[go: up one dir, main page]

WO1991000622A1 - Composite supraconducteur a dopage a base d'argent - Google Patents

Composite supraconducteur a dopage a base d'argent Download PDF

Info

Publication number
WO1991000622A1
WO1991000622A1 PCT/AU1990/000288 AU9000288W WO9100622A1 WO 1991000622 A1 WO1991000622 A1 WO 1991000622A1 AU 9000288 W AU9000288 W AU 9000288W WO 9100622 A1 WO9100622 A1 WO 9100622A1
Authority
WO
WIPO (PCT)
Prior art keywords
composite
superconductor
accordance
silver
phase
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Ceased
Application number
PCT/AU1990/000288
Other languages
English (en)
Inventor
Shi Xue Dou
Hue Kun Liu
Kang Ho Song
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Unisearch Ltd
Original Assignee
Unisearch Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Unisearch Ltd filed Critical Unisearch Ltd
Publication of WO1991000622A1 publication Critical patent/WO1991000622A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/01—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics
    • C04B35/45—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on copper oxide or solid solutions thereof with other oxides
    • C04B35/4521—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on copper oxide or solid solutions thereof with other oxides containing bismuth oxide
    • C04B35/4525—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on copper oxide or solid solutions thereof with other oxides containing bismuth oxide also containing lead oxide
    • 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
    • H10N60/0268—Manufacture or treatment of devices comprising copper oxide
    • H10N60/0661—Processes performed after copper oxide formation, e.g. patterning
    • 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
    • H10N60/0268—Manufacture or treatment of devices comprising copper oxide
    • H10N60/0801—Manufacture or treatment of filaments or composite wires
    • 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
    • H10N60/80—Constructional details
    • H10N60/85—Superconducting active materials
    • H10N60/855—Ceramic superconductors
    • H10N60/857—Ceramic superconductors comprising copper oxide

