Topological defects at octahedral tilting plethora in bi-layered perovskites

Oxygen octahedral distortions, including tilts/rotations, deformations and off-centring in (layered) perovskites, have the key role in their numerous functional properties. Near the polar-centrosymmetric phase boundary in bi-layered perovskite Ca3−xSrxTi2O7 with x≈1, we found the presence of abundant topological eight-state vortex-antivortex pairs, associated with four oxygen octahedral tilts at domains and another four different oxygen octahedral tilts at domain walls. Our discovery opens a new revenue to unveil real-space topological defects associated with the possible vector choices in one specific lattice mode. Octahedral distortions have close links to the rich variety of functional properties exhibited by perovskite crystals. Sang-Wook Cheong of Rutgers University in the USA and co-workers report the discovery of a new symmetry state in the double-layered perovskite (Ca,Sr)3Ti2O7 utilizing a combination of transmission electron microscopy, synchrotron x-ray diffraction and dielectric characterizations. This intermediate tetragonal structure appears in the vicinity of the phase transition boundary at which the increasing Ca doping drives the parent tetragonal Sr3Ti2O7 unit cell to undergo an orthorhombic distortion. Associated with the oxygen octahedral tilts along the tetragonal directions in this new intermediate state, there are intriguing topological defects present, which may suggest an avenue towards the realization of unconventional functionalities ultimately.


INTRODUCTION
Copious functional phenomena, including high T c superconductivity, 1 ferroelectricity, 2,3 novel magnetism 4-6 and giant photovoltaic effects, 7,8 have been observed in perovskite (ABO 3 )-related compounds, where those physical properties can be closely associated with oxygen octahedral distortions, including tilts/rotations, deformations and off-centring. For example, the high carrier mobility in transparent conducting cubic BaSnO 3 (ref. 9) or photovoltaic halide perovskites 8,10 is closely related with (nearly) 180°bonding between large B-site cations and an oxygen (or a halide ion), resulting from little octahedral distortions. Even when A-site ions are rather small, the perovskite-related structure can be still stabilised through oxygen octahedral tilts/rotations. 11 It turns out that superconductivity in (La,Ba) 2 CuO 4 is significantly influenced by oxygen octahedral tilts, 12,13 and canted magnetic moments appear in antiferromagnetic perovskites with tilted/ rotated oxygen octahedra through Dzyaloshinskii-Moriya interaction. 2,14 High dielectric response in the vicinity of the morphotropic phase boundary is a consequence of the continuously rotating polarisation with various octahedral tilts. 15,16 Crystal field split can be considerably influenced by compression or elongation of oxygen octahedra, which is the origin of the Jahn-Teller effects for B = Cu 2+ or Mn 3+ (refs 1,17,18).
Remarkably, the simultaneous presence of oxygen octahedral tilt and rotation can result in ferroelectric polarisation in perovskites with even number of layers, which is called hybrid improper ferroelectricity. [19][20][21] It has experimentally verified that bilayered perovskite Ca 3 − x Sr x Ti 2 O 7 (CSTO) is a hybrid improper ferroelectric with switchable polarisation of 8 μC cm − 2 in bulk crystals at room temperature. 20 Ferroelectricity in CSTO described by a hybridisation of two structural modes (octahedral tilt and rotation modes) turns out to be associated with an intriguing domain topology consisting of Z 4 × Z 2 domains and Z 3 vortices with eight domains (four directional domains and two antiphase domains), abundant charged domain walls and unique zipper-like switching kinetics. 22 In Z 4 × Z 2 domains, Z 4 denotes the cyclic group of order 4 for directional variants and Z 2 is for translational variants. In this article, utilising in situ heating transmission electron microscopy (TEM) studies, synchrotron powder X-ray diffraction experiments and dielectric measurements, we report the discovery of a new intermediate tetragonal state in CSTO, which demonstrates a displacive nature of hybrid improper ferroelectricity mechanism different from those predicted from the group-subgroup relation. 