WO2021084785A1 - 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 PDF

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Publication number
WO2021084785A1
WO2021084785A1 PCT/JP2020/019159 JP2020019159W WO2021084785A1 WO 2021084785 A1 WO2021084785 A1 WO 2021084785A1 JP 2020019159 W JP2020019159 W JP 2020019159W WO 2021084785 A1 WO2021084785 A1 WO 2021084785A1
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Prior art keywords
steel sheet
inclusions
strength
less
electrical steel
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English (en)
French (fr)
Japanese (ja)
Inventor
尾田　善彦
善彰 財前
智幸 大久保
田中　孝明
幸乃 宮本
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JFE Steel Corp
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JFE Steel Corp
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Priority to JP2020546191A priority Critical patent/JP7056745B2/ja
Priority to MX2022003841A priority patent/MX2022003841A/es
Priority to KR1020227010998A priority patent/KR102740117B1/ko
Priority to US17/755,318 priority patent/US12381024B2/en
Priority to EP20881606.6A priority patent/EP4053302A4/en
Priority to CN202080072963.6A priority patent/CN114555848A/zh
Publication of WO2021084785A1 publication Critical patent/WO2021084785A1/ja
Anticipated expiration legal-status Critical
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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
    • 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
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/04—Removing impurities by adding a treating agent
    • C21C7/06—Deoxidising, e.g. killing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/10—Handling in a vacuum
    • 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
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    • 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
    • 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
    • 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
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    • C—CHEMISTRY; METALLURGY
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    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the working steps
    • C21D8/1222—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the working steps
    • C21D8/1233—Cold rolling
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    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
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    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the heat treatment
    • C21D8/1272—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1277—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular surface treatment
    • C21D8/1283—Application of a separating or insulating coating
    • 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
    • C22C38/002—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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C—CHEMISTRY; METALLURGY
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    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • C—CHEMISTRY; METALLURGY
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
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    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
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Definitions

  • the present invention relates to a non-oriented electrical steel sheet having excellent high-frequency iron loss characteristics and high fatigue strength with controlled composition and steel sheet structure, and a method for manufacturing the same.
  • IPM motors Embedded magnet type motors
  • a permanent magnet is embedded in a slot portion formed in an electromagnetic steel plate.
  • the width of the bridge portion may be widened, but if the width of the bridge portion is widened, the leakage flux of the permanent magnet increases and the motor efficiency decreases. Problem arises. Therefore, the width of the bridge portion is designed to be as narrow as possible within the range where the rotor strength is established.
  • the electrical steel sheet used as the material of the rotor has a strength that can withstand centrifugal force at high speed rotation, that is, an excellent tensile strength, and a strength that can cope with repeated loads, that is, excellent, even if the width of the bridge portion is narrow. Fatigue strength is required.
  • the tooth portion is excited to 1.50 T or more by the magnetic flux of the magnet, so that the magnetic flux density B 50 is required to be 1.50 T or more. Further, since iron loss due to harmonics occurs on the surface of the rotor, the electromagnetic steel sheet is required to have low high frequency iron loss.
  • Patent Document 1 discloses a high-strength electrical steel sheet having Si: 0.2 to 3.5%, Al: 2.50% or less, and Nb: 0.05 to 8.0%.
  • Patent Document 2 contains a component satisfying Si: 2.0% or more and 3.5% or less, Al: 0.02% or more and 3.0% or less, N: 0.005% or more and 0.020% or less, and has a depth of 10 ⁇ m from the surface of the product plate. High-strength electrical steel sheets having an average crystal grain size of 10 ⁇ m or less are disclosed.
  • the present invention also has a problem that iron loss increases.
  • the present invention has been made in view of these circumstances, and is suitable for use in rotors of IPM motors, has excellent magnetic flux density B 50 and high-frequency iron loss characteristics, has high tensile strength and fatigue strength, and has variations in tensile strength.
  • the purpose is to propose a small number of non-oriented electrical steel sheets together with the manufacturing method.
