EP0438592A1 - Herstellungsverfahren von elektroblechen mit goss-textur, die ausgezeichnete eisenverlustwerte und hohe flussdichte haben - Google Patents

Herstellungsverfahren von elektroblechen mit goss-textur, die ausgezeichnete eisenverlustwerte und hohe flussdichte haben Download PDF

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Publication number
EP0438592A1
EP0438592A1 EP89909241A EP89909241A EP0438592A1 EP 0438592 A1 EP0438592 A1 EP 0438592A1 EP 89909241 A EP89909241 A EP 89909241A EP 89909241 A EP89909241 A EP 89909241A EP 0438592 A1 EP0438592 A1 EP 0438592A1
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Prior art keywords
steel sheet
flux density
annealing
iron loss
subjected
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EP89909241A
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English (en)
French (fr)
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EP0438592A4 (en
EP0438592B1 (de
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S. Nippon Steel Corp. R&D Lab.-Iii Nakashima
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Nippon Steel Corp
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Nippon Steel Corp
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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
    • C21D8/1294—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a localized treatment
    • 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
    • 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
    • C21D8/125—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 application of tension
    • 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
    • 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
    • C21D8/1277—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular surface treatment
    • C21D8/1288—Application of a tension-inducing coating

Definitions

  • the present invention relates to a method of producing a grain oriented electrical steel sheet having a high magnetic flux density and a very low iron loss, wherein a magnetic domain control is carried out at the surface of the steel sheet.
  • a method of reducing iron loss by carrying out an artificial magnetic domain control on the surface of a grain oriented electrical steel sheet having a high magnetic flux density in the direction substantially at a right angle relative to the rolling direction is known.
  • the foregoing method is disclosed in, e.g., official gazettes of Japanese Unexamined Patent Publication No. 18566/1980 and Japanese Unexamined Patent Publication No. 73724/1983, entitled "A Method of Irradiating a Laser Light Beam with a Distance Kept Between the Adjacent Laser Light Beams," an official gazette of Japanese Unexamined Patent Publication No.
  • the inventor conducted research and development work into the development of a grain oriented electrical steel sheet having the required properties, and as a result of this research and development work, found that a remarkably good reduction of iron loss can be obtained with respect to a grain oriented electrical steel sheet having a high magnetic flux density, by carrying out a control to allow an average grain size of each secondarily recrystallized grain to remain within a predetermined range wherein the grain oriented electrical steel sheet is treated such that it is covered with a layer of tension coating and a magnetic domain control is carried out therefor in the direction substantially at a right angle relative to the rolling direction, after completion of the secondary recrystallization, whereby, the present invention was created.
  • the present invention provides a method of producing a grain oriented electrical steel sheet having a very good reduction of iron loss while a magnetic flux density is kept higher than 1.88T in the presence of a magnetizing force of 800 A/m, wherein the method is practiced such that a finally cold rolled steel sheet is subjected to annealing for decarburization, wound in the form of a coil while coated with a separating agent for an annealing operation, subjected to finish annealing at a high temperature, then subjected to flattening annealing with the separating agent removed therefrom, thereafter, before or after completion of the flattening annealing operation, covered with a film of tension coating to allow an intensity of tension per an unit sectional area of the steel sheet to be kept higher than 0.7 kg/mm2, and moreover, before or after completion of the tension coating operation or the flattening annealing operation, an artificial magnetic domain control is carried out for the surface of the steel sheet, wherein the method is characterized in that an average grain size of
  • Steel sheets each containing Si of 3.2% and having one or two or more selected from a group of materials, i.e., MnS, MnSe, CuxS, Sn and Sb utilized therefor as an inhibitor in addition to AlN were finally cold rolled to a thickness of 0.17 m/m, and subsequently, were subjected to annealing for decarburization and then coated with a separator utilized for an annealing. Then, the sheets were subjected to finish annealing at a high temperature while held in the flat state, and after completion of the finish annealing operation, the separator was removed from each of the steel sheets, whereby various kinds of grain oriented electrical steel sheets were produced.
