WO2022004677A1 - 方向性電磁鋼板の製造方法及び設備列 - Google Patents
方向性電磁鋼板の製造方法及び設備列 Download PDFInfo
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- WO2022004677A1 WO2022004677A1 PCT/JP2021/024423 JP2021024423W WO2022004677A1 WO 2022004677 A1 WO2022004677 A1 WO 2022004677A1 JP 2021024423 W JP2021024423 W JP 2021024423W WO 2022004677 A1 WO2022004677 A1 WO 2022004677A1
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 79
- 239000010959 steel Substances 0.000 title claims abstract description 79
- 238000000034 method Methods 0.000 title claims abstract description 35
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 32
- 238000005096 rolling process Methods 0.000 claims abstract description 129
- 238000005097 cold rolling Methods 0.000 claims abstract description 46
- 238000000137 annealing Methods 0.000 claims abstract description 44
- 238000001953 recrystallisation Methods 0.000 claims abstract description 38
- 230000009467 reduction Effects 0.000 claims abstract description 11
- 239000000203 mixture Substances 0.000 claims abstract description 9
- 238000010438 heat treatment Methods 0.000 claims description 65
- 229910001224 Grain-oriented electrical steel Inorganic materials 0.000 claims description 16
- 230000006698 induction Effects 0.000 claims description 9
- 239000012535 impurity Substances 0.000 claims description 5
- 229910052797 bismuth Inorganic materials 0.000 claims description 4
- 238000005098 hot rolling Methods 0.000 abstract description 3
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 22
- 230000000694 effects Effects 0.000 description 13
- CPLXHLVBOLITMK-UHFFFAOYSA-N Magnesium oxide Chemical compound [Mg]=O CPLXHLVBOLITMK-UHFFFAOYSA-N 0.000 description 10
- 229910052742 iron Inorganic materials 0.000 description 9
- 229910052717 sulfur Inorganic materials 0.000 description 9
- 239000003112 inhibitor Substances 0.000 description 7
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 6
- 229910052782 aluminium Inorganic materials 0.000 description 6
- 230000007423 decrease Effects 0.000 description 6
- 239000010731 rolling oil Substances 0.000 description 6
- 229910052711 selenium Inorganic materials 0.000 description 6
- 238000002791 soaking Methods 0.000 description 6
- 230000032683 aging Effects 0.000 description 5
- 230000008859 change Effects 0.000 description 5
- 239000000395 magnesium oxide Substances 0.000 description 5
- 239000011248 coating agent Substances 0.000 description 4
- 238000000576 coating method Methods 0.000 description 4
- 229910052787 antimony Inorganic materials 0.000 description 3
- 239000003795 chemical substances by application Substances 0.000 description 3
- 230000007547 defect Effects 0.000 description 3
- 230000008569 process Effects 0.000 description 3
- 239000000377 silicon dioxide Substances 0.000 description 3
- 238000003466 welding Methods 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 239000000654 additive Substances 0.000 description 2
- 230000000996 additive effect Effects 0.000 description 2
- 229910052796 boron Inorganic materials 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 229910052802 copper Inorganic materials 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 239000000835 fiber Substances 0.000 description 2
- 229910052839 forsterite Inorganic materials 0.000 description 2
- 230000020169 heat generation Effects 0.000 description 2
- 230000010354 integration Effects 0.000 description 2
- HCWCAKKEBCNQJP-UHFFFAOYSA-N magnesium orthosilicate Chemical compound [Mg+2].[Mg+2].[O-][Si]([O-])([O-])[O-] HCWCAKKEBCNQJP-UHFFFAOYSA-N 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 229910052758 niobium Inorganic materials 0.000 description 2
- 229910052698 phosphorus Inorganic materials 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910019142 PO4 Inorganic materials 0.000 description 1
- 229910010413 TiO 2 Inorganic materials 0.000 description 1
- 208000009205 Tinnitus Diseases 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000008119 colloidal silica Substances 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000005261 decarburization Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000001687 destabilization Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 238000009499 grossing Methods 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 230000005415 magnetization Effects 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- NBIIXXVUZAFLBC-UHFFFAOYSA-K phosphate Chemical compound [O-]P([O-])([O-])=O NBIIXXVUZAFLBC-UHFFFAOYSA-K 0.000 description 1
- 239000010452 phosphate Substances 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000000746 purification Methods 0.000 description 1
- 239000002002 slurry Substances 0.000 description 1
- 230000001629 suppression Effects 0.000 description 1
- 229910052718 tin Inorganic materials 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
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- C—CHEMISTRY; METALLURGY
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B31/00—Rolling stand structures; Mounting, adjusting, or interchanging rolls, roll mountings, or stand frames
- B21B31/02—Rolling stand frames or housings; Roll mountings ; Roll chocks
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/34—Methods of heating
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D11/00—Process control or regulation for heat treatments
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- 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
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- 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
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- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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- C22C38/00—Ferrous alloys, e.g. steel alloys
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- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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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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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2201/00—Treatment for obtaining particular effects
- C21D2201/05—Grain orientation
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- 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
- C21D8/1266—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 between cold rolling steps
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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
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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- 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
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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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
- C22C38/18—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
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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
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
Definitions
- the present invention relates to a method for manufacturing grain-oriented electrical steel sheets and a row of equipment.
