Structural, superconducting and magnetic parameters of (Y1−xSmx)SrBaCu3O6+z.
We report here the preparation, X-ray diffraction with Rietveld refinement, AC magnetic susceptibility (χac = χ′ + iχ″), resistivity, iodometric measurements and effect of heat treatments in (Y1−xSmx)SrBaCu3O6+z. Each sample has undergone two types of heat treatment: oxygen annealing [O] and argon annealing followed by oxygen annealing [AO]. For each x, the [AO] heat treatment increases the orthorhombicity ε = (b − a)/(b + a) (for 0 ≤ x ≤ 1), Tc (for x ≥ 0.4) and reduced the linear resistivity parameters with a diminution of the interaction of holes with phonons. At all T < Tc and for any applied field Hdc, we observed an enhancement of AC magnetic shielding and the irreversibility line in the samples [AO] for x > 0.5, revealing an improvement in the pinning properties. Remarkable correlations were found. In the [AO] samples, the measured data are explained by the increase in phase purity, in cationic and chain oxygen ordering, psh and the decrease in d[Cu(1)─(Sr/Ba)].
- chain oxygen order-disorder
- heat treatments control of Tc
- Rietveld refinement structure
- phase transition
- irreversibility line
- AC magnetic shielding
- (Y1−xSmx)(SrBa)Cu3O6+z type-II superconductors
YBa2Cu3O6.95 is superconducting below 92 K and characterized by double Cu(2)O2 layers (oriented along the a-b plane) responsible for carrying the supercurrent and Cu(1)O chains (along the b direction) that provide a charge reservoir for these planes [1, 2].
The four distinct crystallographic sites Y, Ba, Cu plane, and Cu chain can be substituted with different elements. Single-phase LnBa2Cu3O6+z (Ln = rare earth) can be synthesized with Tc = 92 K. All these compounds show an orthorhombically distorted oxygen-deficient triple-perovskite structure and both the orthorhombic distortion and Tc depend sensitively on the oxygen content (6 + z) . Wada et al. , Izumi et al.  studied the structural and superconducting properties of La1+xBa2−xCu3Oy (with 0 ≤ x ≤ 0.5). They concluded that in order to have Tc maximal, this structure must have an ordered arrangement of La and Ba along c axis with an occupation factor of 0 and 1 for the oxygen at (1/2, 0, 0) and (0, 1/2, 0), respectively.
We want to see if an isovalent substitution of Ba+2 by Sr+2 with smaller ionic radius can modify the results discussed above when Y+3 is replaced by the rare earth Sm+3 with bigger ionic radius. Understanding the effect of the Y and Ba atomic plans on the superconductivity in these compounds, we have studied the structural, superconducting and magnetic properties of (Y1−xSmx)SrBaCu3O6+z. We found that the effect of heat treatments on these properties depended on the content of Sm.
2. Experimental techniques
We prepared the polycrystalline samples by solid-state sintering of oxides (Y2O3, Sm2O3, CuO) with a purity of 99.999% and carbonates (SrCO3 99.999% pure, BaCO3 with a purity of 99.99%). All these chemicals were thoroughly mixed in desired proportions and calcined at 950°C in air for 12–18 h. The obtained ceramic was ground, mixed, pelletized and heated in air at 980°C for 16–24 h. This was repeated twice. For each sample, the circular pellets were subjected to heat treatment in oxygen at 450°C for 60–72 h and furnace cooled. This was denoted as sample [O].
X-ray diffraction spectra of the samples were measured with Philips diffractometer fitted with a secondary beam graphite monochromator and using Cu Kα (40 kV/20 mA) radiation. The angle 2θ was varied from 20° to 120° in steps of 0.025°and the counting time per step was 10 s. The XRD spectra were resolved with Rietveld refinement.
A detailed description of the basic arrangement of the experiment of the AC magnetic susceptibility can be found in . The sample in the form of a slab is placed in the magnetic field Hext = Hdc + Hac cos(ωt) with the static component Hdc and the AC component with the amplitude Hac and the frequency f = ω/2π. The sample’s magnetic response was detected by a pick-up coil surrounding the sample. Superconducting transitions were determined by the measure of the real (χ′) and the imaginary (χ″) parts of the AC magnetic susceptibility as a function of temperature in Hac = 0.11 Oe and at f = 1500 Hz. Also, χ′ and χ″ were measured in 0 < Hdc < 150 Oe with applied Hac.
We used the Van Der Pauw method  for measuring resistivity ρ(T). The sample was attached to a cane in a cryostat with closed helium circuit with a cryogenic pump, a regulator of temperature (1 μA–10 mA) and 1 μV resolution digital voltmeter controlled with a computer. Tc was determined by both the measured χ′(T) and ρ(T).
