WO2006104287A1 - Re123系酸化物超電導体とその製造方法 - Google Patents
Re123系酸化物超電導体とその製造方法 Download PDFInfo
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- WO2006104287A1 WO2006104287A1 PCT/JP2006/307415 JP2006307415W WO2006104287A1 WO 2006104287 A1 WO2006104287 A1 WO 2006104287A1 JP 2006307415 W JP2006307415 W JP 2006307415W WO 2006104287 A1 WO2006104287 A1 WO 2006104287A1
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- oxide superconductor
- temperature
- raw material
- superconductor
- oxide
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- 239000002887 superconductor Substances 0.000 title claims abstract description 143
- 238000000034 method Methods 0.000 title claims abstract description 39
- 238000004519 manufacturing process Methods 0.000 title claims description 36
- 239000002994 raw material Substances 0.000 claims abstract description 100
- 239000000463 material Substances 0.000 claims abstract description 50
- 229910052727 yttrium Inorganic materials 0.000 claims abstract description 13
- 229910052775 Thulium Inorganic materials 0.000 claims abstract description 12
- 229910052692 Dysprosium Inorganic materials 0.000 claims abstract description 11
- 229910052691 Erbium Inorganic materials 0.000 claims abstract description 11
- 229910052693 Europium Inorganic materials 0.000 claims abstract description 11
- 229910052688 Gadolinium Inorganic materials 0.000 claims abstract description 11
- 229910052689 Holmium Inorganic materials 0.000 claims abstract description 11
- 229910052765 Lutetium Inorganic materials 0.000 claims abstract description 11
- 229910052779 Neodymium Inorganic materials 0.000 claims abstract description 11
- 229910052772 Samarium Inorganic materials 0.000 claims abstract description 11
- 229910052769 Ytterbium Inorganic materials 0.000 claims abstract description 11
- 229910052746 lanthanum Inorganic materials 0.000 claims abstract description 11
- 239000013078 crystal Substances 0.000 claims description 90
- 238000010438 heat treatment Methods 0.000 claims description 67
- 239000007791 liquid phase Substances 0.000 claims description 56
- 238000002844 melting Methods 0.000 claims description 47
- 230000008018 melting Effects 0.000 claims description 47
- 239000012071 phase Substances 0.000 claims description 42
- 229910052760 oxygen Inorganic materials 0.000 claims description 39
- 239000001301 oxygen Substances 0.000 claims description 37
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 36
- 239000002245 particle Substances 0.000 claims description 26
- 239000012298 atmosphere Substances 0.000 claims description 21
- 239000000203 mixture Substances 0.000 claims description 15
- 239000007769 metal material Substances 0.000 claims description 12
- 230000008569 process Effects 0.000 claims description 12
- 229910052709 silver Inorganic materials 0.000 claims description 9
- 230000002829 reductive effect Effects 0.000 claims description 8
- 230000036961 partial effect Effects 0.000 claims description 7
- 238000004090 dissolution Methods 0.000 claims description 5
- 229910044991 metal oxide Inorganic materials 0.000 claims description 5
- 150000004706 metal oxides Chemical class 0.000 claims description 5
- 230000009467 reduction Effects 0.000 claims description 5
- 150000001875 compounds Chemical class 0.000 claims description 3
- 239000002243 precursor Substances 0.000 claims description 2
- 239000002253 acid Substances 0.000 claims 1
- 230000001568 sexual effect Effects 0.000 claims 1
- 239000000126 substance Substances 0.000 claims 1
- 239000007788 liquid Substances 0.000 abstract description 12
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 abstract description 6
- 229910052757 nitrogen Inorganic materials 0.000 abstract description 3
- 239000000843 powder Substances 0.000 description 83
- 239000000758 substrate Substances 0.000 description 57
- 238000006243 chemical reaction Methods 0.000 description 45
- 239000010410 layer Substances 0.000 description 39
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- 238000002076 thermal analysis method Methods 0.000 description 25
- 238000002156 mixing Methods 0.000 description 19
- 238000005755 formation reaction Methods 0.000 description 13
- 238000002441 X-ray diffraction Methods 0.000 description 12
- 230000015572 biosynthetic process Effects 0.000 description 12
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- 230000002427 irreversible effect Effects 0.000 description 6
- 238000011276 addition treatment Methods 0.000 description 5
- 239000010419 fine particle Substances 0.000 description 5
- 238000012545 processing Methods 0.000 description 5
- 239000004178 amaranth Substances 0.000 description 4
- 239000012300 argon atmosphere Substances 0.000 description 4
- 230000005540 biological transmission Effects 0.000 description 4
- 238000004455 differential thermal analysis Methods 0.000 description 4
- 230000004907 flux Effects 0.000 description 4
- 239000002184 metal Substances 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 4
- 238000006213 oxygenation reaction Methods 0.000 description 4
- 239000000523 sample Substances 0.000 description 4
- 230000008859 change Effects 0.000 description 3
- 239000002131 composite material Substances 0.000 description 3
- 238000007796 conventional method Methods 0.000 description 3
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- 238000011161 development Methods 0.000 description 3
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- 239000000155 melt Substances 0.000 description 3
- 238000011946 reduction process Methods 0.000 description 3
- 238000010583 slow cooling Methods 0.000 description 3
- 230000002195 synergetic effect Effects 0.000 description 3
- 238000011282 treatment Methods 0.000 description 3
- 229910052788 barium Inorganic materials 0.000 description 2
- 239000004020 conductor Substances 0.000 description 2
- 229910052802 copper Inorganic materials 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
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- 239000004615 ingredient Substances 0.000 description 2
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- 229910052698 phosphorus Inorganic materials 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 230000007704 transition Effects 0.000 description 2
- 230000010415 tropism Effects 0.000 description 2
- 101100194326 Caenorhabditis elegans rei-2 gene Proteins 0.000 description 1
- 241000238366 Cephalopoda Species 0.000 description 1
- 229910002480 Cu-O Inorganic materials 0.000 description 1
- 240000007594 Oryza sativa Species 0.000 description 1
- 235000007164 Oryza sativa Nutrition 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
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- 239000011248 coating agent Substances 0.000 description 1
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- 150000002926 oxygen Chemical class 0.000 description 1
- 239000008188 pellet Substances 0.000 description 1
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- C01G—COMPOUNDS CONTAINING METALS NOT COVERED BY SUBCLASSES C01D OR C01F
- C01G3/00—Compounds of copper
- C01G3/006—Compounds containing, besides copper, two or more other elements, with the exception of oxygen or hydrogen
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01B—CABLES; CONDUCTORS; INSULATORS; SELECTION OF MATERIALS FOR THEIR CONDUCTIVE, INSULATING OR DIELECTRIC PROPERTIES
- H01B12/00—Superconductive or hyperconductive conductors, cables, or transmission lines
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B82—NANOTECHNOLOGY
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- Y10S505/00—Superconductor technology: apparatus, material, process
- Y10S505/70—High TC, above 30 k, superconducting device, article, or structured stock
- Y10S505/704—Wire, fiber, or cable
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- Y10T29/49014—Superconductor
Definitions
- the present invention relates to a RE 1 2 3 oxide superconductor and a method for producing the same.
