WO2021199400A1 - 無方向性電磁鋼板およびその製造方法 - Google Patents
無方向性電磁鋼板およびその製造方法 Download PDFInfo
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- WO2021199400A1 WO2021199400A1 PCT/JP2020/015170 JP2020015170W WO2021199400A1 WO 2021199400 A1 WO2021199400 A1 WO 2021199400A1 JP 2020015170 W JP2020015170 W JP 2020015170W WO 2021199400 A1 WO2021199400 A1 WO 2021199400A1
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- steel sheet
- oriented electrical
- electrical steel
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 39
- 239000010959 steel Substances 0.000 title claims abstract description 39
- 238000004519 manufacturing process Methods 0.000 title claims description 19
- 239000013078 crystal Substances 0.000 claims abstract description 35
- 239000000463 material Substances 0.000 claims abstract description 22
- 239000000126 substance Substances 0.000 claims abstract description 21
- 239000000203 mixture Substances 0.000 claims abstract description 16
- 239000012535 impurity Substances 0.000 claims abstract description 9
- 238000000137 annealing Methods 0.000 claims description 53
- 229910000565 Non-oriented electrical steel Inorganic materials 0.000 claims description 41
- 238000000034 method Methods 0.000 claims description 21
- 238000002791 soaking Methods 0.000 claims description 18
- 238000005097 cold rolling Methods 0.000 claims description 17
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 49
- 239000011572 manganese Substances 0.000 description 26
- 229910052742 iron Inorganic materials 0.000 description 23
- 230000000694 effects Effects 0.000 description 16
- 238000005554 pickling Methods 0.000 description 14
- 239000002585 base Substances 0.000 description 12
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 12
- 239000010949 copper Substances 0.000 description 11
- 229910052710 silicon Inorganic materials 0.000 description 11
- 239000010936 titanium Substances 0.000 description 11
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 10
- 239000010953 base metal Substances 0.000 description 9
- 239000011248 coating agent Substances 0.000 description 9
- 238000000576 coating method Methods 0.000 description 9
- 230000004907 flux Effects 0.000 description 9
- 239000002244 precipitate Substances 0.000 description 9
- 229910052748 manganese Inorganic materials 0.000 description 8
- 239000010955 niobium Substances 0.000 description 8
- 238000005098 hot rolling Methods 0.000 description 7
- 229910052757 nitrogen Inorganic materials 0.000 description 7
- 229910052782 aluminium Inorganic materials 0.000 description 6
- 229910052799 carbon Inorganic materials 0.000 description 6
- 230000009467 reduction Effects 0.000 description 6
- 238000005728 strengthening Methods 0.000 description 6
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 5
- 229910052787 antimony Inorganic materials 0.000 description 5
- 230000007423 decrease Effects 0.000 description 5
- 230000006872 improvement Effects 0.000 description 5
- 150000001247 metal acetylides Chemical class 0.000 description 5
- 150000004767 nitrides Chemical class 0.000 description 5
- 230000008569 process Effects 0.000 description 5
- 229910052718 tin Inorganic materials 0.000 description 5
- NBIIXXVUZAFLBC-UHFFFAOYSA-N Phosphoric acid Chemical compound OP(O)(O)=O NBIIXXVUZAFLBC-UHFFFAOYSA-N 0.000 description 4
- 239000011162 core material Substances 0.000 description 4
- 239000002245 particle Substances 0.000 description 4
- 229910052719 titanium Inorganic materials 0.000 description 4
- HEMHJVSKTPXQMS-UHFFFAOYSA-M Sodium hydroxide Chemical compound [OH-].[Na+] HEMHJVSKTPXQMS-UHFFFAOYSA-M 0.000 description 3
- 239000002131 composite material Substances 0.000 description 3
- 229910052802 copper Inorganic materials 0.000 description 3
- 230000006866 deterioration Effects 0.000 description 3
- 238000009413 insulation Methods 0.000 description 3
- 239000007788 liquid Substances 0.000 description 3
- 238000005259 measurement Methods 0.000 description 3
- 229910052759 nickel Inorganic materials 0.000 description 3
- 238000005096 rolling process Methods 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 238000009864 tensile test Methods 0.000 description 3
- 229910052720 vanadium Inorganic materials 0.000 description 3
- 229910052726 zirconium Inorganic materials 0.000 description 3
- VEXZGXHMUGYJMC-UHFFFAOYSA-N Hydrochloric acid Chemical compound Cl VEXZGXHMUGYJMC-UHFFFAOYSA-N 0.000 description 2
- QAOWNCQODCNURD-UHFFFAOYSA-N Sulfuric acid Chemical compound OS(O)(=O)=O QAOWNCQODCNURD-UHFFFAOYSA-N 0.000 description 2
- 238000010521 absorption reaction Methods 0.000 description 2
- 229910000147 aluminium phosphate Inorganic materials 0.000 description 2
- 150000001875 compounds Chemical class 0.000 description 2
- 239000010419 fine particle Substances 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000002354 inductively-coupled plasma atomic emission spectroscopy Methods 0.000 description 2
- 239000011261 inert gas Substances 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 229910052758 niobium Inorganic materials 0.000 description 2
- 229910052761 rare earth metal Inorganic materials 0.000 description 2
- 150000003839 salts Chemical class 0.000 description 2
- 229910052717 sulfur Inorganic materials 0.000 description 2
- 238000010998 test method Methods 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910001224 Grain-oriented electrical steel Inorganic materials 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 239000003513 alkali Substances 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- ILRRQNADMUWWFW-UHFFFAOYSA-K aluminium phosphate Chemical compound O1[Al]2OP1(=O)O2 ILRRQNADMUWWFW-UHFFFAOYSA-K 0.000 description 1
- 150000003863 ammonium salts Chemical class 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- WATWJIUSRGPENY-UHFFFAOYSA-N antimony atom Chemical compound [Sb] WATWJIUSRGPENY-UHFFFAOYSA-N 0.000 description 1
- 239000007864 aqueous solution Substances 0.000 description 1
- 229910052785 arsenic Inorganic materials 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 230000033228 biological regulation Effects 0.000 description 1
- 229910052797 bismuth Inorganic materials 0.000 description 1
- 229910052796 boron Inorganic materials 0.000 description 1
- 238000011088 calibration curve Methods 0.000 description 1
- 150000004649 carbonic acid derivatives Chemical class 0.000 description 1
- KRVSOGSZCMJSLX-UHFFFAOYSA-L chromic acid Substances O[Cr](O)(=O)=O KRVSOGSZCMJSLX-UHFFFAOYSA-L 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 229920006026 co-polymeric resin Polymers 0.000 description 1
- 239000010960 cold rolled steel Substances 0.000 description 1
- 239000008119 colloidal silica Substances 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 239000007822 coupling agent Substances 0.000 description 1
- 238000005238 degreasing Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 239000000839 emulsion Substances 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000007613 environmental effect Effects 0.000 description 1
- AWJWCTOOIBYHON-UHFFFAOYSA-N furo[3,4-b]pyrazine-5,7-dione Chemical compound C1=CN=C2C(=O)OC(=O)C2=N1 AWJWCTOOIBYHON-UHFFFAOYSA-N 0.000 description 1
- 238000007654 immersion Methods 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 229910052745 lead Inorganic materials 0.000 description 1
- 230000005389 magnetism Effects 0.000 description 1
- 229910001463 metal phosphate Inorganic materials 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 238000005121 nitriding Methods 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000002203 pretreatment Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 238000004080 punching Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 229920005989 resin Polymers 0.000 description 1
