US3764406A - Hot working method of producing cubeon edge oriented silicon iron from cast slabs - Google Patents

Hot working method of producing cubeon edge oriented silicon iron from cast slabs Download PDF

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Publication number
US3764406A
US3764406A US00195553A US3764406DA US3764406A US 3764406 A US3764406 A US 3764406A US 00195553 A US00195553 A US 00195553A US 3764406D A US3764406D A US 3764406DA US 3764406 A US3764406 A US 3764406A
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Prior art keywords
hot
slabs
slab
cast
thickness
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US00195553A
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M Littmann
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Armco Advanced Materials Corp
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Armco Inc
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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
    • 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
    • C21D8/1205—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

Definitions

  • a process for the production of cube-on-edge siliconiron sheet stock having uniformly good magnetic properties comprising melting, refining, casting into slabs, hot reducing to hot rolled thin band, removing the hot mill scale, cold reducing to final thickness in one or more stages, decarburizing and recrystallizing in a wet hydrogen anneal, coating with a separator and annealing in hydrogen above about 1100 C.
  • the cast slabs are initially hot reduced at least at a temperature of 750 to 1250 C., then heated above 1350 C. and hot rolled to a thickness of 2.5 mm. or less.
  • the initial hot reduction produces a structure which prevents excessive grain growth during the subsequent heating and hot rolling steps.
  • This invention relates to a method of producing oriented silicon-iron sheet or strip for magnetic purposes.
  • the orientation with which the present invention is concerned is that wherein the grains or crystals are oriented in the cube-on-edge position, i.e. designated (l l0)[00l] in accordance with the Miller Indices.
  • the invention relates to a method of producing grain-oriented silicon-iron sheet or strip containing from about 2% to 4% silicon of uniformly excellent magnetic properties.
  • the invention has particular utility in the production of grain-oriented silicon-iron sheet or strip wherein the molten steel is strand or continuously cast into a continuous slab of thickness suitable for direct hot rolling.
  • Cube-on-edge oriented silicon-iron sheet or strip is generally made by a series of steps including melting, refining, casting and hot reducing ingots or slabs to hot rolled bands of about 2.5 mm. thickness or less. After annealing and scale removal, the hot rolled band is cold reduced in one or more stages, with intermediate anneals if necessary, to a final thickness of about 0.25 to about 0.35 mm. The strip is then usually recrystallized and decarburized at final thickness by a continuous anneal in a wet hydrogen atmosphere. Finally, the strip is coated with an annealing separator and box annealed for several hours in dry hydrogen at a temperature above about 1100 C.
  • the cube-on-edge grains consume other grains in the matrix having a different orientation.
  • the primary grain growth inhibitor which must be present in the form of small, uniformly distributed inclusions, is usually manganese sulfide, but other inhibitors, e.g., manganese selenide, aluminium nitride, or mixtures thereof, may also be used for this purpose.
  • U.S. Pat. 2,599,340 issued June 3, 1952, to M. F. Littmann and J. E. Heck, discloses a process for the production of cube-on-edge silicon-iron wherein slabs rolled from ingots are heated to a temperature above about 1260 C., and particularly from about 1350 to about 1400 C. prior to hot rolling. This heating step not only prepares the metal for hot rolling but also dissolves the inhibitor present therein so that upon subsequent hot rolling the inhibitor is precipitated in the desired form of small, uniformly distributed inclusions, thereby satisfying one of the two essential conditions for obtaining highly oriented cube-on-edge material.
  • slab casting into a continuous slab or casting into individual slabs of a thickness suitable for direct hot rolling is now being used for making ferrous sheet stock.
  • the term slab as used herein is intended to include cast bodies ranging in thickness from about 10 to about 30 cm. These casting techniques are advantageous in that they avoid the loss of material from the butt and top portions of conventional ingots, which ordinarily must be cropped.
  • slabs of silicon-iron are strand cast into a thickness of 15 cm., cut to suitable length and reheated to about 1350 to 1400 C. in order to dis solve the inhibitor prior to hot rolling.
