WO2013187268A1 - FIL SUPRACONDUCTEUR MgB2 ET SON PROCÉDÉ DE FABRICATION - Google Patents

FIL SUPRACONDUCTEUR MgB2 ET SON PROCÉDÉ DE FABRICATION Download PDF

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Publication number
WO2013187268A1
WO2013187268A1 PCT/JP2013/065310 JP2013065310W WO2013187268A1 WO 2013187268 A1 WO2013187268 A1 WO 2013187268A1 JP 2013065310 W JP2013065310 W JP 2013065310W WO 2013187268 A1 WO2013187268 A1 WO 2013187268A1
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acid
magnesium
superconducting wire
magnesium diboride
mgb
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PCT/JP2013/065310
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English (en)
Japanese (ja)
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和英 田中
近藤　保夫
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株式会社 日立製作所
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    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F6/00—Superconducting magnets; Superconducting coils
    • H01F6/06—Coils, e.g. winding, insulating, terminating or casing arrangements therefor
    • 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
    • H10N60/0856—Manufacture or treatment of devices comprising metal borides, e.g. MgB2
    • 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
    • H10N60/20—Permanent superconducting devices
    • H10N60/202—Permanent superconducting devices comprising metal borides, e.g. MgB2

Definitions

  • the present invention relates to a magnesium diboride (hereinafter abbreviated as MgB 2 ) superconducting wire, and in particular, relates to a MgB 2 superconducting wire that achieves both improved superconducting properties and a longer practical area, and a method for producing the same.
  • MgB 2 magnesium diboride
  • MgB 2 superconductor has the highest critical temperature (39 K) as a metal-based superconductor, and is expected as a superconducting material for realizing a superconducting electromagnet that operates without liquid helium (for example, 10 to 20 K). If the MgB 2 superconductor is applied to a superconducting magnet in a superconducting magnet system (eg, NMR or MRI), the temperature margin (difference between critical temperature and operating temperature) can be made larger than before, so that quenching is less likely to occur and thermal A highly stable superconducting magnet system can be provided.
  • a superconducting magnet system eg, NMR or MRI
  • MgB 2 superconducting wire is a method of filling a metal tube with a mixed powder of Mg (magnesium) powder and B (boron) powder or MgB 2 powder and further adding a third element to the metal tube, and then drawing the wire.
  • Mg manganesium
  • B boron
  • MgB 2 powder MgB 2 powder
  • the powder in tube method in order to sinter produced and the MgB 2 phase by reacting a Mg powder and the B powder, the heat treatment at the normal 600 ° C. or higher temperature range after the wire drawing is performed.
  • MgB 2 superconducting wire Since MgB 2 superconducting wire is still under development, various research and development have been conducted with the aim of improving the superconducting properties. Further, as a superconducting wire constituting the superconducting electromagnet, it is necessary to maintain a high current density even in a high magnetic field generated by the superconducting electromagnet itself and to make a uniform long wire (for example, a length of 1 km or more). .
  • MgB 2 superconducting wire In order to improve the superconducting properties of the MgB 2 superconducting wire, it prevents Mg oxidation and improves the MgB 2 phase formation rate, or suppresses the coarsening of the MgB 2 phase grains (ie increases the grain boundaries). It is effective to improve the density of the magnetic flux pinning center. In order to realize these (antioxidation of Mg and suppression of coarsening of crystal grains), it is effective to lower the temperature of the heat treatment for generating the MgB 2 phase.
  • Patent Document 1 Japanese Patent Laid-Open No. 2008-120659 discloses a method for producing a magnesium diboride superconductor in which a mixed powder of magnesium and boron is fired, and is 0.9 to 25 mol% with respect to magnesium.
  • a method for producing a magnesium diboride superconductor is disclosed, wherein silver is added to form a mixed powder, and the firing temperature is set to less than 600 ° C.
  • Patent Document 1 it is possible to provide a magnesium diboride superconductor having superconducting characteristics similar to or higher than those obtained at a firing temperature of 600 ° C. or higher even when fired at a firing temperature of less than 600 ° C. Has been.
