One of the superconducting materials with high critical temperatures that have been successfully discovered is the Gd1Ba2Cu3O7−δ (GBCO-123 system) with a critical temperature of 94 K by Yamaguchi, 2014  so it is very possible to be utilized with liquid nitrogen cooling. However, the GBCO-123 superconductor has Tc and Jc which are still strongly influenced by magnetic fields . Therefore, research is still needed to improve the performance of the superconductor in high temperatures and high magnetic fields.
In this research substitution of Ba was carried out, i.e. Sr in the Gd1Ba2Cu3O7−δ superconductor system with the chemical formula Gd1(Ba2−xSrx)Cu3O7−δ. The selected Sr element refers to the results of research from Zhuo, 1999 , the effect of Sr substitution on Ba in the Hg0,7Pb0,3Ba2Ca2Cu3Oy superconductor. Sr substitution of Ba can cause a decrease in lattice c parameter of 0.7 Å. It was found that the irreversibility line for Sr substituted compounds shifted towards higher temperatures compared to pure samples without Sr. From analysis of the reversible magnetization, it shows that the magnetization fluctuation is much reduced, and the interlayer-coupling magnetization strength can be increased. The critical field over Hc2 is almost twice compared to pure samples without Sr.
The effect of Sr substitution on superconductivity, especially the hole doping mechanism in the Hg2(Ba1−ySry)2YCu2O8−δ system has been investigated by Toulemonde et al. . It was explained that it was possible to increase Tc from 0 K for y = 0 to 42 K for y = 1.0. The distribution of charge between the cell unit atoms shows the transfer of charge into the CuO2 plane through two doping, i.e. through O(2)-Cu and Ba/Sr-O(1) bonds respectively. In research conducted by C.H. Chin et al. 2003, substitution of Gd with Ca and Sr has been carried out . The relationship between Tc and orthorobicity and ÐO(1)-Ba-O(1) angles along the a-axis has been explained.
In this study, Sr substitution was carried out in the GBCO-123 system phase in relation to the doping impact of Sr in the formation of the Gd1Ba2Cu3O7−δ phase. To get a homogeneous mixture in the study a wet mixing method using nitric acid as a solvent is used.
2. Experiment Method
In the synthesis of Gd1(Ba2−xSrx)Cu3O7−δ compounds, the Gd2O3, SrO, BaO and CuO powder materials with purity > 99.9% and HNO3 with purity 65% (Sigma-Aldrich)are used. The Gd1(Ba2−xSrx)Cu3O7−δ compounds having compositions of x = 0.0, 0.05, 0.15, 0.25 and 0.5 were prepared by the solid state reaction methods, mixing is done by a wet-mixing method using HNO3 according to previous research . After the powder was weighed according to the stoichiometric composition then mixed in 100 ml of HNO3, stirred using a magnetic stirrer for 24 hours. The mixture is then heated at 250˚C to form a crust. The sample mixture is crushed in a mortar and calcined in a furnace at 400˚C for 2 hours, continued at 500˚C for 2 hours and finally at 600˚C for 6 hours. After grinding the sample is heated at 900˚C for 15 minutes. The results are crushed and then molded into pellets with a hydraulic press at 500 Pa pressure on a 1.5 cm diameter mold. The pellets are sintered according to the atmosphere in the furnace for 12 hours at 900˚C. The sample is cooled according to cooling in the furnace.
The sample was characterized by XRD at an angle of 2θ = 50˚ - 60˚, the existence of the Gd1Ba2Cu3O7−δ phase was analyzed by using Match-126.96.36.199 Software. Identification of the diffraction peaks of experiment result matched with reference entry number 96-153-9606 with formula Gd1Ba2Cu3O7 from CODInorg REV211633 2018.10.25 was used. For analyzing the changes of structural Rietca software was used.