  • the degree of the cube-on-edge orientation of the product of strand cast slabs has tended to be much more variable than material produced from ingots, especially across the width of the strip.
  • the present invention it has been found that limiting the grain size in the slabs, after reheatin to high temperature and prior to hot rolling, to a diameter not exceeding that represented by about 4.5 ASTM at 1 (corresponding to an average diameter of about 7 mm. or less) has a beneficial elfect on the development of cube-on-edge texture in the final product. Apparently the smaller grain size promotes more complete recrystallization during the processing anneals subsequent to hot rolling.
  • control of the grain size in the slabs after the high temperature reheating can be achieved by hot reducing (prerolling) the cast slab by at least about 5%, before reheating, at a temperature below that at which excessive grain growth occurs.
  • excessive grain growth in the slab may begin between about 1260 and 1350 C.
  • this initial hot 3 4 reduction is carried out within the range of about 750 Percent to 1250 C., and preferably between about 850 and Carbon 0.034 1150 C.
  • Manganese 0.062 The initial hot rolling step of the present invention re- Sulfur 0.0 24 sults in a marked reduction in the size of the grains in 5 Silicon 3.17 the slab after reheating to about 1400 C.
  • a hot reduc- Balance substantially iron.
  • tion of about 25% results in a grain size after reheating of about 5 mm. average diameter (i.e. about 5-6 ASTM grain size at 1x). At least about 5% initial hot reduction is required. Reductions between about and about 10 50% are preferred.
  • Example 1 For purposes of comparison, part of the heat of Example 1 was subjected to subsequent processing in accordance with the present invention and part in accordance with conventional practice. That portion processed in accordance with the present invention was strand cast to cm. thickness, while that portion processed in accordance with conventional practice was strand cast to 15 cm. thickness.
  • the two processes are summarized below in tabular form and designated as A and B respectively.
  • FIG. 1 15 a photograph at (b X magmfi l n of a ness (2 stages with interthickness (2 stages Witt: transverse section of a 15- cm. thlckness strand cast slab medlate anneal 925 lltermedlate annealat 925 in the as cast condition; 8..- Dggggbgrgze-strip altereal at 6... Dggggbgrize-strip glnneal at FIG 2 1s photograph at O'SX magmficanon of a 9... Box anneal at 1,200 O. for 24 7.-. Box anneal at 1,200 Cf ior 24 transverse section of the strand cast slab of FIG. 1 after hours in dry hydrogen. hours in dry hydrogen. reheating to about 1400 C.;
  • FIG. 3 is a photograph at 0.5x magnification of a Example 2 transverse section of a 20 cm. thickness strand cast slab A h t M d fi d d h of the same heat as FIG. 1 in the as-cast condition; ea was me e re me an cast t e
  • FIG 4 is a photograph at 05X magnification of a ner as that of Example 1, having the following composilongitudinal section of the slab of FIG. 3 after being hot reduced 25% in thickness at 1035 C., in accordance with Percent the invention; and g 0'030
  • FIG. 5 is a photograph at 0.5x magnification of a 0'057 transverse section of the initially hot rolled slab of FIG. 4 q. ur 0024 after reheating to about 1400 C. S1 Icon 7".
  • a Charge is melted in COIlVeH-
  • the magnetic properties of the final products of the tlonal manner in an open hearth, electric arc furnace, or heats of Examples 1 and 2 produced by both processes A basic oxygen furnace, and tapped into a ladel to Which and B are compared in Table I.
  • the permeability of material produced by Example 1 process A ranges between 1820 and 1840 with an average above 1830, as compared to permeability ranges of from A heat Was Processed 111 the above descrlbed manner 1745 to 1840 and an average of about 1804 for material and strand cast into slabs having the following composiproduced from strand cast slabs in accordance with proction: ess B.
  • Example 3 A heat was melted, refined and cast, in the same manner as that of Example 1, except that all the slabs were strand cast to 20 cm. thickness.
