US3159511A - Process of producing single-oriented silicon steel - Google Patents

Process of producing single-oriented silicon steel Download PDF

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US3159511A
US3159511A US198395A US19839562A US3159511A US 3159511 A US3159511 A US 3159511A US 198395 A US198395 A US 198395A US 19839562 A US19839562 A US 19839562A US 3159511 A US3159511 A US 3159511A
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silicon steel
rolling
anneal
temperature
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Taguchi Satorn
Sakakura Akira
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Yawata Iron and Steel Co Ltd
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    • 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
    • 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
    • C21D3/00—Diffusion processes for extraction of non-metals; Furnaces therefor
    • C21D3/02—Extraction of non-metals
    • C21D3/04—Decarburising
    • 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

  • PROCESS OF PRODUCING SINGLE-ORIENTED SILICON STEEL Filed May 16, 1962 3 Sheets-Sheet 3 INVENTOR3 SATaRu Mal/CHI A IRA SAKA KURA United States Patent 3,159,511 PROCESS 6F PRQDUCING SINGLE-URIENTEB SILICON STEEL Saturn Taguchi andAidra 'Sakairura, Yawata, Japan, as-
  • This invention relates to an improved process for producing single-oriented silicon steel sheets or strips of outstanding magnetic qualities.
  • Silicon steel sheets which have so far been used for iron cores for transformers, generators, and the like, are of a soft magnetic material. Many attempts have been made to control the crystal orientation of the silicon steel sheet in accordance with its use, because the silicon steel has a body centered cubic crystal structure in which three mutually vertical directions of easy magnetization or cube axes 100 are present and, as a consequence thereof, it a magnetic field is applied parallel with one of these directions, the amount of energy necessary to magnetize the silicon steel core will be at a minimum.
  • a silicon steel sheet according to the invention is of the (110) [001] type.
  • the direction of easy magnetization 100 is parallel with only one direction which is the rolling direction on the rolling surface, and the two other directions of easy magnetization l00 are so oriented relative to the first-mentioned direction as to form 45 degrees with the rolling surface.
  • This type of silicon steel sheet is called a single-oriented silicon steel sheet and has superior magnetic characteristics specifically in the rolling direction.
  • Single-oriented silicon steel having outstanding magnetic properties must, of course, be carefully distinguished from othernon-oriented silicon steels such as electric Patented Dec. 1, 1964 ice grade, armature grade and motor grade steels of magnetic induction values, at 10 oersteds in the order of 13,000 to 14,000 gausses, with which this invention is not concerned.
  • B designates the magnetic flux density in a'magnetic field of 10 oersteds and therefore, the better the parallel relation of the axis of easy magnetization with the rolling direction, the higher the value shown by B and the less the electric power'loss in case the sheet is used as an'iron core.
  • the value of B in the rolling direction as shown by single-oriented silicon steel sheet marketed today is 17,000 to 18,000 gausses. It is considered that, in case B is lower than 17,000 gausses, the sheet does not perform as a singleoriented silicon steel sheet.
  • U.S. Patents 2,287,466 to Carpenter and 2,287,467 to Carpenter and Jackson obtain straightgrain permeability in silicon steels, coupled with low core and hysteresis losses from silicon steels by hot rolling a silicon steel containing from about 1 to 4% of silicon to a hot-rolled sheet, then subjecting the hot-rolled sheet to a cold rolling reduction in a single stage by about 67 to 83%, and finally heat treating the steel at temperatures between 700 and 1200 C.
  • the unpiclded material is advantageously subjected to a decarburizing box anneal at 650 to 925 C. for two 'to twenty-four hours prior to cold rolling.
  • Decarburization has been recommended because it was recognized that carbon present in electrical steels in amounts substantially greater than 0.02%, as iron caribide, adversely affects the electrical properties.
  • the decarburizati-on can also be carried out after cold rolling, for'instance cold rolling in two stages, 'by first decarburizing the cold rolled silicon steel strip containing from about 1.5 to 4% of silicon at a temperature of about 800 C. and then holding the strip at a tempera ture of about 850 to 900 C. in a non-oxidizing atmosphere for about four to twenty-four hours and thereafter subjecting the'strip to a heat treatment at higher temperature between 900 and 1200 C. (British Patent 667,279 to Thompson-Houston Co. and US. Patent 2,534,141 to Morill et a1.), thereby achieving perfection of the texture of the cold rolled strip and relief of mechanical strain.
