WO2019132133A1 - Feuille d'acier électrique orientée et son procédé de préparation - Google Patents

Feuille d'acier électrique orientée et son procédé de préparation Download PDF

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Publication number
WO2019132133A1
WO2019132133A1 PCT/KR2018/005675 KR2018005675W WO2019132133A1 WO 2019132133 A1 WO2019132133 A1 WO 2019132133A1 KR 2018005675 W KR2018005675 W KR 2018005675W WO 2019132133 A1 WO2019132133 A1 WO 2019132133A1
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Prior art keywords
steel sheet
slab
electrical steel
weight
formula
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PCT/KR2018/005675
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English (en)
Korean (ko)
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WO2019132133A8 (fr
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김재겸
한규석
박유준
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주식회사 포스코
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Publication of WO2019132133A1 publication Critical patent/WO2019132133A1/fr
Publication of WO2019132133A8 publication Critical patent/WO2019132133A8/fr

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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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
    • C21D8/1222—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—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
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • 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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur

Definitions

  • a directional electric steel sheet and a method of manufacturing a directional electric steel sheet relates to a method of manufacturing a grain-oriented electrical steel sheet and a grain-oriented electrical steel sheet excellent in magnetic properties by stably growing crystal grains having a very high degree of integration in a Goss orientation at the time of secondary recrystallization high-temperature annealing using S, Se-based precipitates and La segregation will be. More specifically, the present invention relates to a method for producing a grain-oriented electrical steel sheet and a grain-oriented electrical steel sheet having excellent magnetic properties by controlling the correlation between Mn, S, Se and La in an alloy component.
  • the directional electric steel sheet has excellent magnetic properties in the rolling direction by forming the Goss aggregate structure ( ⁇ 110 ⁇ ⁇ 001 ⁇ texture) on the entire steel sheet by using the abnormal crystal growth phenomenon called secondary recrystallization and is excellent in one- It is a soft magnetic material used as an iron core of an electronic device requiring characteristics.
  • magnetic properties can be expressed by magnetic flux density and iron loss, and high magnetic flux density can be obtained by precisely aligning the orientation of the grain in the ⁇ 110 ⁇ ⁇ 001 > orientation.
  • the electric steel sheet having a high magnetic flux density not only makes it possible to reduce the size of the iron core material of the electric equipment, but also reduces the hysteresis loss, thereby achieving miniaturization and high efficiency at the same time.
  • the iron loss is a power loss consumed as heat energy when an arbitrary alternating magnetic field is applied to the steel sheet, and varies greatly depending on the magnetic flux density and plate thickness of the steel sheet, the amount of impurities in the steel sheet, the resistivity and the size of the secondary recrystallization, The higher the specific resistivity and the lower the plate thickness and the impurity content in the steel sheet, the lower the iron loss and the higher the efficiency of the electric equipment.
  • Secondary recrystallization of the grain-oriented electrical steel sheet occurs when normal grain growth inhibits the movement of grain boundaries normally grown by precipitates, inclusions, or elements segregated at grain boundaries or grain boundaries, unlike ordinary grain growth.
  • the degree of integration with respect to the Goss orientation is high
  • complicated processes such as component control in steelmaking, reheating of slabs in hot rolling and hot rolling process control, hot-rolled sheet annealing, primary recrystallization annealing, and secondary recrystallization annealing are required. It must be precisely and strictly controlled.
  • a study on the production of directional electric steel sheet by secondary recrystallization of Goss orientation, called precipitate and inclusions that inhibit grain growth, is referred to as an inhibi tor.
  • MnS was used as a grain growth inhibitor in the directional electric steel sheet which was initially developed, and it was manufactured by the two - step rolling method. As a result, the secondary recrystallization was stable, but the magnetic flux density was not so high and the iron loss was high.
  • a manufacturing method has been used in which a precipitate such as AIN or MnS [Se] is used as a grain growth inhibitor to cause secondary recrystallization.
  • a precipitate such as AIN or MnS [Se] is used as a grain growth inhibitor to cause secondary recrystallization.
  • Such a manufacturing method has an advantage of stably inducing secondary recrystallization, but in order to exhibit a strong grain growth inhibiting effect, the precipitates must be distributed very finely and uniformly on the steel sheet.
