WO2023181820A1 - 連続焼鈍装置及び連続溶融亜鉛めっき装置、並びに鋼板の製造方法 - Google Patents

連続焼鈍装置及び連続溶融亜鉛めっき装置、並びに鋼板の製造方法 Download PDF

Info

Publication number
WO2023181820A1
WO2023181820A1 PCT/JP2023/007690 JP2023007690W WO2023181820A1 WO 2023181820 A1 WO2023181820 A1 WO 2023181820A1 JP 2023007690 W JP2023007690 W JP 2023007690W WO 2023181820 A1 WO2023181820 A1 WO 2023181820A1
Authority
WO
WIPO (PCT)
Prior art keywords
steel sheet
cold
rolled steel
magnetic field
less
Prior art date
Legal status (The legal status 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 status listed.)
Ceased
Application number
PCT/JP2023/007690
Other languages
English (en)
French (fr)
Japanese (ja)
Inventor
一輝 遠藤
涼平 森本
勇樹 田路
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
JFE Steel Corp
Original Assignee
JFE Steel Corp
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 JFE Steel Corp filed Critical JFE Steel Corp
Priority to JP2023555692A priority Critical patent/JP7380965B1/ja
Priority to CN202380029116.5A priority patent/CN118946671A/zh
Priority to MX2024011171A priority patent/MX2024011171A/es
Priority to KR1020247033711A priority patent/KR20240162098A/ko
Priority to US18/844,156 priority patent/US20250171872A1/en
Priority to EP23774419.8A priority patent/EP4474497A4/en
Publication of WO2023181820A1 publication Critical patent/WO2023181820A1/ja
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

Links

Images

Classifications

    • 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
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/54—Furnaces for treating strips or wire
    • C21D9/56—Continuous furnaces for strip or wire
    • C21D9/562—Details
    • 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
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/54—Furnaces for treating strips or wire
    • C21D9/56—Continuous furnaces for strip or wire
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • B32B15/013—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of a metal other than iron or aluminium
    • 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
    • C21D3/00—Diffusion processes for extraction of non-metals; Furnaces therefor
    • C21D3/02—Extraction of non-metals
    • C21D3/06—Extraction of hydrogen
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/005—Furnaces in which the charge is moving up or down
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/54—Furnaces for treating strips or wire
    • C21D9/56—Continuous furnaces for strip or wire
    • C21D9/561—Continuous furnaces for strip or wire with a controlled atmosphere or 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/54—Furnaces for treating strips or wire
    • C21D9/56—Continuous furnaces for strip or wire
    • C21D9/573—Continuous furnaces for strip or wire with cooling
    • 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
    • C22C38/008—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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/003—Apparatus
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/003—Apparatus
    • C23C2/0035—Means for continuously moving substrate through, into or out of the bath
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/003—Apparatus
    • C23C2/0038—Apparatus characterised by the pre-treatment chambers located immediately upstream of the bath or occurring locally before the dipping process
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/14—Removing excess of molten coatings; Controlling or regulating the coating thickness
    • C23C2/24—Removing excess of molten coatings; Controlling or regulating the coating thickness using magnetic or electric fields
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/26—After-treatment
    • C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
    • C23C2/36—Elongated material
    • C23C2/40—Plates; Strips

