WO2024136120A1 - Acier inoxydable ferritique à maniabilité et résistance à la formation de crête améliorées, et son procédé de fabrication - Google Patents

Acier inoxydable ferritique à maniabilité et résistance à la formation de crête améliorées, et son procédé de fabrication Download PDF

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Publication number
WO2024136120A1
WO2024136120A1 PCT/KR2023/017890 KR2023017890W WO2024136120A1 WO 2024136120 A1 WO2024136120 A1 WO 2024136120A1 KR 2023017890 W KR2023017890 W KR 2023017890W WO 2024136120 A1 WO2024136120 A1 WO 2024136120A1
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Prior art keywords
stainless steel
ferritic stainless
manufacturing
ridging
improved
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PCT/KR2023/017890
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English (en)
Korean (ko)
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최가영
김상석
김동훈
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주식회사 포스코
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Publication of WO2024136120A1 publication Critical patent/WO2024136120A1/fr

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    • 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • 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
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—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
    • 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
    • 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 a ferritic stainless steel with improved processability and anti-scratch properties and a method of manufacturing the same.
  • Ferritic stainless steel has excellent corrosion resistance while adding a small amount of expensive alloy elements, making it more cost-competitive than austenitic stainless steel. Ferritic stainless steels are used in building materials, transportation equipment, home appliances, and kitchen appliances.
  • Ferritic stainless steel cold-rolled products have a problem in that stripe-shaped ridging defects occur during forming processing such as deep drawing. These ridging defects not only worsen the appearance of the product, but also increase the manufacturing cost because a polishing process is added after molding when severe ridging occurs.
  • the present invention aims to provide a ferritic stainless steel with improved processability and ridging and a manufacturing method thereof by controlling the crystal grain size of the final cold-rolled annealed material by optimizing the steel components and manufacturing process to improve the processability of cold-rolled products. .
  • the ferritic stainless steel with improved processability and resistance to scuffing according to an aspect of the present invention has, in weight percent, carbon (C): 0.0005 to 0.02%, nitrogen (N): 0.01 to 0.2%, and silicon (Si): 0.01 to 0.02%. 1.0%, manganese (Mn): 0.01 to 1.0%, phosphorus (P): 0.001 to 0.05%, chromium (Cr): 13.0 to 20.0%, titanium (Ti): 0.05 to 0.2%, remaining iron (Fe) and inevitable It contains impurities, satisfies the following equation (1), and has a crystal grain size of 20 to 25 ⁇ m.
  • Equation (1) 2*[Ti]/[N] ⁇ 2.3
  • the ridging height measured after being stretched by 15% may be 10 ⁇ m or less.
  • Ferritic stainless steel with improved processability and anti-stinging properties may have an elongation of 32% or more.
  • the method for manufacturing ferritic stainless steel with improved processability and resistance to scuffing includes, in weight percent: carbon (C): 0.0005 to 0.02%, nitrogen (N): 0.01 to 0.2%, silicon (Si): 0.01 to 1.0%, manganese (Mn): 0.01 to 1.0%, phosphorus (P): 0.001 to 0.05%, chromium (Cr): 13.0 to 20.0%, titanium (Ti): 0.05 to 0.2%, remainder iron (Fe) and manufacturing a slab containing unavoidable impurities and satisfying the following formula (1); reheating the slab; Hot rolling and then hot rolling annealing the reheated slab; And it may include the step of cold rolling the hot rolled material and then cold rolling and annealing it at 800 to 850°C.
  • Equation (1) 2*[Ti]/[N] ⁇ 2.3
  • the reheating step may be performed at 1,000 to 1,300°C.
  • the stainless steel may have a crystal grain size within the range of 20 to 25 ⁇ m.
  • the ridging height of the stainless steel measured after being stretched by 15% may be 10 ⁇ m or less.
