WO2023074476A1 - 方向性電磁鋼板の製造方法 - Google Patents

方向性電磁鋼板の製造方法 Download PDF

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Publication number
WO2023074476A1
WO2023074476A1 PCT/JP2022/038828 JP2022038828W WO2023074476A1 WO 2023074476 A1 WO2023074476 A1 WO 2023074476A1 JP 2022038828 W JP2022038828 W JP 2022038828W WO 2023074476 A1 WO2023074476 A1 WO 2023074476A1
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Prior art keywords
steel sheet
coil
atmosphere
temperature
annealing
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Ceased
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PCT/JP2022/038828
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English (en)
French (fr)
Japanese (ja)
Inventor
魁 河原
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JFE Steel Corp
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JFE Steel Corp
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Priority to JP2023513544A priority Critical patent/JP7662030B2/ja
Priority to EP22886804.8A priority patent/EP4394057A4/en
Priority to US18/691,886 priority patent/US20250122589A1/en
Priority to CN202280069414.2A priority patent/CN118103531A/zh
Priority to KR1020247011678A priority patent/KR20240066266A/ko
Publication of WO2023074476A1 publication Critical patent/WO2023074476A1/ja
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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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
    • 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
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the working steps
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the heat treatment
    • C21D8/1255—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the heat treatment with diffusion of elements, e.g. decarburising, nitriding
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the heat treatment
    • C21D8/1261—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the heat treatment
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1277—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular surface treatment
    • C21D8/1283—Application of a separating or insulating coating
    • 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
    • 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
    • H01F1/16—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 in the form of sheets
    • H01F1/18—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 in the form of sheets with insulating coating
    • 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
    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/05—Grain orientation
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/20—Recycling

