US3069299A - Process for producing magnetic material - Google Patents

Process for producing magnetic material Download PDF

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Publication number
US3069299A
US3069299A US840290A US84029059A US3069299A US 3069299 A US3069299 A US 3069299A US 840290 A US840290 A US 840290A US 84029059 A US84029059 A US 84029059A US 3069299 A US3069299 A US 3069299A
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percent
sheet
strip
iron
texture
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US840290A
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Howard C Fiedler
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General Electric Co
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General Electric Co
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Publication date
Priority to BE563542D priority Critical patent/BE563542A/xx
Priority to BE571059D priority patent/BE571059A/xx
Priority to GB39883/57A priority patent/GB832438A/en
Priority to FR1197045D priority patent/FR1197045A/fr
Priority to DEG23613A priority patent/DE1159978B/de
Priority to GB27326/58A priority patent/GB845167A/en
Priority to FR1213741D priority patent/FR1213741A/fr
Priority to DEG25589A priority patent/DE1176164B/de
Application filed by General Electric Co filed Critical General Electric Co
Priority to US840290A priority patent/US3069299A/en
Priority to GB27546/60A priority patent/GB919206A/en
Priority to DEG30439A priority patent/DE1181255B/de
Priority to BE595029A priority patent/BE595029R/fr
Priority to FR838547A priority patent/FR1270837A/fr
Application granted granted Critical
Publication of US3069299A publication Critical patent/US3069299A/en
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B21B3/02—Rolling special iron alloys, e.g. stainless steel
    • 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
    • C21D8/1205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular fabrication or treatment of ingot or slab
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/84—Controlled slow cooling
    • 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
    • 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
    • C21D8/1222—Hot rolling
    • 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
    • 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
    • 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
    • C21D8/1255—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 with diffusion of elements, e.g. decarburising, nitriding