  • Patent Document 2 Japanese Patent Application Laid-Open No. 2012-014912 discloses a manufacturing method of a magnesium diboride superconducting wire that is drawn after filling a metal pipe with a raw material powder, and includes a fatty acid metal salt or the fatty acid metal.
  • a method for producing a magnesium diboride superconducting wire characterized by adding a mixture of a salt and a fatty acid to the raw material powder is disclosed. According to Patent Document 2, it has been reported to be able to provide a high performance and wire length Shakuka the manufacturing method of the MgB 2 superconducting wire combining its and MgB 2 superconducting wire according to which the superconducting properties.
  • Patent Document 1 and Patent Document 2 described above are considered to be useful prior arts, the present inventors have made various MgB 2 superconductors as superconducting coil wires based on the descriptions in Patent Document 1 and Patent Document 2. Wires were prepared and their superconducting properties were evaluated. However, the superconducting property of the obtained MgB 2 superconducting wire is almost the same as that of Patent Document 2, and the improvement of the superconducting property as expected from the combination with the technology of Patent Document 1 was not obtained.
  • the superconducting characteristics eg, critical current density-magnetic field characteristics
  • the performance of the superconducting magnet eg, the maximum generated magnetic field
  • an object of the present invention in the MgB 2 superconducting wire according to a powder-in-tube method, higher performance and wire length MgB 2 superconducting wire and scale of is both realization of superconducting properties and a manufacturing method thereof There is.
  • One aspect of the present invention is an MgB 2 superconducting wire comprising a magnesium diboride (MgB 2 ) core and a metal sheath covering the MgB 2 core in order to achieve the above object,
  • the MgB 2 core is a MgB 2 polycrystal
  • alkali metal oxide particles and magnesium-silver alloy (Mg-Ag alloy) particles having a higher ionization tendency than Mg are dispersed,
  • the average particle diameter of the Mg-Ag alloy particles is 1 ⁇ m or less
  • An MgB 2 superconducting wire is provided, wherein the alkali metal oxide particles have an average particle size of 0.1 ⁇ m or less.
  • a manufacturing method of the MgB 2 superconducting wire comprising a metal sheath covering the MgB 2 core and said MgB 2 core, Preparing a powder filling the MgB 2 core; Filling the metal tube serving as the metal sheath with the filled powder to produce a powder-filled billet; Applying a wire drawing process to the powder-filled billet to produce a precursor wire; A step of performing a heat treatment on the precursor wire to form the MgB 2 core, The step of preparing the filling powder includes a step of preparing an additive by mixing an alkali metal fatty acid salt having a higher ionization tendency than Mg and a silver oxide (Ag 2 O) powder, and the additive and the Mg powder.
  • a step of mixing B powder The heat treatment is performed in a non-oxidizing atmosphere and in a temperature range of 500 ° C. or more and 550 ° C. or less,
  • the MgB 2 core is a MgB 2 polycrystal, In the MgB 2 polycrystal, oxide particles of alkali metal and Mg-Ag alloy particles constituting the fatty acid alkali metal salt are dispersed, The average particle diameter of the Mg-Ag alloy particles is 1 ⁇ m or less, Provided is a method for producing a MgB 2 superconducting wire, wherein the alkali metal oxide particles have an average particle size of 0.1 ⁇ m or less.
  • the present invention in the MgB 2 superconducting wire by the powder-in-tube method, it is possible to provide an MgB 2 superconducting wire in which both higher performance of the superconducting characteristics and longer wire are embodied, and a method for manufacturing the same. it can.
  • FIG. 3 is a schematic cross-sectional view of AgO particles coated with a fatty acid alkali metal salt.
  • 3 is a graph showing the relationship between the critical current density of MgB 2 superconducting wire and the molar ratio of AgO addition to Mg addition with and without addition of fatty acid alkali metal salt.