- the grain-oriented electrical steel sheet is a steel sheet having an excellent magnetic property having a crystal structure (goss orientation) in which the ⁇ 001> orientation, which is the axis of easy magnetization of iron, is highly integrated in the rolling direction of the steel sheet.
- Patent Document 1 proposes a method of heat-treating a steel sheet at a low temperature (aging treatment) during cold rolling.
- the cooling rate during hot-rolled sheet annealing or pre-annealing for finish cold rolling (final cold rolling) is set to 30 ° C / s or more, and the steel plate temperature is 150 to 300 ° C for 2 minutes during finish cold rolling.
- Patent Document 3 proposes a means for raising the temperature of a steel sheet to a high temperature during cold rolling (warm rolling).
- Patent Document 4 proposes a technique (inhibitorless method) capable of expressing secondary recrystallization without containing a component forming an inhibitor.
- the inhibitorless method is a method of expressing secondary recrystallization by controlling the texture (organization) using higher purified steel. This method eliminates the need for high-temperature steel slab heating and enables low-cost production, but on the other hand, the inhibitor does not have the effect of promoting secondary recrystallization, so it is more delicate to create the texture. Control is required. In particular, in a manufacturing method involving a cold rolling process having a rolling reduction of 80% or more, the characteristics can be significantly affected by the difference in the conditions of the rolling process.
- An object of the present invention is to provide a method for manufacturing a grain-oriented electrical steel sheet having stable magnetic properties in the same coil together with a row of equipment that can be used in the method.
- the present inventors have conducted diligent studies and found that the above problems can be solved by associating the rolling speed in cold rolling with the temperature of the steel sheet, and completed the present invention.
- the temperature of the steel sheet during rolling rises due to the processing heat generated by rolling, but at the same time, heat is removed by the roll in contact with the steel sheet. It will decrease. Since the rolling reduction amount is the same regardless of the rolling speed, even if the rolling speed decreases, the same amount of processing heat is generated, but the time in contact with the roll becomes longer due to the decrease in speed, so the roll The amount of heat removed increases. Therefore, in the portion where the rolling speed is lowered, the temperature of the steel sheet after rolling is lower than that in the portion where the rolling speed is maintained, which impairs the uniformity of the texture of the steel sheet and the iron loss characteristic in the final product. Can be a factor that disperses.
- the rolling speed is set to be less than half of the preset rolling speed set value R 0 (mpm).
- the equipment row of the present invention is provided with a heating device and a cold rolling mill in this order, and the heating by the heating device fluctuates in conjunction with the rolling speed of the cold rolling mill, and this equipment row shall be used. Therefore, even if the rolling speed is changed to less than half of the preset rolling speed set value R 0 (mpm), the steel sheet temperature can be made to satisfy a specific condition.
- the gist of the present invention is as follows. [1] By mass%, C: 0.01-0.10%, Si: 2.0-4.5%, Mn: 0.01-0.5%, Al: less than 0.0100%, S: 0.0070% or less, Se: 0.0070% or less, Contains N: 0.0050% or less and O: 0.0050% or less, A steel slab having a composition of Fe and unavoidable impurities in the balance is hot-rolled to obtain a hot-rolled plate, and the hot-rolled plate is annealed to obtain a hot-rolled plate annealed plate.
- a directional electromagnetic steel sheet that is cold-rolled two or more times with an intermediate annealing sandwiched between them to obtain a cold-rolled plate with a final plate thickness, and the cold-rolled plate is subjected to primary recrystallization annealing and secondary recrystallization annealing.
- the steel plate temperature T 0 (° C) and the rolling speed are 0.5 ⁇ R 0 while the rolling reduction at least once is 80% or more and the rolling speed is the set value R 0 (mpm).
- the steel plate temperature T 1 (° C) while it is less than or equal to (mpm) is Equation: T 1 ⁇ T 0 + 10 °C (1)
- the heating of the heating device is the steel plate temperature T 0 (° C) while the rolling speed of the cold rolling mill is the set value R 0 (mpm), and the rolling speed is 0.5 ⁇ R 0 (mpm) or less. While the steel plate temperature T 1 (° C) is Equation: T 1 ⁇ T 0 + 10 °C (1)
- the equipment row of the above [5] which varies in conjunction with the rolling speed of the cold rolling mill so as to satisfy the above conditions.
- a method for manufacturing a grain-oriented electrical steel sheet having stable magnetic characteristics in the same coil can be carried out using the equipment sequence of the present invention.
- the steel slab used in the manufacturing method of the present invention can be manufactured by a known manufacturing method, and examples of the manufacturing method include steelmaking-continuous casting, ingot-bulk rolling and the like.
- composition of the steel slab is as follows.
- “%” indication regarding the component composition means “mass%” unless otherwise specified.
- C 0.01-0.10%
- C is an element necessary for improving the rolled texture. If it is less than 0.01%, the amount of fine carbides required for improving the texture is small and a sufficient effect cannot be obtained, and if it exceeds 0.10%, decarburization becomes difficult.
- Si 2.0-4.5%
- Si is an element that improves iron loss by increasing electrical resistance. Below 2.0%, this effect is poor, and above 4.5%, cold rolling becomes extremely difficult.