  • the stainless steel may have an elongation of 32% or more.
  • the present invention can provide a ferritic stainless steel with improved processability and ridging and a manufacturing method thereof by controlling the crystal grain size of the final cold-rolled annealed material by optimizing the steel components and manufacturing process to improve the processability of cold-rolled products. there is.
  • Figure 1 is a graph showing the ridging height (solid line) and elongation (dotted line) according to annealing temperature when manufacturing stainless steel according to an embodiment.
  • Figure 2a is a photograph showing the crystal grain size of stainless steel manufactured at a cold rolling annealing temperature of 750°C.
  • Figure 2b is a photograph showing the crystal grain size of stainless steel manufactured at a cold rolling annealing temperature of 800°C.
  • Figure 2c is a photograph showing the crystal grain size of stainless steel manufactured at a cold rolling annealing temperature of 850°C.
  • Figure 2d is a photograph showing the crystal grain size of stainless steel manufactured at a cold rolling annealing temperature of 900°C.
  • Figure 2e is a photograph showing the crystal grain size of stainless steel manufactured at a cold rolling annealing temperature of 950°C.
  • the ferritic stainless steel with improved processability and scratch resistance includes, in weight percent, carbon (C): 0.0005 to 0.02%, nitrogen (N): 0.01 to 0.2%, silicon (Si): 0.01 to 1.0%, Manganese (Mn): 0.01 to 1.0%, phosphorus (P): 0.001 to 0.05%, chromium (Cr): 13.0 to 20.0%, titanium (Ti): 0.05 to 0.2%, including the remaining iron (Fe) and inevitable impurities. and satisfies the following equation (1), and the crystal grain size may satisfy the range of 20 to 25 ⁇ m.
  • Equation (1) 2*[Ti]/[N] ⁇ 2.3
  • the ferritic stainless steel with improved processability and resistance to scuffing according to an aspect of the present invention has, in weight percent, carbon (C): 0.0005 to 0.02%, nitrogen (N): 0.01 to 0.2%, and silicon (Si): 0.01 to 0.02%. 1.0%, manganese (Mn): 0.01 to 1.0%, phosphorus (P): 0.001 to 0.05%, chromium (Cr): 13.0 to 20.0%, titanium (Ti): 0.05 to 0.2%, remaining iron (Fe) and inevitable May contain impurities.
  • the carbon (C) content may be 0.0005 to 0.02 wt%, preferably 0.01 to 0.02 wt%.
  • C is an element that greatly affects the improvement of steel strength. If the amount of carbon (C) is less than 0.0005 wt%, the refining price to produce a high-purity product may be expensive. However, if the carbon content exceeds 0.02 wt%, corrosion resistance and formability may be reduced.
  • the nitrogen (N) content may be 0.01 to 0.2 wt%, preferably 0.04 to 0.2 wt%.
  • Nitrogen is an element that forms nitride, and it exists in an interstitial form, so if it is excessively contained, it can lead to a decrease in impact toughness and formability. Considering this, the upper limit of nitrogen content is limited to 0.2 wt% or less. However, if the nitrogen (N) content is too low, TiN crystallization may be lowered and the equiaxed crystal rate of the slab may be lowered.
  • the content of silicon (Si) may be 0.01 to 1.0 wt%, preferably 0.05 to 0.60 wt%.
  • Si can be added to deoxidize molten steel during steelmaking and is an effective element in stabilizing ferrite. If the amount of silicon (Si) is less than 0.01 wt%, the refining price becomes expensive. However, if the silicon content exceeds 1.0 wt%, there is a problem that the formability decreases due to increased impurities.
  • the content of manganese (Mn) may be 0.01 to 1.0 wt%, preferably 0.20 to 0.95 wt%.
  • Mn is an effective element in improving corrosion resistance. If the amount of manganese (Mn) is less than 0.01 wt%, the refining price becomes expensive, and if it exceeds 1.0 wt%, impurities increase and formability deteriorates.
  • the content of phosphorus (P) may be 0.001 to 0.05 wt%, preferably 0.001 to 0.020 wt%.
  • the amount of phosphorus (P) is less than 0.001 wt%, there is a problem that the refining price becomes expensive. However, if the phosphorus content exceeds 0.05 wt%, impurities increase and formability is reduced.
  • the content of chromium (Cr) may be 13.0 to 20.0 wt%, preferably 13.5 to 17.5 wt%.
  • Cr is an effective element in ensuring corrosion resistance of steel. If the amount of chromium (Cr) is less than 13.0 wt%, there is a problem that corrosion resistance deteriorates. However, if the chromium content exceeds 20.0wt%, there is a problem of poor formability.
