research communications
Symmetry reduction due to gallium substitution in the garnet Li6.43(2)Ga0.52(3)La2.67(4)Zr2O12
aChemische Kristallographie fester Stoffe, Institut für Anorganische Chemie und Kristallographie, FB02, Leobener Strasse/NW2, and MAPEX Center for Materials and Processes, Universität Bremen, Bibliotheksstrasse 1, 28359 Bremen, Germany, and bInstitut für Physikalische Chemie und Elektrochemie, Leibniz Universität Hannover, Callinstrasse 3-3a, D-30167 Hannover, Germany
*Correspondence e-mail: lrobben@uni-bremen.de
Single-crystal structure refinements on lithium lanthanum zirconate (LLZO; Li7La3Zr2O12) substituted with gallium were successfully carried out in the cubic symmetry I3d. Gallium was found on two lithium sites as well as on the lanthanum position. Due to the structural distortion of the resulting Li6.43(2)Ga0.52(3)La2.67(4)Zr2O12 (Ga–LLZO) single crystals, a reduction of the LLZO cubic garnet symmetry from Iad to I3d was necessary, which could hardly be analysed from X-ray powder diffraction data.
CCDC reference: 1451178
1. Chemical context
Garnets can be described with the ideal formula A3B2(XO4)3 in Iad, with different coordination polyhedra of the respective elements with oxygen, resulting in a distorted cube for A (e.g. Ca), an octahedron for B (e.g. Al) and a tetrahedron for X (e.g. Si). The variability of the elements on the crystallographic sites (thereby keeping the high symmetry) gives rise to interesting material properties like ferrimagnetism (Geller, 1967). In recent years, garnet-type compounds containing Li have gained considerable interest as promising electrolyte materials for all-solid-state Li-ion batteries. The so-called `Li-stuffed' garnets, which contain more Li than available on tetrahedral sites (X), meaning that excess Li occupies other sites as well, show an increase in Li-ion mobility. An exhaustive overview of these compounds was recently given by Thangadurai et al. (2014). The garnet-type fast lithium ion conductor Li7La3Zr2O12, abbreviated as LLZO, is such an `Li-stuffed' garnet. Awaka et al. (2009) described the of pure LLZO at ambient conditions in I41/acd. Even a small amount of Al in the structure (Al-LLZO) stabilizes the cubic garnet symmetry described in Iad by Geiger et al. (2011). These authors reported that Al could be found on two different tetrahedral sites using 27Al MAS NMR spectroscopy but a final analysis was not possible due to the minor Al content. Rettenwander et al. (2014) reported on 71Ga MAS NMR spectroscopy measurements on gallium substituted Li7-3xGaxLa3Zr2O12 (Ga–LLZO) indicating a fourfold coordination of the gallium atoms. The authors excluded the presence of Ga at the 24d position (Iad) and assumed that the could be lower than indicated by diffraction methods. In principle, the following exchanges are possible: (i) 3 Li+ ↔ Ga3+ + 2 voids, which is the most probable one and yields a good explanation for the higher conductivity due to the higher lithium atom jump probability to empty positions as discussed (Rettenwander et al., 2014); (ii) La3+ ↔ Ga3+, a valence-neutral exchange which should lead to a dynamical disorder of the gallium atoms in order to lower the and shorten the Ga—O bond lengths for bond-valence balance, taking the different radii into account. The valence-neutral exchange should finally lead to higher displacement parameters of the atoms on the lanthanum position compared to that of the lighter zirconium atoms. (iii) Zr4+ ↔ Ga3+ + Li+, which needs slightly more lithium for charge balance and could therefore be of minor probability.
2. Structural commentary
The a = 12.9681 (15) Å. The determination with XPREP (Bruker, 2014) leads at once to the highest possible Iad. However, a satisfactory structure solution or with published structural data (Geiger et al., 2011) in this type was not possible. Consequently, structure solutions by (Bruker, 2009) were tried in all possible subgroups of Iad and the lowest R-values were obtained for the charge-flipping run in I3d. Subsequent refinements lead to the present structure model and clearly indicate the substitution of Ga3+ on the former 24c La3+ site as well as 24d Li+ site in the in Iad. The latter site splits into two sites due to the symmetry reduction as indicated by the Bärnighausen tree (Bärnighausen, 1980) given in Fig. 1. The deviation from six symmetry-equivalent Zr—O distances in LLZO (Iad) results in a distortion of the ZrO6 octahedron with Zr—O distances of 3 × 2.095 (2) and 3 × 2.113 (2) Å in Ga–LLZO. Another significant reduction of the highest possible symmetry for LLZO is the distortion of the eightfold coordinate La position (Fig. 2), for which distances between 2.496 (2) and 2.595 (2) Å are found in Ga–LLZO. This distortion results from the splitting of the 96h position of the oxygen atom in Iad into two 48e positions in I3d (Fig. 1). Because the two lithium positions (Li22 and Li32) occupied by gallium are in principle identical to those positions of the higher symmetry structure (but with slightly shorter bond length due to the gallium substitution, viz. 4 × 1.916 (1) Å in LLZO and 4 × 1.908 (2) Å in Ga–LLZO), and the Li1 and Li2 positions are not occupied by gallium, the symmetry reduction is a confirmation of gallium atoms to be found also on the lanthanum position. This is also supported by the higher displacement parameter of the La site compared to the Zr site, as explained previously.
