Correlation between Crystal Structure and Thermoelectric Properties of Sr 1 − x Ti 0.9 Nb 0.1 O 3 − δ Ceramics

: Polycrystalline Sr 1 − x Ti 0.9 Nb 0.1 O 3 − δ (x = 0, 0.1, 0.2) ceramics have been prepared by the solid state method and their structural and thermoelectric properties have been studied by neutron powder di ﬀ raction (NPD), thermal, and transport measurements. The structural analysis of Sr 1-x Ti 0.9 Nb 0.1 O 3 − δ (x = 0.1, 0.2) conﬁrms the presence of a signiﬁcant amount of oxygen vacancies, associated with the Sr-deﬁciency of the materials. The analysis of the anisotropic displacement parameters (ADPs) indicates a strong softening of the overall phonon modes for these samples, which is conﬁrmed by the extremely low thermal conductivity value ( κ ≈ 1.6 W m-1 K − 1 at 823 K) found for Sr 1 − x Ti 0.9 Nb 0.1 O 3 − δ (x = 0.1, 0.2). This approach of introducing A-site cation vacancies for decreasing the thermal conductivity seems more e ﬀ ective than the classical substitution of strontium by rare-earth elements in SrTiO 3 and opens a new optimization scheme for the thermoelectric properties of oxides.


Introduction
Thermoelectric (TE) materials enable direct conversion of waste heat into electrical energy, or vice versa; they can pump heat by using electricity through the thermoelectric effect. By exploiting these properties, thermoelectric device applications are concerned with power generation and environmental-friendly refrigeration [1][2][3][4][5]. Despite the significant benefits of thermoelectric devices, such as low cost electricity, green energy technology without using any moving part, stability, and reliability, the correct performance largely depends on the material efficiency [6]. This efficiency may be evaluated in terms of the figure of merit (zT) (Equation (1)):

Materials and Methods
Samples of composition Sr 1−x Ti 0.9 Nb 0.1 O 3−δ (x = 0, 0.1, 0.2) were prepared by a conventional solidstate reaction. Stoichiometric amounts of SrCO 3 (>99.9%, Sigma-Aldrich, Merck KGaA, Darmstadt, Germany), TiO 2 (>99.995%, Sigma-Aldrich, Merck KGaA, Darmstadt, Germany), and Nb 2 O 5 (>99.99%, Sigma-Aldrich, Merck KGaA, Darmstadt, Germany) were heated at 1000 • C for 6 h in air. The resulting powders were then ground in a mortar and heated again under the same conditions. Finally, the powder was calcined at 1400 • C for 5 h in 5% H 2 /95% N 2 . The use of this reducing atmosphere allows the reduction of part of Ti 4+ to Ti 3+ , which dramatically affects the thermoelectric properties. For this reason, the sintering of 10 mm diameter pellets was carried out under the same conditions (1400 • C, 5 h, 5% H 2 ).
Phase characterization was achieved using temperature-dependent NPD data collected at the D2B diffractometer of the ILL (Grenoble), with wavelengths λ = 1.051 or 1.594 Å. An amount of 2 g of the sample were packed in a cylindrical vanadium holder (dia. 8 mm), and the counting time was 2 h in the high-intensity mode. The coherent scattering lengths for the elements contained in the sample are: Sr (7.02 fm), Ti (−3.438 fm), Nb (7.054 fm), and O (5.803 fm) [33]. The Fullprof software was used to refine the structure [34]. The refinement was carried out with no regions excluded from the data. The zero-point error, scale factor, background coefficients, pseudo-Voigt shape parameters, occupancy of the elements, atomic coordinates, and anisotropic displacements for all the atoms were refined.
The Seebeck coefficient was determined by using a commercial MMR-technologies system (MMR Technologies Inc, San Jose, California, USA). Measurements were completed under vacuum conditions (10 −3 mbar) from 300 to 800 K. A constantan wire was utilized as a reference for comparison with bar-shaped samples, previously cut with a diamond saw perpendicular to the pressing direction. Reproducibility was tested with different contacts and constantan wires.
The thermal diffusivity (α) of Sr 1−x Ti 0.9 Nb 0.1 O 3−δ (x = 0, 0.1, 0.2) samples was measured from 300 to 800 K using a Linseis LFA 1000 instrument (Linseis Messgeraete GmbH, Selb, Germany). In order to maximize the heat absorption and emissivity of the sample, a thin graphite coating was applied to the surface of the pellet. The thermal conductivity (κ) was calculated by κ = αC p d, where C p is the specific heat and d is the sample density. Specific heat was calculated using the well-known Dulong-Petit equation.

