WO2023075287A1 - Acier inoxydable ferritique et son procédé de fabrication - Google Patents

Acier inoxydable ferritique et son procédé de fabrication Download PDF

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WO2023075287A1
WO2023075287A1 PCT/KR2022/015994 KR2022015994W WO2023075287A1 WO 2023075287 A1 WO2023075287 A1 WO 2023075287A1 KR 2022015994 W KR2022015994 W KR 2022015994W WO 2023075287 A1 WO2023075287 A1 WO 2023075287A1
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hot
rolled sheet
ferritic stainless
stainless steel
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PCT/KR2022/015994
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English (en)
Korean (ko)
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박수호
전지웅
유지현
김회훈
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주식회사 포스코
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Priority to CN202280071865.XA priority Critical patent/CN118159680A/zh
Publication of WO2023075287A1 publication Critical patent/WO2023075287A1/fr

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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C47/00—Winding-up, coiling or winding-off metal wire, metal band or other flexible metal material characterised by features relevant to metal processing only
    • B21C47/02—Winding-up or coiling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • 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
    • C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
    • C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
    • C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
    • 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
    • C21D2211/005—Ferrite

Definitions

  • the present invention relates to ferritic stainless steel and a manufacturing method thereof, and more particularly, to a ferritic stainless steel having improved elongation while omitting upper annealing and a manufacturing method thereof.
  • Ferritic stainless steel is a steel material with high price competitiveness compared to austenitic stainless steel because it contains fewer expensive alloy elements. Ferritic stainless steel has excellent corrosion resistance and is widely used for building materials, transportation equipment, home appliances, and kitchen equipment.
  • 430 series hot rolled steel undergoes a box annealing process, and the box annealing process is performed for 35 to 50 hours at 800 to 850 ° C., which is a phase transformation temperature from austenite to ferrite.
  • the purpose of the phase annealing is to recrystallize the deformed structure formed during hot rolling and to decompose the austenite phase into a ferrite phase and carbides.
  • the upper annealing process has problems in that productivity is lowered due to long-term heat treatment as well as high energy consumption. Therefore, development of continuous annealing manufacturing technology that can reduce manufacturing cost due to energy reduction and productivity improvement has been promoted.
  • Patent Document 1 it is disclosed that one or more passes are performed at a reduction rate of 20% or more per rough rolling pass during hot rolling for 430 steel designed to allow continuous annealing, and in Patent Document 2, finishing rolling start temperature It has been disclosed that the quality characteristics are good without occurrence of sticking defects when operating at 950 ° C or higher and the coiling temperature is 650 ° C or lower.
  • the elongation may be lowered due to the formation of fine Cr carbide precipitated during cooling after hot rolling.
  • Patent Document 1 Japan Patent Publication Office 57-70230 (Publication Date: 1997.02.10.)
  • Patent Document 2 Japanese Patent Publication No. 57-155326 (published on December 22, 1989)
  • An object of the present invention for solving the above problems is to provide a ferritic stainless steel with improved elongation and a manufacturing method thereof, while omitting the upper annealing and performing the continuous annealing.
  • Ferritic stainless steel in weight%, C: 0.01% or more and 0.1% or less, Si: 0.01% or more and 1.0% or less, Mn: 0.01% or more and 1.5% or less, P: more than 0% 0.05% or less, S: more than 0% and 0.005% or less, Cr: 13.0% or more and 18.0% or less, N: 0.005% or more and 0.1% or less, Al: 0.005% or more and 0.2% or less, Ni: 0.05% or more and 0.25% or less, the balance It includes Fe (iron) and other unavoidable impurities, and may have an Ac1 value defined in Equation (1) below of 920 or more and less than 990.
  • ferritic stainless steel according to an embodiment of the present invention may have an elongation of 27% or more.
  • C 0.01% or more and 0.1% or less
  • Si 0.01% or more and 1.0% or less
  • Mn 0.01% or more and 1.5% or less
  • P More than 0% and 0.05% or less
  • S More than 0% and 0.005% or less
  • Cr More than 0% and 0.005% or less
  • Cr More than 0% and 0.005% or less
  • N More than 0% and 0.005% or less
  • Al More than 0.005% or more and 0.2% or less
  • Equation (2) 840 ⁇ T (HRA, °C) ⁇ Ac1 - 20
  • Equation (3) 870 ⁇ T (CRA, °C) ⁇ Ac1 - 20