of the obtained single crystals could be well indexed using a body-centered cubic lattice with lattice parameter3. Synthesis and crystallization
The synthesis was configured to yield a compound with nominal composition Li6.25Ga0.25La3Zr2O12. 2 g of a stoichiometric mixture of the pre-dried (30 h at 373 K in vacuum) educts Li2O (with an excess of 10%wt to compensate the lithium loss due to thermal treatment), La2O3, ZrO2 and Ga2O3 was weighted into a WC milling beaker (45 ml, 100 WC milling balls of 5 mm diameter, Fritsch, Germany) under inert conditions (glovebox) and high-energy ball-milled in a planetary ball mill (Pulverisette 7 premium line, Fritsch, Germany) under argon atmosphere for 8 h at a rotational speed of 10 s−1 as reported previously (Düvel et al., 2012) for Al-substituted LLZO. The obtained powder was pressed to a pellet using a uniaxial pressure of 0.8 GPa. A stack of three pellets was placed on a platinum ring seated on a corundum plate, covered with a corundum crucible and heated for 12 h at 1323 K in a muffle furnace before cooling to room-temperature. The middle pellet from the stack had smooth green color and showed visible grains. The surface of the pellet was grey and brittle and consisted mainly of lanthanum zirconates due to Li loss. From this pellet single crystals were extracted using a polarization microscope. of X-ray powder diffraction data of the green product shows a mixture of 96.8 (9)%wt cubic garnet-type Ga–LLZO and 3.2 (9)%wt Li2ZrO3 with a lattice parameter of a = 12.9738 (19) Å for its garnet-type structure. Energy dispersive X-ray analysis of the single crystal gave a tentative formula of Li6.5 (1)Ga0.5 (1)La2.8 (1)Zr2.0 (1)O12, in good agreement with the refined formula Li6.43 (2)Ga0.52 (3)La2.67 (4)Zr2O12 determined from single crystal X-ray diffraction data.
4. Refinement
Crystal data, data collection and structure . Structure was carried out as a two-component (merohedral) twin. Sites showing a statistical occupancy were constrained with respect to positions and anisotropic displacement parameters. An independent of the anisotropic displacement parameters of Ga and Li on the Ga2/Li22 and Ga3/Li33 sites was not possible, although the reflection-to-parameter ratio is rather high. To ensure charge neutrality during the of the Ga and Li occupancies on the Ga2/Li22 and Ga3/Li33 sites, the occupancies were restrained to exchange three Li atoms against one Ga atom.
details are summarized in Table 1Supporting information
CCDC reference: 1451178
10.1107/S2056989016001924/wm5261sup1.cif
contains datablock I. DOI:Structure factors: contains datablock I. DOI: 10.1107/S2056989016001924/wm5261Isup2.hkl
Garnets can be described with the ideal formula A3B2(XO4)3 in 3d, with different coordination polyhedra of the respective elements with oxygen, resulting in a distorted cube for A (e.g. Ca), an octahedron for B (e.g. Al) and a tetrahedron for X (e.g. Si). The variability of the elements on the crystallographic sites (thereby keeping the high symmetry) gives rise to interesting material properties like ferrimagnetism (Geller, 1967). In recent years, garnet-type compounds containing Li have gained considerable interest as promising electrolyte materials for all-solid-state Li-ion batteries. The so-called `Li-stuffed' garnets, which contain more Li than available on tetrahedral sites (X), meaning that excess Li occupies other sites as well, show an increase in Li-ion mobility. An exhaustive overview of these compounds was given by Thangadurai et al. (2014). The garnet-type fast lithium ion conductor Li7La3Zr2O12, abbreviated as LLZO, is such an `Li-stuffed' garnet. Awaka et al. (2009) described the of pure LLZO at ambient conditions in I41/acd. Even a small amount of Al in the structure (Al-LLZO) stabilizes the cubic garnet symmetry described in Ia3d by Geiger et al. (2011). These authors reported that Al could be found on two different tetrahedral sites using 27Al MAS NMR spectroscopy but a final analysis was not possible due to the minor Al content. Rettenwander et al. (2014) reported on 71Ga MAS NMR spectroscopy measurements on gallium substituted Li7–3xGaxLa3Zr2O12 (Ga–LLZO) indicating a fourfold coordination of the gallium atoms. The authors excluded the presence of Ga at the 24d position (Ia3d) and assumed that the could be lower than indicated by diffraction methods. In principle, the following exchanges are possible: (i) 3 Li+ ↔ Ga3+ + 2 voids, which is the most probable one and yields a good explanation for the higher conductivity due to the higher lithium atom jump probability to empty positions as discussed (Rettenwander et al., 2014); (ii) La3+ ↔ Ga3+, a valence-neutral exchange which should lead to a dynamical disorder of the gallium atoms in order to lower the and shorten the Ga—O bond lengths for bond-valence balance, taking the different radii into account. The valence-neutral exchange should finally lead to a higher displacement parameters of the atoms on the lanthanum position compared to that of the lighter zirconium atoms. (iii) Zr4+ ↔ Ga3+ + Li+, which need slightly more lithium for charge balance and could therefore be of minor probability.