Definitions

  • the present invention relates to a method for manufacturing a grain-oriented electrical steel sheet having excellent magnetic properties.
  • Grain-oriented electrical steel sheets have extremely excellent magnetic properties in the rolling direction, and are mainly used as materials for cores inside transformers. In recent years, grain-oriented electrical steel sheets are required to have further improved magnetic properties in order to improve the energy use efficiency of such transformers.
  • one of the measures for improving such magnetic properties is to promote secondary recrystallization in grain-oriented electrical steel sheets. It is known to apply an annealing separating agent containing Ti to the surface of the steel sheet in order to improve the adhesion between the steel sheets and promote the formation of the forsterite undercoat during the finish annealing that promotes the secondary recrystallization. At that time, it is also known that Ti contained in such an annealing separator penetrates into the steel sheet and can deteriorate the state of undercoating formation and magnetic properties.
  • Patent Document 1 discloses that the atmosphere for purification annealing (finish annealing) is set to a mixed atmosphere of H 2 and N 2 in a temperature range of 1150 to 1250 ° C during the production of grain-oriented electrical steel sheets.
  • a technique is disclosed in which Ti is prevented from entering or remaining in the steel by
  • finish annealing that also serves as refinement annealing, it is customary to coil the steel sheet and place it in an annealing furnace for long-time annealing.
  • purification annealing is performed according to the description of Patent Document 1
  • Ti penetrates into the steel in the middle winding portion and the inner winding portion of the coil during annealing as shown in FIG.
  • the amount of Ti in the steel was large in the outer winding part, and the amount of Ti in the steel as a whole varied.
  • the present invention has been made in view of the above circumstances, and provides a method for producing a grain-oriented electrical steel sheet for obtaining a grain-oriented electrical steel sheet having excellent magnetic properties with a good formation of an undercoat.
  • the task is to
  • the inventors of the present invention have found that, in the finish annealing process that promotes secondary recrystallization of the grain-oriented electrical steel sheet, the temperature of the coil composed of the steel sheet and the atmosphere gas are controlled. As a result, it is possible to effectively reduce the amount of Ti contained in the annealing separator applied to the surface of the steel sheet that penetrates into the steel sheet and the amount of Ti that remains in the steel, as well as prevent its variation.
  • the present inventors have found that a grain-oriented electrical steel sheet having excellent magnetic properties can be obtained because of the favorable formation of the grains, and have completed the present invention.
  • the gist of the configuration of the present invention is as follows. 1. An annealing separator containing 1.0 to 20 parts by mass of Ti oxide per 100 parts by mass of MgO on the surface of a steel sheet that has been cold-rolled to a final thickness and then decarburized and annealed. After applying and drying, the steel sheet is placed in a finish annealing furnace in a coil state and subjected to finish annealing to obtain a grain-oriented electrical steel sheet. In the temperature rising process of the finish annealing, the atmosphere when the maximum temperature of the coil reaches 1100 ° C. is an atmosphere of H 2 : 100 vol%, and the maximum temperature of the coil is changed from the time when the maximum temperature of the coil reaches 1100 ° C.
  • the H 2 : 100 vol% atmosphere is changed to an H 2 atmosphere containing 5 vol% or more N 2 . , a method for producing a grain-oriented electrical steel sheet.
  • the time for changing the atmosphere of the finish annealing from the H 2 atmosphere to the atmosphere containing N 2 has an upper limit, and the temperature difference in the coil is reduced.
  • FIG. 3 is a diagram showing analysis values of Ti in the steel sheet in the outer winding, middle winding, and inner winding of a conventional coiled steel sheet.
  • the method for producing a grain-oriented electrical steel sheet according to the present invention is particularly characterized by the conditions of finish annealing.
  • a steel sheet when simply referred to as a steel sheet, it means a grain-oriented electrical steel sheet.
  • a steel sheet having a final thickness by cold rolling is subjected to decarburization annealing, and then an annealing separation containing 1.0 to 20 parts by mass of Ti oxide with respect to 100 parts by mass of MgO. After the agent is applied and dried, final annealing is applied.
  • the final plate thickness is a plate thickness generally used as a grain-oriented electrical steel sheet, and specifically, the range of 0.35 mm or less is preferable.
  • the cold rolling conditions that are normally used for the production of grain-oriented electrical steel sheets can be used without particular limitations.
  • the conditions of decarburization annealing that are usually used for producing grain-oriented electrical steel sheets can be used without particular limitations.
  • an annealing separator containing 1.0 to 20 parts by mass of Ti oxide is used with respect to 100 parts by mass of MgO.
  • the Ti oxide is not particularly limited, but TiO 2 is preferable. If the content of the oxide of Ti in the annealing separator is less than 1.0 parts by mass per 100 parts by mass of MgO, the film formation during the final annealing will be insufficient. On the other hand, if the content of Ti oxides exceeds 20 parts by mass per 100 parts by mass of MgO in the annealing separator, Ti increases intrusion into the steel, resulting in magnetic deterioration. From the same point of view, the content of Ti oxide in the annealing separator is preferably 2.0 parts by mass or more, preferably 10 parts by mass or less, and more preferably 8 parts by mass or less with respect to 100 parts by mass of MgO.
  • the coating of the annealing separator the method and conditions for applying the annealing separator that are commonly used in the production of grain-oriented electrical steel sheets can be used without particular limitations.
  • the method and conditions for drying the annealing separator that are commonly used in the production of grain-oriented electrical steel sheets can be used without particular limitations.
