WO2004059666A1 - Nb3Al超伝導線材の製造方法とその方法により得られるNb3Al超伝導線材 - Google Patents
Nb3Al超伝導線材の製造方法とその方法により得られるNb3Al超伝導線材 Download PDFInfo
- Publication number
- WO2004059666A1 WO2004059666A1 PCT/JP2003/016792 JP0316792W WO2004059666A1 WO 2004059666 A1 WO2004059666 A1 WO 2004059666A1 JP 0316792 W JP0316792 W JP 0316792W WO 2004059666 A1 WO2004059666 A1 WO 2004059666A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- superconducting wire
- wire
- wire rod
- nb3al
- treatment
- Prior art date
Links
- 238000000034 method Methods 0.000 title abstract description 40
- 230000008569 process Effects 0.000 title abstract description 9
- 238000001513 hot isostatic pressing Methods 0.000 claims abstract description 42
- 238000010438 heat treatment Methods 0.000 claims abstract description 35
- 239000011159 matrix material Substances 0.000 claims abstract description 27
- 229910052802 copper Inorganic materials 0.000 claims abstract description 18
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 15
- 239000000956 alloy Substances 0.000 claims abstract description 15
- 239000002131 composite material Substances 0.000 claims abstract description 15
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 13
- 239000012298 atmosphere Substances 0.000 claims abstract description 12
- 239000011261 inert gas Substances 0.000 claims abstract description 11
- 239000011248 coating agent Substances 0.000 claims abstract description 10
- 238000000576 coating method Methods 0.000 claims abstract description 10
- 239000002243 precursor Substances 0.000 claims abstract description 10
- 229910052709 silver Inorganic materials 0.000 claims abstract description 7
- 229910052715 tantalum Inorganic materials 0.000 claims abstract description 7
- 238000004519 manufacturing process Methods 0.000 claims description 26
- 239000011162 core material Substances 0.000 claims description 23
- 238000010791 quenching Methods 0.000 claims description 23
- 230000000171 quenching effect Effects 0.000 claims description 23
- 239000003381 stabilizer Substances 0.000 claims description 14
- 230000009467 reduction Effects 0.000 claims description 7
- 238000005482 strain hardening Methods 0.000 claims description 4
- 239000000463 material Substances 0.000 abstract description 28
- 230000006641 stabilisation Effects 0.000 abstract description 6
- 238000011105 stabilization Methods 0.000 abstract description 6
- 238000001816 cooling Methods 0.000 abstract description 4
- 239000010949 copper Substances 0.000 description 42
- 230000000087 stabilizing effect Effects 0.000 description 29
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 10
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 9
- 230000009466 transformation Effects 0.000 description 9
- 238000007747 plating Methods 0.000 description 6
- 238000005491 wire drawing Methods 0.000 description 6
- 229910052786 argon Inorganic materials 0.000 description 5
- 239000007789 gas Substances 0.000 description 5
- 239000006104 solid solution Substances 0.000 description 5
- 150000001875 compounds Chemical class 0.000 description 4
- 238000001125 extrusion Methods 0.000 description 4
- 238000007733 ion plating Methods 0.000 description 4
- 229910000838 Al alloy Inorganic materials 0.000 description 3
- 238000009792 diffusion process Methods 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 238000003466 welding Methods 0.000 description 3
- 239000012300 argon atmosphere Substances 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 239000011888 foil Substances 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 229910052760 oxygen Inorganic materials 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 241001622925 Acacia coriacea Species 0.000 description 1
- 241000219977 Vigna Species 0.000 description 1
- 235000010726 Vigna sinensis Nutrition 0.000 description 1
- 230000001154 acute effect Effects 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 230000005540 biological transmission Effects 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 239000000835 fiber Substances 0.000 description 1
- 239000000945 filler Substances 0.000 description 1
- 239000010408 film Substances 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 238000009413 insulation Methods 0.000 description 1
- 239000003550 marker Substances 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 230000009257 reactivity Effects 0.000 description 1
- 239000002887 superconductor Substances 0.000 description 1
- 239000010409 thin film Substances 0.000 description 1
- 238000011426 transformation method Methods 0.000 description 1
Classifications
-
- H—ELECTRICITY
- H10—SEMICONDUCTOR DEVICES; ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
- H10N—ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
- H10N60/00—Superconducting devices
- H10N60/01—Manufacture or treatment
- H10N60/0184—Manufacture or treatment of devices comprising intermetallic compounds of type A-15, e.g. Nb3Sn
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T29/00—Metal working
- Y10T29/49—Method of mechanical manufacture
- Y10T29/49002—Electrical device making
- Y10T29/49014—Superconductor
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T29/00—Metal working
- Y10T29/49—Method of mechanical manufacture
- Y10T29/49002—Electrical device making
- Y10T29/49117—Conductor or circuit manufacturing
Definitions
- N b 3 A 1 superconducting wire art manufacturing method of the N b 3 Alpha 1 superconducting wire to be obtained by the method
- the invention of this application relates to N b 3 A 1 superconducting wire obtained Ri by the manufacturing method and method of N b 3 A 1 superconducting wire. More specifically, the invention of this application provides a relatively low cost, the Re Izu round wire and rectangular wire be manufacturable, N • b 3 which can be stabilized more superconductivity N b 3 a 1 obtained by the production process and method of a 1 superconducting wire relate superconducting wire.
