Method for manufacturing Nb.sub.3 Al group superconductor

Abstract

In a method for manufacturing Nb.sub.3 Al phase by a diffusion reaction of Nb.sub.2 Al phase and Nb phase, a part of the Nb.sub.2 Al phase is remained and dispersed in the Nb.sub.3 Al phase homogeneously as for magnetic flux pinning centers for a high magnetic field. As for a method for dispersing the Nb.sub.2 Al phase homogeneously, a Nb.sub.3 Al group superconducting precursory composition obtained by dispersing Nb particles and Nb.sub.2 Al ultrafine particles by a mechanical alloying method is used, and further, by a conventional method for generating Nb.sub.3 Al phase by a diffusion reaction of Nb and an aluminum alloy, A Nb.sub.3 Al group superconductor can be achieved.

Description

BACKGROUND OF THE INVENTION

(1) Field of the Invention

The present invention relates to Nb.sub.3 Al group superconductors, particularly, to Nb.sub.3 Al group superconductors and manufacturing method thereof, Nb.sub.3 Al group superconductive precursory compositions, and superconducting magnets for generating high magnetic field preferable for nuclear fusion apparatus, nuclear magnetic resonance apparatus, and high magnetic field generating apparatus all of which require high magnetic field.

(2) Description of the Prior Art

Nb.sub.3 Al group superconductors have been manufactured, as described in Applied Physics Letters, vol. 52 No. 20 p1724-1725 (1988. 5.16), in a manner that a plurality of aluminum alloy core materials and niobium matrix material are made to an ultrafine multicore cable by a composite manufacturing method, and subsequently, the cable is treated with diffusion heat treatment at 750.degree.-950.degree. C.

Another manufacturing method in which Nb.sub.2 Al powder and Nb powder are mixed, fabricated, and sintered at 1,300.degree.-1,400.degree. C. to be Nb.sub.3 Al is disclosed in The Proceedings of 45th on Cryogenics and Superconductivity (Chiba, Japan, May 14-16, 1991), p246.

Further, other manufacturing method is disclosed in JP-A-3-283322 (1991), in which a composite body is formed by filling mixed powder of Nb.sub.2 Al alloy and niobium into a metallic tube made from niobium or Nb base alloy, a core material is formed by cold working of the composite body, and subsequently, Nb.sub.3 Al superconductor is obtained by heat treatment of the core material for generating Nb.sub.3 Al which changes the cold worked powder to Nb.sub.3 Al.

Among the above described prior art, the composite manufacturing method had a problem that the Nb.sub.3 Al ultrafine multicore cable obtained by normal diffusion heat treatment had low critical temperature and low critical magnetic field, and the critical current density decreased remarkably under a high magnetic field condition such as 20 T level. The method by fabrication and sintering of Nb.sub.2 Al powder and Nb powder necessitated sintering at high temperature, and accordingly, it had a problem although it enhanced yielding of Nb.sub.3 Al that crystal grain size of Nb.sub.3 Al increased and the critical current density decreased under low and medium magnetic field conditions.

That means, a case of Nb.sub.3 Al group superconductors, high critical temperature and high critical magnetic field depending on characteristics of Nb.sub.3 Al material itself can not be realized, and accordingly, the critical current density under a high magnetic field condition is low, and the Nb.sub.3 Al superconductors do not become cable materials for practical use. Generally speaking, it is well known that the critical current density of Nb.sub.3 Al group superconductor depends on size of the crystal grain, although a Nb.sub.3 Al superconducting phase by the above described conventional composite manufacturing method includes fine crystal grains and many magnetic flux pinning centers which are effective under a relatively low magnetic field condition, the Nb.sub.3 Al group superconductors have low critical current density under a high magnetic field condition because of shifting the composition ratio of niobium and aluminum etc.

Further, it is well known that Nb.sub.2 Al non-superconductive phase acts as an effective magnetic flux pinning center under a high magnetic field. However, the conventional diffusion reaction of niobium and aluminum generates aluminum enriched NbAl.sub.3 phase first in accordance with thermal equilibrium, and subsequently generates Nb.sub.2 Al phase and superconductive Nb.sub.3 Al phase through Nb.sub.2 Al phase. Therefore, a great effort is devoted to form Nb.sub.3 Al single phase, but Nb.sub.2 Al non-superconductive phase does not exist in the single phase.

Further, various methods for generating only superconductive Nb.sub.3 Al phase having a large amount of grain boundaries which are magnetic flux pinning centers in Nb.sub.3 Al phase, that means fining the grain size, have been attempted, but any method has not succeeded. Moreover, a method in which a diffusion reaction is performed at high temperature with Nb.sub.2 Al phase and niobium as starting materials was proposed. But, although the proposed method relatively facilitates formation of Nb.sub.3 Al phase, grain size remains still large.