- 239000011347 resin Substances 0.000 description 1
- 229910052711 selenium Inorganic materials 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 239000007858 starting material Substances 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
- GPPXJZIENCGNKB-UHFFFAOYSA-N vanadium Chemical compound [V]#[V] GPPXJZIENCGNKB-UHFFFAOYSA-N 0.000 description 1
Classifications
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- 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
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
- C21D1/76—Adjusting the composition of the atmosphere
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1222—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1233—Cold rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
- C21D8/1261—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest 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 by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
- C21D8/1272—Final recrystallisation annealing
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
- C21D8/1277—Modifying the physical properties 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
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- 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
- C22C38/004—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
- C22C38/008—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
- C22C38/04—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
- C22C38/12—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
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
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- 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
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- 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
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- 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
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- 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
- Y02T—CLIMATE CHANGE MITIGATION TECHNOLOGIES RELATED TO TRANSPORTATION
- Y02T10/00—Road transport of goods or passengers
- Y02T10/60—Other road transportation technologies with climate change mitigation effect
- Y02T10/64—Electric machine technologies in electromobility
Definitions
- the present invention relates to a non-oriented electrical steel sheet and a method for manufacturing the same.
- a slit is provided in the outer periphery of the rotor to embed a magnet. Therefore, due to the centrifugal force during high-speed rotation of the motor, stress is concentrated on the narrow bridge portion such as between the outer circumference of the rotor and the slit. Therefore, the core material used for the rotor is required to have enough strength not to be deformed and broken by centrifugal force.
- Patent Documents 1 to 3 attempts have been made to realize excellent magnetic properties and high strength.
- Patent Documents 1 to 3 are insufficient in reducing iron loss and at high cost. Met.
- the present invention has been made to solve such a problem, and an object of the present invention is to stably provide a non-oriented electrical steel sheet having high strength and excellent magnetic properties at low cost.
- the gist of the present invention is the following non-oriented electrical steel sheet and its manufacturing method.
- the chemical composition of the base material is mass%. C: 0.0050% or less, Si: 3.8-5.0%, Mn: more than 0.2% and less than 2.0%, P: 0.030% or less, S: 0.0030% or less, Al: 0.005 or more and less than 0.050%, N: 0.0005 to 0.0030%, Ti: less than 0.0050%, Nb: less than 0.0050%, Zr: less than 0.0050%, V: less than 0.0050%, Cu: less than 0.20%, Ni: less than 0.50%, Sn: 0 to 0.10%, Sb: 0 to 0.10%, Remaining: Fe and impurities, Satisfy the following equation (i)
- the average crystal grain size of the base material is 10 to 80 ⁇ m.
- the element symbol in the above formula is the content (mass%) of each element.
- the tensile strength is 650 MPa or more.
- the chemical composition is mass%.
- Sn 0.005 to 0.10%
- Sb 0.005 to 0.10%
- the non-oriented electrical steel sheet according to any one of (1) to (3) above.
- Step 1 The method for manufacturing a non-oriented electrical steel sheet according to any one of (1) to (4) above.
- a steel ingot having the chemical composition according to any one of (1) to (3) above is hot-rolled, and then the following step 1 or step 2 is performed.
- Step 2 Cold rolling and finish annealing are performed in order without hot-rolled sheet annealing.
- Step 2 Hot-rolled sheet annealing is performed at a temperature of 950 ° C. or lower, and then cold rolling and finish annealing are performed in this order.
- the finish annealing is performed with a soaking temperature of 750 to 1000 ° C. and a soaking time of 1 to 300 s. Manufacturing method of non-oriented electrical steel sheet.
- non-oriented electrical steel sheets having high strength and excellent magnetic properties can be stably obtained at low cost.
- Si, Mn and Al are elements that have the effect of increasing the electrical resistance of steel and reducing eddy current loss. In addition, these elements are elements that also contribute to increasing the strength of steel.
- Si is the element that most efficiently contributes to the increase in electrical resistance
- Al is the element that most efficiently contributes to the increase in strength.
- Al also has the effect of efficiently increasing the electrical resistance.
- Mn has a lower effect of increasing the electric resistance than Si and Al, but has an advantage that the workability is less likely to be deteriorated.
- the crystal grain size is important to control the crystal grain size in order to increase the strength and improve the magnetic properties. From the viewpoint of increasing strength, it is desirable that the crystals in the steel are fine particles.
- Iron loss mainly consists of hysteresis loss and eddy current loss.
- hysteresis loss in order to reduce the hysteresis loss, it is preferable to make the crystal grains coarser, and in order to reduce the eddy current loss, it is preferable to make the crystal grains finer. That is, there is a trade-off relationship between the two.
- the non-oriented electrical steel sheet according to this embodiment was made based on the above findings. Hereinafter, each requirement of the non-oriented electrical steel sheet according to the present embodiment will be described in detail.
- the non-oriented electrical steel sheet according to the present invention is suitable for a rotor because it has particularly high strength, and is also suitable for a stator because it is excellent in magnetic characteristics. Further, the non-oriented electrical steel sheet according to the present invention preferably has an insulating film on the surface of the base material described below.
- C is an element that causes iron loss deterioration. If the C content exceeds 0.0050%, iron loss deterioration occurs in the non-oriented electrical steel sheet, and good magnetic characteristics cannot be obtained. Therefore, the C content is set to 0.0050% or less.
- the C content is preferably 0.0040% or less, more preferably 0.0035% or less. Since C contributes to increasing the strength of the steel sheet, when it is desired to obtain the effect, the C content is preferably 0.0005% or more, more preferably 0.0010% or more. ..