Definitions

  • the present invention relates to a continuous annealing device, a continuous hot-dip galvanizing device, and a method for manufacturing steel sheets.
  • the present invention is particularly directed to a continuous annealing apparatus and a continuous annealing apparatus for producing a steel plate having a small amount of hydrogen inherent in the steel and having excellent hydrogen embrittlement resistance, which is suitably used in the fields of automobiles, home appliances, and building materials.
  • the present invention relates to a hot-dip galvanizing apparatus and a method for manufacturing steel sheets.
  • the steel sheets are annealed in a reducing atmosphere containing hydrogen.
  • Hydrogen enters. Hydrogen inherent in a steel sheet reduces formability such as ductility, bendability, stretch flangeability, etc. of the steel sheet. Further, hydrogen inherent in the steel plate may cause the steel plate to become brittle and cause delayed fracture. Therefore, a treatment is required to reduce the amount of hydrogen in the steel sheet.
  • the amount of hydrogen in the steel can be reduced by leaving the product coil manufactured in a continuous annealing device and a continuous hot-dip galvanizing device at room temperature.
  • room temperature it takes time for hydrogen to move from the inside of the steel sheet to the surface and desorb from the surface, so it takes several weeks or more to sufficiently reduce the amount of hydrogen in the steel. . Therefore, the space and time required for such dehydrogenation treatment pose problems in the manufacturing process.
  • Patent Document 1 discloses that a steel sheet, a hot-dip galvanized steel sheet, or an alloyed hot-dip galvanized steel sheet after annealing is held in a temperature range of 50° C. or more and 300° C. or less for 1800 seconds or more and 43200 seconds or less. A method of reducing the amount of hydrogen is disclosed.
  • Patent Document 1 there are concerns about changes in mechanical properties such as an increase in yield strength and temper embrittlement due to structural changes due to heating.
  • the present invention provides a continuous annealing apparatus and a continuous hot-dip galvanizing system that can produce steel sheets with excellent hydrogen embrittlement resistance without impairing production efficiency or changing mechanical properties.
  • the purpose of the present invention is to provide an apparatus and a method for manufacturing steel sheets.
  • a steel plate is annealed in a reducing atmosphere containing hydrogen, and then cooled from the annealing temperature to room temperature.
  • CAL continuous annealing line
  • CGL continuous hot-dip galvanizing line
  • a payoff reel for discharging cold-rolled steel sheets from cold-rolled coils The annealing furnace continuously anneales the cold-rolled steel sheet by passing the sheet through the sheet, in which a heating zone, a soaking zone, and a cooling zone are located from the upstream side in the sheet passing direction, and in the heating zone and the soaking zone, reduction containing hydrogen is formed.
  • an annealing furnace for annealing the cold-rolled steel sheet in a neutral atmosphere and cooling the cold-rolled steel sheet in the cooling zone; downstream equipment that continues to pass the cold rolled steel sheet discharged from the annealing furnace; a tension reel that winds up the cold-rolled steel sheet that is being passed through the downstream equipment; a magnetic field application device that applies a steady magnetic field along the width direction of the cold-rolled steel sheet to the cold-rolled steel sheet that is being passed from the cooling zone to the tension reel; Continuous annealing equipment with
  • the magnetic field application device includes an electromagnet located outside the widthwise end of the cold-rolled steel sheet, and the electromagnet has a magnetic pole surface facing the widthwise end surface of the cold-rolled steel sheet.
  • the continuous annealing apparatus according to any one of [3] to [3].
  • the magnetic field application device includes a pair of electromagnets located outside both ends of the cold-rolled steel sheet in the width direction, and each of the pair of electromagnets has a magnetic pole surface facing the end surface of the cold-rolled steel sheet in the width direction.
  • the continuous annealing apparatus according to any one of [1] to [3] above, wherein one of the magnetic pole faces is a north pole and the other is a south pole.
  • a hot-dip galvanizing bath is located downstream of the annealing furnace in the sheet passing direction and immerses the cold-rolled steel sheet to apply hot-dip galvanization to the cold-rolled steel sheet; Continuous hot dip galvanizing equipment.
  • the downstream equipment includes an alloying furnace that is located downstream of the hot-dip galvanizing bath in the sheet-threading direction and heat-alloys the hot-dip galvanized steel sheet by passing the cold-rolled steel sheet through the hot-dip galvanizing bath.
  • Continuous hot-dip galvanizing equipment includes an alloying furnace that is located downstream of the hot-dip galvanizing bath in the sheet-threading direction and heat-alloys the hot-dip galvanized steel sheet by passing the cold-rolled steel sheet through the hot-dip galvanizing bath.
  • the magnetic field application device includes a pair of electromagnets located outside both ends of the cold-rolled steel sheet in the width direction, and each of the pair of electromagnets has a magnetic pole surface facing the end surface of the cold-rolled steel sheet in the width direction.
  • the continuous hot-dip galvanizing apparatus according to any one of [7] to [12] above, wherein one of the magnetic pole surfaces is an N pole and the other is an S pole.
  • (A) A step of paying out the cold rolled steel sheet from the cold rolled coil using a payoff reel, (B) The cold rolled steel sheet is passed through an annealing furnace in which a heating zone, a soaking zone, and a cooling zone are located from the upstream side in the sheet passing direction, and (B-1) In the heating zone and the soaking zone, Annealing the cold rolled steel sheet in a reducing atmosphere containing hydrogen, (B-2) cooling the cold rolled steel sheet in the cooling zone, performing continuous annealing; (C) a step of continuously passing the cold rolled steel sheet discharged from the annealing furnace; (D) a step of winding up the cold-rolled steel sheet with a tension reel to form a product coil; in this order, After step (B-2) and before step (D), a magnetic field application step of applying a steady magnetic field along the width direction of the cold rolled steel sheet to the cold rolled steel sheet during sheet passing.
  • Manufacturing method of steel plate including.
  • Step (C) is (C-1) a step of immersing the cold rolled steel sheet in a hot dip galvanizing bath located downstream of the annealing furnace in the sheet passing direction to apply hot dip galvanization to the cold rolled steel sheet.
  • the step (C) is subsequent to the step (C-1) and includes (C-2) passing the cold rolled steel sheet through an alloying furnace located downstream of the hot dip galvanizing bath in the sheet passing direction.
  • a magnetic field application device including an electromagnet located outside the widthwise end of the cold rolled steel sheet, the electromagnet having a magnetic pole face facing the widthwise end surface of the cold rolled steel sheet, The method for manufacturing a steel plate according to any one of [16] to [25] above, wherein the steady magnetic field is applied.
  • the magnetic field application step includes a pair of electromagnets located outside both ends of the cold rolled steel sheet in the width direction, and each of the pair of electromagnets has a magnetic pole surface facing the end surface of the cold rolled steel sheet in the width direction. and the steady magnetic field is applied by a magnetic field applying device in which one of the magnetic pole faces is a north pole and the other is a south pole, according to any one of [16] to [25] above. manufacturing method of steel plate.
  • the cold-rolled steel sheet contains, in mass%, C: 0.030-0.800%, Si: 0.01-3.00%, Mn: 0.01-10.00%, P: 0.001-0.100%, S: 0.0001-0.0200%, N: 0.0005 to 0.0100%, and Al: 0.001 to 2.000%,
  • the component composition further comprises, in mass%, Ti: 0.200% or less, Nb: 0.200% or less, V: 0.500% or less, W: 0.500% or less, B: 0.0050% or less, Ni: 1.000% or less, Cr: 1.000% or less, Mo: 1.000% or less, Cu: 1.000% or less, Sn: 0.200% or less, Sb: 0.200% or less, Ta: 0.100% or less, Ca: 0.0050% or less, Mg: 0.0050% or less, The method for producing a steel sheet according to [29] above, containing at least one element selected from the group consisting of Zr: 0.1000% or less, and REM: 0.0050% or less.
  • the cold rolled steel sheet has a mass percentage of C: 0.001-0.400%, Si: 0.01-2.00%, Mn: 0.01 to 5.00%, P: 0.001-0.100%, S: 0.0001-0.0200%, Cr: 9.0-28.0%, Ni: 0.01 to 40.0%, N: 0.0005 to 0.500%, and Al: 0.001 to 3.000%,
  • the component composition further comprises, in mass%, Ti: 0.500% or less, Nb: 0.500% or less, V: 0.500% or less, W: 2.000% or less, B: 0.0050% or less, Mo: 2.000% or less, Cu: 3.000% or less, Sn: 0.500% or less, Sb: 0.200% or less, Ta: 0.100% or less, Ca: 0.0050% or less, Mg: 0.0050% or less, The method for producing a steel plate according to [31] above, containing at least one element selected from the group consisting of Zr: 0.1000% or less, and REM: 0.0050% or less.
  • steel sheets with excellent hydrogen embrittlement resistance can be manufactured without impairing production efficiency or changing mechanical properties. be able to.
  • FIG. 1 is a schematic diagram of a continuous annealing apparatus 100 according to an embodiment of the present invention.
  • 1 is a schematic diagram of a continuous hot-dip galvanizing apparatus 200 according to an embodiment of the present invention.
  • FIG. 3 is a schematic diagram of a continuous hot-dip galvanizing apparatus 300 according to another embodiment of the present invention.
  • It is a schematic diagram which shows the structure of a pair of electromagnets 60A and 60B as a magnetic field application device used in each embodiment of this invention, and the magnetic force line generated from the said electromagnets 60A and 60B.
  • (A) and (B) are diagrams schematically showing an example of how a pair of electromagnets 60A and 60B are installed as magnetic field generators for a cold rolled steel sheet S during sheet passing in each embodiment of the present invention. be.
  • One embodiment of the present invention relates to continuous annealing equipment (Continuous Annealing Line: CAL), and another embodiment of the present invention relates to continuous hot-dip galvanizing equipment (Continuous hot-dip Galvanizing Line: CGL) It is.
  • a method for manufacturing a steel plate according to an embodiment of the present invention is realized by a continuous annealing line (CAL) or a continuous hot-dip galvanizing line (CGL).
  • CAL continuous annealing line
  • CGL continuous hot-dip galvanizing line
  • a continuous annealing apparatus (CAL) 100 includes a payoff reel 10 for discharging a cold-rolled steel sheet S from a cold-rolled coil C, and a payoff reel 10 for discharging a cold-rolled steel sheet S from a cold-rolled coil C; an annealing furnace 20 for continuous annealing; a downstream facility 30 for continuously passing the cold rolled steel sheet S discharged from the annealing furnace 20; and a tension reel 50.