21,23 Furthermore, we find the presence of topological eight-state vortex-antivortex defects associated with two-dimensional eight degrees of freedom for oxygen octahedral tilts in the intermediate tetragonal state. Figure 1 depicts the possible octahedral tilts/rotations in bi-layered perovskite CSTO, resulting in different structural states and also domains with different directional order parameters. For each space group, the distortion axes and the corresponding Glazer notations 24 are given with respect to the un-distorted tetragonal I4/mmm (T) structure ( Figure 1b). The term 'rotation' denotes a rotation of the basal oxygen plane around the [001] T axis in a clockwise (+) or counterclockwise (− ) manner (Figure 1c for +). Out-of-phase and in-phase rotation in adjacent layers within one bi-layered perovskite block lead to orthorhombic O* and O′ states, respectively. Note that the presence of an intermediate O* state ( Figure 1c) competing with the ground-state polar O state, responsible for uniaxial negative thermal expansion, has been confirmed in hybrid improper ferroelectricity magnet Ca 3 Mn 2 O 7 (refs 25, 26). The term 'tilt' is associated with a tilt around an inplane axis, and it would move the basal oxygens out of the basal plane and the apical oxygen away from the c axis. In-plane tilting axes can be along o1104 T and o 1004 T directions, leading to orthorhombic O′ ( Figure 1e) and tetragonal T′ states (Figure 1f), respectively. Following the Glazer notation, the T state has the a 0 a 0 c 0 pattern and the T′, O′, O* and O′′ states are described as a − a 0 c 0 , a − a − c 0 , a 0 a 0 c − and a 0 a 0 c + , respectively. Two end members,  21,23 With the underlying square lattice, various symmetry-equivalent domains (phases) may exist in each of those states. It is convenient to define the azimuthal angle of an apical oxygen distortion, φ, as shown in Figure 1d. This φ links all possible directions of apical oxygen motions among those phases; for example, symmetry-equivalent domains of the T′ phase correspond to φ = 0°, 90°, 180°and 270°(red-circled ➊, ➋, ➌ and ➍ in Figure 1f, respectively), whereas those in the O′ phase to φ = 45°, 135°, 225°and 315°(blue, 1, 2, 3 and 4 in Figure 1e, respectively). The domains of the polar O state has φ = 45°± α, 135°± α, 225°± α and 315°± α, where α depends on the sign and magnitude of octahedral rotation (a 0 a 0 c + ; 1 ± , 2 ± , 3 ± and 4 ± in Figure 1d, respectively).

RESULTS
We have performed synchrotron powder X-ray diffraction experiments using the collimated synchrotron-radiation beam with the wavelength of 0.688 Å at the National Synchrotron Radiation Research Center, Taiwan. Homogeneous and phase-pure polycrystalline CSTO (0 ⩽ x ⩽3) specimens were prepared by a solid-state reaction method (Materials and methods). The general structure analysis system program using the Rietveld method with a pseudo-Voigt profile function was exploited to analyse the powder diffraction data. The evolution of octahedral rotation (θ R ) and tilting (θ T ) angles of TiO 6 , and lattice parameters a, b and c as a function of Sr content, x, is summarised in Figure 2a and Supplementary Figure S1a. The phase diagram, constructed from these structural parameters, consists of ferroelectric O (purple, 0 ⩽ x ⩽ 0.9) and paraelectric T states (pink, x ⩾ 1.5). The asymmetric decays of θ R and θ T at x = 0.915-1 defines a sharp and narrow region with only non-zero θ T (yellow, Figure 2a). The highresolution X-ray diffraction data clearly display peak splitting only when x ⩽ 0.9, implying a tetragonal symmetry in this narrow region (Supplementary Figure S1b Figure S1c). The details of X-ray refinement fits are given in Supplementary Section 1 and Supplementary Table  S1. The dielectric constant also shows a marked change in magnitude upon entering the T′ state and displays almost two times larger epsilon (ε) value at the phase boundary of x = 0.9, compared with that of low x values ( Figure 2b). An increase in ε at 350 K can be understood as increasing structural fluctuations when approaching from the ferroelectric O to paraelectric T′ states. Indeed, in situ TEM heating experiments of Ca 2.1 Sr 0.9 Ti 2 O 7 crystals exhibit a two-step transformation upon heating: O → T′ → T. Figure 2c shows first that the intensity of superlattice S 1 -type spots ½(130) T of the O state (cyan triangles) weakens as temperature (T, defined italic T as temperature) is raised from 300 to 450 K. Two additional sets of superlattice S 2 -type ½(200) T and S 3 -type ½ 130 À Á T spots (yellow and green triangles), corresponding to the T′ state, appear when temperature is further raised to 473 K. Finally, all superlattice spots vanish above 713 K. Thus, we have demonstrated the stabilisation of the intermediate T′ state by varying chemical composition as well as temperature. Starting from the O state at low x, Figure 2a shows a faster relaxation of the octahedral rotation (θ R ) than that of tilting (θ T ) with increasing Sr doping, which is also coupled with an increasing trend of orthorhombicity. 