EP2924131B1 - Hochmanganhaltiger austenitischer edelstahl - Google Patents

Hochmanganhaltiger austenitischer edelstahl Download PDF

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Publication number
EP2924131B1
EP2924131B1 EP14162191.2A EP14162191A EP2924131B1 EP 2924131 B1 EP2924131 B1 EP 2924131B1 EP 14162191 A EP14162191 A EP 14162191A EP 2924131 B1 EP2924131 B1 EP 2924131B1
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EP
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Prior art keywords
stainless steel
manganese
cold
austenitic
austenitic high
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EP14162191.2A
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English (en)
French (fr)
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EP2924131A1 (de
Inventor
Arno Breuer
Gabriele BRÜCKNER
Linda Mosecker
Wolfgang Bleck
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Outokumpu Oyj
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Outokumpu Oyj
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Priority to SI201431382T priority Critical patent/SI2924131T1/sl
Application filed by Outokumpu Oyj filed Critical Outokumpu Oyj
Priority to PL14162191T priority patent/PL2924131T3/pl
Priority to ES14162191T priority patent/ES2749234T3/es
Priority to RSP20191231 priority patent/RS59347B1/sr
Priority to LTEP14162191.2T priority patent/LT2924131T/lt
Priority to HUE14162191A priority patent/HUE046585T2/hu
Priority to EP14162191.2A priority patent/EP2924131B1/de
Priority to DK14162191.2T priority patent/DK2924131T3/da
Priority to PT141621912T priority patent/PT2924131T/pt
Priority to KR1020167030176A priority patent/KR101830563B1/ko
Priority to US15/129,502 priority patent/US20170121797A1/en
Priority to MX2016012672A priority patent/MX2016012672A/es
Priority to TW104109969A priority patent/TW201540850A/zh
Priority to PCT/EP2015/056749 priority patent/WO2015144896A2/en
Priority to JP2016559607A priority patent/JP2017512906A/ja
Priority to CN201580016940.2A priority patent/CN106133177B/zh
Publication of EP2924131A1 publication Critical patent/EP2924131A1/de
Priority to ZA2016/06617A priority patent/ZA201606617B/en
Application granted granted Critical
Publication of EP2924131B1 publication Critical patent/EP2924131B1/de
Priority to HRP20191717 priority patent/HRP20191717T1/hr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

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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
    • 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
    • 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
    • C21D8/0236—Cold 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
    • C22C38/02—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
    • C22C38/40—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
    • 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
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—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
    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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