- Si 3.8-5.0%
- Si silicon
- Si is an element that increases the electrical resistance of steel, reduces eddy current loss, and improves high-frequency iron loss.
- Si is an element effective for increasing the strength of steel sheets because it has a large solid solution strengthening ability.
- the Si content is set to 3.8 to 5.0%.
- the Si content is preferably 3.9% or more, more preferably 4.0% or more.
- the Si content is preferably 4.8% or less, more preferably 4.5% or less.
- Mn Exceeding 0.2% and less than 2.0% Mn (manganese) is an element effective for increasing the electrical resistance of steel, reducing eddy current loss, and improving high-frequency iron loss. However, if the Mn content is excessive, the decrease in magnetic flux density becomes remarkable. Therefore, the Mn content is set to more than 0.2% and less than 2.0%.
- the Mn content is preferably 0.3% or more, more preferably 0.4% or more, more preferably more than 0.5%, and even more preferably 0.6% or more. ..
- the Mn content is preferably 1.8% or less, more preferably 1.7% or less, more preferably less than 1.5%, and preferably 1.4% or less. It is more preferably 1.2% or less, and more preferably 1.0% or less.
- the electrical resistance of steel is ensured by appropriately controlling the contents of Si and Mn. Therefore, in addition to the contents of Si and Mn being within the above ranges, it is necessary to satisfy the following formula (i).
- the lvalue of equation (i) is preferably 4.4 or more, and more preferably 4.5 or more.
- the element symbol in the above formula is the content (mass%) of each element.
- the purpose of formula (i) is as follows. As described above, in the present embodiment, by adjusting the contents of Si and Mn to an appropriate range, workability is ensured while achieving high strength and improvement of magnetic properties.
- Si is an element that increases the electrical resistance of steel, reduces eddy current loss, and improves high-frequency iron loss.
- Si is an element effective for increasing the strength of steel sheets because it has a large solid solution strengthening ability.
- the Si content is set to 3.8 to 5.0%.
- the Si content when the Si content is 4.3 to 5.0%, the formula (i) is satisfied regardless of the Mn content. Therefore, in this case, good magnetic properties can be obtained (assuming that the other requirements of the non-oriented electrical steel sheet according to the present embodiment are satisfied). Further, since the Si content satisfies the requirements of the present embodiment, the non-oriented electrical steel sheet has high strength. On the other hand, although Si is a disadvantageous element from the viewpoint of workability, the Si content is at least 5.0% or less, so that the workability is also good.
- the Si content is 3.8% or more and less than 4.3%
- the formula (i) is not satisfied only by the Si content. That is, there is a possibility that the desired magnetic characteristics cannot be obtained only with Si. Therefore, Mn is used to make up for the lack of magnetic properties. That is, the Mn content is increased within the range of more than 0.2% and less than 2.0% so that the formula (i) is satisfied. This enhances the magnetic properties of the non-oriented electrical steel sheet.
- Si since Si is 3.8% or more, the strength of the non-oriented electrical steel sheet is also high.
- workability since the Si content is less than 4.3%, the workability tends to be improved as compared with the case described above (that is, the Si content is 4.3% or more).
- Mn does not easily affect the workability, even if the Mn content is increased so as to satisfy the formula (i), the workability is unlikely to decrease. Further, increasing the Mn content has the effect of increasing the strength, though not as much as Si.
- the Si content and the Mn content are set to be within the above-mentioned numerical range and the formula (i) is satisfied, so that the strength of the non-oriented electrical steel sheet is increased. And workability can be ensured while achieving improvement in magnetic properties.
- P 0.030% or less
- P (phosphorus) is contained in steel as an impurity, and if the content is excessive, the ductility of the steel sheet is significantly lowered. Therefore, the P content is 0.030% or less.
- the P content is preferably 0.025% or less, more preferably 0.020% or less.
- S 0.0030% or less
- S sulfur
- the S content is preferably 0.0025% or less, more preferably 0.0020% or less. Since an extreme reduction in the S content may lead to an increase in manufacturing cost, the S content is preferably 0.0001% or more, more preferably 0.0003% or more, and 0. It is more preferably 0005% or more.
- Al 0.005% or more and less than 0.050%
- Al is an element effective for forming stable crystal grains by combining with N to form AlN. In order to exert this effect, it is necessary to contain 0.005% or more. On the other hand, if it contains 0.050% or more, the effect of refining the crystal grains decreases. Therefore, the Al content is set to 0.005% or more and less than 0.050%.
- the Al content is preferably 0.008% or more, more preferably 0.010% or more, more preferably 0.015% or more, and even more preferably 0.020% or more. .. Further, the Al content is preferably 0.048% or less, and more preferably 0.045% or less.
- Al content means the content of all Al contained in a base material.
- N 0.0005 to 0.0030%
- nitrogen is an element that combines with Al to form AlN and is effective for the miniaturization of stable crystal grains. On the other hand, if it is contained in a large amount, excess AlN is formed, which causes iron loss deterioration. Therefore, the N content is set to 0.0005 to 0.0030%.
- the N content is preferably 0.0007% or more, and more preferably 0.0010% or more.
- the N content is preferably 0.0027% or less, more preferably 0.0025% or less.
- Ti Less than 0.0050% Ti (titanium) is an element that is inevitably mixed and can combine with carbon or nitrogen to form precipitates (carbides, nitrides). When carbides or nitrides are formed, these precipitates themselves deteriorate the magnetic properties. Furthermore, it inhibits the growth of crystal grains during finish annealing and deteriorates the magnetic properties. Therefore, the Ti content is set to less than 0.0050%.
- the Ti content is preferably 0.0040% or less, more preferably 0.0030% or less, and even more preferably 0.0020% or less.
- the Ti content is preferably 0.0005% or more because an extreme reduction in the Ti content may lead to an increase in manufacturing cost.
- Nb Less than 0.0050% Nb (niobium) is an element that contributes to high strength by combining with carbon or nitrogen to form precipitates (carbides, nitrides), but these precipitates themselves are Deteriorates magnetic properties. Therefore, the Nb content is set to less than 0.0050%.
- the Nb content is preferably 0.0040% or less, more preferably 0.0030% or less, and even more preferably 0.0020% or less. The lower the Nb content, the more preferable, and it is preferable that the Nb content is below the measurement limit.
- Zr Less than 0.0050% Zr (zirconium) is an element that contributes to high strength by combining with carbon or nitrogen to form precipitates (carbides, nitrides), but these precipitates themselves are Deteriorates magnetic properties. Therefore, the Zr content is set to less than 0.0050%.