  • a heating zone 22, a soaking zone 24, and a cooling zone 26 are located from the upstream side in the sheet passing direction, and in the heating zone 22 and soaking zone 24, the cold rolled steel sheet S is annealed in a reducing atmosphere containing hydrogen. , the cold rolled steel sheet S is cooled in the cooling zone 26.
  • the annealing furnace 20 of the CAL 100 has an overaging treatment zone 28 downstream of the cooling zone 26, it is not essential.
  • the cold rolled steel sheet S is subjected to an overaging treatment.
  • a product coil of cold rolled annealed steel plate (CR) is manufactured by CAL 100.
  • the method of manufacturing a steel plate according to the first embodiment realized by a continuous annealing apparatus (CAL) 100 is as follows: (A) A cold rolled steel plate (steel strip) (B-1 ) In the heating zone 22 and the soaking zone 24, the cold rolled steel sheet S is annealed in a reducing atmosphere containing hydrogen, and (B-2) in the cooling zone 26, the cold rolled steel sheet S is cooled, performing continuous annealing; C) A step of continuously passing the cold rolled steel sheet S discharged from the annealing furnace 20, and (D) A step of winding up the cold rolled steel sheet S using the tension reel 50 to form a product coil P, in this order.
  • This embodiment is a method for manufacturing a product coil of cold rolled annealed steel plate (CR) using CAL100.
  • a continuous hot-dip galvanizing apparatus (CGL) 200 includes a payoff reel 10 for discharging a cold-rolled steel sheet S from a cold-rolled coil C; An annealing furnace 20 that continuously anneales the sheet, a downstream facility 30 that continues to pass the cold-rolled steel sheet S discharged from the annealing furnace 20, and a downstream facility 30 that winds up the cold-rolled steel sheet S being passed through the annealing furnace 20 to form a product.
  • the tension reel 50 has a coil P.
  • a heating zone 22, a soaking zone 24, and a cooling zone 26 are located from the upstream side in the sheet passing direction, and in the heating zone 22 and soaking zone 24, the cold rolled steel sheet S is annealed in a reducing atmosphere containing hydrogen. , the cold rolled steel sheet S is cooled in the cooling zone 26.
  • the CGL 200 is located downstream of the annealing furnace 20 in the sheet passing direction as a downstream facility 30, and has a hot-dip galvanizing bath 31 in which the cold-rolled steel sheet S is immersed to apply hot-dip galvanization to the cold-rolled steel sheet S; It further includes an alloying furnace 33, which is located downstream of the plating bath 31 in the sheet passing direction, and heats and alloys the hot-dip galvanizing by passing the cold-rolled steel sheet S therethrough.
  • the CGL 200 produces a product coil of alloyed hot-dip galvanized steel (GA) with an alloyed galvanized layer.
  • a product coil of a hot-dip galvanized steel sheet (GI) in which the galvanized layer is not alloyed is manufactured.
  • a method for manufacturing a steel sheet according to a second embodiment realized by a continuous hot-dip galvanizing apparatus (CGL) 200 includes (A) a method of manufacturing a cold-rolled steel sheet (steel strip) from a cold-rolled coil C using a payoff reel 10; ) A step of discharging the S, and (B) passing the cold rolled steel sheet S into the annealing furnace 20 in which the heating zone 22, the soaking zone 24, and the cooling zone 26 are located from the upstream side in the sheet passing direction.
  • the cold rolled steel sheet S is annealed in a reducing atmosphere containing hydrogen
  • the cold rolled steel sheet S is cooled, performing continuous annealing.
  • step (C) is (C-1) a step of immersing the cold rolled steel sheet S in the hot dip galvanizing bath 31 located downstream of the annealing furnace 20 in the sheet passing direction to apply hot dip galvanization to the cold rolled steel sheet S. and (C-2) passing the cold-rolled steel sheet S through the alloying furnace 33 located downstream of the hot-dip galvanizing bath 31 in the sheet-threading direction, and heating and alloying the hot-dip galvanizing.
  • This embodiment is a method for manufacturing a product coil of an alloyed hot-dip galvanized steel sheet (GA) in which a galvanized layer is alloyed using CGL200.
  • a continuous hot dip galvanizing apparatus (CGL) 300 has the same configuration as the CGL 200 except that it does not include an alloying furnace 33.
  • the CGL 300 produces a product coil of hot-dip galvanized steel (GI) in which the galvanized layer is not alloyed.
  • GI hot-dip galvanized steel
  • the method for manufacturing a steel plate according to the third embodiment in which step (C-1) is performed and step (C-2) is not performed is realized, for example, by CGL300 without the alloying furnace 33, and also by CGL200.
  • This can also be achieved by simply passing the steel plate S through the alloying furnace 33 without performing heating and alloying.
  • This embodiment is a method for manufacturing a product coil of hot-dip galvanized steel sheet (GI) in which the galvanized layer is not alloyed using CGL200 or CGL300.
  • GI hot-dip galvanized steel sheet
  • Step (A) Referring to FIGS. 1 to 3, a payoff reel 10 pays out a cold rolled steel sheet S from a cold rolled coil C. That is, in step (A), the cold rolled steel sheet S is paid out from the cold rolled coil C by the payoff reel 10.
  • the discharged cold rolled steel sheet S passes through the welding machine 11, the cleaning equipment 12, and the entrance looper 13, and is supplied to the annealing furnace 20.
  • the upstream equipment between the payoff reel 10 and the annealing furnace 20 is not limited to the welding machine 11, the cleaning equipment 12, and the entrance looper 13, and may be any known or arbitrary equipment.
  • an annealing furnace 20 continuously anneals a cold-rolled steel sheet S by passing it therethrough.
  • a heating zone 22, a soaking zone 24, and a cooling zone 26 are located from the upstream side in the sheet passing direction, and in the heating zone 22 and soaking zone 24, the cold rolled steel sheet S is annealed in a reducing atmosphere containing hydrogen. , the cold rolled steel sheet S is cooled in the cooling zone 26.
  • step (B) continuous annealing is performed by passing the cold rolled steel sheet S through the annealing furnace 20 in which the heating zone 22, soaking zone 24, and cooling zone 26 are located from the upstream side in the sheet passing direction.
  • Cooling zone 26 may be composed of a plurality of cooling zones. Further, a preheating zone may be provided on the upstream side of the heating zone 22 in the sheet passing direction.
  • the annealing furnace 20 of the CAL 100 shown in FIG. 1 has an overaging treatment zone 28 downstream of the cooling zone 26, it is not essential.
  • each zone is illustrated as a vertical furnace, but the present invention is not limited to this, and a horizontal furnace may be used. In the case of a vertical furnace, adjacent bands communicate through throats (throttles) that connect the tops or bottoms of each band.
  • the cold rolled steel sheet S can be directly heated using a burner, or the cold rolled steel sheet S can be indirectly heated using a radiant tube (RT) or an electric heater. Further, heating by induction heating, roll heating, electric resistance heating, direct current heating, salt bath heating, electron beam heating, etc. is also possible.
  • the average temperature inside the heating zone 22 is preferably 500 to 800°C. At the same time that the gas from the soaking zone 24 flows into the heating zone 22, reducing gas is separately supplied.
  • a H 2 -N 2 mixed gas is usually used, for example, a gas having a composition of 1 to 35% by volume of H 2 and the balance consisting of one or both of N 2 and Ar and unavoidable impurities (with a low dew point). : about -60°C).
  • the cold rolled steel sheet S can be indirectly heated using a radiant tube (RT).
  • the average temperature inside the soaking zone 24 is preferably 600 to 950°C.
  • a reducing gas is supplied to the soaking zone 24.
  • a H 2 -N 2 mixed gas is usually used, for example, a gas having a composition of 1 to 35% by volume of H 2 and the balance consisting of one or both of N 2 and Ar and unavoidable impurities (with a low dew point). : about -60°C).
  • cooling zone 26 In the cooling zone 26, the cold rolled steel sheet S is cooled by either gas, a mixture of gas and water, or water. When the cold rolled steel sheet S leaves the annealing furnace 20, it is cooled to about 100 to 400°C in CAL and to about 470 to 530°C in CGL.
  • a plurality of cooling nozzles are provided in the cooling zone 26 along the steel plate conveyance path.
  • the cooling nozzle is a circular tube that is longer than the width of the steel plate, as described in, for example, Japanese Patent Application Publication No. 2010-185101, and is installed so that the extending direction of the circular tube is parallel to the width direction of the steel plate.
  • the circular tube is provided with a plurality of through holes at predetermined intervals along the extending direction of the circular tube at a portion facing the steel plate, and water in the circular tube is injected toward the steel plate from the through holes.
  • the cooling nozzles are provided in pairs to face each other on the front and back sides of the steel plate, and a plurality of pairs (for example, 5 to 10 pairs) of the cooling nozzles are arranged at predetermined intervals along the steel plate conveyance path to form one cooling zone. Configure. It is preferable that about 3 to 6 cooling zones be arranged along the steel plate conveyance path.
  • cold rolled steel sheet S leaving cooling zone 26 is subjected to at least one of isothermal holding, reheating, furnace cooling, and natural cooling.
  • the rolled steel sheet S leaves the annealing furnace 20 it is cooled to about 100 to 400°C.
  • step (C) the cold rolled steel sheet S discharged from the annealing furnace 20 is continuously passed through the downstream equipment 30.
  • CAL 100 includes an outlet looper 35 and a temper rolling mill 36 as downstream equipment 30.
  • the CGL 200 includes a hot dip galvanizing bath 31, a gas wiping device 32, an alloying furnace 33, a cooling device 34, an exit looper 35, and a temper rolling mill 36 as downstream equipment 30.
  • the CGL 300 includes a hot dip galvanizing bath 31, a gas wiping device 32, a cooling device 34, an exit looper 35, and a temper rolling mill 36 as downstream equipment 30.
  • the downstream equipment 30 is not limited to these, and may be any known or arbitrary equipment.
  • the downstream equipment 30 can include a tension leveler, chemical conversion equipment, surface conditioning equipment, oiling equipment, and inspection equipment.
  • hot-dip galvanizing bath 31 is located downstream of annealing furnace 20 in the sheet passing direction, and immerses cold-rolled steel sheet S to apply hot-dip galvanization to cold-rolled steel sheet S. That is, in step (C-1), the cold-rolled steel sheet S is immersed in the hot-dip galvanizing bath 31 located downstream of the annealing furnace 20 in the sheet-threading direction to apply hot-dip galvanization to the cold-rolled steel sheet S.
  • the snout 29 connected to the most downstream zone of the annealing furnace (the cooling zone 26 in FIGS.
  • Hot-dip galvanizing may be performed according to a standard method.
  • Gas is blown onto the cold rolled steel sheet S from a pair of gas wiping devices 32 arranged to sandwich the cold rolled steel sheet S pulled up from the hot dip galvanizing bath 31 to adjust the amount of molten zinc deposited on both sides of the cold rolled steel sheet S. be able to.