Definitions

  • the invention relates to an austenitic high-manganese stainless steel having high strength and high ductility, wherein the stainless steel utilizes the TWIP (TWinning Induced Plasticity) mechanism during the deformation process.
  • TWIP TWinning Induced Plasticity
  • the austenitic stainless steels such as the most versatile and widely used 304 austenitic stainless steel, have a significantly lower strength combined with relatively high residual elongation after cold deformation, such as cold rolling.
  • the ferritic austenitic duplex stainless steels such as the 2304 ferritic austenitic duplex stainless steel, offer a high strength, but loose ductility with even a low cold deformation degree.
  • the austenitic manganese stainless steels with high carbon content are vulnerable to intergranular corrosion after welding in the weld and heat-affected zone due to chromium depletion in this area. Further, the typical manganese stainless steels are in general vulnerable to form martensitic phase after cold deformation, which could lead to delayed cracking.
  • the FR patent 2071667 relates to a nickel-free austenitic stainless steel which contains weight % 0.02 to 0.3 % carbon, 0.1 to 0.3 % silicon, 12.0 to 16.0 % chromium, 8.0 to 17.0 % manganese, 0.05 to 0.3 % nitrogen, 0.1 to 3.0 % copper, 0.1 to 3.0 % molybdenum, the balance being iron and evitable impurities.
  • the object of the FR patent application 2071667 is to have improved softening and better forming properties. However, based on the chemical composition of the FR patent application 2071667 the manganese (Mn) content should not contain more than 17 weight %, because a higher content produces less austenite phase.
  • the EP patent application 1069202 describes a method for manufacturing an austenitic, paramagnetic stainless steel and the steel consists, by weight %, of up to about 0.1 % carbon, about 0.21 to about 0.6 % silicon, about 17 to about 24 % chromium, up to about 2.5 % nickel, greater than about 20 % to less than about 30 % manganese, greater than about 0.6 % to less than about 1.4 % % nitrogen, up to about 0.3 % copper, up to about 1.9 % molybdenum, up to about 0.002 % boron, up to about 0.8 % carbide-forming elements, such as titanium, zirconium, vanadium and niobium, the balance being iron and evitable impurities.
  • Manganese is provided to increase the nitrogen solubility and to stabilize the austenitic and/or ferrite-free microstructure.
  • the material is hot-formed at a temperature of at least 850 °C to a degree of deformation of at least about 3,5 times and actively cooled.
  • the second step it is cold-formed in a deformation of 5 - 20 % below the deposit temperature of nitrides at elevated temperature below 600 °C, but greater than 350 °C.
  • the deformation is in every process step thus carried out at an elevated temperature which increases the manufacturing costs of the produced material.
  • a twinning in the microstructure of a metal material is in general defined as two separate crystals that share some of the same crystal lattice.
  • the TWIP (TWinning Induced Plasticity) stainless steels have austenitic microstructure with face-centered cubic lattice (FCC) along with a relatively low stacking fault energy (SFE) promoting the activation of twinning deformation mechanism, i.e. mechanically induced twinning in the crystal lattice.
  • FCC face-centered cubic lattice
  • SFE stacking fault energy
  • TWIP indicates that twinning often goes along with accomodation plasticity via lattice dislocations.
  • the object of the present invention is to eliminate some drawbacks of the prior art and to achieve an improved austenitic high-manganese stainless steel which utilizes the TWIP (TWinning Induced Plasticity) mechanism in the cold deformation in order to have a high work-hardening rate and good corrosion resistance with low vulnerability for intergranular corrosion after welding and for delayed cracking and stress corrosion cracking.
  • TWIP TWinning Induced Plasticity
  • the austenitic high-manganese stainless steel consists of in weight % 0,03 - 0,1 % carbon, 0,08 - 1,0 % silicon, 14 - 26 % manganese. 10,5 - 18 % chromium, less than 0,8 % nickel, 0,05 - 0,6 % copper, 0,1 - 0,8 % nitrogen and 0,0008 - 0,005 % boron, the rest being iron and inevitable impurities occurred in stainless steels.
  • the austenitic stainless steel of the invention further contains optionally 0,001 - 0,02 % titanium and optionally less than 0,04 % aluminium.
  • the austenitic stainless steel of the invention has a superior ductility and high strength after plastic deformation utilizing in the cold deformation the TWIP (TWinning Induced Plasticity) mechanism.
  • the austenitic stainless steel of the invention combines thus a high strength in the initial annealed state and a high work hardening rate with a high elongation after the cold deformation, such as cold rolling, in connection with a low nickel content.
  • the ranges for the yield strength R p0,2 and the tensile strength R m as well as the elongation to fracture A 80 at the annealed state the austenitic high-manganese stainless steel in accordance with the invention are 470 - 600 MPa for R p0,2 , 800 - 930 MPa for R m and 40 - 60 % for A 80 after annealed at the temperature range of 1000 - 1150 °C.
  • the austenitic high-manganese stainless steel of the invention has a high work-hardening rate of at least 20 % with the deformation degree 10 % and at least 40 % with the deformation degree 20 % for the yield strength R p0,2 . Further, the elongation to fracture A 80 is 25 - 35 % with the deformation degree 10 % and 10 - 20 % with the deformation degree 20 % showing the good ductility.
  • Carbon (C) is a valuable austenite forming and stabilizing element, which enables reduced use of expensive elements nickel and copper.
  • the upper limit for carbon alloying (less than 0,1 %) is set by the risk of carbide precipitation, which deteriorates the corrosion resistance of the stainless steel.