Definitions

  • the present invention relates to a silver doped superconductor composition and to a process for fabricating the composition. More particularly, the invention relates to the fabrication of silver composites including wires, tapes, ultifila ents, silver doped superconductors and any form of the combination of silver and the Bi-Pb-Sr-Ca-Cu-0 superconductor system (BPSCCO system). These composite superconductors are essential for large-scale application of superconductor technology.
  • BPSCCO system Bi-Pb-Sr-Ca-Cu-0 superconductor system
  • T c Transition Temperature oxide superconductors
  • metals such as silver and gold
  • silver has been used for making composite superconductors including wires, tapes and multifilaments. It has been found to be the only metal element among the noble metals that is non-poisoning to ceramic superconductors.
  • This non-poisoning behaviour of Ag is of significant technical importance in the fabrication of Ag-superconductor composites because it offers the attractive features of the possibility of a current shunt, improved environmental resistance, and improved mechanical behaviour, such as flexibility and ductility.
  • cuprate superconductors have a common feature in that they contain ions with high oxidation states, such as Cu ⁇ + and Pb ⁇ + , or excess oxygen. These powerful oxidizing species may oxidize Ag to the oxide, which may dissolve in or react with the superconducting phase to form non-superconducting phases and hence affect the superconductivity.
  • the Bi-Pb-Sr-Ca-Cu-0 material has higher T c (110K) which is nearly 1/3 higher than the operating temperature (77K) as normally required (2/3 of T c ).
  • the Bi-Pb-Sr-Ca-Cu-0 is more flexible than YBa2Cu3 ⁇ 7.
  • Bi-Pb-Sr-Cu-Ca-0 does not suffer any phase transformation up to sintering temperature (900°C), whereas, with YBa2Cu3 ⁇ 7 system, the superconducting orthorhombic to the non-superconducting tetragonal phase transformation occurs at 600-700°C in air.
  • a large amount of cxygen (1/7 of the total oxygen content) will be released or uptaken during the transition.
  • the soaking time in oxygen is long and inconvenient, particularly in dense material and silver clad YB 2Cu3U7 composite where oxygen transport is inhibited by the slow diffusion rate. Thus it is much more difficult to make silver/YBa Cu3U7 composite.
  • Crystallography Difficult to avoid Platelike crystals, microcracks more amenable to texturing. Apparently less brittle.
  • Sensitivity T c is very P02 has little to Oxygen sensitive to P02 effect on T c partial pressure within 0.01 to (Po 2 ) 1.0 atm of P02 Bi-Pb-Sr-Ca-Cu-0 compound has a layered morphology, and crystalline alignment can be achieved by continuous drawing and rolling.
  • higher critical current density than for silver/Bi-Sr-Ca-Cu-O composite, owing to anisotropic current flow, is expected.
  • X-ray diffraction patterns show that lattice parameters were decreased with the Ag addition when samples were treated in air or oxygen, but the lattice parameters remain a constant against silver addition when samples were treated in low partial pressures of oxygen. This indicates that when samples were treated in air or O2, Ag was oxidized into silver oxide which reacts with PbO and CuO to form a solid solution, and hence destroys the superconducting phase, and altered the properties of the superconductors. On the other hand when samples were treated in low oxygen partial pressures silver is surprisingly maintained as isolated metal particles and does not react with superconductors. Thus no negative effect on T c was observed.
  • the inventors' research has also shown that the use of low oxygen partial pressures during he. : treatment as a manufacturing process step scarcely degrades the superconducting transition temperature for the undoped Bi b-Sr-Ca-Cu-O composite, with variations of zero resistance temperature within only 3 degrees being displayed after changes in oxygen pressure between 1.000 and 0.010 atm.
  • the optimum oxygen partial pressures for heat treatment of Bi-Pb-Sr-Ca-Cu-0 were found to coincide with those for silver doped Bi-Pb-Sr-Ca-Cu-0 composite. This new knowledge provides for the optimum processing conditions for preparation of the superconductor composite with improved performance.
  • the present invention provides a process for manufacturing a silver doped composite of the
  • Bi-Pb-Sr-Ca-Cu-0 superconductor comprising the step of heat treating on the Ag-doped Bi-Pb-Sr-Ca-Cu-0 composite under low oxygen partial pressures.
  • the heat treatment step comprises a step of sintering or annealing.
  • the silver doped composite can be manufactured by adding Ag powder to BPXCCO composite or by manufacturing wires and tapes by adding BPSCCO composite to an Ag tube and treating or by manufacturing multifilament.
  • O2 partial pressures of between 0.010 and 0.150 atmospheres may be used, but a range of between 0.010 and 0.080 atmospheres is preferred. We have found that the ideal range is between 0.050 and 0.070 atmospheres of partial pressure of O2 for 30% weight Ag doped samples. The optimal partial pressure decreases with increasing Ag additions.
