WO2017111437A1 - Acier inoxydable duplex pauvre et son procédé de fabrication - Google Patents

Acier inoxydable duplex pauvre et son procédé de fabrication Download PDF

Info

Publication number
WO2017111437A1
WO2017111437A1 PCT/KR2016/014953 KR2016014953W WO2017111437A1 WO 2017111437 A1 WO2017111437 A1 WO 2017111437A1 KR 2016014953 W KR2016014953 W KR 2016014953W WO 2017111437 A1 WO2017111437 A1 WO 2017111437A1
Authority
WO
WIPO (PCT)
Prior art keywords
stainless steel
duplex stainless
lean duplex
steel
present
Prior art date
Application number
PCT/KR2016/014953
Other languages
English (en)
Korean (ko)
Inventor
전종진
김봉운
Original Assignee
주식회사 포스코
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 주식회사 포스코 filed Critical 주식회사 포스코
Priority to CN201680074064.3A priority Critical patent/CN108474087A/zh
Priority to US16/062,876 priority patent/US20180363112A1/en
Publication of WO2017111437A1 publication Critical patent/WO2017111437A1/fr

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D8/0247—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
    • 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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • 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
    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/02—Superplasticity
    • 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
    • C21D2211/001—Austenite
    • 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 lean duplex stainless steel and a method of manufacturing the same, which minimizes the content of expensive alloy elements such as Ni and Mo in the component system, and controls thermal martensite transformation and plastic organic martensite transformation, thereby controlling the austenite phase and the ferrite phase. It relates to a lean duplex stainless steel having a phase structure and a method for producing the same.
  • austenitic stainless steel having good processability and corrosion resistance contains iron (Fe) as a base metal, and contains chromium (Cr) and nickel (Ni) as main raw materials, and molybdenum (Mo) and copper (Cu), etc. It is developed in various steel grades to suit various purposes by adding other elements of.
  • 300-based stainless steel which has excellent corrosion resistance and workability, includes expensive raw materials such as Ni and Mo.
  • 400-based stainless steel has been discussed, but the formability does not reach 300-based stainless steel. This exists.
  • thick plate with less molding than heat / cold rolled material it can be applied to corrosion resistance of 400 series depending on the usage environment.However, it is used as a thick plate due to the thermal shock characteristics and deterioration of welding part of 400 series stainless steel. There are many restrictions.
  • duplex stainless steel mixed with the austenitic phase and the ferrite phase has all the advantages of the austenitic and ferritic systems, and various types of duplex stainless steel have been developed to date.
  • one of the most widely used duplex stainless steels used in high corrosion resistance environment is AL2205 (UNS S31803 or S32205) with 22% Cr, 5.5% Ni, 3% Mo, 0.16% N components.
  • the steels provide excellent corrosion resistance in various corrosive environments, and thus have better corrosion resistance than austenitic, such as AISI 304 and 316.
  • duplex stainless steel contains expensive elements such as Ni and Mo, not only the manufacturing cost is increased but also the Ni and Mo are consumed, and thus the price competitiveness with other steel grades is inferior.
  • Lean duplex stainless steel has the same corrosion resistance as 304 and 316 steel, which is roughly classified as austenitic stainless steel, and has low Ni content, so it is economical and high in strength and easy to secure. It is in the spotlight as a molten steel.
  • Such lean duplex steels include, for example, S32304 (typical component 23Cr-4Ni-0.13N) standardized in ASTMA240, S32101 (typical component 21Cr-1.5Ni-5Mn-0.22N) standardized in ASTMA240.
  • lean duplex steels can reduce manufacturing costs by eliminating expensive elements, they have corrosion resistance equivalent to or higher than that of 304, 304L and 316 steels. However, in some cases, lean duplex steels are overspecified. There is also a demand for duplex steel having corrosion resistance at the system level.
  • the steel grade corresponding to this requirement is not developed at present, and 400 series stainless steel is a structural factor, which has a low DBTT characteristic, which is very weak in impact characteristics, and is difficult to use as a thick plate due to the coarsening of the welded HAZ part structure. .
  • the austenite phase stability at room temperature is lowered, and the austenite phase is transformed into a martensite phase during cooling. do. That is, it is difficult to realize a duplex steel structure having a two-phase structure of ferrite phase and austenite phase at 20% Cr or less, and the martensite phase formed during the cooling process lowers the elongation of the material and causes an impossible process such as a tubing process. .
  • Patent Document 0001 US Registered Patent No. 6096441 (March 2000)
  • Embodiments of the present invention to provide a lean duplex stainless steel having a two-phase structure of austenite and ferrite phase by minimizing the content of expensive alloy elements such as Ni, Mo, etc. in the component system of the duplex stainless steel and Si, N component control.
  • embodiments of the present invention to provide austenite phase stability at room temperature to secure the elongation, to provide a method for producing a lean duplex stainless steel that can ensure corrosion resistance of the 400-based universal steel level.
