EP0611829A1 - Verfahren zum Herstellen von rauscharmen kornorientierten Siliziumstahlblechern mit niedrigen Wattverlusten und mit hervorragenden Formeigenschaften - Google Patents

Verfahren zum Herstellen von rauscharmen kornorientierten Siliziumstahlblechern mit niedrigen Wattverlusten und mit hervorragenden Formeigenschaften Download PDF

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Publication number
EP0611829A1
EP0611829A1 EP9393102347A EP93102347A EP0611829A1 EP 0611829 A1 EP0611829 A1 EP 0611829A1 EP 9393102347 A EP9393102347 A EP 9393102347A EP 93102347 A EP93102347 A EP 93102347A EP 0611829 A1 EP0611829 A1 EP 0611829A1
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Prior art keywords
steel sheet
silicon steel
grain oriented
oriented silicon
electron beam
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French (fr)
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EP0611829B1 (de
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Yukio C/O Technical Research Division Inokuti
Kazuhiro C/O Technical Research Division Suzuki
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JFE Steel Corp
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Kawasaki Steel Corp
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Priority to DE1993631221 priority Critical patent/DE69331221T2/de
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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
    • C21D2221/00—Treating localised areas of an article

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  • This invention relates to a method of producing, by employing electron beam irradiation, a low iron loss grain oriented silicon steel sheet which generates improved magnetostrictive characteristics when used as a stacked iron core and low noise when used in a stacked transformer, as well as superior shape characteristics.
  • Grain oriented silicon steel sheets are used mainly as the core materials of electrical components such as transformers or the like.
  • grain oriented silicon steel sheets are required to have such magnetic characteristics that the magnetic flux density (represented by B8) is high and that the iron loss (represented by W 17/50 ) is low. It is also required that the surfaces of the steel sheet have insulating films with excellent surfaces.
  • Grain oriented silicon steel sheets have undergone various treatments for improving magnetic characteristics. For instance, treatment has been conducted to attain a high degree of concentration of the secondary recrystallization grains in the Goss orientation. It has also been attempted to form, on a forsterite film formed on the surface of the steel sheet, an insulating film having a small thermal expansion coefficient so as to impart a tensile force to the steel sheet. Thus, grain oriented silicon steel sheets have been produced through complicated and diversified processes which require very strict controls.
  • This method exhibits very high energy efficiency, as well as high scanning speed, thus offering remarkably improved production efficiency as compared to known methods for refining magnetic domains.
  • the methods disclosed in our above-mentioned Japanese Patent Laid-Open specifications are directed to production of grain oriented silicon steel sheet for use as a material for a wound core transformer.
  • the wound core formed from a grain oriented steel sheet is subjected to stress-relieving annealing. Therefore, no substantial noise tends to be generated in the wound core transformer during operation of the transformer.
  • a stacked transformer of that kind generates a high level of noise, requiring strong measures to be taken for reducing the noise.
  • United States Patent No. 4,919,733 discloses a method for refining magnetic domains by irradiation with electron beams, wherein the surface energy density on the electron beam scan line is set to a level not lower than 60 J/in2 (9.3J/cm2).
  • Steel sheets which have undergone this electron beam treatment exhibit inferior noise characteristics when employed in a stacked transformer, as compared with steel sheets which have not undergone such electron beam treatment.
  • the noise characteristics are extremely poor during operation of the transformer after the electron beam treatment has been conducted under the conditions mentioned above, as compared with sheets which have not undergone such treatment.
  • United States Patent No. 4,915,750 proposes a method of producing a grain oriented silicon steel sheet for use as a material of a wound core transformer, employing refining of magnetic domains by irradiation with an electron beam. This method is directed only to the production of a wound core transformer as distinguished from a stacked transformer to which the present invention pertains and which suffers from the noise problem.
  • an object of the present invention is to provide a method for producing a grain oriented steel sheet of high quality which generates not only low iron loss but also improved magnetostrictive and noise characteristics, as well as superior shape characteristics, thereby overcoming the above-described problems of the known art.
  • a method of producing a low iron loss grain oriented silicon steel sheet which generates improved magnetostrictive characteristic when used as a stacked iron core and low noise when used in a stacked transformer, as well as superior shape characteristic, comprising the steps of: preparing a grain oriented finish-annealed silicon steel sheet; forming an insulating film on a surface of said grain oriented silicon steel sheet; and irradiating said surface of said grain oriented silicon steel sheet with an electron beam along a multiplicity of spaced paths so as to refine the magnetic domains; wherein the irradiation with said electron beam is conducted continuously or intermittently along a wave-form path on the surface of said grain oriented silicon steel, said wave-form having a period length much smaller than the width of said grain oriented silicon steel sheet and the line interconnecting the centers of the successive waves extends substantially perpendicularly to the direction of rolling of said grain oriented silicon steel sheet.