  • the oxygen is preferably mixed with other, non-reactive gases to give a mixture which totals 1 atmosphere. Nitrogen is preferred.
  • the preferred nominal starting composition for the starting material Bi-Pb-Sr-Ca-CuO complex depends on a number of factors which relate to the process for manufacture of the superconductor (e.g. powder processing, powder forming, heating schedule).
  • a preferred starting composition for the specific set of processing conditions utilised in relation to the embodiment of the invention described herein is 1.6:0.4:1.6:2.0:3.0 (atomic ratio).
  • the Pb content may be varied from 0.3 to 0.5.
  • a partial pressure of O2 of 0.067 atmospheres was found to be ideal in this case.
  • the temperature at which the heat treatment is carried out is in the range of 800-850°C, and preferably in the range of 820-830°C. It will depend on the particular composition being manufactured. Depending upon the powder characteristics, any sintering time below which undesirable reactions occur could be used for sintering.
  • the heat treatment is preferably carried out for a time period of 50-150 hours, preferably 150 hours. This will also depend on the particular composition being manufactured.
  • the amount of silver which can be added to the composition may be up to 80% by weight of the total composition. Preferably it is up to 40% by weight. The actual amount will depend on the composition of the superconductor composite which is utilized. It is a question of getting the correct balance between the superconducting properties of the superconductor and the mechanical properties and current shunt properties given by the silver. A composition including 30% by weight of silver was found to be preferable with the superconductor composition referred to above.
  • the specific composition of the Pb doped Bi-Sr-Ca-Cu-0 superconductor and the temperature and ti ⁇ r.3 variables used in the manufacturing processing thereof are not crucial issues in the present invention.
  • the essential feature of the present invention is the step of heat treating the composite under low oxygen partial pressure.
  • Arconventional powder metallurgical process has been found to be advantageous for the preparation of the silver doped superconductor composite.
  • the Ag-doped Bi-Pb-Sr-Ca-Cu-0 composite is fabricated by mixing and calcining at 800°C to 850°C in a conventional manner. It is then subjected to sintering or annealing in a final firing stage under the process conditions of the present invention.
  • the present invention further provides a process for manufacturing a silver doped composite of the Bi-Pb-Sr-Ca-Cu-0 superconductor, comprising the steps of mixing together Bi2 ⁇ 3, PbO, SrC03, CaCC'3, and CuO in the atomic ratio Bil.6:PbO.3-0.5:SrI.6:Ca2.0: Cu3.0; calcining at 780-820°C for 20 to 3C hours in air with intermediate grinding; mixing with 5-40%, by weight, of Ag powder; and sintering or annealing at 800-85 ⁇ °C in an oxygen-nitrogen mixture with an oxygen partial pressure of 0.05-0.07 atmospheres.
  • a "powder-in-tube” process is preferably used.
  • Pre-prepared Bi-Pb-Sr-Ca-Cu-O powder is poured into a silver tube which is drawn or rolled into wire or tape and then subjected to heat treatment under low oxygen partial pressures.
  • the present invention further provides a process for manufacturing a silver wire or tape composite of the
  • Bi-Pb-Sr-Ca-Cu-O superconductor comprising the steps of:- mixing solutions of Bi2 ⁇ 3 in nitric acid and Pb(N0 3 ) 2 , Ca(N0 3 ) 2 • 4H 2 0, Sr(N0 3 ) 2 , Cu(N03)2 • 3H20 in distilled water in the atomic ratios Bil.6:Pb0.3-0.5:Srl.6:Ca2.0:Cu3.0; freeze drying the mixture to a powder; calcining at 800-850°C for 5 to 15 hours; sintering at 830-870°C for 20 to 150 hours; pouring the powder into an Ag tube; drawing and/or rolling the tube into wire or tape form; heat treating the wire or tape at 800-850°C for 20 to 70 hours in a mixture of oxygen and nitrogen with an oxygen partial pressure of 0.04 to 0.07 atmospheres; and repeating the heat treatment step.
  • the step of heat treating comprises a step of sintering or annealing.
  • a particular advantage of the present invention is that the large variation of T c , J c and lattice parameters which occur when the final firing stage is performed in air or pure oxygen are completely reversible when treatment occurs under the conditions of the present invention.
  • This has the advantage that the entire- process for preparation of the silver doped composites can be performed in air as long as a final heat treatment is conducted under conditions in accordance with the present invention, i.e. it is not necessary to control the atmosphere for heat treatment for all steps except the last heat treatment.
  • a further advantage is that the process of the present invention has no effect on the superconducting transition temperature for the undoped Bi-Pb-Sr-Ca-Cu-0 superconductor.
