EP1413640A1 - Ferritischer nichtrostender stahl für ein element einer abgasstrompassage - Google Patents

Ferritischer nichtrostender stahl für ein element einer abgasstrompassage Download PDF

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Publication number
EP1413640A1
EP1413640A1 EP02743819A EP02743819A EP1413640A1 EP 1413640 A1 EP1413640 A1 EP 1413640A1 EP 02743819 A EP02743819 A EP 02743819A EP 02743819 A EP02743819 A EP 02743819A EP 1413640 A1 EP1413640 A1 EP 1413640A1
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EP
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Prior art keywords
mass
steel
temperature
stainless steel
ferritic stainless
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EP02743819A
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English (en)
French (fr)
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EP1413640B1 (de
EP1413640A4 (de
Inventor
Manabu c/o Stainless Steel Business Div. OKU
Yoshitomo Stainless Steel Business Div. FUJIMURA
Toshirou Stainless Steel Business Div. Nagoya
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Nippon Steel Nisshin Co Ltd
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Nisshin Steel Co Ltd
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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
    • C22C38/02—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • 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
    • C22C38/04—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
    • 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
    • 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
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01N—GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR MACHINES OR ENGINES IN GENERAL; GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR INTERNAL COMBUSTION ENGINES
    • F01N2530/00—Selection of materials for tubes, chambers or housings
    • F01N2530/02—Corrosion resistive metals
    • F01N2530/04—Steel alloys, e.g. stainless steel

