Chemical Bonding and Atomic Structure in Y 2 O 3 : ZrO 2-SrTiO 3 Layered Heterostructures * *

Deposition of nanosized layers of two different metal oxides upon one another produces layered heterostructures with a wide range of new physical properties. For example, a conducting two-dimensional electron gas was discovered at the interface between the two insulators LaAlO3 and SrTiO3. [2] The atomic arrangements within heterostructures of complex functional oxides determine the resulting properties and are not necessarily straightforward to construct based on the bulk crystal structures of the independent components. Garc a-Barriocanal et al. reported that an epitaxial heterostructure of nanometer-sized layers of Y2O3-stabilized ZrO2 (YSZ) and [001]-oriented SrTiO3 (STO) has an up to eight orders of magnitude higher conductivity than bulk YSZ at room temperature. YSZ is a commonly used electrolyte in solid oxide fuel cells (SOFCs) run at high temperatures (> 800 8C), and such an increase in ionic conductivity at lower temperatures would be expected to have a substantial impact on the performance of SOFCs. However, considerable discussion has followed the original publication, with the suggestion that the increased conductivity may be partly electronic in origin. The possibility remains that the conductivity is entirely ionic with indications that the increased conductivity arises from disorder in the oxygen lattice induced in the YSZ layers. 8] Similar, though smaller, increases in conductivity have been found for other layered oxide heterostructures. The exact atomic structure of the YSZ-STO heterostructures remains undetermined. Knowledge of the structure at the boundary between the two component oxide units is crucial for understanding the increase in conductivity, which has been assigned to reconstruction at this interface within the structure. It is difficult to probe the structure of interfaces within thin films experimentally, and previous attempts for YSZ-STO films seem inconsistent. The relative orientation of the YSZ and STO regions has been determined by X-ray diffraction and scanning transmission electron microscopy, 8] with YSZ rotated by 458 about the [001] axis relative to STO. However, electron energy loss spectroscopy suggests that the STO is terminated with a TiO2 layer [3] in layered YSZ-STO, whereas experimental attempts to grow YSZ on STO substrates with different terminations show that [001]oriented YSZ can only be reliably grown epitaxially on SrOterminated STO, leaving the preferred termination of the STO in question. Previous calculations, carried out using only TiO2-terminated STO, [7] determined that oxide ions in the first YSZ layer adopted positions completing the TiO6 octahedra. We assess the stability and electronic structure of different possible atomic arrangements in the YSZ/STO heterostructure using density functional theory (DFT) calculations, focussing on reconstruction at the repeating boundaries between the component YSZ and STO units. We find that the most stable structures, and those which correspond to known oxide crystal chemistry, are not obtained by taking bulk terminations of the YSZ and STO crystals. Instead taking a rock-salt ordered ZrO termination of YSZ gives stable structures with coordination environments which are consistent with known crystal structures, while maintaining insulating electronic behavior and correct YSZ stoichiometry. We have chosen to use DFT calculations, unlike recent classical force field calculations of heterostructures containing YSZ. Although DFT calculations are limited to smaller cells than those used in classical simulations, and are therefore not able to investigate the micrometer scale, they are more transferable than force fields. This is desirable for our structural investigation, since atoms in heterostructures are likely to be in coordination environments different from the constituent bulk phases. Additionally, DFT calculations allow for flexibility in the oxidation state of atoms, and for the calculation of the electronic properties of heterostructures. The simplest model for the buried interfaces within layered heterostructures of two materials is to use terminations of their bulk crystal structures at the interfaces. The two possible terminations in the [001] direction for each of the STO (perovskite) and YSZ (fluorite) crystal structures are shown in Figure 1: STO terminates with either SrO layers or TiO2 layers (both neutral), and YSZ with either Zr or O2 layers (both charged: neglecting Y atoms and O vacancies). This yields four possible interfaces (Figure 2): A) Zr-terminated YSZ and TiO2-terminated STO, B) Zr-terminated YSZ and SrO-terminated STO, C) O2-terminated YSZ and TiO2terminated STO, and D) O2-terminated YSZ and SrO-terminated STO. The construction of heterostructures containing each of these four interfaces is described in detail in the Supporting [*] Dr. M. S. Dyer, Dr. G. R. Darling, Dr. J. B. Claridge, Prof. M. J. Rosseinsky Department of Chemistry, University of Liverpool Liverpool, L69 7ZD (UK) E-mail: m.j.rosseinsky@liv.ac.uk

Matthew S. Dyer, George R. Darling, John B. Claridge, and Matthew J. Rosseinsky* Deposition of nanosized layers of two different metal oxides upon one another produces layered heterostructures with a wide range of new physical properties. [1] For example, a conducting two-dimensional electron gas was discovered at the interface between the two insulators LaAlO 3 and SrTiO 3 . [2] The atomic arrangements within heterostructures of complex functional oxides determine the resulting properties and are not necessarily straightforward to construct based on the bulk crystal structures of the independent components.
