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Ellipsoidal analysis of coordination polyhedra

Nature Communications volume 8, Article number: 14235 (2017) | Download Citation

Abstract

The idea of the coordination polyhedron is essential to understanding chemical structure. Simple polyhedra in crystalline compounds are often deformed due to structural complexity or electronic instabilities so distortion analysis methods are useful. Here we demonstrate that analysis of the minimum bounding ellipsoid of a coordination polyhedron provides a general method for studying distortion, yielding parameters that are sensitive to various orders in metal oxide examples. Ellipsoidal analysis leads to discovery of a general switching of polyhedral distortions at symmetry-disallowed transitions in perovskites that may evidence underlying coordination bistability, and reveals a weak off-centre ‘d5 effect’ for Fe3+ ions that could be exploited in multiferroics. Separating electronic distortions from intrinsic deformations within the low temperature superstructure of magnetite provides new insights into the charge and trimeron orders. Ellipsoidal analysis can be useful for exploring local structure in many materials such as coordination complexes and frameworks, organometallics and organic molecules.

Introduction

Symmetry group analysis provides a rigorous approach for quantifying distortions of coordination polyhedra but large numbers of modes are often present, for example, an MX6 octahedron has 3 rotations and 15 distortion modes. Continuous symmetry and shape distortion approaches provide some simplifications by parameterizing distortions as a numerical deviation from an idealized polyhedron, and by describing distorted structures in terms of similarity to more ideal polyhedral shapes1,2,3,4,5. However, all of these methods require an appropriate reference polyhedron which may be difficult to define for irregular polyhedra such as 5- or 7- coordinate complexes. As a much more simple approach, single parameter approximations to describe polyhedra and their distortions are useful, but commonly used functions based on M–X distances d such as Δ=σ2(d)/<d2> (where variance σ2(d)=<d2>–<d>2 and <> denotes an average) are not sensitive to angular distortions, while angular variance functions ignore distance variations6,7,8.

A simple and general method for analysing distortions of polyhedra that takes account of shape irrespective of coordination number and geometry is to use an ellipsoidal approximation. Vertices of high symmetry polyhedra lie on the surface of a sphere. Deformations of the polyhedra transform the enclosing sphere into an ellipsoid and in this study we calculate the minimum bounding ellipsoid (MBE) of a given coordination polyhedron, which is the ellipsoid of smallest volume that encompasses all atoms, as described in ‘Methods’ section. The MBE can be calculated for any polyhedron, irrespective of coordination number and geometry. All geometric information for the polyhedron is reduced to the properties of the MBE, plus the displacement vector of the central atom relative to the ellipsoid centre for complexes lacking inversion symmetry. The principal ellipsoid radii are ordered R1R2R3. Their mean <R> is related to the polyhedron size and their variance σ2(R) or s.d. σ(R)=σ2(R) quantifies polyhedral distortion. Ellipsoid shape is represented by the parameter S=R3/R2R2/R1 which has range −1≤S≤1 where oblate (axially compressed) and prolate (axially stretched) ellipsoids respectively have S<0 and S>0, and a sphere has S=0. This method allows the magnitude of distortions of different symmetry to be compared directly, as shown in Fig. 1 for tetragonally and trigonally distorted octahedra. Our ellipsoidal approach has not been elaborated previously, although a best fit ellipsoid method was suggested for defining the centre of irregular polyhedra9,10, and an MBE method was recently used to characterize thermal expansion in perovskite-type ABX3 formates11.

Figure 1: Ellipsoidal fits to distorted octahedra.
Figure 1

(a) The fitted MBE (green net) for a tetragonally elongated MX6 octahedron (M/X=blue/red spheres) where M–X bond distances differ but cis X–M–X angles are 90°. (b) MBE fit to a trigonally distorted MX6 octahedron, where M–X distances are equal but cis X–M–X angles deviate from 90°. The two distorted octahedra have identical prolate MBEs with principal ellipsoid radii shown as yellow arrows in b.

