“…Many studies of doping into superconductor oxide ceramics have been made in order to improve their mechanical and superconducting properties [25][26][27][28][29][30]. Engineering applications of high critical temperature (T c ) superconducting ceramics are generally restricted because of their brittleness.…”
“…Many studies of doping into superconductor oxide ceramics have been made in order to improve their mechanical and superconducting properties [25][26][27][28][29][30]. Engineering applications of high critical temperature (T c ) superconducting ceramics are generally restricted because of their brittleness.…”
“…The results in Figs. 7(b) and 7(c) suggest that the ring bulks reinforced by Al alloy ring, except bulk (5), may avoid mechanical fracture during FCM from 6.3 T, because the maximum σ θ total value is +62 MPa, which is nearly the same as the fracture strength (50 ~ 70 MPa) of typical REBaCuO bulks [17], [18]. However, bulk (5) (I.D.…”
Section: Cooling + Fcm Processmentioning
confidence: 95%
“…7(a) shows the TS dependence of the total hoop stress, σ θ total , at the inner edge on the bulk surface for each ring bulk during FCM from B app = 9.4 T, after cooling to 50 K. The σ θ total values decreased, compared to the σ θ FCM values, due to the addition of the compressive stress by cooling. However, a tensile stress larger than +100 MPa is present during FCM from 9.4 T, which suggests the possibility of the bulk fracturing, since the fracture strength of typical Ag-doped REBaCuO bulks is considered to be 50 ~ 70 MPa [17], [18]. Fig.…”
In this paper, the trapped field, B z , thermal hoop stress, σ θ cool , by cooling from 300 to 50 K and electromagnetic hoop stress, σ θ FCM , during field cooled magnetization (FCM) from B app = 6.3 and 9.4 T are investigated numerically for ring-shaped RE-BaCuO bulks with various inner diameters (I.D.) and heights (H) and reinforced by an Al alloy ring. For simplicity, an identical critical current density, J c (B), which is a typical value at 50 K, is assumed in the simulation. The B z value at the center of the ring bulk changes depending on the I.D. and H values of the ring bulk, which results from the different distribution of the superconducting current. As a result, the total hoop stress, σ θ total , (= σ θ cool + σ θ FCM) also changes for each ring bulk and for each B app due to the variation of the σ θ cool and σ θ FCM values. The maximum σ θ total value, which affects the bulk fracture at B app =9.4 T, increases with decreasing the height of ring bulk. These results can present guidelines for designing a trapped-field magnet using ring bulks.
“…Moreover, because untreated defects act as stress concentration points, the addition of silver also helps to limit crack propagation during mechanical stress induced by the trapped field. [27][28][29][30] 10 wt.% of Ag 2 O was added the precursor powder (i.e., a total of 110 %) to obtain a sufficient temperature difference between the seed plate material and the precursor bulk composition, as is common in the preparation of certain (RE)BCO systems, including EuBCO. The silver fills any defects in the bulk sample during the single grain growth process and improves the microstructure, and therefore the mechanical properties of the fully processed sample.…”
Despite the success of top‐seeded melt growth (TSMG) and TSIG, some key aspects of their manufacture need to be addressed including the presence of microstructural defects, inhomogeneities in trapped field and the difficulty of growing large‐diameter bulk monoliths. Recently, a promising new method single‐direction melt growth (SDMG) appears to address the majority of the shortcomings of TSMG and TSIG. Single‐grain EuBCO/Ag bulk with the highest peritectic temperature to date was grown by modified SDMG. This remarkable achievement was made possible by lowering the peritectic temperature of the precursor composition by the addition of silver and by using single‐grain EuBCO fabricated by TSMG as a seed. The EuBCO/Ag bulk grown by SDMG has demonstrated significant improvements in comparison to a reference TSMG sample. A reduction of approximately 30% in defect area (associated primarily with porosity), as well as a significantly enhanced homogeneity of trapped field and critical temperature, was observed. Furthermore, the critical current density curves exhibit a considerable improvement, particularly in the 2–5 T field range. The SDMG technique has considerable potential for scale‐up for the fabrication of large‐diameter bulk single grains, with only growth along the c‐axis involved during the thermal process.
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