  • a further advantage is that the silver doped samples appear denser and better sintered, and the mechanical properties such as ductility and flexibility are improved. The silver particles are distributed in between superconducting grains, improving the connectivity between grains. Thus the critical current density is enhanced.
  • a further advantage is that the present invention enables the achievement of optimum superconducting properties.
  • J c critical current density
  • a further advantage is that the heat treatment step under low oxygen partial pressures affects a completely reversible treatment, i.e., composite produced by heat treating in air, which would contain predominantly low T c (80K) phase (2212) superconductor can be converted to predominantly high T c (110K) phase (2213) superconductor merely by heating under low O2 pressures and vice versa.
  • the present invention yet further provides a process for improving superconductivity of an Ag-doped composite of Bi-Pb-Sr-Ca-Cu-0 superconductor, wherein the predominant phase of the superconductor composite is the low T c (80K) phase (2212), comprising the step of heat treating an Ag-doped Bi-Pb-Sr-Ca-Cu-0 composite where the predominant phase is the low T c (80K) phase (2212) under low oxygen partial pressures, to produce the high T c (110K) phase (2213) as the predominant phase.
  • the reaction conditions of the present invention are such that the Ag does not react with the superconductor complex to form solid solutions of Ag2 ⁇ -CuO-PbO and degrade the superconductivity of the composite. Instead, the silver is advantageously maintained as isolated metal particles in the composite and ⁇ e not react with the superconductor. Further, when undoped superconductor is clad with Ag metal, the metal diffuses into the superconductor's pore space, densifying it without degrading the electronic properties. The resultant composite has advantageous mechanical properties of a metal as well as superconducting properties.
  • the present invention further provides a silver doped composite superconductor, comprising a superconductive compound of the Bi-Pb-Sr-Ca-Cu-0 system doped with up to 80% weight of Ag, the Ag being present substantially as metal unreacted with the superconductive compound.
  • the preferred final composition for the superconductor should approach Bi2- x Pb x Sr2Ca2Cu3 ⁇ y. x is preferably between 0.3 and 0.5. In the above compositions, the superconducting phase may be aligned by repeated pressing and annealing. Other techniques can be used.
  • Fi re 2A shows the normalized temperature dependence of resistivity for Ag-doped samples of Pb-Bi-Sr-Ca-Cu-0 superconductor sintered under pure oxygen (1.000 atm O2);
  • Figure 2B shows the normalized temperature dependence of resistivity for Ag--2oped samples of Pb-Bi-Sr-Ca-Cu-O superconductor sinter -a under air (0.209 atm O2);
  • Figure 3 shows the temperature of zero resistivity as a function of Ag-doped level for samples sintered under 1.000 atm and 0.067 atm oxygen;
  • Figure 4 shows the AC magnetic susceptibility measurements for Ag doped and undoped samples;
  • Figure 5 shows the temperature of zero resistivity as a function of oxygen partial pressure for samples doped with different levels of Ag
  • Figure 6 shows lattice parameters as a function of Ag dopant level for Ag-doped Pb-Bi-Sr-Ca-Cu-0 samples sintered under 0.209 atm (air) and 0.067 atm oxygen; and
  • samples without Ag addition were also prepared by the same processing.
  • the electrical resistivity was measured by the standard four-probe d.c technique.
  • X-ray diffraction patterns were obtained with a Philips type PW 1140/00 powder diffractormeter using CuK radiation.
  • Microstructural and compositional analyses were performed with a JEOL-JXA 840 scanning electron microscope (SEM), equipped with a Link Systems energy dispersive spectrometer (EDS).
  • SEM scanning electron microscope
  • EDS Link Systems energy dispersive spectrometer
  • the quantity of Cu3+ ions was determined by a volumetric measurement technique. In this technique specimens are dissolved in dilute hydrochloric acid, and hence the Cu ⁇ + concentration and the associated oxygen content in the materials can be determined by measuring the volume of the evolved oxygen.
  • Figure 1 shows the temperature dependence of resistivity (shown as voltage drop) for undoped samples treated at four different oxygen partial pressures. This illustrates the relative insensitivity of the Bi-Pb-Sr-Ca-Cu-0 system without Ag to variations in oxygen partial pressure.
  • Figure 2 shows the temperature dependence of resistivity for 0% to 30%wt Ag-doped samples treated in oxygen (A) and air (B) while maintaining other heat treatment conditions the same. It is evident that in contrast to the previous report (S. Jin et al), which claimed non-poisoning behaviour of Ag addition to the superconductivity of Bi-Sr-Ca-Cu-0 for samples treated in O2, the Ag addition drastically suppressed the superconducting transition of Bi-Pb-Sr-Ca-Cu-O. This was so when the samples were treated in air and particularly so when they were treated in oxygen.
