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EP2890825B1 - Acier inoxydable ferritique ayant une excellente résistance à l'oxidation, une bonne résistance à haute température et une bonne formabilité - Google Patents

Acier inoxydable ferritique ayant une excellente résistance à l'oxidation, une bonne résistance à haute température et une bonne formabilité Download PDF

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EP2890825B1
EP2890825B1 EP13759947.8A EP13759947A EP2890825B1 EP 2890825 B1 EP2890825 B1 EP 2890825B1 EP 13759947 A EP13759947 A EP 13759947A EP 2890825 B1 EP2890825 B1 EP 2890825B1
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ferritic stainless
titanium
stainless steel
melt
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EP2890825A1 (fr
Inventor
Eizo Yoshitake
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Cleveland Cliffs Steel Properties Inc
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AK Steel Properties Inc
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Priority to PL13759947T priority Critical patent/PL2890825T3/pl
Priority to SI201331448T priority patent/SI2890825T1/sl
Priority to RS20190532A priority patent/RS58807B1/sr
Priority to HRP20190864TT priority patent/HRP20190864T1/hr
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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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C22C38/06—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
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C22C38/58—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
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D8/0273—Final recrystallisation annealing

Definitions

  • ferritic stainless steel with oxidation resistance, high temperature strength, and good formability characteristics. Columbium and copper are added in amounts to provide high temperature strength, and silicon and manganese are added in amounts to provide oxidation resistance.
  • the present ferritic stainless steel provides better oxidation resistance than known stainless steels such as 18Cr-2Mo and 15Cr-Cb-Ti-Si-Mn. In addition, the present ferritic stainless steel is less expensive to manufacture than other stainless steels such as 18Cr-2Mo and can be produced without a hot band annealing step.
  • WO2012/036313 A1 discloses a heat-resistant ferrite-type stainless steel plate used in exhaust system components.
  • the present ferritic stainless steel are produced with titanium additions and low aluminum concentration to provide room temperature formability from equiaxed as-cast grain structures, as disclosed in U.S. Patent Nos. 6,855,213 and 5,868, 875 .
  • Columbium and copper are added to the ferritic stainless steel for high temperature strength and silicon and manganese are added to improve oxidation resistance.
  • the ferritic stainless steel is produced using process conditions known in the art for use in manufacturing ferritic stainless steels, such as the processes described in U.S. Patent Nos. 6,855,213 and 5,868,875 .
  • Columbium and copper are added to the ferritic stainless steel for high temperature strength and silicon and manganese are added to improve oxidation resistance. It can be produced from material having an as-cast structure of fine equiaxed grains.
  • a ferrous melt for the ferritic stainless steel is provided in a melting furnace such as an electric arc furnace.
  • This ferrous melt may be formed in the melting furnace from solid iron bearing scrap, carbon steel scrap, stainless steel scrap, solid iron containing materials including iron oxides, iron carbide, direct reduced iron, hot briquetted iron, or the melt may be produced upstream of the melting furnace in a blast furnace or any other iron smelting unit capable of providing a ferrous melt.
  • the ferrous melt then will be refined in the melting furnace or transferred to a refining vessel such as an argon-oxygen-decarburization vessel or a vacuum-oxygen-decarburization vessel, followed by a trim station such as a ladle metallurgy furnace or a wire feed station.
  • the steel is cast from a melt containing sufficient titanium and nitrogen but a controlled amount of aluminum for forming small titanium oxide inclusions to provide the necessary nuclei for forming the as-cast equiaxed grain structure so that an annealed sheet produced from this steel also has enhanced ridging characteristics and formability.
  • titanium is added to the melt for deoxidation prior to casting.
  • Deoxidation of the melt with titanium forms small titanium oxide inclusions that provide the nuclei that result in an as-cast equiaxed fine grain structure.
  • aluminum may not be added to this refined melt as a deoxidant and in other embodiments aluminum may be added to this refined melt in a small fraction.
  • titanium and nitrogen are present in the melt prior to casting so that the ratio of the product of titanium and nitrogen divided by residual aluminum is at least 0.14.
