US3662093A - Superconducting electrical conductors - Google Patents

Superconducting electrical conductors Download PDF

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US3662093A
US3662093A US812015A US3662093DA US3662093A US 3662093 A US3662093 A US 3662093A US 812015 A US812015 A US 812015A US 3662093D A US3662093D A US 3662093DA US 3662093 A US3662093 A US 3662093A
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conductor
weight
cent
matrix
filaments
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Martin Norman Wilson
Peter Faraday Smith
Colin Russell Walters
John David Lewin
Robert Walter Broomfield
Robert Leslie Graham
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Imperial Metal Industries Kynoch Ltd
Science Research Council
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Imperial Metal Industries Kynoch Ltd
Science Research Council
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    • 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
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10S—TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10S505/00—Superconductor technology: apparatus, material, process
    • Y10S505/825—Apparatus per se, device per se, or process of making or operating same
    • Y10S505/884—Conductor
    • Y10S505/887—Conductor structure

Definitions

  • FIG. 1 A first figure.
  • SHEET 5 [IF 6 AMPERES AMPERE This invention relates to electrical conductors which have superconducting properties at cryogenic temperatures, i.e. at
  • the invention is also concerned with methods of manufacturing such conductors.
  • the purposes of the stabilizing matrix are to absorb and conduct away the heat evolved both during jumps of flux penetration into the superconductor material during changes in magnetic field and electrical current conditions, and the heat resulting from mechanical movement of the conductor, and to provide a low resistance electrical shunt to enable current temporarily to by-pass any region of superconductor material which becomes non-superconducting because of the any temperature increase, particularly arising from such a flux jump.
  • the return of that region to superconducting properties enables the current to pass once more through the superconductor material alone.
  • coil degradation When substantial lengths of these conductors are wound into coils, they usually attain much lower field strengths than those calculated from tests on short lengths of the conductor.
  • the degradation in performance obtained when coils are wound from the electrical conductors is known as coil degradation.
  • Coil degradation can be overcome by the use of even larger amounts of the stabilizing material, and sophisticated cooling provisions, but the end result is a coil which, although it is not degraded, is expensive to build and is larger than necessary because of its low overall current density. In addition the low overall current density limits the range of application of such coils.
  • Coil degradation arises principally from instabilities in the superconductor known as flux jumps. These occur when the closed loops of current induced in the superconductor material by the magnetic field become unstable and break down with evolution of heat. Therefore, there is a need for a superconductor in which flux jumps are eliminated or are reduced to such a degree that portions of the superconductor are not changed from the superconducting to the non-superconducting state, whereby the stabilizing matrix material could theoretically be eliminated.
  • the actual maximum size for the filament thickness needs to be determined by experiment, and in particular will vary with the current density, the variation of current density with temperature, and the thermal capacity per unit volume of the superconductor material.
  • filaments of such a thickness which would normally be their diameter, would be very difficult to deal with individually, so that a composite of a plurality of superconductor filaments held in a matrix, so as to produce a conductor of reasonable size, would be necessary for winding magnetic coils.
  • a composite superconductor has been proposed in which the filaments are embedded in a matrix of copper, or an insulator (to reduce coil inductance), but the filaments will normally be in electrical contact with one another, even if this only takes place at the ends of the composite conductor.
  • an object of the invention to provide an electrical conductor comprising a plurality of filaments of superconductor material each having a maximum thickness of about 0.005 cm. in which the filaments are effectively not in electrical contact with one another so that flux jumps are at least minimized.
  • an electrical conductor comprises a plurality of filaments of superconductor material contained within and separated from one another by a matrix of at least one non-superconductor material, each filament having a maximum thickness of about 0.005 cm. and being twisted or transposed about the other filaments with a length L along the conductor between each return of that filament to a given angular position relative to the matrix given by the relationship:
  • J is the critical current density in amps/cm.
  • d is the average thickness in cms of each filament perpendicular to the magnetic field
  • p is the electrical resistivity in ohm-cms of the nonsuperconductor material separating the filaments from each other and having the highest electrical resistance
  • B is the rate of change of field in gauss/second to which the electrical conductor is to be subjected
  • a is a number which is greater than 3 and is sufficiently large for the variation in flux rate of change along the length L divided by the mean flux rate of change B along the length L to be less than the thickness d di vided by the thickness of the conductor perpendicular to the field.