  • the composition of the range of about cm. to about 30 cm. thickness has little or no effect on the response to the initial low temperature hot reduction, so long as this initial reduction in thickness is at least about 5%.
  • FIGS. 1-5 are photographs of etched sections of strand ignated as C and D respectively.
  • cast slabs of Example 2 produced both by process A and process B.
  • C D Referring to FIG. 1, which is a transverse section at Process of present invention Conventional process 0'5X magnification of a Slab cast to 15 thickness, it
  • FIG. 2 illustrates the elfect of reheating 4 Reheat to 1,400 0..- 2 Reheat t01,400 C. k a 25 the slab of FIG. 1 to 1400 C., in accordance with con- 33 gigf gggg ggggs 3 5??? i: ventional practice.
  • FIG. 3 1s a transverse ection at ()5 X ific tion hmrs dry hydrogen dry hydmgen of a slab (of Example 2) cast to 20 cm. thickness. It will be noted that the structure is substantially identical to Example 4 that of FIG. 1.
  • FIG. 5 is a transverse section at 0.5x magnification The magnetic properties of the final products of the of the initially hot rolled slab of FIG. 4 after reheating heats of Examples 3 and 4 produced by both processes to 1400 C.
  • Core loss 5 Core loss a. 24 .ss5. 740 .707 24 .705-. 870 .777 4- l6 665-. 735 .712 24 675-. 805 .736
  • the preferred range of initial hot reduction is from 10% to 50%.
  • a 25% initial reduction was found to develop optimum grain refinement in the reheated slab. Reductions below 5% do not introduce sufficient energy to be beneficial. As percent reduction increases over 25%, the benefit as measured by grain size of the reheated slab gradually diminishes to the extent that about 50% reduction may be considered the practical upper limit of this invention.
  • the preferred temperature range for the initial hot reduction is from 850 to 1150 C., as contrasted with the usual soaking pit temperature of 1230 C. for ingots which are rolled into slabs, which constitutes a reduction in excess of 70%.
  • Continuous casting installations are in operation which incorporate in-line hot reduction capability.
  • the residual heat of the cast slab may be sufiicient to permit initial hot reductions within the ranges of the present invention. This could minimize or eliminate reheating of slabs for initial hot rolling.
  • composition not dependent on composition, and may be realized with any inhibitor, e.g., manganese sulfide, manganese selenide, aluminum nitride, or mixtures thereof.
  • any inhibitor e.g., manganese sulfide, manganese selenide, aluminum nitride, or mixtures thereof.
  • heats may be processed to obtain uniform magnetic properties by selecting appropriate combinations of elements within the following ranges:
  • a process for the production of cube-on-edge texture silicon-iron sheet stock containing from about 2% to about 4% silicon comprising the steps of melting a charge of silicon-iron, casting the charge to produce a slab having a thickness of about to about 30 centimeters, heating the slab to a temperature of at least about 750 C. but below about 1250 C., initially hot reducing the slab with a reduction in thickness of 5% to re heating the slab to a temperature between about 1260 and 1400 C.
  • said cold reducing step comprises cold rolling in at least two stages with an intermediate strip anneal between each stage.
  • a process for theproduction of cube-on-edge texture silicon-iron sheet stock containing from about 2% to about 4% silicon comprising the steps of melting a charge of silicon-iron, continuously casting the charge to produce a slab having a thickness of about 10 to about 30 centimeters, initially hot reducing the slab with a reduction in thickness of 5% to 50% while said slab retains the residual heat of the casting step at a temperature of at least about 750 C. but below about 1250 C., reheating the slab to a temperature between about l260 and 1400 C.