  • the slabs are heated at a high temperature for a long period of time before hot rolling to solidify coarse precipitates present in the steel, and then hot rolled in a very short time to perform hot rolling It should be done.
  • a large-scale slab heating equipment is required.
  • the hot rolling and the winding process are strictly controlled, and the precipitates solidified in the hot- 2019/132133 1 »(: 1 ⁇ 1 ⁇ 2018/005675
  • the silsuyul is lowered in accordance with the melting point of the formed low 3 ⁇ 4 0 4 slab washing ( ⁇ vashing) phenomenon occurs when the slab is heated to a high temperature.
  • nitriding treatment is performed using ammonia gas in the first recrystallization annealing step.
  • the ammonia gas is decomposed into hydrogen and nitrogen at a temperature of about 500 ° C or higher.
  • the nitrogen gas is nitrided and reacted with the nitriding element in the steel sheet to form nitrides such as Si, .
  • the low-temperature heating method also has many limitations on the manufacturing process for the precipitation control, so that the problem caused by the complexity of the manufacturing process can not be solved. Therefore require orientation, the magnetic and electric steel in order to improve the productivity, because the decomposition temperature is too high, precipitate-oriented electrical steel sheet production technology using the control is easy to precipitate.
  • the present invention is to provide a method for manufacturing a grain-oriented electrical steel sheet and a grain-oriented electrical steel sheet having high magnetic properties by stably growing crystal grains having a very high degree of integration into a bearing during secondary recrystallization high-temperature annealing using segregation. More specifically, in the alloy component,
  • the directional electrical steel sheet according to one embodiment of the present invention may contain, by weight%: 1.0 to 5.0%, 0: 0.005% (excluding 0%), 1X1: 0.001% to 0.1%, 0.001% to 0.020% 0.001% to 0.050% and 1: 0.001 to 0.1% 2019/132133 1 »(: 1 ⁇ 1 ⁇ 2018/005675
  • the directional electrical steel sheet according to an embodiment of the present invention can satisfy the following expression (2).
  • the grain-oriented electrical steel sheet according to an embodiment of the present invention may further include at least one of 0.01% by weight and 0.005% by weight or less.
  • the method for producing a grain-oriented electrical steel sheet according to the present invention comprises: 1.0 to 5.0% by weight, X: 0.005% or less (excluding 0%), 0.001 to 0.1%, 0.001 to 0.020%, 0.001 to 0.050% and 1 st: 0.001 to 0.1%, the remainder comprising 6 and other unavoidable impurities, ; Heating the slab; Hot rolling the slab to produce a hot rolled sheet; Rolling the hot rolled sheet to manufacture a hot rolled steel plate; A first recrystallization annealing of the cold rolled sheet; And secondary recrystallization annealing the cold rolled sheet after the primary recrystallization annealing has been completed.
  • Heating the slab may heat the slab to 1000 to 1250 < 1 >.
  • the primary recrystallization annealing step may be performed at a dew point temperature of 50 to 701: and a mixed atmosphere of hydrogen and nitrogen.
  • the directional electrical steel sheet according to an embodiment of the present invention may include, Secondary recrystallization using high-temperature annealing and segregation High-density annealing at high temperature allows stable grain growth with high degree of integration in 33 directions.
  • first, second and third, etc. are used to describe various portions, components, regions, layers and / or sections, but are not limited thereto. These terms are only used to distinguish any moiety, element, region, layer or section from another moiety, moiety, region, epitope, or section. Thus, a first portion, component, region, layer or section described below may be referred to as a second portion, component, region, layer or section without departing from the scope of the invention.
  • the terminology used herein is for the purpose of describing particular embodiments only and is not intended to limit the invention.
  • the singular forms as used herein include plural forms as long as the phrases do not expressly express the opposite meaning thereto. Means that a particular feature, region, integer, step, operation, element and / or component is specified and that the presence or absence of other features, regions, integers, steps, operations, elements, and / It does not exclude addition.
  • the further inclusion of an additional element means that the additional element is replaced by an additional amount of the additional element.
  • the grain-oriented electrical steel sheet according to an embodiment of the present invention may contain, by weight%: 1.0% to 5.0%, 0: 0.005% (excluding ⁇ %), 1: 0.001% to 0.1%, 0.001% 0.020%, 0.001% to 0.050%, and 1: 0.001 to 0.1%, the remainder including 6 and other unavoidable impurities.