Taking published crystal structures of metal oxides as examples, we demonstrate below that ellipsoidal analysis based on fitting the MBE provides new insights into phase transitions in perovskites, and complex distortions and electronic orders in iron oxides. Our approach has the advantages of providing sensitivity to both distance and angle distortions and of enabling straightforward comparison of coordination polyhedra of any size and symmetry with many fewer parameters than full symmetry mode analysis.

Results

Critical variations at perovskite tilt transitions

Perovskites are an important class of materials with diverse uses including ferroelectrics, for example, BaTiO3, magnetics and spintronics, for example, La1−xSrxMnO3, and photovoltaics, for example, (CH3NH3)PbI3 (ref. 12). The ideal AMX3 perovskite structure is cubic with cuboctahedral AX12 and octahedral BX6 coordinations for which the MBEs are spheres. An important structural aspect is the tendency of perovskites to form superstructures of long-range ordered tilts or rotations of the MX6 octahedra, and 15 simple tilt systems have been classified13,14,15. Most analyses use structural quantities related to the octahedral tilt angle (φ) as the order parameter for transitions between these phases.

LaAlO3 has one of the simplest and most studied perovskite transitions, between low temperature rhombohedral (space group R3c) and high temperature cubic (m) structures at Tc=820 K. The R3c structure is formed by introduction of a single tilt with loss of some symmetry operations of the cubic phase and the transition is continuous (second order)16,17. Ellipsoidal analysis of the LaO12 and AlO6 polyhedra in LaAlO3 using published structural data17 shows that both ellipsoids change from spherical in the cubic phase to oblate in the R3c regime. Thermal variations of the ellipsoid radii and their average <R> and s.d. σ(R) are shown in Fig. 2.

Figure 2: Ellipsoidal analysis of the m structural transition in LaAlO3.
Figure 2

(a) Variations of the ellipsoid radii, their average <R> and s.d. σ(R) for the LaO12 polyhedron, with a t½ fit to σ(R) points above 700 K shown. (b) Variations of the ellipsoid radii, <R> and σ(R) for the AlO6 octahedron showing linear σ(R) t behaviour approaching the transition. t is the reduced temperature t=(TcT)/Tc.

Tilting of AlO6 octahedra deforms the LaO12 polyhedron and σ(R)La is found to reproduce the temperature variation of the AlO6 tilt angle φ, which is proportional to t½ in the critical region approaching Tc (where t is the reduced temperature t=(TcT)/Tc) as shown in Fig. 2a. σ(R) values for the Al ellipsoid are an order of magnitude smaller but they provide a sensitive measure of AlO6 octahedral strain. This is predicted to vary with φ2 and hence show a t1 critical variation18, as is observed in Fig. 2b. Hence ellipsoidal analysis provides a convenient and automatic way of accurately quantifying of the tilt and distortion of the AlO6 octahedra in LaAlO3, through σ(R)La and σ(R)Al, respectively.

Symmetry-disallowed transitions in perovskites

Although several branches of continuous symmetry descent from the cubic m structure are possible through successive tilting transitions, many investigated perovskites show symmetry-disallowed transitions. These have no group-subgroup relation between structures and hence are necessarily first order. Symmetry-disallowed transitions are relatively common in oxide perovskites, as shown in Supplementary Table 1, but the reason for their prevalence is unclear.

We have performed ellipsoidal analyses for many ABO3 perovskites where good quality structural data are available over multiple temperatures proximate to phase transitions. We use the ellipsoid shape parameter which has range −1≤S≤1, where negative and positive values respectively correspond to oblate and prolate distortions of S=0 spherical coordination. Symmetry-disallowed transitions between perovskite tilt superstructures are discovered to always change the sign of the shape parameter (s(S)=+ or −) for at least one of the two coordination ellipsoids (Fig. 3), whereas this is sometimes but not always observed for symmetry-allowed transitions. Prominent examples are below with further information in Supplementary Note 1 and data citations in Supplementary Table 1.