  • Figure 4 shows the magnetic susceptibility measurements for undoped and Ag-doped samples. The results are in good agreement with the transition temperature measurements.
  • Figure 5 shows the zero resistance temperatures as a function of P02 and Ag addition for samples treated in different atmospheres from 0.010 to 1.000 atm of partial oxygen pressures. It is seen that the superconducting transitions for Ag-doped samples are very sensitive to oxygen partial pressure, contrary to the undoped samples - 14
  • Ag2 ⁇ -PbO-CuO system shows a large liquid region at above 650°C in 1 atm oxygen pressure (E.J. Kohlmeyer and H. Hennig, Z. Erzberg. Metall. 7 330 (1954)). This explains the depression of T c by Ag addition when samples were treated in air or oxygen. Silver oxide reacts with the superconductor to form a non-superconducting phase Ag2 ⁇ -PbO-CuO solid solution, and causes a depletion of CuO and PbO in the superconducting phase.
  • the superconducting network was not affected by up to 30%wt Ag addition as evidenced by T c measurement for samples treated in 0.067 atm of oxygen partial pressure. This is also seen from the normal state conductivity which was dominated by superconducting phase as indicated by a nearly constant temperature coefficient in a range of up to 30%wt Ag addition.
  • a SEM photomicrograph of 30%wt Ag doped sample was taken. It was seen that Ag particles did not form an Ag network up to 30% Ag addition. The Ag particles are uniformly distributed in the superconductor matrix. No Cu3+ ions were detected in Ag-doped and undoped samples by using the volumetric measurement technique.
  • a "powder-in-tube” process is utilized, involving packing a prepared BPSCCO powder in a silver tube and reducing the tube to wire or tape form through drawing or rolling respectively, and including a step of heat treating under low oxygen partial pressures.
  • BPSCCO has a micaceous morphology, which facilitates preferred orientation.
  • a high critical current has been achieved in the BPSCCO superconducting wires.
  • BPSCCO powder is prepared by a process which includes a step of freeze-drying.
  • a number of different ratios of starting materials were used in examples of the process to enable a determination of the most advantageous ratio to use.
  • the powders were immediately transferred to a furnace preheated at 200°C.
  • the powders were calcined at 830°C for lOh, pressed into pellets and sintered at 850°C for 20 to 150 h. During sintering, the pellets showed volume expansions of nearly 100%, indicating the formation of the 110K phase (BPSCCO).
  • the powder was poured into an Ag tube of 10mm outer and 8mm inner diameter, and the composite was drawn to a final outer diameter of 1mm.
  • the wires were then rolled into tapes -of (Ag) thickness of 0.1mm and width of
  • Ag/superconductor tapes of lm length were wound onto ceramic tubes of 35mm outer diameter.
  • the coils were heat-treated under the same conditions as the tapes.
  • the J c was 1913 Acm" 2 at 77K when the coil was treated under 0.067 atm oxygen, and it was 700 Acm" 2 for the coil treated in air.
  • the tape from which the coil was made had a cross-sectional area of 0.16mm 2 and a length of 1000mm.
  • the critical current density was measured of the total length of the coil. It should be pointed out that, although the J c of the coil was lower than that of the straight tape, the fact that the degree of the bending is substantial for what is presumably a uniform cross section demonstrates the feasibility of the production of superconducting oxide ceramic coils.
  • Bi:Pb:Sr:Ca:Cu 1.6:0.4:1.6:2:3 is desirable to enhance J c .
  • the starting compositions, Bi:Pb:Sr:Ca:Cu 1.6:0.4:2:2:4 and 1.6:0.4:1.6:2.2:3.1 cause accelerated formation of the 2223 phase, but a significant amount of non-superconducting phases present in the sample reduces the transport critical current density when the samples are sintered for a longer time.
  • the reaction produced by heat treatment under air and heat treatment under oxygen is completely reversible.
  • Ag-BPCCO composite material or Ag-BPCCO wire/tape which had been prepared with a final heat treatment in air, such that it contained the low T c (80K) phase (2212) as the major phase, and subject it to a heat treatment under low O2 pressure.
  • the temperature and time of the heat treatment step in accordance with the process of the present invention are not critical parameters.
  • Temperature and time may be varied depending on variables such as, for example, particular composition being manufactured, powder characteristics, the amount of silver in the composition.
  • the Ag which is mixed in with the superconductor is predominantly present as isolated metal particles which do not chemically react with the superconductor.
  • This type of com ⁇ ->site material, with Ag being present in the super ⁇ ductor as isolated metal particles has not been produ ed before.