- Bi-based and Y-based oxide superconductor materials have a higher critical temperature (T e ) than metal superconductor materials such as N b 3 Sn, so they can be used for electromagnets and power transmission wires. Application is greatly expected.
- Bi-based oxide superconductor materials have already been put into practical use (refer to Japanese Patent Laid-Open No. 3-1838820), but when a magnetic field is applied parallel to the c-axis, 7 Since the irreversible magnetic field (Bir r) at 7 K (cooling temperature with liquid nitrogen) is as low as 0.5 T or less, its use is limited even if it is made into wire.
- EB a 2 Cu 3 07 Superconductor mainly composed of ⁇ oxide (hereinafter referred to as “RE 1 2 3 oxide superconductor”) is a Bi oxide oxide superconductor material.
- RE 1 2 3 oxide superconductor mainly composed of ⁇ oxide
- J e critical current density
- B i rr irreversible magnetic field
- the heat treatment temperature is as high as 100 ° C. or higher.
- Ag sheath material used for the melting point Ag melting point
- the present invention has excellent superconducting characteristics at liquid nitrogen temperature based on the advantages of developing RE 1 2 3 system oxide superconducting wire with excellent superconducting properties (high critical current density and high irreversible magnetic field). Providing a long-sized RE 1 2 3 oxide superconductor that can be used stably as a single-core or multi-core wire, and a production method that can mass-produce the superconductor The task is to do.
- the present inventor has paid attention to the fact that the heat treatment temperature is lowered, and the RE—B a—O system component (solid phase component) and the B a—Cu—O system component (components that become liquid phases [hereinafter simply referred to as “liquid phase components”)
- the reaction of the “liquid phase component”)) was investigated in detail down to lower temperatures using differential thermal analysis.
- Figure 1 schematically shows a differential thermal analysis curve for the conventional method and the solid-phase one-liquid phase reaction.
- REB in accordance with conventional methods, REB a 2 C u 3 0 7 _ 5 powder heating, showing a thermal analysis curve when the temperature was raised.
- P the curve of the high temperature region, which shows that the REB a 2 C u 3 0 7 _ 5 powder has absorbed heat to dissolve.
- the melting endothermic temperature increases as the ionic radius of RE increases, but is usually around 100 ° C.
- endothermic peak P the temperature begins to appear endothermic peak, i.e., at start occurs endothermic reaction temperature (hereinafter "P, temperature” hereinafter.)
- P endothermic reaction temperature
- B a x - C u y - ⁇ z based source liquid It shows that RE 1 2 3 system oxide (shown as 1 2 3 phase in the figure) is generated through the liquid phase at a temperature or higher when the phase component) starts to dissolve.
- the endothermic peak P 2 is the temperature at which the endothermic peak begins to appear, that is, the temperature at which the endothermic reaction begins (hereinafter referred to as “P 2 temperature”).
- Middle labeled as 1 2 3) indicates that it begins to decompose and melt.
- RE 2 B A_ ⁇ 4 solid component
- the present invention is based on the above novel solid-phase one-liquid phase reaction.
- a non-oriented RE 1 2 3 system oxide is formed in a solid-phase-one-phase reaction, and P 2 Since the RE 1 2 3 phase dissolves above the temperature, the highly oriented RE 1 2 3 series oxide is obtained by a melt growth method using seed crystals (a method of producing crystals by slow cooling after melting). Can be grown.
- the present inventor pays attention to the endothermic peak P 1 in the solid-phase one-liquid phase reaction shown in FIG. 1 (b), and changes P 1, temperature (low temperature liquid phase formation temperature) to the lower temperature side, for example If the temperature can be lowered below the melting point of Ag (about 9600 ° C), one of the reasons for hindering mass production of RE 1 2 3 oxide superconducting wire is the “heat treatment temperature in the melt growth method (RE 1 2 The melting temperature of the 3 system oxide is as high as 100 ° C or higher, and the Ag sheath material (melting point of Ag: approx. 960 ° C) that has been used for wire preparation cannot be used. We came up with the idea that the problem could be resolved, and investigated the factors affecting P and temperature and their effects.