  • the reheating step may be performed at 1100 to 1250 ° C.
  • the hot rolling may be performed at a finish rolling completion temperature of 800 to 950 ° C.
  • the winding may be performed at 750 to 850 ° C.
  • the hot-rolled sheet annealing and pickling and the cold-rolled sheet annealing and pickling may be performed for 30 seconds or more and 10 minutes or less.
  • the cooling after annealing of the hot-rolled sheet and the cooling after annealing of the cold-rolled sheet may be performed at a cooling rate of 10 to 50 ° C./s.
  • the cold rolling may be performed at a reduction ratio of 60 to 90%.
  • a ferritic stainless steel with improved elongation and a manufacturing method thereof by controlling the annealing heat treatment temperature while omitting the upper annealing and performing the continuous annealing.
  • 1 is a graph showing an annealing heat treatment temperature range that can secure an elongation of 27% or more.
  • Ferritic stainless steel in weight%, C: 0.01% or more and 0.1% or less, Si: 0.01% or more and 1.0% or less, Mn: 0.01% or more and 1.5% or less, P: more than 0% 0.05% or less, S: more than 0% and 0.005% or less, Cr: 13.0% or more and 18.0% or less, N: 0.005% or more and 0.1% or less, Al: 0.005% or more and 0.2% or less, Ni: 0.05% or more and 0.25% or less, the balance It includes Fe (iron) and other unavoidable impurities, and may have an Ac1 value defined in Equation (1) below of 920 or more and less than 990.
  • Ferritic stainless steel according to an embodiment of the present invention in weight%, C: 0.01% or more and 0.1% or less, Si: 0.01% or more and 1.0% or less, Mn: 0.01% or more and 1.5% or less, P: more than 0% 0.05% or less, S: more than 0% and 0.005% or less, Cr: 13.0% or more and 18.0% or less, N: 0.005% or more and 0.1% or less, Al: 0.005% or more and 0.2% or less, Ni: 0.05% or more and 0.25% or less, the balance Fe (iron) and other unavoidable impurities may be included.
  • the content of C (carbon) may be 0.01% or more and 0.1% or less.
  • C is a strong austenite phase stabilizing element and is an effective element for increasing material strength by solid solution strengthening. Considering this, C may be added in an amount of 0.01% or more. However, when the content of C is excessive, the strength is excessively increased, and the elongation, toughness and the like of the steel material are reduced. Considering this, the upper limit of the C content may be limited to 0.1%.
  • the content of Si may be 0.01% or more and 1.0% or less.
  • Si is an element added as a deoxidizer in the steelmaking step, and is effective in improving yield strength and corrosion resistance.
  • Si is an element that can enhance the stability of the ferrite phase. Considering this, Si may be added in an amount of 0.01% or more. However, when the content of Si is excessive, elongation and toughness may be deteriorated by causing hardening of the material. Considering this, the upper limit of the Si content may be limited to 1.0%.
  • the content of Mn may be 0.01% or more and 1.5% or less.
  • Mn is an element effective in improving corrosion resistance. Considering this, Mn may be added in an amount of 0.01% or more, preferably 0.2% or more. However, when the content of Mn is excessive, inclusions (MnS) are formed to deteriorate hot workability, ductility and toughness of steel materials. Considering this, the upper limit of the Mn content may be limited to 1.5%, more preferably 1.0%.
  • the content of P (phosphorus) may be more than 0% and 0.05% or less.
  • P is an impurity inevitably contained in steel, and is an element that causes intergranular corrosion during pickling or impairs hot workability. Therefore, it is desirable to control the content of P as low as possible. Considering this, the upper limit of the P content may be limited to 0.05%.
  • the content of S may be greater than 0% and less than or equal to 0.005%.
  • S is an impurity inevitably contained in steel, and is an element that is segregated at grain boundaries and causes impairing hot workability. Therefore, it is desirable to control the content of S as low as possible. Considering this, the upper limit of the S content may be limited to 0.005%.
  • the content of Cr (chromium) may be 13.0% or more and 18.0% or less.
  • Cr is an element that improves corrosion resistance by forming a passivation film in an oxidizing environment. In consideration of this, 13.0% or more of Cr may be added. However, when the content of Cr is excessive, it promotes the formation of delta ( ⁇ ) ferrite in the slab, thereby reducing the elongation and impact toughness, and increasing the manufacturing cost. Considering this, the upper limit of the Cr content may be limited to 18.0%.
  • the content of N may be 0.005% or more and 0.1% or less.
  • N is an interstitial element that is effective in improving the yield strength of steel materials through a solid solution strengthening effect. Considering this, N may be added in an amount of 0.005% or more. However, when the content of N is excessive, impact toughness and moldability may be inferior. Considering this, the upper limit of the N content may be limited to 0.1%.