  • the ferrite fraction (Ferrite fraction, FF (%)) according to the following formula (1) is 60 to 80%
  • modified Md 30 Modified Md according to the following formula (2) 30 , MM (° C.)
  • Md Modified Md according to the following formula (2) 30 , MM (° C.)
  • the chromium (Cr) may comprise 13.5 to 14.5%.
  • the stainless steel may have a Cr equivalent weight of 13.0 to 16.0 according to the following Formula (3).
  • nickel (Ni) may include 0.05% or less.
  • the stainless steel may have a Ni equivalent weight of 5.0 or less according to the following formula (4).
  • Ni equivalent Ni + 18N + 30C + 0.1Mn-0.01Mn 2 ------ Formula (4)
  • the elongation of the stainless steel may be 30% or more.
  • Method for producing a lean duplex stainless steel in weight percent, carbon (C) 0.05 to 0.1%, silicon (Si) 2.0 to 4.0%, manganese (Mn) 4.0 to 8.0%, chromium (Cr ) Hot rolling a lean duplex stainless steel slab containing 13.0 to 15.0%, nitrogen (N) 0.05 to 0.15%, balance iron (Fe) and other unavoidable impurities, and annealing the hot rolled steel sheet at a temperature of 1,050 to 1,150 ° C. And water-cooling.
  • the hot rolled steel sheet may be annealed for 10 to 60 minutes.
  • Embodiments of the present invention can save resources by minimizing or excluding alloy components such as Cr, Ni, Mo, etc. in the component system of the duplex stainless steel can minimize the manufacturing cost of the duplex stainless steel.
  • 1 is a Schaeffler's diagram for explaining the component system of lean duplex stainless steel according to embodiments of the present invention.
  • FIG. 2 is a photograph of a microstructure of a lean duplex stainless steel according to an embodiment of the present invention using a transmission electron microscope (TEM).
  • TEM transmission electron microscope
  • 3 is a graph for explaining the correlation between the stress-elongation of lean duplex stainless steel according to an embodiment of the present invention.
  • Figure 4 is a graph showing the official potential value of lean duplex stainless steel according to an embodiment of the present invention.
  • the amount of carbon (C) is 0.05 to 0.1%.
  • Carbon (C) is an austenite phase forming element and is an effective element for increasing the material strength by solid solution strengthening. Carbon (C) should be added at least 0.05% in order to contribute to the austenite phase stability.
  • Such carbon (C) when excessively added, forms segregated and coarse carbides in the center of the material manufacturing, adversely affecting the post-hot rolling-annealing-cold rolling-cold annealing process, and the ferrite-austenite phase boundary.
  • Cr chromium
  • the amount of silicon (Si) is 2.0 to 4.0%.
  • Silicon (Si) is a ferrite phase forming element and is an element that is concentrated in ferrite during annealing.
  • the content of chromium (Cr) in the lean duplex stainless steel according to the embodiments of the present invention is lower than that of the conventional lean duplex stainless steel, so that 2.0% to 4.0% of the lean duplex stainless steel may be added.
  • silicon (Si) is added in excess of 4.0%, the hardness of the ferrite phase is sharply increased to deteriorate the workability and impact characteristics. Therefore, it is desirable to limit the content of silicon (Si) to 2.0 to 4.0%.
  • the amount of manganese (Mn) is 4.0 to 8.0%.
  • Manganese (Mn) is an element that increases melt flow control, deoxidizer and nitrogen solubility, and is an austenite forming element. Manganese (Mn) is added in place of expensive nickel (Ni). If the manganese (Mn) is less than 4%, austenite stability is lowered at room temperature, transformed to martensite during cooling, making it difficult to maintain two-phase tissue. When the manganese (Mn) is more than 8%, the austenite phase fraction becomes excessively difficult to control the phase fraction. Therefore, it is preferable to limit the content of manganese (Mn) to 4.0 to 8.0%.
  • the amount of chromium (Cr) is 13.0 to 15.0%. Chromium (Cr) is minimized in terms of manufacturing cost reduction of the duplex stainless steel, it is desirable to limit to less than 15.0% to deviate from the existing lean duplex stainless steel component range. However, it is preferable to add more than 13% to ensure corrosion resistance of the duplex stainless steel. Therefore, it is preferable to limit the content of chromium (Cr) to 13.0 to 15.0%. More preferably, the lean duplex stainless steel may include chromium (Cr) in an amount of 13.5 to 14.5%.
  • the amount of nitrogen (N) is 0.05 to 0.15%. Nitrogen (N), together with nickel (Ni) in duplex stainless steel, contributes greatly to the stabilization of the austenite phase, and is one of the elements concentrated on the austenite phase during annealing.
  • the nitrogen (N) content in the manganese (Mn) range of the present invention exceeds 0.15%, blow holes and pin holes, etc., occur during casting due to excess nitrogen solubility. Surface defects and edge cracks are caused during rolling. Therefore, it is preferable to limit the content of nitrogen (N) to 0.05 to 0.15%.
  • the lean duplex stainless steel according to the exemplary embodiment of the present invention may include 0.05% or less of nickel (Ni).
  • Nickel (Ni) is an element that contributes greatly to stabilization of the austenite phase with nitrogen (N) in duplex stainless steel.
  • the lean duplex stainless steel according to an embodiment of the present invention has a ferrite fraction (FF (%)) of 60 to 80% according to Equation (1), and according to Equation (2).
