Effects of Gd211 Particles Characteristic in the Precursor Pellets on the Levitation Force of Single-Domain GdBCO Bulks Prepared by the Gd + 011 TSIG Method

Yuan, Xiaochun; Yang, Wanmin

doi:https://doi.org/10.1155/2018/5481625

Advances in Materials Science and Engineering

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Abstract Introduction Results and Discussion Conclusions Data Availability Conflicts of Interest Acknowledgments References Copyright Related Articles

Research Article | Open Access

Volume 2018 | Article ID 5481625 | https://doi.org/10.1155/2018/5481625

Effects of Gd211 Particles Characteristic in the Precursor Pellets on the Levitation Force of Single-Domain GdBCO Bulks Prepared by the Gd + 011 TSIG Method

Xiaochun Yuan^1,2and Wanmin Yang¹

Academic Editor: Simo-Pekka Hannula

Received27 Feb 2018

Revised01 Jul 2018

Accepted18 Jul 2018

Published26 Aug 2018

Abstract

In this paper, single-domain GdBCO bulks have been fabricated by a new Gd + 011 TSIG method with precursor solid phase pellets (PSPPs) of different Gd211 particle sizes and distributions, prepared by solid state reaction with well-mixed (Gd₂O₃ + BaCuO₂) pellets at different temperatures. The novel results indicated that (1) the average size of Gd211 particles in PSPP is monotonically increasing with increasing the sintering temperature up to 1200°C. (2) With increasing the sintering temperature from 950 to 1200°C, the porous ratio and the density of the PSPP are, respectively, monotonically decreasing and increasing. Furthermore when the sintering temperature is less than 1000°C, the porous ratio is higher and the density is lower than the values of the pressed pellets. (3) With increasing the sintering temperature, the average size of Gd211 particles in the GdBCO bulk first decreases and then increases. In addition, the smallest Gd211 particles are obtained in the sample sintered at 1050°C. (4) The maximum levitation force is obtained in the sample sintered at 1150°C with a relatively larger size of Gd211 particles and lower porosity. This result is significant when fabricating high-quality GdBCO bulk superconductors by controlling the porosity, Gd211 particle size, and their distribution characteristic.

1. Introduction

High-temperature REBCO bulk superconductors (RE is Yb, Y, Gd, Sm, Nd, etc.) are characterized by larger levitation force, higher trapped field, and self-stabilized levitation. These advantages lead to many applications such as magnetic bearing, flywheel, high-field permanent magnets, and levitated transportation systems [1–6]. In order to obtain large single-grain REBCO bulks without weak links, the top seeding technique is employed to avoid the heterogeneous nucleation and promote the growth of the REBa₂Cu₃O_7-y grain epitaxial grown from the seed to a large scale [7–10]. Top-seeded infiltration growth (TSIG) technique is one of the most popular methods for fabrication of single-grain REBCO bulk superconductors. In the traditional TSIG process, a RE₂BaCuO₅ (RE211) solid phase pellet and a liquid phase pellet containing REBa₂Cu₃O_7-y and Ba₃Cu₅O₈ have to be prepared. So, the traditional TSIG process will not only take a long time and expensive cost but is also inefficient during the fabrication of single-domain REBCO superconductor.

In order to reduce the cost and simplify the fabrication process, we have invented a new RE + 011 TSIG method to fabricate single-domain REBCO superconductor by using only one precursor powder BaCuO₂ (011) [11–15]. The traditional solid phase RE211 and the traditional liquid phase (REBa₂Cu₃O_7-y and Ba₃Cu₅O₈) are, respectively, replaced with the new solid phase (RE₂O₃ + xBaCuO₂) and Y₂O₃ + 6CuO + 10BaCuO₂. This method has a considerable number of advantages, for example, improving the production efficiency, reducing the preparation cost, simplifying the experiment process, and enhancing the physical properties of REBCO bulk compared with the traditional TSIG ways. However, the size of the Gd211 particle is significantly larger in the single-domain GdBCO samples prepared by the Gd + 011 TSIG method [11]. Now, the question arises how to reduce the size of Gd211 particles and improve the physical properties. It is necessary to reveal the relationship between the microstructure of the precursor solid phase pellet (PSPP) and the microstructure of the single-domain GdBCO samples. Furthermore, it is required to determine the relationship among the microstructure of the PSPP, the microstructure of the single-domain GdBCO samples, and the superconducting properties. The latter two steps are essential scientific problems to be solved in order to improve the superconducting properties of single-domain GdBCO samples.

