EP0585956A1 - Dicke kornorientierte Elektrostahlbleche mit hervorragenden magnetischen Eigenschaften - Google Patents

Dicke kornorientierte Elektrostahlbleche mit hervorragenden magnetischen Eigenschaften Download PDF

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Publication number
EP0585956A1
EP0585956A1 EP93114263A EP93114263A EP0585956A1 EP 0585956 A1 EP0585956 A1 EP 0585956A1 EP 93114263 A EP93114263 A EP 93114263A EP 93114263 A EP93114263 A EP 93114263A EP 0585956 A1 EP0585956 A1 EP 0585956A1
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grain
sheet
electrical steel
steel sheet
oriented electrical
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EP93114263A
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English (en)
French (fr)
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EP0585956B1 (de
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Yasunari c/o Nippon Steel Corporation Yoshitomi
Nobuyuki C/O Nippon Steel Corporation Takahashi
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Nippon Steel Corp
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Nippon Steel Corp
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    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/14766—Fe-Si based alloys
    • H01F1/14775—Fe-Si based alloys in the form of sheets
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—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
    • 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
    • C21D8/1261—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 following 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
    • C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
    • C21D8/1272—Final recrystallisation annealing

Definitions

  • This invention relates to a thick grain-oriented electrical steel sheet exhibiting excellent magnetic properties and suitable for use as the material for the core of a transformer or the like.
  • Magnetization property is generally expressed as the flux density B8 value at a magnetic field of 800 A/m
  • core loss property is expressed as the W 17/50 core loss value at a frequency of 50 Hz and a magnetization to 1.7 Tesla.
  • the main factor governing core loss property is flux density. Generally speaking, the higher the flux density, the better is the core loss property. Notwithstanding, increasing the flux density causes the secondary recrystallization grain size to be enlarged simultaneously and, to the extent that it does, has a degrading effect on the core loss property. In contrast, magnetic domain control enables an improvement in core loss property irrespective of the secondary recrystallization grain diameter.
  • Grain-oriented electrical steel sheet is produced with use of secondary recrystallization phenomenon in the final annealing step so as to develop a Goss texture wherein the grains have their (110) axes aligned with the sheet surface and their ⁇ 001 ⁇ axes aligned with the rolling direction.
  • the easily magnetizable ⁇ 001 ⁇ axis has to have a high degree of alignment with the rolling direction.
  • JP-B-40-15644 and JP-B-51-13469 teach typical methods for producing a high flux density grain-oriented electrical steel sheet.
  • JP-B-40-15644 describes a method using MnS and AlN as the main inhibitors and
  • JP-B-51-13469 describes a method of using MnS, MnSe, Sb and the like as the main inhibitors. Appropriate control of the size, morphology and distribution of the precipitates functioning as inhibitors is therefore an indispensable requirement in the currently available technology.
  • the laminated core sector has experienced increasing need for thick grain-oriented electrical steel sheet enabling a reduction in the number of laminations.
  • the large rotating machine sector has also long showed an interest in using grain-oriented electrical steel sheet.
  • the need is particularly high for thick grain-oriented electrical steel sheet that allows the number of laminations to be reduced.
  • the object of this invention is to provide a thick grain-oriented electrical steel sheet exhibiting good magnetic properties.
  • Fig. 1 is a graph showing how the core loss property of a product sheet is affected by its carbon content and flux density.
  • Fig. 2 is a graph showing how the core loss property of a product sheet is affected by the shape factor of the grain boundary and the deviation degree of crystal orientation in the grains.
  • Fig. 3 is a graph showing how the core loss property of a product sheet is affected by sheet thickness, in products according to the invention and in comparison products.
  • Fig. 4 shows a typical grain pattern of a thick grain-oriented electrical steel sheet according to the invention.