- Mn 0.01-0.5%
- Mn is a useful element in improving hot workability. If it is less than 0.01%, this effect is poor, and if it exceeds 0.5%, the primary recrystallization texture deteriorates and it becomes difficult to obtain highly integrated secondary recrystallized grains in the Goss orientation.
- the production method of the present invention is an inhibitorless method, and the inhibitor-forming elements Al, S, and Se are suppressed to Al: less than 0.0100%, S: 0.0070% or less, and Se: 0.0070% or less, respectively.
- Al, S, Se are excessively present, AlN, MnS, MnSe and the like coarsened by heating the steel slab make the primary recrystallization structure non-uniform, and secondary recrystallization becomes difficult.
- the amounts of Al, S, and Se are preferably Al: 0.0050% or less, S: 0.0050% or less, and Se: 0.0050% or less, respectively.
- the amounts of Al, S, and Se may be 0%, respectively.
- N 0.0050% or less N is suppressed to 0.0050% or less in order to prevent the action as an inhibitor and prevent the formation of Si nitride after purification annealing.
- the amount of N may be 0%.
- O 0.0050% or less O may be regarded as an inhibitor-forming element, and if it exceeds 0.0050%, it is suppressed to 0.0050% or less because secondary recrystallization is difficult due to the coarse oxide.
- the amount of 0 may be 0%.
- the essential component and the inhibitory component of the steel slab have been described above, but the steel slab can appropriately contain one kind or two or more kinds selected from the following elements.
- Ni 0.005 to 1.50%
- Ni has the function of improving the magnetic properties by increasing the uniformity of the hot-rolled plate structure.
- Ni When Ni is contained, it can be 0.005% or more from the viewpoint of obtaining a sufficient addition effect, and 1.50% or less in order to avoid deterioration of magnetic properties due to destabilization of secondary recrystallization. can do.
- Sn 0.01 to 0.50%
- Sb 0.005 to 0.50%
- Cu 0.01 to 0.50%
- Mo 0.01 to 0.50%
- P 0.0050 to 0.50%
- Cr 0.01 to 1.50%
- Nb 0.0005 to 0.0200%
- B 0.0005-0.0200%
- Bi 0.0005-0.0200% All of these elements contribute effectively to the improvement of iron loss.
- Sn, Sb, Cu, Nb, B, and Bi are elements that may be regarded as auxiliary inhibitors, and it is not preferable to contain them in excess of the upper limit.
- the rest of the composition of the steel slab is Fe and unavoidable impurities.
- a steel slab having the above-mentioned composition is hot-rolled to obtain a hot-rolled plate, and the hot-rolled plate is annealed to obtain a hot-rolled plate annealed plate.
- Pickling may be performed before cold rolling.
- a steel slab having the above composition is hot-rolled to obtain a hot-rolled plate.
- the steel slab can be hot-rolled after being heated to a temperature of, for example, 1050 ° C or higher and lower than 1300 ° C. Since the steel slab in the present invention has an inhibitor component suppressed, it does not need to be subjected to a high temperature treatment of 1300 ° C. or higher because it is completely solid-dissolved. When heated to 1300 ° C or higher, the crystal structure becomes too large and may cause defects called hege, so heating is preferably less than 1300 ° C. From the viewpoint of smooth rolling of the steel slab, it is preferable to heat it to 1050 ° C. or higher.
- the other hot rolling conditions are not particularly limited, and known conditions can be applied.
- the obtained hot-rolled plate is annealed to obtain a hot-rolled plate annealed plate, but at that time, the annealing conditions are not particularly limited, and known conditions can be applied.
- the obtained hot-rolled plate is annealed by hot-rolled plate and then cold-rolled.
- Cold rolling may be performed once or twice or more with intermediate annealing sandwiched between them.
- rolling with a rolling reduction of 80% or more is performed.
- Rolling with a rolling reduction of 80% or more is advantageous in that it can increase the degree of integration of aggregates and create a structure that is advantageous for magnetic properties, but it is greatly affected by fluctuations in rolling speed. According to the present invention, this influence is reduced, and a grain-oriented electrical steel sheet having stable magnetic properties can be obtained in the same coil in a manufacturing method including cold rolling in which a rolling reduction is 80% or more.
- the rolling speed of cold rolling is set in advance in consideration of various conditions such as the production amount and the capacity of the rolling mill.
- the preset rolling speed is applied, but due to the shape defect of the coil applied to cold rolling, ear cracking at the edge part, and hedging defects in the hot rolling process, etc., in the longitudinal direction. In some cases, the rolling speed must be reduced. Further, when a tandem rolling mill is used for cold rolling, the rolling speed is reduced due to the work of welding the leading coil and the trailing coil. Therefore, the actual rolling speed may fluctuate with respect to the preset rolling speed set value R 0 (mpm), and in the above situation, the measured value may be less than half of R 0.
- the part of the coil to which the preset rolling speed setting value R 0 (mpm) is applied is the "stationary part", and the part of the coil where the rolling speed drops to less than half the set value R 0 (mpm) is “decelerated”. Also called “club”.
- the deceleration part due to welding is usually 5 to 20% of the total length of the coil from both ends, and other than that, unless there are special circumstances such as poor coil shape, the rolling speed is set in advance.
