US3130092A - Process of making cubic texture silicon-iron - Google Patents

Process of making cubic texture silicon-iron Download PDF

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US3130092A
US3130092A US816889A US81688959A US3130092A US 3130092 A US3130092 A US 3130092A US 816889 A US816889 A US 816889A US 81688959 A US81688959 A US 81688959A US 3130092 A US3130092 A US 3130092A
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silicon
orientation
iron
reduction
cube
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Dale M Kohler
Martin F Littmann
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Armco Inc
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Armco Inc
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Priority to BE584171A priority patent/BE584171A/fr
Priority to FR809810A priority patent/FR1240322A/fr
Priority to CH558260A priority patent/CH413885A/de
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    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/14766—Fe-Si based alloys
    • H01F1/14775—Fe-Si based alloys in the form of sheets
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
    • C21D8/1233—Cold rolling
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
    • C21D8/1266—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest between cold rolling steps
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
    • C21D8/1272—Final recrystallisation annealing

Definitions

  • Silicon-iron sheet stock having a high degree of preferred orientation has come into widespread commercial use, and in many fields the highly directional permeability of such stock has brought about radical changes in the design of transformers and other electrical apparatus.
  • Such silicon-iron products have had a crystal orientation which may be designated as (110) [001] in the standard notation of Millers indices. This orientation means that the product has a high permeability in the rolling or straight-grain direction, but a poor permeability in other directions.
  • the crystalline structure of silicon-iron is cubic, so that the individual crystals in a polycrystalline material may be visualized as a series of cubes.
  • a cube edge [001] is parallel to the rolling direction and a dodecahedral face (110) is parallel to the rolling plane.
  • Four of the cube edges are parallel to the direction of rolling, but no face of the cube is parallel to the surfaces of the sheet.
  • the orientation has been referred to as a cube-on-edge type.
  • the cube edges which lie transverse to the direction of rolling are not parallel to the surfaces of the sheet. Consequently, the transverse permeability is low because the most effective path for the magnetic flux, is parallel to the cube edges.
  • the attaining of a high degree of cubic texture in silicon-iron is accomplished by secondary recrystallization of a material characterized by some grains which are already in the desired orientation (or within a comparatively few degrees of it), which grains or nuclei grow during the secondary recrystallization at the expense of grains having a substantially different orientation.
  • FIG. 1 is a stereogram of the cube poles of representative individual grains of a silicon-iron piece characterized by the cube-on-edge type of orientation.
  • FIG. 2 is a diagrammatic representation of this type of orientation.
  • FIG. 3 is an X-ray pole-density stereogram of (200) poles showing a derivative orientation designatable as (111)[1l2], produced by cold rolling the material of FIG. 1.
  • FIG. 4 is a diagram of this type of orientation.
  • FIG. 5 is an X-ray pole-density stereogram of (200) poles showing a derivative orientation which may be designated as ()[0O1], resulting from the recrystallization of the product of FIG. 3.
  • FIG. 6 is a diagram of this type of orientation.
  • FIG. 7 is an X-ray pole-density stereogram of (200) poles of material showing a derivative orientation (hereinafter described) produced by another stage of cold rollmg.
  • FIG. 8 is a diagram of this orientation.
  • FIG. 9 is an X-ray pole-density stereogram of (200) poles of the material of FIG. 7 after a primary recrystallization.
  • FIG. 10 is a stereogram of the cube poles of individual grains of the material of FIG. 9 after having been subjected to secondary recrystallization, and showing cubic texture, designatable as (100) [001].
  • FIG. 11 is a diagram of this orientation.
  • FIGS. 3, 5, 7 and 9 numerical indications of the intensities are shown in times random.
  • the silicon-iron material employed in the practice of the invention should have a silicon content sufiiciently high to prevent phase changes during heat treatment, but low enough to prevent brittleness during rolling. A range of 2.5 to 4.0% silicon is satisfactory.