Structural Characterization by Neutron Powder Diffraction (NPD)
The determination of O positions in perovskite oxides containing heavy elements such as Sr is difficult by X-ray diffraction, given the weak scattering factor for O 2− ions; hence neutron diffraction measurements are crucial. In addition to that, our aim was to determine anisotropic displacement factors (ADPs) that may give hints to account for the exceptionally low thermal conductivities observed here. An NPD study for a selected Sr 0.9 (Ti 0.9 Nb 0.1 )O 3−δ sample at RT (25 • C) and elevated temperatures up to 800 • C was essential to unveil these features, allowing to microscopically determine the oxygen contents in oxygen deficient specimens. A short neutron wavelength (λ = 1.051 Å) was chosen to access a wide region of the reciprocal space. The RT neutron pattern confirms the cubic symmetry with unit-cell parameter a = 3.91726(4) Å; the structure was therefore defined in the cubic Pm-3m space group with Sr located at 1b Wyckoff site ( 1 2 , 1 2 , 1 2 ); Ti and Nb distributed at random at 1a (0,0,0) site; and O1 at 3d(1/2,0,0). The Ti vs. Nb and O1 occupancies were refined, yielding a crystallographic formula at RT Sr 0.9 Ti 0.88(1) Nb 0.12(1) O 2.85 (4) , showing a significant oxygen deficiency. The anisotropic displacement Crystals 2020, 10, 100 4 of 12 factors of O1 were also refined. The Ti/Nb rate is similar to that expected, while the oxygen positions show a conspicuous nonstoichiometry. For the determined occupancy factors, the mean oxidation state of Ti is 3.75+. The final structural parameters and agreement factors are gathered at Table 1 for this perovskite oxide at RT. The structural refinement from data collected above RT (300, 600, 800 • C) was correctly performed in Pm3m; the corresponding structural parameters are listed in the Supplementary Materials. The good agreement between observed and calculated profiles is displayed in Figures 1a  and 1b for the 25 and 800 • C patterns, respectively. Crystals 2020, 10, x FOR PEER REVIEW  4 of 13 occupancy factors, the mean oxidation state of Ti is 3.75+. The final structural parameters and agreement factors are gathered at Table 1 for this perovskite oxide at RT. The structural refinement from data collected above RT (300, 600, 800 °C) was correctly performed in Pm3 m; the corresponding structural parameters are listed in the Supplementary Materials. The good agreement between observed and calculated profiles is displayed in Figure 1a and Figure 1b for the 25 and 800 °C patterns, respectively.  Figure 2 illustrates the cubic crystal structure at 800 °C, displaying a remarkable anisotropy in the disk-shaped (oblate) displacement ellipsoids for oxygen atoms. Figure 3 displays the thermal variation of the unit-cell volume of the perovskite oxide; the inset shows the Uij thermal displacement across the measured temperature range. For the cations (Sr, Ti, Nb) the thermal displacement parameters are constrained, by symmetry, to be spherical. For oxygen atoms at 800 °C, the anisotropic ellipsoids exhibit the root mean square (rms) displacements of 0.18 Å perpendicular to the Ti-Ti distance and 0.11 Å parallel to it. This suggests that the thermal vibrations are mainly permitted in a perpendicular direction to the covalent Ti(Nb)-O-Ti(Nb) chemical bonds, as usual in many perovskite-like oxides.   Figure 2 illustrates the cubic crystal structure at 800 • C, displaying a remarkable anisotropy in the disk-shaped (oblate) displacement ellipsoids for oxygen atoms. Figure 3 displays the thermal variation of the unit-cell volume of the perovskite oxide; the inset shows the U ij thermal displacement across the measured temperature range. For the cations (Sr, Ti, Nb) the thermal displacement parameters are constrained, by symmetry, to be spherical. For oxygen atoms at 800 • C, the anisotropic ellipsoids exhibit the root mean square (rms) displacements of 0.18 Å perpendicular to the Ti-Ti distance and 0.11 Å parallel to it. This suggests that the thermal vibrations are mainly permitted in a perpendicular direction to the covalent Ti(Nb)-O-Ti(Nb) chemical bonds, as usual in many perovskite-like oxides.

