Classifications

• • 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
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21B—ROLLING OF METAL
  • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
  • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21B—ROLLING OF METAL
  • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
  • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
  • B21B1/24—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process
  • B21B1/28—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process by cold-rolling, e.g. Steckel cold mill
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21B—ROLLING OF METAL
  • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
  • B21B3/02—Rolling special iron alloys, e.g. stainless steel
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  • 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
  • C21D6/002—Heat treatment of ferrous alloys containing Cr
• • 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
  • C21D6/005—Heat treatment of ferrous alloys containing Mn
• • 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
  • C21D6/007—Heat treatment of ferrous alloys containing Co
• • 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
  • C21D8/1222—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 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
  • C21D8/1261—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
• • 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
  • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
• • 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
  • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
• • 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
  • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
• • 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
  • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
• • 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
  • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
• • 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
  • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
• • 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
  • C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
• • 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
  • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
• • 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
  • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
• • 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
  • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
• • 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
  • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
  • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
  • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
  • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
• • 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
  • H01F1/147—Alloys characterised by their composition
  • H01F1/14766—Fe-Si based alloys
  • H01F1/14775—Fe-Si based alloys in the form of sheets
• • 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
  • H01F1/14791—Fe-Si-Al based alloys, e.g. Sendust
• • 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
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21B—ROLLING OF METAL
  • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
  • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
  • B21B2001/221—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length by cold-rolling
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C2202/00—Physical properties
  • C22C2202/02—Magnetic
• • 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 non-oriented electrical steel sheet and its manufacturing method.
• a motor core is divided into a stator core and a rotor core, but the rotor core of an HEV drive motor is subject to a large centrifugal force due to its large outer diameter.
• the rotor core has a very narrow portion (width: 1 to 2 mm) called a rotor core bridge portion due to its structure, and this portion is in a particularly high stress state during motor operation. Therefore, in order to prevent the rotor core from being damaged by centrifugal force, the magnetic steel sheets used for the rotor core must have high strength.
• the magnetic steel sheet used for the stator core is driven in a high frequency range in order to achieve miniaturization and high output of the motor. Therefore, it is ideal that the magnetic steel sheet used for the motor core has high strength for the rotor core and high magnetic flux density and low iron loss in the high frequency range for the stator core.
• a rotor core material and a stator core material are simultaneously obtained by punching from the same material steel plate, and then each steel plate is laminated to form a rotor core and a stator core. Assemble is preferred.
• Patent Document 1 discloses manufacturing a high-strength non-oriented electrical steel sheet and punching the steel sheet to produce a rotor core material and a stator core.
• a technology is disclosed in which a high-strength rotor core and a low-iron-loss stator core are manufactured from the same material by extracting and laminating materials, assembling a rotor core and a stator core, and then subjecting only the stator core to strain relief annealing.
• Patent Document 2 discloses a method of increasing the specific resistance of steel by adding Cr to reduce iron loss in a high frequency range. is disclosed.
• the present invention has been made to solve the above problems, and an object of the present invention is to provide a non-oriented electrical steel sheet having high strength and high magnetic flux density, high frequency and low core loss even when strain relief annealing is performed, and a method for producing the same. is to provide
• the present inventors refined the average crystal grain size d to 50 ⁇ m or less, and the sum of the area ratios of crystal grains with ⁇ 100> oriented in the rolling direction or the direction perpendicular to the rolling direction S A and the sum of the area ratios of grains with ⁇ 111> orientation in the rolling direction or perpendicular to the rolling direction, S B , satisfies S A ⁇ S B ⁇ 0. It has been found that a non-oriented electrical steel sheet having strength characteristics and high magnetic flux density and low iron loss in a high frequency range can be obtained even when strain relief annealing is performed as a material for a stator core. was Furthermore, it was found that the area ratio of crystals oriented in a specific orientation can be controlled by setting the rapid heating stop temperature, intermediate holding time, etc. during heating in the annealing process within appropriate ranges.
• the present invention was made based on such findings, and has the following configuration.