- the inventors of the present application have intensively studied various methods for manufacturing superconducting wires, and have proposed Nba A1 superconducting materials having excellent high magnetic field characteristics and strain resistance characteristics. It has already succeeded in manufacturing a long superconducting wire with an ultra-fine multi-core structure with excellent stability and AC characteristics without losing its features (Patent No. 20219896).
- a 1 superconducting wire prepared by the rapid thermal quenching transformation method generally, a metal having a small electric resistance and a high thermal conductivity, such as Cu and Ag, is used.
- Superconducting wires are composited by (1) Cu ion plating, (2) Internal Ag composite stabilization, or (3) External Cu pressure bonding composite.
- Internal A g composite stabilization method is a method in which it can be beneficial to incorporate a small A g reactivity with Nb 3 A l Matoritsu box material in the precursor wire as a stabilizing material.
- Ag is exposed to a temperature exceeding its melting point during the rapid thermal quenching treatment, so it is necessary to support it with a matrix material so that the Ag does not break, and the Ag ratio can be increased too much.
- the Ag ratio is adjusted at a ratio of 0.4 or less. In this case, there is a problem that a sufficient stabilizing effect cannot be obtained depending on the use of the superconducting wire. Also, Ag is expensive, resulting in high costs.
- it is possible to use Cu with a high melting point as a stabilizing material but there is a problem that measures must be taken since Cu reacts with the matrix material.
- the Nb 3 A1 superconducting wire obtained by performing rapid heat quenching treatment is covered with Cu tape, and then the wire is processed from round to flat to form Cu and Nb.
- This is a method in which shear deformation is generated between the (matrix material) and the matrix material and Cu are pressed against each other (Japanese Patent Laid-Open No. 2000-113748).
- This method is extremely inexpensive, and provides excellent bonding at the interface between the matrix material and Cu in areas where the shear deformation is large.
- the advantage is that
- the Cu ratio as a stabilizing material is limited to about 0.3 to 0.6, and excellent bonding can be obtained only at about 60% of the entire interface. It was not enough. Above all, this method has the disadvantage that the superconducting wire can be obtained as a flat wire and cannot be manufactured as a round wire with the highest demand.
- the invention of this application has been made in view of the above circumstances, solves the problems of the prior art, is relatively inexpensive, and manufactures both round and rectangular wires. It is an object of the present invention to provide a method for producing an Nb 3 A 1 superconducting wire that is possible and can further stabilize superconductivity, and to provide an Nb 3 A 1 superconducting wire obtained by the method. Disclosure of the invention
- the invention of this application has been made in view of the above circumstances, and solves the problems of the prior art, and provides the following invention. That is, first of all, the invention of this application is based on an ultra-fine multi-layer structure in which a plurality of Nb / Al composite core materials are embedded in a Nb, Ta, Nb-based dilute alloy or a Ta-based dilute alloy as a matrix material. Precursor wire with a core structure is rapidly heated to a temperature range of around 2,000 within 2 seconds, and quenched at a speed of 2000 seconds or more at a temperature range of 400 or less at 2000 seconds. Nb 3 A 1 superconducting wire
- (BC) 680 to 85 A manufacturing method characterized by performing hot isostatic pressing (HIP) treatment for 1 to 200 hours in an inert gas atmosphere at a pressure of 40 atm or more in a temperature range of 0 to 5
- the present invention provides a production method characterized by performing the step (C) prior to the steps (A) and (B).
