EP3126537B1 - Zweiphasiger edelstahl - Google Patents

Zweiphasiger edelstahl Download PDF

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Publication number
EP3126537B1
EP3126537B1 EP15712762.2A EP15712762A EP3126537B1 EP 3126537 B1 EP3126537 B1 EP 3126537B1 EP 15712762 A EP15712762 A EP 15712762A EP 3126537 B1 EP3126537 B1 EP 3126537B1
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EP
European Patent Office
Prior art keywords
stainless steel
dual
phase
present disclosure
weight
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Not-in-force
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EP15712762.2A
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English (en)
French (fr)
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EP3126537A1 (de
Inventor
David C. Berry
Ronald E. Bailey
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ATI Properties LLC
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ATI Properties LLC
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Priority to PL15712762T priority Critical patent/PL3126537T3/pl
Priority to SI201531308T priority patent/SI3126537T1/sl
Publication of EP3126537A1 publication Critical patent/EP3126537A1/de
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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
    • 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
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • 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
    • C22C38/54—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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • 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
    • C21D2211/008—Martensite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C2200/00—Crystalline structure

Definitions

  • the present disclosure relates to a dual-phase stainless steel having a microstructure of ferrite and tempered martensite.
  • the present disclosure relates to cost-effective stainless steels having improved hardness for abrasion-resistant and/or wear-resistant applications.
  • Dual-phase stainless steels can exhibit a combination of desirable properties that make them useful for a wide variety of industrial applications, such as for oil sands extraction and in the sugar industry. These steels are generally characterized by a microstructure of tempered martensite dispersed in a ferrite matrix.
  • ATI 412TM stainless steel typically contains, by weight, 11.75% chromium (Cr), 0.90% manganese (Mn), 0.70% silicon (Si), 0.40% nickel (Ni), 0.030% sulfur (S), 0.020% carbon (C), 0% to 0.040% phosphorus (P), 0% to 0.030% nitrogen (N), and the balance iron (Fe) and other incidental impurities.
  • ATI 412TM stainless steel typically has a Brinell hardness (HB) of about 177 when annealed at about 766° C., and a Brinell hardness of about 258 when annealed at about 843° C.
  • Duracorr® steel which contains, by weight, 11.0% to 12.5% Cr, 0.20% to 0.35% molybdenum (Mo), 0% to 1.50% Mn, 0% to 1.00% Ni, 0% to 0.70% Si, 0% to 0.040% P, 0% to 0.030% N, 0% to 0.025% C, 0% to 0.015% S, and the balance Fe.
  • Mo molybdenum
  • Duracorr® stainless steel contains Mo as an alloying element, i.e., an intentional alloying addition, and not as an incidental impurity. Because of the rising costs of Mo, however, Duracorr® stainless steel may be too costly for certain applications.
  • Duracorr® stainless steel typically has a hardness of about 223 HB, it can be processed to exhibit nominal hardness of 300 HB, which grade is commercially available as Duracorr® 300 stainless steel.
  • Duracorr® and Duracorr® 300 stainless steels have largely the same composition, but the hardness of Duracorr® 300 stainless steel varies from 260 HB to 360 HB.
  • the increased hardness of Duracorr® 300 stainless steel is accompanied by a reduction in toughness.
  • the Charpy V-notch impact energy of Duracorr® 300 stainless steel at -40° C. is only about 20.3 N-m (15 ft-lb) on average.
  • KR20030037751A discloses a method of manufacturing 12Cr ferritic and martensitic hot rolled stainless steel.