Figure 3: Thermal variations of the ellipsoidal shape parameter S for ABO3 perovskites.
Figure 3

Changes of sign in S are observed at the symmetry-disallowed transitions. (a) SR and (b) SAl shape parameters for RAlO3 perovskites (R=La, Ce, Pr and Nd) with sign changes at the Imma transition (denoted by vertical lines). (c) SR variation in RGaO3 perovskites showing a sign change at the Pnma transition for LaGaO3. (d) SB versus temperature for BaPbO3 and BaTbO3 through their Imma→I4/mcm transitions at 573 and 280 K respectively. (e) SBa and (f) STi variations through the three structural phase transitions of BaTiO3 using published structural data from Kwei et al.23 and Miyake et al.24 Off-centre cation displacements D calculated from the former data are also shown.

Orthorhombic-rhombohedral transitions are observed in many perovskites. RAlO3 perovskites (R=La, Ce, Pr and Nd) all display the m transition described above for LaAlO3 (Fig. 3a,b and Supplementary Fig. 1). At lower temperatures, CeAlO3 and PrAlO3 also show a symmetry-disallowed orthorhombic Imma→rhombohedral transition at which the shapes of both R and Al ellipsoids change, from prolate (S>0) in the Imma structure to oblate (S<0) in the R3c regime, as shown in Fig. 3a,b. Other ABO3 perovskites having this Imma (BaCeO3) or a Pnma (PrNiO3, LaCrO3 and LaGaO3) symmetry-disallowed transition also display a sign change in at least one of the two ellipsoids as shown in Fig. 3c and Supplementary Table 1.

Symmetry-disallowed orthorhombic-tetragonal transitions are observed at high temperatures in a few perovskite materials. The Imma→I4/mcm transitions in BaPbO3 and BaTbO3 and the Pnma→I4/mcm transition in CaTiO3 all show a change of s(S)B from positive to negative (Fig. 3d).

The famous perovskite BaTiO3 provides a striking example of s(S) changes. This material forms a series of ferroelectric phases where changes in the polarization defined by off-centre Ti displacement directions [111]→[110]→[100]→[000] (non-polar) gives rise to the R3mAmm2→P4mmm sequence of phase transitions19,20. The first two transitions are symmetry-disallowed although in principle the magnitude of the polarization can vary continuously through them. Evolution of the off-centre Ti displacements and their local order through the transitions have been studied extensively21,22, but accompanying distortions of the TiO6 octahedron are less explored. Shape parameters SBa and STi calculated from published structural data23,24 both show a striking switching behaviour through the R3mAmm2→P4mm transitions in Fig. 3e,f. In contrast, the magnitudes of the off-centre displacements of the cations vary continuously through the transitions. Hence, the ellipsoidal shape parameters provide complementary information to the off-centre distortions. The former demonstrate abrupt changes in local coordination consistent with the first order transitions and further illustrate the general observation of sign switching at symmetry-disallowed changes, while the latter illustrate how the polarization magnitude effectively acts as a primary order parameter for the entire sequence of transitions.

The sign changes in ellipsoidal shape parameter at symmetry-disallowed perovskite phase transitions provide an important structural insight that has not been previously reported, even for much-studied materials like BaTiO3. The prevalence of sign changes suggests that there is a general bistability to the coordination polyhedra in tilted perovskite superstructures. In the simplest ellipsoidal approximation the distortions can be either prolate or oblate, and if these two states are of similar energy then changes of temperature or other tuning variables such as pressure or composition can lead to changes between them. Prolate and oblate distortions are generally accommodated by different tilt systems, resulting in frequent observation of symmetry-disallowed transitions in perovskites. The switching may be enhanced by electronic instabilities such as weak crystal field effects for Ce3+ and Pr3+ in RAlO3 or the second order Jahn–Teller instability of Ti4+ in BaTiO3.