• the non-oriented electrical steel sheet according to the present invention is, in mass %, C: 0.010% or less, Si: 1.0% or more and 5.0% or less, Mn: 0.05% or more and 5.0% or less, P: 0.1% or less, S: 0.01 % or less, Al: 3.0% or less, N: 0.005% or less, the balance being Fe and unavoidable impurities, the average grain size being 50 ⁇ m or less, and crystal grains with ⁇ 100> orientation in the rolling direction or the direction perpendicular to the rolling direction and the sum S B of the area ratios of grains with ⁇ 111> oriented in the rolling direction or perpendicular to the rolling direction satisfies S A ⁇ S B ⁇ 0.
• the sum of the area ratios of grains with ⁇ 100> orientation in the 45° and -45° rolling directions and the area ratio of the grains with ⁇ 111> orientation in the 45° and -45° rolling directions The sum S D preferably satisfies 5 ⁇ S C ⁇ S D ⁇ 0.
• At least one group of components from groups A to D below Cu: 0% to 0.5%, Ni: 0% to 0.5%, W: 0% to 0.05%, Ti: 0 % or more 0.005%, Nb: 0% or more and 0.005% or less, V: 0% or more and 0.010% or less, Ta: 0% or more and 0.002% or less, B: 0% or more and 0.002% or less, Ga: 0% or more and 0.005% or less, It is preferable to contain one or more selected from Pb: 0% to 0.002%, As: 0% to 0.05%, and Ge: 0% to 0.05%.
• Group A Mo: 0.01% to 0.20%
• Group B Cr: 0.1% to 5.0%
• Group C Ca: 0.001% to 0.10%, Mg: 0.001% to 0.10% and REM: 0.001% 1 or 2 or more of 0.10% or less Group D; Sn: 0.001% or more and 0.20% or less and Sb: any one or 2 of 0.001% or more and 0.20% or less
• a method for manufacturing a non-oriented electrical steel sheet according to the present invention is a method for manufacturing a non-oriented electrical steel sheet according to the present invention, wherein a steel material having the composition of the non-oriented electrical steel sheet is subjected to hot rolling.
• the average temperature increase rate V1 to the holding temperature T1 from 400°C to 600°C is 50°C/s or more, the holding time t at the holding temperature T1 is 1 second to 10 seconds, and the holding temperature T1 to 750°C and an annealing step of heating to an annealing temperature T2 of 750°
• the cold rolling step is performed with a work roll diameter of 150 mm ⁇ or more in the final pass, a draft of the final pass of 15% or more, and a strain rate of the final pass. Conducted under conditions of 100 s -1 or more and 1300 s -1 or less.
• the present invention it is possible to provide a non-oriented electrical steel sheet with high strength and high magnetic flux density, high frequency and low core loss even when subjected to strain relief annealing, and a method for producing the same. Therefore, by using the non-oriented electrical steel sheet and the method for manufacturing the same according to the present invention, it is possible to achieve high motor efficiency.
• C 0.010% or less
• C is a harmful element that forms carbides during use of the motor, causes magnetic aging, and deteriorates the core loss characteristics of the motor.
• the C content in the steel sheet should be 0.010% or less. Preferably it is 0.004% or less.
• the lower limit of the amount of C to be added is not particularly specified, it is preferably about 0.0001% because steel sheets with an excessively reduced amount of C are very expensive.
• Si 1.0% to 5.0% Si has the effect of increasing the specific resistance of steel and reducing iron loss, and also has the effect of increasing the strength of steel through solid-solution strengthening.
• the amount of Si added should be 1.0% or more.
• the amount of Si added exceeds 5.0%, the saturation magnetic flux density is lowered and the magnetic flux density is significantly lowered, so the upper limit is made 5.0% or less. Therefore, the amount of Si added should be in the range of 1.0% or more and 5.0% or less. The range is preferably 1.5% or more and less than 4.5%, more preferably 2.0% or more and less than 4.0%.
