EP3699314A1 - Acier inoxydable ferritique utilitaire possédant une excellente aptitude au façonnage à chaud et son procédé de fabrication - Google Patents

Acier inoxydable ferritique utilitaire possédant une excellente aptitude au façonnage à chaud et son procédé de fabrication Download PDF

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Publication number
EP3699314A1
EP3699314A1 EP18892556.4A EP18892556A EP3699314A1 EP 3699314 A1 EP3699314 A1 EP 3699314A1 EP 18892556 A EP18892556 A EP 18892556A EP 3699314 A1 EP3699314 A1 EP 3699314A1
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EP
European Patent Office
Prior art keywords
slab
ferrite
stainless steel
less
manufacturing
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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.)
Pending
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EP18892556.4A
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German (de)
English (en)
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EP3699314A4 (fr
Inventor
Jae-Hwa Lee
Mi-Nam Park
Gyu Jin Jo
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.)
Posco Holdings Inc
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Posco Co Ltd
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Application filed by Posco Co Ltd filed Critical Posco Co Ltd
Publication of EP3699314A1 publication Critical patent/EP3699314A1/fr
Publication of EP3699314A4 publication Critical patent/EP3699314A4/fr
Pending legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
    • 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
    • C22C38/002—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
    • C22C38/02—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • 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 manufacturing method of a utility ferritic stainless steel, More specifically, relates to a manufacturing method of a utility ferritic stainless steel with improved slab hot workability through ferrite factor and ⁇ -ferrite phase fraction control through component control under hot rolling heating temperature conditions of at least 1200°C before hot rolling.
  • Utility ferritic stainless steel is a high-strength STS steel with dual phase (ferrite base + tempered martensite) structure by controlling Ni, Mn content, etc. with a Cr content of 11 to 12.5%. It is a steel type that is used as a substitute for carbon steel in the field of structural materials requiring corrosion resistance / abrasion resistance and weldability. This utility ferritic stainless steel is widely used as a structural material requiring strength and corrosion resistance.
  • austenitic 304 steel having excellent corrosion resistance is used as a structural material, but a large amount of expensive Ni and Cr is included, which causes economic problems.
  • ferritic stainless steel containing 16% or more of Cr, especially in 430 steel corrosion resistance is superior to carbon steel, but workability is poor, and in particular, there is a limitation in the use of a structural material that requires weldability due to problems such as deterioration of toughness of the weld zone due to coarsening of the ferrite structure of the heat-affected zone.
  • 409 steel containing relatively low Cr of about 11% or less corrosion resistance is similar to that of the existing 400-based STS, but due to low impact toughness and yield strength, there are many limitations to apply as a structural material.
  • the embodiments of the present disclosure as the ⁇ -ferrite fraction in the slab structure is controlled by controlling the alloy component and phase fraction conditions, when hot rolling of a wide slab under high temperature heat treatment conditions of 1200 to 1250°C, provide a utility ferritic stainless steel with excellent hot workability that can prevent the occurrence of surface linear flaws and edge cracks, and a manufacturing method thereof.
  • a manufacturing method of a utility ferritic stainless steel with excellent hot workability includes: manufacturing a slab including, in percent (%) by weight of the entire composition, C: 0.005 to 0.020%, N: 0.005 to 0.020%, Si: 0.5 to 0.8%, Mn: 0.5 to 1.5%, Cr: 11.0 to 12.5%, Ni: 0.2 to 0.6%, P: 0.035% or less (excluding 0), S: 0.01% or less (excluding 0), the remainder of iron (Fe) and other inevitable impurities; and hot rolling the slab after heating the slab, and the heating of the slab is performed in a temperature range of 1200 to 1250°C so that the fraction of ⁇ -ferrite phase in the internal structure of the slab is 80 to 95%.
  • the heating time may be 3 hours or more.
  • the manufacturing method may further include: Cu: 0.2% or less and Ti: 0.03% or less.
  • the ferritic stainless steel may further include: Cu: 0.2% or less and Ti: 0.03% or less.
  • the reduction of area in the temperature range of 900 to 1200°C may be 70% or more.
  • a manufacturing method of a utility ferritic stainless steel with excellent hot workability includes: manufacturing a slab comprising, in percent (%) by weight of the entire composition, C: 0.005 to 0.020%, N: 0.005 to 0.020%, Si: 0.5 to 0.8%, Mn: 0.5 to 1.5%, Cr: 11.0 to 12.5%, Ni: 0.2 to 0.6%, P: 0.035% or less (excluding 0), S: 0.01% or less (excluding 0), the remainder of iron (Fe) and other inevitable impurities; and hot rolling the slab after heating the slab, and the heating of the slab is performed in a temperature range of 1200 to 1250°C so that the fraction of ⁇ -ferrite phase in the internal structure of the slab is 80 to 95%.