We have prepared a series of PSPP samples with varying density and Gd211 particle size by sintering the new solid phase (Gd₂O₃ + BaCuO₂) at different temperatures. Based on the prepared samples, a series of single-domain GdBCO bulks has been fabricated by the Gd + 011 TSIG technique. The macroscopic morphology and microstructure of the PSPP and single-domain GdBCO bulks were observed and analyzed. The effects of PSPP on the microstructure and levitation force of single-domain GdBCO bulks have also been investigated based on these samples.

2. Experimental Procedure

The precursor powder BaCuO₂ (011) was prepared by the conventional solid state reaction method using the raw materials BaCO₃ (purity 99.9%) and CuO (purity 99.9%) in air. The powder of Gd₂O₃ (purity 99.9%) and BaCuO₂ (011) were weighed according to the molar ratio Gd₂O₃ : BaCuO₂ = 1 : 1 and well mixed by a ball-milling machine. Consequently, pressed into the pellets of diameter 20 mm. The pressed pellets prepared in this way were sintered at different temperatures (950, 1000, 1050, 1100, 1150, and 1200°C) for 6 h in the air and furnace cooled to room temperature. The resulting sintered samples were used as the precursor solid-phase pellet (PSPP) for the Gd + 011 TSIG process. The liquid phase pellets were prepared from a well-mixed Y₂O₃, CuO, and 011 powder, which were weighed according to the molar ratio Y₂O₃ : CuO : 011 = 1 : 6 : 10, followed by being pressed into the pellets of 30 mm in diameter. Furthermore, Y₂O₃ or Yb₂O₃ was pressed into a plate of thickness 2 mm and diameter 30 mm to support the liquid phase at elevated temperature. The configuration of the precursor sample consisted of three cylindrical pellets and stacked up together along their coaxial line: the top one being the PSPP, followed by the liquid phase pellet and the Y₂O₃ or Yb₂O₃ pellet. Finally, a NdBCO seed was placed on the top surface of the PSPP to promote the epitaxial growth of the GdBCO superconductor during the TSIG process.

The precursor sample was (1) heated up to 920°C at a rate of 120°C/h, (2) heated up to 1065°C at a rate of 60°C/h, (3) held for 1 h to ensure complete infiltration of liquid into the PSPP, (4) cooled to 1040°C at a rate of 60°C/h; (5) the samples were cooled slowly at a rate of 0.3°C/h to 1015°C, and (6) the samples were cooled to room temperature at a rate of 120°C/h. The resulting grown samples were annealed in flowing oxygen at temperature ranging from 450 to 350°C for 200 h so that the single-grain GdBCO bulks could be of superconducting properties.

Microstructure of the PSPP and the single-domain GdBCO bulks were investigated by a scanning electron microscope (SEM). The levitation forces of the GdBCO bulks were measured at 77 K under a zero-field cooling state by self-designed magnetic force and magnetic field measurement system [16].

3. Results and Discussion

3.1. The Morphology and Density of the PSPP

Figure 1 is the morphology of the PSPP with the same initial new solid phase source of (Gd₂O₃ + BaCuO₂) sintered at different temperatures. As can be seen from Figure 1, the pressed pellet was of gray color and made of well-mixed Gd₂O₃ and 011 powders. After sintering at 950°C, some of the Gd₂O₃ reacted with 011 and formed Gd211 phase, causing the color to turn from gray to yellow-green. When the sintering temperature exceeded 1000°C, Gd₂O₃ well reacted with 011 and the PSPP changed to Gd211 phase, and the color of the PSPP changed from green to dark green when the sintering temperature increased to 1200°C.

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The density of the PSPP was plotted as a function of sintering temperature as shown in Figure 2. As can be observed from Figure 2, the density of the PSPP increases as sintering temperature increases from 950 to 1200°C. The density of the PSPP increases from 3.42 to 3.7, 4.41, 4.82, 4.93, and 5.04 g/cm³, when sintering temperature increases from 950 to 1000, 1050, 1100, 1150, and 1200°C. This is agreed with the traditional RE211 solid-phase pellets [17]. The density of the PSPP sintered in the range from 950 to 1000°C was in the range from 3.42 to 3.7 g/cm³, respectively, lower than 3.85 g/cm³ of the pressed sample. This is much different from the traditional RE211 solid-phase pellets [17], which are closely related with the chemical composition of the new solid phase of (Gd₂O₃ + BaCuO₂) and the microstructure of the samples sintered at different temperatures.

