EP2924131A1 - Austenitic stainless steel - Google Patents

Austenitic stainless steel Download PDF

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Publication number
EP2924131A1
EP2924131A1 EP14162191.2A EP14162191A EP2924131A1 EP 2924131 A1 EP2924131 A1 EP 2924131A1 EP 14162191 A EP14162191 A EP 14162191A EP 2924131 A1 EP2924131 A1 EP 2924131A1
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EP
European Patent Office
Prior art keywords
stainless steel
manganese
austenitic
cold
steel according
Prior art date
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Application number
EP14162191.2A
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German (de)
French (fr)
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EP2924131B1 (en
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/en
Application filed by Outokumpu Oyj filed Critical Outokumpu Oyj
Priority to RSP20191231 priority patent/RS59347B1/en
Priority to LTEP14162191.2T priority patent/LT2924131T/en
Priority to PL14162191T priority patent/PL2924131T3/en
Priority to ES14162191T priority patent/ES2749234T3/en
Priority to HUE14162191A priority patent/HUE046585T2/en
Priority to PT141621912T priority patent/PT2924131T/en
Priority to DK14162191.2T priority patent/DK2924131T3/en
Priority to EP14162191.2A priority patent/EP2924131B1/en
Priority to JP2016559607A priority patent/JP2017512906A/en
Priority to US15/129,502 priority patent/US20170121797A1/en
Priority to MX2016012672A priority patent/MX2016012672A/en
Priority to CN201580016940.2A priority patent/CN106133177B/en
Priority to TW104109969A priority patent/TW201540850A/en
Priority to PCT/EP2015/056749 priority patent/WO2015144896A2/en
Priority to KR1020167030176A priority patent/KR101830563B1/en
Publication of EP2924131A1 publication Critical patent/EP2924131A1/en
Priority to ZA2016/06617A priority patent/ZA201606617B/en
Application granted granted Critical
Publication of EP2924131B1 publication Critical patent/EP2924131B1/en
Priority to HRP20191717 priority patent/HRP20191717T1/en
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—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
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys 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

Definitions

  • the invention relates to an austenitic high-manganese stainless steel having high strength and high ductility which 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.
  • 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 po,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 % 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 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.

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

The invention relates to an austenitic high-manganese stainless steel having high strength and ductility. The stainless steel which 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, and the stainless steel is cold deformable utilizing the TWIP (TWinning Induced Plasticity) mechanism.

Description

  • The invention relates to an austenitic high-manganese stainless steel having high strength and high ductility which stainless steel utilizes the TWIP (TWinning Induced Plasticity) mechanism during the deformation process.
  • 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.
  • 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. The term 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. The essential features of the austenitic stainless steel are enlisted in the appended claims.
  • According to the invention 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 Rp0,2 and the tensile strength Rm as well as the elongation to fracture A80 at the annealed state the austenitic high-manganese stainless steel in accordance with the invention are 470 - 600 MPa for Rp0,2, 800 - 930 MPa for Rm and 40 - 60 % for A80 after annealed at the temperature range of 1000 - 1150 °C. When the austenitic stainless steel in accordance with the invention was further cold deformed, such as cold rolled, the effect of TWIP (TWinning Induced Plasticity) mechanism can be shown by means of the respective ranges for the yield strength Rp0,2 and the tensile strength Rm as well as the elongation to fracture A80 enlisted in the following table 1 after the cold rolling with the reduction degrees of 10 % and 20 %: Table 1
    Deformation degree Rp0,2 (MPa) Rm (MPa) A80 (%)
    10% 800-900 900-1030 25 - 35
    20 % 1000-1100 1100-1250 10-20
  • 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 Rpo,2. Further, the elongation to fracture A80 is 25 - 35 % with the deformation degree 10 % and 10 - 20 % with the deformation degree 20 % showing the good ductility.
  • The effects of the main elements in the chemical composition of the austenitic high-manganese stainless steel according to the invention are described, the ranges being in weight %, if not otherwise mentioned.
  • 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. In order to ensure reasonably low use of the above-mentioned alloying elements, 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.
  • 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.
    • Example
  • 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 % 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 Rp0,2 and the tensile strength Rm as well as the elongation to fracture A80.
  • In order to utilize the TWIP effect in the austenitic stainless steel of the invention the stainless steel strip was cold deformed with the reduction degree of 10 % and then determined the yield strength Rp0,2 and the tensile strength Rm as well as the elongation to fracture A80. 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 Rp0,2 (MPa) Rm (MPa) A80 (%)
    0% 500 830 48
    10% 800 950 28
    20 % 1020 1180 14
  • The results show that the austenitic stainless steel in accordance with the invention has high work-hardening rate for the yield strength Rp0,2. Further, the elongation to fracture A80 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 (12)

