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WO2005100627A1 - Feuille d’acier électromagnétique non orienté, d’une excellente capacité à fabriquer les ébauches et d’excellentes caractéristiques magnétiques après recuit de suppression des contraintes, et procédé de fabrication de celle-ci - Google Patents

Feuille d’acier électromagnétique non orienté, d’une excellente capacité à fabriquer les ébauches et d’excellentes caractéristiques magnétiques après recuit de suppression des contraintes, et procédé de fabrication de celle-ci Download PDF

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Publication number
WO2005100627A1
WO2005100627A1 PCT/JP2005/007653 JP2005007653W WO2005100627A1 WO 2005100627 A1 WO2005100627 A1 WO 2005100627A1 JP 2005007653 W JP2005007653 W JP 2005007653W WO 2005100627 A1 WO2005100627 A1 WO 2005100627A1
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WO
WIPO (PCT)
Prior art keywords
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steel sheet
oriented electrical
hot rolling
precipitates
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Ceased
Application number
PCT/JP2005/007653
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English (en)
Japanese (ja)
Inventor
Yoshihiro Arita
Hidekuni Murakami
Kouichi Kirishiki
Yutaka Matsumoto
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Nippon Steel Corp
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Nippon Steel Corp
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Nippon Steel Corp filed Critical Nippon Steel Corp
Priority to JP2006512410A priority Critical patent/JP4660474B2/ja
Publication of WO2005100627A1 publication Critical patent/WO2005100627A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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Classifications

    • 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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular fabrication or treatment of ingot or slab
    • 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
    • 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
    • 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