• Mn 0.05% to 5.0%
• Mn is an element useful for increasing the specific resistance and strength of steel. In order to obtain such effects, it is necessary to contain 0.05% or more of Mn. On the other hand, if the addition exceeds 5.0%, the precipitation of MnC may be accelerated and the magnetic properties of the motor may deteriorate, so the upper limit is made 5.0%. Therefore, the amount of Mn added should be 0.05% or more and 5.0% or less. The range is preferably 0.1% or more and 3.0% or less.
• P 0.1% or less P is a useful element used for adjusting the strength (hardness) of steel. However, if the amount of P added exceeds 0.1%, the toughness decreases and cracks are likely to occur during working, so the upper limit is made 0.1%. Although the lower limit is not specified, it is set to 0.001% because steel sheets with excessively reduced P are very expensive.
• the amount of P added is preferably in the range of 0.003% or more and 0.08% or less.
• S 0.01% or less S is an element that forms fine precipitates and adversely affects the iron loss characteristics of the motor.
• the upper limit is made 0.01%.
• the lower limit is not specified, it is set to 0.0001% because steel sheets with excessively reduced S are very expensive.
• the amount of S added is preferably in the range of 0.0003% to 0.0080%.
• Al 3.0% or less
• Al, like Si, is a useful element that has the effect of increasing the specific resistance of steel and reducing iron loss. In order to obtain such effects, it is preferable to add 0.005% or more. More preferably 0.010% or more, still more preferably 0.015% or more. On the other hand, adding more than 3.0% promotes nitridation of the surface of the steel sheet and may degrade the magnetic properties, so the upper limit is made 3.0%. More preferably, it is 2.0% or less.
• N 0.0050% or less N is an element that forms fine precipitates and adversely affects iron loss characteristics.
• the amount of addition exceeds 0.0050%, the adverse effect becomes remarkable, so the upper limit is made 0.0050%.
• the lower limit is not specified, it is set to 0.0005% because steel sheets with excessively reduced N are very expensive.
• the amount of N added is preferably in the range of 0.0008% to 0.0030%.
• the balance other than the above components is Fe and unavoidable impurities.
• Co, Zn, Mo, Cr, Ca, Mg, REM, Sn, Sb, Cu, Ni, W, Ti, Nb, V, Ta, B, Ga , Pb, As and Ge can be contained within the following range.
• Co 0.0005% or more and 0.0050% or less
• Co has crystals with ⁇ 100> orientation in the rolling direction or the direction perpendicular to the rolling direction when the rapid heating stop temperature during heating in the annealing process, the intermediate holding time, etc. are set in an appropriate range. It has the effect of increasing the sum of area ratios S A of grains and decreasing the sum of area ratios S B of crystal grains with ⁇ 111> oriented in the rolling direction or the direction perpendicular to the rolling direction. That is, by adding a small amount of Co, S A ⁇ S B ⁇ 0 can be stably achieved. In order to obtain such effects, the amount of Co added should be 0.0005% or more.
• Co is preferably added in the range of 0.0005% or more and 0.0050% or less.
• Zn 0.0005% or more and 0.0050% or less
• Zn has a ⁇ 100> This has the effect of increasing the sum S C of the area ratios of grains oriented with ⁇ 111> oriented, and decreasing the sum S D of the area ratios of grains oriented with ⁇ 111> in the 45° rolling direction and the -45° rolling direction. That is, 5 ⁇ S C ⁇ S D ⁇ 0 can be stably achieved by adding a small amount of Zn. In order to obtain such an effect, the amount of Zn added should be 0.0005% or more. On the other hand, if Zn exceeds 0.0050%, the effect saturates, unnecessarily increasing the cost, so the upper limit is made 0.0050%. Therefore, Zn is preferably added in the range of 0.0005% or more and 0.0050% or less.
• Mo 0.01% to 0.20% Mo has the effect of forming fine carbides in the steel and increasing the strength of the steel sheet. In order to obtain such an effect, the amount of Mo added should be 0.01% or more. On the other hand, if the amount of Mo added exceeds 0.20%, carbides are excessively formed and iron loss deteriorates, so the upper limit is made 0.20%. Therefore, Mo is preferably added in the range of 0.01% or more and 0.20% or less.