Definitions

  • This invention relates to the fabrication of polycrystalline, magnetically soft, rolled sheet metal composed principally of an alloy of iron and silicon having a high percentage of the grains comprising the material oriented such that their crystal space lattices are arranged in a substantially identical relationship to the plane of the sheet and to a single direction in the plane of the sheet, and more particularly to an improved process for forming sheet material having this desired orientation.
  • the sheet materials to which this invention is directed are usually referred to in the art as electrical silicon steels or, more properly, silicon-iron, and are conventionally composed principally of iron alloyed with about 2.5 to 4.0 percent, preferably 2.5 to 3.5 percent silicon and relatively minor amounts of various impurities, such as sulfur, manganese, phosphorous and a very low carbon content as finished material.
  • Such alloy-s crystallize in the body-centered cubic crystallographic system at room temperature. As is well known, this refers to the symmetrical distribution or arrangement which the atoms forming the individual crystals or grains assume in such materials. In these materials, the smallest prism possessing the full symmetry of the crystal is termed the unit cell and is cubic in form. This unit cube is composed of nine atoms, each arranged at the corners of the unit.
  • Each unit cell in a given grain or crystal in these materials is substantially identical in shape and orientation with every other unit cell comprising the grain.
  • the unit cells which are body-centered unit cubes comprising these materials each have a high degree of magnetic anisotropy with respect to the crystallographic planes and directions of the unit cube, and hence, each grain or crystal comprising a plurality of such unit cells exhibits a similar magnetic anisotropy.
  • crystals of the silicon-iron alloys to which this invention is directed are known to have their direction of easiest magnetization parallel to the unit cube edges, their next easiest direction of magnetization perpendicular to a plane passed through diagonally-opposite parallel unit cube edges and their least easiest direction of magnetization perpendicular to a plane passed through a pair of diagonally-opposite atoms in a first unit cube face, the central atom and a single atom at the unit face which is parallel to the first face.
  • these crystallographic planes and directions are conventionally identified in terms of Miller indices, a more complete description of which may be found in Structure of Metals, C. S.
  • silicon-iron alloys may be fabricated by unidirectional rolling and heat treatment to form sheet or strip material composed of a plurality of crystals or grains, a majority of which have their atoms arranged so that their crystallographic planes have a similar or substantially identical orientation to the plane of the sheet or strip in a single direction in said plane.
  • This material is usually referred to as Oriented or grain-oriented silicon-iron sheet or strip and is characterized by having 50 percent or more of its component grains oriented so that four of the cube edges of the unit cells of said grains are substantially parallel to the plane of the sheet or the strip and to the direction in which it was rolled and a (110) crystallographic plane substantially parallel to the sheet.
  • these so-oriented grains have a direction of easiest magnetization in the plane of the sheet in the rolling direction and the next easiest direction of magnetization in the plane of the sheet in the transverse rolling direction. This is conventionally referred to as a cube-on-edge orientation or the (110) [001] texture.
  • these materials are prepared by casting large, thick section ingots weighing up to about 4 tons each'from alloys containing from about 2.5 to 4.0 percent by weight silicon, less than 0.035 percent carbon, less than 0.05 percent sulfur, and less than 0.15 percent manganese.
  • thick section it will be understood that such ingots usually have a minimum transverse crosssectional dimension of about two feet.
  • Such ingots are conventionally hot-worked into a strip or sheet-like configuration, usually less than 150 mils in thickness, commonly referred to as hot-rolled band.
  • This band material is usually in an incompletely recrystallized form and may be annealed to effect complete recrystallization, if desired, but this is usually not done in conventional commercial practice.
  • the hot-rolled band is then cold-rolled with appropriate intermediate heat treatment to the finished sheet or strip thickness, usually involving at least a 40 percent 7 reduction in thickness, and given a final or texture producing annealing treatment accompanied by a decarburizing treatment.
  • FIG. 1 is a graph showing the percent cube-on-edge crystal orientation developed from silicon-iron cast in graphite and sand molds, as a function of the final annealing temperature
  • FIG. 2 is a graph similar to that of FIG. 1 in which silicon-iron bodies cooled at rates of 50 C. and C. were used.
  • the present invention is predicated upon the discovery that there is a previously unsuspected relationship between the rate of cooling of a silicon-iron alloy ingot containing selected amounts of manganese and sulfur from temperatures at which the manganese and sulfur are in solution, for example, 1300 to 1400 C. or higher and the degree of oriented crystal texture which can be ultimately developed.
  • a silicon-iron alloy ingot containing selected amounts of manganese and sulfur from temperatures at which the manganese and sulfur are in solution, for example, 1300 to 1400 C. or higher and the degree of oriented crystal texture which can be ultimately developed.
  • the metal can either be cooled directly from the liquid condition, as when originally poured into an ingot mold, or can be cooled from a temperature in excess of that at which the manganese and sulfur are normally in solution, this latter temperature normally being on the order of 1300-1400 C. If the silicon-iron is cooled either from or above these temperatures at a sufiicient rate, the manganese sulfide dispersion is properly distributed throughout the ingot and no further treatment need be carried out. This material is perfectly acceptable for subsequent rolling to produce a cube-ou-edge crystal orientation. Of course, if the ingot is so large as to make it difficult to attain the required cooling rate, then it can be rolled rapidly to reduce the cross-section and thereby increase the cooling rate. It has been found that if the material is cooled at a rate of 50 C. per minute or faster, preferably on the order of about 130 C. per minute, then a fine manganese sulfide dispersion is obtained.
  • the ingot molds were 2% inches by 5 inches in crosssection and one-inch thick slabs were cut from the ingots, heated to 1000 C., rolled without reheating to 80 mil band, pickled, sand-blasted and heat-treated in the band stage for 5 minutes at 900 C.
  • the band material was then cold-rolled to 25 mils in thickness, heat-treated at 860 C. for 1 to 5 minutes and cold-rolled to 12 to 13 mils.
  • the material which was cast in sand and processed to final gauge had a grain size of about 0.038 millimeter when heated for minutes at 950 C.
  • the material which had been cast in graphite and processed to final gauge had a grain size of about 0.030.
  • To ascertain the cooling rates of the metals cast in graphite and sand molds separate one-inch test slabs were heated to above the solution temperature for the manganese and the sulfur (l3001400 C.) and then cooled at rates of 50 C. per minute and 130 C.
  • the curve 15 represents strip from that body which was cooled at a rate of 130 C. per minute
  • the numeral 16 indicates strip from that material which was cooled at about 50 C. per minute.