  • Fig. 1 shows an electron beam irradiation apparatus employed in the experiment.
  • the electron beam irradiation apparatus has a vacuum chamber 1 which has evacuating ports 1a, 1b and which maintains vacuum preferably at a high level of 10 ⁇ 2 Torr or lower.
  • Numeral 2 designates a high-tension insulator
  • numeral 3 designates an electron gun which emits electrons.
  • Numeral 4 denotes an anode disposed to oppose the electron gun 3 so as to accelerate the electrons emitted from the electron gun 3.
  • Numeral 6 denotes a column valve which serves to maintain a high level of vacuum in the region where the electron beam is generated, while 7 designates a condenser lens for condensing the electron beam 5.
  • Numeral 8 designates a biasing coil which biases and deflects the direction of the electron beam 5 condensed by the condenser lens 7 in a wavy or zigzag form, thus making it possible to irradiate a grain oriented silicon steel sheet with the electron beam along a wavy or zigzag form.
  • the electron beam irradiation apparatus has means for selecting irradiation mode between an intermittent irradiation mode and a continuous irradiation mode.
  • a silicon steel slab was prepared having a composition containing C: 0.082 wt%, Si: 3.54 wt%, Mn: 0.82 wt%, Mo: 0.013 wt%, sol.Al: 0.028 wt%, Se: 0.021 wt% and Sb: 0.022 wt%.
  • the slab was heated for 3 hours at 1380°C, followed by hot rolling, whereby a hot-rolled sheet 2.2 mm thick was obtained.
  • the hot-rolled slab was then subjected to a cold rolling and a subsequent annealing conducted for 3 minutes at 1050 °C, followed by a second cold rolling, whereby a final cold-rolled sheet of 0.23 mm thick was obtained.
  • This final cold-rolled sheet was then subjected to decarburization and primary recrystallization annealing conducted in wet hydrogen atmosphere of 840 °C.
  • an annealing separation agent in the form of a slurry composed mainly of MgO was applied to the surface of the steel sheet, and secondary recrystallization annealing was conducted either in accordance with a cycle A or B shown below, followed by a purification annealing.
  • the temperature of the steel sheet was raised at a rate of 10 °C/h and the secondary crystallization annealing was conducted for 50 hours at 850 °C, allowing preferential growth of secondary recrystallization grain of Goss orientation. Then, purification annealing was conducted for 5 hours in a dry hydrogen atmosphere at 1220 °C.
  • the steel sheet was annealed for 15 hours at 850 °C and the temperature was raised to 1180 °C at a rate of 12 °C/hr to allow growth of Goss orientation secondary recrystallized grains. Then, purification annealing was executed for 5 hours in a dry hydrogen atmosphere at 1230 °C.
  • an insulating film mainly composed of a phosphate and colloidal silica was formed on each of the steel sheets, whereby two types of grain oriented silicon steel sheets were obtained.
  • the electron beam was applied along straight paths extending in the direction perpendicular to the direction of rolling of the steel sheet at a scanning pitch P1 of 6 mm.
  • Beam acceleration voltage 150 KV
  • Beam current 1.0 mA
  • Beam diameter 0.20 mm
  • Energy density 6.0 J/cm2 Scanning velocity: 1250 cm/sec
  • the electron beam was applied intermittently so as to irradiate apices 2 and bottoms 3 of the zigzag wave 1.
  • the centers of the consecutive circles show the points irradiated with the electron beam.
  • the zigzag path of the beam was so determined to have an amplitude H of 0.35 mm, a period length of 0.6 mm and a scanning pitch P2 of 6 mm.
  • the angle ⁇ of inclination of the zigzag wave with respect to the direction perpendicular to the steel sheet rolling direction was 18.4°.
  • Beam acceleration voltage 150 KV
  • Beam current 1.0 mA
  • Beam diameter 0.25 mm
  • Energy density 6.0 J/cm2 Scanning velocity: 1000 cm/sec
  • the magnetostrictive characteristic was evaluated on the basis of the exciting electric power which is usually expressed in terms of VA/Kg.