- the present inventor shows that in FIG. 1 (b), in the temperature region between P 1 and P 2 temperatures, and below the melting point of Ag (approximately 96 0), RE 2 B aO 4 (solid phase) reacts with B a x — C u y — ⁇ z- based raw material (liquid phase), and the plate-like RE 1 with excellent crystal orientation and superconductivity on the Ag base material We found that we can produce 2 3 system oxide superconductor. In addition, the present inventor can wire the RE 1 2 3 system oxide superconductor produced by integrating with a base material such as an Ag tube by the solid-phase one-liquid phase reaction, and further, a multi-core structure wire. The possibility that it can be manufactured was also confirmed. The present invention has been made based on the above findings, and the gist thereof is as follows.
- At least RE 2 B A_ ⁇ 4 and B &] (- including ⁇ ⁇ - ⁇ REB was formed using a two-based source of mixed-feed a 2 C u 3 ⁇ 7 _ 5 based oxide superconductor
- a RE 1 2 3 system oxide superconductor characterized by comprising a conductive layer and a holding member for holding the conductive layer.
- RE is one or more elements selected from La, Nd, Sm, Eu, Gd, Dy, Ho, Er, Tm, Yb, Lu, and Y.
- the above-mentioned (1) to (5) are characterized in that the holding member is long and is in contact with the conductive layer partially or entirely in a cross section perpendicular to the longitudinal direction.
- RE 1 2 3 series Oxide superconductor RE 1 2 3 series Oxide superconductor.
- RE is one or more elements selected from La, Nd, Sm, Eu, Gd, Dy, Ho, Er, Tm, Yb, Lu, and Y.
- RE is one or more elements selected from La, Nd, Sm, Eu, Gd, Dy, Ho, Er, Tm, Yb, Lu, and Y.
- the particle size of the mixed raw material is refined to less than 1 ⁇ m, and the melting temperature of the B a X — C′u y — ⁇ z- based raw material is not lowered further.
- the RE 1 2 3 system oxide superconductor is subjected to a pressure treatment at an isotropic pressure of 1 OMPa or more and then a heat treatment.
- the RE 1 2 3 system oxide superconductor is heat-treated under an isotropic pressure of 0.5 MPa or more.
- Figure 1 is a diagram schematically illustrating a differential thermal analysis curve of the RE 2 B A_ ⁇ 4 and B a- C u- ⁇ based solid phase one-liquid phase reaction of the starting materials.
- (A) in accordance with the conventional method, shows the thermal analysis curve when heating the REB a 2 C u 3 ⁇ 7 _ 5 based compound powder was heated, (b), the RE 2 B A_ ⁇ 4 and B a x — C u y — O z
- the heat analysis curve when mixing the raw materials of the Z system, heating, and raising the temperature is shown.
- Fig. 2 shows the thermal analysis curves when various mixed raw materials are heated and heated.
- (A) is a mixture of raw material powder (E r 2 B a 0 4 powder and B a x — Cu y — 0 z- based powder) with a particle size of 1 to 5 x m to obtain an E r 1 2 3-based oxide
- the raw material powder (Ag-free powdered powder containing Ag) containing 3% by mass of Ag using Ag 2 0 was added to the argon atmosphere (1% 0) containing 1% oxygen.
- the thermal analysis curve when the temperature is raised in 2 — A r) is shown.
- (B) is a 1% ⁇ 2 — A r raw material powder (Ag powder powder raw material powder) with a particle size of about 0.1 xm obtained by grinding the above Ag-containing unground powder for about 4 hours with a ball mill. The thermal analysis curve when it heats and heats up is shown.
- (C) shows a thermal analysis curve when the above non-pulverized raw material powder containing Ag is heated in the air and heated up.
- (D) is a raw material powder with a particle size of 1 to 5 m (E r 2 B a 0 4 powder and B a x — Cu y — O z type powder) and an E r 1 2 3 type oxide can be obtained.
- the thermal analysis curve when the raw material powder (Ag-free pulverized raw material powder) mixed at the mixing ratio is heated in the air and heated up is shown.
- Figure 3 is a diagram that schematically shows the knowledge related to lowering temperatures.
- Figure 4 is a mixed raw material powder having a particle size of about 0. 1 m to (1 ⁇ 5 ⁇ E r 2 B A_ ⁇ 4 powder and the B a x _ C u y _ ⁇ z based powder E r B a 2 C were mixed at a mixing ratio of u 3 0 7 _ [delta] is obtained, further, after addition of 3 wt% of a g with a g 2 Omicron, about 4 hours milling), allowed to adhere to M G_ ⁇ substrate, FIG. 3 is a graph showing the X-ray diffraction intensity of a product obtained by heating at 9 40 ° C. for 3 hours in 1% 0 2 — Ar.
- Fig. 6 shows mixed raw material powder with a particle size of about 0.1 m (Er 2 B aO 4 'with 1 to 5 m of B a x _ C u y — O z- based raw material powder', E r B a 2 C u 3 ⁇ 7.
- E r the a et al, after addition of 3 wt% of A g with A g 2 ⁇ , about 4 hours powder
- the product obtained by adhering to the MgO substrate and heating in 94% ° C for 3 hours in 1% ⁇ 2 — Ar was observed with a scanning electron microscope (SEM). It is a figure which shows a result (micrograph of magnification 200.000).
- Figure 7 is a particle size of about 0.1 mixed raw material powder m (l to 5 m of E r 2 B A_ ⁇ 4 powder and the B a x - a C u y - ⁇ z based powder, E r B a 2 C u 3 O 7 _ a is mixed at a mixture ratio, and after adding 3% by mass of Ag using Ag 2 0, the mixture is pulverized for about 4 hours.
- Figure 9 is a diagram showing the temperature dependence of the magnetic susceptibility of the product subjected to oxygenation process (E r B a 2 C u 3 ⁇ 7 _ [delta]).
- FIG. 1 is a diagram illustrating a magnetic field (B) dependency of the critical current density (J c) of the above product was subjected to oxygenation process (E r B a 2 C u 3 ⁇ 7 _ 6)
- FIG. 1 is a diagram showing an embodiment in which crystals of a RE 1 2 3 system superconductor are formed in a plate shape and oriented on an Ag substrate.