  • the textures obtained from the material cooled at 50 C. per minute correspond substantially with that indicated by curve 10 in FIG. 1.
  • the maximum texture obtained was on the order of 80 percent and the texture obtained dropped off rapidly as higher final annealing temperatures were used. This feature of decreasing orientation with increasing annealing temperatures is an important one since it permits the use of only comparatively low heating rates in the texturedeveloping anneal.
  • the percent cube-on-edge texture developed is shown in Table I as a function of the heating rate during the final anneal.
  • manganese is used for this purpose, forming manganese sulfide; however, titanium may equally well be used, forming titanium sulfide. Obviously, manganese and titanium may be used or, in fact, other addition elements known to form stable sulfides may also be used.
  • All of the representative heats weighed 50 pounds and were made in an induction furnace with magnesia cruc1- bles.
  • the alloys were poured at temperatures between 16001650 C. into various sized molds made of different materials.
  • heats 1, 4 and 5 were cast into cast iron molds having a regular mold cavity having a rectangular transverse cross-section with a minimum transverse width of 3%" and a minimum thickness of 1%" and a length of 18".
  • Heats 2 and 3 were cast into graphite molds having a rectangular transverse crosssection with a minimum of transverse width of 6%.”, a minimum thickness of 3 A and a length of 9".
  • Heats 6 and 7 were cast into cast iron molds having a regular mold cavity having a square transverse cross-section with a minimum transverse width and thickness of 3% and a length of 14".
  • the ingots having the 1%" thickness will cool substantially faster than the ingots of 3%" thickness.
  • the ingots were cast into the molds, permitted to cool, removed from the molds and subjected to the following fabrication procedure.
  • Ingots from heats 1, 4 and 5 were machined to form 1%" thick by 3%" wide slabs, heated to 1000 C. 1n a dry hydrogen (dewpoint about 60 F.) atmosphere and hot-rolled to 80 mil thick hand. These hot-rolled bands were then annealed at 900 C. for /2 hour at that ternperature in an atmosphere of dry hydrogen. It should be noted that any conventional protective atmosphere or a vacuum may be used in place of hydrogen at this point. After cooling, the annealed bands were cold-rolled to mil thickness strip. These strips were then subjected to an intermediate anneal in a dry hydrogen atmosphere at about 860 C. Again, other protective atmospheres or vacuum may be used. The strips were in the heated zone for about 3%. minutes and at the 860 C.
  • annealed strips were then cold-rolled to 12 mil thick strip and decarburized by heating for 5 minutes .at 800 C. in wet hydrogen.
  • the decarburized strips were then placed in'a metal retort in a furnace and dry hydrogen (90 dew point) was flowed through the retort as temperature was increased at a rate of 100 C. per hour to 1200 0, held at that temperature for 8 hours and cooled at about 100 C. per hour to 600 C., then furnace-cooled to about 300 C., at which point the retort was removed from the furnace.
  • the ingots from heats 2 and 3 were processed as follows: A slice of about 1" thick by 6%" wide by 9 long was cut from each ingot, the resulting slabs heated to 1000 C. and hot-rolled to mil thick hot-rolled bands. The bands were annealed in the same manner as the bands from heats 1, 4 and 5 and cold-rolled to 25 mil thick strip. One portion of the strip from heat 2 was then annealed in dry hydrogen under the same conditions set forth for the intermediate anneal given strips from heats 1, 4 and S and another portion from heat 2 and all of strip from heat 3 were annealed under the same conditions except the temperature was raised to 950 C. The intermediate grain size of the 860 C.
  • anneal strip from heat 2 had an average measured grain size of 0.007 millimeter, while the 950 C. annealed portion of this same material had a grain size of 0.021 millimeter.
  • the intermediate grain size of the strip from heat 3 was 0.025 millimeter. Both strips from heat 2 and the strip from heat 3 were then cold-reduced to 12 mils thickness and given the decarburization and final annealing treatment given the strips from heats 1, 4 and 5.
  • the ingots from heats 6 and 7 were heated to 1000 C. in dry hydrogen and forged .to a rectangular transverse cross-section of 1%" by 4". A portion of each forged bar was then reheated to 1.000 C. in dry hydrogen and rolled to 80 mil thicknesshot-rolled hand. These bands were annealed as set forth previously and cold-reduced to 25 mil intermediate thickness strip and heated in the same manner in similar strips from ingots l, 4 and 5 at 860 C. The intermediate grain size from the strip from heat 6 was found to be 0.027 millimeter and from the strip from heat 7 to be 0.016 millimeter.
  • the cooling rate of the as-cast structure through the temperature range where the sulfide first precipitates and through the temperature range immediately below that temperature range where growth of these particles may occur is critical to the degree of preferred grain orientation which may be achieved in the final strip material.
  • a process for forming a fine dispersion of sulfide inclusions in silicon-iron castings which are adapted to be formed into sheet-like bodies having a majority of their constituent grains oriented in the (110) [001] texture comprising cooling said casting from a temperature at which the sulfides are in solution to about 1000 C. at a rate of at least 130 C. per minute, reducing said casting by rolling to form a sheet-like body, and annealing said sheet-like body to develop said grain orientation therein.
  • a process for the fabrication of sheet-like bodies of polycrystalline silicon-iron alloy having a majority of their constituent grains oriented in the (110) [001] texture comprising the steps of casting an alloy consisting essentially of from about 2.5 to 4.0 percent silicon, less than about 0.04 percent carbon, from about 0.010 to 0.05 percent sulfur and the remainder substantially all iron, said sulfur being present as sulfide inclusions in the form of a fine dispersion in said casting at temperatures below about 1300 C., cooling the casting at a rate of at least 130 C. per minute from a temperature 8 at which the sulfides are in solution to about 1000" C., producing a metal sheet from said casting, and annealing said metal sheet to refine the same and to develop grain orientation therein.
  • a process for the fabrication of sheet-like bodies of polycrystalline silicon-iron alloy having more than a majority of their constituent grains oriented in the [001] texture comprising the steps of melting an alloy consisting essentially of from about 2.5 to 4.0 percent silicon, less than 0.035 percent carbon, from about 0.015 to 0.05 percent sulfur, and the remainder substantially all iron, casting said alloy into a mold to produce a slab-like ingot, said sulfur being present as sulfide inclusions in the form of a fine dispersion in said castings at temperatures below about 1400 C., cooling said ingot at a rate of at least C.
  • a process as defined in claim 3 in which said hotreduced elongated sheet-like body is cold-rolled to effect at least a 40 percent reduction in thickness, heated in a protective atmosphere to cause the cold-Worked metal to recrystallize, and cold-rolled to eifect at least a 40 percent reduction in thickness prior to the decarburization and texture-development heat treatments.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
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  • Manufacturing & Machinery (AREA)
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  • Crystallography & Structural Chemistry (AREA)
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US840290A 1956-12-31 1959-09-16 Process for producing magnetic material Expired - Lifetime US3069299A (en)