US00195553A 1971-11-04 1971-11-04 Hot working method of producing cubeon edge oriented silicon iron from cast slabs Expired - Lifetime US3764406A (en)

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JP (1) JPS5427820B2 (ru)
AU (1) AU466217B2 (ru)
BE (1) BE790798A (ru)
BR (1) BR7207657D0 (ru)
CA (1) CA978067A (ru)
CS (1) CS213306B2 (ru)
DE (1) DE2252784C3 (ru)
ES (1) ES408258A1 (ru)
FR (1) FR2158458B1 (ru)
GB (1) GB1403271A (ru)
IT (1) IT966868B (ru)
RO (1) RO62344A (ru)
SE (1) SE394692B (ru)
SU (1) SU692570A3 (ru)
ZA (1) ZA727467B (ru)

Cited By (40)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3855019A (en) * 1973-05-07 1974-12-17 Allegheny Ludlum Ind Inc Processing for high permeability silicon steel comprising copper
US3855018A (en) * 1972-09-28 1974-12-17 Allegheny Ludlum Ind Inc Method for producing grain oriented silicon steel comprising copper
US3855020A (en) * 1973-05-07 1974-12-17 Allegheny Ludlum Ind Inc Processing for high permeability silicon steel comprising copper
US3873381A (en) * 1973-03-01 1975-03-25 Armco Steel Corp High permeability cube-on-edge oriented silicon steel and method of making it
US3895974A (en) * 1972-10-11 1975-07-22 Nippon Steel Corp Process for producing a grain-oriented electrical steel sheet having excellent magnetic characteristic
US3925115A (en) * 1974-11-18 1975-12-09 Allegheny Ludlum Ind Inc Process employing cooling in a static atmosphere for high permeability silicon steel comprising copper
US3929522A (en) * 1974-11-18 1975-12-30 Allegheny Ludlum Ind Inc Process involving cooling in a static atmosphere for high permeability silicon steel comprising copper
US3932236A (en) * 1973-01-22 1976-01-13 Nippon Steel Corporation Method for producing a super low watt loss grain oriented electrical steel sheet
US3933537A (en) * 1972-11-28 1976-01-20 Kawasaki Steel Corporation Method for producing electrical steel sheets having a very high magnetic induction
US3948691A (en) * 1970-09-26 1976-04-06 Nippon Steel Corporation Method for manufacturing cold rolled, non-directional electrical steel sheets and strips having a high magnetic flux density
US3969162A (en) * 1972-03-30 1976-07-13 Henke Robert H Method of producing silicon steel strip
US3971678A (en) * 1972-05-31 1976-07-27 Stahlwerke Peine-Salzgitter Aktiengesellschaft Method of making cold-rolled sheet for electrical purposes
US3986902A (en) * 1974-05-22 1976-10-19 United States Steel Corporation Silicon steel suitable for production of oriented silicon steel using low slab reheat temperature
US3988177A (en) * 1973-11-05 1976-10-26 Vereinigte Osterreichische Eisen- Und Stahlwerke-Alpine Montan Aktiengesellschaft Method of producing cold rolled, silicon-alloyed electric sheets
US4006044A (en) * 1971-05-20 1977-02-01 Nippon Steel Corporation Steel slab containing silicon for use in electrical sheet and strip manufactured by continuous casting and method for manufacturing thereof
US4066479A (en) * 1972-07-08 1978-01-03 Nippon Steel Corporation Process for producing non-directional electric steel sheets free from ridging
FR2359902A1 (fr) * 1976-07-27 1978-02-24 Nippon Steel Corp Procede de production de tole d'acier electrique non directionnel denue de nervures
US4088513A (en) * 1976-04-03 1978-05-09 Nippon Steel Corporation Method for heating a silicon-containing steel slab in a walking-beam type heating furnace
US4118255A (en) * 1975-08-01 1978-10-03 Centro Sperimentale Metallurgico S.P.A Process for the production of a silicon steel strip with high magnetic characteristics
US4168189A (en) * 1977-05-20 1979-09-18 Armco Inc. Process of producing an electrically insulative film