Definitions

  • the present invention relates to a non-oriented electrical steel sheet used as an iron core material of electrical equipment and a method for producing the same, and particularly to a non-oriented electrical steel sheet excellent in punching workability and magnetic properties after strain relief annealing. And its manufacturing method.
  • JP-A-7-150248 controls the S i deoxidation and steel (S ol. A1 ⁇ 0. 001% ) S i0 2 and MnO ratio of oxides contained in grain
  • Japanese Patent Application Laid-Open No. Hei 6-73510 discloses a method of controlling extensible inclusions that are harmful to growth, and controlling the Mn / Si of steel components to 0.2 to 1.0. I have.
  • Japanese Patent Application Laid-Open No. 58-117828 discloses a method of appropriately controlling nitrides or oxides generated during deoxidation and further reducing or detoxifying sulfides to improve magnetism.
  • S: 0.01 to 02% when S: 0.01 to 02% is contained, Ca fe or rare earth element is used.
  • Japanese Patent Application Laid-Open No. 4-63228 discloses a method of fixing S by setting S to not more than 0.0050% and setting the heating temperature of the slab to 1100 ° C or less. A method for preventing fine precipitation is disclosed. Disclosure of Invention ⁇
  • An object of the present invention is to provide a steel sheet having good crystal grain growth, low iron loss, and high magnetic flux density.
  • the present invention has been made to solve the above-mentioned problems, and the The effect is as follows. ,
  • the distribution density of Ti precipitates having a diameter of less than 0.1 ⁇ m is 1.0 ⁇ 10 3 / mm 2 or less. Grain-oriented electrical steel sheet.
  • non-oriented electrical steel sheet according to any one of (1) to (4), characterized by containing 0.5%.
  • the steel sheet As a method for producing the steel sheet according to any one of (1) to (5), the steel sheet, hot-rolled, pickled, cold-rolled, and then subjected to finish annealing followed by hot-rolled slab. With regard to heating, it is characterized in that it is retained for 5 minutes or more in the range of 1150 ° C or more and 1250 ° C or less, then continuously for 15 minutes or more in the range of 1050 ° C or more and less than 1150 ° C, and then hot-rolled immediately.
  • non-oriented electrical steel sheet Construction method it is characterized in that it is retained for 5 minutes or more in the range of 1150 ° C or more and 1250 ° C or less, then continuously for 15 minutes or more in the range of 1050 ° C or more and less than 1150 ° C, and then hot-rolled immediately.
  • the steel sheet, hot rolling, pickling, and cold rolling are subjected to finish annealing, followed by finishing of hot rolling.
  • the inventors of the present invention have reduced the inevitable contamination element S to about 0.0010% in steels with Si of 1.5% or less, and have been using slab heating as disclosed in JP-A-4-63228. Even if the temperature was lowered to 1100 ° C or less, the iron loss after strain relief annealing varied and it was not stabilized. Investigation of the cause revealed that despite the low S content and slab heating temperature, MnS, Cu 2 S and its complex sulfide were finely and abundantly dispersed in the steel, and the crystal after strain relief annealing It was found that grain growth was significantly suppressed.
  • these sulfides are spherical with a diameter of about 0.1 to 0.3 ⁇ m, but contain Ti precipitates with a diameter equivalent to about 0.05 ⁇ at the center. It turned out that. The reason why the sulfide takes such a precipitation form is that TiN, which is initially deposited after sintering and heated by hot rolling slab, is finely dispersed, and sulfide is deposited on the nucleus. I understand.
  • the present inventors have focused on sulfides that have a higher growth rate than TiN and are likely to become coarse.
  • sulfide is complex-precipitated with TiN as a nucleus
  • the present inventors have found that a low iron loss can be stably obtained by complex precipitation of a sulfide with respect to BN generated as a fixation of excess N, which will be described later, and completed the present invention.
  • the experimental results that led to the present invention will be described.
  • the cold-rolled sheet thus obtained was subjected to finish annealing at 800 ° C for 10 seconds, and then subjected to strain annealing at 750 ° C for 2 hours, and the crystal grain size and iron loss were measured.
  • the crystal grain size after strain relief annealing was good at 50 ⁇ m or more. Iron loss was obtained.