  • part when a part "includes” or “comprises” an element, unless there is a particular description contrary thereto, the part may further include other elements, not excluding the other elements.
  • ferritic stainless steel is described, and then a manufacturing method of ferrite stainless steel is described.
  • FIG. 1 is a graph showing the correlation between ⁇ -ferrite fraction and hot workability at 1000, 1100, and 1200°C.
  • phase fraction of ⁇ -ferrite during hot rolling causes a difference in deformation resistance to processing between austenite and ⁇ -ferrite structures when processing materials at high temperatures.
  • linear flaws and edge cracks are generated.
  • hot workability is the most inferior as shown in FIG. 1 when the fraction of ⁇ -ferrite in the range of 15 to 30% at a material surface temperature of 1000 to 1200°C due to contact between the roll and the material during hot rolling.
  • Inventors of the present disclosure have studied microstructures to improve hot workability in ferritic stainless steel. As a result, they discovered that the fraction of ⁇ -ferrite formed in the tissue can be controlled by adjusting the temperature of the slab during heating before hot rolling of the slab. In particular, in the case of utility ferritic stainless steel, the fraction of delta-ferrite varies depending on the heating conditions, and they discovered that a large amount of ⁇ -ferrite structure is formed at higher temperatures. Accordingly, alloy components, phase fraction and the temperature range of the heating step was derived.
  • a utility ferritic stainless steel with excellent hot workability includes, in percent (%) by weight of the entire composition, C: 0.005 to 0.020%, N: 0.005 to 0.020%, Si: 0.5 to 0.8%, Mn: 0.5 to 1.5%, Cr: 11.0 to 12.5%, Ni: 0.2 to 0.6%, P: 0.035% or less (excluding 0), S: 0.01% or less (excluding 0), the remainder of iron (Fe) and other inevitable impurities.
  • the unit is % by weight.
  • the content of C and N is 0.005 to 0.020%.
  • the sum of the two elements exceeds 0.04%, there is a problem that the ductility of the material decreases rapidly, and the toughness of the martensite formed in the weld zone decreases rapidly.
  • the content of Si is 0.5 to 0.8%.
  • Silicon (Si) is usually added as a deoxidizer to reduce inclusions in steel, and when high strength is required, it is preferable to add 0.5% or more since it prevents excessive generation of delta ferrite that can lower strength.
  • the upper limit can be limited to 0.8%.
  • the content of Mn is 0.5 to 1.5%.
  • Manganese (Mn) is an austenite-forming element and is effective in improving toughness because it controls ferrite grain size growth. Therefore, it is preferable to add 0.5% or more to improve toughness and workability of the material. However, if the content is excessive, the workability and toughness of the steel material rapidly decreases, and the upper limit can be limited to 1.5%.
  • the content of Cr is 11.0 to 12.5%.
  • Chromium (Cr) is the most contained element of the corrosion resistance enhancing element of stainless steel, and it is preferable to add 11% or more to express corrosion resistance.
  • the content is excessive, since a large amount of austenite forming elements such as Ni, Mn, and Cu must be added, there is a problem that it is difficult to secure the toughness of the weld zone and the workability of the material, and the upper limit can be limited to 12.5%.
  • the content of Ni is 0.2 to 0.6%.
  • Nickel (Ni) is an austenite-forming element and contributes to the improvement of the toughness of the base material.
  • Ni is an element that improves weld zone toughness by refinement of ferrite grains due to austenite residue during welding and refinement of martensite transformation grains during cooling.
  • it is preferable to add 0.2% or more.
  • the content is excessive, the effect is saturated, causing an increase in cost, and the upper limit can be limited to 0.6%.
  • the content of P is 0.035% or less.
  • Phosphorus (P) is an inevitably contained impurity, and its content is preferably managed as low as possible. Theoretically, it is advantageous to control the content of phosphorus to 0% by weight, but inevitably, it must be contained in the manufacturing process. Therefore, it is important to manage the upper limit, and in the present disclosure, the upper limit is managed as 0.035%.
  • the content of S is 0.01% or less.
  • S Sulfur
  • S Sulfur
  • utility ferritic stainless steel with excellent hot workability may further include Cu: 0.2% or less and Ti: 0.03% or less.
  • the content of Cu is 0.2% or less.
  • Copper (Cu) is an austenite-forming element similar to Ni, which contributes to the improvement of the toughness of the base material. In addition, there is an effect of improving the ductility when adding a certain amount of Cu. However, considering the cost aspect, the content is limited to 0.2% or less.
  • the content of Ti is 0.03% or less.