  • the magnetic induction thus achieved by the various known treatments involving a single cold rolling step in single-oriented silicon steel at constant magnetizing force of 10 oersteds was in the order of 16,000 gausses and with two cold-rolling steps up to 17,300 gausses, until Littm-ann and Heck (US. Patent 2,599,340), Rickett (US. Patent 2,826,520), Crede and co-workers (US. Patent 2,867,557) and others taught that even higher magnetic induction values could be attained, if the silicon steel ingots having the conventional silicon content of electrical steels were subjected to an extensive heat treatment prior to and/or during the hot rolling treatment and, in any event, prior to any cold rolling treatment, whether single or multi-stage.
  • the magnetic induction value which has so far been 16,600 to 17,620 has now been improved by Littmann et al. to be 17,000 to 18,350 and by Crede et al. to be on the average 18,090 at 10 oersteds by subjecting the abovementioned ingots and/ or slabs to a special heat treatment at higher temperatures.
  • Littmann and Heck heat the ingots to about 1290 C., then roll into slabs, heat the slabs in a slab furnace to about or even above 1375 C., without burning, hot roll the slabs as rapidly as possible to about 5.5 to 9 times the final thickness, then open anneal at 760 to 1100 C. and then pickle and subject the hot rolled material to the earlier known cold rolling and annealing treatment.
  • this slab-reheating process was further modified by Crede and co-workers who heat the ingots to a temperature of over 1260 C. for a minimum of hours, which comprise heating for at least three hours to not less than 1345 C., then slab the steel to obtain a hot slab having a thickness of from to 1 /2 inches and a temperature of not less than 1095 C. and then immediately subject the hot slab to a series of hot reductions to produce a strip of a thickness of 0.060 to 0.10 inch before the temperature of the strip decreases below 870 C., so that the direct hot Working from the heated ingot to the hot rolled strip is carried out without an intermediate reheating of the steel.
  • the steel is then subjected to two cold rolling treatments with intermediate open anneal at 870 to 1010 C., and, after termination of cold reduction, an open anneal in a decarburizing atmosphere at 760 to 850 C., and finally a box anneal in dry hydrogen at 1150 to1200 C.
  • Crede and co-workers obtained singleoriented steel, the magnetic induction of which, at oersteds, amounted to 17,600 to 18,690 gausses, with an average of 18,090 gausses, and which satisfactorily low watt losses.
  • an ingot is heated to the conventional temperature of 1000 to 1260 C. and is directly hot-rolled to obtain a hot-rolled sheet and the sheet is treated in two cold-rolling steps, a value of only 16,000 to 17,200 gausses will be obtained.
  • the direct hot rolling with intermediate anneal at 870 C. to 1010 C. only affords a product which shows magnetic induction values of 16,000 to 17,620 gausses; direct hot rolling with subsequent single cold rolling treatment, i.e. without intermediate annealing affords only silicon steel strip with magnetic induction values, at 10 oresteds, below 16,000 gausses.
  • microsegregations of various elements in the steel are made more homogeneous by the conventionally practised slab reheating process than by the direct hot-rolling invented by Crede.
  • Such microsegregation, particularly of phosphorus and manganese, was believed to be responsible for the erratic response of silicon steels to treatments designed to produce a grain-oriented structure.
  • the aluminum content of the silicon steel must be held between 0.010 and 0.030% by weight in the silicon steel ingot at the beginning of the hot rolling treatment.
  • the temperature during the open anneal following the cold rolling stage must not exceed 1050" C., or it will be impossible to attain the outstanding magnetic properties, hitherto achieved exclusively by the more complicated and less economical processes described above, by a single cold rolling stage, without intermediate anneal between a plurality of cold rolling phases.
  • FIG. 1 represents the curves showing the relation between cold rolling and core loss after the final anneal or" silicon steel sheet or strip treated by the process according to our invention.
  • FIG. 2 illustrates the curves showing the relation between the temperature of continuous anneal and core loss after the aforesaid final anneal.
  • PEG. 3 represents the curves showing the relation between aluminum content prior to the final box anneal and core loss after the final box anneal in the process according to our invention.
  • KG. 4 gives the curves showing the relation between carbon content prior to the final box anneal and core loss after the final anneal.