3. Results and Discussion
The X-ray spectra of RBa2Cu3O7−δ are in general similar to the yttrium analogs . Figure 1 is the XRD diffraction spectrum pattern of Gd1Ba2−xSrxCu3O7−δ phase for x = 0, 0.05, 0.15 and 0.25. The results match of the XRD experiment and reference number entry 96-153-9606, peaks diffraction of Gd1Ba2−xSrxCu3O7−δ phase has been identified. Amount (in %) of the identified the peaks area that match as Gd1Ba2Cu3O7 phase shown in Figure 2, shows that the increase of Sr content does no significant differences. For all of samples amount are more than 85%, this indicates that a single-phase not yet reached. This may be related to the higher melting point of SrO compared to BaO, i.e. 2531˚C and 1923˚C respectively. It is cause a shift in the reaction temperature (sintering) of the Gd1(Ba2−xSrx)Cu3O7−δ phase formation to at higher temperatures.
Differential Thermal Analysis (DTA) in flowing air was carried out on the precursor powder with a heating rate 10˚/minute to investigate the sintering temperature for Gd1(Ba2−xSrx)Cu3O7−δ phase formation. The DTA characterization results for Gd1(Ba1.95Sr0.05)Cu3O7−δ as shown in Figure 3. From Figure 3, peak at temperature 920˚C and 1038˚C was observed. According some researchers previously it is shown that the Gd1Ba2Cu3O7−δ phase can formed at temperatures between 900˚C - 950˚C   . As a result Figure 3 suggests that a temperature at temperature 920˚C represents thechemical reaction temperature (sintering temperature) for formation of the Gd1(Ba1.95Sr0.05)Cu3O7−δ phase. The YBCO-123 family superconductor has a peritectic temperature at temperatures between 980˚C - 1090˚C   . The endothermic DTA peaks under oxygen corresponding to the peritectic melting reaction which takes place at
Figure 1. X-ray diffraction spectrum pattern of Gd1(Ba2−xSrx)Cu3O7−δ: (a) x = 0, (b) x = 0.05; (c) x = 0.15; (d) x = 0.25; (e) x = 0.5. Reference database used: formula of Gd1Ba2Cu3O7 entry number 96-153-9606 from CODInorg REV211633 2018.10.25.
Figure 2. The identified peaks area of the diffraction peaks for Gd1(Ba2−xSrx)Cu3O7−δ.
Figure 3. Measurement results with DTA for Gd1(Ba1.95Sr0.05)Cu3O7−δ.
1073˚C  and the peritectic temperature of GBCO-123 bulk superconductors, i.e. 1030˚C . Therefore we suggest that a temperature at 1038˚C represents the peritectic melting reaction temperature for the Gd1Ba1.95Sr0.05Cu3O7−δ.
Analyzes of the X-ray diffraction data was conducted by using the orthorhombic structural with Pmmm (47) space groups by the Rietveld structural refinement to obtain structural parameters. This is carried out by Rietica program. Refinements results shows the good of fitness (GOF) = 1.69, 2.57, 2.64, 3.17 and 2.78 for Sr content x = 0.00, 0.05, 0.15, 0.25 and 0.50 respectively. The refinement results, the value of a ¹ b < c were obtained, so that Gd1Ba2−xSrxCu3O7−δ phase is in the orthorhombic structure. The changes of the lattice parameters for Sr substitution are as given in Figure 4.
In Figure 1, the peaks in the four main regions of the Bragg angle 2θ around 32˚ to 33˚, 38˚ to 39˚, 45˚ to 49˚, 57˚ to 60˚   was indexing according diffraction from Gd1Ba2Cu3O7 phase. In Figure 1, the main diffractions showing
Figure 4. The changes of lattice constants in different Sr contents in the Gd1Ba2−xSrxCu3O7−δ.
the changes in the Gd1Ba2−xSrxCu3O7−δ phase cell parameters are: (013) and (103) at 2θ = 32 - 32.8˚, (020) and (200) at 2θ = 46˚ - 47.5˚, and (123) and (213) at 2θ = 57.5˚ - 59˚. Each pair of the above diffractions is accompanied by additional overlapping reflections (110), (006) and (116), respectively. The splitting of these diffractions peaks indicates changes in the orthorhombicity of the unit cell . This is correlation with changes of the lattice parameter a, b, and c as shown in Figure 4.