Fractional Atomic Coordinates and Isotropic or Equivalent Isotropic Displacement Parameters (Å 2 )
x y z U iso */U eq Occ. ( Regarding Sr 0.8 (Ti 0.9 Nb 0.1 )O 3-δ , a NPD pattern was collected at RT with λ = 1.594 Å. The crystal structure was refined in the Pm-3m space group as described above. This time a minor impurity of TiO 2 (rutile) was detected and introduced as a second phase in the refinement. The limited number of diffraction peaks obtained with this longer wavelength did not allow the anisotropic refinement of oxygen displacement factors. The mixed Ti vs. Nb and O occupancy were refined yielding the crystallographic composition Sr 0.8 Ti 0.875(3) Nb 0.125(3) O 2.50 (2) , showing an important oxygen deficiency, associated with the Sr deficiency. For the determined occupancy factors, the oxidation state of Ti is 3.16+ (assuming pentavalent Nb). The final structural parameters and the refinement agreement factors are listed in Table 2 for this perovskite oxide at room temperature. The excellent agreement between observed and calculated profiles is displayed in Figure 4. Regarding Sr0.8(Ti0.9Nb0.1)O3-δ, a NPD pattern was collected at RT with = 1.594 Å. The crystal structure was refined in the Pm-3m space group as described above. This time a minor impurity of TiO2 (rutile) was detected and introduced as a second phase in the refinement. The limited number of diffraction peaks obtained with this longer wavelength did not allow the anisotropic refinement of oxygen displacement factors. The mixed Ti vs. Nb and O occupancy were refined yielding the crystallographic composition Sr0.8Ti0.875(3)Nb0.125(3)O2.50 (2), showing an important oxygen deficiency, associated with the Sr deficiency. For the determined occupancy factors, the oxidation state of Ti is 3.16+ (assuming pentavalent Nb). The final structural parameters and the refinement agreement factors are listed in Table 2 for this perovskite oxide at room temperature. The excellent agreement between observed and calculated profiles is displayed in Figure 4.

Analysis of the Anisotropic Displacement Parameters (ADPs)
The ADPs of the various atoms of the structure can give important insight into their vibrations. We analyze the mean square displacements (MSD), which are the main semi-axes of the ellipsoids described by the ADPs (basically the Uiso/Uij of Tables 1 and 2), following the treatment by Mi et al.

Analysis of the Anisotropic Displacement Parameters (ADPs)
The ADPs of the various atoms of the structure can give important insight into their vibrations. We analyze the mean square displacements (MSD), which are the main semi-axes of the ellipsoids described by the ADPs (basically the U iso /U ij of Tables 1 and 2), following the treatment by Mi et al. [35]. The Debye temperature (θ D ) can be obtained from Equation (2): where U iso is an atomic-mass weighted average obtained from the U iso of Table 1, taking into account each occupancy, too. The m is an averaged mono-atomic mass for the unit cell, and d D describes additional site-disorder. A least-squares fit yields θ D = 452 K, with a negligible d D~0 .013 Å (inset Figure 3). This low value of the Debye temperature suggests a softening of the phonon-modes in A-site cation deficient Nb:STO.  [27] demonstrated that Nb-doped SrTiO 3 compositions are donor-doped perovskites. A donor dopant has higher cationic charge than the host cation that it replaces. In the case of Sr 0.9 Ti 0.9 Nb 0.1 O 3-δ , the Nb 5+ is substituting and reducing part of Ti 4+ and is thus trying to bring either more oxide ions or more electrons into the structure [27]. On the other hand, the introduction of vacancies in the A-site perovskite position alters the charge compensation by electronic species and cation vacancies and therefore modifies the electronic properties of the system. Our NPD data clearly show that the effect of electron doping brought about by the conspicuous oxygen deficiency compensates the hole-doping effect induced by Sr vacancies, yielding a net oxidation state for Ti lower than 4+, i.e., injecting electrons into the system. Figure 5a shows the evolution of the Seebeck coefficient with temperature for the three compositions. S(T) is negative, indicating n-type electrical transport. For SrTi 0.9 Nb 0.1 O 3−δ , there is a slight increase of the absolute value of the Seebeck coefficient between