The method disclosed in JP-A-3-283322 (1991) neither indicate any improvement on critical current density under a high magnetic field condition, nor any special consideration on a relationship between the Nb.sub.2 Al non-superconductive phase and the magnetic flux pinning centers under a high magnetic field condition.

SUMMARY OF THE INVENTION

(1) Objects of the Invention

One of the objects of the present invention is to provide Nb.sub.3 Al group superconductors having high critical current density under high magnetic field condition such as 20 T level and manufacturing method thereof, Nb.sub.3 Al group superconductive precursory compositions, and superconducting magnets for generating high magnetic field.

Another object of the present invention is to provide Nb.sub.3 Al group superconductors having high critical current density under a whole condition from low magnetic field to high magnetic field and manufacturing method thereof, Nb.sub.3 Al group superconductive precursory compositions, and superconducting magnets for generating high magnetic field.

(2) Methods of solving the Problems

In order to achieve the above objects, the present invention provides a composition wherein Nb.sub.2 Al phase is dispersed in Nb.sub.3 Al phase in the Nb.sub.3 Al group superconductors generated by a diffusion reaction of Nb.sub.2 Al and Nb or Nb alloys. Preferable structure for improving the critical current density under a high magnetic field condition in the above method is such that a grain size of the Nb.sub.2 Al phase is utmost 0.1 .mu.m in average diameter and an interval between each grain is in a range of 0.01-0.1 .mu.m.

In order to obtain the Nb.sub.3 Al group superconductors having the above described composition and structure, a method wherein Nb particles and Nb.sub.2 Al fine particles are dispersed and mixed each other by a mechanical alloying method is preferable because the method makes it possible to obtain large amount of the Nb.sub.3 Al group superconductive precursory compositions having a most homogeneously dispersed structure. That means, dispersing Nb.sub.2 Al fine particles having utmost 0.1 .mu.m in average diameter in Nb particles having 1-100 .mu.m in average diameter by the mechanical alloying method enables the hard Nb.sub.2 Al fine particles be dispersed in relatively soft Nb particles homogeneously.

Further, in order to obtain a superconductor having a large current carrying capacity for practical use, it is preferable to perform a deformation processing on the above Nb.sub.3 Al group superconductive precursory composition with deformation ratio at least 1000, and subsequently, to treat by a diffusion reaction at 1,000.degree.-1,800.degree. C.

Besides, the Nb.sub.3 Al group superconductors having an electro-magnetically stable multifilamentary structure can be obtained by deformation processing of the Nb.sub.3 Al group superconductive precursory composition to tubular or linear shapes, subsequent deformation processing for composing with Al alloy matrix, and a diffusion reaction.

In the present invention, the Nb.sub.3 Al group superconductors can have high critical current densities in a whole region from a low magnetic field to a high magnetic field by artificially controlling and using substantially two kinds of different magnetic flux pinning centers.

In accordance with the present invention, a part of Nb.sub.2 Al phase and niobium phase remain without reacting each other although the Nb.sub.2 Al phase and the niobium phase are used as starting materials and the remained Nb.sub.2 Al phase has a function as a magnetic flux pinning center under a high magmatic field. That means, in a chemical reaction expressed by the following equation, all of reactants are not necessarily converted to Nb.sub.3 Al phase but a part of which remain as Nb.sub.2 Al phase which disperses in Nb.sub.3 Al phase of the Nb.sub.3 Al group superconductor by terminating the reaction before completing the reaction;

2Nb.sub.2 Al+2Nb.fwdarw.Nb.sub.3 Al+Nb.sub.2 Al+Nb.fwdarw.2Nb.sub.3 Al

Accordingly, the objects of the present invention can be achieved by the diffusion reaction of lower temperature and shorter time than that of the reaction for converting all of the reactants to Nb.sub.3 Al phase.

In the present invention, it was revealed experimentally that the structure wherein a grain size of the Nb.sub.2 Al phase dispersed in the Nb.sub.3 Al phase has utmost 0.1 .mu.m in diameter and an interval between each grain is in a range of 0.01-0.1 .mu.m is significantly preferable state for making the Nb.sub.2 Al phase have a function as magnetic flux pinning center under a high magnetic field condition. Because of remarkable difficulty in dispersing Nb.sub.2 Al phase in Nb.sub.3 Al phase homogeneously by conventional powder metallurgy, a mechanical alloying method wherein Nb.sub.2 Al fine particles having utmost 0.1 .mu.m in diameter are dispersed in Nb particles having 1-100 .mu.m in diameter was adopted in the present invention. As a result, it became possible to disperse the particles homogeneously in a form that a plurality of the Nb.sub.2 Al fine particles 2 bite into the Nb particle 1 as shown in FIG. 2 because of softness of the Nb particle. Further, it was confirmed that the Nb particle was crushed by the subsequent fabrication.