  • the steel is to be stabilized, sufficient amount of the titanium beyond that required for deoxidation can be added for combining with carbon and nitrogen in the melt but preferably less than that required for saturation with nitrogen, i.e ., in a sub-equilibrium amount, thereby avoiding or at least minimizing precipitation of large titanium nitride inclusions before solidification.
  • the maximum amount of titanium for "sub-equilibrium" is generally illustrated in FIG. 4 of U.S. Pat. No. 4,964,926 ,
  • one or more stabilizing elements such as columbium, zirconium, tantalum and vanadium can be added to the melt as well.
  • the cast steel is hot processed into a sheet.
  • sheet is meant to include continuous strip or cut lengths formed from continuous strip and the term “hot processed” means the as-cast steel will be reheated, if necessary, and then reduced to a predetermined thickness such as by hot rolling. If hot rolled, a steel slab is reheated to 2000° to 2350°F (1093°-1288°C), hot rolled using a finishing temperature of 1500 - 1800°F (816 - 982°C) and coiled at a temperature of 1000 - 1400°F (538 - 760°C).
  • the hot rolled sheet is also known as the "hot band.”
  • the hot band may be annealed at a peak metal temperature of 1700 - 2100°F (926 - 1149°C). In other embodiments, the sheet does not undergo a hot band annealing step.
  • the hot band may be descaled and cold reduced at least 40% to a desired final sheet thickness. In other embodiments, the hot band may be descaled and cold reduced at least 50% to a desired final sheet thickness. Thereafter, the cold reduced sheet can be final annealed at a peak metal temperature of 1800 - 2100°F (982-1149°C).
  • the ferritic stainless steel can be produced from a hot processed sheet made by a number of methods.
  • the sheet can be produced from slabs formed from ingots or continuous cast slabs of 50-200 mm thickness which are reheated to 2000° to 2350°F (1093°-1288°C) followed by hot rolling to provide a starting hot processed sheet of 1 - 7 mm thickness or the sheet can be hot processed from strip continuously cast into thicknesses of 2 - 52 mm.
  • the present process is applicable to sheet produced by methods wherein continuous cast slabs or slabs produced from ingots are fed directly to a hot rolling mill with or without significant reheating, or ingots hot reduced into slabs of sufficient temperature to be hot rolled in to sheet with or without further reheating.
  • Titanium is used for deoxidation of the ferritic stainless steel melt prior to casting.
  • the amount of titanium in the melt is 0.30% or less. Unless otherwise expressly stated, all concentrations stated as “%" are percent by weight.
  • titanium can be present in a sub-equilibrium amount.
  • the term "sub-equilibrium” means the amount of titanium is controlled so that the solubility product of the titanium compounds formed are below the saturation level at the steel liquidus temperature thereby avoiding excessive titanium nitride precipitation in the melt.
  • Excessive nitrogen is not a problem for those manufacturers that refine ferritic stainless steel melts in an argon oxygen decarburization vessel. Nitrogen substantially below 0.010% can be obtained when refining the stainless steel in an argon oxygen decarburization vessel thereby allowing increased amount of titanium to be tolerated and still be at sub-equilibrium.
  • sufficient time after adding the titanium to the melt should elapse to allow the titanium oxide inclusions to form before casting the melt. If the melt is cast immediately after adding titanium, the as-cast structure of the casting can include larger columnar grains. The amount of time that should elapse can be determined by one of ordinary skill in the art without undue experimentation. Ingots cast in the laboratory less than 5 minutes after adding the titanium to the melt had large as-cast columnar grains even when the product of titanium and nitrogen divided by residual aluminum was at least 0.14.
  • Sufficient nitrogen should be present in the steel prior to casting so that the ratio of the product of titanium and nitrogen divided by aluminum is at least 0.14.
  • the amount of nitrogen present in the melt is ⁇ 0.020%.
  • nitrogen concentrations after melting in an electric arc furnace may be as high as 0.05%
  • the amount of dissolved N can be reduced during argon gas refining in an argon oxygen decarburization vessel to less than 0.02%. Precipitation of excessive TiN can be avoided by reducing the sub-equilibrium amount of Ti to be added to the melt for any given nitrogen content.
  • the amount of nitrogen in the melt can be reduced in an argon oxygen decarburization vessel for an anticipated amount of Ti contained in the melt.
  • Total residual aluminum can be controlled or minimized relative to the amounts of titanium and nitrogen.
  • Minimum amounts of titanium and nitrogen must be present in the melt relative to the aluminum.
  • the ratio of the product of titanium and nitrogen divided by residual aluminum at least 0.14 and at least 0.23 in some embodiments.
  • the amount of aluminum is ⁇ 0.020%. In some embodiments, the amount of aluminum is ⁇ 0.013% and in other embodiments, it is reduced to ⁇ 0.010%. If aluminum is not purposefully alloyed with the melt during refining or casting such as for deoxidation immediately prior to casting, total aluminum should be controlled or reduced to less than 0.020%.
