WO2018080167A1 - Tôle en acier électrique à grains orientés et procédé de fabrication de celle-ci - Google Patents

Tôle en acier électrique à grains orientés et procédé de fabrication de celle-ci Download PDF

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Publication number
WO2018080167A1
WO2018080167A1 PCT/KR2017/011849 KR2017011849W WO2018080167A1 WO 2018080167 A1 WO2018080167 A1 WO 2018080167A1 KR 2017011849 W KR2017011849 W KR 2017011849W WO 2018080167 A1 WO2018080167 A1 WO 2018080167A1
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Prior art keywords
grain
steel sheet
electrical steel
oriented electrical
weight
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PCT/KR2017/011849
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English (en)
Korean (ko)
Inventor
박창수
한규석
주형돈
서진욱
김우신
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주식회사 포스코
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Priority to EP17866141.9A priority Critical patent/EP3533896B1/fr
Priority to CN201780066820.2A priority patent/CN109906284B/zh
Priority to US16/345,488 priority patent/US20190309387A1/en
Priority to JP2019522885A priority patent/JP6808830B2/ja
Publication of WO2018080167A1 publication Critical patent/WO2018080167A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • 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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C2202/00—Physical properties
    • C22C2202/02—Magnetic
    • 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
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/14766—Fe-Si based alloys
    • H01F1/14775—Fe-Si based alloys in the form of sheets