- the value R 0 (mpm) can be applied.
- the upper limit of T 1 (° C) is not particularly limited and can be set as appropriate.
- the temperature may be such that the performance of the rolling oil can be sufficiently exhibited, and the upper limit can be, for example, 265 ° C. or lower.
- T 1 (° C) can satisfy the above formula (1) and can be T 0 + 100 ° C or less.
- the rolling speed can be assumed to be an arbitrary position in the rolling process, and can be, for example, the speed on the exit side of the rolling mill.
- the set value R 0 (mpm) of the rolling speed is not particularly limited, and may be, for example, 200 (mpm) or more, preferably 600 (mpm) or more.
- the upper limit varies depending on the equipment, but it is preferably 2000 (mpm) or less because an increase in rolling speed also promotes an increase in deformation resistance.
- the rolling speed of the speed reduction section is the speed at the same position as the set value.
- the deceleration part is a part where the speed drops to half (0.5 ⁇ R 0 ) or less of the set value R 0 (mpm), and is usually 0.1 ⁇ R 0 (mpm) or more and 0.5 ⁇ R 0 (mpm) or less.
- the rolling speed of the stationary part is as per the set value R 0 (mpm) of the rolling speed, but a width of about ⁇ 10% is acceptable.
- the set value R 0 (mpm) of the rolling speed includes the case where the measured value of the rolling speed is R 0 (mpm) ⁇ 0.1 ⁇ R 0 (mpm).
- the temperature of the steel sheet can be assumed to be an arbitrary position in the rolling process, for example, it can be the temperature on the entrance side of the rolling mill, and in a rolling mill equipped with a heating device on the entry side of the rolling mill, It is the exit side of the heating device. From the viewpoint of stable control, it is preferable to set the temperature of the steel sheet immediately after leaving the heating device.
- T 0 which is the temperature of the steel plate in the stationary portion, can be appropriately set according to the composition of the steel slab, the characteristics of the desired steel plate, and the like, and can be, for example, 20 ° C or higher, preferably 50 ° C or higher. Moreover, the upper limit can be set as appropriate.
- the upper limit can be set in consideration of the temperature at which the performance of the rolling oil can be sufficiently exhibited, and it may differ depending on the type of rolling oil.
- the upper limit can be, for example, 250 ° C. or lower, preferably 150 ° C. or lower.
- the manufacturing method of the present invention uses an equipment row in which a heating device and a cold rolling mill are provided in this order, and the heating by the heating device fluctuates in conjunction with the rolling speed of the cold rolling mill. Can be done by.
- the heating by the heating device which fluctuates in conjunction with the rolling speed may be performed so as to satisfy the above (1) and (1') according to the change of the rolling speed, and the heating is performed by the heating device accompanying the change of the rolling speed. It can be executed in consideration of the change in output. Normally, the decrease in rolling speed and the increase in the output of the heating device are linked, and the increase in the rolling speed and the decrease in the output of the heating device (including the output off) are linked. It also includes increasing the output of the heating device when the rolling speed falls below a predetermined value, or decreasing or turning off the output of the heating device when the pressure rate exceeds a predetermined value.
- the temperature of T 1 is preferably within the range in which the performance of the rolling oil is maintained. These controls are preferably performed by a mechanism in which fluctuations in rolling speed are reflected in the output control of the heating device.
- the heating method of the heating device is not particularly limited, but heating methods such as induction heating, energization heating, and infrared heating are preferable because the temperature can be raised in a short time and synchronization with the rolling speed is easy.
- the phenomenon of lowering the temperature of the steel sheet when the rolling speed decreases is essentially the same regardless of which rolling mill is used, but the aging time between passes is short like a tandem rolling mill, and it depends on the aging.
- the manufacturing method of the present invention is advantageous when cold rolling is performed by a tandem rolling mill.
- a heating device is placed just before the first stand. This is because if heating is performed immediately before the first stand, the influence of the heating extends to all the stands during rolling, and the texture can be improved with higher efficiency than heating between the stands in the middle.
- the obtained cold-rolled plate with the final plate thickness (also referred to as “final cold-rolled plate”) is subjected to primary recrystallization annealing and secondary recrystallization annealing to obtain grain-oriented electrical steel sheets.
- primary recrystallization annealing is applied to the final cold-rolled sheet, an annealing separator is applied to the surface of the steel sheet, and then secondary recrystallization annealing can be performed.
- the primary recrystallization annealing is not particularly limited and can be carried out by a known method.
- the annealing separator is not particularly limited, and known annealing separators can be used.
- a water slurry having magnesia as a main agent and an additive such as TiO 2 added as necessary can be used.
- Annealing separators containing silica, alumina and the like can also be used.
- the secondary recrystallization annealing is not particularly limited and can be performed by a known method.
- a separating agent containing magnesia as a main agent is used, a film mainly containing forsterite is formed together with secondary recrystallization. If a film mainly composed of forsterite is not formed after the secondary recrystallization annealing, various additional steps such as a process of forming a new film and a process of smoothing the surface may be performed.
- the type of the insulating film is not particularly limited, and any known insulating film can be used, and a coating liquid containing a phosphate-chromic acid-colloidal silica is applied to a steel sheet.