  • Titanium alloys may contain as much as 20% Al which may contribute total Al to the melt.
  • stabilizing elements may also include columbium, vanadium or mixtures thereof.
  • this second stabilizing element may be limited to ⁇ 0.50% when deep formability is required.
  • the invention includes columbium in concentrations of 0.5% or less. Some embodiments include columbium in concentrations of 0.28 - 0.43%. Vanadium can be present in amounts less than 0.5%. Some embodiments of the ferritic stainless steels include 0.008 - 0.098% vanadium.
  • the ferritic stainless steels contain 1.0 - 2.0% copper. Some embodiments include 1.16-1.31% copper.
  • Silicon is generally present in the ferritic stainless steels in an amount of 1.0 - 1.7%. In some embodiments, silicon is present in an amount of 1.27 - 1.35%. A small amount of silicon generally is present in a ferritic stainless steel to promote formation of the ferrite phase. Silicon also enhances high temperature oxidation resistance and provides high temperature strength. In most embodiments, silicon does not exceed about 1.7% because the steel can become too hard and the elongation can be adversely affected.
  • Manganese is present in the ferritic stainless steel in an amount of 0.4 - 1.5%. In some embodiments, manganese is present in an amount of 0.97 - 1.00%. Manganese improves oxidation resistance and spalling resistance at high temperatures. Accordingly, some embodiments include manganese in amounts of at least 0.4%. However, manganese is an austenite former and affects the stabilization of the ferrite phase. If the amount of manganese exceeds about 1.5%, the stabilization and formability of the steel can be affected.
  • Carbon is present in the ferritic stainless steel in an amount of up to 0.02%. In some embodiments, the carbon content is ⁇ 0.02%. In still other embodiments, it is 0.0054-0.0133%.
  • Chromium is present in some embodiments of the ferritic stainless steels in an amount of 15-20%. If chromium is greater than about 25%, the formability of the steel can be reduced.
  • oxygen is present in the steel in an amount ⁇ 100 ppm.
  • oxygen in the melt can be within the range of 10-60 ppm thereby providing a very clean steel having small titanium oxide inclusions that aid in forming the nucleation sites responsible for the fine as-cast equiaxed grain structure.
  • Sulfur is present in the ferritic stainless steel in an amount of ⁇ 0.01%.
  • Phosphorus can deteriorate formability in hot rolling and can cause pitting. It is present in the ferritic stainless steel in an amount of ⁇ 0.05%.
  • nickel is an austenite former and affects the stabilization of the ferrite phase. Accordingly, in some embodiments, nickel is limited to ⁇ 1.0%. In some embodiments, nickel is present in amounts of 0.13- 0.19%.
  • Molybdenum also improves corrosion resistance. Some embodiments include 3.0% or less molybdenum. Some embodiments include 0.03 - 0.049% molybdenum.
  • boron in the steels of the present invention in an amount of ⁇ 0.010%. In some embodiments, boron is present in an amount of 0.0001 - 0.002%. Boron can improve the resistance to secondary work embrittlement of steel so that the steel sheet will be less likely to split during deep drawing applications and multi-step forming applications.
  • the ferritic stainless steels may also include other elements known in the art of steelmaking that can be present as residual elements, i.e ., impurities from steelmaking process.
  • Embodiments of the ferritic stainless steels and comparative reference steels were made with the compositions set forth in Table 1 below.
  • HT #831187 is Type 444 stainless steel
  • HT #830843 is 15 CrCb stainless steel, which is a product of AK Steel Corporation, West Chester, Ohio.
  • the oxidation resistance of several of several of the steel compositions described in Example 1 and Table 1 above was tested at 930°C for 200 hours in air.
  • the results of the tests are set forth in Table 2 below.
  • the individual compositions are each identified by their respective ID number.
  • the oxidation resistance was evaluated using two factors. One was the amount of weight gain, and the other was degree of spalling. For each material, except HT #920097, the reported weight gain value is an average of two tests. For HT #920097, eight samples were tested and the minimum, average, and maximum of these eight tests has been reported. Table 2 Oxidation resistance test results at 930°C for 200 hours in air.
  • HT #930354 One plant produced hot band coil with the composition set forth in Table 1 (HT #930354, CL #681158-03) was finish-processed without hot band annealing to 1.5 mm gauge.
  • a hot band annealing step was included, the plant-produced coils of HT#930354 resulted in r-bar values of 1.34, 1.31, 1.38, and 1.34, as shown in Table 5.
  • the hot band annealing step was not included, it resulted in higher r-bar of 1.46, as shown by Table 7 below.
  • Table 7 -Longitudinal tensile properties (ASTM E8/E8M), stretch r-values, and ridging resistances.

