Abstract:MgB 2 commercial powder was encased in a Ni tube and rolled into a monocore tape of about 5 mm in width and 0.3 mm in thickness. Different kinds of metal powder, i.e., In, Sn, Ag, Cu and Ni, were added to the MgB 2 core. Addition of the low melting point metal powder, e.g., In and Sn, has been found to enhance significantly the value in MgB 2 tapes. Annealing at a low temperature yields further increase in the of tapes with In and Sn addition. The enhancement in by the In addition and the low temperature annea… Show more
“…The wires were annealed at 873 K for 2 h in Ar atmosphere. The details of the specimen preparation are found in [5] and [9].…”
Section: Samplesmentioning
confidence: 99%
“…The transport critical current density of the core in the PIT MgB 2 conductors depends on such parameters as the raw powder quality, sheath material, fabrication procedure, heat-treatment condition, and so on. In order to improve the critical current I c , the addition of metal powders, such as indium (In), to the MgB 2 core has been tried by some of the present authors [5,6]. Among them, it has been shown that 10 vol% In addition and annealing enhances I c by a factor of 6 to 7.…”
The effects of stress-strain on the critical current, I c , of ex situ powder-in-tube (PIT)-processed Ni-sheathed MgB 2 tapes and round wires as well as in situ PIT-processed Cu-sheathed wires at 4.2 K in a magnetic field up to 5 T have been studied. The effect of In powder addition on the Ni-sheathed MgB 2 wire was not so clear compared with that in the tape, in which the irreversible strain, ε irr , for the I c degradation onset increases significantly by the addition. This is attributed to the difference in the microstructure of the core associated with cold workings. A peak and gradual degradation behaviour of I c with strain beyond ε irr was found in the wire, whereas no evident peak and a steep degradation behaviour was found in the tape. As a possible reason, the difference in the triaxial residual stress state at 4.2 K due to the difference in geometry of the cross-section is suspected. The transverse compression tests revealed that I c of the wire did not degrade up to 270 MPa. Again, the effect of In addition was minimal. The Young's modulus of MgB 2 , 31-41 GPa, at room temperature was estimated by a tensile test of Cu sheath wire using a high-accuracy extensometer and the law of mixtures. The tensile strain dependence of I c in the Cu sheath wire was similar to that in the Ni-sheathed wire, ε irr being 0.4%. However, the stress corresponding to ε irr , 50 MPa, was about 1/10 of that for the Ni-sheath wire and the irreversible transverse compressive stress, 150 MPa, was also lower. The effect of bending strain on the I c in Cu-sheathed wire was compared with that of the tensile strain.
“…The wires were annealed at 873 K for 2 h in Ar atmosphere. The details of the specimen preparation are found in [5] and [9].…”
Section: Samplesmentioning
confidence: 99%
“…The transport critical current density of the core in the PIT MgB 2 conductors depends on such parameters as the raw powder quality, sheath material, fabrication procedure, heat-treatment condition, and so on. In order to improve the critical current I c , the addition of metal powders, such as indium (In), to the MgB 2 core has been tried by some of the present authors [5,6]. Among them, it has been shown that 10 vol% In addition and annealing enhances I c by a factor of 6 to 7.…”
The effects of stress-strain on the critical current, I c , of ex situ powder-in-tube (PIT)-processed Ni-sheathed MgB 2 tapes and round wires as well as in situ PIT-processed Cu-sheathed wires at 4.2 K in a magnetic field up to 5 T have been studied. The effect of In powder addition on the Ni-sheathed MgB 2 wire was not so clear compared with that in the tape, in which the irreversible strain, ε irr , for the I c degradation onset increases significantly by the addition. This is attributed to the difference in the microstructure of the core associated with cold workings. A peak and gradual degradation behaviour of I c with strain beyond ε irr was found in the wire, whereas no evident peak and a steep degradation behaviour was found in the tape. As a possible reason, the difference in the triaxial residual stress state at 4.2 K due to the difference in geometry of the cross-section is suspected. The transverse compression tests revealed that I c of the wire did not degrade up to 270 MPa. Again, the effect of In addition was minimal. The Young's modulus of MgB 2 , 31-41 GPa, at room temperature was estimated by a tensile test of Cu sheath wire using a high-accuracy extensometer and the law of mixtures. The tensile strain dependence of I c in the Cu sheath wire was similar to that in the Ni-sheathed wire, ε irr being 0.4%. However, the stress corresponding to ε irr , 50 MPa, was about 1/10 of that for the Ni-sheath wire and the irreversible transverse compressive stress, 150 MPa, was also lower. The effect of bending strain on the I c in Cu-sheathed wire was compared with that of the tensile strain.
“…The trials for enhancement of H c2 and J c in MgB 2 have been performed in single crystal, bulk, wire and thin film [66][67][68][69][70][71][72][73][74]. Two bands in MgB 2 (p and s bands) take part in not only the superconducting gap but also H c2 and its anisotropy (H // ab, H // c).…”
Abstract. We review superconductivity in MgB 2 in terms of crystal and electronic structure, electron-phonon coupling, two-gap superconductivity and application. Finally, we introduce the development of new superconducting materials in related compounds.
Synopsis: Since the discovery in 2001, MgB 2 has gained much interests as a new hope of superconductors for its applicability at temperatures of liquid H 2 (~20 K) or liquid Ne (~27 K). Then large efforts have been dedicated to the processing of MgB 2 wires. Ex situ and in situ techniques are two major techniques for the fabrication of MgB 2 wires. The ex situ process uses previously reacted MgB 2 powders filled into appropriate sheath tubes which are then fabricated into a wire. In the in situ process a mixture of Mg and B powders is encased in a sheath tube, and after the wire fabrication, the MgB 2 core is synthesized in situ by the heat treatment. C or SiC nano-powders are effective dopants to enhance the high-field performance of MgB 2 wires. Wires a few kilometers long have been produced via both processes. The diffusion process starting from a composite of Mg rod or pipe and B powder is another promising process in MgB 2 wire fabrication. The connectivity of MgB 2 grains is still poor due to the insufficient packing factor of powders, voids caused by the volume contraction during MgB 2 formation, and the envelope of MgO and other insulating phase around MgB 2 grains. This poor connectivity reduces the critical current density of MgB 2 wires. Improved powder quality, fabrication techniques, and dopants may appreciably improve the performance of MgB 2 wires. Presently, the main target of MgB 2 wire application is direct-current use at 20 K, such as for MRI magnets. In this article, material aspects, fabrication process, superconducting performance and future possibilities of MgB 2 wires are briefly surveyed.
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