From Figure 1, for samples with x = 0.05 - 0.25 at an angle 2θ between 46.5˚ - 47.5˚ the diffraction planes (200) and (020) appear clearly separated, each at an angle of 2θ = 46.84˚ and 47.14˚. This indicates that the Gd1Ba2−xSrxCu3O7−δ phase formed is in the orthorhombic cell unit. Meanwhile, samples with x = 0 and 0.05, the separation between the diffraction planes (200) and (020) appear to shrink, this gives an indication that the Gd1Ba2−xSrxCu3O7−δ phase formed is still orthorhombic but with smaller in the orthorhombicity (Figure 7).
As shown in Figure 4 in a range x = 0 - 0.25, the lattice constants of a, b and c trend to changes towards smaller sizes with the increasing Sr elements content. But the decreases lattice parameter of b is relatively more slowly compared the changes of a, therefore the changes of orthorhombicity take place. The changes can be understood from the size effect and oxygen redistribution along a and/or b-direction .
Size of the ionic radii of Ba and Sr elements are different, i.e. Ba2+ and Sr2+ having ionic radius sizes of 1.49 Å and 1.32 Å respectively, but have the same valence state . Because the ionic radius of Sr2+ is smaller, substitution of Ba with Sr causes the three lattice parameters a, b and c to be decreased with increasing Sr content. The decreases give an indication that Sr elements have entered the Ba-site. This is according to increasing Sr content in the cases of cation substitution on YBCO-system superconductors as given in   .
From Figure 4, reveals there a little different of the decrease of lattice parameters of a and b for range x = 0 - 0.25. While for Sr content of x > 0.5, lattice constants of a and b increases but with different gradient. The different of changes may be correlated with different distribution oxygen along a-direction and b-direction. According to orthorhombic and tetragonal structures in reference 21, from refinement results, the occupancy for O(1)-site and O(5)-site are nO(1) and nO(5) respectively as shown in Figure 5. It reveals that in range of x = 0 - 0.2 oxygen occupancy for O(1)-site along b-direction is relatively constant, while the O(5)-site along a-direction decreases. Therefore, the changes in the lattice parameter of a and b noting same. The large amount of Sr2+ substituting for Ba2+ results in contract stress around B-site. For keep a balance structure inner stress must be produced. For this reason redistribution oxygen at O(5)-site and oxygen at O(1)-site. In this case occupancyoxygen on O(5)-site conducted so that the difference occupancy oxygen at O(1)-site and O(5)-site became smaller and reduces of the orthorhombicity occurred as shown in Figure 7. From the refinement results, the total oxygen as given by the sum of the occupancy parameters , i.e.
where nO(1) and nO(5) are occupancy for O(1) and O(5) site respectively The calculation results of Equation (1) as shown in Figure 6. From this figure can be shown that oxygen content decreases in range Sr content of x = 0 - 0.25 and then increases for x > 0.25.
From Figure 4 it appears that there are significant differences the lattice parameters values of a and b, indicating that the GdBa2Cu3O7−δ phase doped Sr has an orthorhombic structure. The relative changes of the lattice constants of a and b can be recognized from orthorhombicity splitting which is defined ,
Figure 5. The change of occupancy for O(1)-site and O(5)-site.
Figure 6. The oxygen content in Sr variation on Gd1(Ba2−xSrx)Cu3Oy compound.
The calculate results theorthorombiciity splitting by using Equation (2) as shown in Figure 7 were obtained. It appears with Sr content increases that the orthorombicity of the Gd1(Ba2−xSrx)Cu3O7−δ phase is changes. First, from x = 0 - 0.05 orthorombicity increase, then in range x = 0.05 - 0.25 decreases and for x > 0.25 decrease more sharply take place. In the range of x = 0.05 - 0.50 the changes of lattice constants a and b diminish the orthorhombicity. However, all the added samples are conserved with the orthorhombic structure similar to the pure sample and no orthorhombic-to-tetragonal transition occurs.