  • the method includes the steps of hot rolling a steel slab comprising 0.03 wt.% or less of C, Cr 11 to 13.5 wt.%, 1.0 wt.% or less of Ni, 1.0 wt.% or less of Si, 0.2 wt.% or less of Mo, 1.0 wt.% or less of Cu, 1.0 wt.% or less of Mn, a balance of Fe and incidental impurities; heat treating the hot rolled steel sheet in a specified temperature range for at least 10 min, followed by cooling.
  • CN102899587A relates to a double phase stainless steel, which comprises the following chemical components, by weight: less than or equal to 0.02% of C, less than or equal to 0.02% of N, less than or equal to 0.03% of P, less than or equal to 0.015% of S, less than or equal to 0.35% of Si, 1.0-3.0% of Mn, 10.5-13.5% of Cr, 0.5-1.5% of Ni, 8(C+N)-0.35% of Ti, 0.10-0.30% of Nb+Mo, and the balance of Fe and unavoidable impurities, wherein the ferrite factor KFF is in 6.0-11.5.
  • JP2008138270A relates to a high strength Cr-containing stainless steel sheet having excellent workability.
  • the high strength stainless steel sheet having excellent workability has a composition comprising, by mass, 0.001 to 0.03% C, 0.001 to 0.03% N, 0.05 to 0.5% Si, 0.05 to 5% Mn, ⁇ 0.05% P, 0.3 to 5% Ni, 0.01 to 3% Cu, 10 to 18% Cr and 0.005 to 0.50% Al, and the balance Fe with inevitable impurities.
  • high hardness levels for example, up to about 350 HB, may be desirable in combination with higher toughness than is available from Duracorr® 300 stainless steel.
  • an in-service work hardenability up to about 450-500 HB, for example, may be required in certain applications.
  • any such alloys are cost-effective
  • the invention provides a dual-phase ferritic-martensitic stainless steel in accordance with claim 1 of the appended claims.
  • a high-hardness dual-phase ferritic-martensitic stainless steel is described.
  • the stainless steel comprises, by weight, 11.5% to 12% Cr, 0.8% to 1.5% Mn, 0.75% to 1.5% Ni, 0% to 0.5% Si, 0% to 0.2% Mo, up to 0.0025% B, Fe, and impurities.
  • the stainless steel according to the present disclosure exhibits Brinell hardness (HB) of 300 HB or greater and Charpy V-notch impact energy at -40°C (CVN) such that CVN (ft-lb)+(0.4 ⁇ HB) is 160 or greater.
  • HB Brinell hardness
  • CVN Charpy V-notch impact energy at -40°C
  • an embodiment of an article of manufacture including a high-hardness dual-phase ferritic-martensitic stainless steel is described.
  • the stainless steel comprises, by weight, 11.5% to 12% Cr, 0.8% to 1.5% Mn, 0.75% to 1.5% Ni, 0% to 0.5% Si, 0% to 0.2% Mo, up to 0.0025% B, Fe, and impurities.
  • the stainless steel exhibits Brinell hardness (HB) of 300 HB or greater and Charpy V-notch impact energy at -40°C (CVN) such that CVN (ft-lb)+(0.4xHB) is 160 or greater.
  • Figure 1 is a graph plotting Brinell hardness and Charpy V-notch impact energy of non-limiting embodiments of stainless steels according to the present disclosure in comparison to certain conventional steels.
  • the present disclosure in part, is directed to cost-effective dual-phase ferritic-martensitic stainless steels having advantageous hardness and which are suitable for use in various applications requiring abrasion resistance and/or wear resistance.
  • embodiments of dual-phase ferritic-martensitic stainless steels according to the present disclosure comprise, by weight, 11.5% to 12% Cr, 0.8% to 1.5% Mn, 0.75% to 1.5% Ni, 0% to 0.5% Si, 0% to 0.2% Mo, up to 0.0025% B, Fe, and impurities.
  • the stainless steels exhibit Brinell hardness (HB) of 300 HB or greater and Charpy V-notch impact energy at -40°C (CVN) such that the following is satisfied: CVN (ft-lb)+(0.4 ⁇ HB) is 160 or greater.
  • embodiments of the stainless steels according to the present disclosure include a Cr content of 11.5% to 12%, by weight.
  • Mn may be provided in the alloys of the present disclosure to improve work hardenability.
  • a Mn content of about 0.8% (by weight) or more may be required to achieve the desired work hardening effects.
  • excessive Mn may undesirably segregate during processing of the stainless steels.
  • embodiments of the stainless steels according to the present disclosure include a Mn content of 0.8% to 1.5%, by weight.
  • the Mn content of the stainless steels may be 1.0% to 1.5%, by weight.