- the Zr content is preferably 0.0040% or less, more preferably 0.0030% or less, and even more preferably 0.0020% or less. The lower the Zr content, the more preferable, and it is preferable that the Zr content is below the measurement limit.
- V Less than 0.0050% V (vanadium) is an element that contributes to high strength by combining with carbon or nitrogen to form precipitates (carbides, nitrides), but these precipitates themselves are Deteriorates magnetic properties. Therefore, the V content is set to less than 0.0050%.
- the V content is preferably 0.0040% or less, more preferably 0.0030% or less, and even more preferably 0.0020% or less. The lower the V content, the more preferable, and it is preferable that the V content is below the measurement limit.
- Cu less than 0.20%
- Cu (copper) is an element that is inevitably mixed.
- the intentional addition of Cu increases the manufacturing cost of the steel sheet. Therefore, in the present invention, it is not necessary to add positively, and the impurity level may be used.
- the Cu content shall be less than 0.20%, which is the maximum value that can be unavoidably mixed in the manufacturing process.
- the Cu content is preferably 0.15% or less, more preferably 0.10% or less.
- the lower limit of the Cu content is not particularly limited, but an extreme reduction in the Cu content may lead to an increase in manufacturing cost. Therefore, the Cu content is preferably 0.001% or more, more preferably 0.003% or more, and further preferably 0.005% or more.
- Ni less than 0.50%
- Ni nickel
- Ni nickel
- Ni is an element that is inevitably mixed.
- Ni is also an element that improves the strength of the steel sheet, it may be added intentionally.
- Ni since Ni is expensive, its content should be less than 0.50% when it is intentionally added.
- the Ni content is preferably 0.40% or less, more preferably 0.30% or less.
- the lower limit of the Ni content is not particularly limited, but an extreme reduction in the Ni content may lead to an increase in manufacturing cost. Therefore, the Ni content is preferably 0.001% or more, more preferably 0.003% or more, and further preferably 0.005% or more.
- Sn 0 to 0.10%
- Sb 0 to 0.10%
- Sn (tin) and Sb (antimony) are elements useful for ensuring low iron loss by segregating on the surface and suppressing oxidation and nitriding during annealing. It also has the effect of segregating at the grain boundaries to improve the texture and increase the magnetic flux density. Therefore, at least one of Sn and Sb may be contained if necessary. However, if the content of these elements is excessive, the toughness of the steel may decrease, making cold rolling difficult. Therefore, the contents of Sn and Sb are set to 0.10% or less, respectively. The contents of Sn and Sb are preferably 0.06% or less, respectively. When the above effect is desired, the content of at least one of Sn and Sb is preferably 0.005% or more, and more preferably 0.010% or more.
- the balance is Fe and impurities.
- impurity is a component mixed with raw materials such as ore and scrap, and various factors in the manufacturing process when steel is industrially manufactured, and is allowed as long as it does not adversely affect the present invention. Means something.
- the content of Cr and Mo as impurity elements is not particularly specified.
- the effect of the present invention is not particularly affected.
- Ca and Mg are contained in the range of 0.002% or less, the effect of the present invention is not particularly affected, and even if the rare earth element (REM) is contained in the range of 0.004% or less, the present invention is not particularly affected. There is no particular effect on the effect of the invention.
- REM rare earth element
- O is also an impurity element, but even if it is contained in the range of 0.05% or less, the effect of the present invention is not affected. Since O may be mixed in the annealing step, even if it is contained in the range of 0.01% or less in the content of the slab stage (that is, the ladle value), the effect of the present invention is not particularly affected.
- elements such as Pb, Bi, As, B, and Se may be included, but if the content of each is in the range of 0.0050% or less, the effect of the present invention is impaired. It's not a thing.
- the chemical composition of the base material described above may be measured by a general analysis method.
- the steel component may be measured using ICP-AES (Inductively Coupled Plasma-Atomic Emission Spectrometry).
- C and S may be measured by using the combustion-infrared absorption method
- N may be measured by using the inert gas melting-heat conductivity method
- O may be measured by using the inert gas melting-non-dispersion infrared absorption method.
- Crystal grain size As described above, it is desirable that the crystals in the steel are fine particles from the viewpoint of increasing the strength. In addition, it is preferable to coarsen the crystal grains in order to reduce the hysteresis loss, and it is preferable to make the crystal grains finer in order to reduce the eddy current loss.
- the average crystal grain size of the base metal is less than 10 ⁇ m, the hysteresis loss becomes remarkably deteriorated and it becomes difficult to improve the magnetic characteristics.
- the average crystal grain size exceeds 80 ⁇ m, the strength of the steel decreases. Therefore, the average crystal grain size of the base material is 10 to 80 ⁇ m.
- the average crystal grain size is preferably 12 ⁇ m or more, and more preferably 14 ⁇ m or more.
- the average crystal grain size is preferably 70 ⁇ m or less, more preferably 60 ⁇ m or less.
- the average crystal grain size of the base material shall be determined according to JIS G 0551 (2013) "Steel-Crystal Grain Size Microscopic Test Method”.
- Magnetic characteristics in the non-oriented electrical steel sheet according to the present invention excellent magnetic characteristics means that the iron loss W 10/400 is low and the magnetic flux density B 50 is high.
- the above magnetic characteristics are measured in accordance with the Epstein method specified in JIS C 2550-1 (2011).
- having high strength means that the tensile strength is 650 MPa or more.
- the tensile strength is preferably 660 MPa or more.
- the tensile strength is measured by performing a tensile test in accordance with JIS Z 2241 (2011).
- non-oriented electrical steel sheet it is preferable that an insulation film is formed on the surface of the base metal. Since non-oriented electrical steel sheets are used after punching out a core blank, they are laminated and used. Therefore, by providing an insulating film on the surface of the base metal, the eddy current between the plates can be reduced and the eddy current loss is reduced as the core. It becomes possible to reduce.
- the type of the insulating coating is not particularly limited, and it is possible to use a known insulating coating used as the insulating coating of the non-oriented electrical steel sheet.
- Examples of such an insulating film include a composite insulating film mainly composed of an inorganic substance and further containing an organic substance.
- the composite insulating coating is mainly composed of, for example, at least one of a chromic acid metal salt, a phosphoric acid metal salt, and an inorganic substance such as colloidal silica, a Zr compound, and a Ti compound, and fine organic resin particles are dispersed. It is an insulating film.
- an insulating film using a metal phosphate, a Zr or Ti coupling agent, or these carbonates or ammonium salts as a starting material is used. It is preferably used.
- the amount of the insulating coating adhered is not particularly limited , but is preferably about 200 to 1500 mg / m 2 per side, and more preferably 300 to 1200 mg / m 2 per side.