  • 3 is a graph showing the relationship between the critical current density of MgB 2 superconducting wire and the molar ratio of the amount of lithium stearate added to the amount of Mg added.
  • 4 is a graph showing the relationship between the critical current density of MgB 2 superconducting wire and the molar ratio of AgO addition amount to Mg addition amount. Is a graph showing the relationship between the critical current density and the applied magnetic field of MgB 2 superconducting wire.
  • the present invention can be modified or changed as follows in the MgB 2 superconducting wire (I) and the method (II) for producing the MgB 2 superconducting wire according to the present invention described above.
  • the alkali metal oxide particles are mainly present in the grain boundary region of each crystal particle of the MgB 2 polycrystal, and the Mg-Ag alloy particles are mainly present inside the crystal particles.
  • “mainly present in the grain boundary region” means that there are more in the grain boundary region than in the crystal grain
  • “mainly present in the crystal grain” means It means that there are more inside the crystal grain than in the region.
  • the content of the alkali metal and the addition amount of the fatty acid alkali metal salt are 0.5% or more and 20% or less in a molar ratio with respect to the Mg content and the Mg addition amount in the MgB 2 polycrystal, respectively.
  • the content of Ag and the addition amount of Ag 2 O are 0.8% or more and 40% or less in molar ratio with respect to the Mg content and the Mg addition amount, respectively.
  • the alkali metal is at least one selected from lithium (Li) and potassium (K).
  • the metal sheath and the metal tube have a structure in which iron, copper, niobium, tantalum, nickel, an alloy thereof, or a composite thereof is combined.
  • (V) Fatty acid constituting the fatty acid alkali metal salt is butyric acid, valeric acid, caproic acid, enanthic acid, caprylic acid, pelargonic acid, capric acid, lauric acid, myristic acid, pentadecylic acid, palmitic acid, palmitoleic acid, margarine Acid, stearic acid, oleic acid, vaccenic acid, linoleic acid, linolenic acid, eleostearic acid, nonadecanoic acid, arachidic acid, icosatrienoic acid, arachidonic acid, behenic acid, lignoceric acid, nervonic acid, serotic acid, montanic acid, and It is one selected from melicic acid.
  • the present invention is, in another aspect, provides a superconducting coil, characterized in that using the MgB 2 superconducting wire according to the present invention described above.
  • the present invention provides, as another aspect, a superconducting magnet system using the superconducting coil according to the present invention.
  • the present inventors tried to improve the superconducting characteristics of the MgB 2 superconducting wire by combining the techniques of Patent Documents 1 and 2, but the superconducting characteristics expected from a simple combination are expected. Improvement was not obtained. Therefore, as a result of investigating in detail the factors that did not improve the superconducting characteristics, Ag particles added based on Patent Document 1 coalesce during wire drawing, and therefore desirable fine dispersion cannot be realized. There was found. The inventors of the present invention have intensively studied in order to realize a fine structure suitable for improving the superconducting characteristics, and finally found a suitable manufacturing method to complete the present invention.
  • FIG. 1A is a schematic cross-sectional view showing a structural example of an MgB 2 superconducting wire according to the present invention.
  • the MgB 2 superconducting wire 1 has a structure composed of an MgB 2 core 10 and a metal sheath 20.
  • FIG. 1A shows a case where the metal sheath 20 is a composite structure (hereinafter referred to as a Cu / Fe structure) composed of a copper (Cu) layer serving as a stabilization layer 23 and an iron (Fe) layer serving as a barrier layer 22. It was.
  • the stabilization layer 23 copper (Cu), aluminum (Al), silver (Ag), gold (Au), or an alloy thereof can be used.
  • niobium (Nb), iron (Fe), tantalum (Ta), nickel (Ni), or an alloy thereof can be used.
  • FIG. 1B is a schematic cross-sectional view showing another structural example of the MgB 2 superconducting wire according to the present invention.
  • the MgB 2 superconducting wire 2 has a structure composed of a plurality of MgB 2 cores 10 and a metal sheath 21.