  • the noise (dB) of each transformer was measured by using a sound level meter specified by JIS (Japanese Industrial Standard) 1502 at positions directly above the three legs and at positions spaced 50 cm apart from the respective legs. Then, the mean values of the measured noise levels were calculated. The results of the measurement were evaluated by normalizing them to the values at 1.7 T/50 Hz. The noise measurement was conducted by using an A scale as specified by JIS 1502.
  • test pieces of 150 mm width were cut in a direction perpendicular to the rolling direction from each steel sheet before electron beam irradiation and from the steel sheet after electron beam irradiation. Then, each test piece was placed on a flat surface with its concave side facing upward, and one side edge of the test piece was pressed into contact with the flat surface as shown in Fig. 7. The distance t (mm) between the other side edge and the flat surface was measured and used as the index of the amount of warp or deflection. This amount will be referred to as "C" deflection.
  • the inventors also conducted an experiment to examine how the magnetostrictive characteristics, noise characteristics and shape characteristics are influenced by the energy density of the electron beam when the irradiation is conducted in a spot manner along a zigzag path.
  • the amplitude H of the zigzag wave was varied within the range between 0.35 and 0.80 mm.
  • the energy density also was varied within the range between 1 and 30 J/cm2.
  • the scanning pitch P2 was fixed at 6 mm.
  • Beam acceleration voltage 150 kV
  • Beam current 0.5 to 1.5 mA
  • Beam diameter 0.2 to 0.3 mm
  • the energy density is 60 J/in2 (9.3 J/cm2) or greater.
  • the present invention makes it possible to effectively refine the magnetic domains with an energy density level much lower than that employed in the above mentioned United States Patent.
  • the present invention improves not only the magnetic characteristics but also other important characteristics such as magnetostrictive characteristics, noise characteristics and steel shape characteristics of the sheet.
  • a silicon steel slab was prepared having a composition containing C: 0.079 wt%, Si: 3.36 wt%, Mn: 0.08 wt%, Mo: 0.012 wt%, sol.Al: 0.025 wt%, Se: 0.019 wt% and Sb: 0.025 wt%.
  • the slab was heated for 3 hours at 1360°C, followed by hot rolling, whereby a hot-rolled sheet of 2.2 mm thick was obtained.
  • the hot-rolled slab was then subjected to cold rolling and subsequent annealing conducted for 2 minutes at 1050 °C, followed by a second cold rolling, whereby a final cold-rolled sheet 0.23 mm thick was obtained.
  • This final cold-rolled sheet was then subjected to decarburization and primary recrystallization annealing conducted in a wet hydrogen atmosphere at 840 °C.
  • an annealing separation agent in the form of a slurry composed mainly of MgO was applied to the surface of the steel sheet, and the temperature of the steel sheet was raised at a rate of 10 °C/h and annealing was conducted for 15 hours at 850 °C. Then, the steel temperature was raised to 1180 °C at a rate of 12 °C/hr to allow preferential growth of the secondary recrystallized grains, followed by purification annealing which was conducted for 5 hours in a dry hydrogen atmosphere of 1220 °C.
  • an insulating film mainly composed of a phosphate and colloidal silica was formed on each of the steel sheets, whereby grain oriented silicon steel sheets were obtained.
  • the electron beam was applied intermittently so as to irradiate apices 2 and bottoms 3 of the zigzag wave 1.
  • the centers of the consecutive circles show the points irradiated with the electron beam.
  • the zigzag path of the beam was so determined to have an amplitude H of 0.23 mm, period length of 0.4 mm and a scanning pitch P2 of 6 mm.
  • the angle ⁇ of inclination of the zigzag wave with respect to the direction perpendicular to the steel sheet rolling direction was 11.3°.
  • the inventors also conducted an experiment to examine how the magnetic characteristics, magnetostrictive characteristics, noise characteristics and shape characteristics are influenced by the angle ⁇ of inclination of the zigzag wave of Fig. 3 with respect to a direction perpendicular to the rolling direction, when irradiation is conducted in a spot manner along zigzag path.
  • the period length L was fixed at 0.4 mm whereas the amplitude H of the zigzag wave was varied within the range between 0 and 0.2 mm.
  • the inclination angle ⁇ also was varied within the range between 0 and 45°.
  • the angle ⁇ being 0 means that the irradiation was conducted along a linear path.
  • the scanning pitch P2 was fixed to 6 mm.
  • Beam acceleration voltage 150 kV
  • Beam current 0.5 to 1.5 mA
  • Beam diameter 0.2 to 0.3 mm
  • the iron loss is expressed in terms of ⁇ W 17/50 which is the difference between the value W 17/50 measured before the electron beam irradiation and that measured after the irradiation.
