1. Introduction
The coexistence of superconductivity and magnetic order in the rutheno-cuprates compounds like RuSr2GdCu2O8 (Ru-1212) and their properties has been extensively studied [1] -[4] . Motivated by the discovery of high-Tc su- perconductivity in cuprates and the colossal magneto resistance effects in manganites, the research was initially focused on 3d transition-metal compounds [5] . However, as it has become increasingly clear that interesting physical phenomena of similar origin also happen in 4d and 5d electron systems, they have been getting a fair amount of attention recently. Among the 4d or 5d transition-metal compounds, ruthenium oxides probably have attracted most attention because of the discovery of superconductivity in Sr2RuO4 compound [6] and the poten- tial of unique perovskite ferromagnetic metal SrRuO3 compound [7] for thin-film applications such as tunneling magneto-resistance or ferroelectric random access memory. These ruthenites also show diverse physical proper- ties depending on the composition or crystal structures. For example, when Sr ion is replaced by Ca ion in the above-mentioned ruthenates, the metallic and magnetic properties are significantly suppressed [8] [9] . From all these studies, it becomes evident that the preparation method plays a very important role, particularly for ob- taining the different physical properties [10] . The research into electrical properties of these compounds requires very pure materials in order to optimize the particular properties of the prepared materials. In this paper, we pro- vide information about the structural, electrical and magnetic properties of the prepared samples using the stoichiometric composition of (Ca1−xSrx) RuO3 system (CSRO) for x = 0.0, 0.07, 0.10, 0.15 and 1.0.
2. Experimental Process
2.1. Synthesis
The nano-crystalline samples of the CSRO system were synthesized by solid-state reaction technique at ambient pressure. The starting materials were: RuO2 anhydrous (99.9% STREM), SrCO3 (99.5% CERAC) and CaCO3 (99.99% BAKER). The structure of each reagent was corroborated by XRD. Prior to weighing, SrCO3 and CaCO3 were pre-heated during 10 - 20 min at 120˚C, in order to be dehydrated. The stoichiometric mixture of these compounds was done in an agate mortar in air, during 15 min, resulting inhomogenous slurry. The milled polycrystals were annealed between 700˚C and 800˚C in a thermolyne 46,100 furnace (±4˚C) during two days in air, to decompose the carbonates. The resultant nano-crystals of the samples with 0 ≤ x ≤ 1.0 were compressed into pellets (diameter 13 mm thickness 1.0 - 1.5 ± 0.05 mm), by the application of a pressure of 1/4 ton/cm2 for 15 min in vacuum. Specimens compacted were sintered at 800˚C during four days in air.
2.2. Characterization
All reagents and samples were characterized by (XRD), using a Bruker-AXS D8-Advance diffractometer with λ (CuKα) = 1.54 Å radiation and graphite monocromator. Diffraction patterns were collected at room temperature on the 5˚ - 70˚ in a 2θ-range with a step size of 0.017 and time per step of 397 s. The change in morphology grain size in CSRO system obtained by different heat treatments, was observed by scanning electron microscopy (SEM) on a JOEL JSM-6610LV. The micrographs 50.00 KX, were taken with a voltage of 20 KV, current intensity of 1000 pA and WD = 10 mm. The Energy Dispersive X-Ray (EDX) was performed on the same equipment equipped with an Oxford/Link System electron probe microanalyser (EPMA). The standard four-probe method with DC resistance measurement was used as a function of temperature. The system is made up in a close-cycle refrigerator tool with conventional equipment for low-level electrical measurements. Continuous monitoring of all electrical parameters during a measurements cycle allows systematic errors in the resistance values to be detected in real-time, permitting clean R vs. T profiles to be obtained with no need of additional mathematical treatment to the experimental data [11] . The magnetization was obtained on a VSM-P525 vibrating sample magnetometer. To measure the zero field-cooled (ZFC) and the field-cooled (FC) magnetization, the samples were cooled down to 2 K at zero field and 100 Oe, respectively [12] . Then the samples were measured upon heating at 100 Oe.
3. Results and Discussion
The XRD patterns of (Ca1−xSrx) RuO3 system are shown in the Figure 1. From those spectra, samples with x = 0.07, 0.10 and 0.15 show a solubility up to x = 0.15. Meanwhile, for x = 0.0 and x = 1.0, we observed a single orthorhombic phase identified as CaRuO3 PDF (70-2790) when x = 0, and SrRuO3 PDF (70-2791), when x = 1.0 [13] [14] . The samples with x = 0.07 - 0.15 (that have not been reported before in the literature) show very weak reflections of a tetragonal secondary phase (identified as RuO2 PDF (43-1027)) [15] . In the same referred samples, the Ca ion content variation shows shifts in the peaks. Then, with the calculated lattice parameters a, b, c, and the unit cell volume (V) of each of the compounds considering the following Miller index (h k l): (4 0 0), (0 4 0) and (0 0 4), which are shown in the following Table 1, can be observed that little peaks shift.