The changes lattice parameters of a, b and c indicate there are the changes in unit cell volume. The unit cell volume dependence of Sr content, as shown in Figure 8, reveals that the unit cell volume is decreases with increasing Sr content. For range on x = 0 - 0.5 the total decrease about 1.7%. The variation in lattice parameters (a, b, c) and unit cell volume with increasing Sr concentration show that Sr2+ may be incorporated into the crystal structure of the Gd1Ba2Cu3O7−δ phase, the cation of Sr occupy the Ba-sites. The pattern changes of the cell unit volume almost to resemble a pattern the changes in oxygen content as in Figure 6. It indicates that the cation substitution of Sr may result in a change of the oxygencontent in Gd1Ba2−xSrxCu3O7−δ phase. Therefore, the changes of the unit cell volume giving an indication of the changes in oxygen content in the crystalline structure of Gd1Ba2−xSrxCu3O7−δ phase, which is another factor that affects the lattice constant  .
In the synthesis of Gd1Ba2−xSrxCu3O7−δ phase compounds, the Sr element can replace the Ba element. The refinement results, for x = 0, 0.05, 0.15, 0.25 and 0.50 the value lattice parameters of a ¹ b < c were obtained, so that Gd1Ba2−xSrxCu3O7−δ phase is in the orthorhombic structure. The increasing Sr content causes the
Figure 7. The orthorombicity in different Sr contents in the Gd1Ba2−xSrxCu3O7−δ.
Figure 8. Changes in the volume of cell units due to increased content of Sr.
changes lattice parameters of a, b and c. In the range of x = 0.05 - 0.50 the changes of lattice constants a and b diminish the orthorhombicity. However, all the samples are conserved with the orthorhombic structure and no orthorhombic-to-tetragonal transition occurs.
This report is part of the fundamental research report with contract No. 486 127/UN14.2 /PNL.01.03.00/2016. The authors are thankful to RISTEKDIKTI and LPPM of Udayana University.
 Yamaguchi, T., Shingai, Y., Konishi, M., Ohya, M., Ashibe, Y. and Yumura, H. (2014) Large Current and Low AC Loss High Temperature Superconducting Power Cable Using REBCO Wires. SEI Technical Review, No. 78, 79-85.
 Jirsa, M., Rameš, M., Duran, I., Entler, S., Melíšek, T., Kovác, P. and Viererbl, L. (2016) Electromagnetic Properties of REBaCuO Superconducting Tapes Considered for Magnets of Fusion Reactors. Fusion Engineering and Design, 124, 73-76.
 Zhuo, Y., Oh, S.-M., Choi, J.-H., Kim, M.-S., Lee, S.-I., Kiryakov, N.P., Kuznetsov, M.S. and Lee, S. (1999) Effects of Sr Substitution on Dimensionality and Superconducting Properties of Hg0.7Pb0.3Ba2Ca2Cu3Oy. Physical Review B, 60, Article ID: 13094.
 Toulemonde, P., Odier, P., Bordet, P., Le Floch, S. and Suard, E. (2004) Effect of Sr Substitution on Superconductivity in Hg2(Ba1−ySry)2YCu2O8−δ (Part 2): Bond Valence Sum Approach of the Hole Distribution. Journal of Physics: Conference Series, 16, 4077-4087.
 Chin, C.H. and Kao, H.C.I. (2003) Effect of Substitution in the (Gd1−xCax)Ba2Cu3Oy and Gd(Ba2-xAx)Cu3Oy (A= Ca, Sr) Superconducting Compounds. Physica C, 388-389, 381-382.