US4202711A (en) * 1978-10-18 1980-05-13 Armco, Incl. Process for producing oriented silicon iron from strand cast slabs
US4204891A (en) * 1978-11-27 1980-05-27 Nippon Steel Corporation Method for preventing the edge crack in a grain oriented silicon steel sheet produced from a continuously cast steel slab
US4225366A (en) * 1978-10-02 1980-09-30 Nippon Steel Corporation Process for producing grain oriented electrical silicon steel sheet containing aluminium
FR2481151A1 (fr) * 1980-04-26 1981-10-30 Nippon Steel Corp Procede de production d'un feuillard d'acier electromagnetique a grain oriente
US4302257A (en) * 1978-03-11 1981-11-24 Nippon Steel Corporation Process for producing a grain-oriented silicon steel sheet
US4319936A (en) * 1980-12-08 1982-03-16 Armco Inc. Process for production of oriented silicon steel
US4339287A (en) * 1979-05-16 1982-07-13 Nippon Steel Corporation Process for producing grain-oriented silicon steel strip
US4468686A (en) * 1981-11-13 1984-08-28 Intersil, Inc. Field terminating structure
US4478653A (en) * 1983-03-10 1984-10-23 Armco Inc. Process for producing grain-oriented silicon steel
US4579608A (en) * 1980-08-27 1986-04-01 Kawasaki Steel Corporation Grain-oriented silicon steel sheets having a very low iron loss and methods for producing the same
EP0193373A2 (en) * 1985-02-25 1986-09-03 Armco Advanced Materials Corporation Method of producing cube-on-edge oriented silicon steel from strand cast slab
US4623406A (en) * 1982-09-24 1986-11-18 Nippon Steel Corporation Method for producing a grain-oriented electrical steel sheet having a high magnetic flux density
US4623407A (en) * 1982-09-24 1986-11-18 Nippon Steel Corporation Method for producing a grain-oriented electrical steel sheet having a high magnetic flux density
DE4001524A1 (de) * 1989-01-19 1990-07-26 Armco Advanced Materials Verfahren zur herstellung von warmgewalztem kornorientiertem siliziumstahl
EP0411356A2 (en) * 1989-07-12 1991-02-06 Nippon Steel Corporation Method of hot rolling continuously cast grain-oriented electrical steel slab
US5288736A (en) * 1992-11-12 1994-02-22 Armco Inc. Method for producing regular grain oriented electrical steel using a single stage cold reduction
US5421911A (en) * 1993-11-22 1995-06-06 Armco Inc. Regular grain oriented electrical steel production process
US20030062147A1 (en) * 2001-09-13 2003-04-03 Ak Properties, Inc. Method of continuously casting electrical steel strip with controlled spray cooling
US20050015031A1 (en) * 2003-07-17 2005-01-20 Lin Chuan Shen Chair
US20050124922A1 (en) * 2003-07-17 2005-06-09 Chuan-Shen Lin Chair

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AT336916B (de) * 1974-03-22 1977-06-10 Philips Nv Magazin fur in kassetten untergebrachte bandformige aufzeichnungstrager
JPS5319913A (en) * 1976-08-10 1978-02-23 Nippon Steel Corp Preparation of unidirectional silicon steel sheet superior in magnetism from continuous casting slab
JPS5353522A (en) * 1976-10-27 1978-05-16 Kawasaki Steel Co Method of making continuously cast slab for directive silicon steel
JPS597768B2 (ja) * 1981-05-30 1984-02-21 新日本製鐵株式会社 磁性の優れた一方向性電磁鋼板の製造法
DE4311151C1 (de) * 1993-04-05 1994-07-28 Thyssen Stahl Ag Verfahren zur Herstellung von kornorientierten Elektroblechen mit verbesserten Ummagnetisierungsverlusten
DE4311150C1 (de) * 1993-04-05 1993-12-23 Thyssen Stahl Ag Verfahren zur Herstellung von Warmband für die Erzeugung von kornorientierten Elektroblechen
DE19735062A1 (de) * 1997-08-13 1999-02-18 Thyssen Stahl Ag Verfahren zur Herstellung von kornorientiertem Elektroblech und Verwendung eines Stahls für Elektroblech

