarini et al. noted in their dynamical mean-field theory (DMFT) simulations21,60,61 on YTiO3 and LaMnO3 that orthorhombic distortions (rotations, A-cation motions) can produce a sufficiently large crystal field splitting localizing electrons, irrespective of Jahn–Teller distortions.

It is often thought that SrVO3 is a good example of failure of mean-field-like theories, and that SrVO3 shows a correlated behavior beyond Hartree–Fock descriptions, i.e., formation of Hubbard bands and a coherent peak at the Fermi level EF due to the electronic correlation in the ground state, revealed by photoemission experiments. This viewpoint classifies SrVO3 into a strongly correlated metal category and dynamical correction in the ground-state description is surely necessary to describe the basic property of the correlated perovskites. We emphasize that the metallic nature of SrVO3 is a simple consequence of the cubic structure being the lowest total energy phase. We note that the SQS-PM approach that is deliberately restricted to a single- determinant mean field gives a clear upper Hubbard band and this bandwidth W associated with t2g is 1.6 eV (SQS-PM DFT), matching well the angle-resolved photoemission spectoscopy62 (ARPES) that gives Wt2g = 1.3 eV and DMFT63,64,65 in which Wt2g is estimated to 0.9, 1.2, or 1.35 eV depending on the DMFT parameters. In contrast, N-DFT using a single monomorphous unit cell gives a bandwidth Wt2g of 2.6 eV as cited by ref. 65.

Gapping mechanism 3: compounds with two electrons in t2g levels

Although a metallic behavior would be expected for LaVO3 (t2g2eg0) with its two electrons distributed in three t2g partners, it is experimentally found to be insulating at all temperatures and no metal–insulator phase transition has been reported in its bulk form6.

In order to understand the mechanism for gapping in this group, we initially break orbital occupancies by nudging two electrons in two out of three t2g orbitals on the V3+ site in the assumed high-symmetry cubic phase (e.g., (1, 1, 0) t2g occupancies). Following variational self-consistency, LaVO3 reaches a lower total energy (∆E = −321 meV/f.u with respect to the (2/3, 2/3, 2/3) degenerate cubic phase) with an insulating electronic structure having a bandgap located between two occupied and one unoccupied formerly t2g levels (Fig. 5a). From this imposed orbital broken symmetry, we conclude that the electronic structure is unstable in the high- symmetry cubic phase of rare-earth vanadates and that these materials should therefore have a secondary contribution to the bandgap due to a Jahn–Teller distortion.

This can be verified by allowing LaVO3 to lower its energy within the PM spin order, by letting it develop O6 rotations and anti-polar motions, resulting in an orthorhombic symmetry. This structure develops a sizable in-phase Jahn–Teller motion similar to that displayed by LaMnO3, albeit smaller (Supplementary Table 7), and is insulating with a large bandgap of 1.60 eV located between t2g levels (Fig. 5c). Again, the JT distortion is but secondary for the gap opening, as evidenced by the fact that a Pbnm distorted structure in which we artificially eliminated the JT distortion already exhibits similar characteristics in terms of magnetic moments and bandgap value (Fig. 5b). Rotations driven by pure steric effects, showing energy gain around 700 meV/f.u with respect to the degenerate cubic phase (compared with the 321 meV/f.u produced by the intrinsic electronic instability), are again sufficient to alleviate orbital degeneracies.

At low temperatures, LaVO3 transforms to an AFM-C insulator. This LT phase develops an alternative and sizable Jahn–Teller motion (Supplementary Table 7), for the octahedral distortion is in antiphase along the c axis, while it is in-phase for the JT motion appearing in Pbnm phases (Supplementary Fig. 1). This alternative JT motion lowers the symmetry from Pbnm to P21/b and produces a specific orbital pattern, different from that appearing in Pbnm phases (Fig. 5d; Supplementary Fig. 3). The extra d electron with respect to YTiO3 is localized in a rock-salt pattern of an orbital corresponding to either a adxy + βdxz or a adxy + βdyz (α2 + β2 = 1) combination. The orbital pattern favors an AFM-C order through the Kugel–Khomskii mechanism66 without significantly changing the bandgap and magnetic moments (Fig. 2).

We see that due to pure steric effects, the O6 rotations are sufficiently large to produce a new basis of orbitals, rendering a localized state in the Pbnm symmetry. The JT motion appearing in the LT phase is reminiscent of the native electronic instability of these materials29 and of the “orbital-order” phase transition reported experimentally6. Finally, the observation of the insulating phase in the orthorhombic symmetry without Jahn–Teller motion is again compatible with DMFT simulations of Pavarini et al. on YVO3 and LaVO320.