  • the alloying furnace 33 is located downstream of the hot dip galvanizing bath 31 and the gas wiping device 32 in the sheet passing direction, passes the cold rolled steel sheet S, and heats and alloys the hot dip galvanizing. . That is, in step (C-2), the cold rolled steel sheet S is passed through the alloying furnace 33 located downstream of the hot dip galvanizing bath 31 and the gas wiping device 32 in the sheet passing direction, and the hot dip galvanizing is heated and alloyed. do. Alloying treatment may be performed according to a conventional method.
  • the heating means in the alloying furnace 33 is not particularly limited, and examples thereof include heating with high temperature gas and induction heating.
  • the alloying furnace 33 is an optional facility in the CGL, and the alloying process is an optional step in the method for manufacturing a steel plate using the CGL.
  • the cooling device 34 is located downstream of the gas wiping device 32 and the alloying furnace 33 in the sheet passing direction.
  • the cold-rolled steel sheet S can be cooled by passing the cold-rolled steel sheet S through the cooling device 34.
  • the cooling device 34 cools the cold rolled steel sheet S by water cooling, air cooling, gas cooling, mist cooling, or the like.
  • Step (D) Referring to FIGS. 1 to 3, the cold rolled steel sheet S that has passed through the downstream equipment 30 is finally wound up by a tension reel 50 as a winding device to become a product coil P.
  • the CAL 100 of the first embodiment, the CGL 200 of the second embodiment, and the CGL 300 of the third embodiment are used for cold-rolled steel sheets S that are being passed from the cooling zone 26 to the tension reel 50. It is important to have a magnetic field applying device 60 that applies a steady magnetic field along the width direction of the steel plate S. That is, in the method for manufacturing a steel sheet according to the first, second, and third embodiments, after step (B-2) and before step (D), the cold rolled steel sheet S is Therefore, it is important to include a magnetic field application step in which a steady magnetic field is applied along the width direction of the cold rolled steel sheet S.
  • the hydrogen contained in the cold-rolled steel sheet S during annealing can be sufficiently and efficiently reduced, and a steel sheet with excellent hydrogen embrittlement resistance can be manufactured. Furthermore, since the application of a steady magnetic field is incorporated into the steel plate manufacturing process (inline) using CAL100, CGL200, or CGL300, production efficiency is not impaired. Furthermore, since hydrogen is desorbed not by heating but by applying a steady magnetic field, there is no concern that the mechanical properties of the steel sheet will change.
  • Magnetic field application device 60 Each embodiment of the present invention can be realized by installing a magnetic field application device 60 as shown in FIG. 4 and FIGS. A steady magnetic field is applied to the cold rolled steel sheet S during threading using the device 60.
  • magnetic field application device 60 includes a pair of electromagnets 60A and 60B located on the outer sides of both widthwise ends of cold-rolled steel sheet S, respectively.
  • the electromagnets 60A and 60B each include iron cores 62A and 62B, coils 64A and 64B around which these iron cores 62A and 62B are wound, and a drive power source (not shown) for passing current through these coils 64A and 64B.
  • the electromagnets 60A, 60B can be magnetized and a steady magnetic field can be generated.
  • the axial direction of the coils 64A, 64B coincides with the width direction of the cold rolled steel sheet S.
  • the pair of electromagnets 60A and 60B each have magnetic pole faces 66A and 66B that face the widthwise end face of the cold rolled steel sheet S with a predetermined distance therebetween.
  • the pair of magnetic pole surfaces 66A and 66B are located at the same position in the passing direction of the cold-rolled steel sheet S, and face each other with the cold-rolled steel sheet S in between. Therefore, as shown in FIG. 4, the main magnetic flux of the steady magnetic field generated by the pair of electromagnets 60A and 60B is directed from the magnetic pole face 66A (N pole) to the magnetic pole face 66B (S pole), and in that direction. coincides with the width direction of the cold rolled steel sheet S. Thereby, a steady magnetic field can be applied uniformly along the width direction of the cold rolled steel sheet S. As shown in FIGS.
  • continuous direct current means a direct current whose current value is maintained continuously (preferably constant) rather than in a pulsed manner.
  • a steady magnetic field means a magnetic field that is maintained continuously rather than in a pulsed manner, and includes a magnetic field formed by a stationary magnet and a magnetic field formed by an electromagnet supplied with continuous direct current. including.
  • the installation mode of the pair of electromagnets 60A and 60B is preferably as described above, the installation mode is not limited as long as a steady magnetic field with a magnetic flux component in the width direction of the cold rolled steel sheet S is generated.
  • the configuration of the magnetic field application device 60 is not limited to the pair of electromagnets 60A and 60B as long as a steady magnetic field with a magnetic flux component in the width direction of the cold rolled steel sheet S is generated.
  • the magnetic field applying device 60 may be only one of the electromagnet 60A and the electromagnet 60B. If the magnetic field formed by one of the electromagnets has enough strength to apply a magnetic field along the width direction of the cold rolled steel sheet S to the entire width of the cold rolled steel sheet S, only one of the electromagnets may be used.
  • the position of the magnetic field application device 60 is as long as it can apply a magnetic field to the cold rolled steel sheet S being passed from the cooling zone 26 to the tension reel 50. Not limited.
  • a magnetic field application device 60 can be provided in the cooling zone 26.
  • the magnetic field application step can be performed in step (B-2). Note that the entire magnetic field application device 60 does not need to be located inside the cooling zone 26, and at least the electromagnets 60A and 60B may be located inside the cooling zone 26.
  • the magnetic field application device 60 can be provided at a position where the downstream equipment 30 can apply a magnetic field to the cold rolled steel sheet S being passed through.
  • the magnetic field application step can be performed in step (C). Specifically, (i) between the overaging treatment zone 28 and the exit looper 35, (ii) within the exit looper 35, (iii) between the exit looper 35 and the temper rolling mill 36, (iv) )
  • a magnetic field applying device 60 can be provided between at least one of the temper rolling mill 36 and the tension reel 50.
  • the magnetic field application device 60 may be provided both in the cooling zone 26 and at a position where the downstream equipment 30 can apply a magnetic field to the cold rolled steel sheet S being passed. That is, the magnetic field application step may be performed in both step (B-2) and step (C). Further, the magnetic field application device 60 may be provided in the overaging treatment zone 28 to perform the magnetic field application step during the overaging treatment.
  • the preferred position of the magnetic field application device 60 that is, the preferred implementation of the magnetic field application step.
  • the magnetic field application device 60 can be provided at a first position upstream of the hot-dip galvanizing bath 31 at a position where it can apply a magnetic field to the cold-rolled steel sheet S that is being passed.
  • the magnetic field application step can be performed before step (C-1).
  • the magnetic field application device 60 can be provided in the cooling zone 26.
  • the entire magnetic field application device 60 does not need to be located inside the cooling zone 26, and at least the electromagnets 60A and 60B need only be located inside the cooling zone 26. Furthermore, at least the electromagnets 60A and 60B of the magnetic field application device 60 can be installed inside the snout 29.
  • the magnetic field applying device 60 can be provided at a second position downstream of the hot-dip galvanizing bath 31 where it can apply a magnetic field to the cold-rolled steel sheet S that is being passed.
  • the magnetic field application step can be performed after step (C-1). Specifically, (i) between the hot dip galvanizing bath 31 and the gas wiping device 32, (ii) between the gas wiping device 32 and the alloying furnace 33, (iii) inside the alloying furnace 33, (iv) An air cooling zone between the alloying furnace 33 and the cooling device 34, (v) between the cooling device 34 and the exit looper 35, (vi) inside the exit looper 35, (vii) between the exit looper 35 and temper rolling.
  • a magnetic field applying device 60 can be provided at least one of (viii) between the temper rolling mill 36 and the tension reel 50. In particular, it is preferable to provide the magnetic field application device 60 in the air cooling zone (iv).
  • the magnetic field application device 60 is provided at the first position rather than the second position. That is, the magnetic field application step is preferably performed before step (C-1) rather than after step (C-1). However, the magnetic field application device 60 may be provided at both the first position and the second position. That is, the magnetic field application step may be performed both before and after step (C-1).
  • the magnetic field application device 60 can be provided at a first position upstream of the hot-dip galvanizing bath 31 at a position where it can apply a magnetic field to the cold-rolled steel sheet S that is being passed.
  • the magnetic field application step can be performed before step (C-1).
  • the magnetic field application device 60 can be provided in the cooling zone 26.
  • the entire magnetic field application device 60 does not need to be located inside the cooling zone 26, and at least the electromagnets 60A and 60B need only be located inside the cooling zone 26. Furthermore, at least the electromagnets 60A and 60B of the magnetic field application device 60 can be installed inside the snout 29.
  • the magnetic field applying device 60 can be provided at a second position downstream of the hot-dip galvanizing bath 31 where it can apply a magnetic field to the cold-rolled steel sheet S that is being passed.
  • the magnetic field application step can be performed after step (C-1). Specifically, (i) an air cooling zone between the hot dip galvanizing bath 31 and the gas wiping device 32, (ii) an air cooling zone between the gas wiping device 32 and the cooling device 34, and (iii) a cooling device 34 and the outlet looper. 35, (iv) inside the exit looper 35, (v) between the exit looper 35 and the temper rolling mill 36, and (vi) between the temper rolling mill 36 and the tension reel 50.
  • a magnetic field applying device 60 can be provided in the magnetic field application device 60 . In particular, it is preferable to provide the magnetic field application device 60 in the air cooling zone (ii).
