WO2022107757A1 - Matériau de barre en acier inoxydable et composant électromagnétique - Google Patents

Matériau de barre en acier inoxydable et composant électromagnétique Download PDF

Info

Publication number
WO2022107757A1
WO2022107757A1 PCT/JP2021/042062 JP2021042062W WO2022107757A1 WO 2022107757 A1 WO2022107757 A1 WO 2022107757A1 JP 2021042062 W JP2021042062 W JP 2021042062W WO 2022107757 A1 WO2022107757 A1 WO 2022107757A1
Authority
WO
WIPO (PCT)
Prior art keywords
less
content
amount
steel
rod
Prior art date
Application number
PCT/JP2021/042062
Other languages
English (en)
Japanese (ja)
Inventor
祥太 山先
光司 高野
幸寛 西田
規介 田中
雅之 東城
Original Assignee
日鉄ステンレス株式会社
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by 日鉄ステンレス株式会社 filed Critical 日鉄ステンレス株式会社
Priority to EP21894631.7A priority Critical patent/EP4249612A1/fr
Priority to MX2023005833A priority patent/MX2023005833A/es
Priority to JP2022563763A priority patent/JPWO2022107757A1/ja
Priority to KR1020237016897A priority patent/KR20230088905A/ko
Priority to US18/037,694 priority patent/US20240011137A1/en
Priority to CN202180077648.7A priority patent/CN116438321A/zh
Publication of WO2022107757A1 publication Critical patent/WO2022107757A1/fr

Links

Classifications

    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/007—Heat treatment of ferrous alloys containing Co
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
    • C21D8/1222—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
    • C21D8/1261—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations
    • 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
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
    • 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
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/0075—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rods of limited length
    • 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