room temperature (S = -90 µV K −1 ) and 723 K (S = -137 µV K −1 ). However, samples containing A-site cation vacancies, present a value of S(T) that remains almost constant with temperature up to 723 K. It is worth noting that the Seebeck coefficient is improved by A-site cation deficiency, reaching a maximum value of S(T) = -163 µV K −1 at room temperature for Sr 0.8 Ti 0.9 Nb 0.1 O 3−δ. These measurements are in good agreement with the results found by Kovalevsky et al. [36]. In a typical semiconductor, one can expect a decrease in Seebeck coefficient when increasing the charge carrier concentration, but in this system, this variation would be attributed to a combined result of the presence of defects. Concerning the electrical resistivity (Figure 5b), there is a slight decrease with temperature for the three samples. Sr 1−x Ti 0.9 Nb 0.1 O 3−δ have similar resistivities for x = 0 and 0.1 (ρ ≈ 9 × 10 −3 Ω m at RT and ρ ≈ 8 × 10 −4 Ω m at 780 K). However, upon introducing the highest concentration of vacancies (x = 0.2), the electrical resistivity abruptly rises (ρ ≈ 0.18 Ω m at room temperature and ρ ≈ 7 × 10 −3 Ω m at 780 K). This undesirable increase of the electrical resistivity could be related to the presence of TiO 2 as minor phase and the large amount of oxygen vacancies, as determined from NPD data, which perturb the Ti-O-Ti paths that permit the electronic conduction in these materials, despite the nominal oxidation state of this perovskite, well below 4+. A high level of donor substitution could drive to a notable number of planar defects, which may induce localization of electronic charge carriers, increasing the Seebeck coefficient and the electrical resistivity [36]. Other authors suggest the instability of the fraction of Ti +3 ions that become easily oxidized to Ti 4+ [37], thus diminishing the related electrons in the conduction band. As a result, the highest power factor (S 2 ρ -1 ) at room temperature was found for Sr 0.9 Ti 0.9 Nb 0.1 O 3−δ (PF = 0.019 mW m −1 K −2 ) (Figure 5c). of oxygen vacancies, as determined from NPD data, which perturb the Ti-O-Ti paths that permit the electronic conduction in these materials, despite the nominal oxidation state of this perovskite, well below 4+. A high level of donor substitution could drive to a notable number of planar defects, which may induce localization of electronic charge carriers, increasing the Seebeck coefficient and the electrical resistivity [36]. Other authors suggest the instability of the fraction of Ti +3 ions that become easily oxidized to Ti 4+ [37], thus diminishing the related electrons in the conduction band. As a result, the highest power factor (S 2 ρ -1 ) at room temperature was found for Sr0.9Ti0.9Nb0.1O3−δ (PF = 0.019 mW m −1 K −2 ) (Figure 5c). Power factors of Sr1-xTi0.9Nb0.1O3−δ (x = 0, 0.1) at higher temperatures (723 K) are comparable, due to the similar Seebeck coefficient and resistivity, reaching values of 0.025 and 0.022 mW m −1 K −2 for Sr0.9Ti0.9Nb0.1O3-δ and SrTi0.9Nb0.1O3−δ, respectively.  Temperature dependence of the thermal conductivity (κ) is represented in Figure 6a. The relative density of the three studied samples was ≈ 90%; this means that the differences between the compounds' thermal conductivity cannot be associated with porosity.

Thermoelectric Properties
Total thermal conductivity achieved for SrTi 0.9 Nb 0.1 O 3−δ (κ ≈ 4.8 W/m K at room temperature) is in good agreement with the value found by Kovalevsky et al. [36] for SrTi 0.8 Nb 0.2 O 3−δ (κ ≈ 5.6 W m −1 K −1 at room temperature). However, an impressive reduction of the thermal conductivity is observed when vacancies are introduced in the perovskite structure, finding room temperature values of κ ≈ 2.7 W m −1 K −1 (reduction of 44%) and ≈2.3 W m −1 K −1 (reduction of 52%) for Sr 0.8 Ti 0.9 Nb 0.1 O 3−δ and Sr 0.9 Ti 0.9 Nb 0.1 O 3-δ , respectively. This reduction of κ is observed for all the measured temperature range, leading to a total thermal conductivity value κ ≈1.6 W m −1 K −1 at 823 K for Sr 1−x Ti 0.9 Nb 0.1 O 3−δ (x = 0.1, 0.2). This approach for reducing thermal conductivity seems more effective than the classical introduction of rare-earth elements in the A-site of the perovskite, where thermal conductivity values between 3-4 W m −1 K −1 at 823 K are achieved for Sr 1−x RE x TiO 3 (RE = La, Nd, Sm, Gd, Dy) [38,39].