  • the magnetic field application device 60 is provided at the first position rather than the second position. That is, the magnetic field application step is preferably performed before step (C-1) rather than after step (C-1). However, the magnetic field application device 60 may be provided at both the first position and the second position. That is, the magnetic field application step may be performed both before and after step (C-1).
  • the magnetic flux density in the width direction of the cold rolled steel sheet S is preferably 0.1 T or more, It is more preferably 0.2T or more, and even more preferably 0.5T or more.
  • the magnetic flux density in the width direction of the cold rolled steel sheet S is preferably 15T or less, more preferably 14T or less.
  • the magnetic flux density in the width direction of the cold rolled steel sheet S can be adjusted by adjusting the number of turns of the coil and the current value.
  • Magnetic flux density in the width direction of the cold-rolled steel sheet S can be measured in-line by installing a Tesla meter near the width-direction end face of the cold-rolled steel sheet S during threading and near the magnetic field generation surface of the magnetic field application device 60. It can be measured by Alternatively, once the number of turns of the coil in the magnetic field application device 60 and the magnitude of the current value are determined, the "magnetic flux density in the width direction of the cold-rolled steel sheet S" can be determined in advance off-line.
  • the time for applying the magnetic field to the cold rolled steel sheet S is preferably 1 second or more, more preferably 5 seconds or more, and 10 seconds or more. It is more preferable to set it to more than a second.
  • the time for applying the magnetic field to the cold rolled steel sheet S is preferably 3600 seconds or less, more preferably 1800 seconds or less, and even more preferably 900 seconds or less.
  • the time period for which a magnetic field is applied to the cold-rolled steel sheet S means the time period during which a magnetic field is applied to each position in the sheet width direction of the cold-rolled steel sheet S, and each position is connected to a plurality of magnetic field application devices 60.
  • a magnetic field When a magnetic field is applied from , it means the cumulative time.
  • the cumulative time during which each portion of the cold-rolled steel sheet S faces the pair of electromagnets 60A and 60B can be defined as the magnetic field application time.
  • the magnetic field application time can be adjusted by the threading speed of the cold rolled steel sheet S and the position of the magnetic field application device 60 (for example, the number of the pair of electromagnets 60A, 60B shown in FIG. 4 along the threading direction). .
  • the cold rolled steel sheets S supplied to CAL100, CGL200, and CGL300 are not particularly limited.
  • the cold-rolled steel plate S preferably has a thickness of less than 6 mm, and includes, for example, a high-strength steel plate having a tensile strength of 590 MPa or more and a stainless steel plate.
  • composition of cold-rolled steel sheet high-strength steel sheet
  • mass % is simply written as "%”.
  • C 0.030-0.800% C has the effect of increasing the strength of the steel plate. From the viewpoint of obtaining this effect, the amount of C is set to 0.030% or more, preferably 0.080% or more. However, when the amount of C is excessive, the steel sheet becomes extremely brittle regardless of the amount of hydrogen in the steel sheet. Therefore, the amount of C should be 0.800% or less, preferably 0.500% or less.
  • Si 0.01-3.00% Si has the effect of increasing the strength of the steel plate. From the viewpoint of obtaining this effect, the amount of Si is set to 0.01% or more, preferably 0.10% or more. However, when the amount of Si is excessive, the steel plate becomes brittle and its ductility decreases, red scale etc. occur and the surface quality deteriorates, and the plating quality deteriorates. Therefore, the amount of Si should be 3.00% or less, preferably 2.50% or less.
  • Mn 0.01-10.00% Mn has the effect of increasing the strength of the steel plate through solid solution strengthening. From the viewpoint of obtaining this effect, the amount of Mn is set to 0.01% or more, preferably 0.5% or more. However, when the amount of Mn is excessive, unevenness tends to occur in the steel structure due to segregation of Mn, and hydrogen embrittlement originating from the unevenness may become apparent. Therefore, the Mn content should be 10.00% or less, preferably 8.00% or less.
  • P 0.001 ⁇ 0.100%
  • P is an element that has a solid solution strengthening effect and can be added depending on the desired strength. From the viewpoint of obtaining such effects, the amount of P is set to 0.001% or more, preferably 0.003% or more. However, when the amount of P is excessive, weldability deteriorates, and when alloying zinc plating, the alloying speed decreases, impairing the quality of the zinc plating. Therefore, the amount of P should be 0.100% or less, preferably 0.050% or less.
  • S 0.0001-0.0200% S segregates at grain boundaries and makes the steel brittle during hot working, and also exists as a sulfide and reduces local deformability. Therefore, the amount of S is set to 0.0200% or less, preferably 0.0100% or less, and more preferably 0.0050% or less. On the other hand, due to production technology constraints, the S content is set to 0.0001% or more.
  • N 0.0005-0.0100%
  • N is an element that deteriorates the aging resistance of steel. Therefore, the amount of N is set to 0.0100% or less, preferably 0.0070% or less. The smaller the amount of N, the more preferable it is, but due to constraints on production technology, the amount of N is set to 0.0005% or more, preferably 0.0010% or more.
  • Al acts as a deoxidizing agent and is an element effective in improving the cleanliness of steel. From the viewpoint of obtaining this effect, the amount of Al is set to 0.001% or more, preferably 0.010% or more. However, if the amount of Al is excessive, cracks may occur during continuous casting. Therefore, the amount of Al should be 2.000% or less, preferably 1.200% or less.
  • the remainder other than the above components is Fe and inevitable impurities. However, it may optionally contain at least one element selected from the following.
  • Ti 0.200% or less Ti contributes to increasing the strength of the steel sheet through precipitation strengthening of the steel and fine grain strengthening by suppressing the growth of ferrite crystal grains. Therefore, when adding Ti, the amount of Ti is preferably 0.005% or more, more preferably 0.010% or more. However, when the amount of Ti is excessive, a large amount of carbonitrides may precipitate, leading to a decrease in formability. Therefore, when adding Ti, the amount of Ti should be 0.200% or less, preferably 0.100% or less.
  • Nb 0.200% or less
  • V 0.500% or less
  • W 0.500% or less
  • Nb, V, and W are effective for precipitation strengthening of steel. Therefore, when adding Nb, V, and W, the content of each element is preferably 0.005% or more, more preferably 0.010% or more. However, if each content is excessive, a large amount of carbonitrides may precipitate and formability may deteriorate. Therefore, when adding Nb, the amount of Nb should be 0.200% or less, preferably 0.100% or less. When V and W are added, the content of each element is 0.500% or less, preferably 0.300% or less.
  • B 0.0050% or less B is effective in strengthening grain boundaries and increasing the strength of steel sheets. Therefore, when adding B, the amount of B is preferably 0.0003% or more. However, when the amount of B is excessive, moldability may deteriorate. Therefore, when adding B, the amount of B should be 0.0050% or less, preferably 0.0030% or less.
  • Ni 1.000% or less
  • Ni is an element that increases the strength of steel through solid solution strengthening. Therefore, when adding Ni, the amount of Ni is preferably 0.005% or more. However, when the amount of Ni is excessive, the area ratio of hard martensite becomes excessive, which increases the number of microvoids at the grain boundaries of martensite during a tensile test, and further propagates cracks, resulting in ductile may decrease. Therefore, when adding Ni, the amount of Ni should be 1.000% or less.
  • Cr 1.000% or less
  • Mo 1.000% or less Cr and Mo have the effect of improving the balance between strength and formability. Therefore, when adding Cr and Mo, the content of each element is preferably 0.005% or more. However, if each content is excessive, the area ratio of hard martensite becomes excessive, and during the tensile test, microvoids at grain boundaries of martensite increase, and crack propagation progresses. Ductility may decrease. Therefore, when adding Cr and Mo, the content of each element should be 1.000% or less.
  • Cu 1.000% or less
  • Cu is an element effective in strengthening steel. Therefore, when adding Cu, the amount of Cu is preferably 0.005% or more. However, when the amount of Cu is excessive, the area ratio of hard martensite becomes excessive, microvoids at grain boundaries of tempered martensite increase during a tensile test, and crack propagation progresses. Ductility may decrease. Therefore, when adding Cu, the amount of Cu is 1.000% or less.
  • Sn 0.200% or less
  • Sb 0.200% or less
  • Sn and Sb suppress decarburization in an area of several tens of ⁇ m on the steel plate surface layer caused by nitriding and oxidation of the steel plate surface, and improve strength and material stability. It is effective in ensuring sex. Therefore, when adding Sn and Sb, the content of each element is preferably 0.002% or more. However, if each content is excessive, toughness may decrease. Therefore, when adding Sn and Sb, the content of each element should be 0.200% or less.
  • Ta 0.100% or less Ta, like Ti and Nb, generates alloy carbides and alloy carbonitrides and contributes to high strength.
  • Nb carbide and Nb carbonitride by partially forming a solid solution in Nb carbide and Nb carbonitride to form composite precipitates such as (Nb, Ta) (C, N), coarsening of the precipitates is significantly suppressed and precipitation It is thought that this has the effect of stabilizing the contribution to strength due to reinforcement. Therefore, when adding Ta, the amount of Ta is preferably 0.001% or more. However, even if Ta is added excessively, the precipitate stabilizing effect may become saturated, and the alloy cost also increases. Therefore, when adding Ta, the amount of Ta should be 0.100% or less.
  • Ca 0.0050% or less
  • Mg 0.0050% or less
  • Zr 0.1000% or less
  • REM Rare Earth Metal
  • Ca, Mg, Zr and REM change the shape of the sulfide. It is an effective element for spheroidizing and improving the adverse effects of sulfide on formability.
  • the content of each element is preferably 0.0005% or more. However, when each content is excessive, inclusions and the like increase, and surface and internal defects may occur. Therefore, when adding these elements, the content of each element should be 0.0050% or less.
  • composition of cold rolled steel sheet stainless steel sheet
  • mass % is simply written as “%”.
  • C 0.001-0.400%
  • C is an essential element for obtaining high strength in stainless steel. However, during tempering in steel manufacturing, it combines with Cr and precipitates as carbides, which deteriorates the corrosion resistance and toughness of the steel. If the C content is less than 0.001%, sufficient strength cannot be obtained, and if it exceeds 0.400%, the deterioration becomes noticeable. Therefore, the amount of C is set to 0.001 to 0.400%.