- the amount of the insulating film adhered is measured after the fact, various known measuring methods can be used. For example, a method of measuring the mass difference before and after immersion in the sodium hydroxide aqueous solution, or a calibration curve. A fluorescent X-ray method using a linear method or the like may be appropriately used.
- the manufacturing method of the non-oriented electrical steel sheet according to the present invention is not particularly limited.
- a steel ingot having the above-mentioned chemical components is hot-rolled, and then the following steps are performed. It can be manufactured by performing step 1 or step 2.
- Step 1) Cold rolling and finish annealing are performed in order without hot-rolled sheet annealing.
- Step 2) Hot-rolled sheet annealing is performed at a temperature of 950 ° C. or lower, and then cold rolling and finish annealing are performed in this order.
- the insulating film is formed on the surface of the base material, the insulating film is formed after the finish annealing.
- each step will be described in detail.
- ⁇ Hot rolling process> A steel ingot (slab) having the above chemical composition is heated, and the heated steel ingot is hot-rolled to obtain a hot-rolled plate.
- the heating temperature of the ingot when subjected to hot rolling is not particularly specified, but is preferably 1050 to 1250 ° C., for example.
- the plate thickness of the hot-rolled plate after hot rolling is not particularly specified, but it is preferably about 1.5 to 3.0 mm in consideration of the final plate thickness of the base metal, for example. ..
- hot-rolled sheet annealing may be performed for the purpose of increasing the magnetic flux density of the steel sheet. That is, in step 1, the hot-rolled plate annealing step is omitted. In step 2, a hot-rolled plate annealing step is performed.
- the annealing temperature is set to 950 ° C. or lower.
- the hot-rolled steel sheet is annealed at 700 to 950 ° C. by soaking for 10 to 150 s. The soaking condition is more preferably 10 to 150 s at 800 to 930 ° C.
- annealing by soaking heat at 600 to 850 ° C. for 30 minutes to 24 hours is preferable for the hot-rolled steel sheet. More preferably, the heat is equalized from 1 h to 20 h at 650 to 800 ° C. Although the magnetic characteristics are inferior to those in which the hot-rolled plate annealing step is performed, the above-mentioned hot-rolled plate annealing step may be omitted in order to reduce costs (step 1).
- pickling After the hot-rolled plate annealing, pickling may be carried out.
- the pickling removes the scale layer formed on the surface of the base metal.
- the pickling conditions such as the concentration of the acid used for pickling, the concentration of the accelerator used for pickling, and the temperature of the pickling solution are not particularly limited, and known pickling conditions may be used. can.
- the pickling step is preferably performed before the hot-rolled plate is annealed from the viewpoint of descalability. In this case, it is not necessary to perform pickling after annealing the hot-rolled plate.
- the hot-rolled plate annealing is omitted, the hot-rolled plate may be pickled for the purpose of removing the scale layer from the hot-rolled plate.
- Cold rolling is performed in step 1 after the hot rolling step, and in step 2 after the pickling (when hot rolling sheet annealing is carried out by box annealing, it may be after the hot rolling sheet annealing step). Is carried out.
- cold rolling for example, a pickling plate from which the scale layer has been removed is rolled at a rolling reduction ratio such that the final plate thickness of the base metal is 0.10 to 0.35 mm.
- finish annealing is performed.
- a continuous annealing furnace for finish annealing.
- the finish annealing step is an important step for controlling the average crystal grain size of the base metal.
- the soaking temperature is 750 to 1000 ° C.
- the soaking time is 1 to 300 s
- the soaking temperature is more preferably 760 to 980 ° C, still more preferably 770 to 960 ° C.
- the proportion of H 2 in the atmosphere is more preferably 15-90% by volume.
- the dew point of the atmosphere is more preferably 20 ° C. or lower, and even more preferably 10 ° C. or lower.
- a step of forming an insulating film may be carried out.
- the step of forming the insulating coating is not particularly limited, and the treatment liquid may be applied and dried by a known method using the known insulating coating treatment liquid as described above.
- the surface of the base material on which the insulating film is formed may be subjected to arbitrary pretreatment such as degreasing treatment with alkali or pickling treatment with hydrochloric acid, sulfuric acid, phosphoric acid, etc. before applying the treatment liquid.
- the surface may be the surface as it is after finish annealing without performing these pretreatments.
- the strength and magnetism of the non-oriented electrical steel sheet are increased. Workability can be ensured while achieving improvement in characteristics. Furthermore, since the average crystal grain size of the base metal is 10 to 80 ⁇ m, it is possible to enhance the magnetic characteristics while increasing the strength of the non-oriented electrical steel sheet also in this respect. As described above, in the present embodiment, expensive special elements such as Ni and Cu as in Patent Document 1, Ti and V as in Patent Document 2, and Ca as in Patent Document 3 are not added in a large amount. Workability can be ensured while achieving high strength and improvement of magnetic properties of non-oriented electrical steel sheets.
- hot rolling was performed at a finishing temperature of 850 ° C. and a finishing plate thickness of 2.0 mm, and the slab was wound at 650 ° C. to obtain a hot-rolled steel sheet.
- the obtained hot-rolled steel sheet was annealed at the annealing temperature shown in Table 2, and the scale on the surface was removed by pickling.
- the soaking time in the hot-rolled plate annealing was set to 30 s.
- the pickled sheet thus obtained (the pickled sheet from which the scale of the hot-rolled steel sheet was removed when the hot-rolled sheet annealing was omitted) was cold-rolled to obtain a cold-rolled steel sheet having a plate thickness of 0.25 mm.
- the finishing annealing conditions (equalizing temperature (annealing temperature)) are obtained so that the average crystal grain size is as shown in Table 2 below.
- the soaking time were changed and annealed. Specifically, when the average crystal grain size was controlled to be large, the soaking temperature was made higher and / or the soaking time was made longer. When the average crystal grain size was controlled to be small, the opposite was true.
- Table 2 shows specific soaking temperature (annealing temperature) and soaking time. Then, an insulating film was applied to produce a non-oriented electrical steel sheet, which was used as a test material.
- the above-mentioned insulating coating is coated with an insulating coating made of aluminum phosphate and an acrylic-styrene copolymer resin emulsion having a particle size of 0.2 ⁇ m so as to have a predetermined adhesion amount, and baked in the air at 350 ° C. Formed.
- JIS No. 5 tensile test pieces were taken according to JIS Z 2241 (2011) so that the longitudinal direction coincided with the rolling direction of the steel sheet. Then, a tensile test was performed using the above test piece according to JIS Z 2241 (2011), and the tensile strength was measured. The tensile strength was set at 650 MPa or more as a passing level. The above results are also shown in Table 2.