- the invention of this application is based on an ultra-fine multi-core structure in which a plurality of NbZA1 composite cores are embedded in Nb, Ta, Nb-based dilute alloy or Ta-based dilute alloy as a matrix material. Rapid heating and quenching treatment of a precursor wire having a temperature of 200 ° C. in a nearby temperature range within 2 seconds and a rapid cooling of 400 ° C. or less at a speed of 200 ns or more Nb 3 A 1 superconducting wire obtained by applying
- HIP hot isostatic pressing
- the seventh provides Nb 3 A 1 multifilamentary superconducting wire, characterized by being produced by any of the methods.
- FIG. 1 is a conceptual diagram illustrating a rapid heating and quenching apparatus used for manufacturing the Nb 3 A 1 superconducting wire of the present invention.
- FIG. 7 is a diagram illustrating the results, in which a black mark of the marker indicates that the HIP processing was performed. In this case, the white circle shows the case where the HIP processing was not performed.
- the method of manufacturing the Nb 3 A 1 ultrafine multi-core superconducting wire provided by the invention of this application is based on the Nb 3 A 1 superconducting wire obtained by performing the rapid heating and quenching
- Nb 3 A 1 multifilamentary superconducting wire relative to precursor wire having a multifilamentary structure consisting FILLER instrument like NbZA l complex core material and the matrix material, in the vicinity of 2000
- the temperature range is rapidly heated within 2 seconds, and the temperature range is set to 400 and below.
- the core material of the Nb / A1 composite in the precursor wire has a composition that forms a Nb-A1 supersaturated solid solution, more preferably Nb-21 to 28 at% Al alloy by rapid heating and quenching. Is preferred. Deviating from this composition is not preferable because the properties of the resulting superconducting wire are significantly deteriorated. Further, it is desirable that the NbZA1 composite core material has a structure in which A1 having a size of 1 m or less is uniformly dispersed in Nb in order to enhance the properties of the obtained superconducting wire.
- the shape of A1 may be any shape such as a granular shape, a thread shape, a thin film shape, and the like, and the dimension in this case indicates a diameter, a thickness, or the like in the above shape.
- Such an Nb / A 1 composite core material is prepared by, for example, a rod-in-tube method, a clad-chip-extrusion method, a jelly-roll method, It can be prepared by various methods such as a powder-in-tube method.
- the matrix material has excellent cold workability for forming an ultra-fine multi-core structure, etc., maintains strength during rapid heating near 2000, and affects the Nb 3 A 1 superconductivity.
- Nb, Ta, Nb-based dilute alloys or Ta-based dilute alloys have been selected because they do not exist.
- a dilute alloy is a alloy containing 3% or less of alloying elements in a single element, 5% or less in total, and Nb or Ta content of 95% or more. Gold is shown as a preferred example.
- the core material of the Nb / A1 composite material is changed to Nb-21 to 28 at% Al alloy filament (Nb-A1 supersaturated solid solution). If rapid heating is not performed as described above, a diffusion reaction occurs between the Nb / Al composite core material and the matrix material, which is not preferable. Unless quenching is performed as described above, the Nb—A1 supersaturated solid solution is not generated, and the NbZA1 compound is generated in the filament, which is not preferable because the wire becomes brittle.
- the temperature near 2000 can be set to a temperature range of about 1700 to 2100, and more specifically, a temperature range of about 1900 to 2100.
- the Nb 3 A1 superconducting wire is coated with Cu or Ag as a stabilizing material.
- means for covering the stabilizing material is not particularly limited. Insert example, may be subjected to C u plated or A g plated in Nb 3 A l superconducting wire, the Nb 3 A 1 superconducting wire in C u tube or sterling A g tubes made of oxygen-free copper You may do so.
- the amount of the stabilizing material can be set in a wide range depending on the application of the superconducting wire. For example, when the stabilizing material is C11, it can be arbitrarily set from a material having a small Cu ratio of 0.1 or less to a material having a large Cu ratio of 50 or more.
- Nb3A1 superconducting wire it is important that the entire Nb3A1 superconducting wire be in the form of a wire covered with the desired amount of stabilizing material.