  • the grain-oriented electrical steel sheet of the present invention is produced by sequentially conducting the steps of casting molten steel obtained by a conventional steelmaking method either continuously or by the ingot making method, if the ingot making method is used slabbing the ingot to obtain a slab, hot rolling the slab to obtain a hot-rolled sheet, annealing the hot-rolled sheet as required, subjecting the sheet to a one stage cold rolling or two or more stages of cold rolling with intermediate annealing, decarburization annealing the cold-rolled sheet, and subjecting the decarburized sheet to final finish annealing.
  • the inventors made a broad-based study of the conditions required for realizing good magnetic properties in the process for producing thick grain-oriented electrical steel sheet. This enabled them to ascertain the requirements that must be met by the product.
  • Fig. 1 shows the effect of the product C content and flux density on the product core loss property.
  • a silicon steel slab comprising, by weight, 3.21 - 3.30 % Si, 0.025 - 0.085 % C, 0.025 - 0.030 % acid-soluble Al, 0.0075 - 0.0086 % N, 0.070 - 0.161 % Mn, 0.005 - 0.029 % S and the balance Fe and unavoidable impurities was heated at 1150 - 1380 °C for 1 hr, the slab was hot rolled into a 2.8 mm-thick hot-rolled sheet, one portion of the hot-rolled sheet was annealed at 900 - 1100 °C and another portion thereof was not annealed, and the sheets were cold rolled at a reduction ratio of about 83 % to a thickness of 0.48 mm.
  • the so-obtained cold-rolled sheets were subjected to decarburization annealing (atmosphere: 25 % N2 and 75 % H2; dew point: 65 °C) in the temperature range of 810 - 860 °C for 250 sec. Then, a portion of each sheet was subjected to nitriding treatment, with which N was increased by 0.0102 - 0.0195 %, using NH3 gas during 750 °C x 30 sec additional annealing and another portion of each sheet was not subjected to nitriding treatment.
  • decarburization annealing atmosphere: 25 % N2 and 75 % H2; dew point: 65 °C
  • the sheets were coated with an annealing separation agent consisting mainly of MgO, the coated sheets were rolled into (5-ton) coils measuring 200 - 1500 mm in inside diameter, the coils were subjected to final finishing annealing by heating to 1200 °C at a temperature increase rate of 15 °C/hr in an annealing atmosphere containing 10 - 100 % N2 (remainder H2), and by holding them at 1200 °C for 20 hr in an H2 annealing atmosphere.
  • an annealing separation agent consisting mainly of MgO
  • the coils were applied with a tensile coating and then cut to a size for a single sheet tester, flattened, maintained at 850 °C for 4 hr for strain relieving annealing, whereafter the magnetic properties were measured.
  • the final product thickness was 0.50 mm.
  • Fig. 2 relates to those among the products of the test of Fig. 1 which had a carbon content of not more than 0.0050 % and a flux density B8 of not less than 1.83 T and shows how the core loss property of these products was affected by the shape factor (SF) of the grain boundary of grains with the same area as the circle with diameter exceeding 5 mm has and the deviation degree ( ⁇ ) of crystal orientation in grains of a diameter exceeding 5 mm.
  • shape factor shape factor
  • ⁇ deviation degree
  • the value of SF is 1 for a circular grain and decreases with increasing irregularity (bumpiness) of the grain boundary configuration.
  • the deviation degree ( ⁇ ) of crystal orientation in grains of a diameter exceeding 5 mm represents the difference in orientation in the grain in relation to that at the grain center of gravity.
  • the crystal orientation deviation ( ⁇ ) in the grains generally tends to increase with increasing distance from the center of gravity in the rolling direction.
  • ECP Electron Channeling Pattern
  • SF is expressed as the average value (SF (average value)) for 101 - 151 grains with diameters greater than 5 mm
  • ⁇ is expressed as the average value ( ⁇ (average value)) of the maximum orientation deviations (difference in orientation between that at the center of gravity and that at the point furthest from the center of gravity in the rolling direction) of 81 - 113 grains.
  • the inventors produced products measuring 0.36 - 1.00 mm in thickness with slabs, as starting materials, the same as those used in the explanation of Fig. 1 under the same processing conditions as explained with regard to Fig. 1 except that the thickness of the hot-rolled sheets was 2.3 - 5.0 mm.
  • the basic principle underlying the present invention is that of achieving a specified combination of product grain boundary configuration and crystal orientation deviation.
  • the tendency for spike magnetic domains to form in the vicinity of the grain boundaries becomes even more remarkable when crystal orientation deviation is present in the grains.