- test No. which is a comparative example.
- the test No. which is a comparative example.
- the test No. which is a comparative example.
- the strength was inferior, or the toughness was significantly deteriorated, which made the production difficult.
- the test No. In No. 1 since the Si content was lower than the specified range, the tensile strength was inferior.
- test No. In No. 8 the Si content exceeded the specified range, and Test No. In No. 12, the P content exceeded the specified range, and Test No. In No. 18, since the annealing temperature of the hot-rolled plate exceeded the specified range, the toughness deteriorated and the toughness was broken during cold rolling, and the average crystal grain size, tensile strength and magnetic properties could not be measured. Furthermore, the test No. In Nos. 11 and 34, the Mn content exceeded the specified range, resulting in inferior magnetic flux density. Test No. In No. 32, the Mn content was below the specified range, resulting in inferior iron loss.
- Test No. 19 the Al content was below the specified range, and Test No. In 21 and 33, since the Al content exceeded the specified range, it was difficult to adjust the average crystal grain size, resulting in inferior tensile strength. Test No. In 31, the iron loss was inferior because the equation (i) was not satisfied.
- non-oriented electrical steel sheets having high strength and excellent magnetic properties can be stably obtained at low cost.
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Abstract
Description
C:0.0050%以下、
Si:3.8~5.0%、
Mn:0.2%を超えて2.0%未満、
P:0.030%以下、
S:0.0030%以下、
Al:0.005以上0.050%未満、
N:0.0005~0.0030%、
Ti:0.0050%未満、
Nb:0.0050%未満、
Zr:0.0050%未満、
V:0.0050%未満、
Cu:0.20%未満、
Ni:0.50%未満、
Sn:0~0.10%、
Sb:0~0.10%、
残部:Feおよび不純物であり、
下記(i)式を満足し、
前記母材の平均結晶粒径が、10~80μmである、
無方向性電磁鋼板。
Si+0.5×Mn≧4.3 ・・・(i)
但し、上記式中の元素記号は、各元素の含有量(質量%)である。
上記(1)に記載の無方向性電磁鋼板。
Sn:0.005~0.10%、および、
Sb:0.005~0.10%、
から選択される1種または2種を含有する、
上記(1)または(2)に記載の無方向性電磁鋼板。
上記(1)から(3)までのいずれかに記載の無方向性電磁鋼板。
上記(1)から(3)までのいずれかに記載の化学組成を有する鋼塊に対して熱間圧延を施し、次いで以下の工程1または工程2を行い、
(工程1)熱延板焼鈍を行わずに、冷間圧延および仕上焼鈍を順に行う。
(工程2)950℃以下の温度で熱延板焼鈍を行い、次いで前記冷間圧延および前記仕上焼鈍を順に行う。
前記仕上焼鈍は、均熱温度を750~1000℃とし、均熱時間を1~300sとして行う、
無方向性電磁鋼板の製造方法。
本発明に係る無方向性電磁鋼板は、特に高い強度を有するため、ロータに好適であり、また磁気特性にも優れることから、ステータにも好適である。また、本発明に係る無方向性電磁鋼板は、以下に説明する母材の表面に絶縁被膜を備えていることが好ましい。
各元素の限定理由は下記のとおりである。なお、以下の説明において含有量についての「%」は、「質量%」を意味する。また、本実施形態において、「~」を用いて表される数値範囲は、「~」の前後に記載される数値を下限値及び上限値として含む範囲を意味する。
C(炭素)は、鉄損劣化を引き起こす元素である。C含有量が0.0050%を超えると、無方向性電磁鋼板において鉄損劣化が生じ、良好な磁気特性を得ることができない。したがって、C含有量は0.0050%以下とする。C含有量は0.0040%以下であるのが好ましく、0.0035%以下であるのがより好ましい。なお、Cは鋼板の高強度化に寄与することから、その効果を得たい場合には、C含有量は0.0005%以上であるのが好ましく、0.0010%以上であるのがより好ましい。
Si(ケイ素)は、鋼の電気抵抗を上昇させて渦電流損を低減させ、高周波鉄損を改善する元素である。また、Siは、固溶強化能が大きいため、鋼板の高強度化にも有効な元素である。一方、Si含有量が過剰であると、加工性が著しく劣化し、冷間圧延を実施することが困難となる。したがって、Si含有量は3.8~5.0%とする。Si含有量は3.9%以上であるのが好ましく、4.0%以上であるのがより好ましい。また、Si含有量は4.8%以下であるのが好ましく、4.5%以下であるのがより好ましい。
Mn(マンガン)は、鋼の電気抵抗を上昇させて渦電流損を低減し、高周波鉄損を改善するために有効な元素である。しかし、Mn含有量が過剰であると、磁束密度の低下が顕著となる。したがって、Mn含有量は0.2%を超えて2.0%未満とする。Mn含有量は0.3%以上であるのが好ましく、0.4%以上であるのがより好ましく、0.5%超であることがより好ましく、0.6%以上であることがより好ましい。また、Mn含有量は1.8%以下であるのが好ましく、1.7%以下であるのがより好ましく、1.5%未満であるのがより好ましく、1.4%以下であるのがより好ましく、1.2%以下であることがより好ましく、1.0%以下であることがより好ましい。
Si+0.5×Mn≧4.3 ・・・(i)
但し、上記式中の元素記号は、各元素の含有量(質量%)である。