20 The sudden suppression of octahedral rotations occurs when the azimuthal angle φ suddenly switches from ∼ 45°at x = 0.9 to 0°in the T′ state (Figure 1a), indicating a likely discontinuous change of the tilting order parameter and a first-order phase transition. Note that we do not observe any evidence for an intermediate  Figure 3b) and its corresponding diffraction pattern along the [001] T direction. The curved dark-contrast lines reveal boundaries of four T′-phase domains merging at one core, which is a non-T′ state. With the underlying square lattice, 4 symmetry-equivalent domains, named Z 1 × Z 4 domains, may exist; four translational variants associated with the translation vectors (½, ½, 0), (0, ½, ½) and (½, 0, ½) where out-of-plane phase shifts are involved in the latter two. However, the domain topology can be renamed as Z 2 × Z 2 domains when the in-plane order parameters (octahedral tilts) of one bilayer is considered; two directional variants ([010] Ttilt producing ➊/➌ and [100] T -tilt producing ➋/➍) and two translational variants associated with the in-pane translation vector (½, ½, 0) between ➊-➌ and ➋-➍ (Figure 1f). Our results demonstrate that four domains, corresponding to red-circled ➊, ➋, ➌ and ➍ in Figure 1f, form an exclusive vortex-like pattern with 90°-rotating apical oxygen distortions (red arrows in Figure 3a). These four domains are represented by four values of apical oxygen azimuthal angles φ = 0°, 90°, 180°and 270°; for example, domains ➊ and ➌ correspond to φ = 0°and 180°, respectively. Note that the domain network (Figure 3a) can be described by two proper colouring, i.e., two colours is sufficient to identify the domains without neighbouring domains sharing the same colour (white and green in Supplementary Figure S3a), and the vortex network can be constructed by cutting through two types of closed loops (blue and light blue in Supplementary Figure S3a) based on a graph-theoretical description. 28 Intriguingly, those curved domain walls exhibit two distinct extinction rules in the superlattice DF-TEM images. Figure 3c shows a DF-TEM image using a S 1 spot (light-blue circled in Figure 3b), revealing only a part of domain walls. A complementary domain-wall map is obtained using a S 3 spot for DF-TEM imaging (blue-dotted circled in Figure 3b). The inequivalent nature of these two DF-TEM images with different superlattice peaks with ab plane components indicates an orthorhombic-like local structure at those walls, instead of, e.g., a high-symmetry T state. Considering a pure tilting nature of the matrix T′ state and the distinct extinction rules, those domain walls are likely in the O′ state (  cation ordering is also confirmed from the observation of a brighter contrast of perovskite layers than that of rock-salt layers (Figure 3e). The observation of eight-state vortex-antivortex defects composed of T′ and O′ state suggests an X 3 − modedriven phase transition. Figure 4a summarises two types of Z 4 vortices (types i and ii) and two types of Z 4 antivortices (types iii and iv) observed in Figure 3a. Topological charge or winding number 'n' is assigned when vectors rotate clockwise by 2πn along the clockwise direction around a core. Then, the topological charges of types i, ii, iii and iv topological defects are +1, +1, − 1 and − 1, respectively, which indicates that types i and ii are vortices and types iii and iv are antivortices. We emphasise that vectors in a type i topological defect rotate opposite to those in a type ii topological defect, but they have the same topological charge, so both of them are vortices. A Z 4 vortex is always surrounded by antivortices and vice versa; for example, the vortex 'I' in Figure 3a is connected to the antivortex 'iii' and the antivortex 'iv'. Figure 4b illustrates the local structure around a type i Z 4 vortex (Figure 4a) with red-circled ➊, ➋, ➌ and ➍ domains, and domain walls of DW➊➋ (blue-broken lines), DW➊➍ (light-blue-broken), DW➌➍ (blue) and DW➋➌ (light blue). By averaging the structure of neighbouring domains, DW➊➋ and DW➌➍ share the same [110] T -tilting axis, but are different in the origin by a half of the unit cell. Similarly, DW➋➌ and DW➊➍ have the same tilting axis, which is consistent with the extinction rules observed in Figures 3c and d. On the other hand, a geometric frustration of oxygen octahedral distortions between two antiphase domains occurs likely in DW➊➌ (Figure 4c), leading to an undistorted domain wall in a T structure-like high-symmetric state. The absence of Z 3 vortices where three types of domain walls merge at one point reveals the nonexistence of (½, ½, 0)type APB such as DW➊➌, which, in turn, indicates a much higher energy associated with APBs.