- Nb 3 A l should have no air between the superconductive wire and the stabilizing material is hot isostatic compacting of the next step in (HIP) C This is because the u-tube or Ag-tube is crushed and the bonding interface is improved.
- HIP hot isostatic compacting of the next step in (HIP) C
- the HIP treatment is performed for 10 minutes or more in an inert gas atmosphere at a pressure of 40 atm or more, so that good bonding to the interface of the stabilizing material Z matrix material is obtained. . If the pressure is less than 40 atm or the time is less than 10 minutes, it is not preferable because a good interface between the stabilizer and the matrix material cannot be obtained.
- the processing temperature is preferably 450 or more when Cu is coated as a stabilizing material, and 380 or more when Ag is coated as it is preferable because good bonding can be realized.
- step (C) heat treatment is performed for 1 to 200 hours in a temperature range of 680 to 850 to transform the Nb—21 to 28 at% Al alloy filament into Nb 3 A1 filament. I have to.
- Nb 3 A 1 multifilamentary superconducting wire is manufacturing.
- Makikome coiled by the Nb 3 A 1 multifilamentary superconducting wire rod such as bending covered with a dielectric film
- the insulating coating and the processing into the desired shape can be performed before the step (B).
- Nb 3 A 1 ultrafine multi-core superconducting wire provided by the invention of this application, before or after the step (A), (D) cold working with a cross-sectional reduction rate of 60% or less is performed.
- Nb 3 after quenching The A1 superconducting wire has excellent composition workability in both the matrix material and the Nb—21 to 28 at% A1 alloy filament. Therefore, before or after coating with a stabilizing material, by performing cold working following mild reduction of area of 60%, it is possible to improve the characteristics of Nb 3 A 1 multifilamentary superconducting wires obtained .
- the process (BC) may be performed in the temperature range of 680 to 850 instead of the processes (B) and (C).
- Steps (B) and (C) can be performed simultaneously by performing hot isostatic pressing (HIP) for 1 to 200 hours in an inert gas atmosphere at a pressure of 40 atm or more. It is possible.
- HIP hot isostatic pressing
- a 1 can be used as a stabilizing material.
- the melting point of A 1 (at 660) is lower than the heat treatment temperature for the transformation in step (C)
- disposing A 1 on the Nb 3 A 1 ultrafine multifilamentary superconducting wire is performed in the step ( Must be done after C).
- the HIP treatment is performed for 10 minutes or more in an inert gas atmosphere at a temperature range of 230 to 50 Ot: and a pressure of 40 atm or more.
- a 1 as a stabilizing material as in the case of the above-mentioned Cu, Ag, an Nb 3 A 1 conductive wire or vacuum-sealed by A 1 tube, A 1 plated, A 1 Conform Techniques such as extrusion can be used.
- HIP treatment temperature is less than 23 Ot :, a good bonding interface is not formed, and if it exceeds 500, A1 undergoes a diffusion reaction with the matrix material to form a thick intermediate compound. Not preferred.
- Nb 3 A 1 multifilamentary superconducting wire is the transmission of elementary particles Since high rate, Nb 3 A 1 multifilamentary superconducting wire using A 1 as the stabilizer is a very useful as a superconducting magnet or the like for use in the study of high-energy physics.
- the method of manufacturing the Nb 3 A 1 ultrafine multifilamentary superconducting wire of the invention of this application makes it possible to achieve extremely good bonding at the interface between the stabilizing material and the matrix material.
- a superconducting wire having excellent characteristics can be obtained.
- this method is simple and lower in cost than the conventional (1) Cu ion plating method and (2) internal Ag complex stabilization method.
- the amount of the stabilizer can be set in a wide range, and A1 can be used as the stabilizer.
- the method of the invention of this application is higher in cost than the conventional (3) composite method of external Cu pressure welding, it is significantly superior in terms of the stabilizing characteristics and application of the obtained wire. That is, it can be said that the method of the invention of this application is the most excellent as a whole as compared with the conventional method of manufacturing a superconducting wire.
- Nb foil and an A1 foil with a thickness of 3: 1 at% are superimposed and wound into a roll, processed into a line by extrusion and wire drawing (jelly-roll method), The wire was cut into a predetermined length.