  • FIG. 5 gives macrostructure photographs (actual size) showing the relation between aluminum content prior to the final anneal and crystal grain size after the final anneal with reference to six different samples, A, B, C, D, E and F.
  • FIG. 6 is a diagram showing the relation between the rate of reduction of the thickness in the secondary whereby it is removed as carbon oxide.
  • Silicon steel adapted for carrying out the improved process of producing single-oriented steel strip or sheets
  • silicon according to our invention must contain from 2.0 to 4.0% .by weight of silicon, silicon contents of 2.9 to 3.2% being preferred.
  • the starting material must further contain the above defined amounts of aluminum.
  • the carbon content should be between 0.02 and 0.06%, about 0.04% being preferred.
  • the carbon content is not to limit the composition of the material of the present invention.- However, it is difficult to reduce the carbon content to less than 0.02% in the industrially obtained ordinary ingot. If the carbon content is greater than 0.06%, troublesome decarburization treatment will be required in order to eliminate the detrimental eifect'of the residual carbon on the magnetic characteristics of the product. Therefore, a content of 0.02 to 0.06% C is recommended in the starting material for the process ofthe present in vention.
  • the products produced by these known methods are nonoriented silicon steel sheets and their industrial uses are different from those of the products of the present inven tion.
  • Theobject of adding aluminum in the known methods is to prevent the 7 phase from appearing, where as, in the present process, the 7 phase would not be expected to and does not appear, irrespective of the presence or absence of aluminum.
  • the art had, therefore, considered the presence of aluminumin silicon steel used as starting material in the production of singletempt to use a determined aluminum content.
  • the magnetic permeability ime proves, because altuninum was believed to form oxide such as A1 0 in the steel which would be detrimental to the magnetic characteristics.
  • the ingot in the present invention is heated to a maximum of 1260 C. and is bloomed in a blooming mill (slab mill) so as to obtain a slab of conventional dimensions, and the slab is then reheated to 1000 to 1260" C.
  • the resulting product is finally box annealed at a temperature within the range of about 1000 to 1200 C. for several hours. 4
  • B when the aluminum content is 0.020%, B will be of such high value as 17,800 gausses. This is a value which has hitherto never been obtained in the production of single-oriented steel involving the'conventional slab reheating process.
  • the aluminum content is held above 0.010 and up to 0.030% in the present invention. It will now be shown that a superior singleoriented silicon steel sheet can be obtainedin a single cold-rolling treatment by adding the above-defined small amount of aluminum.
  • FIGURE 6A shows the variation of the core loss value as against varying aluminum contents in the case that a stock having such chemical composition as is shown also in Table II was heated to 1200 C. and was bloomed to be converted to a slab, the slab was again heated to 1250 C. and was hot-rolled to a hot-rolled sheet of 1.6mm. thickness and the sheet was pickled, then coldrolled at a rate of depression of about 80%, continuously annealed at 850 C. for three minutes, then secondarily cold-rolled to reduce the thickness variously and finally is unexpectedly obtained, due to the effect of the abovedefined aluminum content, without such secondary coldrolling step, than with the same.
  • WIS/50 which shows watts 15 kilogausses at a frequency of 50 cycles per second, and Watts loss per kilogram.
  • FIG. 2 shows the test results of core loss in which a silicon steel containing the composition given in. Table II is bloomed and is then hot-rolled to a hot-rolled sheet of 1.6 mm. thickness, then cold rolled with a reduction of 80%, continuously annealed at different temperatures between 700 and 1200 C. for three minutes, respectively, and finally annealed at the temperature of 1200 C. for twenty hours.
  • the temperature range of 750 to 950 C. is preferred with a view to obtaining a final product having optional magnetic properties, and decarburization is advantageously effected within that temperature range.
  • the temperature of the continuous annealing is higher than the temperature of 1050 C.
  • FIGURE 63 shows the variation of the core loss value as against varying aluminum contents in the case that a silicon steel sheet having such chemical composition as is shown in Table II was first heated to 1200 C., was bloomed,
  • a highly oriented crystal grain favored with smooth boundary is developed in the silicon steel by the final anneal, thereby alfording a final product of excellent magnetic properties.
  • the short time continuous anneal serves the purpose of improving the recrystallized struc ture by the development of crystal grain growth of large and uniform size.