Definitions

  • the present invention relates to electromagnetic stainless steel, particularly stainless steel rod-shaped steel having excellent high-speed cold forging property, machinability, and soft magnetic properties, and electromagnetic parts using the same.
  • Japanese Unexamined Patent Publication No. 6-49606 Japanese Unexamined Patent Publication No. 6-49605 Japanese Unexamined Patent Publication No. 3-44448
  • the present invention has been made to solve the above problems, and the gist of the present invention is the following stainless steel rod-shaped steel materials and electromagnetic parts.
  • the chemical composition is mass%. C: 0.001 to 0.030%, Si: 0.01 to 4.00%, Mn: 0.01 to 2.00%, Ni: 0.01 to 4.00%, Cr: 8.0 to Contains 35.0%, Mo: 0.01 to 5.00%, Cu: 0.01 to 2.00%, N: 0.001 to 0.030%, Al: 7,000% or less. moreover, Ti: 0 to 2.00%, Nb: 0 to 2.00%, B: 0 to 0.1000%, and so on.
  • a stainless rod-shaped steel material having an average particle size of a nitride of 10 ⁇ m or less and a solid solution N content in steel of 0.020% by mass or less.
  • the chemical composition is mass%.
  • C 0.001 to 0.030%, Si: 0.01 to 4.00%, Mn: 0.01 to 2.00%, Ni: 0.01 to 4.00%, Cr: 8.0 to Contains 35.0%, Mo: 0.01 to 5.00%, Cu: 0.01 to 2.00%, N: 0.001 to 0.030%, Al: 7,000% or less.
  • Ti 0 to 2.00%, Nb: 0 to 2.00%, B: 0 to 0.1000%, and so on. It contains one or more selected from Ti: 0.001% or more, Nb: 0.001% or more, and B: 0.0001% or more.
  • Group 3 Pb 0.0001 to 0.30%
  • Se 0.0001 to 0.80%
  • Te 0.0001 to 0.30%
  • Bi 0.0001 to 0.50%
  • S 0
  • the present inventors conducted various studies in order to obtain stainless steel rod-shaped steel materials and electromagnetic parts having excellent high-speed cold forging properties, machinability, and soft magnetic properties. As a result, the following findings (a) to (c) were obtained.
  • a combination of ferritic stainless steel whose composition is adjusted with one or more of B, Ti, and Nb and a hot rolling process (finish rolling inlet temperature, finish rolling roll diameter, heat treatment temperature) to obtain the average grain size of nitrides.
  • the amount of solid melt N and the amount of solid melt B in steel can be reduced.
  • the high-speed cold forging property has a compression rate of 70%, the unbreakable strain rate is 0.1 / s or more, the machinability has a cutting resistance of 50 mm or more, and the soft magnetic property is maintained.
  • the present invention was made based on the above findings. In addition, a preferred embodiment of the present invention will be described in detail. In the following description, a preferred embodiment of the present invention will be described as the present invention. Hereinafter, each requirement of the present invention will be described in detail.
  • the "bar-shaped steel material” includes “bar steel”, “wire rod”, “steel wire”, “deformed wire”, “deformed bar steel” and the like.
  • the average particle size of the nitride is controlled. Specifically, the average particle size of the nitride is 10 ⁇ m or less. This is because when the average particle size of the nitride exceeds 10 ⁇ m, the high-speed cold forging property is deteriorated by the coarse nitride.
  • the average particle size of the nitride is more preferably 7 ⁇ m or less, and even more preferably 5 ⁇ m or less.
  • the average particle size of the nitride is preferably 0.01 ⁇ m or more.
  • the nitride includes carbonitride.
  • the average particle diameter of the nitride is the surface layer portion, the central portion, and the 1/4 depth position portion existing between the surface layer portion and the central portion in the L cross section of the rod-shaped steel material (cross section including the center line of the rod-shaped steel material).
  • the amount of solid solution N in steel is 0.020% by mass or less, or the amount of solid solution B is 0.015% by mass or less.
  • the soft magnetic properties and high-speed cold forging property are improved.
  • an invention having a suitable component composition described later and an average particle size of the above-mentioned nitride and defining the amount of solid-dissolved N in steel to be 0.020% by mass or less will be referred to as "Invention 1".
  • an invention having a suitable component composition of the present invention and the average particle size of the above-mentioned nitride and defining the amount of solid solution B in steel to be 0.015% by mass or less is referred to as "the present invention 2".
  • Amount of solid solution N in steel In the rod-shaped steel material according to the present invention 1, the amount of solid solution N in steel is controlled. Specifically, the amount of solid solution N in the steel is 0.020% by mass or less. This is because when the amount of solid solution N in the steel exceeds 0.020% by mass, the soft magnetic properties and high-speed cold forging property are deteriorated due to the lattice strain due to the solid solution N.
  • the amount of solid solution N in the steel is more preferably 0.015% by mass or less, and further preferably 0.01% by mass or less.
  • the amount of solid solution N in the steel is preferably 0.00001% by mass or more. Since the crystal structure of the steel of the present invention is ferritic steel, the amount of solid solution N in the steel corresponds to the amount of solid solution N in the ferrite phase.
  • the problem of the present invention can be solved by controlling the amount of solid solution B in the steel.
  • the amount of solid solution B in the steel is 0.015% by mass or less. This is because when the amount of the solid solution B in the steel exceeds 0.015% by mass, the soft magnetic properties and the high-speed cold forging property are deteriorated due to the lattice strain due to the solid solution B.
  • the amount of solid solution B in the steel is more preferably 0.010% by mass or less, and further preferably 0.005% by mass or less.
  • the amount of solid solution B in the steel is preferably 0.00001% by mass or more. Since the crystal structure of the steel of the present invention is ferritic steel, the amount of solid solution B in the steel corresponds to the amount of solid solution B in the ferrite phase.