- 120 wires are bundled and packed in a Nb pipe, and a long precursor with an ultra-fine multi-core wire structure in which a 120-core Nb / A1 composite is embedded in an Nb matrix by extrusion and wire drawing.
- the body wire was created.
- This precursor wire was heated to 2000 in 0.1 second by energizing while moving at a speed of 1 m / s using the rapid heating and quenching device shown in Fig. 1, and then passed through the Ga bath. Quenched. Here, it was confirmed that the Nb / A1 complex in this wire was changed to a Nb—A1 solid solution. Was.
- this wire was subjected to Cu plating so that the copper ratio became (a) 0.4 and (b) 0.2, and was subjected to mild wire drawing with a reduction in area of about 5%.
- Nb / Nb-25 at% A1 wire obtained by rapid heating and quenching in the same manner as in Example 1 was covered with an oxygen-free copper pipe, and the wire was drawn so that the copper and the wire were in light contact with each other.
- the surplus copper pipes at both ends were sandwiched between vice and crushed. By welding this crushed part in a vacuum, Nb / Nb—
- a 1 wire was sealed in vacuum.
- argon Kiri ⁇ gas 900 atm, subjected for 1 hour to HIP treatment at 600 in a vacuum, subjected to transformation heat treatment of 800 in 10 hours, Nb 3 A 1 multifilamentary superconducting wire Wood was obtained.
- Nb 3 A 1 multifilamentary superconducting wire Wood was obtained.
- a wire rod obtained by rapid heating and quenching in the same manner as in Example 1 was subjected to Cu plating, and an alumina fiber was wound around the surface to perform heat-resistant insulation treatment.
- the inner diameter was 20 mm
- the outer diameter was 3 Omm
- 9 0 0 atm was a HIP treatment for 1 0 hours 8 0 0 argon gas atmosphere, be N b-A 1 supersaturated solid solution in the wire is transformed into N b 3 A 1-phase confirmed.
- observation of the cross section confirmed that a strong bond was formed at the interface between Nb and Cu.
- the critical current of the coil are substantially coinciding with the critical current of the short sample, it was found that the stabilized N b 3 A 1 superconducting magnet can be realized.
- a wire rod obtained by rapid heating and quenching in the same manner as in Example 1 was flattened by crushing by a single-hole processing.
- the copper plated applied to the rectangular wire is subjected to a transformation heat treatment and HIP treatment under the same conditions as in Example 1 to obtain a N b 3 A 1 superconducting wire.
- a transformation heat treatment and HIP treatment under the same conditions as in Example 1 to obtain a N b 3 A 1 superconducting wire.
- a wire rod obtained by rapid heating and quenching in the same manner as in Example 1 was subjected to Cu plating, then subjected to HIP treatment at various temperature, pressure and time conditions, and then subjected to a transformation heat treatment under the same conditions as in Example 1 to obtain Nb 3 A 1 superconducting wire was obtained.
- a wire rod obtained by rapid heating and quenching in the same manner as in Example 1 was subjected to an Ag plating over the entire surface so that the Ag ratio became 0.2, and then subjected to light wire drawing with a reduction in area of about 5%.
- a HIP treatment at 600 at 900 bar under an argon atmosphere was performed for 1 hour, followed by a transformation heat treatment at 800 at 10 in vacuum for 10 hours to obtain an Nb 3 A1 superconducting wire.
- Example 6 In the same manner as in Example 6, an Ag plating with an Ag ratio of 0.2 was performed, and a wire rod that had been subjected to wire drawing with a reduction in area of about 5% was subjected to HIP treatment under various temperature, pressure, and time conditions. followed by transformation heat treatment under the same conditions as in example 6 to give us N b 3 a 1 superconducting wire.
- the wire rod obtained by rapid heating and quenching in the same manner as in Example 1 was subjected to transformation heat treatment at 800 at 10 ° C. in a vacuum, and then covered with A 1 pipe and subjected to mild wire drawing. The end was crushed with a vise and welded in a vacuum to produce a wire sealed in a long A1 tube. Next, this wire was subjected to HIP treatment in argon gas at 900 atm and 400 to obtain an Nb 3 A1 superconducting wire.
- the A1 tube-filled Nb 3 A 1 superconducting wire produced in the same manner as in Example 8 was subjected to HIP treatment in an argon gas at 900 atm and 55 Ot for 30 minutes to obtain an Nb 3 A1 superconducting wire.