  • FIG. 1B shows a case where the metal sheath 21 is composed of a Cu layer that becomes the stabilization layer 24 and an Fe layer that becomes the barrier layer 22.
  • FIG. 2 is a schematic cross-sectional view showing the fine structure of the MgB 2 core of the MgB 2 superconducting wire according to the present invention.
  • MgB 2 core 10 of MgB 2 superconducting wire 1 according to the present invention is a polycrystal MgB 2 crystal grains 11, Mg-Ag alloy particles 12 and the oxide of an alkaline metal Particles 13 are dispersed in the MgB 2 polycrystal.
  • the Mg—Ag alloy particles 12 have an average particle size of 0.05 ⁇ m or more and 1 ⁇ m or less, and are present in the interior of the particle more than the grain boundary region of the MgB 2 crystal particle 11.
  • Alkali metal oxide particles 13 have an average particle size of 0.01 ⁇ m or more and 0.1 ⁇ m or less, and are present more in the grain boundary region than inside the MgB 2 crystal particles 11.
  • Mg-Ag alloy particles 12 exceeds 1 ⁇ m, the effect of improving the superconducting properties is hardly obtained.
  • the average particle size of the alkali metal oxide particles 13 exceeds 0.1 ⁇ m, the effect of improving the superconducting properties is hardly obtained.
  • Mg-Ag alloy particles having an average particle size of less than 0.05 ⁇ m and alkali metal oxide particles having an average particle size of less than 0.01 ⁇ m are formed and dispersed while being controlled within the scope of the production method according to the present invention described later. It is difficult.
  • the Ag content in the MgB 2 core 10 is preferably 0.8% to 40% in terms of a molar ratio with respect to the Mg content. If the Ag content is outside this range, it will not reach the level at which the effect of improving the superconducting properties is required.
  • the alkali metal content in the MgB 2 core 10 is preferably 0.5% or more and 20% or less in terms of a molar ratio with respect to the Mg content. If the alkali metal content is out of the range, it does not reach a level where the effect of improving the superconducting characteristics is required. The rules for the Ag content and the alkali metal content will be described in detail later.
  • FIG. 3 is a flowchart showing a process example of a method for producing an MgB 2 superconducting wire according to the present invention.
  • the manufacturing method according to the present invention will be described with reference to FIG. 3 using the MgB 2 superconducting wire (the embodiment of FIG. 1A) as an example.
  • Mg powder, B powder, AgO powder, and fatty acid alkali metal salt powder are prepared as starting materials.
  • AgO powder is used as an Ag supply source. Thereby, coalescence of Ag component particles during the wire drawing process can be suppressed.
  • AgO powder and fatty acid alkali metal salt powder are thoroughly mixed using a mixing device to prepare an additive composed of AgO particles coated with a fatty acid alkali metal salt.
  • FIG. 4 is a schematic cross-sectional view of AgO particles coated with a fatty acid alkali metal salt.
  • the aggregation of the AgO particles 31 is further suppressed, and in the steps (mixing step, wire drawing step, heat treatment step) described later, in the filled powder and the MgB 2 core
  • the dispersion state of the Ag component in the inside becomes good.
  • a mixing device a planetary ball mill device, a ball mill device, a V mixer, a floating bowl mixing, or the like can be used.
  • the alkali metal constituting the fatty acid alkali metal salt an element having a higher ionization tendency than Mg is preferable.
  • the ionization tendency of a metal indicates the degree of easy oxidation (magnification of the reducing power), and the metal having a higher ionization tendency has a stronger reducing power.
  • AgO thermally decomposes into Ag and O 2 at around 230 ° C, but by using an alkali metal that has a higher ionization tendency than Mg, the alkali metal is preferentially oxidized, thus preventing oxidation of Mg. be able to. That is, such an alkali metal functions as an oxygen getter agent (reducing agent) at the time of AgO decomposition.
  • the alkali metal is preferably Li and / or K.