  • modified Md 30 (modified Md 30, MM (°C)) has a number equal to or less than 110 °C.
  • the modified Md 30 according to Equation (2) exceeds 110 ° C.
  • the elongation of lean duplex stainless steel is shown to be less than 30%, specifically about 10 to 15% of the workability is very weak.
  • the stainless steel may have a Cr equivalent weight of 13.0 to 16.0 according to the following Formula (3).
  • the stainless steel may have a Ni equivalent weight of 5.0 or less according to the following Formula (4).
  • Ni equivalent Ni + 18N + 30C + 0.1Mn-0.01Mn 2 ------ Formula (4)
  • 1 is a Schaeffler's diagram for explaining the component system of lean duplex stainless steel according to embodiments of the present invention.
  • lean duplex stainless steel according to an embodiment of the present invention is reduced Cr equivalent and Ni equivalent as the content of chromium (Cr) and nickel (Ni), the existing lean duplex steel It can be seen that the Cr and Ni equivalents are located in a lower region.
  • Method for producing a lean duplex stainless steel in weight percent, carbon (C) 0.05 to 0.1%, silicon (Si) 2.0 to 4.0%, manganese (Mn) 4.0 to 8.0%, chromium (Cr ) Hot rolled lean duplex stainless steel slab containing 13.0 to 15.0%, nitrogen (N) 0.05 to 0.15%, balance iron (Fe) and other unavoidable impurities, and annealing the hot rolled steel sheet at a temperature of 1,050 to 1,150 ° C. , Water-cooled to produce lean duplex stainless steel.
  • the lean duplex stainless steel slab of the above composition may be thick rolled by a conventional method, and the hot rolled steel sheet may have a thickness of 5 to 20 mm.
  • the hot rolled steel sheet is annealed for 10 to 60 minutes at a temperature of 1,050 to 1,150 °C.
  • the martensitic phase transformation does not occur during the cooling of the microstructure and the ferrite phase and the austenite phase are maintained in two-phase structure, so that the ferrite phase fraction is maintained at 60 to 80% and the crystal Md 30 is 110 ° C. or less. It can have a value of.
  • the lean duplex stainless steel slabs including the component system according to the inventive steels and the comparative steels of Table 1 below were prepared, followed by thick plate rolling to prepare thick rolled specimens of 10 mmt.
  • Table 1 below shows the composition of the low cost lean duplex stainless steel, which is the steel grade of the present invention.
  • Cr chromium
  • Mn manganese
  • Si silicon
  • N nitrogen
  • the thick plate rolled specimens were maintained at an annealing temperature of 1,100 ° C. for 30 minutes and then cooled to evaluate materials, property changes, tensile properties, and corrosion resistance.
  • the tissues of the inventive steels 1 to 3 and the comparative steels 1 to 4 were observed to confirm the transformation onto the martensite phase.
  • the ferrite predicted fraction and the modified Md 30 value were calculated with reference to the compositions and formulas (1) and (2) in Table 1 above.
  • the tensile test was carried out by taking ASTM sub-size tensile test specimens in the rolling direction, specifying the temperature at the time of the tensile test at room temperature and the strain rate of 20 mm / min.
  • FIG. 2 is a photograph of a microstructure of a lean duplex stainless steel according to an embodiment of the present invention using a transmission electron microscope (TEM).
  • TEM transmission electron microscope
  • FIG. 2 shows the microstructure of inventive steel 1 of the present invention. As shown in the tissue photograph of Figure 2, when prepared in the component range of the present invention, it can be seen that the austenite phase is maintained in the austenite phase, without transformation into a martensite phase.
  • the phase stability of austenite is increased, so that the modified Md 30 is maintained at 110 ° C. or less, thereby ensuring processability of 30% or more of elongation.
  • the nitrogen (N) content is more than 0.15%, since the decrease of the real rate due to the edge crack bundle during rolling occurs, it is preferable to limit it to 0.15% or less.
  • 3 is a graph for explaining the correlation between the stress-elongation of lean duplex stainless steel according to an embodiment of the present invention.
  • inventive steel 1 is a graph of tensile properties of inventive steel 1 and comparative steel 2 of the present invention.
  • ASTM sub-size tensile specimens were taken in the rolling direction, and the tensile test was carried out at the temperature of the tensile test at room temperature and the deformation rate of 20 mm / min.
  • Figure 4 is a graph showing the official potential value of lean duplex stainless steel according to an embodiment of the present invention.
  • FIG. 4 is a graph comparing the official potential value of the invention steel 1 of the present invention with the official potential value of the 400 series general-purpose steel STS 409 steel, STS 430 steel.
  • Inventive steel 1, STS 409 steel, STS 430 steel is shown in Figure 4 by measuring the official potential of each specimen in 1.0% NaCl solution. Accordingly, it was confirmed that the lean duplex stainless steel according to the embodiment of the present invention has corrosion resistance between STS 409 steel and STS 430 steel.
  • Lean duplex stainless steel and its manufacturing method according to embodiments of the present invention can be applied to steel materials for industrial equipment, such as freshwater equipment, pulp, paper, chemical equipment.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