  • C 0.001 to 0.030% C enhances the strength and machinability of the steel material. Therefore, the C content is set to 0.001% or more. However, if C is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability deteriorate. Therefore, the C content is set to 0.030% or less.
  • the C content is preferably 0.020% or less, more preferably 0.015% or less.
  • Si 0.01-4.00% Si is contained as a deoxidizing element to improve soft magnetic properties and machinability. Therefore, the Si content is preferably 0.01% or more, preferably 0.10% or more. However, if Si is excessively contained, high-speed cold forging property, soft magnetic property, and machinability are deteriorated. Therefore, the Si content is set to 4.00% or less. The Si content is preferably 3.00% or less, more preferably 1.50% or less.
  • Mn 0.01-2.00% Mn improves the strength, soft magnetic properties, and machinability of steel materials. Therefore, the Mn content is preferably 0.01% or more, preferably 0.05% or more. However, if Mn is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. In addition, corrosion resistance may decrease. Therefore, the Mn content is set to 2.00% or less. The Mn content is preferably 1.00% or less, and more preferably 0.50% or less.
  • Ni 0.01-4.00% Ni improves the toughness and soft magnetic properties of steel materials, high-speed cold forging, and machinability. Therefore, the Ni content is preferably 0.01% or more, preferably 0.05% or more. However, if Ni is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. Therefore, the Ni content is set to 4.00% or less. The Ni content is preferably 3.00% or less, more preferably 1.00% or less, and even more preferably 0.50% or less.
  • Cr 8.0 to 35.0% Cr improves corrosion resistance, soft magnetic properties, high-speed cold forging, and machinability. Therefore, the Cr content is set to 8.0% or more. The Cr content is preferably 10.0% or more. However, if Cr is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. The Cr content should be 35.0% or less. The Cr content is preferably 21.0% or less, more preferably 20.0% or less.
  • Mo 0.01-5.00% Mo improves corrosion resistance, soft magnetic properties, high-speed cold forging, and machinability. Therefore, the Mo content is 0.01% or more. However, if Mo is excessively contained, high-speed cold forging property, soft magnetic property, and machinability are deteriorated. Therefore, the Mo content is set to 5.00% or less.
  • the Mo content is preferably 3.00% or less, more preferably 2.00% or less, and even more preferably 1.50% or less.
  • Cu 0.01-2.00%
  • the Cu content is preferably 0.01% or more, preferably 0.05% or more.
  • the Cu content is set to 2.00% or less.
  • the Cu content is preferably 1.00% or less, more preferably 0.80% or less, still more preferably 0.40% or less.
  • N 0.001 to 0.030% N improves the strength and machinability of the steel material. It is also an element that forms a nitride. Therefore, the N content is preferably 0.001% or more, preferably 0.002% or more. However, if N is excessively contained, the soft magnetic properties, machinability, and high-speed cold forging property are deteriorated. In addition, the average particle size of the nitride becomes large, and the amount of solid solution N increases. Therefore, the N content is set to 0.030% or less. The N content is preferably 0.025% or less, more preferably 0.020% or less.
  • Al 7,000% or less
  • Al has the effect of promoting deoxidation and improving the cleanliness level of inclusions.
  • the addition of Al enhances soft magnetic properties, high-speed cold forging, and machinability.
  • the Al content is set to 7,000% or less.
  • the Al content is preferably 3.000% or less, more preferably 0.100% or less, and even more preferably 0.020% or less.
  • the Al content is preferably 0.001% or more.
  • the rod-shaped steel material according to the present invention contains one or more elements selected from Ti: 0.001% or more, Nb: 0.001% or more, and B: 0.0001% or more within the following component range. Incorporate in. These elements are the main elements constituting the nitride and need to be controlled because they are related to the average particle size of the nitride and the amount of solid solution N. Of Ti, Nb, and B, the element not selected above may not be contained or may be contained within the following component range.
  • Ti 0 to 2.00% Ti has the effects of enhancing the strength, soft magnetic properties, high-speed cold forging property, and machinability of steel materials. Further, Ti forms a nitride and is related to the amount of solid solution N. Further, since carbonitride is formed, the formation of Cr carbide is suppressed and the formation of a Cr-deficient layer is suppressed. As a result, it has the effect of preventing intergranular corrosion. Therefore, the Ti content is set to 0.001% or more. However, if Ti is excessively contained, the soft magnetic properties, machinability, and high-speed cold forging property are deteriorated. In addition, the average particle size of the nitride becomes large. Therefore, the Ti content is set to 2.00% or less.
  • the Ti content is preferably 1.00% or less, more preferably 0.50% or less, further preferably 0.50% or less, and even more preferably 0.25% or less. In addition, it is preferably contained in an amount of 0.01% or more in order to exhibit the effect. More preferably, 0.05% or more. It may be 0.10% or more.
  • Nb 0 to 2.00%
  • Nb has the effect of enhancing the strength, soft magnetic properties, high-speed cold forging property, and machinability of the steel material. Further, Nb forms a nitride and is related to the amount of solid solution N. Further, since carbonitride is formed, the formation of Cr carbide is suppressed and the formation of a Cr-deficient layer is suppressed. As a result, it has the effect of preventing intergranular corrosion. Therefore, the Nb content is set to 0.001% or more. However, if Nb is excessively contained, the soft magnetic properties, machinability, and high-speed cold forging property are deteriorated. In addition, the average particle size of the nitride becomes large.
  • the Nb content is set to 2.00% or less.
  • the Nb content is preferably 1.00% or less, more preferably 0.80% or less, and even more preferably 0.60% or less.
  • it is preferably contained in an amount of 0.02% or more in order to exhibit the effect. More preferably, 0.05% or more. It may be 0.10% or more.
  • B 0 to 0.1000%