- A is a figure which shows the whole growth aspect
- (b) is a figure which shows the cross section.
- FIG. 1 2 shows mixed raw powder with a particle size of approximately 0.1 l (same as E r 2 B aO 4 powder with l ⁇ 5 ⁇ m B 3 ] ( — (1 ⁇ ⁇ 0 2 system powder £ r B a 2 Cu 3 0 7. Mix in a mixing ratio to obtain ⁇ , and add 4% by weight of Ag using Ag 2 0, then fill the powder into the Ag pipe for about 4 hours. After that, the surface was reduced to a thickness of '0.3 mm, and it was 8% at 9 2 5 ° C in 1% ⁇ 2 — Ar.
- FIG. 3 is a graph showing the X-ray diffraction intensity of a product produced by heating at 8 75 ° C. for 2 hours after heating for 2 minutes.
- FIG. 13 is a diagram showing the microstructure of the cross section of the product.
- FIG. 1 4 shows mixed raw material powder with a particle size of about 0.1 l ⁇ m (same as E r 2 B aO 4 powder of 1 to 5 ⁇ 01 B a x — C u y — 0 z system powder a 2 Cu 3 ⁇ 7 — Mix at a mixing ratio to obtain ⁇ , and add 4% by weight of Ag using Ag 2 0, then grind for about 4 hours) After that, the material whose surface thickness was reduced to 0.3 mm was heated in 1% ⁇ 2 — Ar at 9 25 ° C for 8 minutes, and then heated at 4 different temperatures for 2 hours.
- FIG. 6 is a diagram showing the temperature dependence of magnetization of a product. (A) 8 75 ° C, (b) 8500 ° C, (c) 825 ° C, (d) 80 ° C.
- FIG. 15 is a diagram showing the current-voltage characteristics of the product shown in FIG.
- RE solid phase
- RE is one or more elements selected from La, Nd, Sm, Eu, Gd, Dy, Ho, Er, Tm, Yb, Lu and Y. It is.
- the inventor first investigated the factors affecting P and temperature in Fig. 1 (b).
- Figure 2 shows the thermal analysis curves when various mixed materials are heated and heated.
- the thermal analysis curve shown in (a) in Fig. 2 shows the raw powder (E r 2 B aO 4 powder and B a x — C u y — ⁇ 2 system powder) are mixed at a mixing ratio to obtain an E r 1 2 3 system oxide, and 3 masses using Ag 2 0 % Thermal analysis curve when the raw material powder with added Ag (unground raw material powder containing Ag) is heated in an argon atmosphere (l% ⁇ 2 _ A r) containing 1% oxygen. It is.
- the thermal analysis curve shown in Fig. 2 (b) is the raw powder with a particle size of about 0.1 / im obtained by grinding the above powdered Ag-free powder with Ag for 4 hours with a pole mill (ground powder with Ag) ) Is a thermal analysis curve when heated in 1% 0 2 — A r and heated up.
- the B a x — Cu y _ O z system raw material starts to dissolve, and a solid phase one liquid that generates RE 1 2 3 system oxide
- the temperature at which the phase reaction begins to occur, that is, P and the temperature can be adjusted appropriately.
- the thermal analysis curve shown in (c) of Fig. 2 is a thermal analysis curve when the above Ag-containing unground raw powder is heated in the atmosphere and heated.
- the P and temperature in this thermal analysis curve is about 890 ° C.
- the thermal analysis curve shown in (d) of Fig. 2 shows that the raw powder (E r 2 B a 0 4 powder and B a x — Cu y — O z- based powder) with a particle size of 1 to 5 im 23 Thermal analysis of raw material powder mixed at a mixing ratio to obtain a 3-based oxide (because it does not contain Ag, henceforth referred to as “Ag-free non-pulverized raw material powder”) and heated in the air It is a curve.
- P and temperature in this thermal analysis curve are about 920 ° C.
- FIG. 3 shows a summary of the findings related to lowering the above temperatures.
- (zl) reduce the particle size of the raw material powder
- (z2) reduce the oxygen partial pressure of the reaction atmosphere
- (z3) add the required amount of Ag to the raw material powder.
- the temperature can be lowered (P, temperature lowering) by one or more of these.
- This knowledge is the knowledge forming the basis of the present invention.
- the above (zl), (z 2), and / or (z3) can be selected as appropriate, and the temperature can be adjusted and set to the required temperature.
- the material is not limited to one having a specific melting point.
- (zl), (z2), and Z or (z3) may be selected as appropriate, and the temperature may be set to a required temperature, or the above (zl), (z2), and / or ( A substrate having a required melting point may be selected in relation to P and temperature adjusted and set by appropriately selecting z3).
- the present inventor used a MgO substrate as a base material, formed a RE12-3 oxide superconductor layer thereon, and investigated its crystal orientation and superconducting characteristics. The results of one survey are described below.
- the melting point of MgO is 1600 ° C or higher, and it is located on the higher temperature side than P 1, temperature and P 2 temperature.
- Z) Highly oriented polycrystal ” is suitable as a substrate for evaluating the orientation of the polycrystal formed.
- Fig. 4 shows the X-ray diffraction intensity of the product obtained by the above heating.
- the intensity of Miller index (0 0 ⁇ ) is strong, so on the MgO substrate, E r B a 2 C u has a crystal structure with the c-axis oriented perpendicular to the substrate surface. 30 7 _ ⁇ is formed.
- FIGS. 4 and 5 show the E r B a 2 C u 3 0 7 _ s, a result of observation with a scanning electron microscope (SEM) to (photomicrograph magnification 3 0 0). From this figure it, the M g O board, 1 0 ⁇ 1 0 0 E r B a 2 C u 30 7 which m approximately plate-like crystals having a crystal structure that is connected without a gap. [Delta] is formed I understand that ' Thus, as shown in FIGS. 4 and 5, by the solid-liquid reaction of the present invention, on the MgO substrate, the c-axis is oriented perpendicular to the substrate surface, and the a-b surface is the substrate. plate-shaped E having parallel crystal structure on the surface r B a 2 C u 3 0 7. s are formed.