IaThe 3d. However, a satisfactory structure solution or with published structural data (Geiger et al., 2011) in this type was not possible. Consequently, structure solutions by (Bruker, 2009) were tried in all possible subgroups of Ia3d and the lowest R-values were obtained for the charge-flipping run in I43d. Subsequent refinements lead to the present structure model and clearly indicate the substitution of Ga3+ on the former 24c La3+ site and 24d Li+ site in the in Ia3d.. The latter site splits into two sites due to the symmetry reduction as indicated by the Bärnighausen tree (Bärnighausen, 1980) given in Fig. 1. The deviation from six symmetry-equivalent Zr—O distances in LLZO (Ia3d) results in a distortion of the ZrO6 octahedron with Zr—O distances of 3 × 2.095 (2) Å and 3 × 2.113 (2) Å in Ga–LLZO. Another significant reduction of the highest possible symmetry for LLZO is the distortion of the eightfold coordinate La position (Fig. 2), for which distances between 2.496 (2) and 2.595 (2) Å are found in Ga–LLZO. This distortion results from the splitting of the 96h position of the oxygen atoms in Ia3d into two 48e positions in I43d (Fig. 1). Because the two lithium positions (Li22 and Li32) occupied by gallium are in principle identical to those positions of the higher symmetry structure (but with slightly shorter bond length due to the gallium substitution, viz. 4 × 1.916 (1) Å in LLZO and 4 × 1.908 (2) Å in Ga–LLZO), and the Li1 and Li2 positions are not occupied by gallium, the symmetry reduction is a confirmation of gallium atoms to be found also on the lanthanum position. This is also supported by the higher displacement parameter of the La site compared to the Zr site, as explained previously.
of the obtained single crystals could be well indexed using a body-centered cubic lattice with lattice parameter a = 12.9681 (15) Å. The determination with XPREP (Bruker, 2014) lead at once to the highest possible IaThe synthesis was configured to yield a compound with nominal composition Li6.25La3Ga0.25Zr2O12. 2 g of a stoichiometric mixture of the pre-dried (30 h at 373 K in vacuum) educts Li2O (with an excess of 10%wt to compensate the lithium loss due to thermal treatment), La2O3, ZrO2 and Ga2O3 was weighted into a WC milling beaker (45 ml, 100 WC milling balls of 5 mm diameter, Fritsch, Germany) under inert conditions (glovebox) and high-energy ball-milled in a planetary ball mill (Pulverisette 7 premium line, Fritsch, Germany) under argon atmosphere for 8 h at a rotational speed of 10 s−1 as reported previously (Düvel et al., 2012) for Al-substituted LLZO. The obtained powder was pressed to a pellet using a uniaxial pressure of 0.8 GPa. A stack of three pellets was placed on a platinum ring seated on a corundum plate, covered with a corundum crucible and heated for 12 h at 1323 K in a muffle furnace before cooling to room-temperature. The middle pellet from the stack had smooth green color and showed visible grains. The surface of the pellet was grey and brittle and consisted mainly of lanthanum zirconates due to Li loss. From this pellet single crystals were extracted using a polarization microscope.
of X-ray powder diffraction data of the green product shows a mixture of 96.8 (9)%wt cubic garnet-type Ga–LLZO and 3.2 (9)%wt Li2ZrO3 with a lattice parameter of a = 12.9738 (19) Å for its garnet-type structure. Energy dispersive X-ray analysis of the single-crystal gave a tentative formula of Li6.5 (1)Ga0.5 (1)La2.8 (1)Zr2.0 (1)O12, in good agreement with the refined formula Li6.43 (2)Ga0.52 (3)La2.67 (4)Zr2O12 determined from single-crystal X-ray diffraction data.Crystal data, data collection and structure
details are summarized in Table 1. Structure was carried out as a two-component (merohedral) twin. Sites showing a statistical occupancy were constrained with respect to positions and anisotropic displacement parameters. An independent of the anisotropic displacement parameters of Ga and Li on the Ga2/Li22 and Ga3/Li33 sites was not possible, although the reflection-to-parameter ratio is rather high. To ensure charge neutrality during the of the Ga and Li occupancies on the Ga2/Li22 and Ga3/Li33 sites, the occupancies were restrained to exchange three Li atoms against one Ga atom.Garnets can be described with the ideal formula A3B2(XO4)3 in 3d, with different coordination polyhedra of the respective elements with oxygen, resulting in a distorted cube for A (e.g. Ca), an octahedron for B (e.g. Al) and a tetrahedron for X (e.g. Si). The variability of the elements on the crystallographic sites (thereby keeping the high symmetry) gives rise to interesting material properties like ferrimagnetism (Geller, 1967). In recent years, garnet-type compounds containing Li have gained considerable interest as promising electrolyte materials for all-solid-state Li-ion batteries. The so-called `Li-stuffed' garnets, which contain more Li than available on tetrahedral sites (X), meaning that excess Li occupies other sites as well, show an increase in Li-ion mobility. An exhaustive overview of these compounds was given by Thangadurai et al. (2014). The garnet-type fast lithium ion conductor Li7La3Zr2O12, abbreviated as LLZO, is such an `Li-stuffed' garnet. Awaka et al. (2009) described the of pure LLZO at ambient conditions in I41/acd. Even a small amount of Al in the structure (Al-LLZO) stabilizes the cubic garnet symmetry described in Ia3d by Geiger et al. (2011). These authors reported that Al could be found on two different tetrahedral sites using 27Al MAS NMR spectroscopy but a final analysis was not possible due to the minor Al content. Rettenwander et al. (2014) reported on 71Ga MAS NMR spectroscopy measurements on gallium substituted Li7–3xGaxLa3Zr2O12 (Ga–LLZO) indicating a fourfold coordination of the gallium atoms. The authors excluded the presence of Ga at the 24d position (Ia3d) and assumed that the could be lower than indicated by diffraction methods. In principle, the following exchanges are possible: (i) 3 Li+ ↔ Ga3+ + 2 voids, which is the most probable one and yields a good explanation for the higher conductivity due to the higher lithium atom jump probability to empty positions as discussed (Rettenwander et al., 2014); (ii) La3+ ↔ Ga3+, a valence-neutral exchange which should lead to a dynamical disorder of the gallium atoms in order to lower the and shorten the Ga—O bond lengths for bond-valence balance, taking the different radii into account. The valence-neutral exchange should finally lead to a higher displacement parameters of the atoms on the lanthanum position compared to that of the lighter zirconium atoms. (iii) Zr4+ ↔ Ga3+ + Li+, which need slightly more lithium for charge balance and could therefore be of minor probability.