  • the final product should have a high degree of purity by which is meant freedom from carbon, sulphur, nitrogen, oxygen, inclusions and the like. Purity is usually attained in the production of the metal in known ways, although carbon may be reduced at any early heat treating stage of the routing by subjecting the material to a decarburizing anneal, preferably in accordance with the teachings of the Carpenter et a1. Patent No. 2,287,467, issued June 23, 1942.
  • a preferred range of silicon is from 2.90 to 3.30%.
  • the cube-on-edge material should contain .007% or less carbon, .03 to .15 manganese, and .015 to .030% sulfur, the remainder being substantially all iron with normal impurities, and with a total oxide content of .015 or less.
  • the low carbon content is important because it makes for low core loss values.
  • the total oxide content is preferably no more than .004% in the final product just before secondary recrystallization.
  • Hot rolled silicon-iron is generally characterized by an incompletely developed preferred crystal orientation.
  • the crystals In both hot and cold rolling, the crystals not only become longer but tend to change their orientation by a process of slip in preferred directions and on preferred crystallographic planes. In this manner, deformation produces a preferred texture in the material, with the individual crystals in various conditions of stress. Raising the temperature after deformation permits the crystals to release their stresses through recrystallization; and the crystals generally change-in orientation by the adoption of adjacent positions of lower energy.
  • the art has hitherto learned various procedures for producing from polycrystalline silicon-iron the material above designated as of the cube-on-edge type, by subjecting the hot rolled material to one or to a series of controlled cold reductions followed by heat treatments.
  • Our researches have indicated that the cube-on-edge or (110) [001] orientation is in many instances at least a derivative of a (111) [112] orientation produced by tilting the crystals in the rolling direction by a sufficient amount and then causing them to assume a related low energy position which is the cube-on-edge orientation.
  • FIG. 1 of this application is a stereogram of the cube poles of typical cube-on-edge silicon-iron, clearly indicated in a crystal position such as is illustrated in FIG. 2 hereof.
  • two small cubes 1 and 2 have been shown, the rolling direction being indicated by an arrow, and the planes of the surfaces of the sheet material being understood to be parallel to the plane of the paper on which the drawing is made.
  • the first step is to cold reduce such material within certain limits so as to bring about the tilted condition of the crystals indicated in the pole-density stereogram which forms FIG. 3 hereof and illustrated by the small cubes 3 and 4 of FIG. 4.
  • a cold reduction generally of about 55% to 90% will produce the eifect, it being understood that the tilting will vary with the degree of cold rolling reduction.
  • the orientation at this stage will respond generally to the notation (111) [112] of Millers indices.
  • the intermediate anneal which accomplishes this is an anneal, either open or box, preferably at about 1200 to 2200 F and preferably in dry hydrogen. If an open or strip anneal is used, a temperature of 1500 to 1700 F. is preferred. If a box anneal is used, a preferred range is 1400 to 1600 F., although good results may be obtained over the entire range given above, namely 1200 to 2200 F.
  • the annealing atmosphere should be such as to preclude undue oxidation.
  • the material is next subjected to a second cold rolling treatment.
  • the crystals are again tilted, and this produces the complex pole density stereogram which forms FIG. 7 hereof.
  • a study of this stereoa gram will indicate that the orientation of the crystals is substantially that diagrammed at 7, 8, 9 and 10 in FIG. 8.
  • the crystal orientation illustrated is obtained by rotating the cubes substantially 30 each way about the transverse axis, and then substantially 10 about an axis normal to the sheet surface. If this index were to be described by the use of Millers indices, It would approximate a (7,10,15 [E310] orientation.
  • the cold rolling treatment must be controlled as to extent.
  • a cold rolling reduction of about 50% to 80% Will generally be found effective.
  • This second cold rolling is, however, affected by the nature of the intermediate anneal previously outlined.
  • the intermediate anneal is an open or strip anneal an optimum range of reduction in the second
  • the material is next subjected to an intermediate ancold rolling treatment will be found to be about 60% to 70%. If a box anneal has been practiced, a percentage reduction in the second stage of cold rolling of a some what higher value, namely 70% to will be found best.
  • a material oriented as shown in FIGS. 7 and 8 can be caused to assume the orientation indicated by the pole density stereogram set forth here as FIG. 9, by primary recrystallization.