3.2. Microstructure of the PSPP

Figure 3 is the SEM showing the PSPP sintered at different temperatures. As we have mentioned in Section 2, the pressed PSPP (Figure 3(a)) is composed of Gd₂O₃ and 011 powder. There are several large dark particles in Figure 3(a) which correspond to the 011 phase. The 011 phase particles are melted and reacted with Gd₂O₃ powder to form Gd211, when the pressed PSPP is sintered at T_s ≥ 950°C, and thus resulted in the formation of the Gd211 particles and pores in the samples, as shown in Figures 3(b)–3(g). There are many smaller and nanometer Gd211 particles as well as relatively larger pores appeared in the sample, as shown in Figure 3(b). The above process results in a reduction of the density to 3.42 g/cm³ compared with the pressed PSPP (3.85 g/cm³). The size of the Gd211 particles and the pores are increasing and decreasing with increasing the sintering temperature. This causes the density of PSPP gradually to increase from 3.70 to 5.04 g/cm³, when the sintering temperature increases from 1000 to 1200°C. The particles have been identified with the energy dispersive spectrometer (EDS) during the microstructure observation by SEM, and the results indicate that Gd, Ba, and Cu elements are in the molar ratio Gd : Ba : Cu = 2 : 1 : 1, which identified that these are Gd211 particles. The mean size of Gd211 particles for each sample was calculated by an international common software Nano Measurer. As we can see from Figure 3, The average size of the Gd211 particles is either 1.65, 2.45, 3.33, 3.64, or 4.23 μm in the samples sintered at temperature 1000, 1050, 1100, 1150, or 1200°C, respectively.

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3.3. Morphology of the Single-Domain GdBCO Bulks

Figure 4 is the morphology of the single-domain GdBCO samples prepared by the Gd + 011 TSIG method with the PSPP of the same initial new solid phase (Gd₂O₃ + 011) sintered at different temperatures 25 (corresponding to the unsintered sample), 950, 1000, 1050, 1100, 1150°C, and 1200°C, denoted as S1, S2, S3, S4, S5, S6, and S7, respectively. As can be seen from Figure 4, all the samples exhibit clear, fourfold growth sectors on their top surface, indicating that they are grown in the form of a single domain [18]. In addition, no spontaneous GdBCO grains were observed in the samples.

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3.4. Levitation Force of the Single-Domain GdBCO Samples

The levitation forces of the GdBCO samples were measured under a zero-field cooling state at 77 K by a customized laboratory-made instrument. A magnet with a diameter 20 mm and a surface field of 0.5 T was employed for the levitation force measurements. The maximum levitation force was achieved at the smallest gap (0.5 mm) between the magnet and the GdBCO samples. The levitation force versus distance (between the magnet and the samples) curves are shown in Figure 5. The insert in Figure 5 shows the dependence of the maximum levitation force () on the sintering temperature of the PSPP varying from 25 to 1200°C. As can be seen from the figure, the maximum levitation force monotonically increases from 25.1 to 38.1 N with the increasing sintering temperature from 25 (corresponding to the unsintered sample) to 1150°C. Furthermore, it can be observed that the maximum levitation force decreases in the range 1150°C–1200°C.

3.5. Microstructure of the Single-Domain GdBCO Samples

Figure 6 is the SEM photographs of the GdBCO samples. It can be seen from Figures 6(a)–6(g) that there are many gray particles distributed in the GdBa₂Cu₃O_7-y (Gd123) phase matrix. The gray particles have been identified with EDS, and the results indicate that Gd, Ba, and Cu elements are in the molar ratio Gd : Ba : Cu = 2 : 1 : 1, which indicate that these are Gd211 particles; the size of Gd211 particle in the single-domain GdBCO samples first decreases and then increases with increasing Gd211 particles in the PSPP. The Gd211 particle distribution and their mean size in the GdBCO samples were also calculated with the software Nano Measurer and are plotted in Figure 7. As we can see from Figure 7, the average size of the Gd211 particles decreases from 10.9 to 2.81 μm with increasing sintering temperature from 25 to 1050°C corresponding to the samples S1 to S4. Here, 25°C corresponds to the unsintered samples. The average size of the Gd211 particles however increases from 2.81 to 3.96 μm with the increasing sintering temperature from 1050 to 1200°C, corresponding to the samples S4 to S7. The latter observation is in agreement with other experimental results in the literature that the larger the size of Gd211 particles in PSPP, the bigger the Gd211 particles in GdBCO samples [19, 20]. However, the results of the samples S1, S2, S3, and S4 indicate that the smaller the size of Gd211 particles in PSPP, the bigger Gd211 particles in GdBCO samples. These observed relationships allude to a new phenomenon which is substantially different from other results obtained in the traditional TSIG method. It can be conjectured that the smaller size Gd211 particles are of a lower chemical potential and thus easy to decompose, while the comparatively larger Gd211 particles grow bigger and bigger during the melting growth process of the single-domain GdBCO crystal.