The electronic (κ e ) and lattice (κ L ) dependence of the thermal conductivity is represented in Figure 6b. The electronic thermal conductivity contribution was calculated using the well-known Wiedemann-Franz law, which states κ e = LσT, where L is the Lorentz number (L ≈ 2·10 −8 W Ω K −2 ), σ is the electrical conductivity (σ = ρ −1 ), and T corresponds to the absolute temperature. Lattice contribution dominates the total thermal conductivity. κ L decreases monotonically with the increase of temperature for the samples, typical of semiconductors (Figure 6a). Point defects scatter optical phonons effectively, for this reason, the strontium and oxygen vacancies associated with these compounds are responsible for the decrease of the lattice thermal conductivity in these samples.
Crystals 2020, 10, x FOR PEER REVIEW 9 of 13 Temperature dependence of the thermal conductivity (κ) is represented in Figure 6a. The relative density of the three studied samples was ≈ 90%; this means that the differences between the compounds' thermal conductivity cannot be associated with porosity. Total thermal conductivity achieved for SrTi0.9Nb0.1O3−δ (κ ≈ 4.8 W / m K at room temperature) is in good agreement with the value found by Kovalevsky et al. [36] for SrTi0.8Nb0.2O3−δ (κ ≈ 5.6 W m −1 K −1 at room temperature). However, an impressive reduction of the thermal conductivity is observed when vacancies are introduced in the perovskite structure, finding room temperature values of κ ≈ 2.7 W m −1 K −1 (reduction of 44%) and ≈2.3 W m −1 K −1 (reduction of 52%) for Sr0.8Ti0.9Nb0.1O3−δ and Sr0.9Ti0.9Nb0.1O3-δ, respectively. This reduction of κ is observed for all the measured temperature range, leading to a total thermal conductivity value κ ≈1.6 W m −1 K −1 at 823 K for Sr1−xTi0.9Nb0.1O3−δ (x = 0.1, 0.2). This approach for reducing thermal conductivity seems more effective than the classical introduction of rare-earth elements in the A-site of the perovskite, where thermal conductivity values between 3-4 W m −1 K −1 at 823 K are achieved for Sr1−xRExTiO3 (RE = La, Nd, Sm, Gd, Dy) [38,39].
The electronic (κe) and lattice (κL) dependence of the thermal conductivity is represented in Figure 6b. The electronic thermal conductivity contribution was calculated using the well-known Wiedemann-Franz law, which states κe = LσT, where L is the Lorentz number (L ≈ 2•10 −8 W Ω K −2 ), σ is the electrical conductivity (σ = ρ −1 ), and T corresponds to the absolute temperature. Lattice contribution dominates the total thermal conductivity. κL decreases monotonically with the increase of temperature for the samples, typical of semiconductors (Figure 6a). Point defects scatter optical phonons effectively, for this reason, the strontium and oxygen vacancies associated with these compounds are responsible for the decrease of the lattice thermal conductivity in these samples.
As shown in Figure 6b, the lowest κL was found for Sr0.9Ti0.9Nb0.1O3−δ, (κ ≈ 2.2 W/m K at room temperature), which is reduced by ≈ 53 % compared to that of SrTi0.9Nb0.1O3−δ. Both types of vacancies, As shown in Figure 6b, the lowest κ L was found for Sr 0.9 Ti 0.9 Nb 0.1 O 3−δ , (κ ≈ 2.2 W/m K at room temperature), which is reduced by ≈ 53 % compared to that of SrTi 0.9 Nb 0.1 O 3−δ . Both types of vacancies, A-cation and oxygen vacancies, are participating in this reduction. The electronic thermal conductivity for the sample with the largest A-cation vacancies (x = 0.2) is much decreased due to the higher presence of oxygen vacancies that impair the electrical conductivity, as commented above. It seems that the optimum oxygen deficiency values are those found for the Sr 0.9 Ti 0.9 Nb 0.1 O 3-δ specimen.