By performing a deformation processing on the Nb.sub.3 Al group superconductive precursory composition obtained by the above described manner with deformation ratio at least 1000, and subsequent treating by a diffusion reaction at 1,000.degree.-1,800.degree. C., the Nb.sub.3 Al group superconductor was obtained wherein a part of respective Nb.sub.2 Al phase 2 and Nb phase 1 reacts to generate Nb.sub.3 Al 3 phase, and the Nb.sub.2 Al phase 2 is homogeneously dispersed in the Nb.sub.3 Al phase 3 as schematically shown in FIG. 1.

As explained above, the present invention generates Nb.sub.3 Al phase at lower temperature than that of the conventional method. Accordingly, the Nb.sub.3 Al phase acts as magnetic flux pinning centers under a low magnetic field condition, and the Nb.sub.2 Al phase dispersing homogeneously in the Nb.sub.3 Al phase acts effectively as magnetic flux pinning centers under a high magnetic field condition. As for the Nb phase, Nb alloys can be used in a range that the above reaction is not disturbed.

Further, a conventional reaction of niobium or Nb alloys with aluminum or Al alloys to generate Nb.sub.3 Al as expressed by the following equation can be superimposed to the above reaction effectively in practical use;

2Nb.sub.2 Al+5Nb+Al.fwdarw.2Nb.sub.3 Al+Nb.sub.2 Al+Nb

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a schematic cross section of the Nb.sub.3 Al group superconductor for explaining a structure of the present invention,

FIG. 2 is a schematic cross section of the Nb.sub.3 Al group superconductive precursory composition for explaining a structure of the present invention,

FIG. 3 is a graph showing a magnetic field/critical current density characteristics at 4.2K of the Nb.sub.3 Al group superconductor manufactured by the prior art and the present invention, and

FIG. 4 is a schematic cross section of a superconducting coil for explaining a structure of the present invention.

DETAILED DESCRIPTION OF THE EMBODIMENTS

The embodiments of the present invention are explained hereinafter referring to figures in comparison with the prior art. But the present invention is not restricted by the embodiments.

Embodiment 1

Niobium powder having about 50 .mu.m in diameter and Nb.sub.2 Al fine powder which was obtained by arc-melting and pulverizing to 0.07 .mu.m in average diameter were mixed by approximately 1:1, and the mixed powder was converted to integrated powder by a mechanical alloying method using a high energy ball milling in an inert gas atmosphere. The integrated powder had a cross section shown in FIG. 2 in which a plurality of hard Nb.sub.2 Al fine powder 2 were dispersed homogeneously in the soft and large Nb particle 1, and the Nb particle was deformed to a flat shape by a large plastic deformation.

Next, the integrated powder, that is the Nb.sub.3 Al group superconductive precursory composition, was put into a tube made from niobium having 11.0 mm in outer diameter and 7.0 mm in inner diameter and sealed hermetically. Then, the tube was drawn to be wire having 1.0 mm in outer diameter for obtaining composite multicore cables. Deformation ratio (decreasing fraction of cross sectional area) at the time was about 5.times.10.sup.4. Subsequently, the wire was heated at 1,200.degree. C. for 30 minutes for diffusion reaction to be Nb.sub.3 Al group superconductor, and then, copper was plated on surface of the wire for about 10 .mu.m thick.

Subsequently, samples were cut out from the superconductor, critical temperatures were measured under various temperatures by a resistive method, and critical currents were measured under various magnetic fields at 4.2K.

As for the critical temperature, 17.9K at middle point temperature was obtained, and it revealed that the superconductor manufactured by the present invention could be improved by 2.3K in comparison with 15.6K of the Nb.sub.3 Al conductor manufactured by the conventional composite manufacturing method. The critical current was taken as the current at a point when the voltage 1 .mu.V/cm was generated, and the critical current density was calculated by per cross sectional area without copper stabilizing material. The result is shown in FIG. 3. The curve line 4 in FIG. 3 indicates magnetic field of the present embodiment/critical current density characteristics, and the curve line 5 indicates magnetic field of Nb.sub.3 Al ultrafine multicore material by the conventional composite manufacturing method/critical current density characteristics. As the figure reveals, the superconductor obtained by the method of the present invention has higher critical current densities than that obtained by the conventional method, especially at high magnetic field in a range higher than 15-16 T. For instance, in a magnetic field of 20 T, the superconductor of the present invention is the Nb.sub.3 Al superconductor for high magnetic field having almost 1000 times critical current density in comparison with that of the prior art.