  • the present inventors have found that the amount of Zn and Mo added is appropriately controlled and the inclusions in the steel are reduced in the non-oriented electrical steel sheet containing a non-recrystallized structure. Therefore, it was found that not only the magnetic flux density B 50 and the high-frequency iron loss characteristic are excellent, but also the fatigue strength and the tensile strength are high, and the variation in the tensile strength can be reduced.
  • the present invention has been made based on such findings, and the present invention has the following configurations.
  • 1. By mass%, C: 0 to 0.0100%, P: 0 to 0.100%, Si: 2.00 to 5.00%, Mn: 0 to 5.00%, Al: 0 to 3.00%, S: 0 to 0.0100%, N: 0 to 0.0050% or less, Zn: 0.0005 to 0.0030%, Mo: 0.001 to 0.100%, Cu: 0 to 0.2%, Nb: 0 to 0.010%, and O: 0 to 0.0050%, and the balance is Fe and unavoidable impurities.
  • Non-directional having a composition of steel plate components, a ratio of unrecrystallized structures of 5 to 70%, and a structure in which the number of inclusions having a diameter of 5 ⁇ m or more is 5 pieces / mm 2 or less.
  • Sex electromagnetic steel plate Sex electromagnetic steel plate.
  • the non-oriented electrical steel sheet according to 1 or 2 further containing Ca: 0.0010 to 0.0050% by mass as the steel sheet component.
  • non-oriented electrical steel sheet according to any one of 1 to 3 above, further comprising Sn: 0.001 to 0.100% by mass and / or Sb: 0.0010 to 0.1000% by mass as the steel sheet component.
  • a rotor material for a high-speed motor which not only has excellent magnetic flux density B 50 and high-frequency iron loss characteristics, but also has high fatigue strength and high variation in tensile strength.
  • Some non-oriented electrical steel sheets have an unrecrystallized structure.
  • the unrecrystallized structure of the non-oriented electrical steel sheet is a structure that has not been recrystallized. Recrystallization means that crystal grains having a remarkably low dislocation density are generated and grown by holding the material at a high temperature, and recrystallized grains and unrecrystallized grains can be distinguished by observation with an optical microscope.
  • the ratio of the unrecrystallized structure in the steel is large, the fatigue strength tends to increase, but the iron loss tends to worsen.
  • the inventors first investigated the effect of the unrecrystallized structure on the fatigue strength, in terms of mass%, C: 0.0015%, Si: 3.7%, Al: 0.5%, Mn: 0.7%, P. Steel with: 0.01%, S: 0.001%, N: 0.0016%, Zn: 0.0012%, O: 0.0015% (hereinafter,% of the steel component means mass%) is melted in the laboratory to form a plate. Hot rolling was performed to a thickness of 1.6 mm to prepare a hot rolled plate.
  • This hot-rolled plate is annealed with a hot-rolled plate at 950 ° C for 30 s in a 100 vol% N 2 atmosphere, pickled, then cold-rolled to a plate thickness of 0.25 mm, and 550 in a 20 vol% H 2 -80 vol% N 2 atmosphere. Finish annealing was performed at about 800 ° C. for 10 s to obtain a finish annealing plate.
  • a fatigue test piece having a width of 5 mm and a length of 150 mm at a parallel portion was cut out from the finished annealed plate in the rolling direction and the direction perpendicular to the rolling direction.
  • the parallel part was mirror-finished and further polished with No. 800 emery paper in the longitudinal direction.
  • the mirror finish refers to a surface polished with a diamond grindstone of No. 500 count.
  • FIG. 1 shows the effect of the unrecrystallized structure on the fatigue strength of the steel sheet.
  • the fatigue strength in the present invention shows the average value in the rolling direction and the rolling perpendicular direction.
  • polished steel plate rolling direction cross-section after etching by nital, performed by an optical microscope, and five places sampled randomly per steel plate 1 m 2, the non-recrystallization of the measurement range per 1 cm 2 1 place The grain ratio was calculated.
  • the ratio of unrecrystallized grains in the present invention is the ratio in the entire structure, that is, the area ratio, and such a ratio is the result of using this measurement method.