  • the recrystallized structure of the metal after an anneal within this temperature range has a relatively large grain of uniform size, while at an anneal of a higher temperature than 1050 C. a crystal grain of irregular and coarse size is grown, so that a highly oriented grain growth cannot be expected after the final anneal.
  • the carbon content of the silicon steel has decreased so low due to decarburizing effect by boxannealing the hot-rolled strip with rnill scales deposited thereon that the carbon does not interfere with grain growth at the final annealing core loss after, the improved results will be obtained even though the steel is subjected directly to the final anneal without recourse to a short time continuous anneal after the cold rolling step. How ever, a short time continuous anneal is preferable in order to improve a consistent quality of the final product.
  • the final box anneal is preferably carried out in a neutral or reducing atmosphere at a higher temperature than 1000 C. for at least five hours in order to obtain a grain-oriented silicon steel having low core loss. It is desirable .to anneal the steel for a number of hours at an elevated temperature, but an anneal at a higher temperature than 1250" C. for more than forty hours is not ef fective in spite of an elevated temperature and long hours.
  • FIG. ,4 gives thecurves showing the relation between carbon content prior to the final anneal and core loss after the final anneal in which the steel having analysis of sample D or similar analysis is hot rolled, then cold rolled in a single stage with a reduction in thickness of 80 percent, annealed continuously at the temperature of 850 C. for three minutes, and finally annealed at the temperature of 1200 C. for twenty hours, which indicate clearly that carbon has a considerably adverse effect on 1 1 the steel, and suggest that 0.008% C. is requisite prior to the final anneal.
  • our invention cornprises the usual slab reheating hot rolling process of silicon steel stock containing 2.04.0% Si, and 0.0l0.030% Al, then cold rolling in a single step, continuously annealing at 750-950 C. for a short time, and finally annealing at 1000-1200 0; therefore, our process is very simple compared with the most recent processes, yet it provides for a commercial production of single oriented silicon steel with the best hitherto achieved magnetic properties including low core loss in an inexpensive manner.
  • Hot rolled silicon steel strip of the composition of sample D in Table I with hot mill scale thereon is boxannealed at 750 C. for about 5 hours immediately after rot rolling (analysis after box-anneal: 0.010% C, 2.95% Si, 0.017% Al in all, 0.015% acid-soluble Al, 0.008% Ti, 0.0102% N in all, 0.0072% N as AlN).
  • the strip is then pickled, cold rolled in a single strip with a reduction in thickness of 80% to the final gauge, 0.33 mm., and then annealed continuously at 1200 C. for twenty hours.
  • the test values after the final anneal are a core loss of 1.08 watts per kilogram at kilogausses at 50 cycles, and a magnetic induction of 18,050 gausses at 10 oersteds.
  • Hot Ingot A1 Ingot Slab Reheat- Rolling Open Cold Process and/or Designation of Steel Percent Soaking Temp. ing of Temp. Anneal Rolling Temp. Slab at first Stand Armeo Transeor Mir U.S. Steel USS Transformer 52 M-l4 Yawata Hilite Cor H12.
  • the hot-rolled strip is then pickled, and then cold rolled with a reduction in thickness of 80 percent in a single step to the final gauge, 0.33 mm. Thereafter, it is continuously annealed at 850 C. for three minutes, and finally annealed at 1200 C. for twenty hours.
  • Core loss and magnetic induction values obtained after the anneal have been reported in Table I. Particularly, the sample D containing 0.017% A1 prior to the final anneal affords a core loss of 1.11 watts per kilogram at 15 kilogausses at 50 cycles, a magnetic induction of 17,800 gausses at 10 oersteds, and high orientation.
  • the macrostructure of after box-anneal 0.007% C, 2.96% Si, 0.015% A1 in all, 0.011% acid-soluble Al, 0.006% Ti, 0.0079% N in all, 0.0049% N as AlN) is pickled, then cold rolled in a single step with a reduction in thickness of to the final gauge, 0.33 111111., and finally annealed at 1200 C. for twenty hours.
  • Core loss and magnetic induction after the final anneal are 1.31 watts per kilogram at 15 kilogausses at 50 cycles and 17,300 gausses at 10 oersteds.