Definitions

  • It relates to a grain-oriented electrical steel sheet and a method of manufacturing the same. More specifically
  • the present invention relates to a grain-oriented electrical steel sheet containing a predetermined amount of B, Ba, and -Y and segregated at grain boundaries, and a method of manufacturing the same.
  • a grain-oriented electrical steel sheet is a soft magnetic material having excellent magnetic properties in the rolling direction composed of grains having a Goss orientation, which has a crystal orientation of ⁇ 110 ⁇ ⁇ 001>.
  • magnetic properties are due to magnetic flux density and iron loss. Can be expressed, and high, the magnetic flux density can be obtained by precisely arranging the orientation of crystal grains in ⁇ 110 ⁇ ⁇ 001> orientation. Electrical steel sheet with high magnetic flux density can reduce the size of iron core material of electric equipment, as well as reduce hysteresis loss, thereby increasing the miniaturization and high efficiency of electric equipment.
  • the iron loss is a power loss consumed as heat energy when an arbitrary AC magnetic field to the steel sheet, grater, and greatly changed by such magnetic flux density and thickness, impurity, resistivity, and secondary recrystallized grains size in the steel sheet, and the magnetic flux density
  • the electrical steel sheet has a strong development of Goss texture in the ⁇ 110 ⁇ ⁇ 001> direction in the rolling direction of the steel sheet.
  • An abnormal grain growth called recrystallization must be formed. This abnormal crystal growth occurs when normal grain growth, unlike normal grain growth, is suppressed by the movement of grain boundaries that normally grow by precipitates, inclusions, or elements that are dissolved or segregated at grain boundaries. As such, precipitates and inclusions that inhibit grain growth are specifically called grain growth inhibitors (inh ibi tor), and research on the grain-oriented electrical steel sheet manufacturing technology by secondary recrystallization of ⁇ 110 ⁇ Inhibitors have been used to form a highly integrated secondary recrystallization for the ⁇ 110 ⁇ ⁇ 001> orientation to secure excellent magnetic properties.
  • grain growth inhibitors inh ibi tor
  • precipitates such as A1N and MnS [Se] are mainly used as grain growth inhibitors.
  • decarburization is carried out, and then nitrogen is supplied to the inside of the steel sheet through a separate nitriding process using ammonia gas to cause secondary recrystallization by nitride of A1 system that exhibits strong grain growth suppression effect.
  • nitrogen is supplied to the inside of the steel sheet through a separate nitriding process using ammonia gas to cause secondary recrystallization by nitride of A1 system that exhibits strong grain growth suppression effect.
  • the high temperature annealing process intensifies the instability of the precipitates due to denitrification or remodeling due to the atmosphere inside the furnace, and the necessity of long-term purifying annealing for 30 hours or longer at high temperatures involves complexity and cost burden in the manufacturing process.
  • Ba and Y are excellent in inhibiting grain growth enough to enable secondary recrystallization, and are not affected by the atmosphere in the furnace during the high temperature annealing process.
  • Ba and Y have the disadvantage of weakening the binding force of grain boundaries. Therefore, there is a problem that a number of intergranular cracks are generated in the cold rolling process that requires a strong rolling, and thus the productivity decrease cannot be avoided.
  • the grain-oriented electrical steel sheet according to an embodiment of the present invention in weight percent, Si: 1.0 To 7.0%, B: 0.001 to 0.13 ⁇ 4, and B a and Y alone or in total, from 0.005% to 0.5% by weight, the balance including Fe and other unavoidable impurities.
  • the grain-oriented electrical steel sheet according to one embodiment of the present invention may satisfy the following Equation 1.
  • Mn may further comprise 0.01% to 0.5%.
  • the average particle diameter of the grains having a particle size of 2 GPa or more may be 10 GPa or more.
  • the balance being heated by a slab containing Fe and other unavoidable impurities; Hot rolling the slab to produce a hot rolled plate; Cold rolling the hot rolled sheet to produce a cold rolled sheet; Whether the cold rolled sheet is subjected to primary recrystallization annealing; And; And a second recrystallization annealing of the cold rolled plate on which the first recrystallization annealing is completed.
  • the slab may satisfy the following formula 1. '
  • the slab may further comprise Mn: 0.01% to 0.5%.
  • the slab In the step of heating the slab, it may be heated to 1000 to 128 (TC.
  • TC In the step of cold rolling the hot rolled sheet to produce a cold rolled sheet,
  • the secondary recrystallization annealing step includes a temperature raising step and a cracking step, and the temperature of the cracking step may be 900 to 1250 ° C.
  • the grain-oriented electrical steel sheet according to an embodiment of the present invention has excellent magnetic properties by stably forming a goth crystal grain.
  • the grain boundary strengthening effect reduces grain boundary cracks even under cold rolling, resulting in improved productivity and lower manufacturing costs.
  • first, second and third rounds are used to describe various parts, components, regions, layers and / or sections, but are not limited to these. These terms are only used to distinguish one part, component, region, layer or section from another part, component, region, layer or section. Accordingly, the first portion, component, region, layer or section described below may be referred to as the second portion, component, region, layer or section without departing from the scope of the invention.
  • % means weight% and lppm is 0.002 weight%.
  • the existing grain-oriented electrical steel sheet technology uses precipitates such as A1N and MnS as grain growth inhibitors, and all the processes strictly control the distribution of the precipitates and conditions for removing the remaining precipitates in the secondary recrystallized steel sheet. The process conditions are extremely limited.
  • a grain growth inhibitor do not use precipitates such as A1N, MnS.
  • B and Ba or Y as a grain growth inhibitor to increase the Goss grain fraction, it is possible to obtain an excellent electrical steel sheet.
  • the grain-oriented electrical steel sheet according to an embodiment of the present invention is increased in%, Si: 1.0 to 7.0%, Mn: 0.01% to 0.5%, B: 0.001 to 0.1%, and Ba and Y alone or in total, 0.005 Increase% to 0.5 increase%, the balance is Fe and Contains other unavoidable impurities. ⁇