Gapping mechanism 4: compounds with unstable single local electronic occupation patterns disproportionating into a double local environment

Although CaFeO3 and YNiO3 develop an electronic degeneracy similar to that of LaMnO3 with a single eg electron, we note that CaFeO3 and YNiO3 are metallic within the orthorhombic Pbnm PM phase, and become insulating in a lower symmetry space group—the P21/n monoclinic structure. We present here details for YNiO3; the very same conclusions are drawn for CaFeO3 in Supplementary Note 8.

We start from an ideal Pm-3m cubic phase and artificially offer breaking of the degeneracy of the Ni3+ t2g6eg1 levels by forcing a specific eg partner occupancy (e.g., (1, 0) instead of (0.5, 0.5)). However, the imposed orbital broken symmetry does not survive the variational self-consistency and the eg electron spreads equally on the two orbitals. We offer an additional symmetry-breaking route by breaking of the degeneracy of the Ni3+ levels via forcing eg-level occupancies on two different Ni sites to be (1, 1) and (0, 0) respectively. This yields a rock-salt pattern of Ni sites with half-filled and empty eg levels, respectively, i.e., mimicking Ni sites with 2 + and 4 + formal oxidation states (FOS). Following variational self-consistency, YNiO3 is trapped in such a state that proves to be of lower energy by 15 meV/f.u compared with the degenerate cubic phase, still with degenerate eg levels on each Ni site and no gap (Fig. 6a). In this OBS, we detect slightly different electronic structures between neighboring transition metal sites (labeled NiL and NiS), yielding different eg-level occupancies and magnetic moments (Fig. 6c). We determine from this probing of the linear response of the system to orbital nudging that the electronic structure is latently unstable and prone therefore to yield distortions in order to produce two types of B environments, one with half-filled (Ni2+) and one with empty (Ni4+) eg states.

Building on our determination of the role of electronic instability, we can now perform the structural relaxation starting from the cubic phase with or without the OBS. Without OBS, YNiO3 relaxes to an orthorhombic Pbnm symmetry (∆E = −921 meV/f.u energy lowering with respect to the cubic phase without OBS) that is metallic. This phase is characterized by the usual O6 rotations and by a single local environment (SLE) for B cations. With OBS, we find that the material relaxes to a P21/n monoclinic phase that is insulating with a gap of 0.50 eV (Fig. 6b) and more stable than the Pbnm symmetry (∆E = −23 meV/f.u with respect to the Pbnm phase, Fig. 6f). Along with the usual Pbnm structural distortions, this phase develops a striking feature: there is a bond disproportionation of two O6 groups, producing a rock-salt pattern of collapsed and extended octahedral (for which Ni cations sitting at their center are labeled NiS and NiL, respectively) due to a sizable breathing mode (Supplementary Table 7), resulting in a double local environment (DLE) for B cations, each having very different B–O bonds. Consistently with the electronic instability identified in the cubic cell, the DLE results in different electronic structures for NiL and NiS ions, characterized by two magnetic moments, the former larger than 1 and the latter approaching 0 (Fig. 6b, d). This is also reflected by the partial charge-density maps (Fig. 6e) obtained from electronic states located between −1 eV and the Fermi level, showing that electrons prefer to occupy eg levels on NiL sites. Thus, YNiO3 reaches insulation through disproportionation effects transforming the 3 + unstable formal oxidation state (FOS) of Ni ions, to its more stable 2 + /4 + stable FOS in the insulating phase67.

Remarkably, although the observation of 2 + /4 + FOS in the insulating phase is consistent with the Wannier analysis discussed in ref. 28, the physical charge density \(\rho (\vec r)\) around NiS and NiL cations is nearly indistinguishable—and similar to that extracted in the metallic Pbnm or cubic phases—as clearly seen in Fig. 3 in ref. 68 owing to a charge self-regulation mechanism68,69,70, whereby the ligands resupply the 3d site with charge lost. This result has sometimes been interpreted in terms of a “ligand-hole” language in refs. 17,28,71 Thus, there is no apparent “physical charge ordering”, in agreement with previous DMFT17 or DFT + U28 studies. That the extent of charge transfer, the lack of physical charge ordering, and the magnitude of disproportionation are reasonably depicted by DFT can be judged by examining the ensuing calculated bond lengths vs. experiment: Supplementary Table 7 shows that the predicted amplitude associated with the bond disproportionation distortion is in excellent agreement with experimental quantities in CaFeO3 and YNiO3.