Embodiment 2

Nb.sub.3 Al group superconducting precursory composition prepared by dispersing and mixing of Nb particles and Nb.sub.2 Al fine particles by the mechanical alloying method as same as the embodiment 1 was used for manufacturing composite single core wire by fabricating a hollowed cylinder having 11.0 mm O.D. and 7.0 mm I.D., inserting an alloy rod of Al--Mg 5 atomic per cent having 6.5 mm in diameter into the above hollowed cylinder, and drawing to be a wire having 3.0 mm O.D. Subsequently, a composite multicore wire was manufactured by bundling 37 of the above composite single core wires, inserting the bundle into a hollowed niobium cylinder having 25.5 mm O.D. and 21.5 mm I.D., and drawing to be a wire having 1.0 mm O.D. A deformation ratio of the drawing was about 8.times.10.sup.3. And, a diameter of the Al--Mg 5 atomic per cent core material (matrix) was about 70 .mu.m. Subsequently, after the above wire was treated at 1,200.degree. C. for 30 minutes for a diffusion reaction to be the Nb.sub.3 Al group superconductor, copper was plated on surface of the wire for about 10 .mu.m thick, and further a heat treatment at 850.degree. C. for 50 hours in vacuum was performed.

As same as the embodiment 1, critical temperatures and magnetic field/critical current density characteristics of samples were measured. The result of the measurement revealed that the critical temperature was 17.5K, somewhat lower than that of the embodiment 1, and, as for the magnetic field/critical current density characteristics, large critical current densities were obtained in a range of magnetic field less than 18 T as shown by the curve line 6 in FIG. 3. This is because of yielding Nb.sub.3 Al phase which is generated by a reaction of Nb phase and Al--Mg alloy matrix phase in addition of Nb.sub.3 Al phase which is generated by a reaction of Nb phase and Nb.sub.2 Al phase.

Consequently, in comparison with the superconductor of the prior art shown by the curve line 5 in FIG. 3, the superconductor of the present invention was improved remarkably on the critical current density in a whole range of the magnetic field.

Embodiment 3

Nb.sub.3 Al group superconducting precursory composition prepared by dispersing and mixing of Nb particles and Nb.sub.2 Al fine particles by the mechanical alloying method as same as the embodiment 1 was used for manufacturing composite single core wire by fabricating a rod having 6.5 mm O.D., inserting the above rod into a hollowed cylinder of Al--Mg 5 atomic per cent alloy having 11.0 mm O.D. and 7.0 mm I.D., cladding outer surface of the hollowed cylinder with a niobium tube, and drawing to be a wire having 3.0 mm O.D. Subsequently, a composite multicore wire was manufactured by bundling 37 of the above composite single core wires, inserting the bundle into a hollowed niobium cylinder having 25.5 mm O.D. and 21.5 mm I.D., and drawing to be a wire having 1.0 mm O.D. Subsequently, after the above wire was treated at 1,200.degree. C. for 30 minutes for a diffusion reaction to be the Nb.sub.3 Al group superconductor, copper was plated on surface of the wire for about 10 .mu.m thick, and further a heat treatment at 850.degree. C. for 50 hours in vacuum was performed.

The result of measurement of critical temperatures and critical current densities on the samples revealed similar characteristics with those of the embodiment 2, and, in comparison with the superconductor of the prior art, the superconductor of the present invention was improved remarkably on the critical current density in a whole range of the magnetic field.

Embodiment 4

Nb.sub.3 Al group superconducting precursory composition prepared by dispersing and mixing of Nb particles and Nb.sub.2 Al fine particles by the mechanical alloying method as same as the embodiment 1 was used for manufacturing a composite wire by fabricating a plate, rolling the plate to be a foil of 0.1 mm thick, rolling an Al--Mg 5 atomic per cent alloy to be a foil of 0.1 mm thick, laminating the above two kinds of foils, winding up the laminate to be a roll so that the cross section forms a spiral, inserting the roll into a niobium tube having 25.5 mm O.D. and 21.5 mm I.D. and drawing the above tube to be the composite wire having 1.0 mm in diameter.