  • the addition of Mn in combination with the addition of other alloying elements can advantageously affect work hardenability such that the steels attain a hardness of 450 HB or greater.
  • Ni may be provided in the alloys of the present disclosure to help stabilize the martensitic phase of the dual-phase (martensitic-ferritic) alloys.
  • a Ni content of about 0.75% by weight or more may be required to provide a material including higher levels of martensite than in Duracorr® 300 stainless steel.
  • the nickel content of the alloys may promote hardness of the alloys' martensite phase by stabilizing austenite formation during heat treatment, allowing more time for carbon diffusion.
  • due to the high cost of Ni it may be desirable to limit the Ni content.
  • embodiments of the steels according to the present disclosure include a Ni content of 0.75% to 1.5% (by weight) to provide a cost-effective dual-phase stainless steel with high hardness levels up to about 350 HB, in combination with higher toughness than is typical of Duracorr® 300 stainless steel.
  • the Ni content of stainless steels according to the present disclosure may be 1.0% to 1.5%, by weight.
  • the level of Si may be limited to (1) destabilize the ferritic phase of the dual-phase stainless steels and/or (2) avoid embrittling phases such as the sigma phase. Accordingly, certain embodiments of the steels according to the present disclosure include 0% to no more than about 0.5% Si, by weight.
  • the level of Mo may be limited to (1) destabilize the ferritic phase of the dual-phase stainless steels and/or (2) avoid embrittling phases such as the sigma phase. Accordingly, embodiments of the steels according to the present disclosure include 0% to no more than 0.2% Mo, by weight. In certain other embodiments of the steels according to the present disclosure, the Mo concentration is 0% to no more than 0.1%, by weight.
  • B may be provided in the dual-phase stainless steels of the present disclosure to improve martensite hardness.
  • Steels of the present disclosure may include up to 0.0025% B, by weight. In certain embodiments of the steels, the B content is 0.002% to 0.0025%, by weight.
  • Incidental elements and impurities in the disclosed alloys may include, for example, one or more of C, N, P, and S.
  • the total content of these elements is no more than 0.1%, by weight.
  • C may be present in the steels disclosed herein in an amount no more than 0.025%, by weight.
  • S may be present in the steels disclosed herein in an amount no more than 0.01%, by weight.
  • N may be present in the steels disclosed herein in an amount no more than 0.03%, by weight.
  • Incidental levels of various metallic elements also may be present in embodiments of alloys according to the present disclosure.
  • certain non-limiting embodiments of alloys according to the present disclosure may include up to 0.25% copper (Cu), by weight.
  • dual-phase ferritic-martensitic stainless steels comprise by weight: 11.5% to 12% Cr; 1.0% to 1.5% Mn; 1.0% to 1.5% Ni; 0% to 0.5% Si; 0% to 0.1% Mo; up to 0.0025% B; 0% to 0.025% C; 0% to 0.01% S; 0% to 0.03% N, Fe, and impurities.
  • the stainless steels further comprise P.
  • the total concentration of C, N, P, and S is no greater than 0.1%, by weight.
  • the concentration of B in the steels is 0.002% to 0.0025%, by weight.
  • the steels include no more than 0.25% Cu, by weight.
  • dual-phase ferritic-martensitic stainless steels consist essentially of, by weight: 11.5% to 12% chromium; 0.8% to 1.5% manganese; 0.75% to 1.5% nickel; 0% to 0.5% silicon; 0% to 0.2% molybdenum; up to 0.0025% boron; 0% to 0.025% carbon; 0% to 0.01% sulfur; 0% to 0.03% nitrogen; optionally at least one of copper and phosphorus; iron; and impurities.
  • dual-phase ferritic-martensitic stainless steels consist essentially of, by weight: 11.5% to 12% chromium; 1.0% to 1.5% manganese; 1.0% to 1.5% nickel; 0% to 0.5% silicon; 0% to 0.1% molybdenum; up to 0.0025% boron; 0% to 0.025% carbon; 0% to 0.01% sulfur; 0% to 0.03% nitrogen; optionally at least one of copper and phosphorus; iron; and impurities.