  • a process for producing single-oriented silicon steel sheet which comprises blooming a silicon steel ingot containing 24% by weight Si to produce a silicon steel stock, hot-rolling said stock, pickling said rolled material, subjecting said material to a single cold-rolling, reducing the stock thickness by 65 to thereby producing the sheet of the final thickness, continuously annealing the material in a decarburizing atmosphere at a temperature of between 750 to 950 C., and finally annealing at a temperature of 1,000 to 1,200 C., thereby producing a silicon steel sheet of secondary recrystallization and of good grain-orientation in the direction of cold-rolling, and of a magnetic induction, at 10 oersteds, of greater than 17,000 gausses, the improvement, in combination therewith, wherein (a) said ingot is heated to a temperature of maximally 1260 C.
  • silicon steel 13 14 stock which is reheated to a temperature of maxisentially of 0.02% by weight of Al, 2 to 4% by weight m-ally 1260 C., and of Si, with the balance being essentially iron.
  • said stock consisting essentially of 0.01 to 0.03%

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Cited By (32)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2006864A1 (enrdf_load_stackoverflow) * 1968-04-24 1970-01-02 Yawata Iron & Steel Co
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
DE2303416A1 (de) * 1972-02-11 1973-08-23 Allegheny Ludlum Ind Inc Verfahren zur herstellung eines kornorientierten kupferhaltigen si-stahls
US3853641A (en) * 1968-04-02 1974-12-10 Nippon Steel Corp Method for producing single-oriented silicon steel sheets having high magnetic induction
US3855018A (en) * 1972-09-28 1974-12-17 Allegheny Ludlum Ind Inc Method for producing grain oriented silicon steel comprising copper
US3855021A (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
US3855019A (en) * 1973-05-07 1974-12-17 Allegheny Ludlum Ind Inc Processing for high permeability silicon steel comprising copper
US3902930A (en) * 1972-03-13 1975-09-02 Nippon Musical Instruments Mfg Method of manufacturing iron-silicon-aluminum alloy particularly suitable for magnetic head core
US3932235A (en) * 1973-07-24 1976-01-13 Westinghouse Electric Corporation Method of improving the core-loss characteristics of cube-on-edge oriented silicon-iron
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
US3954521A (en) * 1968-12-23 1976-05-04 Allegheny Ludlum Industries, Inc. Method of producing grain oriented silicon steel
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
US3990923A (en) * 1974-04-25 1976-11-09 Nippon Steel Corporation Method of producing grain oriented electromagnetic steel sheet
US4030950A (en) * 1976-06-17 1977-06-21 Allegheny Ludlum Industries, Inc. Process for cube-on-edge oriented boron-bearing silicon steel including normalizing
FR2438092A1 (fr) * 1978-10-05 1980-04-30 Armco Inc Procede de recuit apres decarburation d'acier au silicium oriente
US4863532A (en) * 1981-08-05 1989-09-05 Nippon Steel Corporation Grain-oriented electromagnetic steel sheet
US4938807A (en) * 1988-02-03 1990-07-03 Nippon Steel Corporation Process for production of grain oriented electrical steel sheet having high flux density
US4997493A (en) * 1987-11-27 1991-03-05 Nippon Steel Corporation Process for production of double-oriented electrical steel sheet having high flux density
US5082509A (en) * 1989-04-14 1992-01-21 Nippon Steel Corporation Method of producing oriented electrical steel sheet having superior magnetic properties
US5125991A (en) * 1987-09-10 1992-06-30 Kawasaki Steel Corporation Silicon steel sheets having low iron loss and method of producing the same
EP0606884A1 (en) * 1993-01-12 1994-07-20 Nippon Steel Corporation Grain-oriented electrical steel sheet with very low core loss and method of producing the same
DE19745445C1 (de) * 1997-10-15 1999-07-08 Thyssenkrupp Stahl Ag Verfahren zur Herstellung von kornorientiertem Elektroblech mit geringem Ummagnetisierungsverlust und hoher Polarisation