  • the carbon content is low enough to maintain good corrosion resistance. The reduction of the carbon content to low levels by the decarburization process is non-economical, and therefore, the carbon content shall not be less than 0,03 %.
  • Silicon (Si) is added to stainless steels for deoxidizing purposes during melting and should not be below 0,08 %. Because silicon is a ferrite forming element, its content must be limited below 1 %.
  • Manganese (Mn) is a key element of the austenitic stainless steel of the invention, ensuring the stable austenitic crystal structure and enabling the twinning mechanism and, further, the reduction of the use of more expensive nickel. Manganese also increases the solubility of nitrogen to the stainless steel. Plastic deformation accompanied with twinning deformation easily occurs in the case of an amount of manganese of 14 % or more without deformed structure, i.e. the strain-induced martensite. A high manganese content makes the decarburization process of the steel more difficult, impairs the surface quality and reduces the corrosion resistance of the steel. Therefore the manganese content shall be less than 26 %.
  • Chromium (Cr) is responsible of ensuring corrosion resistance of a stainless steel. Therefore, the chromium content in this stainless steel shall be at the minimum 10,5 %. Chromium is important in terms of avoiding the delayed cracking phenomenon. By increasing the content from this level the corrosion resistance of the steel can be improved. However, because chromium is a ferrite forming element, the increasing of the chromium content increases the need for expensive austenite formers, such as nickel and manganese or necessitates impractically high carbon and nitrogen contents. Therefore, the chromium content shall be lower than 18 %. Chromium also increases the solubility of nitrogen.
  • Nickel (Ni) is a strong austenite former and stabilizer, but nickel is an expensive element. However, very low nickel contents would necessitate impractically high alloying with the other austenite forming and stabilizing elements. Therefore, the nickel content shall be preferably lower than 0,8 % but preferably less than 0,5 %.
  • Copper (Cu) is present as a residual of 0,1 - 0,6 %. Copper is a weak stabilizer of the austenite phase but, however, has a strong effect on the resistance to martensite formation. Copper also has a positive effect on ductility and forming properties.
  • Nitrogen (N) is a strong austenite former and stabilizer. Therefore, nitrogen alloying improves the cost efficiency of the steel by enabling lower use of nickel and copper.
  • nitrogen content shall be at least 0,1 %. High nitrogen contents increase the strength of the steel and thus make forming operations more difficult. Furthermore, risk of nitride precipitation increases with increasing nitrogen content. For these reasons, the nitrogen content shall not exceed 0,8 %, preferably the nitrogen content shall be lower than 0,6 %.
  • Nitrogen increases the stacking fault energy (SFE), which is used for the prediction of the TWIP-effect, and thus enables for and facilitates the TWIP-effect.
  • SFE stacking fault energy
  • the austenitic stainless steel according to the invention does not form during cold rolling any deformation martensite at the room temperature or above. Therefore, the stainless steel of the invention has a high ductility.
  • the austenitic stainless steel according to the invention is also free of stress corrosion cracking and delayed cracking, just even after aging process in air and also in 5 % sodium chloride (NaCl) environment.
  • the austenitic stainless steel in accordance with invention was melted in the production scale and then cast into a slab form with the chemical composition in weight %, where the Mo-content of 0.02% is an accidental impurity.
  • Table 2 C Si Mn Cr Mo Ni Ti Cu Al N B 0.08 0.5 20 13 0.02 0.2 0.003 0.5 0.01 0.43 0.0023
  • the slabs were further hot rolled into the thickness of 4,0 mm and then annealed at the temperature 1080 °C.
  • the austenitic stainless steel of the invention was further cold rolled with the rolling degree of 50 % to the thickness of 2,0 mm and annealed at the temperature 1080 °C.
  • the annealed strip product was then tested by determining the yield strength R p0,2 and the tensile strength R m as well as the elongation to fracture A 80 .
  • the stainless steel strip was cold deformed with the reduction degree of 10 % and then determined the yield strength R p0,2 and the tensile strength R m as well as the elongation to fracture A 80 .
  • the respective actions were also made for the cold deformed strip having the reduction degree of 20 %.
  • the results for those test results are described in the following table: Table 3 Reduction degree R p0,2 (MPa) R m (MPa) A 80 (%) 0 % 500 830 48 10 % 800 950 28 20 % 1020 1180 14
  • the austenitic stainless steel in accordance with the invention has high work-hardening rate for the yield strength R p0,2 .
  • the elongation to fracture A 80 is 28 % with the deformation degree 10 % and 14 % with the deformation degree 20 % shows still a good ductility at high strength after cold rolling.
  • the austenitic stainless steel of the invention can be manufactured as slabs, blooms, billets and flat products such as coils, strips, plates, sheets, and long products such as bars, rods, wires, profiles and shapes, and tubular products such as pipes, tubes and can be applied for instance in automotive construction, tanks and crash relevant parts, construction and rail vehicles.
  • the high-manganese austenitic stainless steel in accordance with the invention can be cold deformed in the state of as hot strip annealed, as cold strip annealed and as hot and cold strip annealed and cold rolled in order to utilize the TWIP effect for higher yield and tensile strength values with still high ductility.