  • dual-phase ferritic-martensitic stainless steels consist of, by weight: 11.5% to 12% chromium; 0.8% to 1.5% manganese; 0.75% to 1.5% nickel; 0% to 0.5% silicon; 0% to 0.2% molybdenum; up to 0.0025% boron; 0% to 0.025% carbon; 0% to 0.01% sulfur; 0% to 0.03% nitrogen; optionally at least one of copper and phosphorus; iron; and impurities.
  • dual-phase ferritic-martensitic stainless steels consist of, by weight: 11.5% to 12% chromium; 1.0% to 1.5% manganese; 1.0% to 1.5% nickel; 0% to 0.5% silicon; 0% to 0.1% molybdenum; up to 0.0025% boron; 0% to 0.025% carbon; 0% to 0.01% sulfur; 0% to 0.03% nitrogen; optionally at least one of copper and phosphorus; iron; and impurities.
  • hardness is generally inversely related to toughness.
  • Brinell hardness (HB) is the primary measure of hardness
  • Charpy V-notch impact energy at -40°C (CVN) is the primary measure of toughness.
  • CVN (ft-lb)+(0.4xHB) of the steels is about 160 or greater.
  • hardness is about 300 HB or greater
  • CVN is about 67.8 N-m (50 ft-lb) or greater.
  • the steels according to the present disclosure have an in-service work hardenability up to a hardness of about 450 HB or greater.
  • Table 1 includes the compositions and certain properties of an embodiment of the dual-phase ferritic-martensitic stainless steels according to the present disclosure and of conventional ATI 412TM stainless steel and conventional Duracorr® 300 stainless steel. Heats of the three alloys listed in Table 1 were melted into slabs weighing about 6818 kg (15,000 lb) and rolled at a temperature of about 1066°C (1950°F) to produce material about 6 mm thick. Following the rolling process, the steels were annealed at 766°C or 843°C, for 15 minutes, and air cooled.
  • the mechanical properties of the experimental steel embodiment listed in Table 1 were measured and compared to those of the two listed conventional steels.
  • the Brinell hardness and CVN at -40°C (ft-lb) are shown in Table 1 for the three alloys.
  • the tensile tests were conducted according to the American Society for Testing and Materials (ASTM) standard A370 at room temperature, using a tungsten carbide ball indenter, on samples measuring about 5 cm in gauge length and about 0.5 cm in thickness.
  • the Charpy tests were conducted according to ASTM standard A370 and E23 at about -40°C on transverse samples measuring about 10 mm ⁇ 2.5 mm. Because these samples are considered subsize per ASTM-A370, the measured impact energy was converted to standard size specimen values in Table 1.
  • the experimental steel sample of the present disclosure exhibited very favorable hardness and toughness (CVN impact energy) relative to the conventional alloys. This was particularly unexpected and surprising.
  • Commercially available alloys providing comparable hardness and toughness typically are carbon steels, which would not withstand corrosive environments.
  • dual-phase stainless steels according to the present disclosure are prepared using conventional stainless steel production practices including, for example, melting of starting materials in an electric furnace, decarburization via AOD, and casting to an ingot.
  • Ingots may be cast, for example, by continuous casting or ingot pouring.
  • the cast material may be heat treated (austenitized) or sold as-rolled.
  • alloys according to the present disclosure are numerous. As described and evidenced above, the dual-phase stainless steels described herein are capable of being used in many applications where abrasion resistance and/or wear resistance is important. Articles of manufacture for which the steels according to the present disclosure would be particularly advantageous include, for example, parts and equipment used in oil sands extraction and parts and equipment used in sugar processing. Other applications for the stainless steels according to the present disclosure will be readily apparent to ordinarily skill practitioners. Those having ordinary skill may readily manufacture these and other articles of manufacture from the stainless steels according to the present disclosure using conventional manufacturing techniques.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Production Of Liquid Hydrocarbon Mixture For Refining Petroleum (AREA)