  • the grain growth after strain relief annealing and the effect of improving iron loss at ⁇ ⁇ 0.4% or more and at S: 0.0012, 0.0025% are considered as follows.
  • increasing the Mn raises the MnS precipitation start temperature.
  • MnS comes to precede BN at the time of hot-rolling heating, and the BN that subsequently precipitates becomes compositely precipitated with MnS as nuclei.
  • the formation of fine precipitates of B can be suppressed. It is considered that crystal grain growth and iron loss after the strain relief annealing are obtained.
  • the cold-rolled sheet thus obtained was subjected to a finish annealing at 800 ° C for 10 seconds, followed by a strain relief annealing at 750 ° C for 2 hours to observe the precipitates and crystal grain size of the steel sheet. Iron loss was measured.
  • Mn 0.4% or more and Ti was 0.0015% or less.
  • Sample 4 5 is, sulfides density after stress relief annealing is 3. 0 X 10 5 or less, the average crystal grain size becomes more 50 // m, good iron loss was obtained.
  • these samples there are many spherical sulfides with a diameter of 0.2 to 0.3 ⁇ m, and on the outer periphery, multiple fine Ti precipitates equivalent to the diameter of less than 0.1 ⁇ m are precipitated. Many were confirmed.
  • the sulfide density after strain relief annealing is as high as 4.5 ⁇ 10 5 / mm 2 or more, and the average crystal grain size is as small as 35 ⁇ or less. Small and bad iron loss.
  • the sulfides found in these samples were as small as 0.1 m or less in diameter, and many of the sulfides contained Ti precipitates at the center.
  • the Mn is at 0.4% or more, as high as Ti sulfide density after stress relief annealing also samples 6, 9 is greater than 0, 0015% is 3. 8 X 10 5 cells / 2 or more
  • the average grain size was less than 45 ⁇ , and the iron loss was relatively poor.
  • the sulfides were distributed over a wide range from 0.05 to 0.3 ⁇ m in diameter, and the morphology of the sulfides with the Ti precipitates was also different at the outer periphery or the center. Note that the distribution density of Ti precipitates less than 0.1 ⁇ m in diameter was as low as less than 1,0 ⁇ 10 3 / mm 2 in all samples.
  • sample 3 kept at 1100 ° C, although not as high as the 1200 ° C heating material (sample 2), the ratio of multiple precipitation was as low as 5%, and neither the crystal grain size nor the iron loss was even better.
  • This result is considered as follows. First, when held at 1200 ° C, MnS is precipitated due to the high Mn of 0.42%, but B is hot-rolled as it is undeposited. Occasionally, single and fine B precipitates are formed, and crystal grain growth and iron loss are significantly deteriorated. Next, if the temperature is kept at 1100 ° C, the distribution of MnS becomes coarse and the number of nuclei in which BN is compositely precipitated becomes insufficient. It is considered that the diameter and iron loss could not be obtained.
  • Table 3 Table 3
  • the present invention preferentially and optimally precipitates MnS by optimizing the amount of Mn and the heating cycle of hot rolling, and simultaneously precipitates both MnS and BN by multiple precipitation of fine BN.
  • the amount of Mn must be increased and the amount of A1 must be reduced. This is because A1 consumes N as A1N, and the grain growth is prevented by A1N itself.
  • the present invention optimizes the precipitation temperature of MnS and TiN, and optimizes the heating cycle of hot rolling, so that first, MnS is coarsely deposited, and then, fine TiN is compositely precipitated. They found a way to render the precipitates harmless and improve crystal grain growth and iron loss.
  • Si is an effective element for increasing electric resistance, but if added in excess of 1.5%, hardness increases, magnetic flux density decreases, and cost increases, so the upper limit was 1.5%.
  • Mn is an important element for expressing the present invention.
  • the purpose of the present invention is to precipitate BN and / or TiN using sulfides containing MnS as nuclei, and for that purpose, MnS must be sufficiently precipitated before the deposition temperature of and / or TiN. .
  • the object is achieved by setting Mn to 0.4% or more. You. If the content exceeds 1.5%, the saturation magnetic flux density is significantly reduced. The upper limit of 1.5% was set because the lowering of the ⁇ ⁇ a transformation temperature made it difficult to control the structure of the hot-rolled sheet.