- the method of applying to and baking at about 800 ° C is preferable.
- Japanese Patent Application Laid-Open No. 50-79442 and Japanese Patent Application Laid-Open No. 48-39338 can be referred to.
- the shape of the steel sheet may be adjusted by flattening annealing, and further, flattening annealing that also serves as baking of the insulating film may be performed.
- Example 1 By mass%, C: 0.04%, Si: 3.2%, Mn: 0.05%, Al: 0.005%, Sb: 0.01% and S, Se, N, O are each reduced to 50ppm or less, and the balance Fe and unavoidable.
- a steel slab composed of impurities was heated to 1180 ° C. and hot-rolled to form a 2.0 mm hot-rolled coil, which was then annealed at 1050 ° C. for 50 seconds. Next, it was reduced to a plate thickness of 0.23 mm using a tandem rolling mill (roll diameter 300 mm ⁇ , 4 stands) to form a cold-rolled plate.
- the set speed of the rolling speed was 350 mmp (steady part), and the rolling speed was reduced to 100 mmp at the tip and tail end (decelerated part).
- the tail end is a portion 200 m from both ends with respect to the total length of 1800 m in the longitudinal direction of the coil.
- a rolling mill equipped with an induction heating device on the entry side of the first pass of the rolling mill was used, and the output to the induction heating device was changed according to the change in the rolling speed to control the steel sheet temperature.
- the steel sheet temperature is the temperature immediately after leaving the heating device. Specifically, in the deceleration section, the temperature of the steel sheet was set to 50 ° C. by positively heating with an induction heating device.
- the stationary part was rolled at room temperature (25 ° C.).
- FIG. 1 shows changes in rolling speed and steel plate speed.
- the horizontal axis is the distance from the tip of the coil (rolling distance (m)).
- the obtained cold rolled sheet was subjected to primary recrystallization annealing at a soaking temperature of 850 ° C. and a soaking time of 90 seconds.
- An annealing separator containing MgO as a main component was applied to the obtained primary recrystallization annealed plate, and secondary recrystallization annealing was performed at a maximum reaching temperature of 1190 ° C. and a holding time of 6 hours at the maximum temperature.
- a coating solution containing phosphate as the main component was applied to the obtained secondary recrystallization annealed plate, and annealing was performed at 900 ° C. for 120 seconds, which also served as strain removal as well as baking.
- the maximum iron loss difference ( ⁇ W 17/50 (W / kg)) between the deceleration part (100mpm) during rolling of the obtained steel sheet and the stationary part (350mpm) was 0.008W / kg.
- the deceleration part was not heated at room temperature (25 ° C), and the maximum iron loss difference ( ⁇ W 17/50 ) was obtained in the same manner as above, and it was 0.017 W / kg.
- Example 2 By mass%, it contains C: 0.05%, Si: 3.3%, Mn: 0.06%, Al: 0.005%, Cr: 0.01%, P: 0.01%, S, Se and O are less than 50ppm respectively, and N is 35ppm.
- the steel slab consisting of the balance Fe and unavoidable impurities is heated to 1100 ° C, then hot-rolled to make a hot-rolled coil with a plate thickness of 2.0 mm, and then annealed at 1050 ° C for 60 seconds. did. Then, using a tandem rolling mill (roll diameter 380 mm ⁇ , 4 stands), it was reduced to 0.25 mm to form a cold rolled plate.
- the rolling speed was changed in the same coil, and at the same time, the temperature of the steel sheet was changed by the induction heating device installed on the entry side of the first pass of the rolling mill.
- Table 1 shows the rolling conditions. In a tandem rolling mill, the rolling speed changes for each pass, but the rolling speed shown in Table 1 is the speed on the side of the final stand of the rolling mill. The reduction rate for one stand (first pass) was 32%.
- the obtained cold rolled sheet was subjected to primary recrystallization annealing at a soaking temperature of 800 ° C. and a soaking time of 50 seconds. From the primary recrystallization annealed sheet, 10 test pieces of 30 mm ⁇ 30 mm were cut out from the part (deceleration part) where the temperature of the steel sheet was changed by induction heating during cold rolling, and the X-ray inverse strength was measured.
- an annealing separator containing MgO as the main component was applied to the primary recrystallization annealed plate, and secondary recrystallization annealing was performed at a maximum reaching temperature of 1210 ° C. and a holding time of 3 hours at the maximum temperature.
- a coating solution containing a phosphate-chromate-coloidal silica at a weight ratio of 3: 1: 2 was applied to the obtained secondary recrystallization annealed plate, and a baking treatment was performed at 800 ° C. for 30 seconds.
- Table 1 shows the calculated values of the steel plate temperature after one stand (first pass), but in the example of the invention, it can be seen that the temperature difference between the stationary portion and the deceleration portion is small.
- the calculated value of the steel sheet temperature takes into consideration the "processing heat generation” generated in the steel sheet by rolling, the “friction heat generation” generated between the roll and the steel sheet, and the “roll heat removal” generated by the contacting roll. Is.
- Example 3 The steel slab containing the components shown in Table 2 was heated to 1200 ° C., hot-rolled to obtain a hot-rolled coil having a plate thickness of 2.2 mm, and then annealed at 950 ° C. for 30 seconds. Then, using a tandem rolling mill (roll diameter 280 mm ⁇ 4 stand), it was reduced to 0.27 mm to form a cold rolled plate.