- SEM scanning electron microscope
- Fig. 6 shows that the mixed raw material powder containing 3% by mass of Ag with a particle size of about 0.1 l ⁇ m (same as the 1 to 5 ⁇ m Er 2 B a 0 4 powder B a x — C u y — ⁇ z- based powder is produced by E r B a 2 C u 3 0 7 — ⁇ and non-superconducting phase E r 2 B a C u 0 5 (hereinafter referred to as “E r 2 1 1 phase”) mixed with excess mixing ratio, even after the addition of 3 wt% of a g with a g 2 ⁇ , about 4 o'clock Mako ⁇ ), allowed to adhere to M G_ ⁇ substrate, l% ⁇ 2 _A
- SEM scanning electron microscope
- the M g O board, the plate-shaped E r B a 2 C u 3 0 7 - crystal connection without a gap of s-based oxide, and, in addition to the crystal, of about several m E r B a 2 C u 3 0 7 _ ⁇ having a crystalline structure with needle-shaped E r 2 1 1 phase fine particles (confirmed by electron beam microanalyzer) must be formed I understand.
- the non-superconducting phase RE 2 B a C u 0 5 (hereinafter referred to as “RE 2 1 1 phase”) present in the superconductor (bulk body) pins the magnetic flux that has penetrated into the superconductor to significantly improve the current characteristics. It is known that the needle-shaped one is superior to the granular one in terms of the pinning effect, but this action is achieved by the plate formed on the MgO substrate. RE 2 1 1 phase that exists in the form of dispersed REI 2 3 oxide crystals (Non-superconducting phase) can naturally be expected.
- the c-axis is oriented perpendicular to the substrate surface
- the a-b surface is parallel to the substrate surface
- the RE 2 1 1 phase Non-superconducting phase
- a plate-like RE 1 2 3 oxide superconductor having a crystal structure in which fine particles are dispersed and excellent in crystal orientation and current characteristics can be formed stably.
- the present inventor uses a raw material powder obtained by mixing G d 2 B aO 4 powder and B a x —C u y _O z- type powder, and even when no Ag is added, O Stable formation of plate-like G d B a 2 C u 3 0 7 _ fi with excellent crystal orientation as in the case of Er B a 2 Cu 3 0 7 _ s described above I confirmed that I can do it.
- the present inventor has the MgO substrate, the c-axis is oriented perpendicular to the substrate surface, and the a_b plane is parallel to the substrate surface.
- a plate-like RE 1 2 3 oxide superconductor composed of a crystal structure and excellent in “crystal orientation and current characteristics”, and RE 2 1 1 phase (non-superconducting phase) fine particles dispersed in the crystal structure It was confirmed that a plate-like RE 1 2 3 oxide superconductor having excellent crystal orientation composed of the included crystal structure can be stably formed.
- the present inventor applied a RE 1 2 3 oxide superconductor excellent in crystal orientation to the Ag base material widely used in the PIT method and the like by using the solid-phase one-liquid reaction of the present invention.
- the MgO substrate was replaced with an Ag substrate, a RE E.1 23-based oxide was formed on the Ag substrate, and the crystal orientation and superconducting properties of the oxide were investigated. The following is a description of the survey results Light up.
- the product obtained by the heating was subjected to an oxygen addition treatment at 300 to 700 ° C.
- Figure 7 shows the X-ray diffraction intensity of the product obtained by the above heating. As shown in Fig. 7, since the intensity of Miller index (0 0 ⁇ ) appears strongly, on the Ag substrate, the c axis is oriented perpendicular to the substrate surface. E r B a 2 C u 3 0 7 ⁇ is generated.
- FIG. 8 shows the result of observation of the above product (E r B a 2 Cu 3 0 7 — ⁇ ) with a scanning electron microscope (SEM) (micrograph with a magnification of 200,000). From Figure 8, on the A g substrate, 1 0 E m approximately plate-like crystals having a crystal structure that led no gap r B a 2 C u 3 0 7 - ⁇ are seen to have been formed.
- SEM scanning electron microscope
- the product (E r B a 2 C u 3 0 7 - s ) is a superconductor with an on-set critical temperature (T c ) of about 9 OK or higher.
- T c critical temperature
- the c-axis is oriented perpendicularly to the substrate surface and the ab surface is parallel to the substrate surface without using a seed crystal that becomes the nucleus of the oriented crystal.
- B a 2 C u 30 7. 6 superconductor is formed.
- the product (E r B a 2 C u 3 0 7 — ⁇ ) has a current of about 0.5 X 1 0 4 AZ cm 2 even in a magnetic field of 2 ⁇ .
- the irreversible magnetic field (B irr) is high (the irreversible magnetic field (B irr) of the Bi superconducting material is 0.5 T or less).
- the present inventor determines the P and temperature at which the endothermic reaction starts, the melting point of the Ag base material (about 96 0 ° C) can be lowered to the following temperatures, and as a result, a plate-like RE 1 2 3 oxide superconductor with excellent crystal orientation and current characteristics can be stabilized on the Ag substrate.
- the knowledge that it can be formed is obtained.
- the product According to the X-ray diffraction intensity and SEM photograph of the product obtained by the above heating, the product has a crystal structure in which E r 2 11 1 phase (non-superconducting phase) fine particles are dispersed. It was confirmed to be a 2 C u 30 7. ⁇ .
- E r 2 1 1 phase (non-superconducting phase) fine particles act to pin the magnetic flux penetrating into the superconductor.