  • Silicon () increases the specific resistivity of the oriented electrical steel sheet material, thereby lowering iron loss ( 1 : 0 1 083 ), that is, iron loss. If the content is too small, the specific resistance decreases, the wastewater loss increases, and the iron loss can be deteriorated. Further, during the primary recrystallization annealing, a phase transformation between ferrite and austenite occurs, and the primary recrystallization texture can be severely damaged. In addition, during the secondary recrystallization annealing, phase transformation between ferrite and austenite occurs and secondary recrystallization becomes unstable, and the 0 053 texture can be severely damaged.
  • silver may be contained in an amount of 1.0 to 5.0% by weight. More specifically from 2.0 to 4.0% by weight.
  • Carbon is an element contributing to grain refinement by increasing the phase transformation between ferrite and austenite and improving elongation.
  • (:) Is an essential element for improving the rolling property of an electric steel sheet having poor brittleness and poor rolling property. However, when they remain in the final product, they are formed due to the magnetic aging effect 2019/132133 1 »(: 1 ⁇ 1 ⁇ 2018/005675
  • the carbide should be controlled in the proper amount because it is an element which tends to lengthen the magnetism in the product plate.
  • decarburization is performed when the primary recrystallization annealing is performed in the manufacturing process, and the content of 0 in the final electrical steel sheet produced after decarburization annealing may be 0.005% by weight or less. More specifically, it may be 0.003% by weight or less.
  • (:) may contain 0.01 to 0.1% by weight in the slab.
  • the manganese ( 11) has an effect of reducing the iron loss by increasing the resistivity in the same way as the ⁇ . It is also an important element for forming a 6- system precipitate and causing secondary recrystallization as a grain growth inhibitor. When the content of 3 ⁇ 4 is too small, a sufficient effect as an inhibitor can not be expected because the number and volume to be formed are low.
  • the content of 3 ⁇ 4 can be set to 0.001 to 0.10% by weight. More specifically from 0.01 to 0.08% by weight.
  • Sulfur is an important element for causing secondary recrystallization as a crystal growth inhibitor by forming precipitates.
  • the effect can be reduced. 3 If the content is too large, the occurrence of edge cracks in the performance and hot rolling stages may increase, which may result in a reduction in the rate of water loss. Therefore, the content of the pound can be limited to 0.001 to 0.020% by weight. More specifically from 0.007 to 0.015% by weight.
  • Selenium is an important element for causing secondary recrystallization as a grain growth inhibitor by forming a precipitate as in the case of selenium.
  • the occurrence of edge cracks in the slab performance and hot rolling process by excess 8 content is important element for causing secondary recrystallization as a grain growth inhibitor by forming a precipitate as in the case of selenium.
  • the effect of inhibiting grain growth may be reduced. 3 6 If the content is too large, the occurrence of cracking in the performance and hot rolling stage may increase, which may result in a decrease in the yield rate. Therefore, the content of muscle may be limited to 0.001 to 0.050% by weight. More specifically, the root can be contained in an amount of 0.007 to 0.03% by weight.
  • the grain-oriented electrical steel sheet can satisfy Equation (1). [Formula 1]
  • the value of expression 1 can be -0.47 to 0.18.
  • the grain-oriented electrical steel sheet can satisfy Equation (2). [Formula 2]
  • the grain electric steel sheet according to an embodiment of the present invention may further include at least one of 0.01% by weight or less and 0.005% by weight or less.
  • the 6- system precipitate is used as a crystal grain growth inhibitor, Use segregation to solve. Therefore, the content of Si can be suppressed. More specifically, it may further include at least one of 0.005 wt% or less and 0.003 wt% or less of Si.
  • impurities such as total, V, and the like may be included.
  • impurities such as total, V, and the like may be included.
  • ⁇ , V, etc. are also strong carbonitride formation elements. 0.01% by weight or less.
  • the magnetism can be further improved. Specifically, on the basis of the thickness of 0.30, the iron loss in the 1.71 631 503 ⁇ 4 condition of the oriented electrical steel sheet may be 1.51 or less. More specifically, on a 0.30 < th > thickness basis, 2019/132133 1 »(: 1 ⁇ 1 ⁇ 2018/005675
  • the iron loss in the 1.71 6 3 , 50 3 ⁇ 4 condition of the electric steel sheet may be 0.9-1.8 3 ⁇ 4 .
  • the magnetic flux density under a magnetic field induced ⁇ of 800/1/111 of a grain-oriented electrical steel sheet 8) may be at least 1.881. More specifically from 1.9 to 1.951 :. If the magnetic flux density 8) is 1.8 or more, there is an advantage that the transformer efficiency is high and the noise is small.
  • a method of manufacturing a grain-oriented electrical steel sheet according to an embodiment of the present invention includes the steps of: fabricating a slab; Heating the slab; Hot rolling the slab to produce a hot rolled sheet; Cold rolling the hot rolled steel sheet to manufacture a steel plate; A first recrystallization annealing step of annealing the steel plate; And secondary recrystallization annealing the cold rolled sheet after the primary recrystallization annealing has been completed.
  • the molten steel whose composition is adjusted in the steelmaking process is made into a slab through continuous casting.