  • a group of materials i.e., MnS, MnSe, CuxS, Sn and Sb utilized therefor as an inhibitor in addition to AlN
  • each of the resultant grain oriented electrical steel sheets was covered with a film of tensile coating, to allow an intensity of tension per an unit sectional area of each grain oriented electrical steel sheet to be maintained at a level of 1.0 kg/mm2.
  • a pulsed laser light beam was irradiated to the surface of each grain oriented electrical steel sheet in the direction at a right angle relative to the rolling direction under conditions of an energy density of 2.0 J/cm2, an irradiation width of 0.25 m/m and an irradiation distance of 5 m/m.
  • a magnetic flux density B8 (magnetic flux density in the presence of a magnetizing force of 800 A/m) and an iron loss W 15/50 were measured with respect to the respective grain oriented electrical steel sheets.
  • a grain size of each secondarily recrystallized grain in the rolling surface was measured by employing a line segment method with respect to three directions, i.e., the rolling direction, the direction of 45 degrees relative to the rolling direction and the direction at a right angle relative to the rolling direction, whereby an average grain size was determined with respect to the respective grain oriented electrical steel sheets (it should be noted that an average grain size determined for carrying out the present invention with respect to all the grain oriented electrical steel sheets was measured by employing the aforementioned method).
  • a relationship among the average grain size, the magnetic flux density B8 and the iron loss W 15/50 is illustrated in Fig. 1.
  • the abscissa designates an average grain size and the ordinate designates a magnetic flux density B8.
  • four marks i.e., a double circle mark, a single circle mark, a triangular mark and a X-shaped mark designate an iron loss W 15/50, respectively.
  • the abscissa designates an average grain size and the ordinate designate a magnetic flux density B8.
  • the respective steel sheets were annealed while the opposite surfaces thereof were oriented in the vertical direction and they were normally held in the wound state in the form of a coil, because the finish annealing operation at a high temperature took a long time while they were kept at a high temperature.
  • a radius of curvature as measured along the inner periphery of each coil was smaller than about 400 m/m during the finish annealing operation at a high temperature. This is because if a radius of curvature is larger, the installation is unavoidably enlarged, resulting in grain oriented electrical steel sheets disadvantageously produced at a high cost.
  • Silicon steel slabs each containing C of 0.065%, Si of 3.0%, Mn of 0.075%, S of 0.025%, an acid soluble aluminum of 0.0260%, N of 0.0085% and a residual of unavoidably contained elements were heated at a temperature of 1,350°C for 120 minutes and then hot rolled to have a thickness of 1.1 to 5.0 m/m.
  • the hot rolled steel plates were annealed at a temperature of 1,120°C for 2 minutes and then cooled down to 300°C at a cooling rate of 30°C/sec.
  • the finish annealing at a high temperature was performed such that the atmosphere comprising H2 of 75% and N2 of 25% was maintained during elevation of the working temperature, the working temperature was elevated up to 1,200°C at an elevating rate of 15°C/hour and the cold rolled steel sheets were then annealed at a temperature of 1,200°C for 20 hours in a hydrogen atmosphere. Thereafter, a magnetic flux density B8 and an average grain size of each secondarily recrystallized grain were measured with respect to the respective products of grain oriented electrical steel sheets. A relationship among a reduction ratio of the cold rolling, the magnetic flux density B8 and the average grain size is illustrated in Fig. 3.
  • the abscissa designates a reduction ratio of the cold rolling and the ordinate designates a magnetic flux density and an average grain size.
  • the grain oriented electrical steel sheet each having excellent properties such that the reduction ratio of the cold rolling remains within 83 to 92%, the average grain size ranges from 11 to 50 m/m and the magnetic flux density is kept higher than 1.88T can be obtained.
  • the grain oriented electrical steel sheets each having a high magnetic flux density and a very low value of iron loss can be obtained by allowing the respective grain oriented electrical steel sheets (derived from, e.g., Experiment III) having excellent properties such that the average grain size ranges from 11 to 50 m/m and the magnetic flux density is kept higher than 1.88T to be covered with a layer of tension coating which assures an intensity of tension higher than 0.7 kg/mm2 and then treating the surface of each of the grain oriented electrical steel sheets under an artificial magnetic domain control.