  • the surface of the steel sheet is coated with an annealing separator and dried, and then the steel sheet is placed in a final annealing furnace in the form of a coil and subjected to final annealing.
  • the atmosphere at least when the maximum temperature of the coil reaches 1100° C. must be an atmosphere of H 2 : 100 vol %. This is because nitrogen will penetrate into the steel sheet and degrade the magnetism if these conditions are not satisfied.
  • the maximum temperature of the coil may be allowed to reach 1100°C while maintaining the atmosphere of H 2 : 100 vol% before the maximum temperature of the coil reaches 1100°C, and the temperature may be continued.
  • the maximum temperature of the coil was determined by placing thermocouples at the bottom of the sample coil so as to contact two points, the outer winding side and the center part of the middle winding. Defined as the temperature measured by the pair. On the other hand, the minimum temperature of the coil is defined as the temperature measured by the thermocouple at the center of the middle winding.
  • the temperature difference between the maximum temperature and the minimum temperature of the coil is within 75 ° C. from the time when the maximum temperature of the coil reaches 1100 ° C. in the temperature rising process of the finish annealing, and By the time 15 hours have passed, the H 2 : 100 vol % atmosphere is changed to an H 2 atmosphere containing 5 vol % or more of N 2 .
  • the starting point for calculating the timing of changing to the H 2 atmosphere containing N 2 is the time when the maximum temperature of the coil reaches 1100°C.
  • the starting point of such timing is the time when the temperature reaches 1100 ° C., because if the temperature is lower than that, the Ti oxide (especially titanium oxide) in the annealing separator is not decomposed and the film is formed as TiN. Because it is not fixed inside.
  • the time for changing the atmosphere of H 2 100 vol % to the atmosphere of H 2 containing N 2 after the maximum temperature of the coil reaches 1100° C. shall be within 15 hours. This is because if the time exceeds 15 hours, Ti penetrates into the steel sheet and degrades the magnetism. From the same point of view, the time for changing the atmosphere of H 2 : 100 vol% to the H 2 atmosphere containing N 2 from the time the maximum temperature of the coil reaches 1100 ° C. is preferably within 12 hours, and within 10 hours. is more preferred.
  • the lower limit of such time is typically when the temperature difference between the highest and lowest coil temperatures is within 75°C. Moreover, the lower limit of such time is specifically about 8 hours.
  • the reaction between titanium and nitrogen may be insufficient.
  • the coiled steel sheet used in the present invention may have extremely large dimensions. In such a case, when the maximum temperature of the coil reaches 1100°C, the difference between the maximum temperature and the minimum temperature of the coil is usually not within 75°C. , it takes some time.
  • the temperature difference between the maximum temperature and the minimum temperature of the coil is It is important that the temperature is within 75°C. That is, it is essential that the temperature difference between the maximum and minimum coil temperatures is within 75°C by the time 15 hours have passed since the maximum temperature of the coil reached 1100°C. If the atmosphere is changed while the temperature difference between the maximum temperature and the minimum temperature exceeds 75°C, the formation of the undercoat on the inner winding of the coil deteriorates. On the other hand, the smaller the temperature difference between the maximum temperature and the minimum temperature of the coil at the timing of changing the atmosphere, the better, and it may be 0°C.
  • the industrial temperature is about 50°C. In order to control the temperature difference as described above, it is effective to apply a method of suppressing heat input from the outside, particularly heat input to the outer winding side, at appropriate timing.
  • the H 2 atmosphere containing N 2 after the change is an atmosphere containing 5 vol % or more of N 2 . This is because if the amount of N 2 is less than 5 vol %, the reaction with titanium becomes insufficient.
  • the upper limit of the amount of N 2 is not particularly limited, but considering productivity, it is about 25 vol% or less. From the same point of view, the content of N 2 in the H 2 atmosphere after the change is preferably 8 vol% or more, preferably 20 vol% or less, and more preferably 15 vol% or less.
  • the outer winding of the coil is defined as a range of 20% of the coil radius from the outermost circumference of the coil.
  • the inner winding of the coil is defined as a range of 20% of the coil radius from the innermost circumference of the coil.
  • the middle turn of the coil is defined as the range excluding the outer and inner turns of the coil.
  • the outer winding portion, the inner winding portion, and the middle winding portion of the coil are defined as portions having the respective ranges described above.
  • Conditions for finish annealing other than the conditions for finish annealing described above are not particularly limited, and conventional methods can be followed. Moreover, regarding the conditions of the manufacturing method related to the steel sheet not described above, any conventional method can be used.
  • a cold-rolled steel sheet with a thickness of 0.23 mm was subjected to decarburization annealing, and then the surface of the steel sheet was coated with an annealing separator containing 5 parts by mass of TiO 2 per 100 parts by mass of MgO. After drying, the steel sheet was placed in a coiled state in a finish annealing furnace and subjected to finish annealing to produce a grain-oriented electrical steel sheet.
  • thermocouples were arranged on the bottom of the coil so as to contact two places, the outer winding portion and the middle winding central portion.
  • the iron loss W 17/50 per 1 kg of the steel sheet when magnetized to 1.7 T in an alternating magnetic field with an excitation frequency of 50 Hz was measured for the obtained grain-oriented electrical steel sheet (coil).
  • Table 1 shows the iron loss W 17/50 in the outer winding of the coil.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Metallurgy (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Organic Chemistry (AREA)
  • Electromagnetism (AREA)
  • Manufacturing & Machinery (AREA)
  • Dispersion Chemistry (AREA)
  • Power Engineering (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)
PCT/JP2022/038828 2021-10-29 2022-10-18 方向性電磁鋼板の製造方法 Ceased WO2023074476A1 (ja)