  • Titanium (Ti) is an element that fixes carbon and nitrogen, and forms a precipitate to lower the content of solid solution C and solid solution N to improve corrosion resistance of steel.
  • the content is excessive, surface defects may occur due to coarse Ti inclusions, and there is a problem in that manufacturing costs increase, and the upper limit may be limited to 0.03%.
  • the remaining component of the present disclosure is iron (Fe).
  • Fe iron
  • impurities that are not intended from the raw material or the surrounding environment can be inevitably mixed, and therefore cannot be excluded. Since these impurities are known to anyone skilled in the ordinary manufacturing process, they are not specifically mentioned in this specification.
  • the utility ferritic stainless steel with excellent hot workability that satisfies the aforementioned alloy composition may satisfy a range of 10.5 to 12.0 in a ferrite factor represented by the following equation (1).
  • Ferrite factor Cr + 6 Si ⁇ 2 Mn + 4 Ni + 40 C + N
  • Cr and Si are ferrite forming elements, which inhibit the formation of austenite at high temperatures
  • Mn, Ni, C, and N are austenite forming elements, which promote the formation of austenite at high temperatures. That is, the larger the ferrite factor, the more difficult it is to form austenite at high temperatures.
  • the ferrite factor exceeds 12
  • the formation of ⁇ -ferrite single-phase structure during heat treatment may cause hot workability deterioration due to grain coarsening.
  • the ferrite factor is less than 10.5
  • the ⁇ -ferrite fraction falls within a range of 15 to 30% due to a decrease in the material temperature during hot rolling, and thus there is a problem of inferior hot workability. Therefore, it is preferable that the ferrite factor satisfies the range of 10.5 to 12.
  • the fraction of the ⁇ -ferrite phase upon heating before hot rolling of utility ferritic stainless steel with excellent hot workability satisfying the aforementioned alloy composition may be 80 to 95%.
  • a manufacturing method of a utility ferritic stainless steel with excellent hot workability includes a manufacturing a slab comprising, in percent (%) by weight of the entire composition, C: 0.005 to 0.020%, N: 0.005 to 0.020%, Si: 0.5 to 0.8%, Mn: 0.5 to 1.5%, Cr: 11.0 to 12.5%, Ni: 0.2 to 0.6%, P: 0.035% or less (excluding 0), S: 0.01% or less (excluding 0), the remainder of iron (Fe) and other inevitable impurities; and a hot rolling the slab after heating the slab, and the heating of the slab may be performed in a temperature range of 1200 to 1250°C so that the fraction of ⁇ -ferrite phase in the internal structure of the slab is 80 to 95%.
  • the molten steel containing the above composition is cast into a slab in a continuous casting machine, the cooled slab is heated, and then hot rolled to produce a hot rolled product.
  • the produced slab is subjected to a heating process before hot rolling.
  • the present disclosure adjusts the heating temperature of the slab to control the fraction of ⁇ -ferrite phase in the internal structure of the slab to be 80 to 95% during the heating process.
  • FIG. 2 is a picture for explaining the change in the microstructure during the high-temperature slab heat treatment according to Examples and Comparative Examples of the present disclosure.
  • the ⁇ -ferrite measured in the present disclosure refers to the ⁇ -ferrite content present during slab heating before hot rolling.
  • the specimens heat-treated at 1250°C for various alloying components were quenched and quantified through observation of microstructures at room temperature as shown in FIG. 2 .
  • phase fraction of the initial slab state greatly affects the hot workability of the material, and the results are shown in FIG. 3 .
  • FIG. 3 is a result showing the reduction of area (%) measured through a high temperature gleeble tensile test at various hot rolling temperatures of 900 to 1200°C after maintaining for 3 hours at a temperature of 1250°C using various alloy components.
  • the measured reduction of area means that the higher the value, the better the hot workability.
  • the heating temperature of the slab is set to 1200 to 1250°C. To this end, it is achieved by charging the slab into the interior of the furnace and then maintaining the interior of the furnace at 1200 to 1250°C for at least 3 hours.
  • the utility ferritic stainless steel manufactured according to an embodiment of the present disclosure is capable of producing wide materials, while minimizing the occurrence of linear flaws and edge cracks.
  • the ferritic stainless steel according to the present disclosure has improved durability and can be used as a material for bus structures.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Heat Treatment Of Steel (AREA)
EP18892556.4A 2017-12-22 2018-11-07 Acier inoxydable ferritique utilitaire possédant une excellente aptitude au façonnage à chaud et son procédé de fabrication Pending EP3699314A4 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
KR1020170178047A KR101987665B1 (ko) 2017-12-22 2017-12-22 열간가공성이 우수한 유틸리티 페라이트계 스테인리스강 및 그 제조방법
PCT/KR2018/013418 WO2019124729A1 (fr) 2017-12-22 2018-11-07 Acier inoxydable ferritique utilitaire possédant une excellente aptitude au façonnage à chaud et son procédé de fabrication