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

Claims (1)

  1. Acier inoxydable ferritique constitué des éléments suivants en pourcentage en poids :
    0,020 % ou moins de carbone
    0,020 % ou moins d'azote
    15 à 20 % de chrome
    0,30 % ou moins de titane
    0,28 à 0,50 % de niobium
    1,0 à 2,00 % de cuivre
    1,0 à 1,7 % de silicium
    0,4 à 1,5 % de manganèse
    0,050 % ou moins de phosphore
    0,01 % ou moins de soufre
    0,020 % ou moins d'aluminium
    facultativement un ou plusieurs éléments sélectionnés dans le groupe constitué de 3,0 % ou moins de molybdène, 0,010 % ou moins de bore, 0,5 % ou moins de vanadium, et 1,0 % ou moins de nickel, et le reste étant du fer et des impuretés inévitables,
    à condition que la relation : % de titane × % d ' azote / % d ' aluminum ≥ 0,14
    Figure imgb0003
     soit satisfaite.
EP13759947.8A 2012-08-31 2013-08-28 Acier inoxydable ferritique ayant une excellente résistance à l'oxidation, une bonne résistance à haute température et une bonne formabilité Active EP2890825B1 (fr)

Priority Applications (4)

Application Number Priority Date Filing Date Title
PL13759947T PL2890825T3 (pl) 2012-08-31 2013-08-28 Ferrytyczne stale nierdzewne o doskonałej odporności na utlenianie z dobrą wytrzymałością na wysokie temperatury i dobrą odkształcalnością
SI201331448T SI2890825T1 (sl) 2012-08-31 2013-08-28 Feritno nerjavno jeklo z odlično odpornostjo proti oksidaciji, dobro trdnostjo pri visokih temperaturah in dobro oblikovalnostjo
RS20190532A RS58807B1 (sr) 2012-08-31 2013-08-28 Feritni nerđajući čelik sa odličnom otpornošću na oksidaciju, dobrom izdržljivošću na visoku temperaturu, i dobre obradivosti
HRP20190864TT HRP20190864T1 (hr) 2012-08-31 2013-08-28 Feritni nehrđajući čelik s odličnom otpornošću na oksidaciju, dobrom otpornošću na visoke temperature i dobrom formabilnošću