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Figures 3, 5, and 6 reveal that the largest levitation force is not obtained in samples with smaller Gd211 particles in PSPP (S1–S3); neither in samples with smaller Gd211 particles in single-domain GdBCO samples (S4-S5), rather in S6 with relatively larger Gd211 particles in the PSPP (3.64 μm) and single-domain GdBCO bulk (3.21 μm). This is closely related with the critical current densities (J_c) of the samples because the levitation force can be expressed as a function of volume , J_c, and the radius of the shielding current loop r of the samples [21]. But J_c is closely related with the flux pinning force of the samples, so the levitation force is directly dependent on the flux pinning properties of the sample.

In order to make clear this reason, we have to find out the relationship between the levitation force and the microstructure of the samples, especially the differences of Gd211 particles of the samples because the defects, such as stacking faults, dislocations, and twin boundaries around the Gd211/Gd123 interface can act as the flux pinning centers [20, 22, 23]. As we know that the fabricated samples are of the same initial composition (Gd₂O₃ + BaCuO₂) and the same weight and shape, and the GdBCO bulks are also of nearly the same volume and the radius of the shielding current loop r, the levitation force is closely dependent on the Gd211 particles distribution and the density of the samples. For sample S1, the size of Gd211 particles is the largest (about 10.9 μm) in the single-domain GdBCO bulks. Furthermore, its high-level porosity is produced by the reaction of 011 with Gd₂O₃ phase. Consequently, the flux pinning force and levitation force (25.1 N) are at a minimum.

Compared with S1, the porosity is gradually reduced in samples S2, S3, and S4, as shown in Figures 3(b), 3(c), and 3(d), respectively. Moreover, the number of larger size Gd211 particles is significantly reduced and the number of smaller size Gd211 particles is increased as it is evident in Figures 6(b), 6(c), and 6(d). The facts result in a gradual enhancement of the flux pinning and levitation force. The levitation force is increased from 25.1 to 29.1, 31.5, and 34.9 N corresponding the samples S1, S2, S3, and S4. For the samples S5 and S6, although the large size Gd211 particles in the PSPP (Figures 3(e) and 3(f)) result in an increment of the Gd211 particles, the porosity is significantly reduced, resulting in a further increase of levitation force to 36.7 and 38.1 N. For the sample S7, the size of Gd211 particles is the largest in the PSPP (Figure 3); however, the Gd211 particles are smaller than those in the samples S1 and S2, while being slightly larger than those in the samples S5 and S6 (Figure 6). In addition, the porosity is reduced to a lowest level, but the difference is very insignificant compared with the sample S6, resulting in a reduction of the levitation force to 33.6 N (S7). The largest levitation force is achieved in the sample S6 with relatively larger size Gd211 particles and lower porosity.

4. Conclusions

Single-domain GdBCO bulks have been fabricated by the Gd + 011 TSIG technique in air using the PSPP with different Gd211 particle sizes and porosity. It is found that (i) the size of the Gd211 particles in the PSPP is increasing with increasing of the sintering temperature from 950 to 1200°C, (ii) the porosity of the PSPP is decreasing with the increasing of the sintering temperature from 950 to 1200°C, (iii) the largest levitation force is achieved in the sample S6 with relatively larger size Gd211 particles and lower porosity, and (iv) in order to further improve the microstructure and physical properties of the single-domain GdBCO bulk, the PSPP should possess the following properties: (a) the Gd211 particles are of spherical or ellipsoidal shape and smaller size and (b) the Gd211 particles should improve the density and homogeneity and reduce the porosity of the PSPP. These results are very important in fabricating the high-quality single-domain GdBCO bulk superconductor.

Data Availability

The data used to support the findings of this study are available from the corresponding author upon request.

Conflicts of Interest

The authors declare that they have no conflicts of interest.

Acknowledgments

Helpful discussions with Professor Alireza Baghai-Wadji (University of Cape Town) are gratefully acknowledged. This work was supported by the National Natural Science Foundation in China (nos. 51572164 and 51342001), the Key Grant Project of Ministry of Education of the People’s Republic of China (no. 311033), the Research Fund for the Doctoral Program of Higher Education of China (no. 20120202110003), the Innovation Team in Shaanxi Province (no. 2014KTC-18), and the Fundamental Research Funds for the Central Universities (no. GK201706001).

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Copyright © 2018 Xiaochun Yuan and Wanmin Yang. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

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