  • A1 is an element required for steel deoxidation. Oxygen non-deoxidized with less than Sol.0.01% is left in the steel to form oxides of Si0 2 ⁇ MnO, grain growth which was combined stretching of the effect of Mn which is added over 0.4% Therefore, the lower limit of Sol. A1 was set at 0.01%. If Sol. A1 exceeds 0.04%, A1N will precipitate instead of BN, making it difficult to realize the present invention. In addition, ensuring precipitation of TiN and utilizing scrap at customers Therefore, the upper limit of Sol. A1 was set to 0.04%.
  • the upper limit is defined as 0.0015% as an allowable amount that can be rendered harmless by Mn S, Cu 2 S, a composite sulfide thereof, and a composite precipitation. If the Ti content exceeds 0.0015%, the temperature at which TiN starts to precipitate becomes too high to control the preferential precipitation of MnS.
  • N produces TiN and A1N in addition to BN.
  • S. l. A1 In the present invention containing 0.01 to 0.04%, when A1N is formed, crystal grain growth is significantly deteriorated. Therefore, it is necessary to add B to suppress the formation of A1N. Therefore, the amount of B to be added must be increased as N becomes higher. However, excessive addition of B causes embrittlement of the steel sheet and lowers productivity, so the upper limit of N was set to 0.0030%.
  • S is necessary for generating sulfide that becomes a precipitation nucleus of BN and / or TiN, and the object of the present invention is achieved by containing 0.0010% or more. However, if it exceeds 0.0040%, the amount of sulfide precipitation itself increases, and the grain growth is hindered, so the upper limit was made 0.0040%.
  • B is an element that must be added to suppress the generation of A1N that is harmful to crystal grain growth, but for that purpose it is necessary to add B / N of 0.5 or more. The effect is saturated even if it is added excessively to N, so the upper limit is B / N 1. It was set to 5.
  • Sn, Cu, Ni is annealed, particularly is effective in suppressing nitride Ya oxidation of the steel sheet surface during stress relief annealing, 3 0 1.1:
  • the steel of the present invention containing 0.01 to 0 04%. Is particularly preferable because it is easily nitrided.
  • the addition amount is less than 0.01%, there is no effect, and if it exceeds 0.50%, the effect is saturated and the cost increases, so the addition amount range is 0.01% or more. 0.50% or less. Since the nitriding and oxidation inhibiting effects of Sn, Cu, and Ni are equivalent, it is sufficient that the above-mentioned addition amount range is satisfied by a single or a composite. In addition, it is also possible to add 0.001 to 0.5% of one or more of REM, Ca, and Mg.
  • Sn is an extremely effective element for improving the magnetic flux density in the present invention. This is because, in the present invention, since the Mn is increased, the ⁇ ⁇ transformation temperature is inevitably lowered, and the grain growth of the hot-rolled sheet cannot be sufficiently promoted. . If the amount of addition is less than 0.01%, there is no effect, and if it exceeds 0.50%, the effect will be saturated and the cost will increase, so the range of addition is 0.01% or more 0 50% or less. Furthermore, Sn also has the effect of suppressing nitriding and oxidation of the steel sheet surface during strain relief annealing, and it is desirable to add Sn also from that viewpoint.
  • the number ratio of the sulfide containing Mn in which the B precipitate is compositely deposited is specified to be 10% or more. This is based on the results of observations on a single sample with almost no fine B precipitates.
  • the crystal grain size is an important factor for achieving both punching workability and magnetism. For steel sheets subjected to stamping, if the grain size exceeds 30 ⁇ , the punching workability deteriorates, so the crystal grain size was set to 30 ⁇ or less. For electrical products, the required iron loss cannot be satisfied if the grain size is less than 50 m, so the crystal grain size after 750 ° C x 2 hours of strain relief annealing, which is commonly used Was defined as 50 ⁇ m or more.
  • the distribution density In order to obtain a crystal grain size of 50 ⁇ or more after strain relief annealing, the distribution density must be 3.0 X 10 5 grains / mm 2 or less.
  • the distribution density described here refers to the number of precipitates in which Mn, S or Cu, S, or Mn, Cu, S is detected by observing a chemically polished sample after mirror polishing with a scanning or transmission electron microscope. It is divided by the observation visual field area (or the total area when multiple visual fields are observed).
  • the Ti precipitates can be rendered harmless by complex precipitation of sulfides as nuclei, even though they are fine enough to be less than ⁇ . ⁇ in diameter.