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
US201261695771P 2012-08-31 2012-08-31
US13/837,500 US20140065005A1 (en) 2012-08-31 2013-03-15 Ferritic Stainless Steel with Excellent Oxidation Resistance, Good High Temperature Strength, and Good Formability
PCT/US2013/056999 WO2014036091A1 (fr) 2012-08-31 2013-08-28 Acier inoxydable ferritique avec une excellente résistance à l'oxydation, une bonne résistance à température élevée, et une bonne aptitude au formage

Publications (2)

Publication Number Publication Date
EP2890825A1 EP2890825A1 (fr) 2015-07-08
EP2890825B1 true EP2890825B1 (fr) 2019-04-03

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EP13759947.8A Active EP2890825B1 (fr) 2012-08-31 2013-08-28 Acier inoxydable ferritique ayant une excellente résistance à l'oxidation, une bonne résistance à haute température et une bonne formabilité

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US (2) US20140065005A1 (fr)
EP (1) EP2890825B1 (fr)
JP (1) JP6194956B2 (fr)
KR (2) KR20150080485A (fr)
CN (2) CN104769147A (fr)
AU (1) AU2013308922B2 (fr)
BR (1) BR112015004228A2 (fr)
CA (1) CA2882361C (fr)
ES (1) ES2728229T3 (fr)
HR (1) HRP20190864T1 (fr)
HU (1) HUE043997T2 (fr)
MX (1) MX377538B (fr)
MY (1) MY172722A (fr)
PL (1) PL2890825T3 (fr)
RS (1) RS58807B1 (fr)
RU (1) RU2650467C2 (fr)
SI (1) SI2890825T1 (fr)
WO (1) WO2014036091A1 (fr)
ZA (1) ZA201502075B (fr)

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US20140065005A1 (en) * 2012-08-31 2014-03-06 Eizo Yoshitake Ferritic Stainless Steel with Excellent Oxidation Resistance, Good High Temperature Strength, and Good Formability
EP3333277B1 (fr) 2015-08-05 2019-04-24 Sidenor Investigación y Desarrollo, S.A. Acier faiblement allié à résistance élevée et à résistance élevée à l'oxydation à chaud
CN107675075A (zh) * 2017-09-05 2018-02-09 王业双 一种高性能耐高温铁素体不锈钢及其制备方法
JP6420893B1 (ja) * 2017-12-26 2018-11-07 日新製鋼株式会社 フェライト系ステンレス鋼
CN114787395B (zh) * 2019-12-18 2025-02-25 欧瑞康美科（美国）公司 铁基高耐腐蚀性和耐磨性合金
JP7725440B2 (ja) * 2022-11-01 2025-08-19 株式会社豊田中央研究所 構造用ジョイントおよび骨格構造体

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Also Published As

Publication number Publication date
AU2013308922B2 (en) 2016-08-04
ES2728229T3 (es) 2019-10-23
US20140065005A1 (en) 2014-03-06
JP2015532684A (ja) 2015-11-12
CA2882361A1 (fr) 2014-03-06
CN108823509A (zh) 2018-11-16
WO2014036091A1 (fr) 2014-03-06
RU2650467C2 (ru) 2018-04-13
MY172722A (en) 2019-12-11
MX2015002677A (es) 2015-05-12
CN104769147A (zh) 2015-07-08
MX377538B (es) 2025-03-10
HUE043997T2 (hu) 2019-09-30
JP6194956B2 (ja) 2017-09-13
CN104769147A8 (zh) 2018-10-09
SI2890825T1 (sl) 2019-06-28
CA2882361C (fr) 2019-06-18
RS58807B1 (sr) 2019-07-31
US20140065006A1 (en) 2014-03-06
KR20200028502A (ko) 2020-03-16
AU2013308922A1 (en) 2015-03-05
BR112015004228A2 (pt) 2017-07-04
PL2890825T3 (pl) 2019-09-30
KR20150080485A (ko) 2015-07-09
RU2015108849A (ru) 2016-10-20
HRP20190864T1 (hr) 2019-06-28
EP2890825A1 (fr) 2015-07-08
ZA201502075B (en) 2016-03-30

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