WO2007049915A1 (en) * 2005-10-25 2007-05-03 Posco Corrosion resistance improved steel sheet for autmotive muffler and method of producing the steel sheet
WO2008032483A1 (fr) 2006-09-13 2008-03-20 Nippon Steel Corporation Procédé de fabrication de feuilles d'acier au silicium à grains orientés de haute densité de flux magnétique
WO2011114178A1 (en) 2010-03-19 2011-09-22 Arcelormittal Investigación Y Desarrollo Sl Process for the production of grain oriented electrical steel
CN101297055B (zh) * 2005-10-25 2012-11-28 Posco公司 用于机动车消音器的抗蚀性提高的钢板及该钢板的生产方法
DE102011054004A1 (de) 2011-09-28 2013-03-28 Thyssenkrupp Electrical Steel Gmbh Verfahren zum Herstellen eines kornorientierten, für elektrotechnische Anwendungen bestimmten Elektrobands oder -blechs
EP2933350A1 (en) 2014-04-14 2015-10-21 Mikhail Borisovich Tsyrlin Production method for high-permeability grain-oriented electrical steel
EP3693496A1 (de) 2019-02-06 2020-08-12 Rembrandtin Lack GmbH Nfg.KG Wässrige zusammensetzung zur beschichtung von kornorientiertem stahl
CN113897558A (zh) * 2021-10-08 2022-01-07 北京北冶功能材料有限公司 一种高饱和磁感高磁导率铁基软磁材料及其制备方法

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3136666A (en) * 1960-01-27 1964-06-09 Yawata Iron & Steel Co Method for producing secondary recrystallization grain of cube texture
US3130093A (en) * 1960-11-08 1964-04-21 Armco Steel Corp Production of silicon-iron sheets having cubic texture
BE756731A (fr) * 1969-11-03 1971-03-01 Forges De La Loire St Chamond Procede de fabrication d'aciers a grains orientes a usages magnetiques,et produits obtenus
JPS4926415B1 (enrdf_load_stackoverflow) * 1970-09-26 1974-07-09

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2287466A (en) * 1939-12-05 1942-06-23 American Rolling Mill Co Process of producing high permeability silicon steel
US2599340A (en) * 1948-10-21 1952-06-03 Armco Steel Corp Process of increasing the permeability of oriented silicon steels
US2867557A (en) * 1956-08-02 1959-01-06 Allegheny Ludlum Steel Method of producing silicon steel strip

Family Cites Families (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
BE512625A (enrdf_load_stackoverflow) *

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2287466A (en) * 1939-12-05 1942-06-23 American Rolling Mill Co Process of producing high permeability silicon steel
US2599340A (en) * 1948-10-21 1952-06-03 Armco Steel Corp Process of increasing the permeability of oriented silicon steels
US2867557A (en) * 1956-08-02 1959-01-06 Allegheny Ludlum Steel Method of producing silicon steel strip

Cited By (40)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3853641A (en) * 1968-04-02 1974-12-10 Nippon Steel Corp Method for producing single-oriented silicon steel sheets having high magnetic induction
FR2006864A1 (enrdf_load_stackoverflow) * 1968-04-24 1970-01-02 Yawata Iron & Steel Co
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
US3954521A (en) * 1968-12-23 1976-05-04 Allegheny Ludlum Industries, Inc. Method of producing grain oriented silicon steel
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
DE2303416A1 (de) * 1972-02-11 1973-08-23 Allegheny Ludlum Ind Inc Verfahren zur herstellung eines kornorientierten kupferhaltigen si-stahls
US3902930A (en) * 1972-03-13 1975-09-02 Nippon Musical Instruments Mfg Method of manufacturing iron-silicon-aluminum alloy particularly suitable for magnetic head core
US3971678A (en) * 1972-05-31 1976-07-27 Stahlwerke Peine-Salzgitter Aktiengesellschaft Method of making cold-rolled sheet for electrical purposes
US3855018A (en) * 1972-09-28 1974-12-17 Allegheny Ludlum Ind Inc Method for producing grain oriented silicon steel comprising copper
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
US3855021A (en) * 1973-05-07 1974-12-17 Allegheny Ludlum Ind Inc Processing for high permeability silicon steel comprising copper
US3932235A (en) * 1973-07-24 1976-01-13 Westinghouse Electric Corporation Method of improving the core-loss characteristics of cube-on-edge oriented silicon-iron