  • a method of manufacturing an electrical conductor comprises taking a plurality of filaments of superconductor material, providing them with a matrix of at least one non-superconductor material, and the matrix separating the filaments from each other, and twisting or transposing each filament about the other filaments with a distance L along the conductor between each return of that filament to a given angular position relative to the matrix given by the relationship:
  • L M 21 X 1 where k is a space factor equal to the ratio between the linear dimensions of superconductor and those of superconductor plus matrix materials in a direction parallel to the magnetic field to which the conductor is to be subjected, J is the maximum current density in amps/cm to be carried by the superconductor material (in zero or very low magnetic fields), d is the average thickness in cms of each filament perpendicular to the magnetic field, p is the electrical resistivity in ohm-cm.
  • B is the rate of change of field in gauss/second to which the electrical conductor is to be subjected
  • a is a number which is greater than 3 a nd is sufficiently large for the variation in flux rate of change B along the length L divided by the mean flux rate of change B along the length L to be less than the thickness d divided by the thickness of the conductor perpendicular to the field.
  • the number a is greater than 10.
  • a value for a of greater than 3 will not always be satisfactory, particularly for irregular arrays of superconducting filaments, and for large conductors.
  • the minimum value ofa varies with the square root of the quotient between the conductor thickness perpendicular to the field and the filament thickness d.
  • the value ofL calculated by the preceding formula must be multiplied by the approximate correction factor (S/S d)" If the matrix separating the filaments is composed of more than one material, the values of p and S to be used in the preceding formula are those corresponding to the material which has the highest value ofp.
  • the matrix is preferably a ductile material to enable the superconductor and non-superconductor materials to be worked together to produce the required physical dimensions. Also, because the length L increases with the resistivity p of the nonsuperconductor material, for practicability the resistivity p needs to be at a substantial level.
  • the matrix is of a ductile copper-base alloy which contains not less than 50 weight/cent copper and has an electrical resistivity of at least 6 micro-ohm-cm. at 20 C.
  • the copper-base alloy may contain the alloying additions up to 50 weight/cent nickel, up to 30 weight/cent manganese, up to 40 weight/cent zinc, up to 8 weight/cent tin, up to 10 weight/cent aluminum, up to 4 weight/cent silicon, up to 2 weight/cent iron, up to 2 weight/cent chromium and up to l weight/cent phosphorus.
  • the ductile copper-base alloy contains 5-50 weight/cent nickel, 0-2 weight/cent manganese, balance copper, which produces an electrical resistance for that range of alloys of at least 7 micro-ohm-cm. at 4.2 K., whereby a high degree of electrical insulation is achieved between the superconductor filaments, so that the length L can be substantial, although the ductility of the alloy enables the matrix and the filaments to be co-processed. In this way the electrical conductor can be manufactured using a co-processingroute. Also these alloys have hardnesses which can be very similar to selected superconductor materials.
  • the length L increases with the resistivity p of the non-superconductor matrix material.
  • the resistivity p is preferably as high as possible and the present invention contemplates a highly resistive matrix whereby there is produced a large L.
  • the value of L has a limit determined by the value of a being sufficiently large for the variation in flux rate of change along the length L divided by the mean flux rate of change B along the length L to be less than the thickness d divided by the thickness of the conductor perpendicular to the field.
  • a ductile matrix is preferred, in which case a non-superconductor material is chosen which has a high resistivity, for example the cupro-nickel alloys mentioned above.
  • a further factor involved is the critical current density J in the superconductor material; this is dictated byv the selection of superconductor made.
  • space factor k which is equal to the ratio between the linear dimensions of superconductor and those of superconductor plus matrix materials in a direction parallel to the field to which the conductor is to be subjected.
  • thickness d of the superconductor filaments this has the limited maximum value described above prescribed by the requirement that any flux jumps in each superconductor filament will not increase the temperature of the filament above that at which the conductor can carry the required transport current. in practice a maximum filament diameter is about 0.005 cm.
  • the fourth factor is B which is arranged to be as low as possible, consistent with a reasonable rate of change of the field and possib le variations in the power supply to the conductor. A typical B is 1,000 gauss per second.
