According to the review paper, an SRO with an orthorhombic unit cell volume of 240.9 Å3 ((=3.9052 × 3.950 × 4) should have RRR ~ 20. However, in our case, RRRs were 3 and 9 for the SRO100 film and the SRO111 film, respectively. A single-crystalline SRO thin film on STO (110) substrate having an orthorhombic unit cell volume of 240.9 Å3 was reported to have RRR ~ 8 [26]. So, a simple explanation in terms of structural factor such as volume expansion is not enough to explain the different RRR values even though we accept that PLD-grown SRO films have more tendency to have larger lattice volumes and have lower RRR values. Siemons et A-1210477 clinical trial al. estimated

that the Ru vacancy concentration causing drastic change of RRR is much smaller than a few percent for the range of samples they studied, from the fact that the decrease of the Curie temperature is as small as approximately 10 K [27]. Thus, the effect of a very small amount of Ru vacancy in SRO thin films seems to be critical for RRR but should be much smaller than the effect of strain on the ferromagnetic selleck inhibitor properties [27]. This is consistent with the observation of robust low-spin configuration for nearly all thin films of SrRuO3. Figure 4b shows the temperature dependence of the magnetization at 500 Oe after high field cooling at 7 T. [The same specimen was used for these measurements by only changing the field direction with respect to the crystallographic axis - one along the HDAC assay in-plane direction, H //and the other

along the surface normal direction, H ⟂.] For the SRO111 film, the magnitude of magnetization along the surface normal direction

was larger than that along the in-plane direction. This was similar to the observations for the SRO100 film and was interpreted PD184352 (CI-1040) in terms of compressive strain [5, 6]. To estimate the changes in the ferromagnetic transition temperature, we plotted magnetization of the SRO100 film and the SRO film grown on STO (110) substrate on the same plot [7]. From Fig. 4(b), it can be seen that the ferromagnetic transition temperature of the SRO111 film is about 10 K higher than those of the SRO100 film and SRO film grown on STO (110) substrate. These increased ferromagnetic transition temperatures of films grown on a cubic (111) substrate were also reported for manganese oxide [28–30]. Figure 4c shows magnetic hysteresis curves at 5 K for applied fields along two directions. Here, we found that magnetization along the surface normal direction increased more rapidly than that along the in-plane direction. For fields along the surface normal direction, the coercive field was very well defined for both films. The coercive field for the SRO111 film was approximately 0.7 T, which was slightly larger than the value of approximately 0.5 T for the SRO100 film. Finally, we found that the saturated magnetic moments with a 6-T applied field were smaller than 2 μB/Ru. This was in contrast to the observed approximately 3.5 μB/Ru in the SRO film grown on STO (111) substrate [22].