- the generation of the RE 1 2 3 oxide superconductor on the Ag substrate is essentially due to the solid-phase one-liquid reaction that occurs on the Ag, the solid-liquid phase of the present invention. If reaction is used, a RE 1 2 3 oxide superconductor excellent in crystal orientation and current characteristics can be formed on a long Ag substrate as well.
- the long Ag base material is a base material widely used for Bi-based superconducting oxide wire and multi-core wire material
- the RE 1 2 3 oxide superconductor of the present invention Is suitable for the production of single-core or multi-core wire by the PIT method using a long Ag substrate.
- fe REB a 2 C u 3 O is produced by using at least RE 2 B a 0 4 and 'B a x — Cu y — O z- based raw materials for the holding member. 7.
- a conductive layer containing a ⁇ - based oxide superconductor is formed.
- RE is one or more selected from La, Nd, Sm, Eu, Gd, Dy, Ho, Er, Tm, Yb, Lu and Y. Selected in consideration of the desired crystal orientation and superconducting properties
- the B a x — C u y —O z- based raw material is a mixture of a metal oxide and Z or a compound thereof (for example, B a Cu 0 2 , C u 0) at a required mixing ratio. You may add 15 mass% or less Ag or Ag oxide to this mixed raw material. Addition of Ag or Ag oxide is preferable from the viewpoint of lowering P and temperature.
- the mixing ratio (x, y, z) of Ba, Cu, and O can be selected as appropriate in consideration of the composition, characteristics, structure, etc. of the RE 1 2 3 system oxide. A slight amount of solid solution is formed on the substrate, and if necessary, an appropriate amount of RE 2 1 1 phase (non-superconducting phase) is dispersed in the RE 1 2 3 system oxide crystal. If you consider
- the mixing ratio of RE 2 B a 0 4 and B a x — C u y — O z- based raw materials and / or the mixing ratio of Ba, Cu, O (x, y, z) is appropriately selected.
- a RE 1 2 3 oxide superconductor in which the non-superconducting phase (RE 2 1 1 phase) is dispersed can be generated.
- the non-superconducting phase has the function of trapping and fixing (pinning) the magnetic flux that has penetrated into the superconductor, so it is important to improve the magnetic field dependence of the superconducting current.
- Conductive layer containing 6-based oxide superconductor in order to maintain the characteristics of the conductive layer may be one which is coated with a protective layer or stabilizing layer.
- the holding member for holding the conductive layer may be coated with an intermediate layer having a function contributing to improvement of superconducting properties, such as a crystal orientation promoting layer, a strain buffering layer, a diffusion preventing layer, or a current leakage preventing layer.
- the intermediate layer is preferably composed of a metal oxide (for example, MgO), a composite oxide, a metal oxide having a high electrical resistance, or a composite oxide in order to exhibit the above function.
- a metal oxide for example, MgO
- a composite oxide for example, a metal oxide having a high electrical resistance
- a composite oxide in order to exhibit the above function.
- MgO is an intermediate that improves the crystal orientation. It is suitable as a material constituting the layer.
- the holding member is not limited to a specific shape, and the mode in which the holding member holds the conductive layer is not limited to the specific mode.
- the conductive layer may be held in contact with a part of the conductive layer in a cross section perpendicular to the longitudinal direction, or may be in contact with the conductive layer over the entire circumference. The conductive layer may be retained.
- the tubular member is preferably a tubular member having an annular closed cross section or a flat rectangular closed cross section.
- the holding member is preferably made of a metal material.
- Ag or an Ag-based material is most preferable as a metal material that satisfies the above two conditions.
- the holding member must be at least RE 2 B a 0 4 and B a x — C u y _ 0
- the member surface that is in direct contact with the mixed raw material mixed with the z- based raw material may be composed of a composite metal material coated with Ag or an Ag-based material. Further, the holding member may be a member that has been subjected to necessary processing in advance and has been given the orientation of the surface texture in the longitudinal direction of the member.
- RE is one type selected from La, Nd, Sm, Eu, Gd, Dy, Ho, Er, Tm, Yb, Lu, and Y, or Two or more elements.
- the reaction with RE 2 B a 0 4 begins at the same time as the dissolution of the B a x — C u y — O z- based raw material, so REB a 2 C u 3 0 7 _
- the lower limit of the heating temperature for forming 5 oxides was defined as: 8 & ! ( — 0 1 ⁇ – ⁇ The melting temperature of the 2 system raw material, that is, the P and temperature of the endothermic peak.
- the melting temperature (P temperature) of the B a x —C u y —O z- based raw material can be lowered by appropriately adopting the above (zl), (z2), and Z or (z3).
- the particle size of ( ⁇ ⁇ ') mixed raw material is refined to less than 1 m.
- the oxygen partial pressure of the atmosphere containing oxygen is set to 0.0 2 ⁇ ⁇ B a x — C u y — ⁇ z
- One or a combination of means such as adding ( ⁇ 3 ′) 15 mass% or less of Ag or Ag oxide to the mixed raw material. It is preferable to lower the melting temperature of the system raw material.
- the upper limit of the heating temperature may be not more than the melting point of the holding member.
- the heating temperature exceeds the melting point of REB a 2 Cu 3 0 7 — ⁇ oxide, after heating, crystallize by slow cooling, etc., and the REB a 2 Cu 3 0 7 _ s oxide What is necessary is just to perform below the melting point.
- the temperature is lowered by appropriately adopting the above (zl), (z2), and Z or (z3). Therefore, the melting point of the holding member is also in a specific temperature range. There is no need to limit. However, the melting point of the holding member must be P, temperature or higher.
- REB is performed by the solid-phase one-liquid reaction of the present invention.
- a 2 Cu 3 ⁇ 7 Before forming oriented crystals of ⁇ oxide, reduce the surface area once or twice to increase the contact area between a part of the mixed raw material and the holding member. . This is a feature.