  • the fatty acids constituting the fatty acid alkali metal salts include butyric acid, valeric acid, caproic acid, enanthic acid, caprylic acid, pelargonic acid, capric acid, lauric acid, myristic acid, pentadecylic acid, palmitic acid, palmitoleic acid, margaric acid.
  • acids are preferred.
  • the additive obtained above, Mg powder, and B powder are mixed well at a predetermined ratio using a mixing device to prepare a filled powder.
  • a mixing device to prepare a filled powder.
  • the starting material especially Mg powder
  • the mixing ratio (molar ratio) of Mg powder and B powder need not be strictly 1: 2, is preferably 1.0: 1.5 to 1.0: 30, and particularly preferably 1.0: 2.0 to 1.0: 2.5.
  • the obtained additive mixed powder may be subjected to a pre-filling heat treatment (for example, maintained at 100 to 200 ° C. for 1 to 30 hours in an Ar atmosphere) for the purpose of removing remaining moisture and the like.
  • a metal tube to be the metal sheath 20 is prepared.
  • Cu, Al, Ag, Au, or an alloy thereof can be used as the stabilization layer 23 of the metal sheath 20.
  • the barrier layer 22 Nb, Fe, Ta, Ni, or an alloy thereof can be used.
  • ⁇ Fill the metal tube with the filled powder to produce a powder filled billet.
  • wire drawing is repeated using a wire drawing device so that the area reduction rate (cross-sectional area reduction rate) per pass is in the range of 8 to 12%.
  • a core precursor wire is produced.
  • a wire drawing apparatus a hydrostatic pressure extruder, a draw bench, a wire drawing machine, a swager, a cassette roller die, a groove roll, etc. can be utilized as a wire drawing apparatus.
  • the drawn precursor wire is subjected to a heat treatment (sintering heat treatment) in a non-oxidizing atmosphere in a temperature range of 500 ° C. or more and 550 ° C. or less for 1 hour or more and 50 hours or less to produce MgB 2 A phase is generated (forms MgB 2 core 10) to produce MgB 2 superconducting wire 1.
  • the heat treatment is preferably performed in a non-oxidizing atmosphere in order to prevent undesired oxidation of the filling powder.
  • an inert gas such as argon (Ar), nitrogen (N 2 ), or a vacuum having a degree of vacuum higher than a medium vacuum (generally a non-oxidizing atmosphere) is preferable. Both amounts are preferably 10 ppm or less.
  • MgB 2 superconducting wire material in which both superconducting characteristics and wire lengthening that are higher than conventional ones are realized.
  • 1B can be manufactured by a conventional method (for example, a method of further drawing a wire by combining a plurality of single-core wires).
  • FIG. 5 is a graph showing the relationship between the critical current density (J c ) of the MgB 2 superconducting wire and the molar ratio of the AgO addition amount to the Mg addition amount with and without the addition of the fatty acid alkali metal salt. As shown in FIG. 5, in the sample to which no lithium stearate was added, J c decreased as the amount of AgO added increased, but in the sample added with lithium stearate, J c increased as the amount of AgO added increased. Increased.
  • X-ray diffraction (XRD) measurement and microstructure observation by scanning electron microscope (SEM) were performed on the MgB 2 core of each sample.
  • the MgB 2 phase generation rate was 20% or less and the MgO phase diffraction peak was confirmed. Further, it was observed that the Ag-containing phase was aggregated without being finely dispersed.
  • the MgB 2 phase generation rate was 95% or more, and the diffraction peak of the Mg 2 phase was not confirmed, but the diffraction peak of the Li 2 O 2 phase was confirmed. Further, it was observed that the Ag-containing phase was finely dispersed.
  • the heat treatment temperature was set to 600 ° C. using a sample to which no lithium stearate was added, it was separately confirmed that the MgB 2 phase generation rate was 90% or more.
  • FIG. 6 is a graph showing the relationship between the critical current density (J c ) of the MgB 2 superconducting wire and the molar ratio of the lithium stearate addition amount to the Mg addition amount.
