EP3872209A1 - Acier non magnétique à haute résistance et ductilité élevée ayant une excellente soudabilité, et son procédé de fabrication - Google Patents

Acier non magnétique à haute résistance et ductilité élevée ayant une excellente soudabilité, et son procédé de fabrication Download PDF

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EP3872209A1
EP3872209A1 EP19875440.0A EP19875440A EP3872209A1 EP 3872209 A1 EP3872209 A1 EP 3872209A1 EP 19875440 A EP19875440 A EP 19875440A EP 3872209 A1 EP3872209 A1 EP 3872209A1
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Prior art keywords
steel
less
nonmagnetic
strength
present disclosure
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EP19875440.0A
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German (de)
English (en)
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EP3872209A4 (fr
Inventor
Dong-Ho Lee
Sung-Kyu Kim
Un-Hae LEE
Sang-Deok Kang
Sang-Ho Han
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Posco Holdings Inc
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Posco Co Ltd
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Publication of EP3872209A4 publication Critical patent/EP3872209A4/fr
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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
    • C21D6/00—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
    • 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
    • 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
    • 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
    • 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
    • C22C38/02—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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • 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
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite

Definitions

  • the present disclosure relates to a nonmagnetic steel that can be suitably used for components in which an eddy current occurs, such as a distribution board and a transformer, and more particularly, to a nonmagnetic steel that is excellent in not only terms of weldability but also in strength and ductility, and a manufacturing method therefor.
  • a material for a distribution board, a transformer, or the like requires excellent nonmagnetic properties together with high strength.
  • stainless steel to which nickel (Ni) and chromium (Cr) are added in large amounts, has conventionally been used.
  • Ni nickel
  • Cr chromium
  • stainless steel is disadvantageous, in that the strength may be low and the price may be high.
  • ferritic or martensitic stainless steel may be used.
  • the ferritic or martensitic stainless steel is disadvantageous in that high magnetism thereof causes an eddy current, resulting in power loss, and the price is significantly high.
  • steel having an austenite phase has been developed by controlling a manganese (Mn) content and a carbon (C) content in the steel so that the steel may have nonmagnetic properties, together with high strength, at a low price.
  • Mn manganese
  • C carbon
  • the austenite-type steel is advantageous in that the austenite phase can be stably maintained at room temperature and even at an extremely low temperature by controlling the amounts of the two aforementioned elements, and thereby, the nonmagnetic properties can be well maintained.
  • An aspect of the present disclosure is to provide a nonmagnetic steel that is excellent in weldability while having high strength and high ductility at low manufacturing costs by optimizing an alloy composition.
  • Another aspect of the present disclosure is to provide a method for manufacturing the above-described nonmagnetic steel.
  • a high-strength and high-ductility nonmagnetic steel having excellent weldability contains, by wt%, 0.03 to 0.50% of carbon (C), 0.3% or less of silicon (Si), 15 to 30% of manganese (Mn), more than 0% to 2.0% or less of chromium (Cr), more than 0% to 0.5% or less of molybdenum (Mo), 0.01 to 0.1% of titanium (Ti), 0.01 to 0.5% of vanadium (V), 0.2 to 1.0% of aluminum (Al), 0.1% or less of phosphorus (P), 0.01% or less of sulfur (S), and 0.03% or less of nitrogen (N), with a balance of Fe and other inevitable impurities, wherein the nonmagnetic steel has a single-phase austenite structure.
  • a method for manufacturing a high-strength and high-ductility nonmagnetic steel having excellent weldability includes: reheating a steel slab having the above-described alloy composition to a temperature of 1100 to 1250°C; finish-hot rolling the reheated steel slab at a temperature of 800 to 1000°C to manufacture a thick steel sheet; and cooling the thick steel sheet at a cooling rate of 10°C/s or higher.
  • the steel according to the present disclosure it is possible to provide steel having excellent nonmagnetic properties at low cost.
  • the steel according to the present disclosure has excellent weldability as well as excellent strength and ductility.
  • FIG. 1 is a graph illustrating a comparison of results of measuring permeabilities of inventive steel according to an exemplary embodiment in the present disclosure and comparative steel.
  • the inventors of the present disclosure have conducted in-depth research to provide a nonmagnetic steel having not only excellent nonmagnetic properties but also excellent weldability together with high strength and high ductility. As a result, they have found that an optimal component system capable of greatly improving the phase stability of the nonmagnetic steel can be provided.
  • the technical significance of the present disclosure is that Al is added in a certain amount, as well as C, Mn, etc. as alloy elements, to prevent carbon from forming carbides, and Cr and Mo are further added to further improve strength, ductility, and weldability.
  • a high-strength and high-ductility nonmagnetic steel having excellent weldability may contain, by wt%, 0.03 to 0.50% of carbon (C), 0.3% or less of silicon (Si), 15 to 30% of manganese (Mn), more than 0% to 2.0% or less of chromium (Cr), more than 0% to 0.5% or less of molybdenum (Mo), 0.01 to 0.1% of titanium (Ti), 0.01 to 0.5% of vanadium (V), 0.2 to 1.0% of aluminum (Al), 0.1% or less of phosphorus (P), 0.01% or less of sulfur (S), and 0.03% or less of nitrogen (N) .