  • Barium (Ba) and yttrium (Y) act as a grain growth inhibitor in one embodiment of the present invention to suppress the growth of grains in a different orientation than goth grains during secondary recrystallization annealing to improve the magnetic properties of the electrical steel sheet.
  • Ba and Y may each be added alone or in combination.
  • Ba and Y may each comprise 0.005% by weight to 5% by weight alone or in total. That is, when Ba or Y are added alone, the content of Ba or Y may be increased by 0.005% by weight to 0.5% by weight, respectively, and when Ba and Y are added simultaneously, the sum of the content of Ba and Y is ( That is, the total amount may be 0.005% by weight to 0.5% by weight 3 ⁇ 4. If Ba, or Y or its total amount is too small, it is difficult to exert a layered suppression force, and if Ba or Y or its total amount is too large, the brittleness of the steel sheet may increase and cracks may occur during rolling.
  • B Boron
  • boron is segregated at the grain boundaries, so enhancing the grain boundary binding force and serves to reduce the rolling when a crack to "play, rolling count.
  • BN is excellent in high temperature stability and can act as an auxiliary inhibitor that suppresses grain growth together with Ba and Y described above.
  • the content of B may be 0.001 to 0.1 wt%. If too little B is included, it may be insufficient to mitigate grain boundary brittleness by Ba and Y. If too much B is included, the grain boundary segregation of Ba and Y may be suppressed, and a large number of inclusions may be formed during the high temperature annealing process, thereby degrading the magnetic properties.
  • B can satisfy following formula 1 in relationship with Ba and Y.
  • Equation 1 When the value of Equation 1 is less than 0.5, the grain boundary segregation of Ba and Y may be suppressed, and a large number of inclusions may be formed in the high temperature annealing process, thereby degrading the magnetic properties. If the value of Equation 1 is greater than 3, it may be insufficient to mitigate grain boundary brittleness by Ba and Y. Silicon (Si) lowers the iron loss by increasing the resistivity of the material. Iron loss characteristics specific resistance is reduced if the Si content is less than 1.0% by weight in the slab and the electrical steel sheet is: may be reduced. On the contrary, if the Si content in the grain-oriented electrical steel sheet exceeds 7% by weight, the Si content in the grain-oriented electrical steel sheet may be 7% by weight or less since it is difficult to process the transformer.
  • Si Silicon
  • Carbon (C) is an austenite stabilizing element, and is added in more than 0.001% by weight of the slab to refine the coarse columnar structure generated during the playing process and to suppress the central slab segregation of S.
  • it is possible to promote work hardening of the steel sheet during cold rolling to promote the secondary recrystallization nucleation in the ⁇ 110 ⁇ ⁇ 001> orientation in the steel sheet.
  • edge-cracking may occur during hot rolling.
  • the C content in the final electrical steel sheet may be 0.005% by weight or less. More specifically, it may be 0.003% by weight or less.
  • the precipitates such as A1N, MnS, etc. are not used as grain growth inhibitors, the elements used in general oriented electrical steel sheets such as aluminum nitrogen (N) sulfur (S) are managed in an impurity range. -. That is, when inevitably further includes Al, N, S and the like ⁇ A1 0.005% by weight Aha, S may be more than 0.0055% by weight or less and 0.0055% by weight or less.
  • A1N since A1N may not be used as a grain growth inhibitor, aluminum (A1) content may be actively suppressed . All. Therefore, in one embodiment of the present invention A1 is not added or can be controlled to 0.005% by weight or less in the grain-oriented electrical steel sheet. In addition, in the slab, since A1 may be removed during the manufacturing process, A1 may be included in an amount of 0.01 wt% or less.
  • N Nitrogen (N) forms precipitates such as A1N, (Al, Mn) N, (Ai.Si, Mn) N, Si 3 N 4 , BN and so on, in one embodiment of the present invention, N is not added or 0.0055% by weight It can be controlled as follows. More specifically, it may be 0.0030% by weight or less. In one embodiment of the present invention, the immersion process can be omitted, so that the
  • the N content and the N content in the final electrical steel sheet may be substantially the same.
  • S is an element with high solid solution temperature and high segregation during hot rolling. In one embodiment of the invention is not added, or can be controlled to 0.0055% by weight or less. More specifically, the content may be 0.0035 wt% or less.
  • Mn manganese
  • the use of Mi S as a grain growth inhibitor manganese (Mn) may not be added.
  • Mn has an effect of improving magnetism as a resistivity element, it may be further included as an optional component in slabs and electrical steel sheets.
  • the content of Mn may be 0.01 increase 3 ⁇ 4> or more.
  • the amount exceeds 0.5% by weight magnetic transformation may occur due to phase transformation after the second recrystallization.
  • the balance is added in place of iron (Fe).
  • components such as Ti, Mg, and Ca react with oxygen in the steel to form oxides, which may interfere with the movement of the final product as a substance and cause magnetic deterioration. It is necessary. Therefore, if they are inevitably contained, it can be managed to 0.005% by weight or less for each component.
  • the average grain diameter of grains having a grain diameter of 2 mm or more is 10 mm 3 or more. If the average grain size of the crystal grains having a grain size of 2 GPa or more is less than 10 ⁇ m, the grains may not grow sufficiently and the magnetism may be degraded. In one embodiment of the present invention, the grain size of the grain is the diameter of the grain equivalent of the circle . Means length.
  • the grain-oriented electrical steel sheet according to an embodiment of the present invention has excellent magnetic properties by stably forming a goth crystal grain.
  • the grain-oriented electrical steel sheet according to an embodiment of the present invention may have a magnetic flux density of 3 ⁇ 4 measured at a magnetic field of 800 A / m, may be 1.88T or more.
  • Method for producing a grain-oriented electrical steel sheet according to an embodiment of the present invention by weight of Si: 1.0 to 7.0%, B: 0.001 to 0.1% and Ba and Y alone or in a total amount of 0.15% by weight to 0.5% by weight Heating the slab comprising% and the balance comprising Fe and other unavoidable impurities; Hot rolling the slab to produce a hot rolled plate; Cold rolled hot rolled sheet Manufacturing; Primary recrystallization annealing of the cold rolled sheet; And; And performing a second recrystallization annealing of the cold rolled plate on which the first recrystallization annealing is completed.