We can finally check the relative role of the amplitude associated with rotations with respect to the disproportionation effects (we recall that, alone, the latter does not open a gap in YNiO3). To that end, we have performed calculations for other RNiO3 members (R = Gd, Sm, Nd, and Pr) in which O6 rotations progressively decrease (Supplementary Note 9). Surprisingly, we find that only R = Gd and R = Sm are relaxing to a monoclinic phase with a DLE, while R = Nd and Pr are more stable within the orthorhombic symmetry and a SLE (Fig. 6f). Moreover, only R = Y, Sm, and Gd become insulating, while the other two compounds remain metallic (Fig. 6g). We conclude that the O6 rotation amplitudes are controlling the ability to disproportionate to an insulating PM phase in nickelates.

However, we find that all the considered nickelates exhibit an AFM-S order, based on ↑↑↓↓ spin chains of Ni cations in the (ab) plane with different stackings along the c axis72, in their ground state. It thus produces a monoclinic P21/n symmetry that is insulating. We observe that the AFM-S phase shares all the key features of the monoclinic P21/n PM phase, except the fact that the magnetic moment associated with NiS cations becomes exactly null. The complex AFM-S order, which is compatible with the symmetry of the breathing mode, is therefore crucial to open the bandgap via forcing disproportionation effects when materials develop small O6 rotations.

Compounds with an unstable electronic configuration in a SLE structure therefore reach insulation through several sequential factors: (i) they possess an electronic instability, yielding disproportionation effects already in the high-symmetry cubic phase to get rid of the B cation unstable electronic configuration originating from an unstable formal oxidation state; (ii) the disproportionation is strongly linked to the amplitude of the octahedral rotations, appearing first due to steric effects; (iii) antiferromagnetic interactions force the disproportionation when O6 rotations are weak. Our results reconcile the experimental phase diagram of rare-earth nickelates, and most notably, the PM metal to PM insulator or PM metal to AFM-insulator as a function of the rare-earth ionic radius12. Moreover, we unify the different models proposed to explain the metal–insulator phase transition (MIT) with (i) the existence of an electronic instability in rare-earth nickelates (DMFT73,74 and DFT with AFM order30) and (ii) a structurally triggered Peierls MIT in RNiO3 and AFeO3 (A = Ca, Sr) compounds, although the DFT calculations were restricted to simple spin-ordered states30,40.

Finally, the disproportionation effect was described in terms of a “novel correlation effect”17, but as seen here, and in refs. 28,68, it is predictable by the static mean-field DFT. The very recent DMFT simulations of RNiO3 compounds performed by Hampel et al.74 closely match our DFT + U results presented in Fig. 6f, g.


Our DFT calculations of both LT magnetically ordered and HT spin-disordered PM phases reveal the minimal theoretical ingredients required to explain the trends in metal–nonmetal behavior in oxide perovskites, and the associated trends in forms of magnetism and structural selectivity. This includes spin polarization, magnetic interactions, and lower energy phase search through the polymorphous representation—allowing large enough (super) cells, so that various modalities of structural and electronic symmetry breaking can exercise their ability to lower the total energy. This leads one to identify four generic mechanisms opening a bandgap in oxide perovskites. Two mechanisms are related to purely structural symmetry breaking, such as natural octahedral symmetry and its associated symmetry-lowering distortions, such as octahedral tilting and rotations, due to steric effects. The two other mechanisms are related to intrinsic electronic instabilities of transition metals, originating either from spontaneous orbital symmetry breaking, i.e., Jahn–Teller effect or an unstable formal oxidation state of transition metals (disproportionation effect), both manifested by dedicated structural distortions.

Previous statements that DFT fails in describing gapping trends in Mott insulators were premature and often based on a naive application of DFT without properly exploring channels of energy-lowering symmetry breaking, rather than on the failure of the description of interelectronic interactions underlying the density functional theory itself. Indeed, the sequential steps of offering to the system symmetry-breaking modes appear to explain gapping, the nature of the magnetic order, and both the space group symmetries and sublattice distortions (Jahn–Teller and octahedral rotations) in both low temperature and high temperature phases of all ABO3 perovskites with B = 3d. This approach does not require explicit dynamical correlations, or the Mott picture of electron localization on atomic sites with the ensuing formation of upper and lower Hubbard bands (Fig. 1). The basic interactions of crystal field splitting, lattice distortions, and spin polarizations are sufficient to produce insulation in these compounds, and the celebrated Mott–Hubbard mechanism for gap opening (Fig. 1a) may not apply so generally to perovskite oxides. Thus, although these oxides are certainly complicated, they are not obviously strongly dynamically correlated materials and are not good examples where DFT with current exchange-correlation functionals fails.