• Cr 0.1% to 5.0% Cr has the effect of increasing the specific resistance of steel and reducing iron loss. In order to obtain such effects, the amount of Cr added should be 0.1% or more. On the other hand, if the amount of Cr added exceeds 0.1%, the saturation magnetic flux density is lowered and the magnetic flux density is remarkably lowered, so the upper limit is made 5.0%. Therefore, Cr is preferably added in the range of 0.1% or more and 5.0% or less.
• Ca 0.001% to 0.10% Ca is an element that fixes S as sulfide and contributes to the reduction of core loss. In order to obtain such effects, the amount of Ca added should be 0.001% or more. On the other hand, if the amount of Ca added exceeds 0.10%, the effect saturates, unnecessarily leading to an increase in cost, so the upper limit is made 0.10%. Therefore, Ca is preferably added in the range of 0.001% or more and 0.10% or less.
• Mg 0.001% to 0.10%
• Mg is an element that fixes S as a sulfide and contributes to the reduction of iron loss.
• the amount of Mg added should be 0.001% or more.
• the upper limit is made 0.10%. Therefore, it is preferable to add Mg in the range of 0.001% or more and 0.10% or less.
• REM 0.001% to 0.10% REM is a group of elements that fix S as sulfides and contribute to the reduction of iron loss. In order to obtain such effects, the amount of REM added should be 0.001% or more. On the other hand, if the amount of REM added exceeds 0.10%, the effect saturates, unnecessarily increasing the cost, so the upper limit is made 0.10%. Therefore, REM is preferably added in the range of 0.001% or more and 0.10% or less.
• Sn 0.001% or more and 0.20% or less
• Sn is an element that is effective in improving the magnetic flux density and reducing iron loss by improving the texture.
• the amount of Sn added should be 0.001% or more.
• Sn is preferably added in the range of 0.001% or more and 0.20% or less.
• Sb 0.001% or more and 0.20% or less
• Sb is an element that is effective in improving the magnetic flux density and reducing iron loss by improving the texture.
• the amount of Sb added should be 0.001% or more.
• Sb is preferably added in the range of 0.001% or more and 0.20% or less.
• Cu 0% to 0.5%
• Ni 0% to 0.5%
• Cu and Ni are elements that improve the toughness of steel and can be added as appropriate.
• the upper limit of the amount to be added is preferably 0.5%. More preferably, the amount of addition is in the range of 0.01% or more and 0.1% or less.
• W 0% or more and 0.05% or less W can be added as appropriate because it forms fine carbides and increases the strength of the steel sheet through precipitation strengthening, thereby improving the punching fatigue strength.
• the amount of addition exceeds the above range, excessive carbide is formed and iron loss deteriorates. Therefore, the amount of W to be added is in the range of 0% or more and 0.05% or less. A preferable upper limit of the amount to be added is 0.02%.
• Ti, Nb, V, and Ta form fine carbonitrides. It can be added as appropriate in order to improve the punching fatigue strength by forming and increasing the strength of the steel sheet by precipitation strengthening. On the other hand, if the addition amount exceeds the above range, carbonitrides are excessively formed, resulting in deterioration of iron loss. Therefore, the additive amounts of Ti, Nb, V, and Ta are Ti: 0% to 0.005%, Nb: 0% to 0.005%, V: 0% to 0.010%, and Ta: 0% to 0.002%. range. The upper limits of the preferred amount of addition are Ti: 0.002%, Nb: 0.002%, V: 0.005%, and Ta: 0.001%.
• B 0% to 0.002%
• Ga 0% to 0.005%
• the amounts of B and Ga to be added are respectively in the range of B: 0% to 0.002% and Ga: 0% to 0.005%.
• the upper limit of the preferable addition amount is B: 0.001% and Ga: 0.002%.
• Pb 0% or more and 0.002% or less Pb forms fine Pb particles and improves the punching fatigue strength by increasing the strength of the steel sheet through precipitation strengthening, so it can be added as appropriate.