  • Si 0.01 ⁇ 2.00%
  • Si is an element useful as a deoxidizing agent. From the viewpoint of obtaining this effect, the amount of Si is set to 0.01% or more. However, when the amount of Si is excessive, Si dissolved in the steel deteriorates the workability of the steel. Therefore, Si should be 2.00% or less.
  • Mn 0.01-5.00% Mn has the effect of increasing the strength of steel. From the viewpoint of obtaining this effect, the amount of Mn is set to 0.01% or more. However, when the amount of Mn is excessive, the workability of the steel decreases. Therefore, the Mn content is set to 5.00% or less.
  • P is an element that promotes grain boundary destruction due to grain boundary segregation. Therefore, it is desirable that the amount of P be as low as possible, and should be 0.100% or less, preferably 0.030% or less, and more preferably 0.020% or less. On the other hand, due to production technology constraints, the amount of P is set to 0.001% or more.
  • S 0.0001-0.0200%
  • S exists as sulfide inclusions such as MnS and reduces ductility, corrosion resistance, etc. Therefore, the S amount is desirably low, and is set to 0.0200% or less, preferably 0.0100% or less, and more preferably 0.0050% or less.
  • the S content is set to 0.0001% or more.
  • Cr 9.0 ⁇ 28.0%
  • Cr is a basic element constituting stainless steel, and is also an important element that exhibits corrosion resistance.
  • the Cr content is set to 9.0 to 28.0%.
  • Ni 0.01-40.0% Ni is an element that improves the corrosion resistance of stainless steel. If the amount of Ni is less than 0.01%, the effect will not be fully exhibited. On the other hand, when the amount of Ni is excessive, not only the formability is deteriorated but also stress corrosion cracking is likely to occur. Therefore, the Ni amount is set to 0.01 to 40.0%.
  • N 0.0005-0.500% N is an element harmful to improving the corrosion resistance of stainless steel. Therefore, the amount of N is set to 0.500% or less, preferably 0.200% or less. The smaller the amount of N, the more preferable it is, but due to constraints on production technology, the amount of N is set to 0.0005% or more.
  • Al 0.001-3.000%
  • Al has the effect of suppressing the peeling of oxide scale. From the viewpoint of obtaining these effects, the amount of Al is set to 0.001% or more. However, when the amount of Al is excessive, a decrease in elongation and a deterioration in surface quality occur. Therefore, the amount of Al is set to 3.000% or less.
  • the remainder other than the above components is Fe and inevitable impurities. However, it may optionally contain at least one element selected from the following.
  • Ti 0.500% or less Ti combines with C, N, and S to improve corrosion resistance, intergranular corrosion resistance, and deep drawability. However, when the amount of Ti exceeds 0.500%, the toughness deteriorates due to solid solution Ti. Therefore, when adding Ti, the amount of Ti should be 0.500% or less.
  • Nb 0.500% or less Like Ti, Nb combines with C, N, and S to improve corrosion resistance, intergranular corrosion resistance, and deep drawability. In addition to improving workability and high-temperature strength, it also suppresses crevice corrosion and promotes repassivation. However, excessive addition causes hardening and deteriorates moldability. Therefore, when adding Nb, the amount of Nb should be 0.500% or less.
  • V 0.500% or less V suppresses crevice corrosion. However, excessive addition deteriorates moldability. Therefore, when adding V, the amount of V should be 0.500% or less.
  • W 2.000% or less W contributes to improving corrosion resistance and high temperature strength.
  • excessive addition leads to deterioration of toughness and increase in cost during production of steel sheets. Therefore, when adding W, the amount of W should be 2.000% or less.
  • B 0.0050% or less B improves the secondary workability of the product by segregating at grain boundaries. However, excessive addition results in deterioration of workability and corrosion resistance. Therefore, when adding B, the amount of B should be 0.0050% or less.
  • Mo 2.000% or less
  • Mo is an element that improves corrosion resistance and particularly suppresses crevice corrosion.
  • excessive addition deteriorates moldability. Therefore, when adding Mo, the amount of Mo should be 2.000% or less.
  • Cu 3.000% or less
  • Cu is an austenite stabilizing element and is effective in refining crystal grains through phase transformation. It also inhibits crevice corrosion and promotes repassivation. However, excessive addition deteriorates toughness and formability. Therefore, when adding Cu, the amount of Cu is 3.000% or less.
  • Sn 0.500% or less Sn contributes to improving corrosion resistance and high temperature strength. However, excessive addition may cause slab cracking during steel sheet production. Therefore, when adding Sn, the amount of Sn should be 0.500% or less.
  • Sb 0.200% or less Sb segregates at grain boundaries and has the effect of increasing high-temperature strength. However, excessive addition may cause cracks during welding due to Sb segregation. Therefore, when adding Sb, the amount of Sb should be 0.200% or less.
  • Ta 0.100% or less Ta combines with C and N and contributes to improving toughness. However, if excessively added, the effect becomes saturated, leading to an increase in manufacturing costs. Therefore, when adding Ta, the amount of Ta was set to 0.100% or less.
  • Ca 0.0050% or less
  • Mg 0.0050% or less
  • Zr 0.1000% or less
  • REM Rare Earth Metal
  • Ca, Mg, Zr and REM change the shape of the sulfide. It is an effective element for spheroidizing and improving the adverse effects of sulfide on formability.
  • the content of each element is preferably 0.0005% or more. However, when each content is excessive, inclusions and the like increase, and surface and internal defects may occur. Therefore, when adding these elements, the content of each element should be 0.0050% or less.
  • the amount of diffusible hydrogen in the product coil is preferably 0.50 mass ppm or less, more preferably 0.30 mass ppm or less, and 0.50 mass ppm or less. More preferably, the content is 20 mass ppm or less. Note that there is no particular lower limit to the amount of diffusible hydrogen in the product coil, but due to constraints on production technology, the amount of diffusible hydrogen in the product coil may be 0.01 mass ppm or more.
  • the method for measuring the amount of diffusible hydrogen in the product coil is as follows.
  • a test piece with a length of 30 mm and a width of 5 mm is taken from the product coil.
  • the hot-dip galvanized layer or alloyed hot-dip galvanized layer of the test piece is removed by grinding or alkali.
  • the amount of hydrogen released from the test piece is measured by thermal desorption spectrometry (TDS). Specifically, the test piece was continuously heated from room temperature to 300°C at a heating rate of 200°C/h, then cooled to room temperature, and the cumulative amount of hydrogen released from the test piece from room temperature to 210°C was measured. , the amount of diffusible hydrogen in the product coil.
  • a steel having a composition having the elements shown in Table 1 with the remainder consisting of Fe and unavoidable impurities was melted in a converter and made into a slab by a continuous casting method. The obtained slab was hot rolled and cold rolled to obtain a cold rolled coil.
  • some standards produce product coils of cold-rolled annealed steel (CR) by CAL as shown in Figure 1, while other standards produce product coils of cold-rolled annealed steel (CR) without heat alloying by CGL as shown in Figure 2.
  • production coils of hot-dip galvanized steel (GI) were produced, and for the remaining levels, production coils of alloyed galvanized steel (GA) were produced by CGL shown in FIG.
  • Magnetic flux densities (in the sheet width direction) shown in Table 2 are applied to the cold-rolled steel sheet during threading using the magnetic field application device shown in FIGS. 4 and 5 (A) and (B).
  • a steady magnetic field was applied along the width direction of the cold-rolled steel sheet under the following conditions: and magnetic field application time.
  • Magnetic field application location indicates the area where the magnetic field application process in CAL or CGL was performed, that is, the location where the magnetic field application device was installed.
  • (B-2)" means that in CAL and CGL, a magnetic field application device was installed in the cooling zone, and the magnetic field application process was performed in the cooling zone of step (B-2).
  • (C) means that the magnetic field application device is installed at a position where it can apply a magnetic field to the cold-rolled steel sheet being passed through the downstream equipment, and is located downstream of the cooling zone and upstream of the tension reel. Specifically, (i) between the overaging treatment zone 28 and the outlet looper 35, (ii) inside the outlet looper 35, (iii) between the outlet looper 35 and the temper rolling mill 36, ( iv) This means that a magnetic field application device is installed at at least one location between the temper rolling mill 36 and the tension reel 50. That is, "(C)” means that in CAL, a magnetic field application step was performed at step (C), specifically, at least one of the above (i) to (iv).
  • Before (C-1) is a position downstream of the cooling zone and upstream of the hot-dip galvanizing bath in CGL, specifically, a magnetic field application device is installed in the snout 29, and from step (B-2) This means that the magnetic field application step was performed after and before step (C-1).
  • "After (C-1)” refers to a position downstream of the hot-dip galvanizing bath and upstream of the tension reel in the CGL, specifically, (i) between the hot-dip galvanizing bath 31 and the gas wiping device 32; ii) between the gas wiping device 32 and the alloying furnace 33; (iii) within the alloying furnace 33; (iv) between the alloying furnace 33 and the cooling device 34; (v) between the cooling device 34 and the outlet.
  • the tensile test was conducted in accordance with JIS Z 2241 (2011) using a JIS No. 5 test piece whose tensile direction was perpendicular to the rolling direction of the steel plate, and the TS (tensile strength) and EL (total elongation) was measured.
  • the hydrogen embrittlement resistance was evaluated from the above tensile test as follows. When the value obtained by dividing the EL of the steel sheet after applying the magnetic field measured above by the EL' when the hydrogen content in the steel of the same steel sheet is 0.00 mass ppm is 0.70 or more, the hydrogen embrittlement resistance is good. It was determined that In addition, EL' reduces the hydrogen in the steel by leaving the same steel plate in the atmosphere for a long time, and then after confirming that the amount of hydrogen in the steel is 0.00 mass ppm by TDS. , was measured by performing a tensile test.
  • steel sheets with excellent hydrogen embrittlement resistance can be manufactured without impairing production efficiency or changing mechanical properties. be able to.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Organic Chemistry (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Oil, Petroleum & Natural Gas (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
  • Coating With Molten Metal (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
PCT/JP2023/007690 2022-03-25 2023-03-01 連続焼鈍装置及び連続溶融亜鉛めっき装置、並びに鋼板の製造方法 Ceased WO2023181820A1 (ja)