Cited By (47)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3948691A (en) * 1970-09-26 1976-04-06 Nippon Steel Corporation Method for manufacturing cold rolled, non-directional electrical steel sheets and strips having a high magnetic flux density
US4006044A (en) * 1971-05-20 1977-02-01 Nippon Steel Corporation Steel slab containing silicon for use in electrical sheet and strip manufactured by continuous casting and method for manufacturing thereof
US3969162A (en) * 1972-03-30 1976-07-13 Henke Robert H Method of producing silicon steel strip
US3971678A (en) * 1972-05-31 1976-07-27 Stahlwerke Peine-Salzgitter Aktiengesellschaft Method of making cold-rolled sheet for electrical purposes
US4066479A (en) * 1972-07-08 1978-01-03 Nippon Steel Corporation Process for producing non-directional electric steel sheets free from ridging
US3855018A (en) * 1972-09-28 1974-12-17 Allegheny Ludlum Ind Inc Method for producing grain oriented silicon steel comprising copper
US3895974A (en) * 1972-10-11 1975-07-22 Nippon Steel Corp Process for producing a grain-oriented electrical steel sheet having excellent magnetic characteristic
US3933537A (en) * 1972-11-28 1976-01-20 Kawasaki Steel Corporation Method for producing electrical steel sheets having a very high magnetic induction
US3932236A (en) * 1973-01-22 1976-01-13 Nippon Steel Corporation Method for producing a super low watt loss grain oriented electrical steel sheet
US3873381A (en) * 1973-03-01 1975-03-25 Armco Steel Corp High permeability cube-on-edge oriented silicon steel and method of making it
US3855019A (en) * 1973-05-07 1974-12-17 Allegheny Ludlum Ind Inc Processing for high permeability silicon steel comprising copper
US3855020A (en) * 1973-05-07 1974-12-17 Allegheny Ludlum Ind Inc Processing for high permeability silicon steel comprising copper
US3988177A (en) * 1973-11-05 1976-10-26 Vereinigte Osterreichische Eisen- Und Stahlwerke-Alpine Montan Aktiengesellschaft Method of producing cold rolled, silicon-alloyed electric sheets
US3986902A (en) * 1974-05-22 1976-10-19 United States Steel Corporation Silicon steel suitable for production of oriented silicon steel using low slab reheat temperature
US3925115A (en) * 1974-11-18 1975-12-09 Allegheny Ludlum Ind Inc Process employing cooling in a static atmosphere for high permeability silicon steel comprising copper
US3929522A (en) * 1974-11-18 1975-12-30 Allegheny Ludlum Ind Inc Process involving cooling in a static atmosphere for high permeability silicon steel comprising copper
US4118255A (en) * 1975-08-01 1978-10-03 Centro Sperimentale Metallurgico S.P.A Process for the production of a silicon steel strip with high magnetic characteristics
US4088513A (en) * 1976-04-03 1978-05-09 Nippon Steel Corporation Method for heating a silicon-containing steel slab in a walking-beam type heating furnace
FR2359902A1 (fr) * 1976-07-27 1978-02-24 Nippon Steel Corp Procede de production de tole d'acier electrique non directionnel denue de nervures
US4168189A (en) * 1977-05-20 1979-09-18 Armco Inc. Process of producing an electrically insulative film
US4302257A (en) * 1978-03-11 1981-11-24 Nippon Steel Corporation Process for producing a grain-oriented silicon steel sheet
US4225366A (en) * 1978-10-02 1980-09-30 Nippon Steel Corporation Process for producing grain oriented electrical silicon steel sheet containing aluminium
US4202711A (en) * 1978-10-18 1980-05-13 Armco, Incl. Process for producing oriented silicon iron from strand cast slabs
US4204891A (en) * 1978-11-27 1980-05-27 Nippon Steel Corporation Method for preventing the edge crack in a grain oriented silicon steel sheet produced from a continuously cast steel slab