  1. Austenitic high-manganese stainless steel having high strength and ductility, characterized in that the stainless steel which 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, is cold deformable utilizing the TWIP (TWinning Induced Plasticity) mechanism.
  2. Austenitic high-manganese stainless steel according to the claim 1, characterized in that at the annealed state the ranges for the yield strength Rp0,2 and the tensile strength Rm as well as the elongation to fracture A80 for the austenitic ferromanganese stainless steel are 470 - 600 MPa for Rp0,2, 800 - 930 MPa for Rm and 40 - 60 % for A80.
  3. Austenitic high-manganese stainless steel according to the claim 1 or 2, characterized in that the work-hardening rate based on the cold deformation for the yield strength Rp0,2 is at least 20 % with the cold deformation degree 10 %.
  4. Austenitic high-manganese stainless steel according to the claim 1, 2 or 3, characterized in that the work-hardening rate based on the cold deformation for the yield strength Rp0,2 is at least 40 % with the cold deformation degree 20 %.
  5. Austenitic high-manganese stainless steel according to any of the preceding claims, characterized in that elongation to fracture A80 is 25 - 35 % with the cold deformation degree 10 %.
  6. Austenitic high-manganese stainless steel according to any of the preceding claims, characterized in that elongation to fracture A80 is 10 - 20 % with the cold deformation degree 20 %.
  7. Austenitic high-manganese stainless steel according to any of the preceding claims, characterized in that the stainless steel contains optionally 0,001 - 0,02 % titanium and optionally less than 0,04 % aluminium.
  8. Austenitic high-manganese stainless steel according to any of the preceding claims, characterized in that the stainless steel is cold deformable for the TWIP effect in the state of as hot strip annealed.
  9. Austenitic high-manganese stainless steel according to any of the preceding claims 1 - 7, characterized in that the stainless steel is cold deformable for the TWIP effect in the state of as cold strip annealed.
  10. Austenitic high-manganese stainless steel according to any of the preceding claims 1 - 7, characterized in that the stainless steel is cold deformable for the TWIP effect in the state of as hot and cold strip annealed and cold rolled.
  11. Austenitic high-manganese stainless steel according to any of the preceding claims, characterized in that the austenitic stainless steel is manufactured as slabs, blooms, billets, flat products such as coils, strips, plates, sheets, long products such as bars, rods, wires, profiles and shapes, tubular products such as pipes, tubes.
  12. Austenitic high-manganese stainless steel according to any of the preceding claims, characterized in that the austenitic stainless steel is applied for instance in automotive construction, tanks and crash relevant parts, construction and rail vehicles.
EP14162191.2A 2014-03-28 2014-03-28 Austenitic high-manganese stainless steel Active EP2924131B1 (en)

Priority Applications (18)

Application Number Priority Date Filing Date Title
RSP20191231 RS59347B1 (en) 2014-03-28 2014-03-28 Austenitic high-manganese stainless steel
LTEP14162191.2T LT2924131T (en) 2014-03-28 2014-03-28 Austenitic MANGANIC STAINLESS STEEL
PL14162191T PL2924131T3 (en) 2014-03-28 2014-03-28 Austenitic high-manganese stainless steel
ES14162191T ES2749234T3 (en) 2014-03-28 2014-03-28 Austenitic stainless steel with high manganese content
HUE14162191A HUE046585T2 (en) 2014-03-28 2014-03-28 Austenitic high manganese stainless steel
PT141621912T PT2924131T (en) 2014-03-28 2014-03-28 AUSTENITIC STAINLESS STEEL WITH HIGH MANGANESE CONTENT
DK14162191.2T DK2924131T3 (en) 2014-03-28 2014-03-28 AUSTENITIC STAINLESS STEEL
EP14162191.2A EP2924131B1 (en) 2014-03-28 2014-03-28 Austenitic high-manganese stainless steel
SI201431382T SI2924131T1 (en) 2014-03-28 2014-03-28 Austenitic high manganese stainless steel
MX2016012672A MX2016012672A (en) 2014-03-28 2015-03-27 Austenitic stainless steel.
JP2016559607A JP2017512906A (en) 2014-03-28 2015-03-27 Austenitic stainless steel
CN201580016940.2A CN106133177B (en) 2014-03-28 2015-03-27 Austenitic stainless steel
TW104109969A TW201540850A (en) 2014-03-28 2015-03-27 Vostian Iron Stainless Steel
PCT/EP2015/056749 WO2015144896A2 (en) 2014-03-28 2015-03-27 Austenitic stainless steel
KR1020167030176A KR101830563B1 (en) 2014-03-28 2015-03-27 Austenitic stainless steel
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 (en) 2014-03-28 2019-09-20 Austenitic high-manganese stainless steel