For each x, the same sample [O] was then heated in argon at 850°C for about 12 h, cooled to 20°C and oxygen was allowed to flow instead of argon and the sample was annealed at 450°C for about 72 h. This sample is denoted as [AO]. XRD, resistivity and AC susceptibility measurements were done on a part of this sample. We measured 6 + z by iodometry technique on a part of each sample.
3.1. Crystalline structure
The X-ray diffraction spectra of all the samples are shown in Figure 1 . After the [AO] heat treatment, the reflections were sharper so the samples were well crystallized. The [AO] heat treatment increases the orthorhombic cleaving. For example, the (123) and (213) peaks at 2θ ≈ 58.5° (and (200) and (006) reflections at 2θ ≈ 47°) which were ill-resolved for the [O] samples were clearly identified after the [AO] heat treatment, as shown in Figure 1. Some weak unidentified impurity peaks (marked by crosses in Figure 1(a) were seen in the [O] samples and their amplitudes increase with x. They disappeared after the [AO] treatment shown in Figure 1(b). This indicates an improvement of crystallographic quality of the samples [AO].
In Figure 2 we show, respectively, the variation of the parameters a, b, c and the volume V of the unit cell obtained with Rietveld refinement  as a function of x and heat treatment. When x increases, the lattice parameter a (c and the volume V of the unit cell) increased but b is constant leading to a decrease of the orthorhombicity (ε = (b − a)/(b + a)) ε [O] in Figure 3. The substitution of Y+3 (0.893 Å) by the rare earth Sm+3 (0.965 Å), with a superior ionic radius, leads to a linear increase of c and V.
The orthorhombicity depends strongly on the Sm content x. When x increases from 0 to 1, ε decreases quickly from 8.24 × 10−3 to 1.5 × 10−3 in the samples [O] in Figure 3. This indicated a structural phase transition from orthorhombic to tetragonal. ε decreases slowly from 9.9 × 10−3 to 5.24 × 10−3 with an orthorhombic symmetry in the samples [AO]. We found also that the orthorhombicity depends strongly on the heat treatment [AO]. For each x, the latter increased the orthorhombicity (for 0 ≤ x ≤1). The increase was maximum, from 1.5 × 10−3 to 5.24 × 10−3 for x = 1 in .
3.2. Real part of the AC magnetic susceptibility and Tc
The critical temperature Tc of the transition from the superconductor to the normal state depends strongly on the effect of [AO] heat treatment as seen in the real part of AC susceptibility χ′(T) in Figure 4. The imaginary part of AC susceptibility χ″(T) in Figure 4 shows a single peak Tp. This defined clearly the value of Tc for all the samples. We can see in Figure 5 that when x was increased from 0 to 1, Tc[O] decreased from 83 K to 79.3 K. Tc[AO] first decreases from 81.7 K (for x = 0) to 81.2 K (for x = 0.2) (like in the samples [O]) and then increases to 85 K for SmSrBaCu3O6+z. For each x, the [AO] heat treatment increases Tc for x ≥ 0.4 and decreases it for x < 0.4. A maximum of increase in Tc of 6 K was observed in SmSrBaCu3O6+z [AO] .
For each x, the [AO] heat treatment increases ε (for 0 ≤ x ≤ 1) in Figure 3 and Tc (for x ≥ 0.4) in Figure 5. The [AO] heat treatment makes the coupling of the superconducting grains by Josephson junctions took place at higher temperature. This effect is revealed by the net displacement of Tp to higher temperature for x ≥ 0.4.
Table 1 shows the exact measured values of the structural parameters a, b, c, V and ε of each sample as a function of the heat treatment.
3.3. Real part of the AC magnetic susceptibility and the shielding effect
The effect of [AO] heat treatment on Tc was remarkable. The temperature at which the diamagnetism sets in is taken as Tc and it was found to be dependent on both x and the heat treatment employed. Since the same sample was used for both heat treatments, one can compare the diamagnetic response and note that screening current of the [AO] sample increased considerably compared to that of the [O] sample for each x (see, for example, the case x = 0.8 in Figure 6(a)). Table 1 shows the exact measured values of the superconducting parameters Tc, Tp, ΔTc and ΔTp of each sample as a function of the heat treatment.
We can see in Figure 7 the shielding effect S which is the amplitude of the real part of the AC susceptibility [10, 11, 12]. S represents the exclusion of the magnetic flux by the sample in alternative dynamic mode. S was set arbitrarily equal to 0.89, 0.97 and 1, respectively, for x = 0.5, 0.8, and 1, for the sample [AO] at 55 K and for Hdc = 0 Oe.