  • Equations (1) to (2) described above can be equally satisfied within the alloy component of the slab.
  • the heating of the slab is preferably carried out at a low temperature of 1,250 deg. Or less, more preferably 1,150 deg. Or less to partially refine the precipitate.
  • the heating furnace can be repaired by melting the surface of the slab and the lifetime of the heating furnace can be shortened.
  • the slab is heated to 1,250 ° (: or less, more preferably, to 1, 1501 or less, the columnar structure of the slab is prevented from being grown to a great extent, and cracks are generated in the width direction of the plate in the subsequent hot rolling process. It is possible to prevent the occurrence of the abnormality, thereby improving the error rate.
  • the heating temperature of the slab may be 1000 to 12501 :. 2019/132133 1 »(: 1 ⁇ 1 ⁇ 2018/005675
  • a hot rolled sheet having a thickness of 1.5 to 4.0 mm can be produced by hot rolling.
  • the hot-rolled hot-rolled sheet can be subjected to hot rolling without annealing the hot-rolled sheet or annealing the hot-rolled sheet if necessary.
  • the hot - rolled sheet can be heated to 9001 ° C or higher, cooled, and then cooled to make the hot - rolled sheet uniform.
  • the hot-rolled sheet is rolled to form a cold-rolled sheet.
  • the hot rolling is carried out using a reverse roughing machine or a tandem 311 (10111) rolling machine by means of two or more cold rolling processes, including one cold rolling or intermediate annealing, to produce a plate of final product thickness.
  • a reverse roughing machine or a tandem 311 (10111) rolling machine by means of two or more cold rolling processes, including one cold rolling or intermediate annealing, to produce a plate of final product thickness.
  • the temperature of the steel sheet during cold rolling is set at 100 Or more is advantageous for improving the magnetic properties.
  • the cold-rolled steel plate is subjected to primary recrystallization annealing.
  • Primary recrystallization occurs in which the core of the goss grain is generated in the primary recrystallization annealing step.
  • Decarburization of the steel sheet can be achieved during the primary recrystallization annealing process.
  • the primary recrystallization annealing temperature may be 800 to 9501. If the annealing temperature is low, decarburization time may take a long time. When the annealing temperature is high, the primary recrystallized grains grow to a great extent, and the crystal growth driving force drops, so that stable secondary recrystallization is not formed.
  • the annealing time is not a big problem in exerting the effect of the present invention, but can be processed within 5 minutes in consideration of productivity.
  • only decarburization is performed, and sedimentation may not be performed. That is, the first recrystallization annealing can be performed only at a dew point temperature of 5010 to 70 ⁇ and a hydrogen and nitrogen mixed atmosphere.
  • the primary recrystallized annealed cold-rolled sheet thus obtained is preferably a rosin-
  • Quot means a precipitate in which one or more of the cubic boron and the cubic boron is bonded.
  • the cold-rolled sheet having undergone the primary recrystallization annealing is subjected to secondary recrystallization annealing.
  • Goss ⁇ 110 ⁇ ⁇ 001 > texture is formed in which the ⁇ 110 ⁇ plane is parallel to the rolling surface and the ⁇ 001> direction is parallel to the rolling direction.
  • the secondary recrystallization annealing can be performed after the annealing separator is applied to the quenched plate in which the primary recrystallization annealing is completed.
  • the annealing separator is not particularly limited, and an annealing separator containing MgO as a main component may be used.
  • the secondary recrystallization annealing is performed at a proper heating rate to cause secondary recrystallization in ⁇ 110 ⁇ ⁇ 001 > Goss orientation, followed by refining annealing, which is an impurity removal process, followed by cooling.
  • the annealing atmosphere gas is heat-treated using a mixed gas of hydrogen and nitrogen in the heating process as in the usual case.
  • 100% hydrogen gas is used for a long time to remove impurities.
  • the cold-rolled steel sheet was subjected to primary recrystallization annealing by maintaining it at a dew point of 6 CTC and a mixed gas atmosphere of hydrogen and nitrogen at a temperature of 850 ° C for 180 seconds.
  • primary recrystallization annealing by maintaining it at a dew point of 6 CTC and a mixed gas atmosphere of hydrogen and nitrogen at a temperature of 850 ° C for 180 seconds.
  • the secondary recrystallization annealing up to 1200 ° C 25 v% nitrogen + 75 v% was in a mixed gas atmosphere of hydrogen, 1200 ° C after reaching the 100v% And maintained in a hydrogen gas atmosphere for 10 hours or longer, followed by cooling.
  • Table 1 shows the magnetic properties of the oriented electrical steel sheet according to each component.
  • the iron loss was measured at 1.7 Tesla and 50 Hz using a single sheet method and the magnetic flux density (Tesla) induced under a magnetic field of 800 A / m was measured.
  • Each iron loss value represents the average by condition. 2019/132133 1 »(: 1/10/01 018/005675
  • inventive example satisfying the formula 1 is excellent in magnetic flux density and iron loss.