Priority Applications (6)

Application Number Priority Date Filing Date Title
JP2023555692A JP7380965B1 (ja) 2022-03-25 2023-03-01 連続焼鈍装置及び連続溶融亜鉛めっき装置、並びに鋼板の製造方法
CN202380029116.5A CN118946671A (zh) 2022-03-25 2023-03-01 连续退火装置和连续热浸镀锌装置以及钢板的制造方法
MX2024011171A MX2024011171A (es) 2022-03-25 2023-03-01 Linea continua de recocido, linea continua de galvanizado por inmersion en caliente y metodo para producir laminas de acero.
KR1020247033711A KR20240162098A (ko) 2022-03-25 2023-03-01 연속 어닐링 장치 및 연속 용융 아연 도금 장치, 그리고 강판의 제조 방법
US18/844,156 US20250171872A1 (en) 2022-03-25 2023-03-01 Continuous annealing line, continuous hot-dip galvanizing line, and method of producing steel sheet
EP23774419.8A EP4474497A4 (en) 2022-03-25 2023-03-01 CONTINUOUS ANNEALING APPARATUS, CONTINUOUS HOT-DIP GALVANIZING APPARATUS AND METHOD FOR PRODUCING STEEL SHEET

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2022050835 2022-03-25
JP2022-050835 2022-03-25