Priority Applications (5)

Application Number Priority Date Filing Date Title
JP2023513544A JP7662030B2 (ja) 2021-10-29 2022-10-18 方向性電磁鋼板の製造方法
EP22886804.8A EP4394057A4 (en) 2021-10-29 2022-10-18 Production method for grain-oriented electrical steel sheet
US18/691,886 US20250122589A1 (en) 2021-10-29 2022-10-18 Method of manufacturing grain-oriented electrical steel sheet
CN202280069414.2A CN118103531A (zh) 2021-10-29 2022-10-18 取向性电磁钢板的制造方法
KR1020247011678A KR20240066266A (ko) 2021-10-29 2022-10-18 방향성 전기 강판의 제조 방법

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Application Number Priority Date Filing Date Title
JP2021-178359 2021-10-29
JP2021178359 2021-10-29

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WO2023074476A1 true WO2023074476A1 (ja) 2023-05-04

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US (1) US20250122589A1 (https=)
EP (1) EP4394057A4 (https=)
JP (1) JP7662030B2 (https=)
KR (1) KR20240066266A (https=)
CN (1) CN118103531A (https=)
WO (1) WO2023074476A1 (https=)

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS6475627A (en) * 1987-09-18 1989-03-22 Nippon Steel Corp Production of grain oriented electrical steel sheet having extremely high magnetic flux density
JPH05195072A (ja) 1991-10-01 1993-08-03 Kawasaki Steel Corp 歪取り焼鈍による鉄損劣化がなく被膜特性に優れる方向性けい素鋼板の製造方法
JP2004285442A (ja) * 2003-03-24 2004-10-14 Jfe Steel Kk 方向性電磁鋼板の仕上焼鈍方法
JP2012031512A (ja) * 2010-06-29 2012-02-16 Jfe Steel Corp 方向性電磁鋼板およびその製造方法
JP2015175036A (ja) * 2014-03-17 2015-10-05 Ｊｆｅスチール株式会社 方向性電磁鋼板の製造方法
WO2017006955A1 (ja) * 2015-07-08 2017-01-12 Ｊｆｅスチール株式会社 方向性電磁鋼板とその製造方法

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS6475627A (en) * 1987-09-18 1989-03-22 Nippon Steel Corp Production of grain oriented electrical steel sheet having extremely high magnetic flux density
JPH05195072A (ja) 1991-10-01 1993-08-03 Kawasaki Steel Corp 歪取り焼鈍による鉄損劣化がなく被膜特性に優れる方向性けい素鋼板の製造方法
JP2004285442A (ja) * 2003-03-24 2004-10-14 Jfe Steel Kk 方向性電磁鋼板の仕上焼鈍方法
JP2012031512A (ja) * 2010-06-29 2012-02-16 Jfe Steel Corp 方向性電磁鋼板およびその製造方法
JP2015175036A (ja) * 2014-03-17 2015-10-05 Ｊｆｅスチール株式会社 方向性電磁鋼板の製造方法
WO2017006955A1 (ja) * 2015-07-08 2017-01-12 Ｊｆｅスチール株式会社 方向性電磁鋼板とその製造方法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of EP4394057A4

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JP7662030B2 (ja) 2025-04-15
KR20240066266A (ko) 2024-05-14
US20250122589A1 (en) 2025-04-17
EP4394057A1 (en) 2024-07-03
JPWO2023074476A1 (https=) 2023-05-04
EP4394057A4 (en) 2025-01-08
CN118103531A (zh) 2024-05-28

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