  • the resulting enlargement of the grain boundary area increases the frequency of spike magnetic domain occurrence.
  • the increased number of spike magnetic domains produced by the invention causes magnetic domain refinement when the tension is imparted to the sheet by the glass film and coating, in this way improving the core loss property.
  • the C content of the slab is preferably in the range of 0.025 - 0.075 % by weight.
  • the product sheet according to the invention preferably contains 2.5 - 4.5 % Si.
  • Al, N, Mn, S, Se, Sb, B, Cu, Nb, Cr, Sn, Ti, Bi etc. can be added as inhibitor-forming elements. While no particular limit is set on the temperature at which the slab is heated, energy cost considerations and the like make it preferable to use a heating temperature of not more than 1300 °C.
  • the heated slab is subjected to hot rolling into a hot-rolled sheet in the following step.
  • the hot-rolled sheet is annealed as required and the sheet is then subjected to a one stage cold rolling or two or more stages of cold rolling with intermediate annealing, for reducing it to the final sheet thickness.
  • the reduction ratio in the final cold rolling is not particularly limited but a reduction ratio of not less than 80 % is preferable from the point of increasing the product magnetic flux density (B8 value).
  • a reduction ratio of not less than 80 % in the final cold rolling ensures that the decarburization annealed sheet has appropriate amounts of sharp (110) ⁇ 001 ⁇ oriented grains and coincident orientation grains ( ⁇ 111 ⁇ ⁇ 112 ⁇ oriented grains or the like) which are likely to be eroded by the ⁇ 110 ⁇ ⁇ 001 ⁇ oriented grains. This makes it possible to obtain a B8 of not less than 1.83 T.
  • the cold-rolled sheet is subjected to decarburization annealing at 700 - 1000 °C. Since the product according to the invention is thick (0.36 - 1.00 mm), the time required for decarburization to the required level tends to be long. For shortening the required time, it is helpful to lower the C content of the molten steel, increase the decarburization annealing temperature, and/or raise the dew point of the annealing atmosphere.
  • the inhibitor strength is insufficient for evolving secondary recrystallization in the decarburized sheet, it is preferable to carry out nitriding treatment using NH3 gas or some other inhibitor strengthening measure.
  • the sheet After the sheet has been coated with an annealing separation agent consisting mainly of MgO, it is rolled into a coil having an inside diameter of 10 - 100,000 mm and then subjected to final finish annealing.
  • an annealing separation agent consisting mainly of MgO
  • the inside diameter is in this range during finish annealing, the presence of a 0.2 - 4 deg crystal orientation deviation in relation to that at the grain center of gravity can be ensured in the sheet grains exceeding 5 mm in diameter.
  • the final product is then obtained by subjecting the sheet to strain relieving and application of a tensile coating.
  • a tensile coating For improving the core loss property of the product, it is preferable to subject it to magnetic domain control using a laser beam or the like.
  • the final product sheet is required to have an Si content by weight of 2.5 - 4.5 %. At a content below 2.5 %, it is hard to obtain a good core loss property, while at a content above 4.5 % there arises a problem of brittleness during ordinary cold rolling.
  • the product according to this invention is thick. Specifically it has a thickness of 0.36 - 1.00 mm.
  • a sheet of a thickness of less than 0.36 mm may in some cases be able to achieve a good core loss property without satisfying the conditions of this invention.
  • a sheet exceeding 1.00 mm is undesirable because the time required for decarburization to the level required by the invention becomes so long as to cause an intolerable increase in production cost.
  • the product has to have a C content of not greater than 0.0050 % and a flux density B8 of not less than 1.83 T. This is because, as shown in Fig. 1, these are the ranges required for obtaining a good core loss property.
  • a C content of not more than 0.0030% is preferred.
  • the shape factors SF representing the boundary configuration characteristics of the sheet grains with the same area as the circle with diameter exceeding 5 mm has are required to have an average value (an average value for the sheet called the "SF (average value)") of less than 0.80.
  • the invention is not limited to any particular method for controlling the SF value and it is possible to select from among control of the primary recrystallization grain diameter before occurrence of secondary recrystallization, use of a grain boundary segregation elements such as Sn, and adjustment of inhibitor strength during secondary recrystallization.