  • the superconductor material is a superconducting niobium-titanium alloy, for example niobium 44 weight/cent titanium, but superconductor binary or higher alloys of the elements niobium, titanium, zirconium, hafnium and tantalum can be used. If required, substantially pure niobium can be used.
  • the superconductor material can be a mixture or tin-rich alloy of niobium with tin, this being co-processed in the matrix
  • the matrix can the resistivity at 20 C. is 1.7 micro-ohm-cm. and the Vickers comprise excess tin or niobium.
  • a suitable heat treatment, for Hardness Numbers are 45 and 1 17 in the annealed and 60 perexample in the range 700 to 950 C. for 5 to 120 minutes, can cent cold-worked conditions respectively with respective ultithen be applied to produce the intermetallic compound Nb Sn 5 mate tensile Strengths f 14 and 24.
  • the most Preferred alloys are the cupmmlckels, additions fi ld, Th upper i i f 950 C must be reduced if necessary thereto of small quantities of silicon, zinc and aluminum as so as not to exceed the melting point of the matrix.
  • Nb Sn has well as manganese improving corrosion resis'ahce and slightly appreciably improved superconducting properties over those increasing electrical resistivities.
  • Other preferred alloys are ofniobium,although it does suffer from brittleness.
  • cross-sectional dimensions of this brittle material can be arranged to be so small that the effects of brittleness are largely overcome, whereby reasonable deformation of the conductor can be achieved without breakage of the superconductor filaments.
  • FIG. 4 is a cross-sectional view of an assembly of supercondllciol' elements and cupro-nickelmatrix material;
  • FIG. 3 shows the way in which the hardness of the two 5 is a Perspective View of a conductor with P of the copper alloys exemplified thereon changes during working. cupro-nickcl matfiX removed; and
  • the abscissa of the graph of FIG. 3 gives a percentage reduc- FIGS- 6 and 7 are Current p Versus field tion in cross-sectional area during the working, while the orkilogauss) cur e o a ous twisted sup uc ors dinates give the hardness as the Vickers Hardness Number. dergoing changing fields.
  • h h h pplicable cupro-nickel alloy can be 30 weight/cent manganese.
  • the most preferred alloys are 11 1 r h superconductor alloy.
  • copper 5 5 weight/cent i k l 2 i h manganese From the above, it can be seen that the required ductile the possible manganese addition having little effect upon elecpp can be SeleCted to match the physi trical resistivity but improving corrosion resistance.
  • characteristics of the superconductor material to be used, and Various specific ductile alloys are listed in the following FIG. 1 and/or Table I then gives the resistivity at 20 C.
  • a billet of the superconductor alloy niobium 44 weight/cent titanium is cast and then forged at about 600700 C. This is pickled in a mixture of nitric and hydrofluoric acids, and is quickly inserted in a prepared can of the alloy copper 25 weight/cent nickel.
  • the can is prepared from a cast and forged billet, and is pickled in 50 percent nitric acid.
  • the can has an external diameter of about 2% inches, although it is envisaged that 9 or 12 inches may be appropriate.
  • the quantities of the superconductor alloy and the cupro-nickel are arranged such that there are about 6 parts of cupro-nickel to 10 parts of the superconductor alloy.
  • the can is evacuated and sealed to minimize any oxidation of the facing surfaces of the superconductor and the cupronickel, and is then extruded at about 350-650 C. with a reduction ratio of about 6:1. After extrusion, room temperature drawing is carried out with a total reduction of about 95 percent, the end result being an elongated hexagonal rod.
  • This rod is cut into, in this example, 61 lengths which are packed into a further can of the cupro-nickel alloy, any gross cavities being filled with further hexagonal rods of the cupronickel alloy.
  • This assembly is shown in FIG. 4. The use of this can and the extra rods of cupro-nickel provide approximately equal quantities of the cupro-nickel and the superconductor alloy.
  • This assembly is evacuated and sealed and is again extruded at about 350-650 C. with a reduction ratio of about 6: 1. This is followed by a series of room temperature drawing to produce a reduction in cross-sectional area of at least 99.5 percent. This produces a wire which has an overall diameter of about 0.01 inch, containing the 61 filaments each of a diameter of about 0.001 inch. (If required, the room temperature drawing can be continued to provide filaments having a diameter of about 0.0005 inch or less.)
  • the wire is twisted at a rate of one turn per inch, i.e. to give a length L 1 inch.