L'invention concerne un acier inoxydable duplex pauvre et son procédé de fabrication. L'acier inoxydable duplex pauvre selon un mode de réalisation de la présente invention comprend, en poids, 0,05 % à 0,1 % de carbone (C), 2,0 % à 4,0 % de silicium (Si), 4,0 % à 8,0 % de manganèse (Mn), 13,0 % à 15,0 % de chrome (Cr), 0,05 % à 0,15 % d'azote (N) et le reste de fer (Fe) et d'impuretés inévitables. Par conséquent, des constituants d'alliage, tels que Cr, Ni et Mo, sont réduits au minimum dans la composition de l'acier inoxydable duplex ou exclus de cette dernière, ce qui permet de réduire au minimum le coût de production, d'obtenir un allongement supérieur ou égal à 30 % et de garantir une résistance à la corrosion à un niveau de l'acier de la série 400 à usage général.
PCT/KR2016/014953 2015-12-21 2016-12-20 Acier inoxydable duplex pauvre et son procédé de fabrication WO2017111437A1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
CN201680074064.3A CN108474087A (zh) 2015-12-21 2016-12-20 节约型双相不锈钢及其制造方法
US16/062,876 US20180363112A1 (en) 2015-12-21 2016-12-20 Lean duplex stainless steel and method of manufacturing the same