IaThe 3d. However, a satisfactory structure solution or with published structural data (Geiger et al., 2011) in this type was not possible. Consequently, structure solutions by (Bruker, 2009) were tried in all possible subgroups of Ia3d and the lowest R-values were obtained for the charge-flipping run in I43d. Subsequent refinements lead to the present structure model and clearly indicate the substitution of Ga3+ on the former 24c La3+ site and 24d Li+ site in the in Ia3d.. The latter site splits into two sites due to the symmetry reduction as indicated by the Bärnighausen tree (Bärnighausen, 1980) given in Fig. 1. The deviation from six symmetry-equivalent Zr—O distances in LLZO (Ia3d) results in a distortion of the ZrO6 octahedron with Zr—O distances of 3 × 2.095 (2) Å and 3 × 2.113 (2) Å in Ga–LLZO. Another significant reduction of the highest possible symmetry for LLZO is the distortion of the eightfold coordinate La position (Fig. 2), for which distances between 2.496 (2) and 2.595 (2) Å are found in Ga–LLZO. This distortion results from the splitting of the 96h position of the oxygen atoms in Ia3d into two 48e positions in I43d (Fig. 1). Because the two lithium positions (Li22 and Li32) occupied by gallium are in principle identical to those positions of the higher symmetry structure (but with slightly shorter bond length due to the gallium substitution, viz. 4 × 1.916 (1) Å in LLZO and 4 × 1.908 (2) Å in Ga–LLZO), and the Li1 and Li2 positions are not occupied by gallium, the symmetry reduction is a confirmation of gallium atoms to be found also on the lanthanum position. This is also supported by the higher displacement parameter of the La site compared to the Zr site, as explained previously.
of the obtained single crystals could be well indexed using a body-centered cubic lattice with lattice parameter a = 12.9681 (15) Å. The determination with XPREP (Bruker, 2014) lead at once to the highest possible IaThe synthesis was configured to yield a compound with nominal composition Li6.25La3Ga0.25Zr2O12. 2 g of a stoichiometric mixture of the pre-dried (30 h at 373 K in vacuum) educts Li2O (with an excess of 10%wt to compensate the lithium loss due to thermal treatment), La2O3, ZrO2 and Ga2O3 was weighted into a WC milling beaker (45 ml, 100 WC milling balls of 5 mm diameter, Fritsch, Germany) under inert conditions (glovebox) and high-energy ball-milled in a planetary ball mill (Pulverisette 7 premium line, Fritsch, Germany) under argon atmosphere for 8 h at a rotational speed of 10 s−1 as reported previously (Düvel et al., 2012) for Al-substituted LLZO. The obtained powder was pressed to a pellet using a uniaxial pressure of 0.8 GPa. A stack of three pellets was placed on a platinum ring seated on a corundum plate, covered with a corundum crucible and heated for 12 h at 1323 K in a muffle furnace before cooling to room-temperature. The middle pellet from the stack had smooth green color and showed visible grains. The surface of the pellet was grey and brittle and consisted mainly of lanthanum zirconates due to Li loss. From this pellet single crystals were extracted using a polarization microscope.
of X-ray powder diffraction data of the green product shows a mixture of 96.8 (9)%wt cubic garnet-type Ga–LLZO and 3.2 (9)%wt Li2ZrO3 with a lattice parameter of a = 12.9738 (19) Å for its garnet-type structure. Energy dispersive X-ray analysis of the single-crystal gave a tentative formula of Li6.5 (1)Ga0.5 (1)La2.8 (1)Zr2.0 (1)O12, in good agreement with the refined formula Li6.43 (2)Ga0.52 (3)La2.67 (4)Zr2O12 determined from single-crystal X-ray diffraction data. detailsCrystal data, data collection and structure