  • the slab is heated.
  • composition of the slab has been described in detail with respect to the composition of the electrical steel sheet, redundant description thereof will be omitted.
  • the heating temperature of the slab is not limited, but when the slab is heated to a temperature of 1280 ° C or less to prevent the growth of the slab columnar structure coarse to prevent the cracking of the plate in the hot rolling process.
  • the heating temperature of the slab can be from 10 WTC to 1280 ° C.
  • the present invention does not use A1N and MnS as a grain growth inhibitor, so it is not necessary to heat the slab with silver or more than 1300 ° C.
  • the slab is hot rolled to produce a hot rolled plate.
  • the hot rolling temperature is not limited, and in one embodiment, the hot rolling may be finished at 95 CTC or less. After cooling by water can be wound up to 600 ° C.
  • the hot rolled sheet may be annealed as necessary.
  • it in order to make the hot-rolled structure uniform, it may be heated to a temperature of 9 (xrc or more, cracked and cooled).
  • Cold rolling is a cold rolled sheet with a thickness of 0.1mm to 0.5mm by using a reverse mill or a tandem mill and a plurality of cold rolling methods including one time cold rolling, multiple cold rolling, or intermediate annealing. Can be prepared.
  • the warm rolling which keeps the temperature of a steel plate more than 100t during cold rolling can be performed.
  • the final rolling rate through cold rolling may be more than 80%.
  • the cold rolled cold rolled sheet is subjected to primary recrystallization annealing.
  • Primary recrystallization In the annealing stage, primary recrystallization occurs, in which nuclei of goth grains are formed.
  • the cold rolled plate In the first recrystallization annealing step, the cold rolled plate may be decarburized. For decarburization
  • the atmosphere may be a mixed gas atmosphere of hydrogen and nitrogen.
  • the carbon content in the cold rolled sheet may be 0.005 weight 3 ⁇ 4 or less.
  • the nitriding process can be omitted.
  • the cold-rolled sheet on which the first recrystallization annealing is completed is subjected to the second recrystallization annealing.
  • the secondary recrystallization annealing can be performed.
  • the annealing separator is not particularly limited, and an annealing separator containing MgO as a main component may be used.
  • Secondary recrystallization annealing includes a temperature raising step and a cracking step.
  • the temperature raising step is a step of raising the temperature of the cold rolled sheet, the primary recrystallization annealing is completed to the temperature of the cracking step.
  • the temperature of the cracking step can be 90 CTC to 1250 ° C. If it is less than 900 ° C goth grains may not be grown enough to decrease the magnetism, and when it exceeds 1250 ° C grains may grow coarse to deteriorate the characteristics of the electrical steel sheet.
  • the temperature raising step may be performed in a mixed gas atmosphere of hydrogen and nitrogen, and the cracking step may be performed in a hydrogen atmosphere.
  • the purified annealing process may be omitted after the completion of the secondary recrystallization annealing.
  • a high temperature annealed annealing is required to remove precipitates such as A1N and MnS, but the method for manufacturing a grain-oriented electrical steel sheet according to an embodiment of the present invention May not require a anneal process.
  • the alloy component of the grain-oriented electrical steel sheet means a base steel sheet except for a coating layer such as an insulating film.
  • the slab was heated at 1150 ° C for 90 minutes and hot rolled to prepare a 2.6 mm thick hot rolled plate.
  • the hot rolled sheet was heated to a temperature of 1050 ° C or more and then maintained at 910 ° C for 90 seconds, water cooled and then pickled. It was then cold rolled to a 0.30ram thickness through a total of seven passes using a Reverse mill. The rolling reduction per pass was applied equally to the test conditions.
  • the cold rolled steel sheet was heated in a furnace, and then heated in a mixed gas atmosphere of hydrogen: 50% by volume and nitrogen: 50% by volume at 120 ° C for 120 seconds at an annealing temperature of 850 ° C. Recrystallization annealing was performed.
  • Secondary recrystallization annealing was raised to 120 CTC in a mixed gas atmosphere of nitrogen: 25% by volume and hydrogen: 75% by volume, and after reaching 1200 ° C., it was annealed after holding for 20 hours in a hydrogen: 100% by volume gas atmosphere.
  • the magnetic flux density was measured under the condition of 800A / m of magnetic field strength using the single sheet measurement method.
  • Example 2 the photograph of the cold rolled steel sheet during the invention material manufacturing process of the sample number 2 and the photograph of the cold rolled steel sheet during the comparative material manufacturing process of the sample number 1 are shown. In the case of the comparative material, it can be seen that the rolling crack is clearly shown.
  • Example 2
  • the slabs were heated at 1150 ° C. for 90 minutes and hot rolled to produce 2.6 mm thick hot rolled 3 ⁇ 4.
  • the hot rolled sheet was heated to a temperature of 1050 ° C or more and then maintained at 910 ° C for 90 seconds, water cooled and then pickled. It was then cold rolled to a 0.30 mm thickness through a total of seven passes using a Reverse mill. The rolling reduction per pass was applied equally to the test conditions.
  • the cold rolled steel sheet was first heated with decarburization in a mixed gas atmosphere of hydrogen: 50% by volume and nitrogen: 50% by volume at 120 TC at an annealing temperature of 85 TC. Recrystallization annealing was performed.
  • MgO was applied, and then wound up in a coil and subjected to secondary recrystallization annealing.
  • the secondary recrystallization annealing was raised to 1200 ° C. in a mixed gas atmosphere of nitrogen: 25% by volume and hydrogen: 75% by volume, and after reaching 1200 ° C., it was quenched after holding for 20 hours in a hydrogen: 100% by volume gas atmosphere.
  • the magnetic flux density was measured under the condition of 800 A / m magnetic field strength using the s ingl e sheet measurement method.
  • the grain size was immersed in hydrochloric acid heated to 60 ° C for 5 minutes to remove the surface coating layer The average value was calculated according to the area.
  • the average grain diameter of the crystal grains having a grain size of 2 ⁇ or more was found to be 10 ⁇ or more, and the magnetic properties were excellent.