The remarkable reduction of the thermal conductivity together with the maintenance of the power factor in Sr 0.9 Ti 0.9 Nb 0.1 O 3−δ results in an increase in the figure of merit ZT (improvement of 42% at 723 K), compared to SrTi 0.9 Nb 0.1 O 3−δ (Figure 7). In the case of the sample Sr 0.8 Ti 0.9 Nb 0.1 O 3−δ , although the reduction in κ is substantial, the worsening of the electronic transport properties diminishes ZT. Although the thermoelectric performance achieved for these materials is still far from the competitive values for applications, this work suggests that the adequate control of A-site cation vacancies can be a promising approach for the optimization of the thermoelectric properties in oxides.
The remarkable reduction of the thermal conductivity together with the maintenance of the power factor in Sr0.9Ti0.9Nb0.1O3−δ results in an increase in the figure of merit ZT (improvement of 42% at 723 K), compared to SrTi0.9Nb0.1O3−δ (Figure 7). In the case of the sample Sr0.8Ti0.9Nb0.1O3−δ, although the reduction in κ is substantial, the worsening of the electronic transport properties diminishes ZT. Although the thermoelectric performance achieved for these materials is still far from the competitive values for applications, this work suggests that the adequate control of A-site cation vacancies can be a promising approach for the optimization of the thermoelectric properties in oxides. . error bars of ± 15% are indicated in the graph. This is based on the addition of 5% error for the Seebeck coefficient, 5% for the thermal conductivity, and 1.5% for the electrical resistivity error (obtained after three repetitions of the measurements).

Conclusions
Sr1−xTi0.9Nb0.1O3−δ (x = 0, 0.1, 0.2) samples were synthesized by the ceramic route to study the impact of A-site cation deficiency on the thermoelectric performance. Rietveld refinements from neutron diffraction data show a substantial oxygen deficiency composition in the samples containing Sr-vacancies, giving compositions of Sr0.9Ti0.88(1)Nb0.12(1)O2.85(4) and Sr0.8Ti0.875(3)Nb0.125(3)O2.50 (2). The existence of Sr-cation and O-anion defects and the reduction of Ti 4+ to Ti 3+ in the samples, affect dramatically the electronic and thermal properties of the materials. The power factors of Sr1−xTi0.9Nb0.1O3−δ (x = 0, 0.1) samples are preserved. However, a higher concentration of vacancies (x = 0.2) results in an undesired increase of resistivity, possibly due to a perturbation of the crystallographic structure. Interestingly, a low thermal conductivity is reached for both A-site cation deficiency compositions, with a minimum value of κ ≈1.6 W m −1 K −1 at 823 K. This exceptionally low value is also in agreement with the highly anisotropic atomic displacement parameters of the oxygen, and with a strong softening of the overall phonon modes for Sr-deficient samples, shown by the decreased Debye-temperature. The outstanding reduction of the thermal conductivity in Sr-deficient samples gives clues to devise optimized thermoelectric materials based on ceramic STO-type perovskite oxides.

Supplementary Materials:
The following are available online at www.mdpi.com/xxx/s1, Table S1. Structural parameters after the Rietveld refinement of Sr0.9(Ti0.9Nb0.1)O3-δ from NPD data at 300 °C in the Pm-3m space group, a = 3.92942 (5) Å, with λ= 1.051 Å. Discrepancy factors: Rp = 2.36%, Rwp = 3.11%, Rexp = 2.03%, RBragg = 4.65, χ2 = 2.51. Table S2. Structural parameters after the Rietveld refinement of Sr0.9(Ti0.9Nb0.1)O3-δ from NPD data error bars of ± 15% are indicated in the graph. This is based on the addition of 5% error for the Seebeck coefficient, 5% for the thermal conductivity, and 1.5% for the electrical resistivity error (obtained after three repetitions of the measurements). 2) results in an undesired increase of resistivity, possibly due to a perturbation of the crystallographic structure. Interestingly, a low thermal conductivity is reached for both A-site cation deficiency compositions, with a minimum value of κ ≈ 1.6 W m −1 K −1 at 823 K. This exceptionally low value is also in agreement with the highly anisotropic atomic displacement parameters of the oxygen, and with a strong softening of the overall phonon modes for Sr-deficient samples, shown by the decreased Debye-temperature. The outstanding reduction of the thermal conductivity in Sr-deficient samples gives clues to devise optimized thermoelectric materials based on ceramic STO-type perovskite oxides.