Publications (2)

Publication Number Publication Date
EP3699314A1 true EP3699314A1 (fr) 2020-08-26
EP3699314A4 EP3699314A4 (fr) 2020-08-26

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EP18892556.4A Pending EP3699314A4 (fr) 2017-12-22 2018-11-07 Acier inoxydable ferritique utilitaire possédant une excellente aptitude au façonnage à chaud et son procédé de fabrication

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US (1) US20200392609A1 (fr)
EP (1) EP3699314A4 (fr)
KR (1) KR101987665B1 (fr)
CN (1) CN111448326B (fr)
WO (1) WO2019124729A1 (fr)

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CN115029622B (zh) * 2022-04-29 2023-05-23 武汉钢铁有限公司 一种高表面质量热轧双相钢及其生产工艺
CN115261744B (zh) * 2022-07-20 2023-10-27 山西太钢不锈钢股份有限公司 一种高韧性低铬铁素体不锈钢中厚板及其制造方法

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US4608099A (en) * 1984-10-10 1986-08-26 Amax Inc. General purpose maintenance-free constructional steel of superior processability
JPS63219527A (ja) * 1987-03-10 1988-09-13 Sumitomo Metal Ind Ltd 冷間加工性にすぐれたフエライトステンレス鋼の製造方法
KR100433250B1 (ko) * 1999-06-17 2004-05-27 주식회사 포스코 용접특성이 우수한 구조용 페라이트계 스테인레스강
KR20090005252A (ko) * 2004-01-29 2009-01-12 제이에프이 스틸 가부시키가이샤 오스테나이트·페라이트계 스테인레스 강
KR101056211B1 (ko) * 2008-11-25 2011-08-11 주식회사 포스코 가공성이 우수한 페라이트계 스테인리스강 및 그의 제조방법
CN102899587B (zh) * 2011-07-25 2015-01-21 宝山钢铁股份有限公司 一种双相不锈钢及其制造方法
KR101463315B1 (ko) * 2012-12-21 2014-11-18 주식회사 포스코 경도와 저온 충격특성이 우수한 스테인리스 열연강판
KR20150074694A (ko) * 2013-12-24 2015-07-02 주식회사 포스코 열간가공성이 우수한 페라이트계 스테인리스강 및 그 제조 방법
KR101685825B1 (ko) * 2015-06-18 2016-12-12 현대제철 주식회사 기계구조용 탄소강재 및 이의 제조 방법

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CN111448326A (zh) 2020-07-24
US20200392609A1 (en) 2020-12-17
CN111448326B (zh) 2022-10-28
EP3699314A4 (fr) 2020-08-26
WO2019124729A1 (fr) 2019-06-27
KR101987665B1 (ko) 2019-06-11

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