  • the molar ratio of the Li addition amount to the Mg addition amount is 0.5% or more and 20% or less regardless of whether the molar ratio of the AgO addition amount to the Mg addition amount is 5% or 10%.
  • J c showed a value exceeding 1000 A / mm 2 .
  • “J c ⁇ 1000 A / mm 2 ” is one index for designing a superconducting coil, and its value is required as a characteristic of the superconducting wire.
  • the addition amount of the alkali metal component in the additive of the filling powder is preferably 0.5% or more and 20% or less in terms of a molar ratio with respect to the Mg addition amount.
  • FIG. 7 is a graph showing the relationship between the critical current density (J c ) of the MgB 2 superconducting wire and the molar ratio of the AgO addition amount to the Mg addition amount.
  • J c critical current density
  • the AgO addition amount in the additive of the filling powder is preferably 0.4% or more and 44% or less, and more preferably 0.8% or more and 40% or less in terms of a molar ratio to the Mg addition amount.
  • Mg powder (average particle size: 40 ⁇ m, purity: 99% or more), B powder (average particle size: 1 ⁇ m, purity is 95% or more), AgO powder (average particle size: 30 nm, Purity: 99% or more) and lithium stearate powder (average particle size: 100 nm, purity: 99% or more) were prepared.
  • B powder average particle size: 1 ⁇ m, purity is 95% or more
  • AgO powder average particle size: 30 nm, Purity: 99% or more
  • lithium stearate powder (average particle size: 100 nm, purity: 99% or more) were prepared.
  • the lithium stearate powder and AgO powder were put into a ball mill pot (both pot and ball made of zirconia), and both powders were sufficiently mixed using a ball mill apparatus to prepare an additive.
  • Mg powder and B powder were additionally charged into the ball mill pot, and the additive, Mg powder and B powder were mixed for 5 hours using a planetary ball mill apparatus to obtain an additive mixed and filled powder.
  • a Cu / Fe tube (outer diameter: 20.0 mm, inner diameter: 16.0 mm, length: 500 mm) in which a stabilization layer / barrier layer was combined was prepared as a metal tube serving as a metal sheath.
  • the Cu / Fe tube was filled with the additive-mixed powder prepared above to prepare a powder-filled billet. After filling, wire drawing is repeated using a draw bench and wire drawing machine so that the area reduction per pass is in the range of 8 to 12%, and a single core precursor wire (outer diameter: 0.6 mm) Length: 1 km) was produced.
  • Example 1 MgB 2 superconductivity of Example 1 was applied to the drawn single-core precursor wire by heat treatment at 550 ° C. for 30 hours in an Ar atmosphere (both water and oxygen were 10 ppm or less). A wire was prepared. The form of the produced superconducting wire is the same as in FIG. 1A.
  • Comparative Example 1 The MgB 2 superconductivity of Comparative Example 1 was the same as Example 1 except that only Mg powder and B powder were used as starting materials (no additives were added) and heat treatment was held at 650 ° C. for 30 hours. A wire was prepared. However, in Comparative Example 1, disconnection occurred a plurality of times during the drawing process, and the long wire could not be manufactured stably.
  • FIG. 8 is a graph showing the relationship (Jc-B characteristics) between the critical current density of the MgB 2 superconducting wire and the applied magnetic field.
  • Jc-B characteristics the critical current density of the MgB 2 superconducting wire and the applied magnetic field.
  • the MgB 2 superconducting wire of Example 1 exhibits a higher critical current density characteristic than the MgB 2 superconducting wire of Comparative Example 1 and Comparative Example 2 (about 5 times that of Comparative Example 1, comparison) About 1.5 times that of Example 2) was confirmed.