Iron oxide polyhedra

Ellipsoidal analysis provides a useful approximation for comparing the distortions and shapes of polyhedra with different coordination numbers and geometries through data-mining of crystallographic databases such as Inorganic Crystal Structure Database (ICSD) or Cambridge Structural Database (CSD) (refs 25, 26). These aspects are illustrated by using 499 iron oxide polyhedra from 390 structures in the ICSD where 98 Fe2+ and 401 Fe3+ sites have coordination numbers between 4 and 6. Results are shown in Fig. 4 and Supplementary Fig. 2, and further information is in Supplementary Note 2.

Figure 4: Ellipsoidal parameter plots for literature FeOn polyhedra.
Figure 4

499 FeOn polyhedra in iron oxides (98 for Fe2+ and 401 for Fe3+) taken from the ICSD with Fe coordination numbers n between 4 and 6 are shown. (a) s.d. σ(R) versus mean ellipsoid radius <R>. (b) σ(R) versus shape parameter S showing limits for oblate (S<0), geometrically scalene (S=0) and prolate (S>0) ellipsoids taking R2=1.81 Å. The inset (which does not obscure any points on the main plot) shows an expansion for the region near S=0.

The plot of ellipsoid s.d. σ(R) versus mean radius <R> plot in Fig. 4a shows differing features for the common FeOn coordinations. The distributions for FeO4 tetrahedra and FeO6 octahedra both have many points near σ(R)=0, reflecting their high ideal symmetries, and are clustered around <R>≈d where d is an average Fe–O distance for each coordination. Ideal values based on standard ionic radii for the predominant high spin Fe3+ state in tetrahedral and octahedral geometries are d=1.89 and 2.05 Å, respectively. Five-coordinate polyhedra are rarer and have less regular geometries, as evidenced by the bulk of the distribution lying between σ(R)≈0.1 and 0.3 Å. Highly anisotropic polyhedra have <R> values far from d and large values of σ(R). Ellipsoids describing FeO4 square planes have principal axes R1R2d and R3≈0 so <R>≈(2/3)d and σ(R)≈(2/3)d. The points at σ(R)>0.8 Å show this coordination, with a cluster of flat square planes at <R>≈1.3 Å and a more distorted variant at <R>=1.8 Å.

The plot of σ(R) versus ellipsoid shape S in Fig. 4b is another useful way to observe the spectrum of iron oxide polyhedra. S varies from near -1 for square planar complexes in the oblate distortion limit through many distorted and regular tetrahedra and octahedra at S≈−0.2 to 0.3. The V-shaped appearance of the distribution results from the most symmetric ellipsoid shapes imposing lower limits on σ(R); oblate coordinations (S<0) have σ(R)=−(2/3)R2S while prolate ellipsoids (S>0) have σ(R)=(2/3)R2S/(1-S). These limits are shown on the plot together with the line for geometrically scalene (triaxial) ellipsoids, which have S=0 but are non-spherical with R3/R2=R2/R1 but R1R2R3. This distortion is seen to be rather rare compared with oblate and prolate coordinations.

Electronic orders in magnetite

Analysis of the coordination environment is important when subtle electronic features such as charge or orbital orders are present. A famous example is the iron oxide spinel magnetite, Fe3O4, where proposed Fe2+/Fe3+ charge order below the Verwey transition at 125 K has been controversial for many decades27,28,29,30,31,32,33,34,35. Conventional analysis of specific radial and tetragonal Jahn–Teller modes in the refined superstructure was recently used to demonstrate Fe2+/Fe3+ charge order and Fe2+ orbital order over 16 independent B-site FeO6 octahedra33. Short distances from Fe2+ sites to B-site neighbours further revealed weak direct Fe–Fe bonding effects that give rise to linear Fe3 units known as trimerons. Comparison of ellipsoidal parameter distributions for the 16 FeO6 octahedra in magnetite, which are constrained through connectivity and cooperative electronic distortions, against the large unconstrained set of six-coordinate iron oxide polyhedra from the above analysis of literature structures in Fig. 5 provides useful structural insights.