US4339287A (en) * 1979-05-16 1982-07-13 Nippon Steel Corporation Process for producing grain-oriented silicon steel strip
FR2481151A1 (fr) * 1980-04-26 1981-10-30 Nippon Steel Corp Procede de production d'un feuillard d'acier electromagnetique a grain oriente
US4406715A (en) * 1980-04-26 1983-09-27 Nippon Steel Corporation Process for producing grain-oriented electromagnetic steel strip
US4579608A (en) * 1980-08-27 1986-04-01 Kawasaki Steel Corporation Grain-oriented silicon steel sheets having a very low iron loss and methods for producing the same
US4319936A (en) * 1980-12-08 1982-03-16 Armco Inc. Process for production of oriented silicon steel
US4468686A (en) * 1981-11-13 1984-08-28 Intersil, Inc. Field terminating structure
US4623407A (en) * 1982-09-24 1986-11-18 Nippon Steel Corporation Method for producing a grain-oriented electrical steel sheet having a high magnetic flux density
US4623406A (en) * 1982-09-24 1986-11-18 Nippon Steel Corporation Method for producing a grain-oriented electrical steel sheet having a high magnetic flux density
US4478653A (en) * 1983-03-10 1984-10-23 Armco Inc. Process for producing grain-oriented silicon steel
EP0193373A3 (en) * 1985-02-25 1987-03-18 Armco Inc. Method of producing cube-on-edge oriented silicon steel from strand cast slab
EP0193373A2 (en) * 1985-02-25 1986-09-03 Armco Advanced Materials Corporation Method of producing cube-on-edge oriented silicon steel from strand cast slab
US4718951A (en) * 1985-02-25 1988-01-12 Armco Inc. Method of producing cube-on-edge oriented silicon steel from strand cast slab
AU595789B2 (en) * 1985-02-25 1990-04-12 Armco Inc. Method of producing cube-on-edge oriented silicon steel from strand cast slab
DE4001524A1 (de) * 1989-01-19 1990-07-26 Armco Advanced Materials Verfahren zur herstellung von warmgewalztem kornorientiertem siliziumstahl
EP0411356A2 (en) * 1989-07-12 1991-02-06 Nippon Steel Corporation Method of hot rolling continuously cast grain-oriented electrical steel slab
EP0411356A3 (en) * 1989-07-12 1992-09-30 Nippon Steel Corporation Method of hot rolling continuously cast grain-oriented electrical steel slab
US5288736A (en) * 1992-11-12 1994-02-22 Armco Inc. Method for producing regular grain oriented electrical steel using a single stage cold reduction
US5421911A (en) * 1993-11-22 1995-06-06 Armco Inc. Regular grain oriented electrical steel production process
US20030062147A1 (en) * 2001-09-13 2003-04-03 Ak Properties, Inc. Method of continuously casting electrical steel strip with controlled spray cooling
US6739384B2 (en) 2001-09-13 2004-05-25 Ak Properties, Inc. Method of continuously casting electrical steel strip with controlled spray cooling
US20050015031A1 (en) * 2003-07-17 2005-01-20 Lin Chuan Shen Chair
US20050124922A1 (en) * 2003-07-17 2005-06-09 Chuan-Shen Lin Chair
US7217248B2 (en) * 2003-07-17 2007-05-15 Chuan-Shen Lin Chair

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DE2252784A1 (de) 1973-05-10
RO62344A (ru) 1977-09-15
FR2158458B1 (ru) 1977-01-14
CA978067A (en) 1975-11-18
AU466217B2 (en) 1975-10-23
SE394692B (sv) 1977-07-04
DE2252784C3 (de) 1978-04-06
IT966868B (it) 1974-02-20
DE2252784B2 (de) 1977-08-04
ES408258A1 (es) 1976-02-16
JPS4853919A (ru) 1973-07-28
ZA727467B (en) 1973-07-25
AU4800272A (en) 1974-04-26
CS213306B2 (en) 1982-04-09
JPS5427820B2 (ru) 1979-09-12
BE790798A (fr) 1973-02-15
SU692570A3 (ru) 1979-10-15
FR2158458A1 (ru) 1973-06-15
BR7207657D0 (pt) 1973-08-21
GB1403271A (en) 1975-08-28

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