Subsequently, after the above wire was treated at 1,200.degree. C. for 30 minutes for a diffusion reaction to be the Nb.sub.3 Al group superconductor, copper was plated on surface of the wire for about 10 .mu.m thick, and further a heat treatment at 850.degree. C. for 50 hours in vacuum was performed.

The result of measurement of critical temperatures and critical current densities on the samples revealed similar characteristics with those of the embodiment 2, and, in comparison with the superconductor of the prior art, the superconductor of the present invention was improved remarkably on the critical current density in a whole range of the magnetic field.

Embodiment 5

A Nb.sub.3 Al superconductor of 0.25 mm thick and 5.0 mm wide was manufactured in accordance with the method explained in the embodiment 2, and was wound tightly in the region (I) of the hollowed cylindrical superconductor such as shown in FIG. 4. A conventional (Nb, Ti).sub.3 Sn ultrafine multicore superconductor was wound tightly in the region (II) as well. The above superconducting coil was a bobbin, in which the coil in the region (I) was 50 mm I.D., 130 mm O.D., and 400 mm in axial length, and the coil in the region (II) was 130 mm I.D., 500 mm O.D., and 400 mm in axial length. The region (I) and (II) were electrically connected in a series, and were energized in liquid helium by a power source.

As a result, a magnetic field of 19.5 T could be generated at the center region of the coil. If the region (I) was also wound by the conventional (Nb, Ti).sub.3 Sn ultrafine multicore superconductor, the maximum magnetic field at 4.2K was about 17 T, and accordingly, it was revealed that the present invention could increase remarkably the magnetic field generated by the superconductor with a coil having a same cross section area. Further, it can be said a significant technical advantage that such a high magnetic field as ever been achieved at 4.2K can be achieved by the present invention.

As above explained, the present invention makes it possible to generate a high magnetic field such as 20 T level at 4.2K, which has never been achieved with a superconducting magnet, with a more compact apparatus than ever economically. Further, as the present invention uses Nb.sub.3 Al group superconductor having high current density in a whole magnetic field from low to high magnetic fields, winding can be performed with only single kind of superconductor, and accordingly, the winding is relatively facilitated. Moreover, becoming it possible to generate a high magnetic field with only the Nb.sub.3 Al group superconductor can solve instantly a problem of induced radioactivity in a nuclear fusion apparatus of a magnetic confinement type, and its advantage is remarkable.

Claims

1. A method for manufacturing Nb.sub.3 Al group superconductor comprising the steps of;

dispersing and mixing Nb particles and Nb.sub.2 Al ultrafine particles by a mechanical alloying method thereby obtaining a Nb.sub.3 Al group superconducting precursory composition,

deforming said Nb.sub.3 Al group superconducting precursory composition with a deforming ratio at least 1,000, and subsequently,

performing a diffusion reaction at 1,000.degree.-1,800.degree. C.

2. A method for manufacturing Nb.sub.3 Al group superconductor comprising the steps of;

dispersing and mixing Nb particles and Nb.sub.2 Al ultrafine particles by a mechanical alloying method thereby obtaining a Nb.sub.3 Al group superconducting precursory composition,

fabricating said Nb.sub.3 Al group superconducting precursory composition to a hollowed cylinder,

inserting an aluminum alloy into said hollowed cylinder,

deforming said hollowed cylinder with said inserted aluminum alloy, and subsequently

performing a diffusion reaction at 1000.degree.-1800.degree. C.

3. A method for manufacturing Nb.sub.3 Al group superconductor comprising the steps of;

dispersing and mixing Nb particles and Nb.sub.2 Al ultrafine particles by a mechanical alloying method thereby obtaining a Nb.sub.3 Al group superconducting precursory composition,

fabricating said Nb.sub.3 Al group superconducting precursory composition to a linear body,

burying a plurality of said linear bodies into an aluminum alloy matrix,

inserting said aluminum alloy matrix with said buried linear bodies into a metallic tube,

deforming said metallic tube with said inserted matrix and linear bodies, and subsequently,

performing a diffusion reaction at 1000.degree.-1800.degree. C.

4. A method for manufacturing Nb.sub.3 Al group superconductor comprising the steps of;

dispersing and mixing Nb particles and Nb.sub.2 Al ultrafine particles by a mechanical alloying method thereby obtaining a Nb.sub.3 Al group superconducting precursory composition,

fabricating said Nb.sub.3 Al group superconducting precursory composition to a foil,

laminating said foil with an aluminum alloy foil to form a laminate,

winding up said laminate to be a roll so that its cross section forms a spiral,

inserting said roll into a metallic tube,

deforming said metallic tube with said inserted roll, and subsequently,

performing a diffusion reaction at 1000.degree.-1800.degree. C.