Claims (9)

  1. Zweiphasiger ferritisch-martensitischer rostfreier Stahl, bestehend aus, nach Gewicht:
    11,5 % bis 12 % Chrom;
    0,8 % bis 1,5 % Mangan;
    0,75 % bis 1,5 % Nickel;
    ≤ 0,5 % Silicium;
    ≤ 0,2 % Molybdän;
    ≤ 0,0025 % Bor;
    ≤ 0,25 % Kupfer;
    ≤ 0,025 % Kohlenstoff;
    ≤ 0,01 % Schwefel;
    ≤ 0,03 % Stickstoff;
    wobei die Gesamtkonzentration von Kohlenstoff + Stickstoff + Schwefel + Phosphor ≤ 0,1 %;
    Reste an Eisen und zufällige Verunreinigungen;
    wobei der Stahl eine Brinellhärte (HB) von 300 HB oder mehr und eine Charpy-Kerbschlagbiegeenergie bei -40 °C (Charpy-V-notch - CVN) derart aufweist, dass CVN (ft-lb) + (0,4 x HB) etwa 160 oder mehr beträgt.
  2. Zweiphasiger ferritisch-martensitischer rostfreier Stahl nach Anspruch 1, wobei der Borgehalt 0,002 % bis 0,0025 % beträgt.
  3. Zweiphasiger ferritisch-martensitischer rostfreier Stahl nach Anspruch 1 oder 2, wobei das Molybdängehalt ≤ 0,1 % beträgt.
  4. Zweiphasiger ferritisch-martensitischer rostfreier Stahl nach einem der vorhergehenden Ansprüche, wobei der Nickelgehalt 1,0 % bis 1,5 % beträgt.
  5. Zweiphasiger ferritisch-martensitischer rostfreier Stahl nach einem der vorhergehenden Ansprüche, wobei der Mangangehalt 1,0 % bis 1,5 % beträgt.
  6. Zweiphasiger ferritisch-martensitischer rostfreier Stahl nach einem der vorhergehenden Ansprüche, wobei CVN des Stahls 67,8 Nm (50 ft-lb) oder mehr beträgt.
  7. Zweiphasiger ferritisch-martensitischer rostfreier Stahl nach einem der vorhergehenden Ansprüche, wobei der Stahl eine Kaltumformung von bis zu einer Härte von 450 HB oder mehr aufweist.
  8. Herstellungserzeugnis, das einen zweiphasigen rostfreien Stahl nach einem der vorhergehenden Ansprüche beinhaltet.
  9. Herstellungserzeugnis nach Anspruch 8, wobei das Herstellungserzeugnis aus Teilen und Ausrüstungen, die bei der Ölsandextraktion verwendet werden, und Teilen und Ausrüstungen ausgewählt ist, die bei der Zuckerverarbeitung verwendet werden.
EP15712762.2A 2014-04-01 2015-03-12 Zweiphasiger edelstahl Not-in-force EP3126537B1 (de)

Priority Applications (2)

Application Number Priority Date Filing Date Title
PL15712762T PL3126537T3 (pl) 2014-04-01 2015-03-12 Dwufazowa stal nierdzewna
SI201531308T SI3126537T1 (sl) 2014-04-01 2015-03-12 Dvo-fazno nerjaveče jeklo

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
US14/231,778 US20150275340A1 (en) 2014-04-01 2014-04-01 Dual-phase stainless steel
PCT/US2015/020122 WO2015153092A1 (en) 2014-04-01 2015-03-12 Dual-phase stainless steel

Publications (2)

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EP3126537A1 EP3126537A1 (de) 2017-02-08
EP3126537B1 true EP3126537B1 (de) 2020-05-13

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US (1) US20150275340A1 (de)
EP (1) EP3126537B1 (de)
JP (1) JP6621419B2 (de)
KR (1) KR20160140733A (de)
CN (1) CN106460128A (de)
AU (1) AU2015241412B2 (de)
CA (1) CA2944491A1 (de)
ES (1) ES2808627T3 (de)
MX (1) MX2016012853A (de)
PL (1) PL3126537T3 (de)
RU (1) RU2721668C2 (de)
SI (1) SI3126537T1 (de)
TW (1) TWI651419B (de)
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AU2015241412B2 (en) 2019-11-21
TWI651419B (zh) 2019-02-21
US20150275340A1 (en) 2015-10-01
CA2944491A1 (en) 2015-10-08
AU2015241412A1 (en) 2016-10-20
KR20160140733A (ko) 2016-12-07
WO2015153092A1 (en) 2015-10-08
JP2017512907A (ja) 2017-05-25
EP3126537A1 (de) 2017-02-08
RU2016142683A3 (de) 2018-12-28
SI3126537T1 (sl) 2020-09-30
JP6621419B2 (ja) 2019-12-18
PL3126537T3 (pl) 2020-11-02
CN106460128A (zh) 2017-02-22
UA119168C2 (uk) 2019-05-10
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TW201602361A (zh) 2016-01-16
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