• the amount of addition exceeds the above range, excessive Pb particles are formed and iron loss deteriorates. Therefore, the amount of Pb to be added is in the range of 0% or more and 0.002% or less. A preferable upper limit of the amount to be added is 0.001%.
• Ge 0% or more and 0.05% or less
• As and Ge are elements effective in improving magnetic flux density and reducing iron loss by improving the texture, and can be added as appropriate. However, even if it is added in excess of 0.05%, the above effect is saturated. For this reason, the upper limit of the amount to be added is preferably 0.05%. More preferably, the amount of addition is in the range of 0.002% or more and 0.01% or less.
• ⁇ Average crystal grain size d is 50 ⁇ m or less>> According to studies by the present inventors, the strength of the steel sheet decreases when the average grain size d is coarse. That is, the target strength characteristics can be achieved by setting the average crystal grain size d to 50 ⁇ m or less. Although the lower limit of the average crystal grain size d need not be specified, it is usually 5 ⁇ m or more when produced by the method described in the present invention.
• a steel material having the above chemical composition is subjected to hot rolling, hot-rolled sheet annealing, pickling, cold rolling, and annealing as necessary. It is a method of obtaining the above-described non-oriented electrical steel sheet according to the present invention by sequentially applying.
• the manufacturing method of the non-oriented electrical steel sheet according to the present invention as long as the composition, cold rolling, and annealing conditions specified in the present invention are within the scope of the present invention, otherwise known techniques may be used.
• the steel material is not particularly limited as long as it has the above composition.
• a method of melting the steel material is not particularly limited, and a known melting method using a converter or an electric furnace can be employed. From issues such as productivity, it is preferable to make a slab (steel material) by a continuous casting method after smelting. good.
• the hot rolling step is a step of hot rolling a steel material having the above composition to obtain a hot rolled sheet.
• the hot-rolling process is not particularly limited as long as it is a process in which a steel material having the above composition is heated and hot-rolled to obtain a hot-rolled sheet having a predetermined size, and a conventional hot-rolling process can be applied.
• a steel material is heated to a temperature of 1000°C or more and 1200°C or less, and the heated steel material is subjected to hot rolling at a finish rolling delivery temperature of 800°C or more and 950°C or less.
• hot rolling After hot rolling is completed, apply appropriate post-rolling cooling (for example, cool the temperature range from 450 ° C to 950 ° C at an average cooling rate of 20 ° C / s to 100 ° C / s),
• a hot-rolling process can be exemplified by coiling at a coiling temperature of 400° C. or higher and 700° C. or lower to form a hot-rolled sheet having a predetermined size and shape.
• the hot-rolled sheet annealing step is a step of normalizing the hot-rolled sheet by heating the hot-rolled sheet and maintaining it at a high temperature.
• the hot-rolled sheet annealing process is not particularly limited, and a common hot-rolled sheet annealing process can be applied. This step is not essential and can be omitted.
• the pickling process is a process of pickling the steel sheet after the hot-rolled sheet annealing process or the hot-rolled sheet when the hot-rolled sheet annealing process is omitted.
• the pickling process is not particularly limited as long as the pickling process can perform cold rolling on the steel sheet after pickling.
• a conventional pickling process using hydrochloric acid or sulfuric acid can be applied. This pickling process may be performed continuously in the same line as the hot-rolled sheet annealing process, or may be performed in a separate line.
• the cold rolling step is a step of cold rolling the pickled plate that has undergone the pickling step.
• the cold rolling process is not particularly limited as long as the steel sheet after pickling can be reduced to a desired thickness, and a common cold rolling process can be applied.
• the cold-rolled sheet may be cold-rolled twice or more with intermediate annealing to obtain a cold-rolled sheet having a predetermined size.
• the cold rolling is performed under the conditions that the final pass work roll diameter D is 150 mm ⁇ or more, the final pass rolling reduction r is 15% or more, and the final pass strain rate ( ⁇ ′ m ) is 100 s ⁇ 1 or more and 1300 s ⁇ 1 or less. It is a cold-rolling process to obtain a cold-rolled sheet by rolling.