  • the content of titanium (Ti) may be 0.05 to 0.2 wt%, preferably 0.05 to 0.17 wt%.
  • Ti is an element that can form precipitates by preferentially combining with interstitial elements such as C and N. If the amount of titanium (Ti) is less than 0.05 wt%, there may be difficulties in manufacturing forming Ti-based inclusions. If the titanium content is excessive, there may be a problem of surface defects occurring where the Ti component reacts with oxygen and turns yellow.
  • the remaining component of the ferritic stainless steel according to the present invention is iron (Fe).
  • Fe iron
  • ferritic stainless steel according to one embodiment may satisfy the following equation (1).
  • Equation (1) 2*[Ti]/[N] ⁇ 2.3
  • the value of 2*[Ti]/[N] may be specifically 0.5 to 2.3, more specifically 1.0 to 2.3, and more specifically 1.7 to 2.3.
  • the ferritic stainless steel according to an embodiment of the present invention has a further improved effect of controlling the microstructure, and can have better processability and resistance to scuffing.
  • the ferritic stainless steel according to one embodiment may have a ridging height of 10 ⁇ m or less measured after being stretched by 15% in a direction perpendicular to the rolling direction.
  • the ferritic stainless steel according to one embodiment may have an elongation of 32% or more, and preferably, the cold-rolled annealed material with a thickness of about 0.4 to 0.6 mm may have an elongation of 32% or more. The higher the elongation, the better the processability can be.
  • Ferritic stainless steel according to one embodiment may have a crystal grain size of 20 to 25 ⁇ m, preferably 20 to 23 ⁇ m.
  • the average grain size of stainless steel is limited to 20 to 25 ⁇ m, the desired elongation and ridging height can be simultaneously satisfied due to the refinement of the casting structure.
  • the method for manufacturing ferritic stainless steel with improved processability and resistance to scuffing includes, in weight percent: carbon (C): 0.0005 to 0.02%, nitrogen (N): 0.01 to 0.2%, silicon (Si): 0.01 to 1.0%, manganese (Mn): 0.01 to 1.0%, phosphorus (P): 0.001 to 0.05%, chromium (Cr): 13.0 to 20.0%, titanium (Ti): 0.05 to 0.2%, remaining iron (Fe) and manufacturing a slab containing unavoidable impurities and satisfying the following formula (1); reheating the slab; Hot rolling and then hot rolling annealing the reheated slab; and cold rolling the hot rolled material and then cold rolling annealing the hot rolled material.
  • Equation (1) 2*[Ti]/[N] ⁇ 2.3
  • the slab can be heated to a temperature of 1,000 to 1,300°C in a hot rolling furnace and then hot rolled to produce a hot rolled steel sheet.
  • the heating temperature may be 1,000°C or higher. However, if the heating temperature is too high, internal crystal grains may become too coarse, and surface oxidation may occur severely, causing surface defects. Considering this, the upper limit of the heating temperature may be limited to 1,300°C.
  • finish rolling may be performed at 700 to 900°C.
  • finish rolling temperature is less than 700°C, sticking may occur on the surface of the slab during hot rolling. However, if the finish rolling temperature exceeds 900°C, coarse ferrite crystal grains may be formed, which may result in poor anti-sting properties.
  • Hot rolled materials recrystallize the casting structure through hot rolling annealing.
  • hot rolling annealing can be performed at a temperature of 700 to 900°C.
  • the hot rolling annealing temperature is low, the stress formed during hot rolling may not be sufficiently removed and workability may be reduced. However, if the hot rolling annealing temperature is too high, the strength may decrease due to grain coarsening and the resistance to cracking may decrease.
  • the hot rolled annealed material can be cold rolled and then cold rolled and annealed to produce a cold rolled steel sheet.
  • cold rolling annealing can be performed at a temperature of 800 to 850°C.
  • the crystal grain size can be controlled to 20 to 25 ⁇ m.
  • the cold rolling annealing temperature exceeds 850°C, the crystal grain size becomes coarse, and as a result, a ⁇ 001 ⁇ /ND crystal orientation structure that reduces the resistance to cracking grows.