García-Barriocanal et al. reported that an epitaxial heterostructure of nanometer-sized layers of Y 2 O 3 -stabilized ZrO 2 (YSZ) and [001]-oriented SrTiO 3 (STO) has an up to eight orders of magnitude higher conductivity than bulk YSZ at room temperature. [3] YSZ is a commonly used electrolyte in solid oxide fuel cells (SOFCs) run at high temperatures (> 800 8C), and such an increase in ionic conductivity at lower temperatures would be expected to have a substantial impact on the performance of SOFCs. [4] However, considerable discussion has followed the original publication, with the suggestion that the increased conductivity may be partly electronic in origin. [5] The possibility remains that the conductivity is entirely ionic [6] with indications that the increased conductivity arises from disorder in the oxygen lattice induced in the YSZ layers. [7,8] Similar, though smaller, increases in conductivity have been found for other layered oxide heterostructures. [9] The exact atomic structure of the YSZ-STO heterostructures remains undetermined. Knowledge of the structure at the boundary between the two component oxide units is crucial for understanding the increase in conductivity, which has been assigned to reconstruction at this interface within the structure. [3] It is difficult to probe the structure of interfaces within thin films experimentally, and previous attempts for YSZ-STO films seem inconsistent. The relative orientation of the YSZ and STO regions has been determined by X-ray diffraction [10] and scanning transmission electron microscopy, [3,8] with YSZ rotated by 458 about the [001] axis relative to STO. However, electron energy loss spectroscopy suggests that the STO is terminated with a TiO 2 layer [3] in layered YSZ-STO, whereas experimental attempts to grow YSZ on STO substrates with different terminations show that [001]oriented YSZ can only be reliably grown epitaxially on SrOterminated STO, [10] leaving the preferred termination of the STO in question. Previous calculations, carried out using only TiO 2 -terminated STO, [7] determined that oxide ions in the first YSZ layer adopted positions completing the TiO 6 octahedra. We assess the stability and electronic structure of different possible atomic arrangements in the YSZ/STO heterostructure using density functional theory (DFT) calculations, focussing on reconstruction at the repeating boundaries between the component YSZ and STO units. We find that the most stable structures, and those which correspond to known oxide crystal chemistry, are not obtained by taking bulk terminations of the YSZ and STO crystals. Instead taking a rock-salt ordered ZrO termination of YSZ gives stable structures with coordination environments which are consistent with known crystal structures, while maintaining insulating electronic behavior and correct YSZ stoichiometry. We have chosen to use DFT calculations, unlike recent classical force field calculations of heterostructures containing YSZ. [11] Although DFT calculations are limited to smaller cells than those used in classical simulations, and are therefore not able to investigate the micrometer scale, they are more transferable than force fields. This is desirable for our structural investigation, since atoms in heterostructures are likely to be in coordination environments different from the constituent bulk phases. Additionally, DFT calculations allow for flexibility in the oxidation state of atoms, and for the calculation of the electronic properties of heterostructures.
The simplest model for the buried interfaces within layered heterostructures of two materials is to use terminations of their bulk crystal structures at the interfaces. The two possible terminations in the [001] direction for each of the STO (perovskite) and YSZ (fluorite) crystal structures are shown in Figure 1: STO terminates with either SrO layers or TiO 2 layers (both neutral), and YSZ with either Zr or O 2 layers (both charged: neglecting Y atoms and O vacancies). This yields four possible interfaces ( Figure 2): A) Zr-terminated YSZ and TiO 2 -terminated STO, B) Zr-terminated YSZ and SrO-terminated STO, C) O 2 -terminated YSZ and TiO 2terminated STO, and D) O 2 -terminated YSZ and SrO-terminated STO.
