Lanthanoid silicate apatite solid electrolytes contain one-dimensional channels. These materials display substantial oxygen mobility at temperatures lower than conventional zirconia-based ionic conductors because interstitial oxygen displacements, mediated by Ln cation vacancies, have a lower activation energy. For these nonstoichiometric apatites, crystal structure solutions derived from X-ray and neutron powder diffraction yield the average atomic arrangement, but these techniques also average over local lattice disorders. Large apatite single crystals permit the evaluation of oxygen migration anisotropy using impedance spectroscopy and the correlation of this behavior to atomic scale domain formation or defect cluster aggregation if present. Aberration-corrected scanning transmission electron microscopy, in both high angle annular dark field (HAADF) and bright field (BF) modalities, was applied to characterize the local atomic structure of Nd 9.33 Si 6 O 26 and Nd 8 Sr 2 Si 6 O 26 apatite electrolytes. Quantitative image analysis found the distribution of metal vacancies and dopant metal in apatites to be remarkably homogeneous at the unit cell scale. This is distinct from other oxide electrolytes including fluorites, perovskites, and melilites, where domain and superstructure formation are a consequence of interstitial oxygen incorporation and prescribe the mode of ionic transport. In the present case, the unexpectedly high perfection of silicate apatites arises from the flexible topological response of one-dimensional channels penetrating the structure, which, in turn, allows robust chemical tailoring of these electrolytes.
■ INTRODUCTIONLanthanoid silicate apatites are one-dimensional tunnel structures that adopt hexagonal (P6 3 /m) or pseudohexagonal crystal symmetry and are candidate electrolytes for next generation solid oxide fuel cells (SOFC) (Figure 1). These materials show significant ionic conductivity at intermediate temperatures (500−700°C) 1 that reduces mechanical stress in the cell assemblages and extends their serviceable lifetimes. The general composition of the apatite prototype is Ln 9.33 □ 0.67 Si 6 O 26 (Ln = La) with Ln 3+ vacancies (□) required for charge balance. More completely, two distinct Ln sites occupy the tunnel (Ln T ) and framework (Ln F ) of apatite and the formula can be recast as [Ln F 3.33 □ 0.67 ][Ln T 6 ][SiO 4 ] 6 O 2 . 2 Extrastoichiometric Ln 3+ can be introduced with an accompanying interstitial oxygen (2Ln 3+ + 3O i 2− ), and both atomistic modeling 3,4 and neutron diffraction 5,6 suggest this substitution creates an [001] 7 conduction path for O 2− . However, intratunnel transport only accounts for two-thirds of the conduction, with the balance by cross-tunnel migration, which is less well understood. In any event, ionic mobility in apatites is quite distinct from the extensively studied yttria-stabilized zirconia 8 electrolytes and other ionic conductors, such as dopedceria 9 and La−Sr−Ga−Mg perovskites, 10 whose O 2− conduction is based on vacancy transport. 11