details are summarized in Table 1. Structure was carried out as a two-component (merohedral) twin. Sites showing a statistical occupancy were constrained with respect to positions and anisotropic displacement parameters. An independent of the anisotropic displacement parameters of Ga and Li on the Ga2/Li22 and Ga3/Li33 sites was not possible, although the reflection-to-parameter ratio is rather high. To ensure charge neutrality during the of the Ga and Li occupancies on the Ga2/Li22 and Ga3/Li33 sites, the occupancies were restrained to exchange three Li atoms against one Ga atom.Data collection: APEX2 (Bruker, 2014); cell
SAINT (Bruker, 2014); data reduction: SAINT (Bruker, 2014); program(s) used to solve structure: TOPAS (Bruker, 2009); program(s) used to refine structure: SHELXL2014 (Sheldrick, 2015); molecular graphics: DIAMOND (Brandenburg, 1999); software used to prepare material for publication: publCIF (Westrip, 2010).Fig. 1. Bärnighausen tree (Bärnighausen, 1980) of the group–subgroup relation between cubic LLZO and the symmetry-reduced cubic Ga–LLZO. | |
Fig. 2. Crystal structure of Li6.43 (2)Ga0.52 (3)La2.67 (4)Zr2O12 (Ga–LLZO) with all possible atom positions between the ZrO6 octahedra (bottom) and the atom position specific coordination polyhedra (top). Displacement ellipsoids (top) are given at the 50% probability level. |
Li6.43Ga0.52La2.67Zr2O12 | Mo Kα radiation, λ = 0.71073 Å |
Mr = 826.20 | Cell parameters from 9913 reflections |
Cubic, I43d | θ = 3.1–72.3° |
a = 12.9681 (15) Å | µ = 13.41 mm−1 |
V = 2180.9 (8) Å3 | T = 301 K |
Z = 8 | Irregular, green |
F(000) = 340 | 0.25 × 0.15 × 0.13 mm |
Dx = 5.033 Mg m−3 |
Bruker APEXII CCD diffractometer | 3508 reflections with I > 2σ(I) |
φ and ω scans | Rint = 0.046 |
Absorption correction: multi-scan (SADABS; Bruker, 2014) | θmax = 72.3°, θmin = 2.2° |
Tmin = 0.495, Tmax = 0.754 | h = −34→34 |
472450 measured reflections | k = −34→34 |
3678 independent reflections | l = −34→34 |
Refinement on F2 | w = 1/[σ2(Fo2) + (0.011P)2 + 8.6617P] where P = (Fo2 + 2Fc2)/3 |
Least-squares matrix: full | (Δ/σ)max = 0.049 |
R[F2 > 2σ(F2)] = 0.026 | Δρmax = 2.08 e Å−3 |
wR(F2) = 0.056 | Δρmin = −1.91 e Å−3 |
S = 1.46 | Extinction correction: SHELXL2014 (Sheldrick, 2015), Fc*=kFc[1+0.001xFc2λ3/sin(2θ)]-1/4 |
3678 reflections | Absolute structure: Flack x determined using 1493 quotients [(I+)-(I-)]/[(I+)+(I-)] (Parsons et al., 2013) |
50 parameters | Absolute structure parameter: 0.045 (9) |
3 restraints |
Li6.43Ga0.52La2.67Zr2O12 | Z = 8 |
Mr = 826.20 | Mo Kα radiation |
Cubic, I43d | µ = 13.41 mm−1 |
a = 12.9681 (15) Å | T = 301 K |
V = 2180.9 (8) Å3 | 0.25 × 0.15 × 0.13 mm |
Bruker APEXII CCD diffractometer | 3678 independent reflections |
Absorption correction: multi-scan (SADABS; Bruker, 2014) | 3508 reflections with I > 2σ(I) |
Tmin = 0.495, Tmax = 0.754 | Rint = 0.046 |
472450 measured reflections |
R[F2 > 2σ(F2)] = 0.026 | 3 restraints |
wR(F2) = 0.056 | Δρmax = 2.08 e Å−3 |
S = 1.46 | Δρmin = −1.91 e Å−3 |
3678 reflections | Absolute structure: Flack x determined using 1493 quotients [(I+)-(I-)]/[(I+)+(I-)] (Parsons et al., 2013) |
50 parameters | Absolute structure parameter: 0.045 (9) |