Claims (9)

  1. Austenitischer hochmanganhaltiger rostfreier Stahl mit hoher Festigkeit und Duktilität, dadurch gekennzeichnet, dass der rostfreie Stahl, in Gewichts-%, aus 0,03 bis 0,1 % Kohlenstoff, 0,08 bis 1,0 % Silicium, 14 bis 26 % Mangan, 10,5 bis 18 % Chrom, unter 0,8 % Nickel, 0,05 bis 0,6 % Kupfer, 0,1 bis 0,8 % Stickstoff und 0,0008 bis 0,005 % Bor, wobei der Rest Eisen und unvermeidbare Verunreinigungen sind, die in rostfreien Stählen vorkommen, gegebenenfalls 0,001 bis 0,02 % Titan und gegebenenfalls unter 0,04 % Aluminium besteht; und im Zustand des Glühens im Temperaturbereich von 1000 bis 1150 °C die Bereiche für die Streckgrenze Rp0,2 und die Zugfestigkeit Rm sowie die Bruchdehnung A80 470 bis 600 MPa für Rp0,2, 800 bis 930 MPa für Rm und 40 bis 60 % für A80 lauten, und der Stahl unter Verwendung des TWIP-Mechanismus oder Mechanismus der durch Zwillingsbildung induzierten Plastizität kaltverformbar ist, sodass die Kaltverfestigungsgeschwindigkeit auf Grundlage eines Kaltverformungsgrads von 10 % für die Streckgrenze Rp0,2 mindestens 20 % beträgt.
  2. Austenitischer hochmanganhaltiger rostfreier Stahl nach Anspruch 1, dadurch gekennzeichnet, dass die Kaltverfestigungsgeschwindigkeit auf Grundlage des Kaltverformungsgrads von 20 % für die Streckgrenze Rp0,2 mindestens 40 % beträgt.
  3. Austenitischer hochmanganhaltiger rostfreier Stahl nach einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, dass die Bruchdehnung A80 25 bis 35 % beim Kaltverformungsgrad von 10 % beträgt.
  4. Austenitischer hochmanganhaltiger rostfreier Stahl nach einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, dass die Bruchdehnung A80 10 bis 20 % beim Kaltverformungsgrad von 20 % beträgt.
  5. Austenitischer hochmanganhaltiger rostfreier Stahl nach einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, dass der rostfreie Stahl im Zustand als warmgewalztes Band, das im Temperaturbereich von 1000 bis 1150 °C geglüht wurde, für den TWIP-Effekt kaltverformbar ist.
  6. Austenitischer hochmanganhaltiger rostfreier Stahl nach einem der vorhergehenden Ansprüche 1 bis 4, dadurch gekennzeichnet, dass der rostfreie Stahl im Zustand als kaltgewalztes Band, das im Temperaturbereich von 1000 bis 1150 °C geglüht wurde, für den TWIP-Effekt kaltverformbar ist.
  7. Austenitischer hochmanganhaltiger rostfreier Stahl nach einem der vorhergehenden Ansprüche 1 bis 4, dadurch gekennzeichnet, dass der rostfreie Stahl im Zustand als Warm- und Kaltband, das im Temperaturbereich von 1000 bis 1150 °C geglüht wurde, und im Zustand des Kaltwalzens für den TWIP-Effekt kaltverformbar ist.
  8. Austenitischer hochmanganhaltiger rostfreier Stahl nach einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, dass der austenitische rostfreie Stahl als Brammen, Blöcke, Knüppel, Flachprodukte wie Bunde, Bänder, Platten, Bleche, Langprodukte wie Stäbe, Stangen, Drähte, Profile und Träger, Rohrprodukte wie Rohre, Röhren hergestellt ist.
  9. Austenitischer hochmanganhaltiger rostfreier Stahl nach einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, dass der austenitische rostfreie Stahl beispielsweise im Fahrzeugbau, bei Behältern und crashrelevanten Teilen, im Baugewerbe und bei Schienenfahrzeugen angewendet wird.
EP14162191.2A 2014-03-28 2014-03-28 Hochmanganhaltiger austenitischer edelstahl Active EP2924131B1 (de)