  • B has the effect of enhancing the soft magnetic properties, high-speed cold forging property, and machinability of the steel material. Further, B forms a boron nitride such as BN, and is related to the amount of solid solution N and the amount of solid solution B. In particular, BN contributes to the improvement of machinability. Therefore, the B content is set to 0.0001% or more. However, if B is excessively contained, the soft magnetic properties, machinability, and high-speed cold forging property are deteriorated. In addition, the average particle size of the nitride becomes large. Therefore, the B content is set to 0.1000% or less. The B content is preferably 0.0200% or less, more preferably 0.0100% or less. Further, in order to exhibit the effect, it is preferably contained in an amount of 0.0005% or more. 0.0010% or more is more preferable. It may be 0.0020% or more.
  • the rod-shaped steel material according to the present invention contains, if necessary, one or more elements selected from Sn, V, W, Ga, Co, Sb and Ta as the elements of the first group. May be good.
  • Sn 0 to 2.50% Sn may be contained as necessary because it has the effects of improving corrosion resistance, soft magnetic properties, high-speed cold forging property, and machinability. However, if Sn is contained in an excessive amount, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. In addition, the toughness decreases due to the grain boundary segregation of Sn. Therefore, the Sn content is set to 2.50% or less.
  • the Sn content is more preferably 1.00% or less, and further preferably 0.20% or less.
  • the Sn content is preferably 0.0001% or more, and more preferably 0.05% or more.
  • V 0-2.0% Since V has an effect of improving soft magnetic properties, high-speed cold forging property, and machinability, it may be contained as necessary. However, if V is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. In addition, the toughness is reduced by the coarse carbonitride. Therefore, the V content is set to 2.0% or less. The V content is preferably 1.0% or less, more preferably 0.5% or less, and even more preferably 0.1% or less. On the other hand, in order to obtain the above effect, the V content is preferably 0.001% or more.
  • W 0 to 3.00% Since W has an effect of improving corrosion resistance, it may be contained if necessary. However, if W is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. In addition, the toughness is reduced by the coarse carbonitride. Therefore, the W content is set to 3.00% or less.
  • the W content is preferably 2.00% or less, more preferably 1.50% or less.
  • the W content is preferably 0.05% or more, and more preferably 0.10% or more.
  • Ga 0-0.05% Since Ga has an effect of improving corrosion resistance, it may be contained if necessary. However, if Ga is excessively contained, the hot workability is deteriorated. Therefore, the Ga content is set to 0.05% or less. On the other hand, in order to obtain the above effect, the Ga content is preferably 0.0004% or more.
  • Co 0-2.50% Since Co has the effects of improving the strength, soft magnetic properties, high-speed cold forging property, and machinability of the steel material, it may be contained as necessary. In addition, the addition of an appropriate amount of Co increases the saturation magnetic flux density, and thus enhances the soft magnetic characteristics. However, if Co is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. Therefore, the Co content is 2.50% or less.
  • the Co content is preferably 1.00% or less, and more preferably 0.80% or less.
  • the Co content is preferably 0.05% or more, more preferably 0.10% or more.
  • Sb 0 to 2.50% Since Sb has an effect of improving corrosion resistance, it may be contained if necessary. However, if Sb is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. Therefore, the Sb content is set to 2.50% or less.
  • the Sb content is more preferably 1.00% or less, and further preferably 0.20% or less.
  • the Sb content is preferably 0.01% or more, and more preferably 0.05% or more.
  • Ta 0-2.50% Since Ta has an effect of improving corrosion resistance, it may be contained if necessary. However, if Ta is excessively contained, the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated. Therefore, the Ta content is 2.50% or less. The Ta content is preferably 1.50% or less, more preferably 0.90% or less. On the other hand, in order to obtain the above effect, the Ta content is preferably 0.01% or more, more preferably 0.04% or more, and further preferably 0.08% or more.
  • the rod-shaped steel material according to the present invention may contain one or more elements selected from Ca, Mg, Zr, and REM as the second group element, if necessary.
  • Ca, Mg, Zr, and REM may be contained, if necessary, for deoxidation.
  • the soft magnetic properties, high-speed cold forging property, and machinability are deteriorated.
  • the toughness is reduced by the coarse inclusions. Therefore, Ca: 0.05% or less, Mg: 0.012% or less, Zr: 0.012% or less, REM: 0.05% or less.
  • the Ca content is preferably 0.010% or less, more preferably 0.005% or less.
  • the Mg content is preferably 0.010% or less, more preferably 0.005% or less.
  • Zr is preferably 0.010% or less, and more preferably 0.005% or less.
  • the REM is preferably 0.010% or less.
  • the Ca content is more preferably 0.0004% or more, and even more preferably 0.001% or more.
  • the Mg content is preferably 0.0004% or more, and more preferably 0.001% or more.
  • the Zr content is more preferably 0.0004% or more, and even more preferably 0.001% or more.
  • the REM content is more preferably 0.0004% or more, and even more preferably 0.001% or more.
  • REM is a general term for 17 elements including 15 elements of lanthanoids, Y and Sc. One or more of these 17 elements can be contained in steel, and the REM content means the total content of these elements.
  • the rod-shaped steel material according to the present invention may contain one or more elements selected from Pb, Se, Te, Bi, S and P as the elements of the third group, if necessary. .. Pb: 0 to 0.30%, Se: 0 to 0.80%, Te: 0 to 0.30%, Bi: 0 to 0.50%, S: 0 to 0.50%, P: 0 to 0.30%, Pb, Se, Te, Bi, S and P may be contained if necessary because of machinability. However, if each of these elements is excessively contained, the soft magnetic properties and the high-speed cold forging property are deteriorated. It also reduces toughness.