Geometry. All e.s.d.'s (except the e.s.d. in the dihedral angle between two l.s. planes) are estimated using the full covariance matrix. The cell e.s.d.'s are taken into account individually in the estimation of e.s.d.'s in distances, angles and torsion angles; correlations between e.s.d.'s in cell parameters are only used when they are defined by crystal symmetry. An approximate (isotropic) treatment of cell e.s.d.'s is used for estimating e.s.d.'s involving l.s. planes. |
Refinement. Refined as a 2-component twin. |
x | y | z | Uiso*/Ueq | Occ. (<1) | |
La1 | 0.62292 (2) | 0.0000 | 0.2500 | 0.00746 (2) | 0.889 (4) |
Ga1 | 0.62292 (2) | 0.0000 | 0.2500 | 0.00746 (2) | 0.111 (4) |
Zr1 | 0.25005 (2) | 0.25005 (2) | 0.25005 (2) | 0.00552 (4) | |
O1 | 0.19586 (18) | 0.28163 (18) | 0.10116 (16) | 0.0118 (3) | |
O2 | 0.46910 (17) | 0.55410 (17) | 0.65064 (16) | 0.0114 (2) | |
Li1 | 0.428 (3) | 0.593 (2) | 0.813 (2) | 0.029 (5) | 0.33333 (14) |
Li2 | 0.642 (3) | 0.178 (2) | 0.065 (2) | 0.029 (5) | 0.33333 (14) |
Ga2 | 0.3750 | 0.5000 | 0.7500 | 0.0061 (4) | 0.0857 (12) |
Li22 | 0.3750 | 0.5000 | 0.7500 | 0.0061 (4) | 0.743 (4) |
Ga3 | 0.2500 | 0.3750 | 0.0000 | 0.0110 (9) | 0.0403 (12) |
Li32 | 0.2500 | 0.3750 | 0.0000 | 0.0110 (9) | 0.879 (4) |
U11 | U22 | U33 | U12 | U13 | U23 | |
La1 | 0.00912 (4) | 0.00656 (5) | 0.00668 (5) | 0.000 | 0.000 | −0.00141 (3) |
Ga1 | 0.00912 (4) | 0.00656 (5) | 0.00668 (5) | 0.000 | 0.000 | −0.00141 (3) |
Zr1 | 0.00552 (4) | 0.00552 (4) | 0.00552 (4) | 0.00021 (3) | 0.00021 (3) | 0.00021 (3) |
O1 | 0.0129 (6) | 0.0138 (6) | 0.0087 (5) | 0.0014 (5) | −0.0007 (5) | 0.0006 (5) |
O2 | 0.0131 (6) | 0.0116 (6) | 0.0096 (5) | 0.0010 (5) | 0.0000 (5) | −0.0013 (4) |
Li1 | 0.051 (15) | 0.015 (6) | 0.022 (6) | −0.013 (9) | −0.013 (8) | 0.006 (6) |
Li2 | 0.051 (15) | 0.015 (6) | 0.022 (6) | −0.013 (9) | −0.013 (8) | 0.006 (6) |
Ga2 | 0.0078 (10) | 0.0052 (6) | 0.0052 (6) | 0.000 | 0.000 | 0.000 |
Li22 | 0.0078 (10) | 0.0052 (6) | 0.0052 (6) | 0.000 | 0.000 | 0.000 |
Ga3 | 0.0100 (14) | 0.013 (2) | 0.0100 (14) | 0.000 | 0.000 | 0.000 |
Li32 | 0.0100 (14) | 0.013 (2) | 0.0100 (14) | 0.000 | 0.000 | 0.000 |
La1—O1i | 2.496 (2) | O2—Li2xxiii | 2.09 (3) |
La1—O1ii | 2.496 (2) | O2—Zr1xxiv | 2.113 (2) |
La1—O2iii | 2.520 (2) | O2—Li1 | 2.23 (4) |
La1—O2iv | 2.520 (2) | O2—La1xxv | 2.520 (2) |
La1—O2v | 2.590 (2) | O2—Li2xxvi | 2.54 (3) |
La1—O2vi | 2.590 (2) | O2—La1xxiii | 2.590 (2) |
La1—O1vii | 2.595 (2) | O2—Li2xxvii | 2.61 (4) |
La1—O1viii | 2.595 (2) | Li1—O2xxviii | 1.91 (4) |
Zr1—O1ix | 2.095 (2) | Li1—O2xxii | 2.04 (3) |
Zr1—O1x | 2.095 (2) | Li1—O1xxix | 2.16 (3) |
Zr1—O1 | 2.095 (2) | Li1—O1xxx | 2.65 (3) |
Zr1—O2xi | 2.113 (2) | Li2—O1viii | 1.90 (3) |
Zr1—O2xii | 2.113 (2) | Li2—O2vi | 2.09 (3) |
Zr1—O2xiii | 2.113 (2) | Li2—O1xvi | 2.22 (4) |
O1—Li2xiv | 1.90 (3) | Li2—O1xxxi | 2.32 (3) |
O1—Ga3 | 1.918 (2) | Li2—O2xxxii | 2.54 (3) |
O1—Li1xv | 2.16 (3) | Li2—O2xxxiii | 2.61 (4) |
O1—Li2xvi | 2.22 (4) | Li2—Li2xxxiv | 2.68 (6) |
O1—Li2xvii | 2.32 (3) | Ga2—O2xxi | 1.908 (2) |
O1—La1xviii | 2.496 (2) | Ga2—O2xxii | 1.908 (2) |
O1—La1xix | 2.595 (2) | Ga2—O2xxviii | 1.908 (2) |
O1—Li1xx | 2.65 (3) | Ga3—O1xxxv | 1.918 (2) |
O2—Ga2 | 1.908 (2) | Ga3—O1xxxvi | 1.918 (2) |
O2—Li1xxi | 1.91 (4) | Ga3—O1xxxvii | 1.918 (2) |
O2—Li1xxii | 2.04 (3) | ||
O1i—La1—O1ii | 73.18 (10) | La1xviii—O1—Li1xx | 79.5 (6) |
O1i—La1—O2iii | 160.55 (5) | La1xix—O1—Li1xx | 68.9 (8) |
O1ii—La1—O2iii | 111.27 (5) | Ga2—O2—Li1xxi | 49.8 (10) |