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
KR10-2015-0182718 2015-12-21
KR1020150182718A KR20170075034A (ko) 2015-12-21 2015-12-21 린 듀플렉스 스테인리스강 및 이의 제조 방법

Publications (1)

Publication Number Publication Date
WO2017111437A1 true WO2017111437A1 (fr) 2017-06-29

Family

ID=59089558

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/KR2016/014953 WO2017111437A1 (fr) 2015-12-21 2016-12-20 Acier inoxydable duplex pauvre et son procédé de fabrication

Country Status (4)

Country Link
US (1) US20180363112A1 (fr)
KR (1) KR20170075034A (fr)
CN (1) CN108474087A (fr)
WO (1) WO2017111437A1 (fr)

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN112111691B (zh) * 2020-08-12 2022-06-21 广西柳钢中金不锈钢有限公司 无铜节镍型冷轧奥氏体不锈钢的制造方法

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2008291282A (ja) * 2007-05-22 2008-12-04 Nippon Steel & Sumikin Stainless Steel Corp 形状凍結性に優れた高強度複相ステンレス鋼板及びその製造方法
KR20090031864A (ko) * 2006-06-16 2009-03-30 인더스틸 크뢰쏘 듀플렉스 스테인리스강
KR101379139B1 (ko) * 2011-11-21 2014-03-28 주식회사 포스코 고강도와 연성이 우수한 린 듀플렉스 스테인리스강 및 그 제조방법
KR20140132423A (ko) * 2013-05-03 2014-11-17 주식회사 포스코 린 듀플렉스 스테인리스 열연강판 제조 방법
KR101504401B1 (ko) * 2012-11-30 2015-03-19 주식회사 포스코 고연성 린 듀플렉스 스테인리스강 및 그 제조방법

Family Cites Families (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4047941A (en) * 1974-09-23 1977-09-13 Allegheny Ludlum Industries, Inc. Duplex ferrit IC-martensitic stainless steel
FR2765243B1 (fr) * 1997-06-30 1999-07-30 Usinor Acier inoxydable austenoferritique a tres bas nickel et presentant un fort allongement en traction
US8562758B2 (en) * 2004-01-29 2013-10-22 Jfe Steel Corporation Austenitic-ferritic stainless steel

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR20090031864A (ko) * 2006-06-16 2009-03-30 인더스틸 크뢰쏘 듀플렉스 스테인리스강
JP2008291282A (ja) * 2007-05-22 2008-12-04 Nippon Steel & Sumikin Stainless Steel Corp 形状凍結性に優れた高強度複相ステンレス鋼板及びその製造方法
KR101379139B1 (ko) * 2011-11-21 2014-03-28 주식회사 포스코 고강도와 연성이 우수한 린 듀플렉스 스테인리스강 및 그 제조방법
KR101504401B1 (ko) * 2012-11-30 2015-03-19 주식회사 포스코 고연성 린 듀플렉스 스테인리스강 및 그 제조방법
KR20140132423A (ko) * 2013-05-03 2014-11-17 주식회사 포스코 린 듀플렉스 스테인리스 열연강판 제조 방법