式(i)の趣旨は以下の通りである。
上述したように、本実施形態においては、SiおよびMnの含有量を適切な範囲に調整することで、高強度化および磁気特性の向上を達成しつつ、加工性を確保する。まず、Siに着目すると、Siは鋼の電気抵抗を上昇させて渦電流損を低減させ、高周波鉄損を改善する元素である。また、Siは、固溶強化能が大きいため、鋼板の高強度化にも有効な元素である。一方、Si含有量が過剰であると、加工性が著しく劣化し、冷間圧延を実施することが困難となる。このような観点から、Si含有量は3.8~5.0%とされる。
P(リン)は、不純物として鋼中に含まれ、その含有量が過剰であると、鋼板の延性が著しく低下する。したがって、P含有量は0.030%以下とする。P含有量は0.025%以下であるのが好ましく、0.020%以下であるのがより好ましい。
S(硫黄)は、MnSの微細析出物を形成することで鉄損を増加させ、鋼板の磁気特性を劣化させる元素である。したがって、S含有量は0.0030%以下とする。S含有量は0.0025%以下であるのが好ましく、0.0020%以下であるのがより好ましい。なお、S含有量の極度の低減は製造コストの増加を招くおそれがあるため、S含有量は0.0001%以上であるのが好ましく、0.0003%以上であるのがより好ましく、0.0005%以上であるのがさらに好ましい。
Al(アルミニウム)は、Nと結合してAlNを形成して安定した結晶粒の微細化に有効な元素である。この効果を発揮させるためには、0.005%以上含有する必要がある。一方、0.050%以上を含有すると結晶粒の微細化効果が減少する。したがって、Al含有量は0.005%以上0.050%未満とする。Al含有量は0.008%以上であるのが好ましく、0.010%以上であるのがより好ましく、0.015%以上であるのがより好ましく、0.020%以上であることがより好ましい。また、Al含有量0.048%以下であるのが好ましく、0.045%以下であるのがより好ましい。なお、本明細書において、Al含有量は、母材に含まれる全Alの含有量を意味する。
N(窒素)は、Alと結合してAlNを形成し、安定した結晶粒の微細化に有効な元素である。一方、大量に含有すると過剰なAlNが形成されて鉄損劣化を招く。したがって、N含有量は0.0005~0.0030%とする。N含有量は0.0007%以上であるのが好ましく、0.0010%以上であるのがより好ましい。また、N含有量は0.0027%以下であるのが好ましく、0.0025%以下であるのがより好ましい。
Ti(チタン)は、不可避的に混入する元素であり、炭素または窒素と結合して析出物(炭化物、窒化物)を形成しうる。炭化物または窒化物が形成された場合には、これらの析出物そのものが磁気特性を劣化させる。さらには、仕上焼鈍中の結晶粒の成長を阻害して、磁気特性を劣化させる。したがって、Ti含有量は0.0050%未満とする。Ti含有量は0.0040%以下であるのが好ましく、0.0030%以下であるのがより好ましく、0.0020%以下であるのがさらに好ましい。なお、Ti含有量の極度の低減は製造コストの増加を招くおそれがあるため、Ti含有量は0.0005%以上であるのが好ましい。
Nb(ニオブ)は、炭素または窒素と結合して析出物(炭化物、窒化物)を形成することで高強度化に寄与する元素であるが、これらの析出物そのものが磁気特性を劣化させる。したがって、Nb含有量は0.0050%未満とする。Nb含有量は0.0040%以下であるのが好ましく、0.0030%以下であるのがより好ましく、0.0020%以下であるのがさらに好ましい。Nb含有量は低ければ低いほど好ましく、測定限界以下であるのが好ましい。
Zr(ジルコニウム)は、炭素または窒素と結合して析出物(炭化物、窒化物)を形成することで高強度化に寄与する元素であるが、これらの析出物そのものが磁気特性を劣化させる。したがって、Zr含有量は0.0050%未満とする。Zr含有量は0.0040%以下であるのが好ましく、0.0030%以下であるのがより好ましく、0.0020%以下であるのがさらに好ましい。Zr含有量は低ければ低いほど好ましく、測定限界以下であるのが好ましい。
V(バナジウム)は、炭素または窒素と結合して析出物(炭化物、窒化物)を形成することで高強度化に寄与する元素であるが、これらの析出物そのものが磁気特性を劣化させる。したがって、V含有量は0.0050%未満とする。V含有量は0.0040%以下であるのが好ましく、0.0030%以下であるのがより好ましく、0.0020%以下であるのがさらに好ましい。V含有量は低ければ低いほど好ましく、測定限界以下であるのが好ましい。
Cu(銅)は、不可避的に混入する元素である。意図的なCuの添加は、鋼板の製造コストを増加させる。したがって、本発明においては積極的に添加する必要はなく、不純物レベルでよい。Cu含有量は、製造工程において不可避的に混入しうる最大値である0.20%未満とする。Cu含有量は0.15%以下であるのが好ましく、0.10%以下であるのがより好ましい。なお、Cu含有量の下限値は、特に限定されるものではないが、Cu含有量の極度の低減は製造コストの増加を招くおそれがある。そのため、Cu含有量は0.001%以上であるのが好ましく、0.003%以上であるのがより好ましく、0.005%以上であるのがさらに好ましい。
Ni(ニッケル)は、不可避的に混入する元素である。しかし、Niは、鋼板の強度を向上させる元素でもあるため、意図的に添加してもよい。ただし、Niは高価であるため、意図的に添加する場合は、その含有量を0.50%未満とする。Ni含有量は0.40%以下であるのが好ましく、0.30%以下であるのがより好ましい。なお、Niの含有量の下限値は、特に限定されるものではないが、Ni含有量の極度の低減は製造コストの増加を招くおそれがある。そのため、Ni含有量は0.001%以上であるのが好ましく、0.003%以上であるのがより好ましく、0.005%以上であるのがさらに好ましい。
Sb:0~0.10%
Sn(スズ)およびSb(アンチモン)は、表面に偏析し焼鈍中の酸化および窒化を抑制することで、低い鉄損を確保するのに有用な元素である。また、結晶粒界に偏析して集合組織を改善し、磁束密度を高める効果もある。そのため、必要に応じてSnおよびSbの少なくとも一方を含有させてもよい。しかしながら、これらの元素の含有量が過剰であると、鋼の靱性が低下して冷間圧延が困難となる可能性がある。したがって、SnおよびSbの含有量は、それぞれ0.10%以下とする。SnおよびSbの含有量は、それぞれ0.06%以下であるのが好ましい。なお、上記の効果を得たい場合には、SnおよびSbの少なくとも一方の含有量を、0.005%以上とするのが好ましく、0.010%以上とするのがより好ましい。
上述のように、高強度化の観点からは、鋼中の結晶は細粒であることが望ましい。加えて、ヒステリシス損を低減するためには結晶粒は粗大化させることが好ましく、渦電流損を低減するためには結晶粒は微細化させることが好ましい。
本発明に係る無方向性電磁鋼板において、磁気特性に優れるとは、鉄損W10/400が低く、磁束密度B50が高いことを意味する。ここで、上記の磁気特性は、JIS C 2550-1(2011)に規定されたエプスタイン法に則して、測定することとする。
本発明に係る無方向性電磁鋼板において、高い強度を有するとは、引張強さが650MPa以上であることを意味するものとする。引張強さは660MPa以上であるのが好ましい。ここで、引張強さは、JIS Z 2241(2011)に準拠した引張試験を行うことで、測定することとする。