Landscapes

  • Engineering & Computer Science (AREA)
  • Chemical & Material Sciences (AREA)
  • Manufacturing & Machinery (AREA)
  • Ceramic Engineering (AREA)
  • Materials Engineering (AREA)
  • Structural Engineering (AREA)
  • Organic Chemistry (AREA)
  • Inorganic Compounds Of Heavy Metals (AREA)
  • Superconductors And Manufacturing Methods Therefor (AREA)

Abstract

L'invention se rapporte à un composite supraconducteur à dopage à base d'argent du système Di-Pb-Sr-Ca-Cu-O. Pour les applications industrielles commerciales, il est nécessaire de stabiliser le supraconducteur au moyen d'un métal normal approprié ayant une conductivité électrique élevée et de bonnes propriétés mécaniques, et qui n'est pas toxique pour le supraconducteur. L'argent est l'un des métaux les plus appropriés à cet égard, mais, dans les procédés normaux de préparation de composites Ag et Bi-Pb-Sr-Ca-Cu-O, on a découvert que l'argent dégrade les propriétés supraconductrices. On a découvert qu'en incluant dans le procédé de préparation une phase de traitement thermique finale de frittage ou de recuit du mélange Ag/Bi-Pb-Sr-Ca-Cu-O dans des conditions de pressions partielles d'oxygène basses, les propriétés supraconductrices sont maintenues. Des pressions partielles d'O2 de l'ordre de 0,05 à 0,07 atmosphères sont de préférence utilisées. Des fils, des bandes et des multifilaments à revêtements à base d'argent peuvent être fabriqués selon un tel procédé.
PCT/AU1990/000288 1989-07-04 1990-07-04 Composite supraconducteur a dopage a base d'argent Ceased WO1991000622A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
AUPJ507889 1989-07-04
AUPJ5078 1989-07-04

Publications (1)

Publication Number Publication Date
WO1991000622A1 true WO1991000622A1 (fr) 1991-01-10

Family

ID=3774036

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/AU1990/000288 Ceased WO1991000622A1 (fr) 1989-07-04 1990-07-04 Composite supraconducteur a dopage a base d'argent

Country Status (1)

Country Link
WO (1) WO1991000622A1 (fr)

Cited By (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0450443A1 (fr) * 1990-04-02 1991-10-09 General Electric Company Préparation d'une bande d'un supraconducteur de Bi-Pb-Ca-Sr-Cu-O polycristallin orienté enduit d'argent
US5118662A (en) * 1989-05-04 1992-06-02 Eastman Kodak Company Article comprising conductive film of crystalline bismuth mixed alkaline earth oxide containing silver
EP0496281A3 (en) * 1991-01-19 1992-10-14 Sumitomo Electric Industries, Limited Method of preparing bismuth oxide superconducting wire
WO1993022799A1 (fr) * 1992-04-27 1993-11-11 Unisearch Limited Materiau composite supraconducteur a revetement d'argent
EP0588240A1 (fr) * 1992-09-11 1994-03-23 Mitsubishi Denki Kabushiki Kaisha Matériau oxyde supraconductrice à temperature élevée contentant Bismuth, et procédé pour sa préparation
AU657804B2 (en) * 1991-10-25 1995-03-23 Bicc Public Limited Company A superconducting ceramic composition
EP0621610A3 (fr) * 1993-04-21 1995-10-11 Vacuumschmelze Gmbh Procédé de traitement thermique des supraconducteurs à haute température dans des tubes contenant de l'argent.
US5670459A (en) * 1990-03-16 1997-09-23 Sumitomo Electric Industries, Ltd. Bismuth oxide superconductor of preparing the same
WO1997044833A1 (fr) * 1996-05-21 1997-11-27 American Superconductor Corporation NOUVELLE REACTION POUR COMPOSITES (Bi,Pb)2Sr2Ca2Cu3Oy HAUTE PERFORMANCE
US6993823B2 (en) * 2002-05-24 2006-02-07 Sumitomo Electric Industries, Ltd. Method of manufacturing oxide superconducting wire
CN113479925A (zh) * 2021-08-10 2021-10-08 福州大学 一种具有超快弛豫时间的铜酸钙纳米片的制备方法和应用