- heating and surface reduction processing may be performed simultaneously.
- simultaneous heating / reducing process it is possible to produce a long R E 1 2 3 system superconductor excellent in crystal orientation and current characteristics.
- Heat treatment for heating to a temperature lower than the temperature may be performed once or more.
- a liquid phase is generated by heating to a temperature (P temperature) above the melting temperature (P, temperature), and then kept at a temperature ( ⁇ temperature) lower than the temperature above the melting temperature (P temperature). Then, heat treatment is performed.
- the formation reaction of the non-superconducting phase can be suppressed, and a conductive layer having excellent crystal orientation can be formed on the surface of the holding member.
- the heat treatment temperature [rho 'temperature)
- ⁇ -based oxide appropriately controlling the size of crystals becomes possible, on the surface of the holding member, it is possible to form a more crystalline orientation excellent REB a 2 C u 3 ⁇ 7 conductive layers ing from _ [delta] oxide.
- the heat treatment is not limited to once but may be performed a plurality of times in order to stabilize and improve the characteristics of the conductive layer.
- the temperature ( ⁇ 'temperature) when the above heat treatment is performed a plurality of times is the temperature at which the starting mixed raw material is heated, that is, a temperature (P, temperature) equal to or higher than the melting temperature (P, temperature) of the B a x — C u y — 0 z- based raw material.
- the temperature is not limited to a specific temperature as long as the temperature is lower than (P temperature).
- the P ′ temperature is a temperature equal to or lower than P 1, from the viewpoint of suppressing the formation of the non-superconducting phase and controlling the formation of the 1 2 3 phase plate crystal.
- the B a x — C u y _ O z system raw material is expressed as' the melting temperature of the raw material. (P 1, temperature)
- heat treatment first stage heat treatment
- the RE 2 B a Cu 0 5 solid phase (2 1 1 It was confirmed that the proportion of phase) increased.
- the first stage heat treatment is completed within a short period of time during which the proportion of the RE 2 B a Cu 0 5 solid phase (2 1 1 phase) does not increase, that is, the composition of the generated liquid phase does not change, Subsequently, when the next heat treatment (second heat treatment) is appropriately performed for several hours at a temperature lower than the first heat treatment temperature (P temperature), and the RE 1 2 3 crystal is grown, the CuO Li RE 1 a 2 C u 3 0 7 The RE 1 2 3 crystals are produced while maintaining a stable liquid phase, so that plate-like crystals are more easily produced and the crystal orientation is more excellent. It believed to form a _ [delta] based oxide or Ranaru conductive layer.
- Figure 1 2 shows that REB a 2 Cu 3 0 7 produced by performing the first stage heat treatment at 9 25 ° C for 8 minutes and then the second stage heat treatment at 875 ° C for 2 hours.
- _ shows the X-ray diffraction pattern of 6-based oxide.
- B a C U_ ⁇ no peak indicating the 2-phase
- 1 2 3 phase (0 0 L) intensity Is appearing strongly.
- the intensity peak without a plane index between (0 0 3) and (0 0 5) is the intensity peak of the 1 2 3 phase (1 0 3).
- the first stage heat treatment is performed at 925 ° C for 8 minutes and then the second stage heat treatment is performed at 85 ° C or 825 for 2 hours, the c-axis It was found that the peak intensity other than (0 0 L) indicating the orientation increased, and the c-axis orientation decreased significantly. This suggests that the heat treatment temperature in the second stage is preferably set to a temperature relatively close to the first heat treatment.
- the R E 123-based oxide superconductor manufactured by the method for manufacturing a superconductor of the present invention may be subjected to a heat treatment after being pressurized at an isotropic pressure of 10 MPa or more. This treatment is preferable in terms of densifying the crystal.
- the R E 123-based oxide superconductor manufactured by the method for manufacturing a superconductor of the present invention may be heat-treated under an isotropic pressure of 0.5 MPa or more. This heat treatment is also preferable in terms of densifying the crystals.
- the RE 1 2 3 oxide superconductor manufactured by the method for manufacturing a superconductor of the present invention includes oxygen at a temperature of 300 to 700 ° C. in the same manner as a normal RE 1 2 3 oxide superconductor. Perform additional processing. By this oxygen addition treatment, it is possible to obtain a R E 1 2 3 oxide superconductor having more excellent superconducting properties.
- a mixed raw material similar to the mixed raw material used in Example 1 was uniaxially molded into a 6 mm pellet, packed in an Ag tube having an inner diameter of 6 mm and an outer diameter of 10 mm, and then subjected to surface reduction processing. It was processed into a strip wire with a width of 3 mm and a thickness of 1 mm. After that, the strip wire was heat treated at 920 ° C 'in the atmosphere, Next, a wire sample having a length of 100 mm was cut from the wire, and oxygen was introduced by slow cooling from 70 ° C. to 400 ° C. over 20 hours in an oxygen stream. .
- the critical current density was 880 AZ cm 2 .
- the above material was heated in an argon atmosphere containing 1% oxygen at 9 2 5 ° C for 8 minutes, followed by (a) 8 75 ° C, (b) 8500 ° C, (c) 8 2 5 ° C, and, (d) at 8 0 0 ° C, 2 hours, heat treatment to form the E r B a 2 C u 30 7. ⁇ .
- the obtained ErB a 2 Cu 3 0 7 _ 5 was subjected to heat treatment for 8 minutes at 9 25 ° C by X-ray diffraction intensity measurement and observation of the crystal surface by a scanning electron microscope (SEM). After that, (a) When heat-treated at 8 75 ° C for 2 hours, ErB a 2 Cu 30 7 _ 6 having particularly excellent c-axis orientation and having a plate-like structure is formed. I was sure that.
- Fig. 12 The X-ray diffraction intensity measurement results are shown in Fig. 12, and the scanning electron microscope observation image is shown in Fig. 13.