- the set value of the rolling speed was 700mpm, and the rolling speed was reduced to 150mpm at the deceleration part.
- the temperature of the steel strip immediately after leaving the heating device will be 50 ° C during the rolling speed according to the set value and 75 ° C at the deceleration part. Heated to.
- the obtained cold rolled sheet was subjected to primary recrystallization annealing at a heating rate of 200 ° C./s between 300 ° C. and 700 ° C., a soaking temperature of 850 ° C., and a soaking time of 40 seconds.
- An annealing separator containing MgO as the main component was applied to the primary recrystallization annealing plate, and secondary recrystallization annealing was performed at the maximum reaching temperature of 1210 ° C. and the holding time of 3 hours at the maximum temperature.
- a coating solution containing a phosphate-chromate-coloidal silica at a weight ratio of 3: 1: 2 was applied to the obtained secondary recrystallization annealed plate, and flattening annealing was performed at 850 ° C. for 30 seconds. After that, a 30 mm ⁇ 280 mm test piece was cut out from each of the stationary part and the deceleration part so that the total weight was 500 g or more, and the iron loss W 17/50 (W / kg) was measured by the Epstein test. The results are shown in Table 2.
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Abstract
Description
このような高い方位集積度を実現するために、例えば、特許文献1では、冷間圧延中に鋼板を低温で熱処理(時効処理)する方法が提案されている。
特許文献2では、熱延板焼鈍又は仕上げ冷間圧延(最終冷間圧延)前焼鈍時の冷却速度を30℃/s以上とし、さらに仕上げ冷間圧延中に鋼板温度150~300℃で2分間以上のパス間時効処理を2回以上行う技術が開示されている。
特許文献3では、冷間圧延中に鋼板温度を高温とする(温間圧延)手段が提案されている。
[1]質量%で、
C:0.01~0.10%、
Si:2.0~4.5%、
Mn:0.01~0.5%、
Al:0.0100%未満、
S:0.0070%以下、
Se:0.0070%以下、
N:0.0050%以下及び
O:0.0050%以下を含有し、
残部がFe及び不可避的不純物の成分組成を有する鋼スラブを、熱間圧延して熱延板とし、前記熱延板を焼鈍して熱延板焼鈍板とし、前記熱延板焼鈍板に1回又は中間焼鈍を挟んだ2回以上の冷間圧延を施して最終板厚の冷延板とし、前記冷延板に一次再結晶焼鈍及び二次再結晶焼鈍を施すことを含む、方向性電磁鋼板の製造方法であって、
前記冷間圧延は、少なくとも1回の圧下率が80%以上であり、かつ圧延速度が設定値R0(mpm)である間の鋼板温度T0(℃)と、圧延速度が0.5×R0(mpm)以下である間の鋼板温度T1(℃)が、
式:T1≧T0+10℃ (1)
を満たす冷間圧延を含む、方向性電磁鋼板の製造方法。
[2]冷間圧延をタンデム圧延機で行う、上記[1]の方向性電磁鋼板の製造方法。
[3]前記タンデム圧延機の入側で熱延板焼鈍板を加熱することにより、圧延速度が設定値R0(mpm)である間の鋼板温度T0(℃)と、圧延速度が0.5×R0(mpm)以下である間の鋼板温度T1(℃)が、
式:T1≧T0+10℃ (1)
を満たすようにする、上記[2]記載の方向性電磁鋼板の製造方法。
[4]鋼スラブが、さらに、質量%で、
Ni:0.005~1.50%、
Sn:0.01~0.50%、
Sb:0.005~0.50%、
Cu:0.01~0.50%、
Mo:0.01~0.50%、
P:0.0050~0.50%
Cr:0.01~1.50%、
Nb:0.0005~0.0200%、
B:0.0005~0.0200%及び