上述のように、本発明に係る無方向性電磁鋼板においては、母材の表面に絶縁被膜が形成されていることが好ましい。無方向性電磁鋼板は、コアブランクを打ち抜いたのち積層され使用されるため、母材の表面に絶縁被膜を設けることで、板間の渦電流を低減することができ、コアとして渦電流損を低減することが可能となる。
本発明に係る無方向性電磁鋼板の製造方法については特に制限されるものではないが、例えば、上述した化学成分を有する鋼塊に対して、熱間圧延を施し、ついで、以下の工程1または工程2を行うことによって製造することが可能である。
(工程1)熱延板焼鈍を行わずに、冷間圧延および仕上焼鈍を順に行う。
(工程2)950℃以下の温度で熱延板焼鈍を行い、次いで冷間圧延および仕上焼鈍を順に行う。
また、絶縁被膜を母材の表面に形成する場合には、上記仕上焼鈍の後に絶縁被膜の形成が行われる。以下、各工程について、詳細に説明する。
上記の化学組成を有する鋼塊(スラブ)を加熱し、加熱された鋼塊に対して熱間圧延を行い、熱延板を得る。ここで、熱間圧延に供する際の鋼塊の加熱温度については、特に規定するものではないが、例えば、1050~1250℃とすることが好ましい。また、熱間圧延後の熱延板の板厚についても、特に規定するものではないが、母材の最終板厚を考慮して、例えば、1.5~3.0mm程度とすることが好ましい。
その後、鋼板の磁束密度を上昇させることを目的として、熱延板焼鈍を実施してもよい。つまり、工程1では熱延板焼鈍工程は省略される。工程2では熱延板焼鈍工程を行う。熱延板焼鈍工程を行う場合、950℃を超える高温の焼鈍を行うと冷間圧延時に破断が生じるおそれがある。したがって、焼鈍温度は950℃以下とする。連続焼鈍の場合には、熱延鋼板に対して、700~950℃で10~150sの均熱による焼鈍を行うことが好ましい。均熱条件は、800~930℃で10~150sとすることがより好ましい。
上記熱延板焼鈍の後には、酸洗が実施されてもよい。当該酸洗により、母材の表面に生成したスケール層が除去される。ここで、酸洗に用いられる酸の濃度、酸洗に用いる促進剤の濃度、酸洗液の温度等の酸洗条件は、特に限定されるものではなく、公知の酸洗条件とすることができる。なお、熱延板焼鈍が箱焼鈍である場合、脱スケール性の観点から、酸洗工程は、熱延板焼鈍前に実施することが好ましい。この場合、熱延板焼鈍後に酸洗を実施する必要はない。熱延板焼鈍を省略した場合、熱間圧延後の熱延板からスケール層を除去する目的で、熱延板に上記酸洗を行ってもよい。
工程1では熱間圧延工程後、工程2では上記酸洗の後(熱延板焼鈍が箱焼鈍で実施される場合は、熱延板焼鈍工程の後になる場合もある。)に、冷間圧延が実施される。冷間圧延では、例えば母材の最終板厚が0.10~0.35mmとなるような圧下率で、スケール層の除去された酸洗板が圧延される。
上記冷間圧延の後には、仕上焼鈍が実施される。本実施形態に係る無方向性電磁鋼板の製造方法では、仕上焼鈍には、連続焼鈍炉を使用することが好ましい。仕上焼鈍工程は、母材の平均結晶粒径を制御するために、重要な工程である。
上記仕上焼鈍の後には、絶縁被膜の形成工程が実施されてもよい。ここで、絶縁被膜の形成工程については、特に限定されるものではなく、上記のような公知の絶縁被膜処理液を用いて、公知の方法により処理液の塗布および乾燥を行えばよい。
以下、実施例によって本発明をより具体的に説明するが、本発明はこれらの実施例に限定されるものではない。
Claims (5)
- 母材の化学組成が、質量%で、
C:0.0050%以下、
Si:3.8~5.0%、
Mn:0.2%を超えて2.0%未満、
P:0.030%以下、
S:0.0030%以下、
Al:0.005%以上0.050%未満、
N:0.0005~0.0030%、
Ti:0.0050%未満、
Nb:0.0050%未満、
Zr:0.0050%未満、
V:0.0050%未満、
Cu:0.20%未満、
Ni:0.50%未満、
Sn:0~0.10%、
Sb:0~0.10%、
残部:Feおよび不純物であり、
下記(i)式を満足し、
前記母材の平均結晶粒径が、10~80μmである、
無方向性電磁鋼板。
Si+0.5×Mn≧4.3 ・・・(i)
但し、上記式中の元素記号は、各元素の含有量(質量%)である。 - 引張強さが650MPa以上である、
請求項1に記載の無方向性電磁鋼板。 - 前記化学組成が、質量%で、
Sn:0.005~0.10%、および、
Sb:0.005~0.10%、
から選択される1種または2種を含有する、
請求項1または請求項2に記載の無方向性電磁鋼板。 - 前記母材の表面に絶縁被膜を有する、
請求項1から請求項3までのいずれかに記載の無方向性電磁鋼板。 - 請求項1から請求項4までのいずれかに記載の無方向性電磁鋼板を製造する方法であって、
請求項1から請求項3までのいずれかに記載の化学組成を有する鋼塊に対して熱間圧延を施し、次いで以下の工程1または工程2を行い、
(工程1)熱延板焼鈍を行わずに、冷間圧延および仕上焼鈍を順に行う。
(工程2)950℃以下の温度で熱延板焼鈍を行い、次いで前記冷間圧延および前記仕上焼鈍を順に行う。
前記仕上焼鈍は、均熱温度を750~1000℃とし、均熱時間を1~300sとして行う、
無方向性電磁鋼板の製造方法。
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- 2020-04-02 US US17/913,550 patent/US20230104017A1/en active Pending
- 2020-04-02 CN CN202080099081.9A patent/CN115398012A/zh active Pending
- 2020-04-02 JP JP2022511460A patent/JP7469694B2/ja active Active
- 2020-04-02 EP EP20928444.7A patent/EP4130304A4/en active Pending
- 2020-04-02 KR KR1020227032799A patent/KR20220144400A/ko not_active Application Discontinuation
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Also Published As
Publication number | Publication date |
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BR112022016302A2 (pt) | 2022-11-29 |
EP4130304A4 (en) | 2023-05-17 |
CN115398012A (zh) | 2022-11-25 |
KR20220144400A (ko) | 2022-10-26 |
EP4130304A1 (en) | 2023-02-08 |
US20230104017A1 (en) | 2023-04-06 |
JPWO2021199400A1 (ja) | 2021-10-07 |
JP7469694B2 (ja) | 2024-04-17 |
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