Non-Patent Citations (6)

* Cited by examiner, † Cited by third party
Title
APPLIED PHYSICS LETTERS, Volume 54, No. 16, issued 17 April 1989, (USA), M. MIMURA et al., "Improvement of the Critical Current Density in the Silver Sheathed Bi-Pb-Sr-Ca-Cu-O Superconducting Tape", see pages 1582 to 1584. *
JAPANESE JOURNAL OF APPLIED PHYSICS 2, LETTERS, Volume 27, No. 8, issued August 1988, (Japan), U. ENDO et al., "Preparation of the High-Tc Phase of Bi-Sr-Ca-Cu-O Superconductor", see pages L1476 to L1479. *
JAPANESE JOURNAL OF APPLIED PHYSICS 2, LETTERS, Volume 28, No. 2, issued February 1989, (Japan), H. SHIMOJIMA et al., "Preparation of the High-Tc Superconductive Bi-Pb-Sr-Ca-Cu-O Film by Pyrolysis of Organic Acid Salts", see pages L226 to L228. *
PHYSICA C, Volume 157, No. 1, issued 1 January 1989, (North-Holland, Amsterdam), H.K. LIU et al., "Stabilisation of 110K Superconducting Phase in Bi-Sr-Ca-Cu-O Pb Substitution", see page 95. *
PHYSICA C, Volume 160, No. 5-6, issued 1 October 1989, (North-Holland, Amsterdam), S.X. DOU et al., "The Interaction of Ag with Bi-Pb-Sr-Ca-Cu-O Superconductor", see pages 533 to 540. *
SUPERCONDUCTOR SCIENCE AND TECHNOLOGY, Volume 3, No. 3, issued March 1990, (Bristol, UK), S.X. DOU et al., "Critical Current Density in Superconducting Bi-Pb-Sr-Ca-Co-O Wires and Coils", see pages 138 to 142. *

Cited By (17)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5118662A (en) * 1989-05-04 1992-06-02 Eastman Kodak Company Article comprising conductive film of crystalline bismuth mixed alkaline earth oxide containing silver
US5670459A (en) * 1990-03-16 1997-09-23 Sumitomo Electric Industries, Ltd. Bismuth oxide superconductor of preparing the same
EP0450443A1 (fr) * 1990-04-02 1991-10-09 General Electric Company Préparation d'une bande d'un supraconducteur de Bi-Pb-Ca-Sr-Cu-O polycristallin orienté enduit d'argent
AU646538B2 (en) * 1991-01-19 1994-02-24 Sumitomo Electric Industries, Ltd. Method of preparing bismuth oxide superconducting wire
US6536096B2 (en) 1991-01-19 2003-03-25 Sumitomo Electric Industries, Ltd Method of preparing bismuth oxide superconducting wire
EP0496281A3 (en) * 1991-01-19 1992-10-14 Sumitomo Electric Industries, Limited Method of preparing bismuth oxide superconducting wire
AU657804B2 (en) * 1991-10-25 1995-03-23 Bicc Public Limited Company A superconducting ceramic composition
WO1993022799A1 (fr) * 1992-04-27 1993-11-11 Unisearch Limited Materiau composite supraconducteur a revetement d'argent
EP0588240A1 (fr) * 1992-09-11 1994-03-23 Mitsubishi Denki Kabushiki Kaisha Matériau oxyde supraconductrice à temperature élevée contentant Bismuth, et procédé pour sa préparation
EP0621610A3 (fr) * 1993-04-21 1995-10-11 Vacuumschmelze Gmbh Procédé de traitement thermique des supraconducteurs à haute température dans des tubes contenant de l'argent.
US5798318A (en) * 1996-05-21 1998-08-25 American Superconductor Corp. Reaction for high performance (Bi,Pb)2 Sr2 Ca2 Cu3 Oy composites
AU727912B2 (en) * 1996-05-21 2001-01-04 American Superconductor Corporation A novel reaction for high performance (Bi,Pb)2Sr2Ca2Cu3Oy composites
US6188920B1 (en) 1996-05-21 2001-02-13 American Superconductor Corporation High performance (Bi,Pb)2Sr2Ca2Cu3Oy composites
WO1997044833A1 (fr) * 1996-05-21 1997-11-27 American Superconductor Corporation NOUVELLE REACTION POUR COMPOSITES (Bi,Pb)2Sr2Ca2Cu3Oy HAUTE PERFORMANCE
US6993823B2 (en) * 2002-05-24 2006-02-07 Sumitomo Electric Industries, Ltd. Method of manufacturing oxide superconducting wire
CN113479925A (zh) * 2021-08-10 2021-10-08 福州大学 一种具有超快弛豫时间的铜酸钙纳米片的制备方法和应用
CN113479925B (zh) * 2021-08-10 2022-07-08 福州大学 一种铜酸钙纳米片的制备方法和应用