  • the magnetic flux density is expressed in terms of ⁇ B8 which is the difference between the value B8 measured before the electron beam irradiation and that measured after the irradiation.
  • the iron loss characteristic is improved as compared with the case of irradiation along linear path when the angle ⁇ of inclination is not greater than 30° but more than 0°.
  • the iron loss increases as compared with the case of irradiation along linear path, when the above-mentioned angle exceeds 30°.
  • the magnetic flux density increases in accordance with the increase in the inclination angle q.
  • the amount of C-deflection decreases in accordance with increase in the inclination angle q, whereby a grain oriented silicon steel sheet having excellent shape characteristics is obtained.
  • the present inventors also have confirmed, through experiments, that various advantageous characteristics obtained with the intermittent electron beam along a zigzag path can be enjoyed also when the irradiation with the electron beam is conducted continuously along such a zigzag path, as will be understood from the description of Examples which will be given later.
  • Any grain oriented silicon steel sheet composition known heretofore may be employed in the present invention. Typically, however, the following composition is preferably employed.
  • This element is effective in uniformly refining the structure both in hot rolling and cold rolling, and also serves in development in Goss orientation.
  • the C content is preferably about 0.01 wt% or greater.
  • the Goss orientation is disturbed when the C content exceeds about 0.10 wt%.
  • the C content,therefore, should not exceed about 0.10 wt%.
  • This element effectively contributes to reduction in the iron loss by enhancing the specific resistance of the steel sheet.
  • Si content below about 2.0 wt% causes not only a reduction of specific resistance but also a random crystal orientation as a result of an ⁇ - ⁇ transformation which takes place in the course of the final hot annealing which is conducted for the purpose of secondary recrystallization/annealing, thus hampering the reduction of the iron loss.
  • cold rolling characteristics are impaired when the Si content exceeds about 4.5 wt%.
  • the lower and upper limits of the Si content therefore, are preferably about 2.0 wt% to 4.5 wt%.
  • the Mn content should be at least about 0.02 wt%. A too large Mn content, however, degrades the magnetic characteristics of the sheet. The upper limit of the Mn content, therefore, is about 0.12 wt%.
  • Inhibitors suitably employed can be sorted into three types: the MnS type, the MnSe type and the AlN type.
  • an inhibitor of the MnS type or MnSe type one or both selected from the group consisting of S: about 0.005 to 0.06 wt% and Se: about 0.005 to 0.06 wt% is preferably used.
  • S and Se are elements which can effectively be used as inhibitor to control secondary recrystallization in grain oriented silicon steel sheet.
  • the inhibitor should be present in an amount which is at least about 0.005 wt%.
  • the effect of the inhibitor is impaired when the content exceeds about 0.06 wt%. Therefore, the lower and upper limits of the content of S or Se is set to about 0.005 wt% and about 0.06 wt%, respectively.
  • both Al about 0.005 to 0.10 wt% and N: about 0.004 to 0.15 wt% are to be present.
  • the contents of Al and N should be determined to fall within the above-mentioned ranges of contents of inhibitor of the MnS or MnSe type for the same reasons as stated above,
  • the inhibitor such as Cr, Mo, Cu, Sn, Ge, Sb, Te, Bi and P. Trace amounts of these elements may be used in combination as the inhibitor. More specifically, contents of Cr, Cu and Sn are preferably not less than about 0.01 wt% but not more than about 0.50 wt%, whereas, for Mo, Ge, Sb, Te and Bi, the contents are preferably not less than about 0.005 wt% but not more than about 0.1 wt%. The content of P is preferably not less than about 0.01 wt% but not more than about 0.2 wt%. Each of these inhibitors may be used alone or a plurality of such inhibitors may be used in combination.
  • a silicon steel slab was prepared with a composition containing C: 0.042 wt%, Si: 3.48 wt%, Mn: 0.073 wt%, Mo: 0.012 wt%, Se: 0.020 wt% and Sb: 0.022 wt%.
  • the slab was heated for 4 hours at 1380°C, followed by hot rolling, whereby a hot-rolled sheet of 2.2 mm thick was obtained.
  • the hot-rolled slab was then subjected to cold rolling and subsequent annealing conducted for 2 minutes at 1050 °C, followed by a second cold rolling, whereby a final cold-rolled sheet of 0.23 mm thick was obtained.