  • the respective grain oriented electrical steel sheets derived from, e.g., Experiment III
  • the magnetic flux density is kept higher than 1.88T
  • the carbon content is lower than 0.12%, as if it exceeds 0.12%, it becomes difficult to accomplish decarburizaiton during an annealing operation to be performed for the purpose of decarburization.
  • the silicon content remains within 2.5 to 4.5%, as if it is lower than 2.5%, each grain oriented electrical steel sheet fails to show a very good reduction of iron loss. If it exceeds 4.5%, the workability is deteriorated.
  • the manganese content remains within 0.030 to 0.200%, as if lower than 0.030%, the workability is deteriorated. If it exceeds 0.200%, the grain oriented electrical steel sheets do not show a very good reduction of iron loss.
  • the total content of one or both of sulfur and selenium remains within 0.01 to 0.06%, as if it is lower than 0.01% or exceeds 0.06%, the grain oriented electrical steel sheets do not show a very good reduction of iron loss.
  • the acid soluble aluminum has a content which remains within 0.010 to 0.050%, as if lower than 0.010%, the grain oriented electrical steel sheets do not have an excellent property of magnetic flux density. If it exceeds 0.050%, the secondary recrystallization is accomplished incorrectly.
  • the nitrogen content remains within 0.0030 to 0.0100%, as if it is lower than 0.0030%, the secondary recrystallization is accomplished incorrectly. If it exceeds 0.0100%, a flaw in the form of a blister appears on the surfaces of the grain oriented electrical steel sheets.
  • the grain oriented electrical steel sheet does not have an excellent magnetic property unless it is at least once annealed at a temperature of from 1,050 to 1,200°C and then quickly cooled until a final cold rolling is performed after completion of the hot rolling.
  • An intensity of tension per unit sectional area of each grain oriented electrical steel sheet appearing in the presence of a surface film (inclusive of forstelite) should be kept higher than 0.7 kg/mm2, as if lower than 0.7 kg/mm2, the grain oriented electrical steel sheets do not show a very good reduction of iron loss.
  • the magnetic flux density is made higher than 1.88T while a magnitude of magnetizing force is maintained at a level of 800 A/m, the grain oriented electrical steel sheets show a very good reduction of iron loss. If the magnetic flux density is made lower than 1.88T, the grain oriented electrical steel sheets do now show a very good reduction of iron loss.
  • each grain oriented electrical steel sheet exhibits a very good reduction of iron loss when produced under conditions such that the average grain size of each secondarily recrystallized grain remains within 11 to 50 m/m
  • the surface of each grain oriented electrical steel sheet is coated with a film which ensures that the intensity of tension per an unit sectional area thereof is kept higher than 0.7 kg/mm2
  • the magnetic flux density is kept higher than 1.88T while the magnitude of magnetizing force is maintained at the level of 800 A/m and artificial magnetic domain control is carried out for the surface of each grain oriented electrical steel sheet in the direction at a substantially right angle relative to the rolling direction.
  • deviation of a Goss orientation from the rolling surface or the like malfunction due to the flattening annealing performed after completion of the annealing at a high temperature is concerned with undesirable reduction of the magnetic flux density at the time when the average grain size exceeds 50 m/m.
  • grain oriented electrical steel sheets each having excellent properties such that the magnetic flux density B8 is kept higher than 1.88T and the average grain size of each secondarily recrystallized grain remains within 11 to 50 m/m while a substance of AlN is utilized therefor as a main inhibitor can be produced under conditions such that they are at least once annealed at a temperature of from 1,050 to 1,200°C until a final cold rolling is performed after completion of the hot rolling, are quickly cooled after completion of the annealing and are then subjected to final cold rolling at a reduction ratio of 83 to 92%.
  • Silicon steel slabs each containing C of 0.080%, Si of 3.2%, Mn of 0.075%, an acid soluble aluminum of 0.0250% and N of 0.0085% and moreover containing one or two or more selected from a group of elements, i.e., S of 0.025% or 0.015%, Se of 0.020%, Sn of 0.12%, Cu of 0.07% and Sb of 0.020% were heated at a temperature of 1,350°C for 120 minutes so that they were hot rolled to provide hot rolled plates each having a thickness of 0.9 to 4.4 m/m.
  • the hot rolled plates were annealed at various temperature within the range from 1,000 to 1,220°C and then cooled down to 300°C at a cooling rate of 35°C/sec. Thereafter, they were subjected to final cold rolling in accordance with a production process I or II to be described later. Specifically, in a case of the production process I, the hot rolled sheets were subjected to final cold rolling immediately after completion of the annealing operation therefor.