- Nb A 1 3 Compound of thickness about 20 m at the boundary of the Nb matrix and A 1 was produced. This is probably because the HIP treatment temperature was too high when A1 was used as a stabilizing material.
- the NbA l 3 of compounds enhances the electrical and thermal resistance between the A 1 and the matrix, is cheap 'Joka degree as compared with the case of Example 8 was reduced .
- the A 1 tube sealed Nb 3 A 1 superconducting wire was produced in the same manner as in Example 8, 900 atm, to obtain a Nb 3 A 1 superconducting wire by 3 hours HIP treatment at 200 3 ⁇ 4 of argon gas.
- any round wire and rectangular wire be manufacturable, N b 3 A 1 than capable of stabilizing more superconductivity N b 3 a 1 superconducting wire obtained by the process and method of conducting wire are provided.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Superconductors And Manufacturing Methods Therefor (AREA)
Abstract
Description
Claims
Priority Applications (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US10/513,857 US7134181B2 (en) | 2002-12-25 | 2003-12-25 | Method for producing Nb3Al superconductive wire |
EP03789636A EP1577903B1 (en) | 2002-12-25 | 2003-12-25 | Method for producing nb3al superconductive wire and nb3al superconductive wire obtained by said method |
DE60328041T DE60328041D1 (de) | 2002-12-25 | 2003-12-25 | Verfahren zur herstellung eines supraleitenden nb3al drahts und durch den prozess hergestellter supraleitender nb3al draht |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2002-374229 | 2002-12-25 | ||
JP2002374229A JP3944573B2 (ja) | 2002-12-25 | 2002-12-25 | Nb3Al超伝導線材の製造方法とその方法により得られるNb3Al超伝導線材 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2004059666A1 true WO2004059666A1 (ja) | 2004-07-15 |
Family
ID=32677288
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2003/016792 WO2004059666A1 (ja) | 2002-12-25 | 2003-12-25 | Nb3Al超伝導線材の製造方法とその方法により得られるNb3Al超伝導線材 |
Country Status (5)
Country | Link |
---|---|
US (1) | US7134181B2 (ja) |
EP (1) | EP1577903B1 (ja) |
JP (1) | JP3944573B2 (ja) |
DE (1) | DE60328041D1 (ja) |
WO (1) | WO2004059666A1 (ja) |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN102543311A (zh) * | 2012-02-23 | 2012-07-04 | 西南交通大学 | 一种Nb3Al/Nb多芯复合超导线材的制备方法 |
CN103329219A (zh) * | 2011-01-18 | 2013-09-25 | 独立行政法人物质·材料研究机构 | 混合阻挡层型Nb3Al超导多芯线材 |
Families Citing this family (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP4822781B2 (ja) * | 2005-09-15 | 2011-11-24 | 独立行政法人理化学研究所 | Nb3Al超伝導コイルの接続方法 |
JP2010244745A (ja) * | 2009-04-02 | 2010-10-28 | Hitachi Cable Ltd | Nb3Al超電導線材、及びNb3Al超電導線材の製造方法 |
CN101872660B (zh) * | 2010-05-21 | 2012-04-18 | 西北有色金属研究院 | 一种矩形截面Cu-Nb多芯复合线材的制备方法 |
CN101859612B (zh) * | 2010-05-24 | 2011-12-07 | 西部超导材料科技有限公司 | 一种Nb3Sn线材用CuNb复合管的制备方法 |
CN105304208B (zh) * | 2015-10-13 | 2017-04-05 | 西部超导材料科技股份有限公司 | 一种Nb3Al超导线材前驱体的制备方法 |
CN109609750B (zh) * | 2019-01-17 | 2024-04-12 | 西南石油大学 | 一种制备高性能超导线材的零张力同步传动热处理系统 |
Citations (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS62278253A (ja) * | 1986-05-26 | 1987-12-03 | Fujikura Ltd | Nb↓3A1系超電導線の製造方法 |