  • An examination of this stereogram will indicate that while the cube edges have been realigned in the rolling direction with reasonable uniformity, the tilting of the cube faces with reference to the plane of the sheet stock has broadened and becomes more heterogeneous.
  • a large number of the grains are tilted by more than 22 /2 from the position illustrated in FIG. 6 as the 120) [001] orientation, and a substantial number have been tilted into the [001] position or within a few degrees of it. It is these last mentioned grains which form the nuclei for the subsequent conversion of the stock to one having preponderantly the cubic orientation, in the process of secondary recrystallization.
  • the original material is, of course, an ingot of silicon-,
  • the cube-on-edge stock which forms the starting material here should have a high degree of perfection of the (110) [001] orientation.
  • the cube-on-edge material preferably has a relatively large grain size (about 5 mm. in diameter).
  • the material having the high degree of (110) [001] orientation is cold re.- prised to a thickness of about /2 to its original thickness, i.e., with a reduction of 55% to 90%, or within the narrower preferred ranges discussed above. It is then recrystallized. Varying heat treatments at this point are possible.
  • An open, strand or continuous anneal may be used; but a box anneal in an inert or reducing atmosphere such as hydrogen is preferred.
  • the material may be heated to a temperature of about 1200 to 2200 F. and held for about two hours at such temperature.
  • the essentials here are to efiect a primary recrystallization and fit the material for further cold reduction, while avoiding the development of oxides at its surfaces.
  • the product having the high degree of (120) [001] orientation is again cold reduced to about /2 to its thickness or with a reduction of 50% to 80%, or preferably within the narrower preferred ranges discussed above.
  • the final rolled product is then given a box anneal in hydrogen. While the attainment of a recrystallizing temperature will produce a substantial number of grains having the desired (100) [001] orientation if the preceding steps have been performed, a product in which at least the majority of the grains have the (100) [001] orientation is obtained when discontinuous or selective grain growth takes place.
  • This grain growth sometimes called secondary recrystallization, takes place at temperatures above about 1900 F.
  • the annealing atmosphere should be pure and non-reactive. Annealing separators may be used. While hydrogen is suitable, the use of vacuum or inert atmospheres like helium, argon or the like is desirable. In the secondary recrystallization, the (100) [001] crystals tend to grow at the expense of the other crystals, producing a very nearly perfect orientation in the cubic texture.
  • the final heat treatment is preferably carried on in accordance with the teachings of the copending application of Kohler (one of the inventors herein) entitled The Production of Oriented Silicon-Iron Sheets by Secondary Recrystallization, Serial No. 813,289, filed May 14, 1959, which teaches in essence the use of an atmosphere in the final heat treatment of hydrogen or a non-reactive gas such as argon or helium, which atmosphere contains a very small amount of a highly polar compound such as hydrogen sulphide, sulphur dioxide, an oxide of carbon, or a mixture of these.
  • the highly polar compound is believed to be absorbed or adsorbed on the crystal planes at the surfaces of the sheet stock so as to satisfy the positive unsatisfied charges there, the result being a shifting of the energies of crystals of difiering orientations in such a way that the (100) [001] orientation becomes the lowest energy orientation by a substantial amount, making for a more positive and complete cubic texture orientation in the stock.
  • the final anneal maybe and preferably is a box anneal, although it has been found that an open, strand or continuous anneal may be used.
  • FIG. 10 The result of the final anneal is illustrated by the stereogram FIG. 10, and diagrammed in FIG. 11. It has been found readily possible in accordance with the teachings of this application to make a silicon-iron prodnct in which in excess of 90% of the surface area of the sheet stock is occupied by grains having the cubic texture, the grains nevertheless being comparatively small, which is favorable to core loss characteristics.
  • a grain size of 7 (ASTM) at 1x magnification or smaller can be produced especially if box annealing treatments are employed.
  • Example A coil of silicon-iron .014 inch in thickness, containing 3% silicon, and already having the (ll0) [001] orientation was selected.
  • This coil was pickled and cold reduced to .0038 inch and exhibited the orientation shown in FIG. 3.
  • the strip was then strand annealed in hydrogen for 2 minutes at 1600 It now had the (120) [001] texture shown in FIG. 5.
  • the material was then again cold rolled to a thickness of .0018 inch. Its orientation at this stage is shown in FIG. 7.