Bi:0.0005~0.0200%
からなる群より選ばれる1種又は2種以上を含有する、上記[1]~[3]のいずれかの方向性電磁鋼板の製造方法。
[5]加熱装置及び冷間圧延機をこの順に備えた設備列であって、前記加熱装置による加熱が、前記冷間圧延機の圧延速度に連動して変動する、設備列。
[6]前記加熱装置の加熱が、前記冷間圧延機の圧延速度が設定値R0(mpm)である間の鋼板温度T0(℃)と、圧延速度が0.5×R0(mpm)以下である間の鋼板温度T1(℃)が、
式:T1≧T0+10℃ (1)
を満たすように、前記冷間圧延機の圧延速度に連動して変動する、上記[5]の設備列。
[7]加熱装置が、誘導加熱、通電加熱又は赤外加熱のいずれかの加熱方式を利用する、上記[5]又は[6]に記載の設備列。
<鋼スラブ>
本発明の製造方法で使用する鋼スラブは、公知の製造方法によって、製造されたものであることができ、製造方法としては、例えば製鋼-連続鋳造、造塊-分塊圧延等が挙げられる。
Cは圧延集合組織改善のために必要な元素である。0.01%未満では集合組織改善に必要な微細炭化物の量が少なく十分な効果が得られず、また、0.10%超では脱炭が困難となる。
Siは電気抵抗を高めることで鉄損を改善する元素である。2.0%未満ではこの効果に乏しく、また、4.5%超では冷間圧延が著しく困難になる。
Mnは熱間加工性を向上させる点で有用な元素である。0.01%未満ではこの効果に乏しく、また、0.5%超では一次再結晶集合組織が劣化し、Goss方位に高度に集積した二次再結晶粒を得るのが難しくなる。
本発明の製造方法はインヒビターレス法であり、インヒビター形成元素であるAl、S、Seは、それぞれ、Al:0.0100%未満、S:0.0070%以下、Se:0.0070%以下に抑制される。Al、S、Seが過剰に存在すると、鋼スラブ加熱によって粗大化したAlN、MnS、MnSe等が一次再結晶組織を不均一にし、二次再結晶が困難となる。Al、S、Seの量は、それぞれ、Al:0.0050%以下、S:0.0050%以下、Se:0.0050%以下が好ましい。Al、S、Seの量は、それぞれ0%でもよい。
Nは、インヒビターとしての作用を防止し、純化焼鈍後にSi窒化物の生成を防止するために、0.0050%以下に抑制される。Nの量は0%でもよい。
Oは、インヒビター形成元素とされることもあり、0.0050%超では粗大な酸化物に起因して二次再結晶を困難にするため、0.0050%以下に抑制される。0の量は0%でもよい。
Niは、熱延板組織の均一性を高めることにより、磁気特性を改善する働きがある。Niを含有させる場合、十分な添加効果を得る点から、0.005%以上とすることができ、また、二次再結晶の不安定化により磁気特性が劣化することを回避するため、1.50%以下とすることができる。
これらの元素はいずれも、鉄損の改善に有効に寄与する。これらの元素を含有させる場合、十分な添加効果を得る点から、それぞれの下限値以上で含有させることができ、また、二次再結晶粒を十分に発達させる点から、それぞれの上限値以下で含有させることができる。中でも、Sn、Sb、Cu、Nb、B、Biは補助インヒビターとみなされることもある元素であり、上限値を超えて含有させることは好ましくない。
本発明の製造方法は、上記の成分組成を有する鋼スラブを、熱間圧延して熱延板とし、前記熱延板を焼鈍して熱延板焼鈍板とし、前記熱延板焼鈍板に1回又は中間焼鈍を挟んだ2回以上の冷間圧延を施して最終板厚の冷延板とし、前記冷延板に一次再結晶焼鈍及び二次再結晶焼鈍を施すことを含む。冷間圧延の前に酸洗を施してもよい。
それ以外の熱間圧延条件は特に限定されず、公知の条件を適用することができる。
式:T1≧T0+10℃ (1)
を満たすことで、同一コイル内の集合組織の変動を抑制し、二次再結晶挙動を安定化させるものである。
同一コイル内の集合組織の均一化の点からは、好ましくは
式:T1≧T0+15℃ (1’)
を満たすこととする。
T1(℃)は、上記式(1)を満たし、かつT0+100℃以下であることができる。
減速部の圧延速度は、設定値と同様の位置での速度である。減速部は設定値R0(mpm)の半分(0.5×R0)以下の速度に低下する部分であり、通常、0.1×R0(mpm)以上0.5×R0(mpm)以下である。
質量%で、C:0.04%、Si:3.2%、Mn:0.05%、Al:0.005%、Sb:0.01%及びS、Se、N、Oをそれぞれ50ppm以下にまで低減させ、残部Fe及び不可避的不純物よりなる鋼スラブを1180℃に加熱し、熱間圧延により2.0mmの熱延コイルとした後、1050℃50秒の熱延板焼鈍を施した。次いで、タンデム圧延機(ロール径300mmφ、4スタンド)を用いて板厚0.23mmまで圧下し、冷延板とした。
この際、圧延速度の設定速度は350mpmであり(定常部)、先尾端では圧延速度を100mpmに低下させた(減速部)。先尾端は、コイルの長手方向の全長1800mに対して、両端からそれぞれ200mの部分である。
冷間圧延においては、圧延機初パス入側に誘導加熱装置を配した圧延機を使用し、圧延速度の変更に合わせ、誘導加熱装置への出力を変更し、鋼板温度を制御した。ここで、鋼板温度は加熱装置を出た直後の温度である。具体的には、減速部では、誘導加熱装置により積極的な加熱を行うことにより鋼板温度を50℃とした。一方、定常部は室温(25℃)で圧延を行った。