  • the fatigue strength of the steel sheet is increased by setting the ratio of the unrecrystallized structure to 5% or more, preferably 15% or more. This is because the fatigue strength and the tensile strength improve as the ratio of the unrecrystallized structure increases.
  • the ratio of the unrecrystallized structure in the steel structure exceeds 70%, the iron loss becomes remarkably high. Therefore, the ratio of the unrecrystallized structure is 70% or less, preferably 60% or less.
  • the inclusions inhibit the growth of crystal grains of the non-directional electromagnetic steel plate, and include, for example, sulfides such as copper sulfide (CuS) and manganese sulfide (MnS), silica (SiO 2 ), and alumina (SiO 2).
  • CuS copper sulfide
  • MnS manganese sulfide
  • SiO 2 silica
  • SiO 2 alumina
  • Oxides such as Al 2 O 3 ) and nitrides such as aluminum nitride (AlN) and titanium nitride (TiN) are known.
  • the inclusion means a non-metal precipitate such as these oxides, sulfides, and nitrides.
  • FIG. 2 shows the effect of the number of inclusions on the fatigue strength.
  • the evaluation of the size and the number of inclusions was as follows. As the size of the inclusions, the diameter equivalent to the circle of the inclusions was determined. The number of inclusions is randomly sampled at 20 points per 1 m 2 of the steel sheet, and the number of inclusions existing in the observation field of view at one such sampling point: 0.1 mm 2 is counted and multiplied by 10 to obtain the number of inclusions per 1 mm 2. It was.
  • inclusions those having a diameter of 5 ⁇ m or more, which affects fatigue strength, were measured.
  • the number of inclusions in the present invention is the average of the number of inclusions in the whole tissue, and the result of using this measurement method is used for such a number.
  • the oxygen concentration of the material used in the test for obtaining the result shown in FIG. 2 was measured and found to be 10 to 100 ppm. It is generally known that the amount of inclusions in steel is reduced by reducing the amount of oxygen. However, in the above test, the result was that the number of inclusions having a diameter of 5 ⁇ m or more and the amount of oxygen were not necessarily correlated. Therefore, it was found that limiting the amount of oxygen is not sufficient to suppress the variation in fatigue intensity, and it is important to control inclusions.
  • the component of the steel sheet (hereinafter,% related to the component of the steel sheet means mass%) is in the following range.
  • Si 2.00-5.00% Since Si is an element effective for increasing the intrinsic resistance of the steel sheet, the lower limit is set to 2.00%, more preferably 3.50% or more. On the other hand, if it exceeds 5.00%, not only the magnetic flux density decreases as the saturation magnetic flux density decreases, but also the fatigue strength decreases. Therefore, the upper limit is set to 5.00%.
  • Al 3.00% or less Al, like Si, is an effective element for increasing the natural resistance. However, if it exceeds 3.00%, not only the decrease in magnetic flux density due to the decrease in saturation magnetic flux density but also the fatigue strength decreases. Therefore, the upper limit is set to 3.00%. Although the lower limit is not particularly specified, it is preferably 0.30% or more, more preferably 0.50% or more from the viewpoint of iron loss.
  • C 0.0100% or less C causes an increase in iron loss due to carbide precipitation. Therefore, in order to suppress the increase in iron loss, it is set to 0.0100% or less, preferably 0.0050% or less.
  • the lower limit is not particularly limited and may be 0%.
  • Mn 5.00% or less Mn is an element effective for increasing the intrinsic resistance of steel sheets. However, if it exceeds 5.00%, the magnetic flux density decreases, so the upper limit is set to 5.00%.
  • the lower limit is not specified, but it is preferably 0.10% or more from the viewpoint of reducing iron loss.
  • P 0.100% or less because if it is added in excess of 0.100%, the steel sheet becomes brittle and cold rolling becomes difficult.
  • the lower limit is not particularly limited and may be 0%.
  • N 0.0050% or less because the amount of nitride precipitated increases when the content is high and iron loss increases.