For each x > 0.5, the [AO] heat treatment increases the shielding effect at all T < Tc and for any applied Hdc. For example, in SmSrBaCu3O6+z (x = 1), S[AO] = 2 S[O] at T = 65 K and Hdc = 126.5 Oe . When Hdc increases, S[AO] decreases slowly than S[O]. For example, at T = 55 K, S[AO] decreases by 10% whereas S[O] decreases by 70%. This indicated an improvement of the quality of the grains and intergranular coupling in the samples [AO].
3.4. Imaginary part of the AC magnetic susceptibility and irreversibility line
Looking to the imaginary part of the AC susceptibility χ″, of the sample Y0.2Sm0.8SrBaCu3O6+z in Figure 6(b) for example, we can see that the width ΔTp at half maximum of the transition in χ″(T) (see Table 1) was smaller in the samples [AO] at all Hdc and the peak Tp shifted less than in the sample [O]. Figure 8 shows the field Hdc as a function of t = Tp/Tc with an enhancement of the irreversibility line due to argon treatment for x ≥ 0.5 . The data can be analyzed with the help of following relation H = K′ (1 − t)n . Straight line plots were obtained when ln(H) was plotted against ln(1 – t) in Figure 9. For example, the value of K′ was estimated to be 1677 and 11,741 Oe, respectively, for the samples [O] and [AO] in SmSrBaCu3O6+z (x = 1). K′ may be interpreted as the field necessary to reduce the intergranular critical current to zero in the limit of Tp = 0 K. We note that the argon treatment considerably increases the value of K′ and n, in Table 1 and Figure 10, indicating an improvement in the pinning properties. The dashed line indicates the value n = 1.5 for the cuprites given by Miller et al. .
Figure 11 shows that the resistivity ρ(T) of the sample SmSrBaCu3O
We saw that the [AO] heat treatment increases the orthorhombic cleaving and eliminated some weak unidentified impurity peaks in Figure 1(b). This indicates a good crystallization and an improvement of crystallographic quality of the samples [AO].
Our samples were prepared in 1 atm of oxygen. Our iodometry measurements show that the total oxygen constant was 6 + z = 6.94 ± 0.04 and do not change after the [AO] heat treatment. But for each x, Tc[AO] increased for x ≥ 0.4. So this increase is not due to z but may lie in some other factor which governs the superconductivity in these samples.
When x increases from 0 to 1, Tc[O] decreases with ε. Tc[AO] decreases with the orthorhombicity ε until x = 0.2 and afterward it increases from 79 to 85 K in SmSrBaCu3O6+z [AO], as shown in Figure 12. When x increases, the parameter b is constant but a (and c) increase indicating an increase of the number of oxygen atoms by chain (NOC) along a axis with a decrease of ε (Tc[O]) from orthorhombic toward tetragonal structure in SmSrBaCu3O6+z [O].
For each x, the [AO] treatment increases the orthorhombicity ε (for 0 ≤ x ≤ 1) and Tc (for x ≥ 0.4). For each x, the parameter a decreases and b increases after the [AO] heat treatment in the unit cell of Figure 2. Some oxygen atoms O(4) go to the vacant site O(5) along b axis. So the (NOC) and the anionic order in the basal plane increases leading to an increase of psh and Tc for x ≥ 0.4 in Figure 15.
For each x ≥ 0.4, the thermal parameter of the apical oxygen O(1) decreased from 2.02 to 0.27 Å2 in the sample [AO] leading to a decrease of the cationic disorder; of Y (0.893 Å) (or Sm (0.965 Å) occupying some Ba (1.42 Å)/Sr (1.12 Å) sites along the c axis. Each sample [O] was heated in argon at 850°C. This action removes all the oxygen atoms from the structure and increases the atomic diffusion and the Y/Sm-Sr/Ba-Y/Sm order along c axis in the unit cell of Figure 2. In fact, the difference of bond valence (B.V.S.): V(Y)-V(Ba) = 0.77 in YBa2Cu3O6.7 and 1.00 in YBa2Cu3O6.32 indicate that the departure from reduced (6 + z) decreases the disorder of Y on the Ba site in YBa2Cu3O6+z . So, the argon heat treatment decreases the disorder of Y/Sm on the Ba/Sr site. This is justified by the fact that impurity peaks seen in the [O] samples in Figure 1(a) disappeared after the [AO] heat treatment in Figure 1(b).