  • FIG. 10 is the X-ray pole figure of the product. The product tested as follows:
  • a process of producing silicon-iron for magnetic uses having high straight-grain and high cross-grain permeabilities which comprises providing a polycrystalline ferrous sheet stock containing substantially 2.5 to 4.0% silicon and having preponderantly a [001] crystal orientation by Millers indices, cold rolling said siliconiron with a reduction of substantially 55 to 90%, and subjecting said silicon-iron to a primary recrystallization in a heat treatment at about 1200 F. to 2200 F., then again cold rolling said silicon-iron with a reduction of substantially 50% to 80%, and heat treating the siliconiron at a temperature of 1900 to 2300 F. under conditions productive of secondary recrystallization whereby first to subject said silicon-iron to primary recrystallization, and thereafter to secondary recrystallization to convert said silicon-iron to a polycrystalline product having preponderantly a (100)[001] orientation.
  • a process of producing silicon-iron for magnetic uses having high straight-grain and high cross-grain permeabilities which comprises providing a polycrystalline silicon-iron containing substantially 2.5 to 4.0% silicon having preponderantly a ()[001] crystal orientation by Millers indices, cold rolling said siliconiron with a reduction of substantially 55 to 90%, whereby to convert it to a material having a (111) [112] orientation, subjecting said silicon-iron to a heat treatment at above the recrystallization temperature whereby to convert the orientation to [0011, again cold rolling said siliconiron with a reduction of substantially 50 to 80% to convert the last mentioned orientation to a derivative orientation in which the crystals are tilted in both transverse directions as respects the rolling direction, and subjecting said silicon-iron to a heat treatment at about 1900 to 2300 F. under conditions productive of sec- 7 ondary recrystallization; whereby I to effect a primary recrystallization followed by a secondary recrystallization.
  • a process of producing silicon-iron sheet stock for magnetic uses having high straight-grain and high crossgrain permeabilities which comprises hot rolling an ingot of silicon-iron containing substantially 2.5 to 4.0% silicon, converting it by at least one cold rolling treatment followed by a recrystallization to a (110) [001] orientation with a straight-grain permeability of at least about 1700 at a magnetizing force of oersteds, converting it by an additional cold rolling treatment with substantially 55 to 90% reduction and a primary recrystallizing heat treatment through a (111) [112] orientation to preponderantly a (120) [001] orientation, and converting it by a cold rolling reduction of substantially to 80% and a primary recrystallizing heat treatment through a derivative cold rolled orientation in which the (120) [001] crystals are tilted in both transverse directions as respects the rolling direction, .to an orientationin which the cube edges are generally aligned in the rolling direction but the cube faces are tilted away from the 110) position, the said tilt
  • a process of making cubic texture silicon-iron sheet stock containing substantially 2.5% to 4.0% silicon which comprises providing a silicon-iron sheet stock the grains of which are characterized by a (110) [001] orientation, cold rolling said stock with a reduction of substantially to 90% reduction, annealing said stock at a temperature of substantially 1200 to 2200 F., again cold rolling said stock with a reduction of substantially 50% to 80%, subjecting said stock to' a primary re crystallization at a temperature of substantially 1075 to 1900 F., and then to a secondary recrystallization at a temperature of substantially 1900 to 2300 F.'
  • a process of making cubic texture silicon-iron sheet stock containing substantially 2.5% to 4.0% silicon which comprises providing a silicon-iron sheet stock the grains of which are characterized by a (110) [001] orientation, cold rolling said stock with a reduction of substantially 75% to 87%, strip-annealing said stock at a temperature of substantially 1500 to 1700 F., again cold rolling said stock with a reduction of substantially to subjecting said stock to a primary recrystallization at a temperature of substantially 1400 to 1700" F., and to a secondary recrystallization at a temperature of substantially 190 to 2300 F.
  • a process of making cubic texture silicon-iron sheet stock containing substantially 2.5 to 4.0% silicon which comprises providing a silicon-iron sheet stock the grains of which are characterized by a (110) [001] orientation, cold rolling said stock with a reduction of substantially 60% to 85%, box annealing said stock at a temperature of substantially 1400 to 1600 F., again coldrrolling with a reduction of 70% to and then subjecting said stock to a primary recrystallization and a secondary recrystallization in a box anneal at a temperature of substantially 1900 to 2300 F.