Figure 5: Ellipsoidal parameters for FeO6 polyhedra.
Figure 5

The plots compare ellipsoidal parameters from iron oxide structures in the ICSD with those in magnetite. Histograms show distributions as log(N+1) for N polyhedra within each interval. Plots (a,c,e) describe 359 FeO6 polyhedra from 317 structures in ICSD. (b,d,f) are for the 16 independent B-site FeO6 octahedra in the reported magnetite superstructure at 90 K (ref. 33), and the single average Fe2.5+O6 octahedral site in the high temperature cubic structure at 130 K is also shown28. (a) s.d. σ(R) versus mean ellipsoid radius <R> for ICSD FeO6 structures. (b) σ(R) versus <R> for FeO6 octahedra in magnetite. (c) Displacements D of the cations from their ellipsoid centres versus <R> for ICSD FeO6 structures. (d) D versus <R> for FeO6 octahedra in magnetite. (e) σ(R) versus σ(R) versus shape parameter S showing limits for oblate (S<0) and prolate (S>0) ellipsoids for ICSD FeO6 structures taking R2=1.9 Å. (f) σ(R) versus S for FeO6 octahedra in magnetite, showing that points within the Fe2+ and Fe3+ distributions lie parallel to the prolate (trigonal elongation) and oblate (tetragonal Jahn–Teller compression) ellipsoid limits. Sets of three sites corresponding to the Fe3+–Fe2+–Fe3+ trimerons with the smallest and largest prolate distortions are encircled; assignments for all trimerons are shown in Supplementary Fig. 3.

The s.d. σ(R) versus mean ellipsoid radius <R> plot for the literature FeO6 polyhedra in Fig. 5a has little structure other than a small displacement between the <R> histograms (which display the number N of polyhedra within each interval as log(N+1) to observe variations from N=0 to N>100) for Fe2+ and Fe3+ according to their ideal Fe–O distances based on ionic radii which are d=2.18 and 2.05 Å. However, the corresponding plot for magnetite (Fig. 5b) has a V-shape with the smallest Fe3+ and largest Fe2+ states having comparably large σ(R) values. This reflects the highly correlated nature of the distortions in magnetite, as each octahedron shares edges with six neighbours leading to an increase in σ(R) with increasing deviation in <R> from the overall structural average. However, instead of meeting with a symmetric V-shape, there is a significant excess in σ(R) for the Fe2+ line relative to that for the Fe3+ line where the two distributions meet at <R>=2.06 Å (corresponding to the average octahedral Fe–O bond length). This excess distortion provides direct evidence for the intrinsic Jahn–Teller distortion of octahedra containing triply-degenerate, high spin 3d6 Fe2+ whereas 3d5 Fe3+ is non-degenerate. The 0.03 Å magnitude of the excess in σ(R) is equivalent to a tetragonal compression where four coplanar Fe–O bonds expand by 0.02 Å and the other pair contract by 0.04 Å. Hence the ellipsoidal σ(R) versus <R> plot is valuable as it enables the single-ion electronic distortion due to Jahn–Teller instability for Fe2+ states to be separated from the correlated deformations of the octahedra due to their high connectivity in the magnetite structure. This is not easily done when using simpler measures of distortion such as the Δ parameter.