  • the result is shown in FIG. in which part of the cupro-nickel matrix has been removed to show the filaments and their rate of twist.
  • the overall conductor diameter is 0.01 inch, and the filament diameters are 0.001 inch.
  • the wire is then provided with a heat treatment for about 1 hour at 350-450 C. to refine the dislocation structure in the superconductor alloy, whereby the superconducting properties of this alloy are maximized, and this also serves to partially anneal the cupro-nickel alloy.
  • this heat treatment can also be applied during the room temperature drawing processes, typically when the wire has reached an overall diameter of about 0.025 inch. When this is carried out, the partial annealing of the cupro-nickel will facilitate the further co-processing.
  • the heat-treated wire is provided with an insulation coating as required, typically of polyvinyl acetate.
  • the formula given above can be used, the various parameters therein being k, the space factor, equal to 0.8; J, the low field current density for niobium 44 weight/cent titanium, as 3 X a filament diameter d of 2.5 X 10 cm.; a resistivity at 42 K. for copper 25 weight/cent nickel of p 3 X 10' ohm-cm; and a rate of change of field B 1,000 (1 kilogauss per second).
  • L as one inch, which is 2.54 cm., a is about 66. This is well above the preferred value of a as 10.
  • the twist pitch L is 1.45 cm. Using the preferred value ofa as 10, the twist pitch L is only 4.4 mm. This may be too high a rate of twist to be performed satisfactorily and economically.
  • the compatibility between the alloys copper 25 weight/cent nickel and niobium 44 weight cent titanium enables reductions of this order without undue difficulty, and it is found that the filaments have a very uniform circular cross section, and are also uniform along their lengths. With filaments of these dimensions, any irregularity along their lengths would rapidly lead to breakage.
  • transposing can be used instead of twisting in order that each filament shall be subjected to the same influence of magnetic flux.
  • a conductor containing large numbers of filaments will probably need to be transposed, the approximate criteria being that transposing is necessary if is greater l'ihan O delta B across conductor 0 mean of modulus B across conductor and mean of modulus along twist where f? is again the rate of change of field and delta is the variation in the rate of change of field, d,is the filament diameter and d is the conductor diameter.
  • an elongated hexagonal rod manufactured as described in the first example is cut into 18 lengths which are packed into a further can of copper 25 weight/cent nickel, any gross cavities being filled with further hexagonal rods of the cupro-nickel alloy. There results a matrix to superconductor ratio of about 2.26:1.
  • the assembly so produced is processed as described in the first example to produce a conductor having an overall diameter of about 0.025 cm. and a filament diameter d of 3.26 X 10 cm.
  • the conductor was provided with a twist having a pitch length L of about cm. determined by the use of the formula with a 3, a space factor k as 0.75, and a rate of change of field B as 360 gauss/second.
  • a conductor was manufactured in the way described in the second example, except that its twist pitch was L 6 cm.
  • a rate of change of field E of 1,400 gauss/second which corresponds to a 27 the dot-and-dash curve of FIG. 7 was produced. This is quite a satisfactory performance, and is better than that of the solid curve of FIG. 6.
  • the conductor can be provided with one or more strands of oxygen-free high conductivity copper to act as an electrical shunt in the event of gross break-down of superconductivity or breakage of the superconductor filaments.
  • These strands can be embodied in the matrix or cabled with the conductor.
  • the matrix includes more than one non-superconductor material, it is the electrical resistance of the matrix material having the highest value thereof and located between the filaments which is to be used for p in the relationship given above because it is'the greatest electrical resistance which is effective in reducing magnetization currents.
  • the matrix is composed entirely of such a material it will be very difficult to protect any coil of appreciable size from burn-out in the event of an accidental transition to the non-superconducting state. Furthermore the low thermal conductivity of the matrix, together with the alternating current heat dissipation in the superconductor, may result in an undesirably large temperature rise in the superconductor.
  • a'matrix containing two materials i.e. one of high resistivity to ensure a reasonable twist rate, and one of low resistivity (and high conductivity) to satisfy electrical protection and heat dissipation requirements.
  • the geometric arrangement of the two components must be such that any electrical path connecting any two filaments must intersect a layer of the high resistivity material; for example one way of achieving this is for each superconducting filament to be first surrounded by a layer of high resistivity alloy, and for the resulting sheathed filaments to be set in a copper matrix. lnterchanging the two materials results in another valid possibility.