Priority Applications (18)

Application Number Priority Date Filing Date Title
PL14162191T PL2924131T3 (pl) 2014-03-28 2014-03-28 Austenityczna wysokomanganowa stal nierdzewna
ES14162191T ES2749234T3 (es) 2014-03-28 2014-03-28 Acero inoxidable austenítico con alto contenido en manganeso
RSP20191231 RS59347B1 (sr) 2014-03-28 2014-03-28 Austenitni nerđajući čelik sa visokim sadržajem mangana
LTEP14162191.2T LT2924131T (lt) 2014-03-28 2014-03-28 Austenitinis manganinis nerūdijantis plienas
HUE14162191A HUE046585T2 (hu) 2014-03-28 2014-03-28 Ausztenites, magas mangántartalmú rozsdamentes acél
EP14162191.2A EP2924131B1 (de) 2014-03-28 2014-03-28 Hochmanganhaltiger austenitischer edelstahl
DK14162191.2T DK2924131T3 (da) 2014-03-28 2014-03-28 Austenitisk rustfrit stål
PT141621912T PT2924131T (pt) 2014-03-28 2014-03-28 Aço inoxidável austenítico com elevado teor em manganês
SI201431382T SI2924131T1 (sl) 2014-03-28 2014-03-28 Avstenitno visokomangansko nerjavno jeklo
MX2016012672A MX2016012672A (es) 2014-03-28 2015-03-27 Acero inoxidable austenitico.
KR1020167030176A KR101830563B1 (ko) 2014-03-28 2015-03-27 오스테나이트계 스테인리스강
TW104109969A TW201540850A (zh) 2014-03-28 2015-03-27 沃斯田鐵系不銹鋼
PCT/EP2015/056749 WO2015144896A2 (en) 2014-03-28 2015-03-27 Austenitic stainless steel
JP2016559607A JP2017512906A (ja) 2014-03-28 2015-03-27 オーステナイト系ステンレス鋼
CN201580016940.2A CN106133177B (zh) 2014-03-28 2015-03-27 奥氏体不锈钢
US15/129,502 US20170121797A1 (en) 2014-03-28 2015-03-27 Austenitic stainless steel
ZA2016/06617A ZA201606617B (en) 2014-03-28 2016-09-23 Austenitic stainless steel
HRP20191717 HRP20191717T1 (hr) 2014-03-28 2019-09-20 Austenitičan nehrđajući čelik s visokim udjelom mangana