O1i—La1—O2iv | 111.27 (5) | Ga2—O2—Li1xxii | 48.0 (8) |
O1ii—La1—O2iv | 160.55 (5) | Li1xxi—O2—Li1xxii | 77.4 (11) |
O2iii—La1—O2iv | 71.21 (10) | Ga2—O2—Li2xxiii | 66.9 (11) |
O1i—La1—O2v | 73.18 (7) | Li1xxi—O2—Li2xxiii | 18.2 (10) |
O1ii—La1—O2v | 95.73 (8) | Li1xxii—O2—Li2xxiii | 85.1 (16) |
O2iii—La1—O2v | 123.67 (5) | Ga2—O2—Zr1xxiv | 128.57 (12) |
O2iv—La1—O2v | 68.75 (9) | Li1xxi—O2—Zr1xxiv | 104.4 (9) |
O1i—La1—O2vi | 95.73 (8) | Li1xxii—O2—Zr1xxiv | 87.4 (8) |
O1ii—La1—O2vi | 73.18 (7) | Li2xxiii—O2—Zr1xxiv | 88.5 (10) |
O2iii—La1—O2vi | 68.75 (9) | Ga2—O2—Li1 | 44.9 (8) |
O2iv—La1—O2vi | 123.67 (5) | Li1xxi—O2—Li1 | 72.9 (12) |
O2v—La1—O2vi | 166.44 (9) | Li1xxii—O2—Li1 | 85.9 (12) |
O1i—La1—O1vii | 125.03 (5) | Li2xxiii—O2—Li1 | 89.7 (13) |
O1ii—La1—O1vii | 68.53 (9) | Zr1xxiv—O2—Li1 | 173.2 (7) |
O2iii—La1—O1vii | 72.72 (6) | Ga2—O2—La1xxv | 94.15 (8) |
O2iv—La1—O1vii | 94.96 (7) | Li1xxi—O2—La1xxv | 143.6 (9) |
O2v—La1—O1vii | 73.07 (5) | Li1xxii—O2—La1xxv | 80.5 (11) |
O2vi—La1—O1vii | 108.77 (5) | Li2xxiii—O2—La1xxv | 161.0 (11) |
O1i—La1—O1viii | 68.53 (9) | Zr1xxiv—O2—La1xxv | 103.05 (9) |
O1ii—La1—O1viii | 125.03 (5) | Li1—O2—La1xxv | 77.0 (9) |
O2iii—La1—O1viii | 94.96 (7) | Ga2—O2—Li2xxvi | 57.6 (8) |
O2iv—La1—O1viii | 72.72 (6) | Li1xxi—O2—Li2xxvi | 76.3 (11) |
O2v—La1—O1viii | 108.77 (5) | Li1xxii—O2—Li2xxvi | 99.9 (14) |
O2vi—La1—O1viii | 73.07 (5) | Li2xxiii—O2—Li2xxvi | 91.0 (11) |
O1vii—La1—O1viii | 165.12 (9) | Zr1xxiv—O2—Li2xxvi | 172.6 (9) |
O1ix—Zr1—O1x | 86.37 (10) | Li1—O2—Li2xxvi | 14.0 (8) |
O1ix—Zr1—O1 | 86.37 (10) | La1xxv—O2—Li2xxvi | 79.4 (7) |
O1x—Zr1—O1 | 86.37 (10) | Ga2—O2—La1xxiii | 122.63 (10) |
O1ix—Zr1—O2xi | 93.51 (9) | Li1xxi—O2—La1xxiii | 95.8 (10) |
O1x—Zr1—O2xi | 179.59 (11) | Li1xxii—O2—La1xxiii | 170.6 (8) |
O1—Zr1—O2xi | 94.02 (9) | Li2xxiii—O2—La1xxiii | 90.4 (8) |
O1ix—Zr1—O2xii | 94.02 (9) | Zr1xxiv—O2—La1xxiii | 100.77 (8) |
O1x—Zr1—O2xii | 93.51 (9) | Li1—O2—La1xxiii | 85.8 (7) |
O1—Zr1—O2xii | 179.59 (11) | La1xxv—O2—La1xxiii | 101.98 (8) |
O2xi—Zr1—O2xii | 86.10 (9) | Li2xxvi—O2—La1xxiii | 71.8 (9) |
O1ix—Zr1—O2xiii | 179.59 (11) | Ga2—O2—Li2xxvii | 56.1 (7) |
O1x—Zr1—O2xiii | 94.02 (9) | Li1xxi—O2—Li2xxvii | 83.4 (14) |
O1—Zr1—O2xiii | 93.51 (9) | Li1xxii—O2—Li2xxvii | 8.2 (9) |
O2xi—Zr1—O2xiii | 86.10 (9) | Li2xxiii—O2—Li2xxvii | 89.2 (9) |
O2xii—Zr1—O2xiii | 86.10 (9) | Zr1xxiv—O2—Li2xxvii | 80.4 (7) |
Li2xiv—O1—Ga3 | 55.1 (12) | Li1—O2—Li2xxvii | 93.0 (11) |
Li2xiv—O1—Zr1 | 100.2 (12) | La1xxv—O2—Li2xxvii | 78.2 (6) |
Ga3—O1—Zr1 | 129.12 (12) | Li2xxvi—O2—Li2xxvii | 107.0 (12) |
Li2xiv—O1—Li1xv | 17.3 (11) | La1xxiii—O2—Li2xxvii | 178.8 (7) |
Ga3—O1—Li1xv | 71.3 (8) | O2xxviii—Li1—O2xxii | 108.5 (14) |
Zr1—O1—Li1xv | 84.8 (8) | O2xxviii—Li1—O1xxix | 98.6 (18) |
Li2xiv—O1—Li2xvi | 80.8 (13) | O2xxii—Li1—O1xxix | 93.9 (12) |
Ga3—O1—Li2xvi | 50.0 (9) | O2xxviii—Li1—O2 | 101.2 (12) |
Zr1—O1—Li2xvi | 85.8 (9) | O2xxii—Li1—O2 | 86.8 (14) |
Li1xv—O1—Li2xvi | 87.3 (14) | O1xxix—Li1—O2 | 158.9 (18) |
Li2xiv—O1—Li2xvii | 78.1 (15) | O2xxviii—Li1—O1xxx | 144.7 (15) |
Ga3—O1—Li2xvii | 48.2 (10) | O2xxii—Li1—O1xxx | 106.5 (15) |
Zr1—O1—Li2xvii | 177.3 (10) | O1xxix—Li1—O1xxx | 83.1 (9) |
Li1xv—O1—Li2xvii | 93.8 (10) | O2—Li1—O1xxx | 76.4 (12) |
Li2xvi—O1—Li2xvii | 91.8 (16) | O1viii—Li2—O2vi | 101.0 (12) |
Li2xiv—O1—La1xviii | 147.5 (13) | O1viii—Li2—O1xvi | 102.1 (17) |
Ga3—O1—La1xviii | 92.55 (8) | O2vi—Li2—O1xvi | 91.1 (12) |
