WO2014036091A1 - Ferritic stainless steel with excellent oxidation resistance, good high temperature strength, and good formability - Google Patents

Ferritic stainless steel with excellent oxidation resistance, good high temperature strength, and good formability Download PDF

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Publication number
WO2014036091A1
WO2014036091A1 PCT/US2013/056999 US2013056999W WO2014036091A1 WO 2014036091 A1 WO2014036091 A1 WO 2014036091A1 US 2013056999 W US2013056999 W US 2013056999W WO 2014036091 A1 WO2014036091 A1 WO 2014036091A1
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Prior art keywords
ferritic stainless
stainless steel
oxidation resistance
less
titanium
Prior art date
Application number
PCT/US2013/056999
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English (en)
French (fr)
Inventor
Eizo Yoshitake
Original Assignee
Ak Steel Properties, Inc.
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Priority to AU2013308922A priority Critical patent/AU2013308922B2/en
Priority to UAA201502423A priority patent/UA114113C2/uk
Application filed by Ak Steel Properties, Inc. filed Critical Ak Steel Properties, Inc.
Priority to ES13759947T priority patent/ES2728229T3/es
Priority to PL13759947T priority patent/PL2890825T3/pl
Priority to MX2015002677A priority patent/MX2015002677A/es
Priority to EP13759947.8A priority patent/EP2890825B1/en
Priority to SI201331448T priority patent/SI2890825T1/sl
Priority to JP2015529983A priority patent/JP6194956B2/ja
Priority to KR1020207006567A priority patent/KR20200028502A/ko
Priority to RU2015108849A priority patent/RU2650467C2/ru
Priority to BR112015004228A priority patent/BR112015004228A2/pt
Priority to KR1020157008118A priority patent/KR20150080485A/ko
Priority to CN201380045477.5A priority patent/CN104769147A/zh
Priority to RS20190532A priority patent/RS58807B1/sr
Priority to CA2882361A priority patent/CA2882361C/en
Publication of WO2014036091A1 publication Critical patent/WO2014036091A1/en
Priority to ZA2015/02075A priority patent/ZA201502075B/en
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
    • C22C38/38—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
    • C22C38/28—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
    • C22C38/40—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.
  • 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, the complete disclosures of which are each incorporated by reference herein.
  • 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
  • titanium oxide inclusions that provide the nuclei that result in an as-cast equiaxed fine grain structure.
  • aluminum oxide A1 2 0 3; in some embodiments 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 can be 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 about 0.14.
  • 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, the disclosure of which is incorporated herein by reference.
  • 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
  • Titanium is used for deoxidation of the ferritic stainless steel melt prior to casting.
  • the amount of titanium in the melt can be 0.30% or less. Unless otherwise expressly stated, all concentrations stated as “%" are percent by weight. In some embodiments, titanium can be present in a sub-equilibrium amount. As used herein, 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 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 about 0.14. In some embodiments, the amount of nitrogen present in the melt is ⁇
  • 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 can be at least about 0.14 in some embodiments, and at least 0.23 in other embodiments.
  • the amount of aluminum is ⁇ 0.020% in some embodiments. In other 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 can 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, zirconium, tantalum, vanadium or mixtures thereof.
  • this second stabilizing element may be limited to ⁇ 0.50% when deep formability is required.
  • Some embodiments include 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.
  • Some embodiments include 1.16-1.31% copper.
  • Silicon is generally present in the ferritic stainless steels in an amount of 1.0 -
  • 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 femtic 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
  • molybdenum 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 made either as deliberate additions or present as residual elements, i.e., impurities from steelmaking process.
  • each ingot was reheated to a temperature of 2300°F (1260°C). It was hot rolled to a strip thickness of 0.200" (5.08 mm). It was then hot band annealed at a temperature of 1825-1975°C (996 - 1079°C). It was then cold rolled to a thickness of 0.079 - 0.098" (2.0 - 2.5mm). The cold rolled strip was final annealed to a temperature of 1885 - 1950°F (1029 1066°C).
  • 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.
  • Example 1 were tested according to the procedure of ASTM Standard E8/E8M test. In addition, the stretch-r values were tested according to the procedure of ASTM Standard E517. Ridging resistance of the compositions was also determined on a qualitative scale of 0-6, where 0 is the best and 6 is unacceptable. The results of these tests are set forth below:
  • HT #930354 One plant produced hot band coil with the composition set forth in Table 1 (HT #930354, CL #681 158-03) 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.