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  • Materials Engineering (AREA)
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Abstract

L'invention concerne, selon un mode de réalisation, une feuille d'acier électrique orientée qui comprend, en % en poids, de 1,0 % à 5,0 % de Si, 0,005 % ou moins de C (à l'exception de 0 %), 0,001 % de Mn, de 0,001 % à 0,020 % de S, de 0,001 % à 0,050 % de Se et de 0,001 % à 0,1 % de La, et le reste étant du Fe et d'autres impuretés inévitables, et qui répond à la formule [1]. Formule [1] : -0,5 < ([Mn]-[La])/(10x[S] + [Se]) < 0,2 (Dans la formule [1], [Mn], [La], [S] et [Se] indiquent la teneur (% en poids) en Mn, La, S et Se, respectivement.)
PCT/KR2018/005675 2017-12-26 2018-05-17 Feuille d'acier électrique orientée et son procédé de préparation WO2019132133A1 (fr)

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Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0835944A1 (fr) * 1996-10-11 1998-04-15 Kawasaki Steel Corporation Procédé pour la fabrication de tÔles d'acier magnétiques
JP2008127634A (ja) * 2006-11-21 2008-06-05 Nippon Steel Corp 一方向性電磁鋼板の製造方法
KR20090014383A (ko) * 2006-06-16 2009-02-10 신닛뽄세이테쯔 카부시키카이샤 고강도 전자기 강판 및 그 제조 방법
KR101131729B1 (ko) * 2004-12-28 2012-03-28 주식회사 포스코 고자속밀도 방향성 전기강판의 제조방법
KR20150095911A (ko) * 2012-12-28 2015-08-21 제이에프이 스틸 가부시키가이샤 방향성 전기 강판의 제조 방법

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR20150073551A (ko) * 2013-12-23 2015-07-01 주식회사 포스코 방향성 전기강판 및 그 제조방법
KR101697988B1 (ko) * 2015-12-22 2017-01-19 주식회사 포스코 방향성 전기강판 및 이의 제조방법

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0835944A1 (fr) * 1996-10-11 1998-04-15 Kawasaki Steel Corporation Procédé pour la fabrication de tÔles d'acier magnétiques
KR101131729B1 (ko) * 2004-12-28 2012-03-28 주식회사 포스코 고자속밀도 방향성 전기강판의 제조방법
KR20090014383A (ko) * 2006-06-16 2009-02-10 신닛뽄세이테쯔 카부시키카이샤 고강도 전자기 강판 및 그 제조 방법
JP2008127634A (ja) * 2006-11-21 2008-06-05 Nippon Steel Corp 一方向性電磁鋼板の製造方法
KR20150095911A (ko) * 2012-12-28 2015-08-21 제이에프이 스틸 가부시키가이샤 방향성 전기 강판의 제조 방법

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