DISCUSSION
The T′ state showing Z 4 vortices occurs in a narrow compositional range of (Ca,Sr) 3 Ti 2 O 7 . When octahedral rotation (thus, hybrid improper ferroelectricity) is suppressed by chemical doping/ionic ordering, Z 4 vortices emerge in the narrow compositional range, where domain and domain walls are intricately intertwined with the T′ and O′ states, arising from the active X 3 − mode. A full isotropy subgroup analysis 29 further implies a missing intermediate orthorhombic Pnnm state, representing order parameter direction (a, b), which is a subgroup of both of the T′ and O′ states, and is expected by symmetry to link domain and domain walls. A similar rule has been also applied to topological Z 6 vortices in hexagonal system, h-In(Mn 0.9 Ga 0.1 )O 3 , where the K 3 mode is characterised by trimerising tilts of the MnO 5 trigonal bipyramids. Three low-symmetry possibilities derived from the parent P6 3 /mmc structure are allowed by the K 3 mode, corresponding to 12 phases of domains and domain walls and an intermediate state link them. 31 Real-space topological defects can be well classified in terms of one specific lattice mode, which leads to a valid physical insight into the phase transition and serves as a platform to uncover additional hidden symmetry and new topological defects. In addition, our new discovery of 'Z 2 × Z 2 domains with Z 4 vortices' unveils that there can be a lot more than just the topological defects (Z 2 × Z 3 domains with Z 6 vortices) in hexagonal rare-earth manganites, which has been extensively investigated since the initial discovery in 2010 (ref. 32). Z 6 vortices observed in improper ferroelectric rare-earth manganites 31,32 and skyrmions in low-symmetry magnets 33 have provided a new paradigm in the quest for mesoscopic self-organised structures with non-trivial topology, which can have novel functionalities. Emphasise that the octahedral distortions in the T′ state is also analogous to that observed in the so-called low-temperature tetragonal state of high-T c superconducting La 2 − x Ba x CuO 4 , in which the CuO 6 octahedra also tilt along the o 1004 T directions 12,13 and are governed by the X 3 + lattice mode. 34 We also note that the T′ structure has been reported in other bi-layered perovskite magnets such as Sr 2 (Ho,Y)Mn 2 O 7 (ref. 35) and Tb 2 Sr(Fe,Co) 2 O 7 (refs 36-38), and magnetism in (layered) perovskites tends to be strongly coupled with structural distortions, so this unique domain topology may not be limited to structural domains and domain walls in (Ca,Sr) 3 Ti 2 O 7 . Our work should initiate further exploration of new types of topological defects.

MATERIALS AND METHODS
Eleven high-quality polycrystalline specimens of Ca 3 − x Sr x Ti 2 O 7 (x = 0, 0.3, 0.5, 0.6, 0.8, 0.85, 0.9, 1, 1.5, 2 and 3) were prepared using a solid-state reaction method. Stoichiometric mixtures of CaCO 3 (Alfa Aesar 99.95%), SrCO 3 (Alfa Aesar 99.99%) and TiO 2 (Alfa Aesar Puratronic 99.995%) powders were ground, pelletised and then sintered at 1,550-1,660°C for 30 h. In the range of 1.1 ⩽ xo1.5, we found a triple-layered A 4 B 3 O 10 phase is more stable and favoured than the bi-layered A 3 B 2 O 7 phase. The powder specimens for acquiring synchrotron X-ray powder diffraction data were sealed in 0.2-mmdiameter capillary quartz tubes. All synchrotron X-ray experiments were performed on beamline BL01C2 at the National Synchrotron Radiation Research Center, Taiwan. The powder diffraction patterns were acquired using a collimated synchrotron-radiation beam with the wavelength of 0.688 Å (18 KeV). Powdered sample were loaded into a 0.2-mm capillary for uniform absorption and faster rotation during data collection. The general structure analysis system program using the Rietveld method with a pseudo-Voigt profile function was exploited to analyse the X-ray powder diffraction data. Specimens for transmission electron microscope (TEM) studies were prepared by mechanical polishing, followed by Ar-ion milling, and studied using a JEOL-2010F TEM at Rutgers University, NJ. We observed Z 4 vortex domains with superlattice DF-TEM imaging taking (1) S 1 = ½(130) T = (120) orth , (2) S 2 = ½(020) T = (110) orth and (3) S 3 ¼½ 130 À Á T ¼ 210 ð Þ orth spots. In situ heating TEM experiment was carried out using a JEOL-2000FX TEM with a high-temperature specimen holder at National Taiwan University in Taiwan. High-angle annular dark-field scanning TEM imaging with atomic-column resolution was carried out using a JEOL-2100F microscope equipped with a spherical aberration Cs-corrector at National Taiwan University in Taiwan. High-angle annular dark-field images were acquired in the condition: 512 × 512 with 0.024 nm per pixel with collection angle between 80 and 210 mrad. For dielectric constant measurements, two electrodes were prepared using Au sputtering on polished specimens with a capacitor geometry, and an LCR metre at f = 44 kHz was utilised.

Data availability
The authors declare that all source data supporting the findings of this study are available within the article and the file.