  • an amount of each component refers to wt%, and a ratio of a structure is based on an area.
  • Carbon (C) is an element important in securing an austenite structure in the steel, and C may be contained in a predetermined amount or more to sufficiently secure the stability of the austenite. In the present disclosure, 0.03% or more of C may be contained for the above-described effect. In a case in which a C content exceeds 0.30%, the nonmagnetic properties deteriorate because carbides are precipitated when C is exposed to a high temperature for a long period of time, for example on a continuous-casting roll. In the present disclosure, however, C may be contained in an amount of up to 0.50% because a predetermined amount of aluminum (Al) is added to reduce formation of carbides.
  • Al aluminum
  • C may be contained in an amount of 0.03 to 0.50%.
  • Silicon (Si) does not greatly affect the stacking fault energy of the steel, and is usually used as a deoxidizer. If a Si content exceeds 0.3%, manufacturing costs increase, and there is a concern that oxides may be excessively formed, causing a deterioration in surface quality of a product.
  • Si may be contained in an amount of 0.3% or less, excluding 0%, taking into account that it is unavoidably added in a steel manufacturing process.
  • Manganese (Mn) is an important element serving to stabilize the austenite structure, and needs to be contained in an amount of 15% or more for the steel to obtain a low permeability.
  • Mn Manganese
  • a C content is low
  • Mn is added in an amount of less than 15%
  • an ⁇ '-martensite phase is formed, resulting in a deterioration in nonmagnetic properties.
  • an Mn content exceeds 30%, manufacturing costs increase significantly, and there is a problem in that oxidation occurs internally or processing cracks and the like are formed during heating in a hot processing step, resulting in a deterioration in surface quality.
  • Mn may be contained in an amount of 15 to 30%.
  • Chromium (Cr) is an element that is effective in suppressing high temperature oxidation to reduce surface defects and improving strength through solid solution strengthening. If Cr is added in a large amount, manufacturing costs increase, and coarse carbides are formed, resulting in a decrease in strength. Taking this into account, Cr may therefore be contained in an amount of 2.0% or less, excluding 0%.
  • Molybdenum (Mo) is an element that is effective in making a precipitate phase fine to increase a precipitation enhancing effect. If Mo is added in a large amount, the alloying cost increases and the precipitate phase is coarsened, and accordingly, the above-described effect cannot be sufficiently obtained. Taking this into account, Mo may therefore be contained in an amount of 0.5% or less, excluding 0%.
  • Titanium (Ti) is an element reacting with nitrogen (N) in the steel to precipitate nitrides and forming twins, and may be added to secure the strength and formability of the steel.
  • Ti improves yield strength by forming a precipitate phase. This effect can be obtained by adding Ti even in a small amount, and thus, Ti may be added in an amount of 0.01% or more.
  • Ti content exceeds 0.1%, there are concerns that precipitates may be excessively formed, thereby causing cracks during rolling or forging, and formability and weldability may deteriorate.
  • Ti may be contained in an amount of 0.01 to 0.1%.
  • Vanadium (V) is useful in improving strength by reacting with carbon, nitrogen, and the like in the steel and forming carbides, nitrides, and the like.
  • V is an element having a great precipitation enhancing effect.
  • V is preferably contained in an amount of 0.01% or more.
  • a V content exceeds 0.5%, there is a concern that precipitates may be excessively formed, resulting in a deterioration in high-temperature workability during hot processing such as rolling or forging, thereby causing cracks.
  • V may be contained in an amount of 0.01 to 0.5%.
  • Aluminum (Al) is added as a deoxidizer and is an element that is effective in preventing formation of carbides in the steel.
  • Al has an effect in controlling a twin fraction to improve formability.
  • Al is preferably contained in an amount of 0.2% or more.
  • an Al content exceeds 1.0%, Al highly tends to form oxides, resulting in poor penetration of a molten pool during arc welding, thereby causing poor welding, and the formation of oxides causes an inferior surface quality of a product.
  • Al may be contained in an amount of 0.2 to 1.0%, more advantageously in an amount of 0.2 to 0.8%.
  • Phosphorus (P) 0.1% or less
  • Phosphorus (P) is an element promoting segregation and causing cracks during casting, and is preferably contained as low as possible. If a P content exceeds 0.1%, castability may deteriorate. Therefore, P may be contained in an amount of 0.1% or less.
  • S is an element forming an inclusion such as MnS to hinder the physical properties of the steel.
  • S is preferably contained as low as possible. If an S content exceeds 0.01%, there is a problem of hot embrittlement. Therefore, S may be contained in an amount of 0.01% or less.
  • N Nitrogen (N) is bonded to titanium (Ti) to form Ti nitrides, but if an N content exceeds 0.03%, free nitrogen (free N) remaining after being bonded to Ti causes problems such as age hardening, which greatly deteriorates a toughness of a base material, and cracks in surfaces of a slab and a steel plate, which deteriorate a surface quality. Therefore, N may be contained in an amount of 0.03% or less.
  • the other component is iron (Fe).
  • unintended impurities may be inevitably mixed from raw materials or surrounding environments in a general manufacturing process, and the impurities cannot be excluded.
  • impurities are known to those of ordinary skill in manufacturing industries, and thus, all descriptions thereof will not be particularly provided in the present specification.
  • the nonmagnetic steel having the above-described alloy composition according to the present disclosure preferably has a single-phase austenite structure as a microstructure.