得られた一次再結晶焼鈍板に、MgOを主剤とする焼鈍分離剤を塗布し、焼鈍の最高到達温度1190℃、最高温度での保持時間6時間の二次再結晶焼鈍を施した。
得られた二次再結晶焼鈍板にリン酸塩を主剤とするコーティング液を塗布し、焼付けと共に歪取りを兼ねた900℃、120秒の焼鈍を行なった。得られた鋼板の圧延時の減速部(100mpm)と、定常部(350mpm)との最大鉄損差(ΔW17/50(W/kg)は、0.008W/kgであった。
質量%で、C:0.05%、Si:3.3%、Mn:0.06%、Al:0.005%、Cr:0.01%、P:0.01%を含有し、S、Se、Oを各々50ppm未満、Nを35ppm未満に抑制し、残部Fe及び不可避的不純物よりなる鋼スラブを1100℃に加熱後、熱間圧延により板厚2.0mmの熱延コイルとした後、1050℃、60秒の熱延板焼鈍を施した。次いで、タンデム圧延機(ロール径380mmφ、4スタンド)を用いて、0.25mmまで圧下し冷延板とした。
一次再結晶焼鈍板から、冷間圧延時に誘導加熱によって鋼板温度を変更した部位(減速部)から、30mm×30mmの試験片を10枚切り出し、X線インバース強度測定を行なった。
得られた二次再結晶焼鈍板にリン酸塩-クロム酸塩-コロイダルシリカを重量比3:1:2で含有する塗布液を塗布し、800℃、30秒の焼き付け処理を行った。さらに800℃、3時間の歪取り焼鈍を行なった後、定常部と減速部のそれぞれから30mm×280mmの試験片10枚を切り出し、エプスタイン試験により、鉄損W17/50(W/kg)を測定した。
表1には、1スタンド(初パス)後の鋼板温度の計算値を示してあるが、発明例では定常部と減速部とで温度差が小さいことがわかる。ここで、鋼板温度の計算値は、圧延によって鋼板内で生じる「加工発熱」及びロールと鋼板間で生じる「摩擦発熱」と、接触しているロールによって生じる「ロール抜熱」とを考慮したものである。
表2に示す成分を含有した鋼スラブを1200℃に加熱後、熱間圧延により板厚2.2mmの熱延コイルとした後、950℃、30秒の熱延板焼鈍を施した。次いで、タンデム圧延機(ロール径280mmφ4スタンド)を用いて、0.27mmまで圧下し冷延板とした。
一次再結晶焼鈍板にMgOを主剤とする焼鈍分離剤を塗布し、焼鈍の最高到達温度1210℃、最高温度での保持時間3時間の二次再結晶焼鈍を施した。
得られた二次再結晶焼鈍板に、リン酸塩-クロム酸塩-コロイダルシリカを重量比3:1:2で含有する塗布液を塗布し、850℃、30秒の平坦化焼鈍を行なった後、定常部と減速部のそれぞれから、30mm×280mmの試験片を総重量が500g以上となるように切り出し、エプスタイン試験により、鉄損W17/50(W/kg)を測定した。結果を表2に示す。
Claims (7)
- 質量%で、
C:0.01~0.10%、
Si:2.0~4.5%、
Mn:0.01~0.5%、
Al:0.0100%未満、
S:0.0070%以下、
Se:0.0070%以下、
N:0.0050%以下及び
O:0.0050%以下を含有し、
残部がFe及び不可避的不純物の成分組成を有する鋼スラブを、熱間圧延して熱延板とし、前記熱延板を焼鈍して熱延板焼鈍板とし、前記熱延板焼鈍板に1回又は中間焼鈍を挟んだ2回以上の冷間圧延を施して最終板厚の冷延板とし、前記冷延板に一次再結晶焼鈍及び二次再結晶焼鈍を施すことを含む、方向性電磁鋼板の製造方法であって、
前記冷間圧延は、少なくとも1回の圧下率が80%以上であり、かつ圧延速度が設定値R0(mpm)である間の鋼板温度T0(℃)と、圧延速度が0.5×R0(mpm)以下である間の鋼板温度T1(℃)が、
式:T1≧T0+10℃ (1)
を満たす冷間圧延を含む、方向性電磁鋼板の製造方法。 - 冷間圧延をタンデム圧延機で行う、請求項1に記載の方向性電磁鋼板の製造方法。
- 前記タンデム圧延機の入側で熱延板焼鈍板を加熱することにより、圧延速度が設定値R0(mpm)である間の鋼板温度T0(℃)と、圧延速度が0.5×R0(mpm)以下である間の鋼板温度T1(℃)が、
式:T1≧T0+10℃ (1)
を満たすようにする、請求項2に記載の方向性電磁鋼板の製造方法。 - 鋼スラブが、さらに、質量%で、
Ni:0.005~1.50%、
Sn:0.01~0.50%、
Sb:0.005~0.50%、
Cu:0.01~0.50%、
Mo:0.01~0.50%、
P:0.0050~0.50%
Cr:0.01~1.50%、
Nb:0.0005~0.0200%、
B:0.0005~0.0200%及び
Bi:0.0005~0.0200%
からなる群より選ばれる1種又は2種以上を含有する、請求項1~3のいずれか一項記載の方向性電磁鋼板の製造方法。 - 加熱装置及び冷間圧延機をこの順に備えた設備列であって、前記加熱装置による入熱量が、前記冷間圧延機の圧延速度に連動して変動する、設備列。
- 前記加熱装置の加熱が、前記冷間圧延機の圧延速度が設定値R0(mpm)である間の鋼板温度T0(℃)と、圧延速度が0.5×R0(mpm)以下である間の鋼板温度T1(℃)が、
式:T1≧T0+10℃ (1)
を満たすように、前記冷間圧延機の圧延速度に連動して変動する、請求項5記載の設備列。 - 前記加熱装置が、誘導加熱、通電加熱又は赤外加熱のいずれかの加熱方式を利用する、請求項5又は6に記載の設備列。
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