  • the hot rolled plates were annealed, they were subjected to intermediate cold rolling to have a predetermined thickness, respectively, they were then annealed at a temperature of 1,000°C for 100 seconds and, thereafter, they were cooled down to 300°C at a cooling rate of 25°C/sec. Subsequently, they were subjected to final cold rolling.
  • the hot rolled sheets were subjected to annealing for decarburizaiton at a temperature of 850°C for 3 minutes in a wet atmosphere comprising H2 of 75% and N2 of 25%, they were then coated with a separator containing a magnesia as a main component for the annealing operation and thereafter, they were wound in the form of a coil having a radius of curvature of about 400 m/m, respectively, so that they were subjected to finish annealing at a high temperature.
  • the atmosphere comprising H2 of 75% and N2 of 25% was maintained during elevation of the working temperature and they were heated up to a temperature of 1,200°C at an elevating rate of 15°C/hour so that they were annealed at a temperature of 1,200°C for 20 hours in a hydrogen atmosphere.
  • the separating agent utilized for the annealing operation was removed and a magnetic domain control treatment, a tension coating operation, an annealing operation and others were then performed in accordance with one of four kinds of methods, i.e., an A method, a B method, a C method and a D method each of which will be described later.
  • the tension coating operation was performed for the respective steel sheets such that an intensity of tension per an unit sectional area of each steel sheet was set to 1.0 kg/mm2. Then, they were subjected to flattening annealing at a temperature of 850 ° C for 30 seconds in additional consideration for baking the layer of tension coating. Subsequently, a pulsed laser light beam was irradiated to the surface of each steel sheet in the direction at a right angle relative to the rolling direction under conditions of an energy density of 2.0 J/cm2, an irradiation width of 0.25 m/m and irradiation distance of 5 m/m.
  • each steel sheet was coated with antimony powder after it was treated in accordance with the A method. Thereafter, it was annealed at a temperature of 800 ° C for 2 hours.
  • a pulse laser light beam was irradiated to the surface of each steel sheet in the direction at a right angle relative to the rolling direction under conditions of an energy density of 3.0 J/cm2, an irradiation width of 0.2 m/m and an irradiation distance of 5 m/m so as to partially remove the forstelite layer from the surface of each steel sheet.
  • the steel sheet was immersed in a nitric acid solution having a concentration of 61% for 20 seconds.
  • a tension coating was performed for the steel sheet such that an intensity of tension per an unit sectional area of the steel sheet was maintained at a level of 1.0 kg/mm2.
  • the steel sheet was subjected to flattening annealing at a temperature of 850 ° C for 30 seconds in additional consideration for baking the tension coating layer.
  • the magnetic flux density B8 and the iron loss were measured.
  • the surface film was removed from the steel sheet which in turn was washed in an acid solution so that an average grain size of each secondarily recrystallized grain in the rolling surface was measured.
  • Components in each steel sheet, a thickness of each hot rolled sheet, a production process (I or II), a soaking temperature during an annealing for hot rolled sheets, a thickness of each steel sheet after completion of an intermediate cold rolling, a thickness of each steel sheet after completion of a final cold rolling, a reduction ratio for the final rolling, an average grain size of each secondarily recrystallized grain, a magnetic domain controlling method (A, B, C or D), a magnetic flux density B8 and an iron loss are shown in Table 1, respectively.
  • the present invention makes it possible to provide a ferrous material having a remarkable low iron loss which is preferably employable for a core or the like in a transformer. Consequently, an energy loss in the transformer or the like electric equipment can be substantially reduced by using the ferrous material of the present invention.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Manufacturing & Machinery (AREA)
  • Electromagnetism (AREA)
  • Mechanical Engineering (AREA)
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  • Manufacturing Of Steel Electrode Plates (AREA)
  • Soft Magnetic Materials (AREA)
EP89909241A 1988-02-16 1989-08-15 Herstellungsverfahren von elektroblechen mit goss-textur, die ausgezeichnete eisenverlustwerte und hohe flussdichte haben Revoked EP0438592B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP63033320A JPH0768580B2 (ja) 1988-02-16 1988-02-16 鉄損の優れた高磁束密度一方向性電磁鋼板
PCT/JP1989/000826 WO1991002823A1 (en) 1988-02-16 1989-08-15 Production method of unidirectional electromagnetic steel sheet having excellent iron loss and high flux density