  • Those with a grain size of 50 / m or more after strain relief annealing and good iron loss have a distribution density of Ti precipitates less than 0.1 ⁇ in diameter equivalent to 1.0 X 10 3 / Since it was nun 2 or less, this was set as the upper limit.
  • the slab heating of hot rolling must be performed in two continuous cycles to detoxify BN and / or TiN using sulfides including MnS, Cu 2 S and their composite sulfides as nuclei.
  • sulfides including MnS, Cu 2 S and their composite sulfides as nuclei.
  • Mn is increased to 0.4% or more
  • precipitation and growth of MnS become remarkable in a temperature range of 1150 ° C or more, but solid solution progresses when the temperature exceeds 1250 ° C. Therefore, the heating temperature in the former stage was set to 1150 ° C or higher and 1250 ° C or lower. Since the growth rate of MnS is high, a residence time of 5 minutes or more in this temperature range is sufficient.
  • the heating temperature in the subsequent stage is set to less than 1150 ° C, and the lower limit temperature is set to 1050 ° from the viewpoint of ensuring rollability. C. If the subsequent heating temperature is lower than 1050 ° C, the precipitation of TiN proceeds, but the formation of single and fine precipitates increases during hot rolling due to insufficient compounding with sulfides.
  • the heating time in the latter stage was set to 15 minutes or more in consideration of the precipitation time of TiN and BN. Even better The magus lasts more than 30 minutes.
  • the exit temperature of the finish rolling of hot rolling is higher than 800 ° C as much as possible at temperatures below ⁇ ⁇ ⁇ transformation.
  • Higher magnetic flux density results in higher magnetic flux density, but the temperature is moderated by the amount of Sn added Therefore, when Sn was added, it was specified as T ⁇ 900_1000XSn [% by mass] in consideration of the degree of relaxation.
  • the hot rolled sheet was pickled, cold rolled to a sheet thickness of 0.50 mm, subjected to finish annealing at 825 ° C for 10 seconds, and then subjected to strain relief annealing at 750 ° C for 2 hours.
  • the crystal grain size, iron loss and magnetic flux density of the sample thus obtained were measured, and the precipitate was observed with a transmission electron microscope.
  • Table 5 in Samples 7 to 12 with Mn of 0.4% or more, good iron loss was obtained when the average crystal grain size after strain relief annealing was 50 ⁇ or more, and the number ratio of composite precipitation Also exceeded 10%.
  • samples 8, 9, 11, and 12, which satisfy 855 ⁇ 900-1000 XSn a magnetic flux density about 0.02T higher was obtained.
  • the hot-rolled sheet is pickled, cold-rolled to a sheet thickness of 0.50 mm, subjected to finish annealing at 825 ° C for 10 seconds, and then subjected to strain relief annealing at 750 ° C for 2 hours to obtain precipitates and grains of the steel sheet. The diameter was observed and the iron loss was measured.
  • samples 7 and 8 as shown in Table 7 Mn is the and Ti at 0.4% or more and 0.0015% or less, at 10, 11, sulfide density after stress relief annealing is 3.0 X10 5 or less, the average crystal grain Good iron loss was obtained when the diameter was 50 / xm or more.
  • a large amount of spherical sulfides with a diameter of 0.2 to 0.3 ⁇ A large number of Ti precipitates were found on the outer periphery of the material.
  • the sulfides found in these samples were as small as 0.1 m or less in diameter, and many sulfides contained fine Ti precipitates.
  • Samples 9 and 12 with Mn values of 0.4% or more, but with a content of more than 0015% also had a high sulfide density after strain relief annealing, a small average crystal grain size, and relatively poor iron loss.
  • the sulfides varied widely in the range of 0.05 to 0.3 m in diameter, and the composite morphology with Ti precipitates also varied at the outer or center of the sulfides. Note that the distribution density of Ti precipitates having a diameter less than 0.1 ⁇ was as low as less than 1.0 ⁇ 10 3 / mm 2 in all samples.
  • the hot-rolled sheet thus obtained was pickled, cold-rolled to a sheet thickness of 0.50 mm, subjected to finish annealing at 850 ° C for 5 seconds, and then subjected to strain relief annealing at 750 ° C for 2 hours.
  • the precipitate and the crystal grain size were observed, and the iron loss was measured.
  • the sulfide density after strain relief annealing was 3.0 ⁇ 10 5 Thereafter, the average crystal grain size became 50 ⁇ m or more, and good iron loss was obtained.