  • the invention is not limited to any particular method for controlling the ⁇ value and it is possible either to conduct final finish annealing with respect to a coil of a diameter suitable for the product grain diameter or to use the heat history between solidification and slab heating to control the slab grain size.
  • the presence of the prescribed crystal orientation deviation in even a single grain results in an improvement in core loss property.
  • the magnetic flux density control, the grain boundary configuration control and the in-grain crystal orientation deviation control By utilizing the combined effect of the product sheet C content control, the magnetic flux density control, the grain boundary configuration control and the in-grain crystal orientation deviation control according to this invention, it is possible to obtain a thick grain-oriented electrical steel sheet exhibiting excellent magnetic properties.
  • the invention can therefore be expected to make a highly significant contribution to industry.
  • a slab comprising, by weight, 0.053 % C, 3.26 % Si, 0.15 % Mn, 0.006 % S, 0.029 % acid-soluble Al, 0.0076 % N and the balance Fe and unavoidable impurities was heated at 1150 °C and then hot rolled into a 2.8 mm hot-rolled sheet.
  • the hot-rolled sheet was annealed by being held at 1120 °C and then at 900 °C, the annealed sheet was subjected to cold rolling at a reduction ratio of about 86 % to a thickness of 0.38 mm.
  • One portion of the sheet (1) was decarburization-annealed at 800 °C for 150 sec, a second portion (2) at 830 °C for 150 sec, and a third portion (3) at 860 °C for 200 sec, (atmosphere: 25 % N2 and 75 % H2; dew point: 65 °C).
  • the annealed sheets were then subjected to nitriding treatment by annealing at 750 °C for 30 sec in an annealing atmosphere containing NH3 gas.
  • the N content of the sheets after the nitriding treatment was 0.0195 - 0.0211 wt %.
  • the sheets were then coated with an annealing separation agent consisting mainly of MgO, rolled into 5-ton coils having an inside diameter of 600 mm and then subjected to final finish annealing in which they were heated to 1200 °C at 15 °C/hr and held at 1200 °C for 20 hr.
  • a first slab (1) comprising 0.045 % C, 3.01 % Si, 0.14 % Mn, 0.008 % S, 0.035 % acid-soluble Al, 0.0061 % N, 0.05 % Sn and the balance Fe and unavoidable impurities and a second slab (2) of the same composition except that the Sn content was less than 0.01 % were heated at 1150 °C and hot rolled to a thickness of 2.3 mm.
  • the hot-rolled sheets were subjected to cold rolling at a reduction ratio of about 79 % to a thickness of 0.48 mm.
  • the cold rolled sheets were annealed at 830 °C for 300 sec (atmosphere: 25 % N2 and 75 % H2; dew point: 62 °C) and were thereafter treated under the same conditions as those of Example 1.
  • the thickness of the final product sheets was 0.50 mm. Table 2 shows the property values of the sheets treated under the respective conditions.
  • a first slab (1) comprising 0.078 % C, 3.21 % Si, 0.12 % Mn, 0.009 % S, 0.034 % acid-soluble Al, 0.0060 % N and the balance Fe and unavoidable impurities, a second slab (2) of the same composition except that the C content was 0.053 %, and a third slab (3) of the same composition except that the C content was 0.039 % were heated at 1200 °C and hot rolled to a thickness of 3.0 mm.
  • the hot-rolled sheets were subjected to cold rolling at a reduction ratio of about 81 % to a thickness of 0.58 mm.
  • the cold rolled sheets were annealed at 830 °C for 450 sec (atmosphere: 25 % N2 and 75 % H2; dew point: 62 °C) and were thereafter treated under the same conditions as those of Example 1.
  • the thickness of the final product sheets was 0.60 mm.
  • Table 3 shows the property values of the sheets treated on the respective conditions.
  • Table 3 Product Sheet Properties Processing conditions C (%) B8 (T) SF ⁇ (deg) W 17/50 (w/kg) Remarks (1) 0.0058 1.82 0.60 1.3 2.41 Comparison (2) 0.0026 1.90 0.57 1.1 1.70 Invention (3) 0.0015 1.86 0.65 2.4 1.89 Invention Remark: SF and ⁇ are the average values defined in the text.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Electromagnetism (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Manufacturing & Machinery (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Dispersion Chemistry (AREA)
  • Power Engineering (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)
  • Soft Magnetic Materials (AREA)
EP93114263A 1992-09-04 1993-09-06 Dicke kornorientierte Elektrostahlbleche mit hervorragenden magnetischen Eigenschaften Revoked EP0585956B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP4237150A JP2659655B2 (ja) 1992-09-04 1992-09-04 磁気特性の優れた厚い板厚の方向性電磁鋼板
JP237150/92 1992-09-04