  • An electrical conductor in a changing magnetic .field comprising a plurality of filaments of a material which is superconductive at temperatures of about 4.2.K. and above contained within and separated from one another by a matrix of at least one material which is not superconductive at about 4.2 K., each filament having a maximum thickness of about 0.005 cm. and being twisted or transposed about the other filaments with a length L along the conductor between each return of that filament to a given angular position relative to the conductor given by the relationship:
  • k is a space factor equal to the ratio between the linear dimensions of superconductor and those of superconductor plus matrix materials in a direction parallel to the magnetic field in which the conductor operates
  • J is the critical current density in amps/cm. of the superconductor material (in zero or very low magnetic fields)
  • d is the average thickness in cms of each filament perpendicular tothe magnetic field
  • p is the electrical resistivity in ohm-cms of the non-superconductor material separating the filaments from each other and having the highest electrical resistance
  • 8 is the rate of change of field in gauss/second
  • a is a number which is greater than 3 and is sufficiently large for the'variation in flux rate of change Q along the length L divided by the mean flux rate of change 8 along the length L to be less than the thickness :1 divided by the thickness of the conductor perpendicular to the field.
  • a conductor according to claim 4 wherein the ductile copper-base alloy contains 5-50 weight/cent nickel, 0-2 weight/cent manganese, balance not less-than 50 weight/cent copper, and has an electrical resistance of at least 7 microohm-cm. at 4.2 K. 1
  • a conductor according to claim 1 wherein the superconductor material is selected from the group consisting of superconductingbinary or higher alloys of niobium, titanium, zirconium, hafnium and tantalum.
  • a conductor according to claim 1 wherein the conductor comprises a plurality of filaments of niobium 44 weight/cent titanium contained within a matrix of the ductile alloy copper 25 weight/cent nickel, k being 0.8, J being 3 X 10 d being 2.5
  • a conductor according to claim l wherein the conduc-. tor comprises a plurality of filaments or niobium 44 weight/cent titanium contained within a matrix of the ductile alloy copper 25 weight/cent nickel, k being 0.8, J being 3 X 10", d being 2.5 X 10, p being 3 X 10 B being not more than 1,000, L being 17 cms approximately and a being 10 at least.
  • a conductor according to claim 1 wherein the conductor comprises a plurality of filaments of niobium 44 weight/cent titanium contained within a matrix of the ductile alloy copper 25 weight/cent nickel, k being 0.8, J being 3 X 10*, d being 2.5 X 10 p being 3 X 10 B being not more than 1,000, L being 56 cm. approximately and a being 3 at least.
  • a conductor according to claim 1 wherein the conductor comprises a plurality of filaments of niobium 44 weight/cent titanium contained within a copper matrix, k
  • B being not more than 1,000, L being 4.4 mm approximately and a being 10 at least.
  • a conductor according to claim 1 wherein the conductor comprises a plurality of filaments of niobium 44 weight/cent titanium contained within a matrix of the ductile alloy copper 25 weight/cent nickel, k being 9.75, J being 3 X 10 d being 3.26 X p being 3 X 10", B being not more than 1,400, L being 6 cm. and a being about 27 at least.
  • a conductor according to claim 1 wherein the conductor comprises a plurality of filaments of niobium 44 weight/cent titanium contained within a matrix of the ductile alloy copper 25 weight/cent nickel, k being 9.75, J being 3 X 10 d being 3.26 X 10, p being 3 X 10', B being not more than 360, L being 6 cms and a being about 53 at least.