  • Pb 0.30% or less
  • Se 0.80% or less
  • Te 0.30% or less
  • Bi 0.50% or less
  • S 0.50 or less
  • the Pb content is preferably 0.1% or less, more preferably 0.05% or less.
  • the Se content is preferably 0.1% or less, and more preferably 0.05% or less.
  • the Te content is preferably 0.1% or less, more preferably 0.05% or less.
  • the Bi content is preferably 0.1% or less, and more preferably 0.05% or less.
  • the S content is preferably 0.1% or less, and more preferably 0.05% or less.
  • the P content is preferably 0.1% or less, and more preferably 0.05% or less.
  • Pb 0.0001% or more
  • Se 0.0001% or more
  • Te 0.0001% or more
  • Bi 0.0001% or more
  • S 0.0001% or more
  • the Pb content is more preferably 0.0004% or more, and further preferably 0.001% or more.
  • the Se content is more preferably 0.0004% or more, and further preferably 0.001% or more.
  • the Te content is more preferably 0.0004% or more, and even more preferably 0.001% or more.
  • the Bi content is more preferably 0.0004% or more, and further preferably 0.001% or more.
  • the S content is more preferably 0.0001% or more, and further preferably 0.0002% or more.
  • the P content is more preferably 0.0004% or more, and further preferably 0.001% or more.
  • the balance is Fe and impurities.
  • impurity is a component mixed with raw materials such as ore and scrap, and various factors in the manufacturing process when the steel sheet is industrially manufactured, and is allowed as long as it does not adversely affect the present invention. Means something.
  • impurities examples include O, Zn, H and the like. Impurities are preferably reduced, but when they are contained, O, Zn and H are preferably 0.01% or less.
  • the stainless steel rod-shaped steel material according to the present invention can obtain the effect as long as it has the above-mentioned configuration regardless of the manufacturing method.
  • the stainless steel rod-shaped steel material according to the present invention can be obtained by the following manufacturing method. It can be obtained stably.
  • a steel having the above chemical composition is melted, a slab having a predetermined diameter is cast, and then hot or hot rod wire rolling is rough-rolled, intermediate-rolled, and finish-rolled. And heat-treat the rod-shaped steel material. It is preferable to perform inclined rolling before rough rolling. Then, if necessary, pickling or the like is performed as appropriate.
  • Finish rolling inlet temperature In hot rolling of rod-shaped steel, it is preferable to control the inlet temperature of finish rolling.
  • the temperature at the finish rolling inlet side of the bar-shaped steel material changes the average particle size of the nitride and also changes the solid solution fraction of N and B contained in the steel. Therefore, the finish rolling inlet temperature affects the soft magnetic properties, high-speed cold forging property, and machinability.
  • the temperature on the finish rolling inlet side of the bar-shaped steel material exceeds 1200 ° C., the nitride is easily melted, and the amount of solid solution N and the amount of solid solution B increase. As a result, the soft magnetic properties and high-speed cold forging property are deteriorated.
  • the finish rolling inlet temperature is preferably 1200 ° C. or lower, preferably 1100 ° C. or lower, and even more preferably 1050 ° C. or lower.
  • the temperature on the finishing rolling inlet side is less than 600 ° C.
  • the amount of solid solution N becomes too small, so that the machinability deteriorates.
  • the presence of the unsolid solution nitride increases the average particle size of the nitride, which reduces the high-speed cold forging property. Therefore, the temperature on the entry side of the finish rolling is set to 600 ° C. or higher.
  • the finish rolling inlet temperature is preferably 700 ° C. or higher, more preferably 800 ° C.
  • the roll diameter of finish rolling affects the strain distribution and amount of bar-shaped steel, and is related to the average particle size of nitrides and the amount of solid melt N in steel. , It affects machinability and needs to be controlled.
  • the diameter of the finished rolled roll is less than 50 mm, strain is not introduced into the center of the rod-shaped steel material, formation of fine nitrides on the dislocations is not promoted, and the average particle diameter of the nitrides becomes large.
  • the amount of solid solution N increases. As a result, the soft magnetic properties and high-speed cold forging property are deteriorated.
  • the diameter of the finished rolled roll is preferably 50 mm or more, preferably 80 mm or more, and more preferably 100 mm or more.
  • the diameter of the finished rolled roll exceeds 500 mm, the nitride becomes too fine and the amount of solid solution N and the amount of solid solution B also increase, resulting in deterioration of machinability and magnetic properties. It is preferable, and 300 mm or less is more preferable.
  • Heat treatment temperature of rod-shaped steel material It is preferable that the hot-rolled rod-shaped steel material is heat-treated.
  • the heat treatment temperature of the bar steel changes the average particle size of the nitride and the solid solution fraction in the steel. Therefore, the heat treatment temperature of the rod-shaped steel material affects the soft magnetic properties, high-speed cold forging property, and machinability.
  • the heat treatment temperature of the rod-shaped steel material exceeds 1300 ° C., the nitride is easily melted, and the amount of solid solution N and the amount of solid solution B increase. As a result, the soft magnetic properties and high-speed cold forging property are deteriorated.
  • the average particle size of the nitride becomes too small, which reduces machinability.
  • the heat treatment temperature is set to 1300 ° C. or lower, preferably 1200 ° C. or lower, and more preferably 1100 ° C. or lower.
  • the heat treatment temperature of the rod-shaped steel material is less than 500 ° C., the amount of solid solution N becomes too small, and the machinability deteriorates.
  • the presence of the unsolid solution nitride increases the average particle size of the nitride, which reduces the high-speed cold forging property. Therefore, the heat treatment temperature is set to 500 ° C. or higher.