Publications (3)

Publication Number Publication Date
EP0438592A1 true EP0438592A1 (de) 1991-07-31
EP0438592A4 EP0438592A4 (en) 1993-10-20
EP0438592B1 EP0438592B1 (de) 1996-05-08

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Application Number Title Priority Date Filing Date
EP89909241A Revoked EP0438592B1 (de) 1988-02-16 1989-08-15 Herstellungsverfahren von elektroblechen mit goss-textur, die ausgezeichnete eisenverlustwerte und hohe flussdichte haben

Country Status (4)

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EP (1) EP0438592B1 (de)
JP (1) JPH0768580B2 (de)
DE (1) DE68926457T2 (de)
WO (1) WO1991002823A1 (de)

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0398114A2 (de) † 1989-05-13 1990-11-22 Nippon Steel Corporation Verfahren zur Herstellung von dünnen kornorientierten Elektroblechen mit geringen Eisenverlusten und hoher Flussdichte
EP0837148A2 (de) * 1996-10-21 1998-04-22 Kawasaki Steel Corporation Kornorientiertes elektromagnetisches Stahlblech
EP0892072A1 (de) * 1997-07-17 1999-01-20 Kawasaki Steel Corporation Kornorientiertes Elektrostahlblech mit ausgezeichneten magnetischen Eigenschaften und dessen Herstellungsverfahren
US9183984B2 (en) 2010-08-06 2015-11-10 Jfe Steel Corporation Grain oriented electrical steel sheet and method for manufacturing the same

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KR101141281B1 (ko) * 2004-12-28 2012-05-04 주식회사 포스코 후물 방향성 전기강판의 제조방법
JP6003197B2 (ja) * 2012-05-07 2016-10-05 Ｊｆｅスチール株式会社 磁区細分化処理方法
JP7031364B2 (ja) * 2018-02-26 2022-03-08 日本製鉄株式会社 方向性電磁鋼板の製造方法
CN108787940B (zh) * 2018-07-31 2023-12-12 立洲（青岛）五金弹簧有限公司 一种ω夹、ω夹的成型装置及成型方法

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EP0234443B1 (de) * 1986-02-14 1995-08-02 Nippon Steel Corporation Verfahren zum Herstellen kornorientierter Elektrobleche aus Stahl mit magnetischen Eigenschaften

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JPS6144131A (ja) * 1984-08-08 1986-03-03 Nippon Steel Corp 磁区制御された極超低鉄損方向性電磁鋼板の製造方法
JPS61133321A (ja) * 1984-11-30 1986-06-20 Nippon Steel Corp 超低鉄損方向性電磁鋼板の製造方法
JPS6250413A (ja) * 1985-08-30 1987-03-05 Kawasaki Steel Corp 方向性珪素鋼帯の平たん化焼鈍方法
JPS6254085A (ja) * 1985-08-31 1987-03-09 Kawasaki Steel Corp 一方向性珪素鋼鈑のフオルステライト絶縁被膜形成方法
JPS6256923A (ja) * 1985-09-06 1987-03-12 Ricoh Co Ltd 光アイソレ−タ−
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FR2007129A1 (de) * 1968-04-27 1970-01-02 Yawata Iron & Steel Co
FR2194788A1 (de) * 1972-08-01 1974-03-01 Nippon Steel Corp
FR2236009A1 (de) * 1973-06-18 1975-01-31 Nippon Steel Corp
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Cited By (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0398114A2 (de) † 1989-05-13 1990-11-22 Nippon Steel Corporation Verfahren zur Herstellung von dünnen kornorientierten Elektroblechen mit geringen Eisenverlusten und hoher Flussdichte
EP0398114B2 (de) † 1989-05-13 2001-12-19 Nippon Steel Corporation Verfahren zur Herstellung von dünnen kornorientierten Elektroblechen mit geringen Eisenverlusten und hoher Flussdichte
EP0837148A2 (de) * 1996-10-21 1998-04-22 Kawasaki Steel Corporation Kornorientiertes elektromagnetisches Stahlblech
EP0837148A3 (de) * 1996-10-21 1998-07-15 Kawasaki Steel Corporation Kornorientiertes elektromagnetisches Stahlblech
US6083326A (en) * 1996-10-21 2000-07-04 Kawasaki Steel Corporation Grain-oriented electromagnetic steel sheet
US6444050B1 (en) 1996-10-21 2002-09-03 Kawasaki Steel Corporation Grain-oriented electromagnetic steel sheet
US6929704B2 (en) 1996-10-21 2005-08-16 Jfe Steel Corporation Grain-oriented electromagnetic steel sheet
EP0892072A1 (de) * 1997-07-17 1999-01-20 Kawasaki Steel Corporation Kornorientiertes Elektrostahlblech mit ausgezeichneten magnetischen Eigenschaften und dessen Herstellungsverfahren
US6110298A (en) * 1997-07-17 2000-08-29 Kawasaki Steel Corporation Grain-oriented electrical steel sheet excellent in magnetic characteristics and production process for same
US9183984B2 (en) 2010-08-06 2015-11-10 Jfe Steel Corporation Grain oriented electrical steel sheet and method for manufacturing the same

Also Published As

Publication number Publication date
WO1991002823A1 (en) 1991-03-07
JPH01208421A (ja) 1989-08-22
EP0438592A4 (en) 1993-10-20
DE68926457D1 (de) 1996-06-13
EP0438592B1 (de) 1996-05-08
JPH0768580B2 (ja) 1995-07-26
DE68926457T2 (de) 1997-01-02

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