Also Published As

Publication number Publication date
KR20170075034A (ko) 2017-07-03
CN108474087A (zh) 2018-08-31
US20180363112A1 (en) 2018-12-20

Similar Documents

Publication Publication Date Title
WO2014104706A1 (fr) Acier à base austénitique à haute résistance ayant une ténacité remarquable d'une zone affectée par la chaleur de soudage et son procédé de préparation
WO2020067685A1 (fr) Acier résistant à l'usure ayant d'excellentes dureté et ténacité au choc et procédé de fabrication de celui-ci
WO2020101227A1 (fr) Acier inoxydable austénitique non magnétique et son procédé de fabrication
WO2018074887A1 (fr) Armature de béton armé à haute résistance et procédé de fabrication de ladite armature de béton armé à haute résistance
WO2019125083A1 (fr) Acier résistant à l'usure possédant une excellente dureté et une excellente ténacité aux chocs, et son procédé de production
WO2011081350A2 (fr) Feuillard d'acier à résistance mécanique élevée ayant une excellente résistance au traitement thermique post-soudage et son procédé de fabrication
WO2020067686A1 (fr) Acier résistant à l'abrasion présentant une excellente dureté et une excellente solidité au choc, et son procédé de fabrication
WO2020060051A1 (fr) Tôle d'acier inoxydable ferritique laminée à chaud et non recuite ayant une excellente solidité au choc, et son procédé de fabrication
WO2018110779A1 (fr) Tôle d'acier faiblement allié ayant une résistance et une ductilité excellentes
WO2020111863A1 (fr) Acier à ultra-haute résistance présentant une usinabilité à froid et une résistance à la ssc excellentes et procédé de fabrication associé
WO2018117477A1 (fr) Acier inoxydable duplex ayant d'excellentes caractéristiques de résistance à la corrosion et d'usinabilité et procédé de fabrication de celui-ci
WO2019117430A1 (fr) Acier inoxydable ferritique ayant une excellente résistance à l'oxydation à haute température et procédé de fabrication associé
WO2016104883A1 (fr) Matériau d'acier inoxydable ferritique présentant une excellente ductilité et son procédé de production
WO2017104995A1 (fr) Acier de haute dureté résistant à l'abrasion avec une ténacité et une résistance à la fissuration de coupe excellentes, et son procédé de fabrication
WO2020085684A1 (fr) Plaque d'acier destinée à un récipient sous pression présentant une excellente ténacité cryogénique et une excellente résistance à l'allongement et son procédé de fabrication
WO2021010599A2 (fr) Acier inoxydable austénitique ayant une résistance améliorée et procédé de fabrication associé
WO2017111437A1 (fr) Acier inoxydable duplex pauvre et son procédé de fabrication
WO2019132226A1 (fr) Acier duplex pauvre à aptitude au pliage améliorée et procédé de fabrication associé
WO2019125076A1 (fr) Acier résistant à l'usure ayant d'excellentes dureté et ténacité au choc et procédé pour la production de celui-ci
WO2019112142A1 (fr) Acier inoxydable austénitique à dureté élevée présentant une excellente résistance à la corrosion
WO2017111250A1 (fr) Acier inoxydable duplex pauvre ayant une résistance à la corrosion et une usinabilité améliorées et procédé de fabrication s'y rapportant
WO2019124729A1 (fr) Acier inoxydable ferritique utilitaire possédant une excellente aptitude au façonnage à chaud et son procédé de fabrication
WO2022139214A1 (fr) Acier inoxydable martensitique ayant une résistance et une résistance à la corrosion améliorées, et son procédé de fabrication
WO2017209431A1 (fr) Acier inoxydable austénitique présentant une résistance à la corrosion et une aptitude au façonnage améliorées et son procédé de production
WO2021125564A1 (fr) Acier inoxydable ferritique à haute résistance pour collier de serrage et son procédé de fabrication

Legal Events

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

Ref document number: 16879304

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: DE

122 Ep: pct application non-entry in european phase

Ref document number: 16879304

Country of ref document: EP

Kind code of ref document: A1