Magnitudes D of the Fe atom displacement relative to the ellipsoid centre are plotted against mean ellipsoid radius <R> in Fig. 5c. Neglecting a few outliers, the distribution has a peak at <R>≈2.0 Å (close to the average Fe–O distance for the predominant Fe3+ state) showing that many near-regular FeO6 polyhedra have off-centre instabilities. (Off-centre displacements might be expected to predominate in the most distorted octahedra, but the data do not support this expectation.) Octahedra at a crystallographic inversion centre have D=0 but there is a striking difference between the D>0 distributions for Fe2+ and Fe3+ states. Fe2+ displacements fall off with increasing D values up to a maximum value of 0.19 Å, whereas Fe3+ displacements range up to D=0.30 Å with a peak in the distribution at D≈0.15 Å. This disparity is greater than might be expected from crystal field effects (as σ(R) distributions for Fe2+ and Fe3+ in Fig. 5a are quite similar) and implies that another influence is significant. This is likely a weak ‘d5 effect’ for the half-filled d-shell of Fe3+, similar to the much stronger d0 effect that gives rise to substantial off-centre displacements (second order Jahn–Teller distortions) for cations such as Ti4+ in BaTiO3 above. d0 distortions have previously been analysed by continuous shape measures36. Recent calculations have suggested that off-centre displacements are favourable for Fe3+ in trigonal bipyramidal coordination37, and they are of interest for possible multiferroics where both electric and magnetic polarizations are generated by the d5 configuration.

Linear variations of D with <R> are observed for both Fe2+ and Fe3+ states in low temperature magnetite in Fig. 5d, but with an excess displacement ΔD≈0.04 Å for Fe3+ ions where the two distributions meet at <R>=2.06 Å. Previous structural analysis showed that these Fe3+ displacements are associated with trimeron formation33,35, as Fe3+ ions move towards the spatially ordered lobes of t2g orbitals of adjacent Fe2+ states resulting in weak Fe–Fe bonds. However, in light of the general analysis of Fe displacements revealed in Fig. 5c, the weak ‘d5 effect’ may also enhance the Fe3+ displacements and hence assist trimeron formation in magnetite.

The V-shaped distribution in the plot of s.d. σ(R) versus ellipsoid shape S for literature FeO6 polyhedra in Fig. 5e has lower limits on σ(R) corresponding to symmetric ellipsoid shapes as described above, and many polyhedra lie close to the oblate (S<0) or prolate (S>0) limits reflecting their high crystallographic symmetries. The corresponding plot for magnetite in Fig. 5f shows remarkable structure giving new insights into the electronic distortion. Points for the 16 FeO6 octahedra fall close to three lines parallel to the symmetric ellipsoid limits. The spinel lattice imposes a prolate trigonal distortion on the unique FeO6 octahedron in the high temperature cubic structure (like that shown in Fig. 1b), and this is broadened into a dispersion of distortions close to the prolate limiting line for the Fe3+ type states in the low temperature structure. The Fe2+ distribution is shifted parallel to the oblate limit, as tetragonal Jahn–Teller compression of Fe2+O6 octahedra gives oblate ellipsoidal distortion. However the points for these octahedra are highly structured and lie very close to two lines, one at fixed oblate distortion, showing dispersed trigonal distortions at constant Jahn–Teller deformation, and the other at a constant average trigonal distortion with varying Jahn–Teller effect. Further analysis of this distribution is required but it appears to be related to trimeron formation, as the three sites in each unit have similar prolate distortions as shown for the least and most distorted trimerons on Fig. 5f, and for all trimerons on Supplementary Fig. 3. This structural correlation within the octahedra forming each trimeron was not evident in previous analyses using conventional symmetry group analysis33. Overall, the σ(R) versus S plot provides an elegant separation of the single-ion electronic distortion, which is tetragonal and oblate, from the trigonal prolate deformations that are intrinsic to the distorted spinel lattice, with the two effects behaving as additive vectors parallel to the ellipsoid limits.

Discussion

The above results demonstrate the utility of ellipsoidal analysis of coordination polyhedra. Our ellipsoidal approximation based on fitting the MBE has the advantages of providing sensitivity to both distance and angle distortions and of enabling straightforward comparison of coordination polyhedra of any size and symmetry with many fewer parameters than full symmetry mode analysis. Although the derived ellipsoidal parameters are not predicated on any particular type of distortion being present, they are shown to be highly sensitive to the orders of interest in the metal oxide examples presented.