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP14162191.2A EP2924131B1 (de) 2014-03-28 2014-03-28 Hochmanganhaltiger austenitischer edelstahl

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EP2924131A1 EP2924131A1 (de) 2015-09-30
EP2924131B1 true EP2924131B1 (de) 2019-08-21

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EP14162191.2A Active EP2924131B1 (de) 2014-03-28 2014-03-28 Hochmanganhaltiger austenitischer edelstahl

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US (1) US20170121797A1 (de)
EP (1) EP2924131B1 (de)
JP (1) JP2017512906A (de)
KR (1) KR101830563B1 (de)
CN (1) CN106133177B (de)
DK (1) DK2924131T3 (de)
ES (1) ES2749234T3 (de)
HR (1) HRP20191717T1 (de)
HU (1) HUE046585T2 (de)
LT (1) LT2924131T (de)
MX (1) MX2016012672A (de)
PL (1) PL2924131T3 (de)
PT (1) PT2924131T (de)
RS (1) RS59347B1 (de)
SI (1) SI2924131T1 (de)
TW (1) TW201540850A (de)
WO (1) WO2015144896A2 (de)
ZA (1) ZA201606617B (de)

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EP3173504A1 (de) * 2015-11-09 2017-05-31 Outokumpu Oyj Verfahren zur herstellung eines austenitischen stahlbauteils und verwendung des bauteils
EP3301197B1 (de) 2016-09-29 2021-10-27 Outokumpu Oyj Verfahren zur kaltverformung eines austenitischen stahls
PL3360981T3 (pl) * 2017-02-10 2020-12-14 Outokumpu Oyj Element stalowy wytworzony przez formowanie na gorąco, sposób wytwarzania i zastosowanie tego elementu
KR102020507B1 (ko) * 2017-12-20 2019-09-10 주식회사 포스코 강도, 표면전도성이 향상된 비자성 오스테나이트계 스테인리스강
CN108103404A (zh) * 2017-12-28 2018-06-01 长沙无道工业设计有限公司 一种高强度不锈钢合金材料及其制备方法
JP7326454B2 (ja) * 2019-01-22 2023-08-15 アペラム 溶接性の改善された鉄－マンガン合金
KR20200092635A (ko) * 2019-01-25 2020-08-04 엘지이노텍 주식회사 디스플레이용 기판
CN110607479B (zh) * 2019-04-24 2021-11-05 上海大学 气门弹簧用不锈钢及其钢丝的制备方法
CN110103530B (zh) * 2019-06-04 2023-03-31 河北工业大学 一种高性能耐蚀twip/不锈钢多层复合材料及制备方法
CN111500942B (zh) * 2020-05-11 2021-08-10 湖南恒基粉末科技有限责任公司 一种高氮含量无磁不锈钢粉末及其制备方法
CN113046534B (zh) * 2021-03-15 2023-02-03 长春工业大学 一种高孪晶密度的高氮无镍奥氏体不锈钢的制备方法
CN113913693A (zh) * 2021-10-08 2022-01-11 赵洪运 一种高强耐蚀海洋工程不锈钢及其制备方法
CN114686784A (zh) * 2022-04-02 2022-07-01 四川罡宸不锈钢有限责任公司 一种节镍型奥氏体不锈钢材料及制备方法