  • the heat treatment temperature is preferably 600 ° C. or higher, more preferably 700 ° C. or higher.
  • the stainless steel rod of the present invention has a compressibility of 70% and a strain rate without cracks of 0.1 / s or more, and can realize excellent high-speed cold forging property.
  • the stainless steel rod-shaped steel material of the present invention has a hole depth (tool life) of 50 mm or more due to drilling, and can realize excellent machinability.
  • the stainless steel rod-shaped steel material of the present invention has a coercive force of 5.0 A / m or less, and can realize excellent soft magnetic properties.
  • Electromagnetic parts are, for example, cores and connectors such as injectors and solenoid valves, and since the rod-shaped steel material used as the material has excellent soft magnetic properties, "magnetic attraction” It can produce effects such as “improvement”, “reducing the diameter of parts”, and “improvement of responsiveness”. In addition, since the rod-shaped steel used as the material has excellent high-speed cold forging and machinability, it is possible to manufacture the part at high production and low cost, and it is also possible to make a near net shape by cold forging. To.
  • the conditions are described below. Specifically, the cast slab is heated, and after inclined rolling, rough rolling, and intermediate rolling, No. Finish rolling was performed at a finish rolling temperature of 1180 ° C. and a finish rolling roll diameter of 480 mm under the conditions of 123, and then No. 1 in Table 6 was performed. Heat treatment was performed at a temperature of 1290 ° C. under the condition of 123 to prepare a bar wire (bar-shaped steel material) having a diameter of 20.0 mm.
  • the obtained bar wire (bar-shaped steel material) was evaluated for the average particle size of the nitride, the amount of solid melt N in the steel, the amount of solid melt B, high-speed cold forging property, soft magnetic properties, and machinability.
  • Table 3 and 4 are examples of the present invention and comparative examples corresponding to the present invention 1, and the amount of solid solution N in the steel is shown in the table.
  • Table 5 shows an example of the present invention and a comparative example corresponding to the present invention 2, and the actual results of the amount of solid solution B in the steel are shown in the table.
  • the average particle size of the nitride is the surface layer portion, the central portion, and the 1/4 depth position portion existing between the surface layer portion and the central portion in the L cross section of the rod-shaped steel material (cross section including the center line of the rod-shaped steel material).
  • one or more visual fields were measured with a visual field of 400 times. Then, the nitride in the observation field of view was identified using FE-SEM / ESD, and the average value of the equivalent circle diameters of the nitride in the same field of view was calculated.
  • the average particle size of the nitride is 0.01 to 5 ⁇ m, it is “A”, if it is 5 to 7 ⁇ m, it is “B”, if it is 7 to 10 ⁇ m, it is “C”, and if it exceeds 10 ⁇ m, it is “D”.
  • the steel bar of the present invention was used, it was "A”, “B”, and “C”, and the average particle size of the nitride was excellent.
  • the nitride includes carbonitride.
  • the high-speed cold forging property was judged from the presence or absence of cracks in the end face by a compression test.
  • a test piece of ⁇ 10 ⁇ 15 mm is prepared, the strain rate is changed under the condition of a compression rate of 70% at room temperature, the test piece is compressed, the side surface of the test piece after the test is observed, the presence or absence of cracks is judged, and high-speed cooling is performed.
  • the forgeability was evaluated. "A” if the compression rate is 70% and the strain rate without cracking is 10 / s or more, "B” if it is 1 / s or more, "C” if it is 0.1 / s or more, and less than 0.1 / s. If so, it was set as "D". When the steel bar of the present invention was used, it was "A”, “B”, and “C”, and was excellent in high-speed cold forging property.
  • the coercive force (A / m) was measured.
  • a ring-shaped test piece having a thickness of 3 mm, an outer diameter of 10 mm, and an inner diameter of 8 mm was prepared, and after being heat-treated at 950 ° C. ⁇ 2 hr, the coercive force was measured. If the coercive force is 2.0 A / m or less, it is "A”, if it is 3.5 A / m or less, it is "B”, if it is 5.0 A / m or less, it is "C”, and if it is over 5.0 A / m. For example, “D” was used. When the steel bar of the present invention was used, it was “A”, “B", and “C”, and had excellent soft magnetic properties.
  • the machinability was evaluated by the tool life.
  • a hole of ⁇ 15 ⁇ 30 mm is prepared and drilled in the longitudinal direction (dry type, drill diameter: ⁇ 4 mm, cutting speed: 25 m / min, feed: 0.1 mm / rev, tool: SKH9) to make the hole uncut.
  • the depth was measured and the machinability was evaluated. If the hole depth (tool life) is 130 mm or more, it is set as "A”, if it is 100 mm or more, it is set as "B”, if it is 50 mm or more, it is set as "C”, and if it is less than 50 mm, it is set as "D”. When the steel bar of the present invention was used, it was "A”, “B", and “C”, and the machinability was excellent.
  • Table 6 shows an example of the present invention and a comparative example corresponding to the present invention 1, and the amount of solid solution N in the steel is shown in the table.
  • Table 7 shows an example of the present invention and a comparative example corresponding to the present invention 2, and the actual results of the amount of solid solution B in the steel are shown in the table.
  • a rod-shaped steel material having excellent soft magnetic properties can be obtained, which is extremely useful in industry.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Manufacturing & Machinery (AREA)
  • Electromagnetism (AREA)
  • Soft Magnetic Materials (AREA)
  • Fuel Cell (AREA)
  • Hard Magnetic Materials (AREA)
  • Heat Treatment Of Steel (AREA)
  • Paper (AREA)
  • Load-Engaging Elements For Cranes (AREA)
  • Superconductors And Manufacturing Methods Therefor (AREA)