Ellipsoidal analysis provides a convenient parameterization of octahedral tilts and strains in perovskites and has led to discovery of a general switching of polyhedral distortions at symmetry-disallowed transitions that may evidence underlying coordination bistability. This method is also useful for comparing large numbers of structures from crystallographic databases, here providing evidence for a weak off-centre ‘d5 effect’ for Fe3+ ions that may be exploited in multiferroics. Ellipsoidal plots for the magnetite superstructure have enabled local electronic distortions to be separated from correlated lattice deformations, providing new representations of the complex electronic order for future analysis.

Coordination polyhedra are ubiquitous to chemical structure so ellipsoidal analysis is likely to prove an equally useful tool for probing coordination complexes and frameworks, organometallics and organic molecules, and could even be applied to larger scale packings of molecules or nanoparticles.

Methods

MBE fitting

The MBE for a given coordination polyhedron is calculated using a Khachiyan minimization algorithm38, resulting in three principal radii and a rotation matrix for the ellipsoid, and off-centre displacement D of the central atom. The principal ellipsoid radii are ordered R1R2R3. Their mean <R> is related to the polyhedron size and their variance σ2(R) or s.d. σ(R)=σ2(R) quantifies distortion. S=R3/R2R2/R1 describes ellipsoid shape. Values of <R>, σ(R) and S enable straightforward analysis and comparison of coordination polyhedra of any size and symmetry.

The MBE fitting algorithm is implemented within the PIEFACE (Polyhedra-Inscribing Ellipsoids For Analysing Crystallographic Environments) software package which uses Python 2.7. PIEFACE fits an ellipsoid to a set of points in Cartesian coordinates to within a supplied tolerance; if the points are coplanar then R3 is set to zero. The algorithm can be accessed directly or operated via simple graphical or command-line interfaces which allows direct input of CIF files, with optional control over parameters such as which atoms are coordinating, the maximum radius to use for coordination searching, and the fit tolerance. A number of other routines have also been implemented for data analysis within the PIEFACE package including output of ellipsoid parameters to a number of formats and interactive visualization of the resulting ellipsoids.

Crystallographic data selection

Structural data were taken from published crystal structures. Where possible, structures obtained from neutron diffraction refinement were used to ensure accurate oxygen positions in the presence of heavy atoms. In the perovskite phase transition examples, variable temperature data were extracted from a single study wherever possible to avoid problems of systematic offsets between different experiments. For analysis of Fe oxide materials, polyhedra with Fe-coordinating atoms other than oxygen were rejected, as were mixed-cation sites with Fe occupations below 80%. Only ambient pressure and temperature structures were used.

Code availability

Version 1.0.0 of PIEFACE used in this study is archived at doi:10.5281/zenodo.198370. Code updates are available at https://github.com/jcumby/PIEFACE.

Data availability

All structural data used for ellipsoid fitting were taken from published crystal structures in the ICSD (version 2015.2)25, except for those for the variable temperature study of LaAlO3 shown in Fig. 2 which were taken fromref. 17.

Additional information

How to cite this article: Cumby, J. & Attfield, J. P. Ellipsoidal analysis of coordination polyhedra. Nat. Commun. 8, 14235 doi: 10.1038/ncomms14235 (2017).

Publisher’s note: Springer Nature remains neutral with regard to jurisdictional claims in published maps and institutional affiliations.

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Acknowledgements

This work was supported by ERC Advanced Grant EC 339312. We thank Dr C. Lithgow for testing of the software.

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Affiliations

  1. Centre for Science at Extreme Conditions and School of Chemistry, University of Edinburgh, West Mains Road, Edinburgh EH9 3JZ, UK

    • James Cumby
    •  & J. Paul Attfield

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Contributions

J.C. and J.P.A. conceived and coordinated the study and wrote the paper. J.C. implemented the algorithm and performed the ellipsoidal analyses.

Competing interests

The authors declare no competing financial interests.

Corresponding author

Correspondence to J. Paul Attfield.

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https://doi.org/10.1038/ncomms14235

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