A series of "empty" tetragonal tungsten bronze (TTB) ferroelectrics, Ba 4-x Sr x Dy 0.67 ! 1.33 Nb 10 O 30 , (x = 0, 0.25, 0.5, 1, 2, 3; ! = vacancy), is reported. With increasing x the unit cell contracts in both the ab plane and c-axis; x ≤ 1 compounds are normal ferroelectrics (FE) with decreasing T C as x increases, while x ≥ 2 are relaxor ferroelectrics (RFE) with associated frequency dependent permittivity peaks and with similar T m and T f (Vogel-Fulcher freezing temperatures) values. This observation is rationalised by differing cation occupancies: for x ≤ 1, Sr 2+ principally occupies the A2-site (co-occupied by Ba 2+ with the A1-site occupied by Dy 3+ and vacancies); for x ≥ 2 significant Sr A1-site occupation leads to the observed RFE characteristics. This FE to RFE crossover is consistent with a previously proposed TTB crystal chemical framework where both a decrease in average Asite size and concurrent increase in A1-site tolerance factor (t A1 ) favour destabilization of long range polar order and relaxor behaviour. The effect of increasing t A1 as a result of Sr occupancy at the A1 site is dominant in the compounds reported here.
2Tetragonal tungsten bronze oxides (TTBs) are perovskite-related structures, general formula A1 2 A2 4 B1 2 B2 8 C 4 O 30 . The TTB structure is derived from the corner-sharing BO 6 perovskite network by rotation of alternate "perovskite columns" in the c-axis which breaks the degeneracy of the A-sites to form the additional A2-and C-sites associated with the pentagonal and trigonal TTB-channels. The retained perovskite-like A1-sites and larger A2-sites are typically occupied by cations of large radius (e.g. Ba 2+ , Na + , Gd 3+ ) while the small C-site accommodates only small cations (e.g. Li + ) and in the majority of TTBs these are All compounds were produced using a standard solid-state method; a detailed procedure for the x = 0 composition has been reported previously. 4 Strontium compounds (x > 0) were prepared from BaCO 3 , SrCO 3 , Nb 2 O 5 , and Dy 2 O 3 (Aldrich, all > 98+ % purity) precursor powders and heated to 1000 ˚C for 2 hours, then 1250 ˚C for 15 hours followed by milling, pressing into pellets and sintering at 1350 °C for 12 hours. Additional milling and heating (1350 °C for 12 hours) was required to yield dense (> 90% theoretical density) single phase ceramics. Powder X-ray diffraction (PXRD) data were collected using a PANalytical Empyrean diffractometer. Dielectric measurements were performed with Agilent 4294A and Wayne Kerr 6500B impedance analysers with the sample mounted in a closed cycle cryocooler or tube furnace. Polarization-electric field (P-E) data were measured using an aixACCT TF2000 Analyzer.PXRD data of all compositions may be indexed to a simple TTB structure with tetragonal symmetry. For x = 3, small amounts of the Fergusonite-type phase, DyNbO 4 , 6 was detected despite additional milling and sintering steps. The DyNbO 4 was estimated to be of 2% phase fraction and 1.4 % weight fraction by Rietveld refinement using a simple t...