The construction of heterostructures containing each of these four interfaces is described in detail in the Supporting Information. We used symmetric blocks of STO and YSZ, with the same termination at each end, giving heterostructures with two equivalent interfaces. This is in agreement with experiments, which show no difference between interfaces on either side of YSZ/STO layers. [3,8] The correct choice of symmetric block is essential to obtain chemically reasonable models. The YSZ block was constructed according to the results of previous calculations. [12] Both STO and YSZ blocks do not have the overall composition of their bulk phases, since the terminating layer is inevitably present in excess. The STO and YSZ blocks are 1-2 nm thick. Experimentally layered heterostructures have been grown with 1 nm thick YSZ layers and 10 nm thick STO. [3] As 10 nm thick STO blocks are computationally infeasible at the level of theory used here, and the centers of the computational STO blocks already resemble bulk STO (see Table S1 in the Supporting Information), we consider our structures to be good approximations of the structures of experimental materials.
Geometry optimization of each heterostructure was performed using periodic DFT, [13] and as an indication of the relative stability of each heterostructure, a heat of formation was calculated with respect to the binary oxides, as described in the Supporting Information. The lowest energy structure for each of the four heterostructures, A-D, is shown in Figure 2. The calculated energies were 26.3, 27.1, À0.5, and À5.1 eV for A-D, respectively, with lower values representing more stable structures.
Structures A and B, with Zr-terminated YSZ blocks, are clearly unstable. The Zr(Y) and O 2 layers of YSZ are formally charged, whereas the SrO and TiO 2 layers of STO are charge neutral. As a result, the symmetric blocks of YSZ built with bulk terminations are formally charged. With Zr-terminated blocks, the additional layer of Zr atoms gives a composition of 14 Zr 4 for the YSZ block, with four excess Zr 4+ ions. The calculations impose charge neutrality within the super-cells, which therefore have more electrons than expected for the ions Sr 2+ , Ti 4+ , Y 3+ , Zr 4+ , and O 2À . Plots of the partial density of states (PDOS) of A and B ( Figure S2 in the Supporting Information) show that the excess electrons populate Zr states within the band gap, and begin to fill the Tidominated conduction band. This reduction of Zr 4+ and Ti 4+ to Zr 3+ and Ti 3+ is clearly energetically expensive, leading to the instability of these models.  The interfaces within A and B also suggest energetically unstable structures. The Ti octahedra terminating the STO block in A (Figure 2 A) are clearly distorted, in some the Ti atom is only five-fold coordinated, in a square-pyramidal geometry. The Zr atoms at the interface in B are similarly under-coordinated with most only bonded to five O atoms (Figure 2 B). To our knowledge five-coordinate Zr is unknown in oxide crystal structures.
In contrast, structures C and D, are constructed using O 2terminated YSZ blocks. These structures represent most closely those proposed in earlier experimental studies. García-Barriocanal et al. [3] proposed TiO 2 -terminated STO and O 2 -terminated YSZ, similar to structure C. Structure D, with SrO-terminated STO and O 2 -terminated YSZ, is effectively that proposed by Cavallaro et al. [10] with an interface region resembling SrZrO 3  Using symmetrical unreconstructed Zr-and O 2 -terminated YSZ blocks clearly leads to heterostructures which do not follow conventional solid-state chemistry. They are either reduced in the case of Zr excess, or contain OÀO bonds in the case of O excess. It is, however, possible to construct symmetric YSZ blocks which are formally charge neutral. Adding O to each end of Zr-terminated YSZ blocks (Figure 1 e), gives rock-salt ordered ZrO terminating layers, similar to the SrO layers in STO (Figure 1 b, and Figure S3 in the Supporting Information) and as observed experimentally for the surface of YSZ. [14] The resulting symmetric ZrOterminated YSZ blocks have the composition [Y 2 O 3 ][ZrO 2 ] 18 , and thus have neither excess Zr nor excess O. The ZrOterminated YSZ blocks were combined with TiO 2 -and SrOterminated STO blocks giving structures E and F, respectively. The final structures, optimized as for A-D, are shown in Figure 3.
The calculated heats of formation for E and F were À2.5 and À6.7 eV, respectively. Structure E is more stable than the other two heterostructures with TiO 2 -terminated STO (A: 26.3 eV and C: À0.5 eV), and structure F is more stable than those with SrO-terminated STO (B: 27.1 eV and D: À5.1 eV). The heterostructure with SrO-terminated STO, F, is more stable than E, in good agreement with experimental obser-vations that epitaxial growth of [001] oriented YSZ was only seen with SrO-terminated STO substrates. [10] Models E and F show none of the structural problems found in A-D. The PDOS plots in Figure 4 show that both are undoped semiconductors, and no OÀO bonds are present in their structures. The calculated gaps (E: 1.78 eV, F: 1.37 eV) are similar to the calculated gap of STO (1.79 eV) which is smaller than that of YSZ. We therefore consider E and F to be the best representative models of YSZ-STO heterostructures proposed to date. We emphasise that they require reconstruction of the terminal layer of the YSZ block away from the bulk termination.