  • the lower limit is not particularly limited and may be 0%.
  • O 0.0050% or less O, if it exceeds 0.0050%, forms an oxide and deteriorates the magnetic characteristics, so the upper limit is set to 0.0050%.
  • the lower limit is not particularly limited and may be 0%.
  • Mo 0.001 to 0.100%
  • the lower limit of Mo is 0.001% in order to stabilize the unrecrystallized structure.
  • the upper limit is set to 0.100%, preferably 0.010%.
  • the upper limit is set to 0.2%, more preferably 0.1%.
  • the lower limit is not particularly limited and may be 0%.
  • Nb 0.010% or less
  • Nb is an element that forms precipitates such as NbC and contributes to high strength.
  • the upper limit is 0.010%, preferably 0.005. % Or less.
  • the lower limit is not particularly limited, but it is desirable that it is 0.001% or more in order to increase the strength.
  • Zn 0.0005 to 0.0030%
  • Zn is an element that is not normally mixed in electrical steel sheets because it has a high vapor pressure and easily volatilizes. However, if the temperature of the molten steel is adjusted by adding scrap after deoxidation, it may be mixed in the steel. In general electrical steel sheets, since a sufficiently recrystallized material is shipped as a product, the strength characteristics are stable even if Zn is mixed. However, in a material such as the present invention in which an unrecrystallized structure remains, the strength may vary.
  • Finish annealing was performed at 680 ° C for 10 s in an 80 vol% N 2 atmosphere. Twenty JIS No. 5 test pieces were sampled from the steel sheet after such finish annealing and a tensile test was performed. From the results of this tensile test, the standard deviation ⁇ was calculated and the relationship between the Zn amount and ⁇ was plotted. When the Zn amount exceeded 0.0030%, ⁇ became 20 MPa or more, and the variation became large. It is considered that this is because the recrystallization behavior becomes unstable due to the inclusion of Zn, and the recrystallization rate varies among 20 lines.
  • the upper limit of Zn is set to 0.0030%.
  • the standard deviation ⁇ can be suppressed to 20 MPa or less in the electrical steel sheet in which the unrecrystallized structure remains. It is preferable that the lower limit is small, but stabilizing it below 0.0005% increases the cost, so the lower limit is set to 0.0005%.
  • the rest of the steel sheet component of the present invention is Fe and unavoidable impurities.
  • the following components can be appropriately contained in addition to the steel sheet components.
  • Cr 0.010-5.000% Cr, like Si, is an effective element for increasing the intrinsic resistance. Therefore, when adding, the lower limit is set to 0.010%. Desirably, the lower limit is 0.100%. On the other hand, if it exceeds 5.000%, the magnetic flux density decreases as the saturation magnetic flux density decreases, so the upper limit is set to 5.000%.
  • Ca 0.0010-0.0050% Ca is an element that fixes S as CaS and contributes to the reduction of iron loss. Therefore, when adding, the lower limit is set to 0.0010%. On the other hand, if it exceeds 0.0050%, the effect will be saturated and the cost will increase unnecessarily, so the upper limit is set to 0.0050%.
  • Sn 0.001 to 0.100% and / or Sb: 0.0010 to 0.1000%
  • Sn is an element that is effective in improving the magnetic flux density by improving the texture. Therefore, when adding, the lower limit is set to 0.001%. On the other hand, if it exceeds 0.100%, the material becomes embrittled, so the upper limit is set to 0.100%.
  • Sb is also an element effective in improving the magnetic flux density by improving the texture. Therefore, when adding, the lower limit is set to 0.0010%. On the other hand, if it exceeds 0.1000%, the material becomes embrittled, so the upper limit is set to 0.1000%.
  • a high-speed driven HEV / EV motor requires a tensile stress of 700 MPa or more, but by satisfying the present invention, it is possible to stably obtain a tensile strength of 700 MPa or more.
  • the iron loss at high frequency that is, W 5 / 3K is 120.0 W / Kg or less. It is possible to have excellent characteristics.