• the work roll diameter D of the final pass is set to 150 mm ⁇ or more.
• the reason why the work roll diameter D of the final pass is set to 150 mm ⁇ or more is to satisfy 5 ⁇ S C ⁇ S D ⁇ 0 and to obtain the desired steel sheet structure. If the work roll diameter D of the final pass is smaller than 150mm ⁇ , it is far from the state of plane compression, so the non-uniformity of shear strain in grain units is enhanced compared to the case where the work roll diameter is large. be.
• the work roll diameter D of the final pass is 150 mm ⁇ or more, 5 ⁇ S C ⁇ S D ⁇ 0 is satisfied and a desired steel sheet structure is obtained.
• the work roll diameter D of the final pass is preferably 170 mm ⁇ or more, more preferably 200 mm ⁇ or more. There is no particular upper limit to the diameter, but if the diameter of the roll is too large, the rolling load increases, so 700 mm ⁇ is preferable.
• the draft r of the final pass is preferably 15% or more.
• the reason why the rolling reduction r of the final pass is set to 15% or more is that the desired steel sheet structure can be easily obtained by obtaining the effects of a series of cold rolling controls. If the rolling reduction r of the final pass is less than 15%, the rolling reduction is too low, making it difficult to control the structure after annealing. On the other hand, when the rolling reduction r of the final pass is 15% or more, the effect of a series of cold rolling control is exhibited. As a result, it becomes easier to obtain the desired steel sheet structure.
• the rolling reduction r of the final pass is preferably 20% or more. In the present invention, it is not necessary to define the upper limit of the rolling reduction ratio r of the final pass, but an excessively high rolling reduction ratio requires a great deal of equipment capacity and makes it difficult to control the shape of the cold-rolled sheet. be.
• the strain rate ( ⁇ ′ m ) in the final pass is preferably 100 s ⁇ 1 or more and 1300 s ⁇ 1 or less.
• the reason why the final pass strain rate ( ⁇ ′ m ) is set to 100 s ⁇ 1 or more and 1300 s ⁇ 1 or less is to obtain the desired steel sheet structure by suppressing breakage during rolling and achieving 5 ⁇ S C ⁇ S D ⁇ 0. is.
• the strain rate ( ⁇ ′ m ) of the final pass is less than 100 s ⁇ 1 , the non-uniformity of the shear strain in the cold-rolled sheet is enhanced, and the nucleation and grain growth in the subsequent annealing process are suppressed. Since it is easier to concentrate in a specific orientation region, the sum of the area ratios of crystal grains with ⁇ 100> orientation in the 45° and -45° rolling directions S C decreases, and crystals with ⁇ 111> orientation in the same direction The sum S D of the grain area ratios increases. As a result, 5 ⁇ S C ⁇ S D ⁇ 0 cannot be satisfied.
• a low strain rate reduces the flow stress, makes it easier to concentrate strain on crystal grains with easily deformable crystal orientations, and makes the strain distribution non-uniform. I'm assuming it's because On the other hand, if the strain rate in the final pass exceeds 1300 s ⁇ 1 , the flow stress will increase excessively and brittle fracture will easily occur during rolling. When the strain rate ( ⁇ ′ m ) of the final pass is 100 s ⁇ 1 or more and 1300 s ⁇ 1 or less, 5 ⁇ S C ⁇ S D ⁇ 0 is satisfied while suppressing breakage during rolling.
• the final pass strain rate ( ⁇ ′ m ) is preferably 150 s ⁇ 1 or more and preferably 1300 s ⁇ 1 or less.
• the strain rate ( ⁇ ' m ) in each pass during cold rolling in the present invention was derived using Ekelund's approximation formula shown in the following formula (1).
• vR is the peripheral speed of the roll (mm/s)
• R' is the radius of the roll (mm)
• h1 is the plate thickness at the entry side of the roll (mm)
• r is the rolling reduction (%).