A closer look at the structures of E and F in Figure 3 shows a surprising level of order at the interfaces between YSZ and STO, particularly the left-hand interface of E, and the right-hand interface of F. The first layers of YSZ at these two interfaces appear well ordered, although the other interfaces are less so. Furthermore, all of the Zr atoms in the YSZ layers directly neighboring the interfaces are sevenfold coordinate. This is the preferred coordination number of Zr in baddeleyite (monoclinic ZrO 2 ), [15] and an entirely reasonable coordination environment for the Zr atoms. In agreement with earlier work, [7] we find that the Ti atoms in E are octahedrally coordinated. The YSZ terminating ZrO layer Figure 3. Structural diagrams of the interfaces formed within an STO-YSZ heterostructure using a ZrO-terminated YSZ block (depicted in Figure S3 in the Supporting Information) and E: TiO 2 -terminated and F: SrO-terminated SrTiO 3 . To best display these two important structures, each structure is viewed along both of the two short lattice vectors, rather than just one. Ti atoms are at the center of the gray polyhedra, other atoms are colored as follows: Sr mid-gray, Zr light gray, Y dark gray, and O black. effectively caps the TiO 2 -terminating layer of STO continuing the perovskite structure with Zr in the A-site. In F, the terminating ZrO layer lies above the SrO-terminating layer of STO in a rock-salt like geometry resembling the layers of neighboring perovskite blocks in Ruddlesden-Popper structures. [16] Thus, in both E and F, the ordered interfaces can be described in terms of simple, well-known structural motifs for metal oxides.
The central region of YSZ in both E and F appears considerably less ordered than at the interfaces. This disorder is largely due to the strain imposed on the YSZ by the STO substrate, consistent with previous work. [7,8] Comparison of bulk YSZ structures calculated with and without strain in Figure S1 in the Supporting Information, clearly shows the deviation from the fluorite structure upon the application of strain. One indication of this structural change is the alteration in the number of Zr and Y atoms bonded to each O. In unstrained YSZ this is four for each O atom, as expected in the fluorite structure. With the application of strain this drops to an average of 3.7 for bulk YSZ, similar to the values of 3.6 and 3.9 for the YSZ regions of E and F (neglecting O atoms at the interface). Similarly the average number of O atoms bonded to Zr and Y atoms drops from 7.8 in unstrained YSZ to 7.2 in strained YSZ and 7.1 and 7.3 in E and F. Although it is tempting to relate this change away from the fluorite structure to the increased ionic conductivity seen experimentally, we note that the O and Zr environments are in fact becoming close to those found in the most stable ZrO 2 polymorph, baddeleyite. Baddeleyite has a distorted fluorite structure with an average of 3.5 Zr atoms bonded to each O atom, and each Zr atom coordinated to 7 O atoms, [15] and YSZ in this structure does not have a greater ionic conductivity than cubic YSZ. [17] Previous calculations on strained YSZ do suggest enhanced O diffusion, however not sufficient to fully account for the increased ionic conductivity observed in YSZ-STO heterostructures. [18] In contrast to the YSZ region, the central STO region in all models remains largely unchanged (Table S1 in the Supporting Information), retaining the perovskite structure.
The results of this study suggest that the buried YSZ-STO [001] interfaces within the heterostructure require reconstruction during the growth process of the component structures to permit energetically stable and crystal-chemically acceptable structures to form. We also confirm that the most stable heterostructure is formed with YSZ and SrOterminated STO, in agreement with experiment. [10] The structures proposed here can be used in calculating properties relevant to ionic transport, such as the influence of oxygen defects, or the concentration and site preference of Y atoms (in particular their proximity to the YSZ-STO interface), or molecular dynamics simulations. The prediction of possible structures could also be an aid to further experimental characterization of YSZ-STO heterostructures. It is interesting to note the relative stability of structures containing excess oxygen at the interface (models C and D), compared to those with oxygen deficiency (models A and B). This suggests further research into the possible contribution of excess oxygen at YSZ-STO interfaces to increased ionic conductivity.
This study shows the benefit of choosing alternative terminations to the simple bulk terminations of materials when constructing repeating buried interfaces in artificial heterostructures. This is consistent with the known reconstruction of oxide surfaces, including YSZ[001] [14,19] and STO[001] [20] but distinct as in a heterostructure the interfaces are buried. Our findings are relevant for such buried interfaces in many heterostructures, particularly those with layers which are not charge neutral such as A(III)B(III)O 3 perovskites and materials with the fluorite structure.