Priority Applications (13)

Application Number Priority Date Filing Date Title
BE563542D BE563542A (de) 1956-12-31
BE571059D BE571059A (de) 1956-12-31
GB39883/57A GB832438A (en) 1956-12-31 1957-12-23 Process for producing silicon-iron alloy sheets
FR1197045D FR1197045A (fr) 1956-12-31 1957-12-23 Perfectionnements aux tôles magnétiques de ferro-silicium
DEG23613A DE1159978B (de) 1956-12-31 1957-12-24 Verfahren zur Herstellung von Blechen oder Platten aus einer Eisen-Silicium-Legierung mit kristallographisch orientiertem Gefuege
GB27326/58A GB845167A (en) 1956-12-31 1958-08-26 Improvements in magnetic material
FR1213741D FR1213741A (fr) 1956-12-31 1958-10-23 Perfectionnements aux tôles ferromagnétiques
DEG25589A DE1176164B (de) 1956-12-31 1958-10-28 Verfahren zur Herstellung von Blechen und Platten aus einer Eisen-Silicium-Legierung mit (110)[001]-Orientierung der Kristallite
US840290A US3069299A (en) 1956-12-31 1959-09-16 Process for producing magnetic material
GB27546/60A GB919206A (en) 1956-12-31 1960-08-09 Improvements in process for producing magnetic material
DEG30439A DE1181255B (de) 1956-12-31 1960-09-06 Verfahren zum Herstellen von Blechen oder Platten aus einer Eisen-Silicium-Legierungmit kristallographisch orientiertem Gefuege
BE595029A BE595029R (fr) 1959-09-16 1960-09-14 Matériau magnétique.
FR838547A FR1270837A (fr) 1956-12-31 1960-09-14 Procédé de fabrication de matériau magnétique