Abstract

Un matériau de barre en acier inoxydable selon la présente invention a une composition chimique qui contient, en % en masse, de 0,001% à 0,030% de C, de 0,01% à 4,00% de Si, de 0,01% à 2,00% de Mn, de 0,01% à 4,00% de Ni, de 8,0% à 35,0% de Cr, de 0,01% à 5,00% de Mo, de 0,01% à 2,00% de Cu, de 0,001% à 0,030% de N, de 7,000% ou moins de Al, de 0% à 2,00% de Ti, de 0% à 2,00% de Nb et de 0% à 0,1% de B, le reste étant constitué de Fe et d'impuretés. Par rapport à ce matériau de barre en acier inoxydable, la composition chimique contient en outre, en % en masse, un ou plusieurs éléments choisis parmi 0,001 % ou plus de Ti, 0,001 % ou plus de Nb et 0,0001 % ou plus de B; le diamètre moyen des particules des nitrures est inférieur ou égal à 10 μm ; et la quantité de N solides dissous dans l'acier est de 0,020 % en masse ou moins.
PCT/JP2021/042062 2020-11-19 2021-11-16 Matériau de barre en acier inoxydable et composant électromagnétique WO2022107757A1 (fr)

Priority Applications (6)

Application Number Priority Date Filing Date Title
EP21894631.7A EP4249612A1 (fr) 2020-11-19 2021-11-16 Matériau de barre en acier inoxydable et composant électromagnétique
MX2023005833A MX2023005833A (es) 2020-11-19 2021-11-16 Material de barra de acero inoxidable y componente electromagnetico.
JP2022563763A JPWO2022107757A1 (fr) 2020-11-19 2021-11-16
KR1020237016897A KR20230088905A (ko) 2020-11-19 2021-11-16 스테인리스 봉상 강재 및 전자 부품
US18/037,694 US20240011137A1 (en) 2020-11-19 2021-11-16 Stainless steel bar material and electromagnetic component
CN202180077648.7A CN116438321A (zh) 2020-11-19 2021-11-16 不锈钢棒状钢材及电磁部件

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2020192251 2020-11-19
JP2020-192251 2020-11-19

Publications (1)

Publication Number Publication Date
WO2022107757A1 true WO2022107757A1 (fr) 2022-05-27

Family

ID=81707995

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2021/042062 WO2022107757A1 (fr) 2020-11-19 2021-11-16 Matériau de barre en acier inoxydable et composant électromagnétique

Country Status (8)

Country Link
US (1) US20240011137A1 (fr)
EP (1) EP4249612A1 (fr)
JP (1) JPWO2022107757A1 (fr)
KR (1) KR20230088905A (fr)
CN (1) CN116438321A (fr)
MX (1) MX2023005833A (fr)
TW (1) TWI773591B (fr)
WO (1) WO2022107757A1 (fr)

Citations (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS59232258A (ja) * 1983-06-14 1984-12-27 Sanyo Tokushu Seikou Kk 靭性にすぐれた快削・耐食軟磁性棒管用鋼
JPH0344448A (ja) 1989-07-11 1991-02-26 Daido Steel Co Ltd 耐食性に優れたステンレス鋼
JPH0649605A (ja) 1992-08-04 1994-02-22 Daido Steel Co Ltd 電磁ステンレス鋼
JPH0649606A (ja) 1992-08-04 1994-02-22 Daido Steel Co Ltd 電磁ステンレス鋼
JP2000160302A (ja) * 1998-11-19 2000-06-13 Sanyo Special Steel Co Ltd 冷間鍛造性に優れた電磁ステンレス鋼
US20030086810A1 (en) * 2001-09-04 2003-05-08 Gunter Schnabel Cold-workable corrosion-resistant chromium steel
JP2006016665A (ja) * 2004-07-01 2006-01-19 Nippon Steel & Sumikin Stainless Steel Corp 耐食性，冷間加工性および靱性に優れる磁性を有する安価ステンレス鋼線材または鋼線。
US20070166183A1 (en) * 2006-01-18 2007-07-19 Crs Holdings Inc. Corrosion-Resistant, Free-Machining, Magnetic Stainless Steel
KR20090025728A (ko) * 2007-09-07 2009-03-11 하미란 열간 단조를 이용한 연자성 스테인리스 부품의 제조방법 및이에 의해 제조된 하우징 및 코어
JP2020063472A (ja) * 2018-10-16 2020-04-23 日鉄ステンレス株式会社 磁気特性に優れたフェライト系ステンレス鋼

Family Cites Families (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109385571B (zh) * 2018-10-11 2020-05-12 中国航发成都发动机有限公司 一种耐热不锈钢材料及其制备方法
CN109182673B (zh) * 2018-11-20 2020-07-10 太原科技大学 一种低成本高强度耐磨不锈钢及其生产方法