  • the single-phase austenite structure makes it possible to keep the steel nonmagnetic even though the steel is subjected to external energy.
  • the nonmagnetic steel according to the present disclosure has a highly stable austenite phase by optimizing an alloy composition, and accordingly, has a relative permeability of 1.01 or less in a magnetic field of 50 kA/m as a characteristic thereof.
  • Loss caused by an eddy current in a material exposed to an electromagnetic field is closely related to the magnetism of the material.
  • the magnetism is proportional to permeability ( ⁇ ). That is, the greater the permeability, the greater the magnetism.
  • a reduction in permeability decreases the magnetism of the material, thereby preventing eddy current loss on a surface when exposed to an electric field, resulting in an increase in energy efficiency.
  • the steel according to the present disclosure may be a thick steel sheet having a thickness of 10 to 40 mm with excellent strength and ductility. Specifically, the steel according to the present disclosure may secure a tensile strength of 450 MPa or more and an elongation of 55% or more.
  • the steel slab is reheated at a temperature of 1100 to 1250°C.
  • the temperature for reheating the steel slab is less than 1100°C, a rolling load may be excessively applied during subsequent hot rolling. On the other hand, if the temperature exceeds 1250°C, severe oxidation may occur internally, resulting in a deterioration in surface quality.
  • the reheating of the steel slab may be performed at a temperature of 1100 to 1250°C.
  • the steel slab reheated as described above may be hot rolled to manufacture a thick steel sheet. At this time, it is preferable to perform finish-hot rolling at a temperature of 800 to 1000°C.
  • the temperature for the finish-hot rolling is less than 800°C, there is a problem in that a load increases during rolling. Meanwhile, the higher the temperature for the finish-hot rolling, the lower the deformation resistance, making the rolling easier, while coarsening the structure and thereby making it impossible to secure target strength. Therefore, the temperature for the finish-hot rolling is preferably limited to 1000°C or less.
  • the thick steel sheet manufactured as described above may be cooled.
  • the cooling is preferably performed at a cooling rate sufficient to suppress formation of carbides in grain boundaries, more preferably at a cooling rate of 10°C/s or higher.
  • a higher cooling rate is more advantageous, and thus, there is no need to particularly limit an upper limit for the cooling rate as long as the cooling rate is within an accelerated cooling rate range.
  • the upper limit may be limited to 80°C/s or less.
  • the cooling of the thick steel sheet may be stopped at a temperature of 500°C or less.
  • the accelerated cooling is performed as described above, if the cooling is stopped at an excessively high temperature, there is a concern that carbides may be generated and grown. When the carbides are generated in a large amount, there may be a problem in that the stability of the austenite decreases and the permeability properties deteriorate.
  • a lower limit for the temperature at which the cooling is terminated is not particularly limited.
  • the final steel (thick steel sheet) obtained by completing the hot rolling and the cooling according to the present disclosure has a highly stable austenite phase with a microstructure, and accordingly has excellent weldability and nonmagnetic properties as well as high strength and high ductility.
  • the steel slabs were reheated at 1200°C and then finish-hot rolled at 950°C to manufacture respective thick steel sheets. Thereafter, the manufactured thick steel sheets were cooled at 20°C/s, and the cooling was terminated at 400°C.
  • a yield strength (YS), a tensile strength (TS), and an elongation (El) were measured for each of the thick steel sheets manufactured as described above.
  • the results are shown in Table 2 below.
  • the yield strength (YS) is expressed as a 0.2% offset value.
  • the permeability refers to a relative permeability which is a ratio of permeability in specific atmosphere to permeability in vacuum.
  • the relative permeability ( ⁇ ) i.e. a ratio between the permeability in the vacuum and the permeability in the atmosphere, was measured using paramagnetic measurement equipment.
  • Conventional Steel that is, stainless steel containing Cr and Ni in a large amount, had a low relative permeability, but it was difficult to secure ductility, and manufacturing costs may be greatly increased because expensive elements were added in a large amount thereto.
  • Comparative Steel 2 containing Cr in a large amount and Comparative Steel 3 containing C in a large amount with a low Al content have a very inferior permeability of 1.01 or more.
  • Comparative Steel 1 having a relatively high Al content without containing Cr and Mo and Comparative Steel 4 having an excessive Al content while containing C in a large amount have a permeability of 1.01 with inferior weldability. Based thereon, it is considered that the strong deoxidation effect of Al in the steel deteriorates arc stability, resulting in surface bead defects, thereby causing welding defects. In addition, it was seen that the strong deoxidation effect of Al in the steel improved recovery rates of other elements such as Ti and precipitate phases such as Al 2 O 3 and Ti (Al) (C.N) were formed, resulting in a deterioration in impact toughness, material quality, or the like.
  • FIG. 1 shows a comparison of results of measuring permeability values of Inventive Steel 2 and Comparative Steel 3, and it can be seen therefrom that Inventive Steel 2 keeps a low permeability overall, whereas Comparative Steel 3 keeps a high permeability.
  • the nonmagnetic steel satisfying the alloy composition proposed in the present disclosure can be obtained at a lower cost.
  • the nonmagnetic steel according to the present disclosure is excellent in weldability as well as strength and ductility, and thus, it is expected that application thereof can be expanded.