  • the content of Al may be 0.005% or more and 0.2% or less.
  • Al is a strong deoxidizer and is an element that lowers the oxygen content in molten steel. Considering this, Al may be added in an amount of 0.005% or more. However, when the content of Al is excessive, non-metallic inclusions may increase, causing sliver defects in the cold-rolled strip and deteriorating weldability. Considering this, the upper limit of the Al content may be limited to 0.2%, more preferably 0.15% or less.
  • the content of Ni (nickel) may be 0.05% or more and 0.25% or less.
  • Ni has the effect of softening steel materials. Considering this, Ni may be added in an amount of 0.05% or more. However, when the Ni content is excessive, there is a problem of increasing cost. Considering this, the upper limit of the Ni content may be limited to 0.25%.
  • the remaining component of the present invention is iron (Fe).
  • Fe iron
  • the Ac1 value defined in Equation (1) below may be 920 or more and less than 990.
  • Ac1 refers to the temperature at which the austenite phase transforms into a ferrite phase.
  • the elongation is improved by controlling the annealing heat treatment temperature based on the Ac1 value calculated through the alloy composition and component range design.
  • the alloy composition and component range can be designed so that the calculated value of Ac1 is 920 or more.
  • the alloy composition and component range can be designed so that the calculated value of Ac1 is less than 990.
  • the ferritic stainless steel according to an embodiment of the present invention may have an elongation of 27% or more.
  • the manufacturing method of ferritic stainless steel according to an embodiment of the present invention in weight%, C: 0.01% or more and 0.1% or less, Si: 0.01% or more 1.0% or less, Mn: 0.01% or more and 1.5% or less, P: 0% or more and 0.05% or less, S: 0% or more and 0.005% or less, Cr: 13.0% or more and 18.0% or less, N: 0.005% or more and 0.1% or less, Al : 0.005% or more and 0.2% or less, Ni: 0.05% or more and 0.25% or less, the balance including Fe (iron) and other unavoidable impurities, and having an Ac1 value defined in Equation (1) below of 920 or more and less than 990, manufacturing a slab step; reheating the slab; After hot rolling the reheated slab, winding it to produce a hot-rolled steel; The step of annealing the hot-rolled steel at a hot-rolled sheet annealing heat treatment temperature T (HRA, ° C) that satisfies
  • Equation (2) 840 ⁇ T (HRA, °C) ⁇ Ac1 - 20
  • Equation (3) 870 ⁇ T (CRA, °C) ⁇ Ac1 - 20
  • a series of hot rolling, hot-rolled sheet annealing and pickling, cold rolling, cold-rolled sheet annealing and pickling may be performed.
  • the slab may be hot rolled at a reheating temperature of 1100 to 1250 ° C.
  • the reheating temperature of the slab may be 1100 ° C or higher. However, if the reheating temperature is too high, the grain diameter of the slab coarsens and the strength may deteriorate. Considering this, the upper limit of the reheating temperature of the slab may be limited to 1250 ° C.
  • the hot rolling may be performed at a finish rolling completion temperature of 800 to 950 °C.
  • the finish rolling completion temperature When the finish rolling completion temperature is low, the rolling load may increase and productivity may decrease. In consideration of this, the finish rolling completion temperature may be 800°C or higher. However, if the finish rolling completion temperature is too high, the grain size may increase and the strength may decrease. In consideration of this, the finish rolling completion temperature may be controlled to 950° C. or less.
  • the winding may be performed at 750 to 850 °C.
  • the winding temperature When the winding temperature is low, it may be difficult to control the shape of the coil, and when the winding temperature is too high, defects may occur in a subsequent process due to continuous phase transformation after winding. Considering this, the winding temperature may be set to 750 to 850 °C.
  • the hot-rolled steel material may be subjected to hot-rolled sheet annealing at a hot-rolled sheet annealing heat treatment temperature T (HRA, ° C.) that satisfies Equation (2) below.
  • Equation (2) 840 ⁇ T (HRA, °C) ⁇ Ac1 - 20
  • the hot-rolled sheet annealing heat treatment temperature T (HRA, °C) When the hot-rolled sheet annealing heat treatment temperature T (HRA, °C) is low, recrystallization is not sufficiently performed. However, since cold-rolled sheet annealing is performed as a post-process, it can proceed at a relatively low temperature. Considering this, the hot-rolled sheet annealing heat treatment temperature T (HRA, °C) may be 840 °C or more. However, when the hot-rolled sheet annealing heat treatment temperature T (HRA, °C) is equal to or higher than the Ac1 temperature, an austenite phase may be formed and a martensite phase may be formed during rapid cooling after heat treatment. Considering this, the upper limit of the hot-rolled sheet annealing heat treatment temperature T (HRA, °C) may be limited to Ac1-20.