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Cited By (14)

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US3702373A (en) * 1971-03-05 1972-11-07 Comp Generale Electricite Intrinsically stable superconductive conductor
US3904809A (en) * 1973-03-01 1975-09-09 Siemens Ag Tubular electrical conductor made up of individual superconducting conductors
US4093817A (en) * 1975-04-23 1978-06-06 Gesellschaft Fur Kernforschung M.B.H. Superconductor
US4254299A (en) * 1976-08-31 1981-03-03 Bbc Brown, Boveri & Company, Limited Electrical superconductor
US4458106A (en) * 1981-11-02 1984-07-03 Japan Atomic Energy Research Institute Super conductive wire
US4803310A (en) * 1987-05-04 1989-02-07 Intermagnetics General Corporation Superconductors having controlled laminar pinning centers, and method of manufacturing same
US4894556A (en) * 1987-06-15 1990-01-16 General Dynamics Corporation, Convair Division Hybrid pulse power transformer
US4927985A (en) * 1988-08-12 1990-05-22 Westinghouse Electric Corp. Cryogenic conductor
WO1996000448A1 (en) * 1994-06-23 1996-01-04 Igc Advanced Superconductors, Inc. Superconductor with high volume copper and a method of making the same
US6199266B1 (en) 1994-04-11 2001-03-13 New England Electric Wire Corporation Method for producing superconducting cable and cable produced thereby
US20040226163A1 (en) * 2003-02-21 2004-11-18 Robert Hentges Increasing the copper to superconductor ratio of a superconductor wire by cladding with copper-based strip
WO2008104141A1 (de) * 2007-02-28 2008-09-04 W.E.T. Automotive Systems Ag Elektrischer leiter
US20130126295A1 (en) * 2011-11-18 2013-05-23 Raymond F. Decker Coin composition and method of manufacturing the same
CN115440415A (zh) * 2022-10-12 2022-12-06 湖南康达科新材料有限公司 一种结合强度高的镍包铜复合带材及其制备方法

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GB1387621A (en) * 1971-04-15 1975-03-19 Imp Metal Ind Kynoch Ltd Composite materials and a method of manufacture thereof
US4148129A (en) * 1976-11-01 1979-04-10 Airco, Inc. Aluminum-stabilized multifilamentary superconductor and method of its manufacture
DE3048418C2 (de) * 1980-12-22 1983-06-09 Siemens AG, 1000 Berlin und 8000 München Kabelförmiger, kryogen stabilisierter Supraleiter für hohe Ströme und Wechselfeldbelastungen
FR2551254B1 (fr) 1983-08-30 1987-10-23 Alsthom Atlantique Brins supraconducteurs utilisables aux frequences industrielles
JP2749652B2 (ja) * 1989-08-09 1998-05-13 古河電気工業株式会社 超電導線
CA3186455A1 (en) * 2015-12-04 2017-06-08 Berkshire Grey Operating Company, Inc. Systems and methods for dynamic processing of objects
CN109521343B (zh) * 2018-12-29 2020-11-10 广东电网有限责任公司 一种引雷塔保护范围的评估方法

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GB1096535A (en) * 1964-03-11 1967-12-29 Siemens Ag A superconductor wire
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Cited By (19)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3702373A (en) * 1971-03-05 1972-11-07 Comp Generale Electricite Intrinsically stable superconductive conductor
US3904809A (en) * 1973-03-01 1975-09-09 Siemens Ag Tubular electrical conductor made up of individual superconducting conductors
US4093817A (en) * 1975-04-23 1978-06-06 Gesellschaft Fur Kernforschung M.B.H. Superconductor
US4254299A (en) * 1976-08-31 1981-03-03 Bbc Brown, Boveri & Company, Limited Electrical superconductor
US4458106A (en) * 1981-11-02 1984-07-03 Japan Atomic Energy Research Institute Super conductive wire
US4803310A (en) * 1987-05-04 1989-02-07 Intermagnetics General Corporation Superconductors having controlled laminar pinning centers, and method of manufacturing same
US4894556A (en) * 1987-06-15 1990-01-16 General Dynamics Corporation, Convair Division Hybrid pulse power transformer
US4927985A (en) * 1988-08-12 1990-05-22 Westinghouse Electric Corp. Cryogenic conductor
US6199266B1 (en) 1994-04-11 2001-03-13 New England Electric Wire Corporation Method for producing superconducting cable and cable produced thereby
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Also Published As

Publication number Publication date
JPS5324800B1 (enrdf_load_stackoverflow) 1978-07-22
DE1917084A1 (de) 1969-10-23
GB1205130A (en) 1970-09-16
NL139426B (nl) 1973-07-16
NL6905301A (enrdf_load_stackoverflow) 1969-10-07
CH492321A (de) 1970-06-15
BE731005A (enrdf_load_stackoverflow) 1969-10-03
DE1917084B2 (de) 1971-06-03
CS194151B2 (en) 1979-11-30
FR2005492A1 (enrdf_load_stackoverflow) 1969-12-12

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