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  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
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Abstract

Une feuille d'acier électrique à grains orientés selon un mode de réalisation de la présente invention comprend, en pourcentage en poids : de 1,0 à 7,0% de Si; de 0,001 à 0,1% de B; et de 0,005 à 0,5% de Ba et de Y, soit seuls soit en combinaison les uns avec les autres, le reste étant du Fe et d'autres impuretés inévitables.
PCT/KR2017/011849 2016-10-26 2017-10-25 Tôle en acier électrique à grains orientés et procédé de fabrication de celle-ci WO2018080167A1 (fr)

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EP17866141.9A EP3533896B1 (fr) 2016-10-26 2017-10-25 Tôle en acier électrique à grains orientés et procédé de fabrication de celle-ci
CN201780066820.2A CN109906284B (zh) 2016-10-26 2017-10-25 取向电工钢板及其制造方法
US16/345,488 US20190309387A1 (en) 2016-10-26 2017-10-25 Grain-oriented electrical steel sheet and method for manufacturing the same
JP2019522885A JP6808830B2 (ja) 2016-10-26 2017-10-25 方向性電磁鋼板およびその製造方法

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KR102271299B1 (ko) * 2019-12-19 2021-06-29 주식회사 포스코 이방향성 전기강판 및 그의 제조방법

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CN109906284A (zh) 2019-06-18
US20190309387A1 (en) 2019-10-10
EP3533896A1 (fr) 2019-09-04
EP3533896A4 (fr) 2019-10-16
JP6808830B2 (ja) 2021-01-06
EP3533896B1 (fr) 2021-03-31
JP2020509153A (ja) 2020-03-26
CN109906284B (zh) 2021-10-15
KR20180045504A (ko) 2018-05-04

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