Our results can be explained by the disorder of the oxygen in the basal plane, on the 0(4) and 0(5) sites along b and a axis, respectively, in Figure 2. This order enhanced the orthorhombic symmetry and increased the ratio (b − a)/(b + a). As seen on Figure 13 when x increases, the interatomic distance d[Cu(1)─(Sr/Ba)] increases for both heat treatments in agreement with the fact that the crystallographic parameter c and the volume of the unit cell increases with x. For each x, the [AO] heat treatment decreases this distance for x ≥ 0.5 (and increases it for x < 0.5). This decreases the distance d[Cu(1)─O(1)] and enhances the transfer of holes from the Cu(1)O chains to the superconducting planes Cu(2)O2 via the apical oxygen O(1) resulting in an increase in the hole density psh and Tc for x ≥ 0.4 in Figure 15. Such an increase leads to optimum superconducting properties and could account for the observed increase in Tc[AO] in agreement with the model of transfer of charges. This is justified by the fact that, when x increases, the parameter b is constant but a (and c) increase leading to an increase of the number of oxygen atoms by chain (NOC) along a axis with a decrease of ε (Tc[O]) from orthorhombic toward tetragonal structure in Figure 12.
When Sm ion occupies Ba (or Sr) site, the same amount of Ba (or Sr) cation is pushed into Y site. Sm is a three-valence ion. It increases the positive charge density around Ba (or Sr) site and the attractive force with oxygen anion. As a result, oxygen vacancies O(5) along the a-axis in the basal plane have higher chance to be filled. On the other hand, Ba+2 (or Sr+2) in Y+3 (or Sm+3) site decrease the attractive force with oxygen anion in Cu(2) plane. This increases the buckling angle Cu(2)─O(3)─Cu(2) along the a axis. When x increased from 0 to 1, the two changes of cation sites increase the parameter a. For each x, the [AO] heat treatment decreases the parameter a and increases b as shown in Figure 2. This increases the number of oxygen atoms by chain (NOC) along b axis leading to an increase of Tc with a decrease of the orthorhombicity ε for x ≥ 0.2 as seen in Figure 12.
In the normal state, the heat treatment [AO] reduced considerably the linear resistivity parameters indicating a diminution of the interaction of carrier charges with phonons. Tc(χ′) and Tc(ρ = 0) were in good agreement.
For each x > 0.5, the [AO] heat treatment improved the shielding effect at all T < Tc and for any applied field indicating an enhancement of the quality of the grains and intergranular coupling in the samples [AO]. Also for x ≥ 0.5, an enhancement of the irreversibility line was noticed in the samples [AO] with an increase of the field K′ showing an improvement in the pinning properties. These results are justified by our XRD spectra, with Rietveld refinement, that showed an improvement of crystallographic quality of the samples [AO] in Figure 1.
The two arguments (cationic and anionic disorders) are justified here by the four remarkable correlations observed between Tc(x), the volume of the unit cell V(x) in Figure 14 and the number psh(x) of holes by Cu(2)─O2 superconducting planes in Figure 15 (deduced from the undersaturation zone of the universal relation Tc/Tcmax (psh) ), and on the other hand, between δTc(x) = Tc[AO] − Tc[O] and δε(x) in Figure 16 and between δTc(x) and δK′(x) in Figure 17. So the structural, electrical and superconducting properties are correlated with the effect of argon heat treatment.
The increase or decrease in Tc must be related to the ionic size of the rare earth Sm, the variation of the Cu(1)-apical oxygen distance, hole density, anionic and cationic disorders, etc.
These studies indicate the optimization of the superconducting properties of the high-Tc superconductors (Y1−xSmx)SrBaCu3O6+z by a simple argon heat treatment. These results are a competition between oxygen disorder in basal plane and cationic disorder along c axis. In the samples [O], we are in the presence of a cationic disorder of Y/Sm on (Sr/Ba) sites that induced an anionic disorder of oxygen’s chains in basal plane. Anionic order dominates in the samples [AO] in agreement with the previsions of [4, 5]. In the samples [AO], the remarkable improvement in the shielding effect (for x > 0.5) and the irreversibility line (for x ≥ 0.5) are explained, respectively, by the improvement of the quality of the grains and intergranular coupling, and to the improvement of the pinning properties and crystallographic quality of these samples. The structural, magnetic and superconducting properties are correlated with the effect of argon heat treatment.
These results were explained by the effect of the ionic size of the rare earth, the decrease in d[Cu(1)─(Sr/Ba)]; the increase in cationic and chain oxygen ordering; the number of holes psh(x) by Cu(2)─O2 superconducting plans and in phase purity for the [AO] samples.
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