  • This final cold-rolled sheet was then subjected to decarburization and primary recrystallization annealing conducted in a wet hydrogen atmosphere of 840 °C.
  • an annealing separation agent in the form of a slurry composed mainly of MgO was applied to the surface of the steel sheet, and the temperature of the steel sheet was raised at a rate of 10 °C/h and annealing was conducted for 20 hours at 850 °C. Then, the temperature was raised to 1180 °C at a rate of 8 °C/hr, allowing preferential growth of secondary recrystallization grain of Goss orientation. Then, purification annealing was conducted for 8 hours in a dry hydrogen atmosphere of 1220 °C.
  • an insulating film mainly composed of a phosphate and colloidal silica was formed on each of the steel sheets, whereby two types of grain oriented silicon steel sheets were obtained.
  • Example A The magnetic characteristics, magnetostrictive characteristics, noise characteristics and steel sheet shape characteristics of the thus-obtained products, referred to as "Sample A” were examined and evaluated.
  • the evaluation methods were the same as those in Experiment 1-(1).
  • the results are shown in Table 3.
  • a silicon steel slab was prepared having a composition containing C: 0.020 wt%, Si: 3.52 wt%, Cu: 0.2 wt%, Sn: 0.08 wt% and Al: 0.024 wt%.
  • the slab was heated for 4 hours at 1380°C, followed by hot rolling, whereby a hot-rolled sheet of 2.2 mm thick was obtained.
  • the hot-rolled slab was then subjected to cold rolling and subsequent annealing conducted for 2 minutes at 1050 °C, followed by a second cold rolling, whereby a final cold-rolled sheet of 0.23 mm thick was obtained.
  • This final cold-rolled sheet was then subjected to decarburization and primary recrystallization annealing conducted in a wet hydrogen atmosphere of 840 °C.
  • an annealing separation agent in the form of a slurry composed mainly of MgO was applied to the surface of the steel sheet, and the temperature of the steel sheet was raised at a rate of 10 °C/h and annealing was conducted for 20 hours at 850 °C. Then, the temperature was raised to 1180 °C at a rate of 8 °C/hr, allowing preferential growth of secondary recrystallization grain of Goss orientation. Then, purification annealing was conducted for 8 hours in a dry hydrogen atmosphere of 1220 °C.
  • an insulating film mainly composed of a phosphate and colloidal silica was formed on each of the steel sheets, whereby two types of grain oriented silicon steel sheets were obtained.
  • Example B The magnetic characteristics, magnetostrictive characteristics, noise characteristics and steel sheet shape characteristics of the thus-obtained product, referred to as "Sample B” were examined and evaluated.
  • the evaluation methods were the same as those in Experiment 1-(1).
  • the results are shown in Table 3.
  • the present invention provides a method which makes it possible to produce a grain oriented silicon steel sheet having superior magnetic characteristics, and in particular obtaining a significantly reduced iron loss, without deterioration of magnetostrictive characteristics, noise characteristics and steel sheet shape characteristics.
  • this advantageous effect is achieved with a smaller level of energy density as compared with known art.

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EP19930102347 1993-02-15 1993-02-15 Verfahren zum Herstellen von rauscharmen kornorientierten Siliziumstahlblechern mit niedrigen Wattverlusten und mit hervorragenden Formeigenschaften Expired - Lifetime EP0611829B1 (de)

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DE1993631221 DE69331221T2 (de) 1993-02-15 1993-02-15 Verfahren zum Herstellen von rauscharmen kornorientierten Siliziumstahlblechern mit niedrigen Wattverlusten und mit hervorragenden Formeigenschaften
EP19930102347 EP0611829B1 (de) 1993-02-15 1993-02-15 Verfahren zum Herstellen von rauscharmen kornorientierten Siliziumstahlblechern mit niedrigen Wattverlusten und mit hervorragenden Formeigenschaften