  • the ⁇ 001 ⁇ /ND crystal orientation structure grows, the plastic anisotropy with the matrix increases, which not only reduces the resistance to scratching but also reduces the surface roughness.
  • the cold rolling annealing temperature is less than 800°C, recrystallization does not occur, which may result in both elongation and anti-stiffness being inferior.
  • grain refinement within the casting structure can be realized to secure the anti-ringing properties and elongation of ferritic stainless steel.
  • Stainless steel manufactured according to one embodiment may have a crystal grain size in the range of 20 to 25 ⁇ m. By satisfying the above grain size range, stainless steel with excellent machinability and desired machinability and anti-ringing properties can be obtained.
  • Stainless steel manufactured according to one embodiment may have a ridging height of 10 ⁇ m or less measured after being stretched by 15% in a direction perpendicular to the rolling direction. By satisfying the above ridging height range, it is possible to obtain stainless steel with fewer streaks after processing and the desired glossiness.
  • Stainless steel manufactured according to one embodiment may have an elongation of 32% or more. By satisfying the above elongation range, the steel material is easily stretched during forming, and stainless steel with excellent formability can be obtained.
  • Slabs were manufactured in a vacuum induction melting furnace for various alloy composition ranges shown in Table 1 below.
  • the manufactured slab was reheated in a furnace at 1,100°C, then hot rolled to produce a hot rolled steel sheet, and then air cooled.
  • the air-cooled hot-rolled steel sheet was hot-rolled and annealed at 850°C, then cold-rolled to a thickness of 0.5 mm, and then cold-rolled and annealed to the temperature shown in Table 2 below to prepare a cold-rolled steel sheet specimen.
  • Equation (1) 2*[Ti]/[N]
  • Table 2 below shows the average grain size in the cast structure at each cold rolling annealing temperature for steels having the alloy composition of Table 1, and the ridging height and elongation measured after being stretched by 15%.
  • Figure 1 shows the correlation between the ridging height and elongation at each cold rolling annealing temperature for steel materials having an alloy composition of steel 3.
  • Crystal grain size was measured by photographing the cast structure using OM (optical microscopy).
  • Figures 2a to 2e are photographs of the crystal grain size of stainless steel obtained by processing a steel material with an alloy composition of Steel 3 at cold rolling annealing temperatures of 750°C, 800°C, 850°C, 900°C, and 950°C, respectively.
  • the ridging height is determined by measuring the size of the specimen. After tensing the specimen by 15% in the direction perpendicular to the rolling direction, the ridging bending height was measured using a surface roughness machine.
  • the elongation rate was calculated from the amount elongated until the moment of fracture when a cold-rolled stainless steel product was uniaxially stretched, divided by the initial length.
  • steels 3, 5, 6, and 9 satisfy the alloy composition, component range, and equation (1) presented in the present invention, and if they satisfy the cold rolling annealing temperature, the casting structure
  • the crystal grain size was refined to 20 to 25 ⁇ m (see FIGS. 2B and 2C), the ridging height was 10 ⁇ m or less, and the elongation was 32% or more.
  • the invention example that satisfies all of the alloy composition, component range, equation (1), and cold rolling annealing temperature is excellent in both workability and anti-ringing properties.
  • steels 1, 2, 4, 7, and 8 have a low content of N that can combine with Ti, even though the value of equation (1) exceeds 2.3 and the cold rolling annealing temperature satisfies 800 to 850°C, resulting in equiaxed crystal grain refinement. could not be implemented. Accordingly, it can be confirmed that the jing resistance is also poor.
  • ferritic stainless steel with improved processability and ridging is provided by optimizing the steel components and manufacturing process and controlling the crystal grain size of the final cold-rolled annealed material, and a manufacturing method thereof. As it is possible, industrial applicability is recognized.