• the annealing step is a step of annealing the cold-rolled sheet that has undergone the cold rolling step. More specifically, the cold-rolled sheet that has undergone the cold rolling process is heated from 200°C to a holding temperature T1 of 400°C or higher and 600°C or lower with an average temperature increase rate V1 of 50°C/s or higher at the holding temperature T1. Heat to an annealing temperature T2 of 750°C or more and 850°C or less under the conditions that the holding time is 1 second or more and 10 seconds or less, and the average heating rate V2 from the holding temperature T1 to 750°C is 15°C/s or more, and then cools.
• the surface of the cold-rolled annealed sheet is coated with an insulation coating, but the method and type of coating are not particularly limited, and a commonly used insulation coating process can be applied.
• the holding temperature T1 during heating is set at 400°C or higher and 600°C or lower.
• the reason why the holding temperature T1 is set to 400°C or higher and 600°C or lower is that the sum of the area ratios of the crystal grains with ⁇ 100> in the rolling direction or the direction perpendicular to the rolling direction and the ⁇ 111> in the rolling direction or the direction perpendicular to the rolling direction are This is because the sum S B of the area ratios of oriented grains is in a range that satisfies S A ⁇ S B ⁇ 0 to obtain a desired steel sheet structure.
• the holding temperature T 1 is less than 400° C., the temperature is too low to obtain the effect of holding, resulting in an increase in S B , and as a result, S A ⁇ S B ⁇ 0 cannot be satisfied.
• the holding temperature T 1 is 600° C. or higher, not only the sum S B of the area ratios but also the sum S A of the area ratios decreases, so that S A ⁇ S B ⁇ 0 cannot be satisfied as a result. .
• the average heating rate V1 from 200°C to the holding temperature T1 is set to 50°C/s or more.
• the reason why the average heating rate V1 is set to 50°C/s or more is that the sum of the area ratios of crystal grains with ⁇ 100> in the rolling direction or in the direction perpendicular to the rolling direction and ⁇ 111> in the rolling direction or the direction perpendicular to the rolling direction This is because the sum S B of the area ratios of the crystal grains oriented toward each other is set to a range that satisfies S A ⁇ S B ⁇ 0 to obtain the desired steel sheet structure.
• the average temperature increase rate V1 from 200°C to the holding temperature T1 is preferably 70°C/s or higher, more preferably 100°C/s or higher. Although there is no particular need to set an upper limit, 500° C./s is preferable because an excessively high rate of temperature rise tends to cause temperature unevenness.
• the holding time t at the holding temperature T1 is 1 second or more and 10 seconds or less.
• the reason why the holding time t is set to 1 second or more and 10 seconds or less is that the sum of the area ratios of the grains with ⁇ 100> orientation in the rolling direction or the direction perpendicular to the rolling direction and the ⁇ 111> orientation in the rolling direction or the direction perpendicular to the rolling direction are This is because the sum S B of the area ratios of the crystal grains is set in a range that satisfies S A ⁇ S B ⁇ 0 to obtain the desired steel sheet structure.
• the holding time t is less than 1 second, the tissue will not recover sufficiently, resulting in an increase in S B , and as a result, S A ⁇ S B ⁇ 0 cannot be satisfied.
• the holding time t is longer than 10 seconds, the tissue recovers excessively and not only S B but also S A decreases. As a result, S A ⁇ S B ⁇ 0 cannot be satisfied.
• the average heating rate V2 from holding temperature T1 to 750°C is set to 15°C/s or more.
• the reason why the average heating rate V2 is set to 15°C/s or more is that the sum of the area ratios S of grains with ⁇ 100> orientation in the rolling direction or the direction perpendicular to the rolling direction and ⁇ 111> orientation in the rolling direction or the direction perpendicular to the rolling direction. This is because the sum S B of the area ratios of the crystal grains oriented toward each other is set to a range that satisfies S A ⁇ S B ⁇ 0 to obtain the desired steel sheet structure.
• the average heating rate V2 is preferably 20°C/s or higher, more preferably 30°C/s or higher. Although it is not necessary to set an upper limit, 200° C./s is preferable because an excessively high rate of temperature rise tends to cause temperature unevenness.