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP14162191.2A EP2924131B1 (en) 2014-03-28 2014-03-28 Austenitic high-manganese stainless steel

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

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CN110103530A (en) * 2019-06-04 2019-08-09 河北工业大学 A kind of high-performance is anti-corrosion TWIP/ stainless steel multilayer composite material and preparation method
EP3705595A4 (en) * 2017-12-20 2020-09-09 Posco Non-magnetic austenitic stainless steel having improved strength and surface conductivity
CN113913693A (en) * 2021-10-08 2022-01-11 赵洪运 High-strength corrosion-resistant ocean engineering stainless steel and preparation method thereof
CN114686784A (en) * 2022-04-02 2022-07-01 四川罡宸不锈钢有限责任公司 Nickel-saving austenitic stainless steel material and preparation method thereof
CN121496295A (en) * 2026-01-13 2026-02-10 山西路安交通科技有限公司 A high-strength stainless steel containing boron for highway guardrails and its preparation method.

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HUE051081T2 (en) * 2017-02-10 2021-03-01 Outokumpu Oy Steel component manufactured by hot forming, method of manufacturing and use of the component
CN108103404A (en) * 2017-12-28 2018-06-01 长沙无道工业设计有限公司 A kind of high-strength stainless steel alloy material and preparation method thereof
CA3126854A1 (en) * 2019-01-22 2020-07-30 Aperam Iron-manganese alloy having improved weldability
KR102665422B1 (en) * 2019-01-25 2024-05-10 엘지이노텍 주식회사 Substrate for display
CN110607479B (en) * 2019-04-24 2021-11-05 上海大学 Stainless steel for valve spring and preparation method thereof
CN111500942B (en) * 2020-05-11 2021-08-10 湖南恒基粉末科技有限责任公司 High-nitrogen-content non-magnetic stainless steel powder and preparation method thereof
CN113046534B (en) * 2021-03-15 2023-02-03 长春工业大学 A preparation method of high nitrogen nickel-free austenitic stainless steel with high twin density
US12221662B2 (en) * 2023-01-12 2025-02-11 City University Of Hong Kong Method of forming a dynamically transformable nanotwinned structure in an austenite steel alloy
CN119980028A (en) * 2025-01-03 2025-05-13 浙江吉森金属科技有限公司 A nickel-saving high-strength non-magnetic stainless steel and a manufacturing method thereof

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EP3705595A4 (en) * 2017-12-20 2020-09-09 Posco Non-magnetic austenitic stainless steel having improved strength and surface conductivity
CN110103530A (en) * 2019-06-04 2019-08-09 河北工业大学 A kind of high-performance is anti-corrosion TWIP/ stainless steel multilayer composite material and preparation method
CN110103530B (en) * 2019-06-04 2023-03-31 河北工业大学 High-performance corrosion-resistant TWIP/stainless steel multilayer composite material and preparation method thereof
CN113913693A (en) * 2021-10-08 2022-01-11 赵洪运 High-strength corrosion-resistant ocean engineering stainless steel and preparation method thereof
CN114686784A (en) * 2022-04-02 2022-07-01 四川罡宸不锈钢有限责任公司 Nickel-saving austenitic stainless steel material and preparation method thereof
CN121496295A (en) * 2026-01-13 2026-02-10 山西路安交通科技有限公司 A high-strength stainless steel containing boron for highway guardrails and its preparation method.

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EP2924131B1 (en) 2019-08-21
RS59347B1 (en) 2019-10-31
MX2016012672A (en) 2016-12-14
ES2749234T3 (en) 2020-03-19
KR20160140828A (en) 2016-12-07
ZA201606617B (en) 2018-05-30
KR101830563B1 (en) 2018-02-20
PL2924131T3 (en) 2020-02-28
US20170121797A1 (en) 2017-05-04
TW201540850A (en) 2015-11-01
CN106133177B (en) 2018-04-27
LT2924131T (en) 2019-09-25
HRP20191717T1 (en) 2019-12-13
JP2017512906A (en) 2017-05-25
HUE046585T2 (en) 2020-03-30
SI2924131T1 (en) 2019-12-31
DK2924131T3 (en) 2019-10-14
PT2924131T (en) 2019-10-30
CN106133177A (en) 2016-11-16
WO2015144896A3 (en) 2016-03-17
WO2015144896A2 (en) 2015-10-01

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