Finally, the net lattice parameters of (Ca1−xSrx) RuO3, x = 0.0, 0.07, 0.10, 0.15 and 1.0 system vary with the inclusion of the Sr-ion content and Ru ion coordination. Since the ionic radius of Ca2+ ion (Ca2+ = 1.34 Å) is lower than the ionic radius of Sr2+ ion (Sr2+ = 1.44 Å) [16] , we conclude that the Ca ions are substituted by Sr ions with the observed unit cell variation in the volume (V) of each of the compounds, see Table 1. For the behavior of the lattice parameters, the solid solution has a substitution mechanism, where the Sr2+ ions substitute Ca2+ ions till x = 0.15. With respect to the examined diffractograms, it is worth to mention that the samples with x = 0.0 and x = 1.0 present a single orthorhombic phase identified as CaRuO3 and SrRuO3, respectively. Is other synthesis way to obtained this compounds reported in the literature, PDF (70-2790) and PDF (70-2791), with low temperature reaction. In contrast, the samples in the x = 0.07 - 0.15 range present reflections of a secondary phase identified as RuO3 [16] . That’s way the idea that the anions contributed to the formation of the mechanism of the solid solution.
The next step was the characterization of the samples achieved by SEM. The observed morphology is presented in Figure 2, shows considerable variations in sizes, very few secondary phases and shapes of particles. The grain size varies between 77 to 266 nm. The presented micrographs in the mentioned Figure 2 were taken on the surface of the representative pellets of the CSRO samples with a magnification of 50 KX. Also, in some regions we observe semi-fusion that can be attributed to the ruthenium content. We can observe the secondary phase in the other gray color.
Figure 3 shows the observed resistance of the sintered materials in relation to the temperature. All the samples of Ca1−xSrxRuO3, x = 0.0, 0.07, 0.10, 0.15 and 1.0 system show a metallic behavior. The observed resistance in CaRuO3 compound (2.009 × 10−2 Ω) is much higher than that of SrRuO3 compound (9.367 × 10−3 Ω). The
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Figure 1. XRD Patterns evolution of CSRO system.
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Table 1. Lattice parameters of CSRO system.
CaRuO3 compound does not exhibit ferromagnetism and its magnetic properties are still under discussion [17] together with long-range magnetic order. Moreover, as seen with the resistance curve, it does not present any anomaly in the measured range of temperature. The SrRuO3 compound shows long-range magnetic ordering. The slope changes of 7 to 155 K, which is called Kondo effect. The temperature at which the pronounced break occurs agrees with the reported one, where Tcurie (150 K) is related to spin scattering [18] .
In the Ca1−xSrxRuO3 samples within the range of 0.07 ≤ x ≤ 0.15, the short-range ferromagnetic interactions appear. This indicates that the ferromagnetism has been suppressed through the process of substitution of Sr2+ ions by Ca2+ ions. For the compounds with large Ca2+ ions doping (x ≥ 0.7), no clear phase transition is discerned, and
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Figure 3. Temperature dependence of resistance of Ca1−xSrxRuO3. The arrows indicate the inflexions.
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Figure 4. Magnetization measurements to 10 K ((M(T)/M(10 K)) vs curves temperature. Ca1−xSrxRuO3 samples with x = 0.07 and 0.15.
only some irreversibility is observed in the magnetization curves of these materials. The disappearance of the long-range magnetic order is commonly related to the distortion of the RuO6 octahedra associated with the partial or total replacement of Sr2+ ions by Ca2+ ions, and the corresponding narrowing of the 4d bandwidth [19] . The samples mentioned before show variations in each one of the profiles. This is because each one has a different chemical composition. Therefore, we can even observe that the resistance of the samples is due to the partial or total composition of Ca2+ ions. Since the substitution of Ca2+ ions for Sr2+ ions introduces and induces the local distortion in the vicinity of calcium ions [20] changing the Ru-O-Ru bond angle and the bandwidth, which weakens the ferromagnetism.
However, for Ca1−xSrxRuO3 (0.07 ≤ x ≤ 0.15) samples, the electrical resistance decreases with the incorporation of Sr2+ ions (2.1 × 10−3 Ω), giving less resistance than that of SrRuO3 (9.3 × 10−3 Ω). With the sample preparation described above, we did not find any superconducting phase. We observe the same behaviors that were reported for other similar compounds [7] [13] [20] - [22] .
The magnetization at 10 K for x = 0.07 and 0.15 samples are based on the application of a magnetic field of 100 Oe, as shown in Figure 4. The values Tc obtained for different samples are at a temperature of ~164 K, which is very close to those reported in the literature [6] . These samples exhibit such behavior because they have two
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Figure 5. The curves of magnetic moment (emu) vs magnetic field (Oe) of sample Ca0.93Sr0.07RuO3.
phases CaRuO3 (1 − x) + (SrRuO3) (x), not one, which explains why both samples have the same transition FM to temperature at Tc―164 K.
Finally, as shown in Figure 5, we measured the magnetic moment (emu) vs. the magnetic field (Oe) for the x = 0.07 sample. This sample has a magnetization applied by a high field at 10 K, whereas at 300 K, it does not present magnetization. A narrow hysteresis involves a small amount of energy dissipated repeatedly, reversing the magnetization. This material could be useful in transformers and other devices for alternating current, where a zero hysteresis would be optimal.
4. Conclusion
In this work, we obtained nano-crystalline samples of CSRO system by solid-state reaction in air at room temperature, in which a solubility up to x = 0.15 was observed. The SEM micrographs exhibit an almost-spherical grain size distribution from 77 to 266 nm. We also observed that the compounds of the CSRO system exhibit metallic behavior. However, for x = 0.07 and 0.15, the samples exhibit a FM transition to temperature Tc at ~164 K, indicating that the transition temperature decreases with increasing Sr ions concentration. Finally, we found that the x = 0.07 sample has a magnetization at temperature of 10 K, whereas at 300 K the sample does not present a hysteresis behavior.
Acknowledgements
This work was partially supported by CONACYT-80380, UNAM-IN109308.
NOTES
*Corresponding author.