Similar Documents

Publication Publication Date Title
Dou et al. Ag-sheathed Bi (Pb) SrCaCuO superconducting tapes
JP3450328B2 (ja) 酸化物超伝導体の改善された処理
Zhang et al. Formation of Bi2Sr2CaCu2Ox/Ag multifilamentary metallic precursor powder-in-tube wires
Haldar et al. Processing high critical current density Bi-2223 wires and tapes
US5430008A (en) Method and composition for improving flux pinning and critical current in superconductors
Dou et al. Critical current density in superconducting Bi-Pb-Sr-Ca-Cu-O wires and coils
Dou et al. Superconductivity in a Ag‐doped Bi‐Pb‐Sr‐Ca‐Cu‐O system
WO1991000622A1 (fr) Composite supraconducteur a dopage a base d'argent
EP2264718B1 (fr) Procede de production et de modification d'un fil d'oxyde supraconducteur
EP0800494B1 (fr) PRODUCTION A BASSE TEMPERATURE (TEMPERATURE T INFERIEURE A 950 oC) DE SUPRACONDUCTEURS D'YBCO A TEXTURATION EN FUSION
WO1997028557A2 (fr) Fils supraconducteurs pour des applications faisant appel a des aimants
Lee et al. Filament-to-filament joining of multi-filamentary Ag/Bi-2223 superconducting tapes
EP0641750B1 (fr) Oxyde métallique et procédé pour sa préparation
WO1993022799A1 (fr) Materiau composite supraconducteur a revetement d'argent
JP2899510B2 (ja) 酸化物超電導体およびその製造方法
US5508252A (en) Bi oxide superconductors
Vacquier et al. HIGH-Tc SUPERCONDUCTOR OXIDE/OXIDE COMPOSITE MATERIALS: A REVIEW AND SOME RESULTS IN THE SYSTEM «Bi-BASED HTS CUPRATES/INSULATING OXIDES»
Lee et al. (Pb, Ti), a new superconductor in the Pb-1212 family
Neumüller et al. Processing and Properties of 2223 BiPbSrCaCuO Silver Sheathed Tapes
Zhang et al. Fabrication and properties of high J/sub c/multifilamentary (Bi, Pb)-2223 tapes with Ag-alloy sheath
Dou High Tc conductor processing techniques
Tenbrink et al. Manufacture and properties of Bi-2212-based Ag-sheathed wires
Jiang et al. Effect of pre-annealing temperature and atmosphere on the microstructure and transport property of Bi-2223/Ag tapes
Chin et al. Superconducting BiPbSrCaCuO wires grown on metal cores by a melt method
Liu et al. Kensington, NSW 2033, Australia

Legal Events

Date Code Title Description
AK Designated states

Kind code of ref document: A1

Designated state(s): AU JP US

AL Designated countries for regional patents

Kind code of ref document: A1

Designated state(s): AT BE CH DE DK ES FR GB IT LU NL SE