- the present invention it is possible to provide a long RE 1 2 3 system oxide superconductor that has stable and excellent superconducting properties and can be used as a single core or multifilament wire. Can do. Therefore, the present invention can be widely used for resource saving, energy, etc. in addition to a strong magnetic field generator, high-voltage power transmission.
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- Inorganic Compounds Of Heavy Metals (AREA)
- Superconductors And Manufacturing Methods Therefor (AREA)
- Superconductor Devices And Manufacturing Methods Thereof (AREA)
Description
Claims
Priority Applications (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US11/887,334 US7964532B2 (en) | 2005-03-31 | 2006-03-31 | RE123-based oxide superconductor and method of production of same |
EP06731363A EP1865515A4 (en) | 2005-03-31 | 2006-03-31 | RE123 OXIDE SUPERCONDUCTOR AND PROCESS FOR PRODUCING THE SAME |
Applications Claiming Priority (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2005-104866 | 2005-03-31 | ||
JP2005104866 | 2005-03-31 | ||
JP2005300766A JP4925639B2 (ja) | 2005-03-31 | 2005-10-14 | Re123系酸化物超電導体とその製造方法 |
JP2005-300766 | 2005-10-14 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2006104287A1 true WO2006104287A1 (ja) | 2006-10-05 |
Family
ID=37053528
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2006/307415 WO2006104287A1 (ja) | 2005-03-31 | 2006-03-31 | Re123系酸化物超電導体とその製造方法 |
Country Status (5)
Country | Link |
---|---|
US (1) | US7964532B2 (ja) |
EP (1) | EP1865515A4 (ja) |
JP (1) | JP4925639B2 (ja) |
KR (1) | KR20070114778A (ja) |
WO (1) | WO2006104287A1 (ja) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN103396114A (zh) * | 2013-07-18 | 2013-11-20 | 陕西师范大学 | 简化制备单畴ybco超导块材的方法 |
Families Citing this family (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US11150065B2 (en) * | 2016-11-02 | 2021-10-19 | Raytheon Company | Thermal energy absorbing structures |
Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH01320710A (ja) * | 1988-06-22 | 1989-12-26 | Furukawa Electric Co Ltd:The | 多芯型酸化物系超電導線の製造方法 |
JP2003020225A (ja) * | 2001-07-06 | 2003-01-24 | Internatl Superconductivity Technology Center | 酸化物超電導体の製造方法及び酸化物超電導体 |
JP2006036574A (ja) * | 2004-07-26 | 2006-02-09 | Nippon Steel Corp | RE−Ba−Cu−O系酸化物超電導体の作製方法 |
Family Cites Families (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4857504A (en) * | 1987-08-25 | 1989-08-15 | University Of Arkansas | Melt-produced high temperature rare earth barium copper oxide superconductor and processes for making same |
JP2636049B2 (ja) | 1988-08-29 | 1997-07-30 | 住友電気工業株式会社 | 酸化物超電導体の製造方法および酸化物超電導線材の製造方法 |
EP0376276B1 (en) * | 1988-12-28 | 1995-04-19 | Ngk Spark Plug Co., Ltd | Ceramic superconducting composition and process and apparatus for preparing thereof |
JP3269841B2 (ja) * | 1992-04-02 | 2002-04-02 | 株式会社フジクラ | 酸化物超電導導体およびその製造方法 |
JP2967154B2 (ja) * | 1996-08-02 | 1999-10-25 | 同和鉱業株式会社 | Agを含み結晶方位の揃った酸化物超電導体及びその製造方法 |
CN1182597C (zh) | 1997-06-18 | 2004-12-29 | 麻省理工学院 | 将金属氟氧化物转化为超导氧化物的受控转化 |
JP3138820B2 (ja) | 1999-09-21 | 2001-02-26 | ヤンマー農機株式会社 | 田植機 |
WO2003014251A1 (en) * | 2001-08-09 | 2003-02-20 | Hitachi Maxell, Ltd. | Non-magnetic particles having a plate shape and method for production thereof, abrasive material, polishing article and abrasive fluid comprising such particles |
-
2005
- 2005-10-14 JP JP2005300766A patent/JP4925639B2/ja not_active Expired - Fee Related
-
2006
- 2006-03-31 EP EP06731363A patent/EP1865515A4/en not_active Withdrawn
- 2006-03-31 US US11/887,334 patent/US7964532B2/en not_active Expired - Fee Related
- 2006-03-31 WO PCT/JP2006/307415 patent/WO2006104287A1/ja active Application Filing
- 2006-03-31 KR KR1020077022031A patent/KR20070114778A/ko not_active Application Discontinuation
Patent Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH01320710A (ja) * | 1988-06-22 | 1989-12-26 | Furukawa Electric Co Ltd:The | 多芯型酸化物系超電導線の製造方法 |
JP2003020225A (ja) * | 2001-07-06 | 2003-01-24 | Internatl Superconductivity Technology Center | 酸化物超電導体の製造方法及び酸化物超電導体 |
JP2006036574A (ja) * | 2004-07-26 | 2006-02-09 | Nippon Steel Corp | RE−Ba−Cu−O系酸化物超電導体の作製方法 |
Non-Patent Citations (1)
Title |
---|
See also references of EP1865515A4 * |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN103396114A (zh) * | 2013-07-18 | 2013-11-20 | 陕西师范大学 | 简化制备单畴ybco超导块材的方法 |
Also Published As
Publication number | Publication date |
---|---|
US20090270260A1 (en) | 2009-10-29 |
KR20070114778A (ko) | 2007-12-04 |
US7964532B2 (en) | 2011-06-21 |
EP1865515A1 (en) | 2007-12-12 |
JP4925639B2 (ja) | 2012-05-09 |
JP2006310259A (ja) | 2006-11-09 |
EP1865515A4 (en) | 2011-12-28 |
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