  • Example 1 For the MgB 2 superconducting wire produced as described above (Example 1, Comparative Examples 1 and 2), using a scanning electron microscope-energy dispersive X-ray analyzer (SEM-EDX), microstructure observation and Composition analysis was performed. As a result, it was confirmed that Example 1 had a structure as shown in FIG. That is, the inside of the MgB 2 crystal grains having an average particle size which is less Mg-Ag alloy particles 1 ⁇ m mainly distributed in the grain boundary regions of the MgB 2 crystal grains having an average particle size of less 0.1 ⁇ m Li 2 O 2 particles were mainly present.
  • SEM-EDX scanning electron microscope-energy dispersive X-ray analyzer
  • the average particle diameter of the MgB 2 crystal particles was about half that of Comparative Example 1 of the prior art.
  • Comparative Example 2 it was observed that large particles (Mg—Ag alloy particles and / or Ag particles) having an average particle diameter of about 10 ⁇ m were unevenly distributed.
  • Example 1 the reasons why the superconducting characteristics were improved in Example 1 were that, compared with the technique of Patent Document 2, the coarsening of MgB 2 crystal grains (increased crystal grain boundaries) was reduced by lowering the heat treatment temperature, and non- It was considered that the fine dispersion of the superconducting phase (Mg-Ag alloy particles, Li 2 O 2 particles) could be realized.
  • the MgB 2 superconducting wire according to the present invention includes a current lead, a power transmission cable, a large magnet, a nuclear magnetic resonance analyzer, a medical magnetic resonance diagnostic device, a superconducting power storage device, a magnetic separation device, and a single crystal pulling device in a magnetic field. It can be applied to devices such as refrigerator-cooled superconducting magnet devices, superconducting energy storage, superconducting generators, and fusion reactor magnets. By using the MgB 2 superconducting wire according to the present invention, the performance and function of these devices can be improved (for example, improvement of the generated magnetic field, miniaturization of the superconducting coil, etc.).

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  • Manufacturing & Machinery (AREA)
  • Inorganic Compounds Of Heavy Metals (AREA)
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Abstract

L'invention concerne : un fil supraconducteur MgB2 en diborure de magnésium formé par l'intermédiaire d'un procédé de poudre en tube et qui présente à la fois une performance augmentée en termes de propriétés de supraconductivité, et une longueur de fil augmentée; et un procédé de fabrication de celui-ci. Ce fil supraconducteur MgB2 comprend un noyau en MgB2 et une gaine métallique pour recouvrir le noyau en MgB2, et est caractérisé en ce que : le noyau en MgB2 est une substance polycristalline en MgB2; des particules d'alliage magnésium-argent (alliage Mg-Ag) et des particules d'oxyde métallique alcalin ayant une tendance d'ionisation supérieure à celle de Mg sont dispersées dans la substance polycristalline en MgB2; le diamètre de particule moyen des particules d'alliage Mg-Ag est de 1 µm ou moins; et le diamètre de particule moyen des particules d'oxyde métallique alcalin est de 0,1 µm ou moins.
PCT/JP2013/065310 2012-06-11 2013-06-03 FIL SUPRACONDUCTEUR MgB2 ET SON PROCÉDÉ DE FABRICATION WO2013187268A1 (fr)

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JP2012-131831 2012-06-11

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CN104129799B (zh) * 2014-07-18 2016-06-08 中国兵器工业第五二研究所烟台分所 一种二硼化镁粉体超导材料的制备方法
CN104916373B (zh) * 2015-05-18 2017-06-06 中国科学院电工研究所 一种二硼化镁线材或带材的制备方法
EP3327733B1 (fr) * 2015-07-24 2023-11-22 Hitachi, Ltd. Fil supraconducteur, bobine supraconductrice, appareil d'irm et appareil de rmn
EP3483902A1 (fr) * 2017-11-14 2019-05-15 Koninklijke Philips N.V. Ensemble d'aimant supraconducteur
KR102002372B1 (ko) * 2019-01-31 2019-07-23 케이.에이.티.(주) 테이핑 방식에 의한 MgB2 초전도 선재 제조방법, 이에 의하여 제조된 MgB2 초전도 선재 및 초전도 다심선재 제조장치

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