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Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1154025A2 (de) * 2000-05-12 2001-11-14 Nippon Steel Corporation Rauscharmes kornorientiertes Elektrostahlblech mit niedrigen Wattverlusten und dessen Herstellungsverfahren
US6666929B1 (en) 1999-05-26 2003-12-23 Acciai Speciali Terni, S.P.A. Process for the improvement of the magnetic characteristics in grain oriented electrical silicon steel sheets by laser treatment
EP2813593A4 (de) * 2012-02-08 2015-11-11 Jfe Steel Corp Kornorientierte elektrostahlplatte
EP2602341A4 (de) * 2010-08-06 2017-07-05 JFE Steel Corporation Kornorientiertes elektrisches stahlblech und herstellungsverfahren dafür
WO2020149330A1 (ja) * 2019-01-16 2020-07-23 日本製鉄株式会社 方向性電磁鋼板の製造方法
JPWO2022050053A1 (de) * 2020-09-04 2022-03-10

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EP0108575A2 (de) * 1982-11-08 1984-05-16 Armco Advanced Materials Corporation Verfahren zum örtlichen Glühen von kornorientiertem Siliciumstahl mit Goss-Textur
EP0220940A2 (de) * 1985-10-24 1987-05-06 Kawasaki Steel Corporation Verfahren und Vorrichtung zur Verbesserung der Eisenverluste von Blechen aus elektromagnetischem Stahl oder aus amorphem Material
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EP0331497A2 (de) * 1988-03-03 1989-09-06 Allegheny Ludlum Corporation Verfahren zum Verbessern der Ummagnetisierungseigenschaften von Elektroblechen
EP0367467A1 (de) * 1988-10-26 1990-05-09 Kawasaki Steel Corporation Kornorientierte Siliziumstahlbleche mit niedrigen Wattverlusten und Verfahren zur Herstellung derselben

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Publication number Priority date Publication date Assignee Title
EP0108575A2 (de) * 1982-11-08 1984-05-16 Armco Advanced Materials Corporation Verfahren zum örtlichen Glühen von kornorientiertem Siliciumstahl mit Goss-Textur
EP0220940A2 (de) * 1985-10-24 1987-05-06 Kawasaki Steel Corporation Verfahren und Vorrichtung zur Verbesserung der Eisenverluste von Blechen aus elektromagnetischem Stahl oder aus amorphem Material
EP0260927A2 (de) * 1986-09-16 1988-03-23 Kawasaki Steel Corporation Verfahren zur Herstellung von kornorientierten Silizium-Stahlblechen mit sehr niedrigen Walzverlusten
EP0331497A2 (de) * 1988-03-03 1989-09-06 Allegheny Ludlum Corporation Verfahren zum Verbessern der Ummagnetisierungseigenschaften von Elektroblechen
EP0367467A1 (de) * 1988-10-26 1990-05-09 Kawasaki Steel Corporation Kornorientierte Siliziumstahlbleche mit niedrigen Wattverlusten und Verfahren zur Herstellung derselben

Cited By (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US6666929B1 (en) 1999-05-26 2003-12-23 Acciai Speciali Terni, S.P.A. Process for the improvement of the magnetic characteristics in grain oriented electrical silicon steel sheets by laser treatment
EP1154025A3 (de) * 2000-05-12 2003-11-26 Nippon Steel Corporation Rauscharmes kornorientiertes Elektrostahlblech mit niedrigen Wattverlusten und dessen Herstellungsverfahren
US6918966B2 (en) 2000-05-12 2005-07-19 Nippon Steel Corporation Low iron loss and low noise grain-oriented electrical steel sheet and a method for producing the same
EP1154025A2 (de) * 2000-05-12 2001-11-14 Nippon Steel Corporation Rauscharmes kornorientiertes Elektrostahlblech mit niedrigen Wattverlusten und dessen Herstellungsverfahren
EP2602341A4 (de) * 2010-08-06 2017-07-05 JFE Steel Corporation Kornorientiertes elektrisches stahlblech und herstellungsverfahren dafür
US9761361B2 (en) 2012-02-08 2017-09-12 Jfe Steel Corporation Grain-oriented electrical steel sheet
EP2813593A4 (de) * 2012-02-08 2015-11-11 Jfe Steel Corp Kornorientierte elektrostahlplatte
WO2020149330A1 (ja) * 2019-01-16 2020-07-23 日本製鉄株式会社 方向性電磁鋼板の製造方法
KR20210111284A (ko) * 2019-01-16 2021-09-10 닛폰세이테츠 가부시키가이샤 방향성 전자 강판의 제조 방법
JPWO2020149330A1 (ja) * 2019-01-16 2021-12-02 日本製鉄株式会社 方向性電磁鋼板の製造方法
EP3913088A4 (de) * 2019-01-16 2022-09-21 Nippon Steel Corporation Verfahren zur herstellung eines kornorientierten elektromagnetischen stahlblechs
JPWO2022050053A1 (de) * 2020-09-04 2022-03-10
WO2022050053A1 (ja) * 2020-09-04 2022-03-10 Ｊｆｅスチール株式会社 方向性電磁鋼板

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