• the annealing temperature T2 is 750°C or higher and 850°C or lower.
• the reason why the annealing temperature T2 is set to 750° C. or more and 850° C. or less is to obtain the desired steel sheet structure by setting the average grain size to 50 ⁇ m or less. If the annealing temperature T2 is less than 750°C, the recrystallization does not progress sufficiently, resulting in a steel sheet structure in which many worked structures remain. Since this unrecrystallized portion contains many regions in which ⁇ 111> is oriented in the direction perpendicular to the rolling direction, SB increases.
• the annealing temperature T2 is 750° C. or higher, sufficient recrystallization occurs and S A ⁇ S B ⁇ 0 can be satisfied.
• the annealing temperature T2 is preferably above 775°C.
• the annealing temperature T2 should be 850°C or lower. Preferably, it is 825°C or less.
• ⁇ Evaluation> ⁇ Tissue Observation ⁇ A test piece for structure observation was taken from the obtained cold-rolled and annealed sheet. Next, the sampled test piece was embedded in a resin with the surface perpendicular to the rolling direction (RD surface) as the observation surface, and mirror-finished by colloidal silica polishing. Electron backscatter diffraction (EBSD) measurements were performed on the mirrored observation plane to obtain local orientation data. At this time, the step size was 2.5 ⁇ m and the measurement area was 20 mm 2 or more. The width of the measurement area was appropriately adjusted so that the number of crystal grains in subsequent analysis was 10,000 or more. The measurement may be performed by scanning the entire area once, or by combining the results of multiple scans using the Combo Scan function.
• RD surface surface perpendicular to the rolling direction
• EBSD Electron backscatter diffraction
• OIM Analysis 8 was used to analyze the obtained local orientation data. Prior to data analysis, coordinate rotation processing was performed so that the A1 axis//rolling direction, the A2 axis//perpendicular to rolling direction, and the A3 axis//plate surface direction of the sample coordinate system. Also, in the analysis software Partition Properties, the grain average data points are sorted under the condition of Formula: GCI [&; Data points unsuitable for analysis were excluded. At this time, valid data points were greater than 98%.
• the Grain Tolerance Angle is 5°
• the Minimum Grain Size is 2
• the Minimum Anti Grain Size is 2
• the Multiple Rows Requirement and the Anti-Grain Multiple Rows Requirement are both As OFF
• the value of Area Average obtained from the preprocessed data using the Grain Size (diameter) function was taken as the average crystal grain size. Also, using the Crystal Direction function, ⁇ 100> and ⁇ 111 The area ratio of crystal grains in which > is oriented was obtained. The Tolerance Angle when calculating the area ratio was set to 15°.
• S ⁇ uvw>//[u'v'w'] represents the area ratio of grains with ⁇ uvw> oriented in the [u'v'w'] direction of the sample coordinate system.
• the area ratio of the orientation that satisfies both ⁇ 100>//[100] and ⁇ 100>//[010] is double counted. The same applies to the rest.
• ⁇ Magnetic property evaluation From the obtained annealed sheet, a magnetic measurement test piece with a width of 30 mm and a length of 280 mm with the length direction in the rolling direction or the direction perpendicular to the rolling direction was taken, and was measured by the Epstein method in accordance with JIS C2550-1: 2011. The magnetic properties of cold-rolled and annealed sheets were evaluated. Evaluation items were saturation magnetic flux density: Bs, magnetic flux density at a magnetic field strength of 5000 A/m: B50, and iron loss W10/800.
• a test piece for magnetic measurement with a width of 30 mm and a length of 280 mm was taken with the longitudinal direction of 45° rolling and -45° rolling, and JIS C2550- 1:2011, the magnetic properties of the cold-rolled annealed sheets were evaluated by the Epstein method.
• the evaluation item was the magnetic flux density at a magnetic field strength of 5000A/m: B50_45°.
• the present invention it is possible to provide a non-oriented electrical steel sheet with high strength and high magnetic flux density, high frequency and low core loss even when subjected to strain relief annealing, and a method for producing the same.

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