JPH04334822A (ja) * | 1991-05-10 | 1992-11-20 | Hitachi Ltd | 化合物超電導線材の製造方法 |
JPH06223647A (ja) * | 1992-12-14 | 1994-08-12 | Furukawa Electric Co Ltd:The | NbTi超電導ビレットの製造方法 |
JPH06283059A (ja) * | 1993-03-25 | 1994-10-07 | Natl Res Inst For Metals | Nb3 Al極細多芯超電導線材の製造法 |
JPH11102617A (ja) * | 1997-09-29 | 1999-04-13 | Hitachi Cable Ltd | Nb3Al系化合物超電導体及びその製造方法 |
JP2000113748A (ja) | 1998-10-09 | 2000-04-21 | Natl Res Inst For Metals | Nb3 Al化合物系超電導線およびその製造方法 |
JP2000195349A (ja) * | 1998-12-25 | 2000-07-14 | Hitachi Cable Ltd | Nb3Al化合物系超電導線およびその製造方法 |
JP2001052547A (ja) * | 1999-06-03 | 2001-02-23 | Natl Res Inst For Metals | Nb3Al化合物系超電導線およびその製造方法 |
JP2002033025A (ja) * | 2000-07-18 | 2002-01-31 | National Institute For Materials Science | Nb3Al超電導多芯線とその製造方法 |
Family Cites Families (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2693255B2 (ja) * | 1990-05-11 | 1997-12-24 | 日立電線株式会社 | Nb▲下3▼Al系超電導線材の製造方法並びに製造装置 |
US5501746A (en) * | 1993-12-16 | 1996-03-26 | Mitsubishi Denki Kabushiki Kaisha | Process for preparing superconducting wire |
US6372054B1 (en) * | 1999-06-04 | 2002-04-16 | Japan As Represented By Director General Of National Research Institute For Metals | Process for producing ultrafine multifilamentary Nb3(A1,Ge) or Nb3(A1,Si) superconducting wire |
JP3577506B2 (ja) * | 1999-11-09 | 2004-10-13 | 独立行政法人物質・材料研究機構 | Cu添加Nb3Al極細多芯超伝導線材とその製造方法 |
JP3588628B2 (ja) * | 2000-04-06 | 2004-11-17 | 独立行政法人物質・材料研究機構 | Nb3Al極細多芯超伝導線の製造方法 |
US6699821B2 (en) * | 2001-04-09 | 2004-03-02 | Composite Materials Technology, Inc. | Nb3Al superconductor and method of manufacture |
-
2002
- 2002-12-25 JP JP2002374229A patent/JP3944573B2/ja not_active Expired - Lifetime
-
2003
- 2003-12-25 WO PCT/JP2003/016792 patent/WO2004059666A1/ja active Application Filing
- 2003-12-25 EP EP03789636A patent/EP1577903B1/en not_active Expired - Lifetime
- 2003-12-25 US US10/513,857 patent/US7134181B2/en not_active Expired - Fee Related
- 2003-12-25 DE DE60328041T patent/DE60328041D1/de not_active Expired - Lifetime
Patent Citations (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS62278253A (ja) * | 1986-05-26 | 1987-12-03 | Fujikura Ltd | Nb↓3A1系超電導線の製造方法 |
JPH04334822A (ja) * | 1991-05-10 | 1992-11-20 | Hitachi Ltd | 化合物超電導線材の製造方法 |
JPH06223647A (ja) * | 1992-12-14 | 1994-08-12 | Furukawa Electric Co Ltd:The | NbTi超電導ビレットの製造方法 |
JPH06283059A (ja) * | 1993-03-25 | 1994-10-07 | Natl Res Inst For Metals | Nb3 Al極細多芯超電導線材の製造法 |
JPH11102617A (ja) * | 1997-09-29 | 1999-04-13 | Hitachi Cable Ltd | Nb3Al系化合物超電導体及びその製造方法 |
JP2000113748A (ja) | 1998-10-09 | 2000-04-21 | Natl Res Inst For Metals | Nb3 Al化合物系超電導線およびその製造方法 |
JP2000195349A (ja) * | 1998-12-25 | 2000-07-14 | Hitachi Cable Ltd | Nb3Al化合物系超電導線およびその製造方法 |
JP2001052547A (ja) * | 1999-06-03 | 2001-02-23 | Natl Res Inst For Metals | Nb3Al化合物系超電導線およびその製造方法 |
JP2002033025A (ja) * | 2000-07-18 | 2002-01-31 | National Institute For Materials Science | Nb3Al超電導多芯線とその製造方法 |
Non-Patent Citations (2)
Title |