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US816889A 1959-05-29 1959-05-29 Process of making cubic texture silicon-iron Expired - Lifetime US3130092A (en)

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Application Number Priority Date Filing Date Title
US816889A US3130092A (en) 1959-05-29 1959-05-29 Process of making cubic texture silicon-iron
BE584171A BE584171A (fr) 1959-05-29 1959-10-30 Procédé de préparation de ferro-silicium
FR809810A FR1240322A (fr) 1959-05-29 1959-11-10 Procédé de fabrication d'alliages fer-silicium à propriétés magnétiques améliorées
CH558260A CH413885A (de) 1959-05-29 1960-05-16 Verfahren zur Herstellung von Silicium-Eisen-Blech für magnetische Zwecke

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Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3212942A (en) * 1962-03-19 1965-10-19 Yawata Iron & Steel Co Process for producing double-oriented magnetic steel sheets
US3278348A (en) * 1965-01-28 1966-10-11 Westinghouse Electric Corp Process for producing doubly oriented cube-on-face magnetic sheet material
US3640780A (en) * 1970-06-25 1972-02-08 United States Steel Corp Method of producing electrical sheet steel with cube texture
EP0206108A2 (de) * 1985-06-26 1986-12-30 Nisshin Steel Co., Ltd. Verfahren zur Herstellung von Elektrostahlblechen
US5135818A (en) * 1989-03-28 1992-08-04 Hitachi Maxell, Ltd. Thin soft magnetic film and method of manufacturing the same
EP0743370A2 (de) * 1995-05-16 1996-11-20 Armco Inc. Kornorientierte Elektrobleche mit erhöhtem elektrischen Durchgangswiderstand und ein Verfahren zum Herstellen dieser Bleche
US20080115864A1 (en) * 2004-11-23 2008-05-22 Alison Behre Flatau Method of texturing polycrystalline iron/gallium alloys and compositions thereof

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2473156A (en) * 1944-11-16 1949-06-14 Armco Steel Corp Process for developing high magnetic permeability and low core loss in very thin silicon steel
DE1009214B (de) * 1954-03-27 1957-05-29 Ver Deutsche Metallwerke Ag Verfahren zur Erzeugung ausgepraegter Wuerfeltextur in magnetisierbaren Baendern undBlechen aus silizium- und/oder aluminiumhaltigen Eisenlegierungen
US2867558A (en) * 1956-12-31 1959-01-06 Gen Electric Method for producing grain-oriented silicon steel
US2992951A (en) * 1960-04-21 1961-07-18 Westinghouse Electric Corp Iron-silicon magnetic sheets
US2992952A (en) * 1955-12-01 1961-07-18 Vacuumschmelze Ag Method of manufacturing magnetic sheets

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2473156A (en) * 1944-11-16 1949-06-14 Armco Steel Corp Process for developing high magnetic permeability and low core loss in very thin silicon steel
DE1009214B (de) * 1954-03-27 1957-05-29 Ver Deutsche Metallwerke Ag Verfahren zur Erzeugung ausgepraegter Wuerfeltextur in magnetisierbaren Baendern undBlechen aus silizium- und/oder aluminiumhaltigen Eisenlegierungen
US2992952A (en) * 1955-12-01 1961-07-18 Vacuumschmelze Ag Method of manufacturing magnetic sheets
US2867558A (en) * 1956-12-31 1959-01-06 Gen Electric Method for producing grain-oriented silicon steel
US2992951A (en) * 1960-04-21 1961-07-18 Westinghouse Electric Corp Iron-silicon magnetic sheets

Cited By (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3212942A (en) * 1962-03-19 1965-10-19 Yawata Iron & Steel Co Process for producing double-oriented magnetic steel sheets
US3278348A (en) * 1965-01-28 1966-10-11 Westinghouse Electric Corp Process for producing doubly oriented cube-on-face magnetic sheet material
US3640780A (en) * 1970-06-25 1972-02-08 United States Steel Corp Method of producing electrical sheet steel with cube texture
EP0206108A2 (de) * 1985-06-26 1986-12-30 Nisshin Steel Co., Ltd. Verfahren zur Herstellung von Elektrostahlblechen
EP0206108A3 (en) * 1985-06-26 1988-12-28 Nisshin Steel Co., Ltd. Process for producing electrical steel sheet
US5135818A (en) * 1989-03-28 1992-08-04 Hitachi Maxell, Ltd. Thin soft magnetic film and method of manufacturing the same
EP0743370A2 (de) * 1995-05-16 1996-11-20 Armco Inc. Kornorientierte Elektrobleche mit erhöhtem elektrischen Durchgangswiderstand und ein Verfahren zum Herstellen dieser Bleche
EP0743370A3 (de) * 1995-05-16 1998-04-01 Armco Inc. Kornorientierte Elektrobleche mit erhöhtem elektrischen Durchgangswiderstand und ein Verfahren zum Herstellen dieser Bleche
US20080115864A1 (en) * 2004-11-23 2008-05-22 Alison Behre Flatau Method of texturing polycrystalline iron/gallium alloys and compositions thereof
US8591669B2 (en) 2004-11-23 2013-11-26 University Of Maryland Method of texturing polycrystalline iron/gallium alloys and compositions thereof

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BE584171A (fr) 1960-02-15
FR1240322A (fr) 1960-09-02

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