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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)
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  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
PCT/US2013/056999 2012-08-31 2013-08-28 Ferritic stainless steel with excellent oxidation resistance, good high temperature strength, and good formability WO2014036091A1 (en)

Priority Applications (17)

Application Number Priority Date Filing Date Title
CN201380045477.5A CN104769147A (zh) 2012-08-31 2013-08-28 具有优异抗氧化性、良好高温强度和良好成形性的铁素体不锈钢
JP2015529983A JP6194956B2 (ja) 2012-08-31 2013-08-28 優れた耐酸化性、良好な高温強度、及び良好な加工性を有するフェライト系ステンレス鋼
ES13759947T ES2728229T3 (es) 2012-08-31 2013-08-28 Acero inoxidable ferrítico con excelente resistencia a la oxidación, buena resistencia a altas temperaturas y buena conformabilidad
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
MX2015002677A MX2015002677A (es) 2012-08-31 2013-08-28 Acero inoxidable ferritico con excelente resistencia a la oxidacion, buena fuerza a alta temperatura y buena conformabilidad.
EP13759947.8A EP2890825B1 (en) 2012-08-31 2013-08-28 Ferritic stainless steel with excellent oxidation resistance, good high temperature strength, and good formability
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
AU2013308922A AU2013308922B2 (en) 2012-08-31 2013-08-28 Ferritic stainless steel with excellent oxidation resistance, good high temperature strength, and good formability
KR1020207006567A KR20200028502A (ko) 2012-08-31 2013-08-28 탁월한 내산화성, 우수한 고온 강도 및 우수한 성형성을 갖는 페라이트계 스테인레스 강
BR112015004228A BR112015004228A2 (pt) 2012-08-31 2013-08-28 aço inoxidável ferrítico com excelente resistência à oxidação, boa resistência a alta temperatura e boa plasticidade
RU2015108849A RU2650467C2 (ru) 2012-08-31 2013-08-28 Ферритная нержавеющая сталь, обладающая превосходной стойкостью к окислению, хорошими жаропрочностью и формуемостью
KR1020157008118A KR20150080485A (ko) 2012-08-31 2013-08-28 탁월한 내산화성, 우수한 고온 강도 및 우수한 성형성을 갖는 페라이트계 스테인레스 강
UAA201502423A UA114113C2 (xx) 2012-08-31 2013-08-28 Феритна нержавіюча сталь
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
CA2882361A CA2882361C (en) 2012-08-31 2013-08-28 Ferritic stainless steel with excellent oxidation resistance, good high temperature strength, and good formability
ZA2015/02075A ZA201502075B (en) 2012-08-31 2015-03-26 Ferritic stainless steel with excellent oxidation resistance, good high temperature strength, and good formability
HRP20190864TT HRP20190864T1 (hr) 2012-08-31 2019-05-09 Feritni nehrđajući čelik s odličnom otpornošću na oksidaciju, dobrom otpornošću na visoke temperature i dobrom formabilnošću

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EP2890825A1 (en) 2015-07-08
US20140065005A1 (en) 2014-03-06
KR20150080485A (ko) 2015-07-09
US20140065006A1 (en) 2014-03-06
JP2015532684A (ja) 2015-11-12
EP2890825B1 (en) 2019-04-03
AU2013308922B2 (en) 2016-08-04
KR20200028502A (ko) 2020-03-16
CN104769147A8 (zh) 2018-10-09
RS58807B1 (sr) 2019-07-31
CA2882361A1 (en) 2014-03-06
AU2013308922A1 (en) 2015-03-05
ES2728229T3 (es) 2019-10-23
HRP20190864T1 (hr) 2019-06-28
PL2890825T3 (pl) 2019-09-30
CN104769147A (zh) 2015-07-08
CA2882361C (en) 2019-06-18
RU2015108849A (ru) 2016-10-20
MX2015002677A (es) 2015-05-12
HUE043997T2 (hu) 2019-09-30
MY172722A (en) 2019-12-11
RU2650467C2 (ru) 2018-04-13
JP6194956B2 (ja) 2017-09-13
BR112015004228A2 (pt) 2017-07-04
CN108823509A (zh) 2018-11-16
SI2890825T1 (sl) 2019-06-28

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