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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
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Abstract

La présente invention concerne un acier inoxydable ferritique à maniabilité et résistance à la formation de crête améliorées, et son procédé de fabrication. Un acier inoxydable ferritique à maniabilité et résistance à la formation de crête améliorées selon un mode de réalisation de la présente invention contient, en % en poids, 0,0005 à 0,02 % de carbone (C), 0,01 à 0,2 % d'azote (N), 0,01 à 1,0 % de silicium (Si), 0,01 à 1,0 % de manganèse (Mn), 0 001 à 0,05 % de phosphore (P), 13,0 à 20,0 % de chrome (Cr), et 0,05 à 0,2 % de titane (Ti), le reste comprenant du fer (Fe) et des impuretés inévitables, satisfait l'expression (1) et peut avoir une taille de grain de 20 à 25 µm. Expression (1) : 2 * [Ti]/[N] ≤ 2,3. Dans l'expression (1), [Ti] et [N] se réfèrent à la teneur (en % en poids) des éléments respectifs.
PCT/KR2023/017890 2022-12-20 2023-11-08 Acier inoxydable ferritique à maniabilité et résistance à la formation de crête améliorées, et son procédé de fabrication WO2024136120A1 (fr)

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KR10-2022-0178903 2022-12-20
KR1020220178903A KR20240097125A (ko) 2022-12-20 2022-12-20 가공성 및 내리징성이 향상된 페라이트계 스테인리스강 및 이의 제조방법

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Citations (5)

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Publication number Priority date Publication date Assignee Title
KR100547536B1 (ko) * 2002-03-27 2006-01-31 신닛뽄세이테쯔 카부시키카이샤 페라이트계 스테인레스 강의 주조 부재 및 강판과 그 제조방법
KR100821059B1 (ko) * 2006-12-28 2008-04-16 주식회사 포스코 내식성 및 장출성형성이 우수한 페라이트계 스테인리스강및 그 제조방법
JP4590719B2 (ja) * 1999-12-03 2010-12-01 Ｊｆｅスチール株式会社 耐リジング性および成形性に優れたフェライト系ステンレス鋼板ならびにその製造方法
KR101569589B1 (ko) * 2013-12-24 2015-11-16 주식회사 포스코 내리징성이 우수한 페라이트계 스테인리스강 및 그 제조방법
KR20170086100A (ko) * 2014-12-11 2017-07-25 제이에프이 스틸 가부시키가이샤 페라이트계 스테인리스강 및 그 제조 방법

Family Cites Families (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR100706524B1 (ko) 2005-12-22 2007-04-12 주식회사 포스코 리징 특성이 개선된 페라이트계 스테인레스강의 제조 방법

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP4590719B2 (ja) * 1999-12-03 2010-12-01 Ｊｆｅスチール株式会社 耐リジング性および成形性に優れたフェライト系ステンレス鋼板ならびにその製造方法
KR100547536B1 (ko) * 2002-03-27 2006-01-31 신닛뽄세이테쯔 카부시키카이샤 페라이트계 스테인레스 강의 주조 부재 및 강판과 그 제조방법
KR100821059B1 (ko) * 2006-12-28 2008-04-16 주식회사 포스코 내식성 및 장출성형성이 우수한 페라이트계 스테인리스강및 그 제조방법
KR101569589B1 (ko) * 2013-12-24 2015-11-16 주식회사 포스코 내리징성이 우수한 페라이트계 스테인리스강 및 그 제조방법
KR20170086100A (ko) * 2014-12-11 2017-07-25 제이에프이 스틸 가부시키가이샤 페라이트계 스테인리스강 및 그 제조 방법

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