---|
INOUE K: "Development of Nb3Al conductors having great potentialities in high energy physics", SUPERCONDUCTING MATERIALS FOR HIGH ENERGY COLLIDERS, 25 October 1999 (1999-10-25), pages 143 - 159 |
See also references of EP1577903A4 |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN103329219A (zh) * | 2011-01-18 | 2013-09-25 | 独立行政法人物质·材料研究机构 | 混合阻挡层型Nb3Al超导多芯线材 |
CN102543311A (zh) * | 2012-02-23 | 2012-07-04 | 西南交通大学 | 一种Nb3Al/Nb多芯复合超导线材的制备方法 |
CN102543311B (zh) * | 2012-02-23 | 2013-10-16 | 西南交通大学 | 一种Nb3Al/Nb多芯复合超导线材的制备方法 |
Also Published As
Publication number | Publication date |
---|---|
US20050176587A1 (en) | 2005-08-11 |
DE60328041D1 (de) | 2009-07-30 |
JP2004207013A (ja) | 2004-07-22 |
EP1577903A4 (en) | 2008-03-26 |
JP3944573B2 (ja) | 2007-07-11 |
US7134181B2 (en) | 2006-11-14 |
EP1577903B1 (en) | 2009-06-17 |
EP1577903A1 (en) | 2005-09-21 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
US7226894B2 (en) | Superconducting wire, method of manufacture thereof and the articles derived therefrom | |
JPH0444365B2 (ja) | ||
JP4443855B2 (ja) | MgB2製の中空フィラメントを基材とする超伝導線材の製法 | |
JP3944573B2 (ja) | Nb3Al超伝導線材の製造方法とその方法により得られるNb3Al超伝導線材 | |
JP4752505B2 (ja) | 酸化物超電導線材の製造方法および酸化物超電導線材の改質方法 | |
JPH0419918A (ja) | Nb↓3Al系超電導線材の製造方法並びに製造装置 | |
US6376099B1 (en) | CU-containing NB3A1 multifilamentary superconductive wire and process for producing the same | |
US6845254B2 (en) | Nb3Ga multifilamentary superconducting wire and process for preparing the same | |
WO2006098269A1 (ja) | 超電導線材の製造方法 | |
JP4556343B2 (ja) | 長尺複合体の製造方法 | |
Flukiger et al. | Composite core Nb/sub 3/Sn wires: preparation and characterization | |
JPH0574235A (ja) | アルミニウム安定化超電導線 | |
JP3673831B2 (ja) | Nb3Sn線材の製造方法 | |
JPH0315115A (ja) | 金属被覆酸化物超電導線材 | |
JP3948291B2 (ja) | Nb3Al系化合物超電導線およびその製造方法 | |
JP4039049B2 (ja) | 多芯酸化物超電導線材の製造方法 | |
JP3257703B2 (ja) | パルス又は交流用電流リード及び前記電流リードにa15型化合物超電導撚線を接続する方法 | |
JPH01189813A (ja) | 酸化物超電導線材 | |
Rudziak et al. | Development of multifilament jelly-roll NbAl precursor for melt-quench processing | |
JPH0760620B2 (ja) | Nb3 Al極細多芯超電導線材の製造法 | |
JP3516060B2 (ja) | Nb3(Al,Ge)またはNb3(Al,Si)極細多芯超伝導線の製造方法 | |
JPH06510157A (ja) | テクスチャード超伝導体とその製造方法 | |
JP2002063816A (ja) | Nb3Al系超電導線の製造方法 | |
JPS63102115A (ja) | 超電導合金線材の製造方法 | |
JPS59191213A (ja) | 化合物複合超電導体の製造方法 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
AK | Designated states |
Kind code of ref document: A1 Designated state(s): US |
|
AL | Designated countries for regional patents |
Kind code of ref document: A1 Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IT LU MC NL PT RO SE SI SK TR |
|
121 | Ep: the epo has been informed by wipo that ep was designated in this application | ||
WWE | Wipo information: entry into national phase |
Ref document number: 2003789636 Country of ref document: EP |
|
WWE | Wipo information: entry into national phase |
Ref document number: 10513857 Country of ref document: US |
|
WWP | Wipo information: published in national office |
Ref document number: 2003789636 Country of ref document: EP |