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  • Physics & Mathematics (AREA)
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  • Organic Chemistry (AREA)
  • Materials Engineering (AREA)
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  • Crystallography & Structural Chemistry (AREA)
  • Dispersion Chemistry (AREA)
  • Power Engineering (AREA)
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  • Soft Magnetic Materials (AREA)

Abstract

Il est prévu un acier électromagnétique non orienté d'une excellente capacité à fabriquer des ébauches et également une perte de fer stable et bonne après recuit pour soulagement des contraintes, possédant une composition chimique, en pourcentage de masse, telle que Si : 1,5 % ou moins, Mn: 0,4 à 1,5 %, Sol.Al: 0,01 à 0,04 %, Ti: 0,0015% ou moins, N: 0,0030 % ou moins, S: 0,0010 à 0,0040%, Sn: 0,01 à 0,50%, B: une quantité satisfaisant à la relation 0,5 ≤ B/N ≤ 1,5, et le solde : Fe et les inévitables impuretés, où 10 % ou davantage, en termes de nombre de pièces, du sulfure contenant des précipitats de Mn sous forme composite avec un précipitat B, et où il possède un diamètre de grain de cristal inférieur ou égal à 30 µm et présente un diamètre de grain de cristal supérieur ou égal à 50 µm après recuit de soulagement des contraintes à 750°C pendant 2 heures ; et un procédé de fabrication de l’acier magnétique non orienté ci-dessus qui consiste à maintenir une brame pour laminage à chaud à une température de 1150 à 1250°C pendant 5 minutes ou davantage, puis à la maintenir à une température de 1050°C ou davantage et inférieure à 1150°C pendant 15 minutes ou davantage, puis juste après, à soumettre la brame résultante à un laminage à chaud à une température de finition de sortie T (°C) de T ≥ 900 - 1000 x Sn [% en masse].
PCT/JP2005/007653 2004-04-16 2005-04-15 Feuille d’acier électromagnétique non orienté, d’une excellente capacité à fabriquer les ébauches et d’excellentes caractéristiques magnétiques après recuit de suppression des contraintes, et procédé de fabrication de celle-ci Ceased WO2005100627A1 (fr)

Priority Applications (1)

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JP2006512410A JP4660474B2 (ja) 2004-04-16 2005-04-15 打抜き加工性と歪取焼鈍後の磁気特性に優れた無方向性電磁鋼板とその製造方法

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JP2004-121446 2004-04-16
JP2004121446 2004-04-16
JP2005-045222 2005-02-22
JP2005045222 2005-02-22

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WO2005100627A1 true WO2005100627A1 (fr) 2005-10-27

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KR (1) KR100872607B1 (fr)
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JPWO2022113264A1 (fr) * 2020-11-27 2022-06-02
WO2022113263A1 (fr) 2020-11-27 2022-06-02 日本製鉄株式会社 Tôle en acier électromagnétique non orienté ainsi que procédé de fabrication de celle-ci, et tôle en acier laminée à chaud
WO2022219742A1 (fr) 2021-04-14 2022-10-20 日本製鉄株式会社 Tôle d'acier laminée à chaud pour tôle d'acier électrique non orientée et son procédé de fabrication
WO2024080140A1 (fr) 2022-10-14 2024-04-18 Ｊｆｅスチール株式会社 Tôle d'acier électromagnétique non orientée et son procédé de fabrication
WO2024142579A1 (fr) 2022-12-27 2024-07-04 Ｊｆｅスチール株式会社 Tôle d'acier magnétique non orientée présentant une excellente aptitude au poinçonnage

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JP6044504B2 (ja) * 2012-10-23 2016-12-14 トヨタ自動車株式会社 希土類磁石の製造方法
TWI751812B (zh) * 2020-11-27 2022-01-01 日商日本製鐵股份有限公司 無方向性電磁鋼板及其製造方法、以及熱軋鋼板
US12024762B2 (en) * 2021-04-02 2024-07-02 Nippon Steel Corporation Non-oriented electrical steel sheet

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Publication number Priority date Publication date Assignee Title
JPH0387313A (ja) * 1989-08-30 1991-04-12 Kawasaki Steel Corp 高透磁率鋼板の製造方法
JPH05140649A (ja) * 1991-07-25 1993-06-08 Nippon Steel Corp 磁気特性が優れた無方向性電磁鋼板の製造方法
JPH1088298A (ja) * 1996-09-19 1998-04-07 Nkk Corp 無方向性電磁鋼板
JP2003064456A (ja) * 2001-08-27 2003-03-05 Sumitomo Metal Ind Ltd セミプロセス用無方向性電磁鋼板とその製造方法