Family Cites Families (18)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE728159C (de) * 1936-10-09 1942-11-21 Boehler & Co Ag Geb Chrom-Mangan-Stickstoff-Stahl
AT214466B (de) * 1959-06-04 1961-04-10 Schoeller Bleckmann Stahlwerke Stahllegierungen zur Herstellung von Schwerstangen für Tiefbohrgestänge
BE754614A (fr) * 1969-12-27 1971-01-18 Nisshin Steel Co Ltd Aciers inoxydables austenitiques
US3904401A (en) * 1974-03-21 1975-09-09 Carpenter Technology Corp Corrosion resistant austenitic stainless steel
JPH0619110B2 (ja) * 1986-05-19 1994-03-16 株式会社神戸製鋼所 極低温用高Ｍｎオ−ステナイトステンレス鋼の製造方法
JPH0536481A (ja) * 1991-07-31 1993-02-12 Toshiba Lighting & Technol Corp 放電ランプ点灯装置
JP2978427B2 (ja) * 1995-05-22 1999-11-15 株式会社神戸製鋼所 極低温用高Ｍｎ非磁性鋼及び製造方法
JPH11209823A (ja) * 1998-01-23 1999-08-03 Kobe Steel Ltd プレス成形性の優れた高強度鋼板の製造方法
AT407882B (de) * 1999-07-15 2001-07-25 Schoeller Bleckmann Oilfield T Verfahren zur herstellung eines paramagnetischen, korrosionsbeständigen werkstoffes u.dgl. werkstoffe mit hoher dehngrenze, festigkeit und zähigkeit
JP5057055B2 (ja) * 2007-07-30 2012-10-24 大同特殊鋼株式会社 非磁性ステンレス鋼の鍛造製品、該鍛造製品を用いたドリルカラー及び該鍛造製品の製造方法
DE102008005803A1 (de) 2008-01-17 2009-07-23 Technische Universität Bergakademie Freiberg Bauteil aus höher kohlnstoffhaltigem austenitischem Stahlformguss, Verfahren zu deren Herstellung und deren Verwendung
CN101250674A (zh) * 2008-04-11 2008-08-27 江苏大学 一种中氮高锰奥氏体不锈钢
JP5444561B2 (ja) * 2009-02-27 2014-03-19 日本冶金工業株式会社 高Ｍｎオーステナイト系ステンレス鋼と服飾用金属部品
DE102009003598A1 (de) * 2009-03-10 2010-09-16 Max-Planck-Institut Für Eisenforschung GmbH Korrosionsbeständiger austenitischer Stahl
DE102010026808B4 (de) * 2010-07-10 2013-02-07 Technische Universität Bergakademie Freiberg Korrosionsbeständiger austenithaltiger phosphorlegierter Stahlguss mit TRIP- bzw. TWIP-Eigenschaften und seine Verwendung
US20120156085A1 (en) * 2010-12-14 2012-06-21 Thompson Peter T Blast Resistant, Non-Magnetic, Stainless Steel Armor
CN102002642A (zh) * 2010-12-31 2011-04-06 上海加宁新技术研究所 一种超高强度无磁不锈钢
CN102560259B (zh) * 2012-01-16 2013-06-19 西南石油大学 一种低成本大膨胀率膨胀管用twip钢的钢管制备方法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
None *

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PT2924131T (pt) 2019-10-30
MX2016012672A (es) 2016-12-14
KR101830563B1 (ko) 2018-02-20
RS59347B1 (sr) 2019-10-31
CN106133177A (zh) 2016-11-16
KR20160140828A (ko) 2016-12-07
US20170121797A1 (en) 2017-05-04
TW201540850A (zh) 2015-11-01
CN106133177B (zh) 2018-04-27
SI2924131T1 (sl) 2019-12-31
ZA201606617B (en) 2018-05-30
HRP20191717T1 (hr) 2019-12-13
WO2015144896A2 (en) 2015-10-01
WO2015144896A3 (en) 2016-03-17
ES2749234T3 (es) 2020-03-19
DK2924131T3 (da) 2019-10-14
LT2924131T (lt) 2019-09-25
EP2924131A1 (de) 2015-09-30
JP2017512906A (ja) 2017-05-25
PL2924131T3 (pl) 2020-02-28

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