  • the hot-rolled sheet annealing may be performed for 30 seconds or more and 10 minutes or less.
  • the hot-rolled sheet annealing time When the hot-rolled sheet annealing time is short, the fraction of residual martensite is high and elongation may be inferior. In consideration of this, the hot-rolled sheet annealing may be performed for 30 seconds or more. However, if the annealing time of the hot-rolled sheet is too long, the strength may decrease due to coarsening of crystal grains, and the thickness of the surface oxide layer may increase, which may increase the pickling time for removing the oxide layer or may not sufficiently remove the oxide layer. In consideration of this, the annealing of the hot-rolled sheet may be controlled to 10 minutes or less.
  • Cooling after the annealing of the hot-rolled sheet may be performed at a cooling rate of 10 to 50° C./s.
  • the cooling rate When the cooling rate is low, elongation and formability may be lowered due to non-uniformity of the structure due to soft nitrification. However, when the cooling rate is too high, the elongation is adversely affected due to excessive hardening. In consideration of this, the cooling rate may be controlled to 10 to 50 °C/s.
  • the cold rolling may be performed at a reduction ratio of 60 to 90%.
  • the reduction ratio When the reduction ratio is low, it is difficult to obtain a recrystallized structure because the stored energy by cold working is not sufficient. However, if the reduction ratio is too high, cracks may occur due to rolling. Considering this, the reduction ratio can be controlled to 60 to 90%.
  • the cold-rolled sheet may be subjected to cold-rolled sheet annealing at a cold-rolled sheet annealing heat treatment temperature T (CRA, ° C) that satisfies Equation (3) below.
  • T cold-rolled sheet annealing heat treatment temperature
  • Equation (3) 870 ⁇ T (CRA, °C) ⁇ Ac1 - 20
  • the cold-rolled sheet annealing heat treatment temperature T may be 870 °C or more.
  • the cold-rolled sheet annealing heat treatment temperature T CRA, °C
  • the upper limit of the cold-rolled sheet annealing heat treatment temperature T can be limited to Ac1-20.
  • the cold-rolled sheet annealing may be performed for 30 seconds or more and 10 minutes or less, and cooling after the cold-rolled sheet annealing may be performed at a cooling rate of 10 to 50° C./s.
  • slabs were prepared. The prepared slab was reheated at 1200 ° C, hot rolled at a finish rolling completion temperature of 800 ° C, and then wound at 750 ° C to manufacture a hot-rolled steel.
  • the prepared hot-rolled steel was subjected to hot-rolled sheet annealing at a hot-rolled sheet annealing heat treatment temperature T (HRA, °C) for 10 minutes, then cooled at a cooling rate of 30 °C / s and then pickled, to obtain a hot-rolled pickled hot-rolled sheet.
  • cold-rolled sheet annealing was performed at a cold-rolled sheet annealing heat treatment temperature T (CRA, °C) for 10 minutes, and then cooled at a cooling rate of 30 °C / s and then pickled to prepare steel.
  • Table 2 below shows the hot-rolled sheet annealing heat treatment temperature T (HRA, °C), cold-rolled sheet annealing heat treatment temperature T (CRA, °C), the thickness and elongation of the manufactured steel.
  • Elongation was measured using a tensile tester from Zwick Roell.
  • Equation (2) 840 ⁇ T (HRA, °C) ⁇ Ac1 - 20
  • Equation (3) 870 ⁇ T (CRA, °C) ⁇ Ac1 - 20
  • 1 is a graph showing an annealing heat treatment temperature range that can secure an elongation of 27% or more.
  • Equation (2) 840 ⁇ T (HRA, °C) ⁇ Ac1 - 20
  • Equation (3) 870 ⁇ T (CRA, °C) ⁇ Ac1 - 20
  • a ferritic stainless steel with improved elongation and a manufacturing method thereof by controlling the annealing heat treatment temperature while omitting the upper annealing and performing the continuous annealing, thereby reducing the upper annealing process that takes a long time. By omitting it, the manufacturing cost can be reduced, so industrial applicability is recognized.

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Abstract

La présente invention divulgue : un acier inoxydable ferritique ayant un allongement amélioré même si le recuit par lots est omis ; et son procédé de fabrication. Un acier inoxydable ferritique selon un mode de réalisation de la présente invention peut comprendre, en poids, 0,01 à 0,1 % de C, 0,01 à 1,0 % de Si, 0,01 à 1,5 % de Mn, P en une quantité supérieure à 0 % et inférieure ou égale à 0,05 %, S en une quantité supérieure à 0 % et inférieure ou égale à 0,005 %, 13,0 à 18,0 % de Cr, 0,005 à 0,1 % de N, 0,005 à 0,2 % d'Al, 0,05 à 0,25 % de Ni, et le reste de Fe (fer) et d'autres impuretés inévitables.
PCT/KR2022/015994 2021-10-26 2022-10-20 Acier inoxydable ferritique et son procédé de fabrication WO2023075287A1 (fr)

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JP2019044215A (ja) * 2017-08-31 2019-03-22 Ｊｆｅスチール株式会社 フェライト系ステンレス鋼板およびその製造方法
KR20210019519A (ko) * 2018-10-19 2021-02-22 제이에프이 스틸 가부시키가이샤 페라이트계 스테인리스 강판 및 그 제조 방법

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