Zr1—O1—La1xviii | 103.48 (9) | O1viii—Li2—O1xxxi | 98.5 (14) |
Li1xv—O1—La1xviii | 163.4 (9) | O2vi—Li2—O1xxxi | 160.3 (14) |
Li2xvi—O1—La1xviii | 79.1 (7) | O1xvi—Li2—O1xxxi | 82.0 (13) |
Li2xvii—O1—La1xviii | 77.3 (7) | O1viii—Li2—O2xxxii | 151.8 (19) |
Li2xiv—O1—La1xix | 94.7 (9) | O2vi—Li2—O2xxxii | 86.9 (13) |
Ga3—O1—La1xix | 123.13 (10) | O1xvi—Li2—O2xxxii | 104.8 (10) |
Zr1—O1—La1xix | 100.26 (9) | O1viii—Li2—O2xxxiii | 84.1 (12) |
Li1xv—O1—La1xix | 89.9 (10) | O2vi—Li2—O2xxxiii | 85.2 (14) |
Li2xvi—O1—La1xix | 173.1 (9) | O1xvi—Li2—O2xxxiii | 173.3 (16) |
Li2xvii—O1—La1xix | 82.1 (10) | O1xxxi—Li2—O2xxxiii | 99.7 (11) |
La1xviii—O1—La1xix | 102.50 (8) | O2xxxii—Li2—O2xxxiii | 69.5 (10) |
Li2xiv—O1—Li1xx | 81.4 (12) | O2xxi—Ga2—O2xxii | 114.14 (7) |
Ga3—O1—Li1xx | 60.5 (8) | O2xxi—Ga2—O2xxviii | 100.49 (13) |
Zr1—O1—Li1xx | 169.2 (8) | O2xxii—Ga2—O2xxviii | 114.14 (7) |
Li1xv—O1—Li1xx | 95.1 (9) | O1—Ga3—O1xxxv | 113.48 (7) |
Li2xvi—O1—Li1xx | 105.0 (14) | O1—Ga3—O1xxxvi | 101.73 (14) |
Li2xvii—O1—Li1xx | 13.3 (11) | O1xxxv—Ga3—O1xxxvi | 113.48 (7) |
Symmetry codes: (i) −y+3/4, x−1/4, −z+1/4; (ii) −y+3/4, −x+1/4, z+1/4; (iii) −x+5/4, −z+3/4, y−1/4; (iv) −x+5/4, z−3/4, −y+3/4; (v) −z+5/4, y−3/4, −x+3/4; (vi) −z+5/4, −y+3/4, x−1/4; (vii) −z+3/4, −y+1/4, x+1/4; (viii) −z+3/4, y−1/4, −x+1/4; (ix) y, z, x; (x) z, x, y; (xi) z−1/4, y−1/4, x−1/4; (xii) y−1/4, x−1/4, z−1/4; (xiii) x−1/4, z−1/4, y−1/4; (xiv) −z+1/4, y+1/4, −x+3/4; (xv) x−1/4, −z+5/4, −y+3/4; (xvi) −x+1, −y+1/2, z; (xvii) x−1/2, −y+1/2, −z; (xviii) −y+1/4, −x+3/4, z−1/4; (xix) z−1/4, −y+1/4, −x+3/4; (xx) y−1/2, z−1/2, x−1/2; (xxi) −x+3/4, z−1/4, −y+5/4; (xxii) x, −y+1, −z+3/2; (xxiii) z+1/4, −y+3/4, −x+5/4; (xxiv) y+1/4, x+1/4, z+1/4; (xxv) −x+5/4, z+1/4, −y+3/4; (xxvi) −z+1/2, x, −y+1; (xxvii) −z+1/2, −x+1, y+1/2; (xxviii) −x+3/4, −z+5/4, y+1/4; (xxix) x+1/4, −z+3/4, −y+5/4; (xxx) z+1/2, x+1/2, y+1/2; (xxxi) x+1/2, −y+1/2, −z; (xxxii) y, −z+1, −x+1/2; (xxxiii) −y+1, z−1/2, −x+1/2; (xxxiv) z+3/4, −y+1/4, −x+3/4; (xxxv) z+1/4, −y+3/4, −x+1/4; (xxxvi) −x+1/2, y, −z; (xxxvii) −z+1/4, −y+3/4, x−1/4. |
Experimental details
Crystal data | |
Chemical formula | Li6.43Ga0.52La2.67Zr2O12 |
Mr | 826.20 |
Crystal system, space group | Cubic, I43d |
Temperature (K) | 301 |
a (Å) | 12.9681 (15) |
V (Å3) | 2180.9 (8) |
Z | 8 |
Radiation type | Mo Kα |
µ (mm−1) | 13.41 |
Crystal size (mm) | 0.25 × 0.15 × 0.13 |
Data collection | |
Diffractometer | Bruker APEXII CCD |
Absorption correction | Multi-scan (SADABS; Bruker, 2014) |
Tmin, Tmax | 0.495, 0.754 |
No. of measured, independent and observed [I > 2σ(I)] reflections | 472450, 3678, 3508 |
Rint | 0.046 |
(sin θ/λ)max (Å−1) | 1.340 |
Refinement | |
R[F2 > 2σ(F2)], wR(F2), S | 0.026, 0.056, 1.46 |
No. of reflections | 3678 |
No. of parameters | 50 |
No. of restraints | 3 |
Δρmax, Δρmin (e Å−3) | 2.08, −1.91 |
Absolute structure | Flack x determined using 1493 quotients [(I+)-(I-)]/[(I+)+(I-)] (Parsons et al., 2013) |
Absolute structure parameter | 0.045 (9) |
Computer programs: APEX2 (Bruker, 2014), SAINT (Bruker, 2014), TOPAS (Bruker, 2009), SHELXL2014 (Sheldrick, 2015), DIAMOND (Brandenburg, 1999), publCIF (Westrip, 2010).
Acknowledgements
Financial support of the Deutsche Forschungsgemeinschaft (DFG) in the Heisenbergprogram (TMG: GE1981/31, GE1981/32) and the Niedersächsisches Ministerium für Wissenschaft und Kultur (MWK) (PH: 74ZN994) is gratefully acknowledged.
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