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  • 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 Steel (AREA)
EP19875440.0A 2018-10-25 2019-10-25 Acier non magnétique à haute résistance et ductilité élevée ayant une excellente soudabilité, et son procédé de fabrication Pending EP3872209A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
KR1020180128433A KR102119962B1 (ko) 2018-10-25 2018-10-25 용접성이 우수한 고강도 및 고연성 비자성 강재 및 이의 제조방법
PCT/KR2019/014166 WO2020085849A1 (fr) 2018-10-25 2019-10-25 Acier non magnétique à haute résistance et ductilité élevée ayant une excellente soudabilité, et son procédé de fabrication

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EP3872209A4 EP3872209A4 (fr) 2021-09-01
EP3872209A1 true EP3872209A1 (fr) 2021-09-01

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EP (1) EP3872209A1 (fr)
KR (1) KR102119962B1 (fr)
CN (1) CN112888803A (fr)
WO (1) WO2020085849A1 (fr)

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JPH02104633A (ja) * 1989-07-28 1990-04-17 Daido Steel Co Ltd 高強度非磁性高マンガン鋼
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JP4529872B2 (ja) * 2005-11-04 2010-08-25 住友金属工業株式会社 高Ｍｎ鋼材及びその製造方法
KR100985286B1 (ko) * 2007-12-28 2010-10-04 주식회사 포스코 내지연파괴 특성이 우수한 고강도 고망간강 및 제조방법
EP2402472B2 (fr) * 2010-07-02 2017-11-15 ThyssenKrupp Steel Europe AG Acier à résistance élevée pouvant être déformé à froid et produit plat en acier constitué d'un tel acier
JP2013023742A (ja) * 2011-07-22 2013-02-04 Kobe Steel Ltd 非磁性鋼線材又は棒鋼
JP6002779B2 (ja) * 2011-12-23 2016-10-05 ポスコＰｏｓｃｏ 非磁性高強度高マンガン鋼板及びその製造方法
KR20160078840A (ko) * 2014-12-24 2016-07-05 주식회사 포스코 항복 강도 및 성형성이 우수한 고강도 고망간강 및 그 제조방법
JP6693217B2 (ja) * 2015-04-02 2020-05-13 日本製鉄株式会社 極低温用高Ｍｎ鋼材

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WO2020085849A8 (fr) 2020-10-08
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