Publications (1)

Publication Number Publication Date
WO2023181820A1 true WO2023181820A1 (ja) 2023-09-28

Family

ID=88100653

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2023/007690 Ceased WO2023181820A1 (ja) 2022-03-25 2023-03-01 連続焼鈍装置及び連続溶融亜鉛めっき装置、並びに鋼板の製造方法

Country Status (7)

Country Link
US (1) US20250171872A1 (https=)
EP (1) EP4474497A4 (https=)
JP (1) JP7380965B1 (https=)
KR (1) KR20240162098A (https=)
CN (1) CN118946671A (https=)
MX (1) MX2024011171A (https=)
WO (1) WO2023181820A1 (https=)

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR20240144275A (ko) * 2022-03-25 2024-10-02 제이에프이 스틸 가부시키가이샤 탈수소 장치 및 강판의 제조 시스템, 그리고 강판의 제조 방법

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS56169719A (en) * 1980-06-02 1981-12-26 Nippon Steel Corp Continuous vibrating method for metal plate
JPS6312555A (ja) * 1986-07-01 1988-01-19 Mitsubishi Heavy Ind Ltd 搬送金属板のステアリング装置
JPH10130739A (ja) * 1996-10-28 1998-05-19 Fuji Photo Film Co Ltd 磁場熱処理方法及び装置
JP2010185101A (ja) 2009-02-12 2010-08-26 Jfe Steel Corp 連続焼鈍炉のガスジェット冷却装置
WO2019188642A1 (ja) 2018-03-30 2019-10-03 Ｊｆｅスチール株式会社 高強度鋼板およびその製造方法
WO2023286440A1 (ja) * 2021-07-14 2023-01-19 Ｊｆｅスチール株式会社 連続焼鈍装置及び連続溶融亜鉛めっき装置、並びに鋼板の製造方法

Family Cites Families (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3661116A (en) * 1970-11-23 1972-05-09 Bethlehem Steel Corp Magnetic stabilizing means for strip
US4655166A (en) * 1979-12-26 1987-04-07 Hitachi, Ltd. Apparatus for preventing oscillation of running strip
KR930000171A (ko) * 1991-06-25 1993-01-15 사이또오 히로시 강대의 연속 이동방법
JP7259974B2 (ja) * 2020-07-14 2023-04-18 Ｊｆｅスチール株式会社 連続焼鈍装置及び連続溶融亜鉛めっき装置、並びに鋼板の製造方法

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS56169719A (en) * 1980-06-02 1981-12-26 Nippon Steel Corp Continuous vibrating method for metal plate
JPS6312555A (ja) * 1986-07-01 1988-01-19 Mitsubishi Heavy Ind Ltd 搬送金属板のステアリング装置
JPH10130739A (ja) * 1996-10-28 1998-05-19 Fuji Photo Film Co Ltd 磁場熱処理方法及び装置
JP2010185101A (ja) 2009-02-12 2010-08-26 Jfe Steel Corp 連続焼鈍炉のガスジェット冷却装置
WO2019188642A1 (ja) 2018-03-30 2019-10-03 Ｊｆｅスチール株式会社 高強度鋼板およびその製造方法
WO2023286440A1 (ja) * 2021-07-14 2023-01-19 Ｊｆｅスチール株式会社 連続焼鈍装置及び連続溶融亜鉛めっき装置、並びに鋼板の製造方法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of EP4474497A4

Also Published As

Publication number Publication date
MX2024011171A (es) 2024-09-23
JPWO2023181820A1 (https=) 2023-09-28
US20250171872A1 (en) 2025-05-29
EP4474497A1 (en) 2024-12-11
CN118946671A (zh) 2024-11-12
JP7380965B1 (ja) 2023-11-15
KR20240162098A (ko) 2024-11-14
EP4474497A4 (en) 2025-05-28

Similar Documents

Publication Publication Date Title
JP7388570B2 (ja) 連続焼鈍装置及び連続溶融亜鉛めっき装置、並びに鋼板の製造方法
KR101570629B1 (ko) 내충격 특성이 우수한 고강도 용융 아연 도금 강판 및 그 제조 방법, 및, 고강도 합금화 용융 아연 도금 강판 및 그 제조 방법
JP5223360B2 (ja) 成形性に優れた高強度溶融亜鉛めっき鋼板およびその製造方法
KR102928754B1 (ko) 연속 어닐링 장치 및 연속 용융 아연 도금 장치, 그리고 강판의 제조 방법
KR101605980B1 (ko) 내지연 파괴 특성이 우수한 고강도 용융 아연 도금 강판 및 그 제조 방법
EP2460901B1 (en) High-strength steel sheet, and process for production thereof
JP5793971B2 (ja) 材質安定性、加工性およびめっき外観に優れた高強度溶融亜鉛めっき鋼板の製造方法
JP4072090B2 (ja) 伸びフランジ成形性に優れた高強度鋼板およびその製造方法
JP5786318B2 (ja) 疲労特性と穴拡げ性に優れた高強度溶融亜鉛めっき鋼板およびその製造方法
JP5370244B2 (ja) 高強度溶融亜鉛めっき鋼板の製造方法
JP4050991B2 (ja) 伸びフランジ成形性に優れた高強度鋼板およびその製造方法
JP2010255113A (ja) 高強度溶融亜鉛めっき鋼板およびその製造方法
JP7380965B1 (ja) 連続焼鈍装置及び連続溶融亜鉛めっき装置、並びに鋼板の製造方法
JP5672743B2 (ja) 高強度溶融亜鉛めっき鋼板およびその製造方法
JP2008248358A (ja) 高強度溶融亜鉛めっき鋼板
JP7384296B2 (ja) 脱水素装置及び鋼板の製造システム、並びに鋼板の製造方法
EP4474490A1 (en) Dehydrogenation device, system for manufacturing steel sheet, and method for manufacturing steel sheet
JP5971155B2 (ja) 高強度溶融亜鉛めっき鋼板の製造方法および高強度溶融亜鉛めっき鋼板
JP5962544B2 (ja) 高強度溶融亜鉛めっき鋼板の製造方法および高強度溶融亜鉛めっき鋼板
JP2009185370A (ja) 高張力溶融亜鉛めっき鋼板およびその製造方法

Legal Events

Date Code Title Description
WWE Wipo information: entry into national phase

Ref document number: 2023555692

Country of ref document: JP

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

Ref document number: 23774419

Country of ref document: EP

Kind code of ref document: A1

WWE Wipo information: entry into national phase

Ref document number: 202417066620

Country of ref document: IN

WWE Wipo information: entry into national phase

Ref document number: 2023774419

Country of ref document: EP

WWE Wipo information: entry into national phase

Ref document number: 18844156

Country of ref document: US

ENP Entry into the national phase

Ref document number: 2023774419

Country of ref document: EP

Effective date: 20240904

WWE Wipo information: entry into national phase

Ref document number: MX/A/2024/011171

Country of ref document: MX

WWE Wipo information: entry into national phase

Ref document number: 202380029116.5

Country of ref document: CN

WWE Wipo information: entry into national phase

Ref document number: 2401006202

Country of ref document: TH

ENP Entry into the national phase

Ref document number: 20247033711

Country of ref document: KR

Kind code of ref document: A

WWE Wipo information: entry into national phase

Ref document number: 1020247033711

Country of ref document: KR

NENP Non-entry into the national phase

Ref country code: DE

WWP Wipo information: published in national office

Ref document number: 18844156

Country of ref document: US