Patent Citations (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS59232258A (ja) * 1983-06-14 1984-12-27 Sanyo Tokushu Seikou Kk 靭性にすぐれた快削・耐食軟磁性棒管用鋼
JPH0344448A (ja) 1989-07-11 1991-02-26 Daido Steel Co Ltd 耐食性に優れたステンレス鋼
JPH0649605A (ja) 1992-08-04 1994-02-22 Daido Steel Co Ltd 電磁ステンレス鋼
JPH0649606A (ja) 1992-08-04 1994-02-22 Daido Steel Co Ltd 電磁ステンレス鋼
JP2000160302A (ja) * 1998-11-19 2000-06-13 Sanyo Special Steel Co Ltd 冷間鍛造性に優れた電磁ステンレス鋼
US20030086810A1 (en) * 2001-09-04 2003-05-08 Gunter Schnabel Cold-workable corrosion-resistant chromium steel
JP2006016665A (ja) * 2004-07-01 2006-01-19 Nippon Steel & Sumikin Stainless Steel Corp 耐食性，冷間加工性および靱性に優れる磁性を有する安価ステンレス鋼線材または鋼線。
US20070166183A1 (en) * 2006-01-18 2007-07-19 Crs Holdings Inc. Corrosion-Resistant, Free-Machining, Magnetic Stainless Steel
KR20090025728A (ko) * 2007-09-07 2009-03-11 하미란 열간 단조를 이용한 연자성 스테인리스 부품의 제조방법 및이에 의해 제조된 하우징 및 코어
JP2020063472A (ja) * 2018-10-16 2020-04-23 日鉄ステンレス株式会社 磁気特性に優れたフェライト系ステンレス鋼

Also Published As

Publication number Publication date
KR20230088905A (ko) 2023-06-20
EP4249612A1 (fr) 2023-09-27
CN116438321A (zh) 2023-07-14
MX2023005833A (es) 2023-06-02
US20240011137A1 (en) 2024-01-11
TWI773591B (zh) 2022-08-01
TW202221147A (zh) 2022-06-01
JPWO2022107757A1 (fr) 2022-05-27

Similar Documents

Publication Publication Date Title
JP4424503B2 (ja) 棒鋼・線材
JP6384629B2 (ja) 高周波焼入れ用鋼
JP5858204B2 (ja) 熱間鍛造用鋼材およびその製造方法ならびにその鋼材を用いた熱間鍛造素形材の製造方法
WO2012011469A1 (fr) Barre ou fil d'acier laminé pour forgeage à chaud
CN109477179B (zh) 高频淬火用钢
JP3614113B2 (ja) 被削性に優れた軸受要素部品用鋼材
KR20190028781A (ko) 고주파 담금질용 강
JP2013234354A (ja) 冷間鍛造用熱間圧延棒鋼または線材
KR20220097991A (ko) 냉간 가공성이 우수한 고경도·고내식성 용도의 마르텐사이트계 스테인리스강 및 그 제조 방법
JP4793298B2 (ja) 非調質鋼材およびその製造方法
CN108138288B (zh) 热锻造用钢及热锻造品
JP2017193767A (ja) 冷間鍛造用鋼およびその製造方法
JP6814655B2 (ja) フェライト系快削ステンレス線材
JP6652021B2 (ja) 熱間鍛造用鋼及び熱間鍛造品
JP6668741B2 (ja) 熱間圧延棒線材
TWI776112B (zh) 冷加工性優異之高硬度、高耐蝕性用途之麻田散鐵系不鏽鋼及其製造方法
TWI773591B (zh) 不鏽鋼棒狀鋼材及電磁零件
WO2021166797A1 (fr) Matériau en acier inoxydable électromagnétique en forme de tige
KR20170121267A (ko) 열간 압연 봉선재, 부품 및 열간 압연 봉선재의 제조 방법
JP2017193766A (ja) 冷間鍛造用鋼
JP6801717B2 (ja) 冷間鍛造用鋼及びその製造方法
US20240150881A1 (en) Ferritic free-cutting stainless steel material
JP2022081452A (ja) 温熱間鍛造用電磁ステンレス棒状鋼材及び電磁部品
JP6766531B2 (ja) 冷間鍛造用鋼およびその製造方法
JP2023144727A (ja) マルテンサイト系ステンレス熱間圧延線材及びその製造方法、並びにマルテンサイト系ステンレス焼鈍線材

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 21894631

Country of ref document: EP

Kind code of ref document: A1

DPE1 Request for preliminary examination filed after expiration of 19th month from priority date (pct application filed from 20040101)
ENP Entry into the national phase

Ref document number: 2022563763

Country of ref document: JP

Kind code of ref document: A

ENP Entry into the national phase

Ref document number: 20237016897

Country of ref document: KR

Kind code of ref document: A

NENP Non-entry into the national phase

Ref country code: DE

ENP Entry into the national phase

Ref document number: 2021894631

Country of ref document: EP

Effective date: 20230619