  • the iron loss tends to increase as the current increases, and in order to avoid this, a high magnetic flux density is required.
  • the magnetic flux density becomes B 50. It is possible to provide a high magnetic flux density of 1.50 T or more.
  • the method for manufacturing the steel sheet of the present invention will be described.
  • the composition component of the steel sheet within the scope of the present invention and further limit the manufacturing method as follows.
  • the molten steel blown in a converter is sequentially degassed (secondary refining), cast, and hot-rolled.
  • Degassing vacuum degassing
  • secondary refining is performed using RH (Ruhrstahl-Heraeus) or DH (Dortmund-Horde).
  • a deoxidizing element such as Al is added, and then the mixture is stirred for 10 minutes or more (also referred to as RH reflux time or DH reflux time in the present invention). Further, in order to prevent Zn from being mixed from scrap or ferroalloy, it is desirable to stir for 5 minutes or more after adding scrap or ferroalloy to evaporate Zn.
  • the finish annealing temperature and take-up temperature during hot rolling are not specified. Further, hot-rolled sheet annealing after hot rolling may or may not be performed. Next, a predetermined sheet thickness is obtained by one cold rolling or two or more cold rollings sandwiching intermediate annealing, and further finish annealing is performed to obtain a non-oriented electrical steel sheet according to the present invention.
  • the finish annealing after cold rolling is preferably 620 ° C or higher and 720 ° C or lower in order to appropriately leave unrecrystallized grains in the steel sheet structure, which is a feature of the present invention.
  • the molten steel blown in the converter is subjected to vacuum degassing treatment, a deoxidizing agent is added during degassing, and the steel is stirred for the time shown in Tables 2 and 4 (RH reflux time), and the steels shown in Tables 1 and 3 are used.
  • slab heating was performed under the conditions of 1140 ° C. ⁇ 1 h, and hot rolling was performed. The finishing temperature for hot rolling was 800 ° C, and the winding temperature was 610 ° C. After winding, hot-rolled plate was annealed under 100vol% N 2 atmosphere conditions.
  • finish annealing was performed at a 20 vol% H 2 -80 vol% N 2 atmosphere and the finish annealing temperature shown in Tables 2 and 4 to obtain a finish annealing plate.
  • the magnetic measurement was performed by cutting out an Epstein sample from the rolling direction and the rolling perpendicular direction of the finished annealed plate and performing the Epstein measurement.
  • the fatigue test was carried out at a tensile-tensile stress ratio of 0.1 and a frequency of 20 Hz, and the stress amplitude that did not cause fracture even after 10 7 repetitions was obtained, and this value was taken as the fatigue strength.
  • the fatigue test piece is cut out from the rolling direction and the direction perpendicular to the rolling of the finished annealed sheet with the width of the parallel part: 5 mm and the length: 150 mm, the parallel part is mirror-finished, and the emery of No. 800 in the longitudinal direction. It was made by polishing with paper.
  • the tensile test was performed by processing the JIS No. 5 test piece so that the rolling direction was the longitudinal direction, in accordance with JIS Z 2241.
  • ⁇ variation in tensile strength
  • 20 JIS No. 5 test pieces were sampled and subjected to a tensile test to obtain the standard deviation ⁇ .
  • the magnetic flux density B 50 at a magnetic field strength of 5000 A / m was measured.
  • the iron loss W 5 / 3K when excited at a frequency of 3 kHz and a magnetic flux density of 0.5 T was measured.
  • Tables 2 and 4 The above test results are shown in Tables 2 and 4, respectively.
  • all the steel sheets satisfying the conditions of the present invention have a fatigue strength of 550 MPa or more, a tensile strength of 700 MPa or more, a standard deviation ⁇ of the tensile strength within 20 MPa, and a magnetic flux density B 50 of 1.5 T or more. Moreover, it can be seen that the iron loss W 5 / 3K has excellent characteristics of 120 W / kg or less.

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KR20250105768A (ko) 2023-12-29 2025-07-09 현대제철 주식회사 무방향성 전기강판 및 그 제조 방법
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