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0387313A (ja) * 1989-08-30 1991-04-12 Kawasaki Steel Corp 高透磁率鋼板の製造方法
JPH05140649A (ja) * 1991-07-25 1993-06-08 Nippon Steel Corp 磁気特性が優れた無方向性電磁鋼板の製造方法
JPH1088298A (ja) * 1996-09-19 1998-04-07 Nkk Corp 無方向性電磁鋼板
JP2003064456A (ja) * 2001-08-27 2003-03-05 Sumitomo Metal Ind Ltd セミプロセス用無方向性電磁鋼板とその製造方法

Cited By (17)

* Cited by examiner, † Cited by third party
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JP7492163B2 (ja) 2020-11-27 2024-05-29 日本製鉄株式会社 無方向性電磁鋼板およびその製造方法、ならびに熱延鋼板
WO2022113263A1 (fr) 2020-11-27 2022-06-02 日本製鉄株式会社 Tôle en acier électromagnétique non orienté ainsi que procédé de fabrication de celle-ci, et tôle en acier laminée à chaud
WO2022113264A1 (fr) 2020-11-27 2022-06-02 日本製鉄株式会社 Tôle en acier électromagnétique non orienté ainsi que procédé de fabrication de celle-ci, et tôle en acier laminée à chaud
KR102871272B1 (ko) 2020-11-27 2025-10-15 닛폰세이테츠 가부시키가이샤 무방향성 전자 강판 및 그 제조 방법, 그리고 열연 강판
CN116457477A (zh) * 2020-11-27 2023-07-18 日本制铁株式会社 无取向性电磁钢板及其制造方法、以及热轧钢板
KR20230109727A (ko) 2020-11-27 2023-07-20 닛폰세이테츠 가부시키가이샤 무방향성 전자 강판 및 그 제조 방법, 그리고 열연 강판
KR20230110338A (ko) 2020-11-27 2023-07-21 닛폰세이테츠 가부시키가이샤 무방향성 전자 강판 및 그 제조 방법, 그리고 열연 강판
CN116547394A (zh) * 2020-11-27 2023-08-04 日本制铁株式会社 无取向性电磁钢板及其制造方法、以及热轧钢板
JPWO2022113264A1 (fr) * 2020-11-27 2022-06-02
EP4253575A4 (fr) * 2020-11-27 2023-12-20 Nippon Steel Corporation Tôle en acier électromagnétique non orienté ainsi que procédé de fabrication de celle-ci, et tôle en acier laminée à chaud
KR20230136755A (ko) 2021-04-14 2023-09-26 닛폰세이테츠 가부시키가이샤 무방향성 전자 강판용 열연 강판 및 그 제조 방법
WO2022219742A1 (fr) 2021-04-14 2022-10-20 日本製鉄株式会社 Tôle d'acier laminée à chaud pour tôle d'acier électrique non orientée et son procédé de fabrication
WO2024080140A1 (fr) 2022-10-14 2024-04-18 Ｊｆｅスチール株式会社 Tôle d'acier électromagnétique non orientée et son procédé de fabrication
KR20250087661A (ko) 2022-10-14 2025-06-16 제이에프이 스틸 가부시키가이샤 무방향성 전자 강판과 그의 제조 방법
WO2024142579A1 (fr) 2022-12-27 2024-07-04 Ｊｆｅスチール株式会社 Tôle d'acier magnétique non orientée présentant une excellente aptitude au poinçonnage
KR20250096858A (ko) 2022-12-27 2025-06-27 제이에프이 스틸 가부시키가이샤 타발 가공성이 우수한 무방향성 전기 강판
EP4624618A1 (fr) 2022-12-27 2025-10-01 JFE Steel Corporation Tôle d'acier magnétique non orientée présentant une excellente aptitude au poinçonnage

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KR100872607B1 (ko) 2008-12-09
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KR20060134154A (ko) 2006-12-27
JPWO2005100627A1 (ja) 2008-03-06

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