 Sumadiyasa, M., Putra Adnyana, I.G.A., Widagda, I.G.A. and Suharta, W.G. (2016) Study Synthesis of (La1−xGdx)Ba2Cu3O7−δ Superconductors at Low Temperature. Journal of Physics: Conference Series, 725, Article ID: 012001.
 Wong-Ng, W., Cook, L.P., Su, H.B., Vaudin, M.D., Chiang, C.K., Welch, D.R., Fuller, E.R., Yang, Z. and Bennett, L.H. (2006) Phase Transformations in the High-Tc Superconducting Compounds Ba2RCu3O7–δ (R= Nd, Sm, Gd, Y, Ho, and Er). Journal of Research of the National Institute of Standards and Technology, 111, 41-55.
 Purwamargapratala, Y., Swinatapura, D. and Eukirman, E. (2007) Influence of Temperature and Time Sintering to Forming of Superconductor. Indonesian Journal of Materials Science, Special Issue, 77-82.
 Matsushima, K., Taka, C. and Nishida, A. (2018) Variations of Superconducting Transition Temperature in YbBa2Cu3O7−δ Ceramics by Gd Substitution. Journal of Physics: Conference Series, 969, Article ID: 012059.
 Namburi, D.K., Shi, Y.H., Dennis, A.R., Durrell, J.H. and Cardwell, D.A. (2018) A Robust Seeding Technique for the Growth of Single Grain (RE)BCO and (RE)BCO-Ag Bulk Superconductors. Superconductor Science and Technology, 31, Article ID: 044003.
 Shi, Y., Hari Babu, N., Iida, K. and Cardwell, D.A. (2007) Growth Rate and Superconducting Properties of Gd-Ba-Cu-O Bulk Superconductors Melt Processed in Air. IEEE Transactions on Applied Superconductivity, 17, 2984-2987.
 Prado, F., Caneiro, A. and Serquis, A. (1998) High Temperature Thermodynamic Properties, Orthorhombic-Tetragonal Transition and Phase Stability of GdBa2Cu3Oy and Related R123 Compounds. Physica C, 295, 235-246.
 Nakanishi, Y., Pavan Kumar Naik, S., Muralidharand, M. and Murakami, M. (2017) Effect of Growth Temperature on Properties of Bulk GdBa2Cu3Oy Superconductors Grown by IG Process. Journal of Physics: Conference Series, 871, Article ID: 012052.
 Yossefov, P., Shter, G.E., Reisner, G.M., Friedman, A., Yeshurun, Y. and Grader, G.S. (1997) Solubility Parameter (X), Powder Properties and Phase Formation in the Ndl+xBa2−xCu3O6.5+x/2+δSystem. Physica C, 275, 299-310.
 Kao, H.C.I., Chin, C.H., Huang, R.C. and Wang, C.M. (2000) Rietveld Analysis on Gd(Ba2−xAx)Cu3Oy (A = Ca, Sr) Superconductors. Physica C, 341-348, 623-624.
 Ha, D.H., Min, H.S., Lee, K.W., Byon, S., Han, G.Y. and Lee, H.K. (2001) Effects of Cation Substitution on the Oxygen Loss in YBCO Superconductors. Journal of the Korean Physical Society, 39, 1041-1045.
 Licci, F., Gauzzi, A., Marezio, M., Radaelli, G.P., Masini, R. and Chaillout-Bougerol, C. (1999) Structural and Electronic Effects of Sr Substitution for Ba in Y(Ba1−xSrx)2Cu3Oy. Physical Review B, 58, 15209-15217.
 Benzi, P., Bottizzo, E. and Rizzi, N. (2004) Oxygen Determination from Cell Dimensions in YBCO Superconductors. Journal of Crystal Growth, 269, 625-629.
 Ramli, A., Shaari, A.H., Baqiah, H. and Talib, Z.A. (2016) Role of Nd2O3 Nanoparticles Addition on Microstructural and Superconducting Properties of YBa2Cu3O7−δ Ceramics. Journal of Rare Earths, 34, 895-900.