US3990923A (en) * 1974-04-25 1976-11-09 Nippon Steel Corporation Method of producing grain oriented electromagnetic steel sheet
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
US4030950A (en) * 1976-06-17 1977-06-21 Allegheny Ludlum Industries, Inc. Process for cube-on-edge oriented boron-bearing silicon steel including normalizing
FR2438092A1 (fr) * 1978-10-05 1980-04-30 Armco Inc Procede de recuit apres decarburation d'acier au silicium oriente
US4863532A (en) * 1981-08-05 1989-09-05 Nippon Steel Corporation Grain-oriented electromagnetic steel sheet
US5125991A (en) * 1987-09-10 1992-06-30 Kawasaki Steel Corporation Silicon steel sheets having low iron loss and method of producing the same
US4997493A (en) * 1987-11-27 1991-03-05 Nippon Steel Corporation Process for production of double-oriented electrical steel sheet having high flux density
US4938807A (en) * 1988-02-03 1990-07-03 Nippon Steel Corporation Process for production of grain oriented electrical steel sheet having high flux density
US5082509A (en) * 1989-04-14 1992-01-21 Nippon Steel Corporation Method of producing oriented electrical steel sheet having superior magnetic properties
EP0606884A1 (en) * 1993-01-12 1994-07-20 Nippon Steel Corporation Grain-oriented electrical steel sheet with very low core loss and method of producing the same
US5833768A (en) * 1993-01-12 1998-11-10 Nippon Steel Corporation Grain-oriented electrical steel sheet with very low core loss and method of producing the same
DE19745445C1 (de) * 1997-10-15 1999-07-08 Thyssenkrupp Stahl Ag Verfahren zur Herstellung von kornorientiertem Elektroblech mit geringem Ummagnetisierungsverlust und hoher Polarisation
CN101297055B (zh) * 2005-10-25 2012-11-28 Posco公司 用于机动车消音器的抗蚀性提高的钢板及该钢板的生产方法
WO2007049915A1 (en) * 2005-10-25 2007-05-03 Posco Corrosion resistance improved steel sheet for autmotive muffler and method of producing the steel sheet
US20080257461A1 (en) * 2005-10-25 2008-10-23 Won-Ho Son Corrosion Resistance Improved Steel Sheet for Autmotive Muffler and Method of Producing the Steel Sheet
US7922968B2 (en) 2005-10-25 2011-04-12 Posco Corrosion resistance improved steel sheet for automotive muffler and method of producing the steel sheet
US20090199935A1 (en) * 2006-09-13 2009-08-13 Akira Sakakura Method of production of high flux density grain-oriented silicon steel sheet
WO2008032483A1 (fr) 2006-09-13 2008-03-20 Nippon Steel Corporation Procédé de fabrication de feuilles d'acier au silicium à grains orientés de haute densité de flux magnétique
WO2011114178A1 (en) 2010-03-19 2011-09-22 Arcelormittal Investigación Y Desarrollo Sl Process for the production of grain oriented electrical steel
WO2011114227A2 (en) 2010-03-19 2011-09-22 Aperam Grain oriented steel strip with high magnetic characteristics, and manufacturing process of the same
DE102011054004A1 (de) 2011-09-28 2013-03-28 Thyssenkrupp Electrical Steel Gmbh Verfahren zum Herstellen eines kornorientierten, für elektrotechnische Anwendungen bestimmten Elektrobands oder -blechs
WO2013045339A1 (de) 2011-09-28 2013-04-04 Thyssenkrupp Steel Europe Ag Verfahren zum herstellen eines kornorientierten, für elektrotechnische anwendungen bestimmten elektrobands oder -blechs
EP2933350A1 (en) 2014-04-14 2015-10-21 Mikhail Borisovich Tsyrlin Production method for high-permeability grain-oriented electrical steel
EP3693496A1 (de) 2019-02-06 2020-08-12 Rembrandtin Lack GmbH Nfg.KG Wässrige zusammensetzung zur beschichtung von kornorientiertem stahl
WO2020161094A1 (de) 2019-02-06 2020-08-13 Rembrandtin Lack Gmbh Nfg. Kg Wässrige zusammensetzung zur beschichtung von kornorientiertem stahl
CN113897558A (zh) * 2021-10-08 2022-01-07 北京北冶功能材料有限公司 一种高饱和磁感高磁导率铁基软磁材料及其制备方法

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FR1192271A (fr) 1959-10-26
DE1226129B (de) 1966-10-06
DE1226129C2 (enrdf_load_stackoverflow) 1967-04-27
GB873149A (en) 1961-07-19

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