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
US832438XA 1956-12-31 1956-12-31
US845167XA 1957-10-29 1957-10-29
US840290A US3069299A (en) 1956-12-31 1959-09-16 Process for producing magnetic material

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BE (2) BE563542A (de)
DE (3) DE1159978B (de)
FR (2) FR1197045A (de)
GB (3) GB832438A (de)

Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3147158A (en) * 1961-11-22 1964-09-01 Gen Electric Process for producing cube-on-edge oriented silicon iron
US3151005A (en) * 1959-07-09 1964-09-29 United States Steel Corp Method of producing grain-oriented electrical steel
US3632456A (en) * 1968-04-27 1972-01-04 Nippon Steel Corp Method for producing an electromagnetic steel sheet of a thin sheet thickness having a high-magnetic induction
US3636579A (en) * 1968-04-24 1972-01-25 Nippon Steel Corp Process for heat-treating electromagnetic steel sheets having a high magnetic induction
JPS501915A (de) * 1973-05-09 1975-01-10
US3872704A (en) * 1971-12-24 1975-03-25 Nippon Steel Corp Method for manufacturing grain-oriented electrical steel sheet and strip in combination with continuous casting
JPS5018445B1 (de) * 1970-03-30 1975-06-28

Families Citing this family (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3438820A (en) * 1965-04-02 1969-04-15 Dominion Foundries & Steel Silicon steel process
JPS5168422A (en) * 1974-12-11 1976-06-14 Nippon Steel Corp Kyojinkono seizoho

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2534141A (en) * 1948-01-14 1950-12-12 Gen Electric Heat-treatment of cold rolled silicon steel strip
US2618843A (en) * 1949-11-21 1952-11-25 United States Steel Corp Preventing cracking of silicon steel during hot rolling
US2867558A (en) * 1956-12-31 1959-01-06 Gen Electric Method for producing grain-oriented silicon steel

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2534141A (en) * 1948-01-14 1950-12-12 Gen Electric Heat-treatment of cold rolled silicon steel strip
US2618843A (en) * 1949-11-21 1952-11-25 United States Steel Corp Preventing cracking of silicon steel during hot rolling
US2867558A (en) * 1956-12-31 1959-01-06 Gen Electric Method for producing grain-oriented silicon steel

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3151005A (en) * 1959-07-09 1964-09-29 United States Steel Corp Method of producing grain-oriented electrical steel
US3147158A (en) * 1961-11-22 1964-09-01 Gen Electric Process for producing cube-on-edge oriented silicon iron
US3636579A (en) * 1968-04-24 1972-01-25 Nippon Steel Corp Process for heat-treating electromagnetic steel sheets having a high magnetic induction
US3632456A (en) * 1968-04-27 1972-01-04 Nippon Steel Corp Method for producing an electromagnetic steel sheet of a thin sheet thickness having a high-magnetic induction
JPS5018445B1 (de) * 1970-03-30 1975-06-28
US3872704A (en) * 1971-12-24 1975-03-25 Nippon Steel Corp Method for manufacturing grain-oriented electrical steel sheet and strip in combination with continuous casting
JPS501915A (de) * 1973-05-09 1975-01-10
JPS5339852B2 (de) * 1973-05-09 1978-10-24

Also Published As

Publication number Publication date
BE571059A (de)
GB919206A (en) 1963-02-20
BE563542A (de)
GB832438A (en) 1960-04-13
FR1213741A (fr) 1960-04-04
DE1176164B (de) 1964-08-20
DE1159978B (de) 1963-12-27
FR1197045A (fr) 1959-11-27
GB845167A (en) 1960-08-17
DE1181255B (de) 1964-11-12

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