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EP0585956A1 true EP0585956A1 (de) 1994-03-09
EP0585956B1 EP0585956B1 (de) 1998-01-07

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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US7736444B1 (en) 2006-04-19 2010-06-15 Silicon Steel Technology, Inc. Method and system for manufacturing electrical silicon steel

Families Citing this family (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US7282102B2 (en) * 2002-11-11 2007-10-16 Posco Method for manufacturing high silicon grain-oriented electrical steel sheet with superior core loss property
JP2016086611A (ja) 2014-10-29 2016-05-19 三菱電機株式会社 回転電機のステータコア冷却構造

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE3538609A1 (de) * 1984-10-31 1986-05-07 Nippon Steel Corp., Tokio/Tokyo Verfahren zur herstellung von kornorientiertem elektrostahlblech
EP0219611B1 (de) * 1985-08-15 1990-05-16 Nippon Steel Corporation Verfahren zur Herstellung eines kornorientierten Elektro-Stahlblechs
EP0378131A2 (de) * 1989-01-07 1990-07-18 Nippon Steel Corporation Verfahren zum Herstellen eines kornorientierten Elektrostahlbandes
EP0390142A2 (de) * 1989-03-30 1990-10-03 Nippon Steel Corporation Verfahren zum Herstellen kornorientierter Elektrobleche mit hoher magnetischer Flussdichte
EP0539858A1 (de) * 1991-10-28 1993-05-05 Nippon Steel Corporation Verfahren zur Herstellung kornorientierter elektrischer Stahlbänder mit magnetischer Permeabilität

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JPH0372027A (ja) * 1989-08-11 1991-03-27 Nippon Steel Corp 鉄損の優れた高磁束密度一方向性電磁鋼板の製造方法

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Publication number Priority date Publication date Assignee Title
DE3538609A1 (de) * 1984-10-31 1986-05-07 Nippon Steel Corp., Tokio/Tokyo Verfahren zur herstellung von kornorientiertem elektrostahlblech
EP0219611B1 (de) * 1985-08-15 1990-05-16 Nippon Steel Corporation Verfahren zur Herstellung eines kornorientierten Elektro-Stahlblechs
EP0378131A2 (de) * 1989-01-07 1990-07-18 Nippon Steel Corporation Verfahren zum Herstellen eines kornorientierten Elektrostahlbandes
EP0390142A2 (de) * 1989-03-30 1990-10-03 Nippon Steel Corporation Verfahren zum Herstellen kornorientierter Elektrobleche mit hoher magnetischer Flussdichte
EP0539858A1 (de) * 1991-10-28 1993-05-05 Nippon Steel Corporation Verfahren zur Herstellung kornorientierter elektrischer Stahlbänder mit magnetischer Permeabilität

Non-Patent Citations (4)

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Title
CHEMICAL ABSTRACTS, vol. 106, no. 22, June 01, 1987, Columbus, Ohio, USA KOBAYASHI, YASUHIRO et al. "Magnetic oriented silicon steel sheets." page 271, column 1, abstract- -no. 180 666K *
CHEMICAL ABSTRACTS, vol. 115, no. 12, September 23, 1991, Columbus, Ohio, USA KOBAYASHI, TAKASHI et al. "Manufacture of unidirectio- nal steel sheets having desird magnetic flux density for electromagnetic cores." page 239, column 2, abstract- -no. 118 412g *
CHEMICAL ABSTRACTS, vol. 116, no. 4, January 27, 1992, Columbus, Ohio, USA NAKAJIMA, SHOZABURO et al. "Manufacture of unidirectio- nal steel sheets for electro- magnetic cores having decreased magnetic loss." page 292, column 2, abstract- -no. 25 611b *
PATENT ABSTRACTS OF JAPAN, unexamined applications, C field, vol. 16, no. 261, June 12, 1992 THE PATENT OFFICE JAPANESE GOVERNMENT page 68 C 950 *

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US7736444B1 (en) 2006-04-19 2010-06-15 Silicon Steel Technology, Inc. Method and system for manufacturing electrical silicon steel

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JP2659655B2 (ja) 1997-09-30
JPH0688170A (ja) 1994-03-29
EP0585956B1 (de) 1998-01-07
DE69316114T2 (de) 1998-04-23
DE69316114D1 (de) 1998-02-12

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