Definitions

  • the present invention relates to a ferritic stainless steel, which is excellent in heat-resistance, low-temperature toughness and weldability, useful as conduit members, e.g. exhaust manifolds, front pipes, center pipes and outer casings of catalytic converters in internal combustion engines of automobiles or the like, for emission of exhaust gas.
  • conduit members e.g. exhaust manifolds, front pipes, center pipes and outer casings of catalytic converters in internal combustion engines of automobiles or the like, for emission of exhaust gas.
  • Conduit members of automobiles for emission of exhaust gas are directly exposed to a high-temperature atmosphere containing exhaust gas during driving automobiles, and subjected to thermal stress caused by repetition of driving and stopping as well as vibration during driving. Mechanical stress is also applied to conduit members at a low temperature, when automobiles are started in winter in cold districts. Therefore, a material for use as the conduit members shall have durability in severe environments.
  • conduit members are fabricated by welding or forming steel sheets or pipes to product shapes, steels necessarily have excellent heat-resistance, weldability and formability for the purpose.
  • Toughness especially low-temperature toughness, is also an important property, in order to secondarily form a stainless steel sheet or pipe without cracks and to render conduit members resistant to mechanical stress at a low temperature.
  • a ferritic stainless steel is often used as a material for such conduit members, due to its small thermal expansion coefficient, thermal fatigue strength and scale spalling resistance in comparison with an austenitic stainless steel. A low price is also an advantage of the ferritic stainless steel.
  • JP3-274245A discloses Nb-alloyed steel and Nb, Si-alloyed steel as new SUS430J1 stainless steels
  • JP5-125491A discloses Nb, Mo-alloyed steel.
  • the Nb, Mo-alloyed steel is useful as parts or members exposed to severe high-temperature atmosphere due to its excellent high-temperature strength and thermal fatigue-resistance.
  • poor formability and inferior low-temperature toughness are disadvantages of the Nb, Mo-alloyed steel.
  • a few reports are published on improvement of formability and low-temperature toughness, the improvement is still insufficient for the purpose. Consumption of expensive Mo at a high ratio is also an disadvantage of the Nb, Mo-alloyed steel.
  • high-temperature strength e.g. resistance to thermal fatigue failure
  • high-temperature oxidation-resistance evaluated as a critical temperature of abnormal oxidation
  • high-temperature strength is more important than high-temperature oxidation-resistance
  • formability and low-temperature toughness are also important factors so as to form a stainless steel sheet or pipe to the complicate profile.
  • the Nb, Mo-alloyed steel is necessarily used for such a part or member with emphasis on heat-resistance regardless poor formability, inferior low-temperature toughness and expensiveness.
  • the present invention aims at provision of a ferritic stainless steel useful as conduit members for emission of exhaust gas.
  • An object of the present invention is to bestow a ferritic stainless steel, which does not contain expensive Mo, with heat-resistance similar to that of Nb, Mo-alloyed steel in addition to excellent formability, low-temperature toughness and weldability.
  • the present invention proposes a ferritic stainless steel, which consists of C up to 0.03 mass %, Si up to 1.0 mass %, Mn up to 1.5 mass %, Ni up to 0.6 mass %, 10-20 mass % of Cr, Nb up to 0.50 mass %, 0.8-2.0 mass % of Cu, Al up to 0.03 mass %, 0.03-0.20 mass % of V, N up to 0.03 mass % and the balance being Fe except inevitable impurities with a provision of Nb ⁇ 8(C+N).
  • the ferritic stainless steel does not contain Mo as an alloying element, but optionally contains 0.05-0.30 mass % of Ti for further improvement of formability and/or 0.0005-0.02 mass % of B for further improvement of secondary formability.
  • Such stainless steels as SUH409, SUS430J1l and SUS429 have been used as materials good of heat-resistance in an atmosphere, to which conduit members are exposed.
  • Such a part or member ordinarily has a complicate profile, so that it shall be made of a stainless steel good of formability and low-temperature toughness, which are never estimated from Mo-alloyed steel.
  • the part or member is likely to break down due to thermal fatigue, since thermal stress is repeatedly applied to the complicate profile.
  • the inventors have researched and examined effects of various alloying elements on properties of such a part or member, and discovered that a ferritic stainless steel is improved in all of high-temperature strength below 900°C, formability and low-temperature toughness by addition of both V and Cu to the same level of Nb, Mo-alloyed steel.
  • Nb-alloyed ferritic stainless steels which contained V at a small ratio and Cu at various ratios, were examined by high-temperature tensile test at 700°C and 800°C for measurement of 0.2%-proof stress. Test results prove that high-temperature strength below 900°C is remarkably raised to a level similar to Nb, Mo-alloyed steel by addition of V at a small ratio and Cu at a controlled ratio.
  • Fig. 1 shows test results of ferritic stainless steels with a basic composition of 17Cr-0.4Nb-0.1V, to which Cu is added at various ratios.
  • Fig. 1 also shows strength of SUS444 steel with basic composition of 18Cr-2Mo-0.4Nb as a comparative example of Nb, Mo-alloyed steel.
  • Values of 0.2%-proof stress at 700°C and 800°C are remarkably raised in response to increase of a Cu content, as noted in Fig. 1.
  • the value of 0.2%-proof stress at 0.8 mass % or more of Cu is similar or superior to that of SUS444 steel, which contains approximately 2 mass % of Mo.
  • the inventors have already confirmed from another test results that a value of 0.2%-proof stress at 900°C is not raised to a level of SUS444 but higher than Nb-containing ferritic stainless steel by increase of V and Cu contents.
  • addition of both V and Cu is effective for improvement of high-temperature strength in a hot zone below 900°C without significant troubles at a temperature higher than 900°C.
  • a ratio of dissolved Nb for improvement of high-temperature strength is also kept at a higher value by presence of V, which converts free C and N to carbonitrides, than V-free steels containing Nb at the same ratio.
  • Increase of dissolved Nb assures that high-temperature strength necessary for the purpose is attained by saved consumption of Nb in comparison with the V-free steels, resulting in improvement of formability and low-temperature toughness.
  • Carbonitrides of Nb and V increase in an annealed matrix of the inventive ferritic stainless steel. Increase of the carbonitrides suppresses crystal growth to coarse grains at a weld heat-affected zone, resulting in improvement of toughness. Formation of chromium carbide, which is harmful on intergranular corrosion-resistance, is also suppressed by increase of the carbonitrides.
  • C and N are generally regarded as elements effective for high-temperature strength, e.g. creep strength, but excess C and N unfavorably degrade oxidation-resistance, formability, low-temperature toughness and weldability.
  • V and Nb are necessarily added at ratios corresponding to concentrations of C and N. Therefore, each of C and N contents is controlled to 0.03 mass % or less (preferably 0.015 mass % or less), in order to avoid increase of V and Nb, which causes a rise of material expense. Si up to 1.0 mass %
  • Si is an element effective for high-temperature oxidation-resistance, but not so effective on high-temperature strength below 900°C. Excess Si hardens a ferritic stainless steel, resulting in degradation of formability and low-temperature toughness. In this sense, a Si content is determined at 1.0 mass % or less (preferably 0.1-0.5 mass %). Mn up to 1.5 mass %
  • Mn is an alloying element, which improves high-temperature oxidation-resistance, especially scale spalling resistance property, of a ferritic stainless steel, but excess Mn degrades formability and weldability.
  • a Mn content is determined at 1.5 mass % or less (preferably 0.5 mass % or less). Ni up to 0.6 mass %
  • Ni is an austenite-stabilizing element. Excess addition of Ni to a steel containing Cr at a relatively small ratio promotes formation of a martensitic phase harmful on thermal fatigue strength and formability, as the same as Mn. Excess Ni also raises a steel cost. Therefore, a Ni content is determined at 0.6 mass % or less (preferably 0.5 mass % or less). 10-20 mass% of Cr
  • Cr is an essential element for stabilization of a ferritic phase and improvement of oxidation-resistance as an important property for high-temperature use. Oxidation-resistance becomes better as increase of a Cr content, but excess Cr causes embrittlement of a stainless steel, resulting in increase of hardness and degradation of formability. In this sense, a Cr content is determined within a range of 10-20 mass %. Cr is preferably controlled to a proper value in response to a temperature on use. For instance, 16-19 mass % of Cr is favorable for oxidation-resistance at a temperature not higher than 950°C, and 12-16 mass % of Cr is favorable for oxidation-resistance at a temperature not higher than 900°C. From 8(C+N) to 0.50 mass % of Nb
  • Nb fixes C and N as carbonitrides, and also improves high-temperature strength in a state dissolved in a steel matrix. However, excess Nb is unfavorable for formability, low-temperature toughness and to welding hot crack-resistance. Nb not less than 8(C+N) is necessary for fixation of C and N, but an upper limit of Nb is determined at 0.5 mass % in order to maintain proper formability, low-temperature toughness and tensile type hot-cracking resistance. A Nb content is preferably controlled within a range of from 8(C+N)+0.10 to 0.45 mass %. 0.8-2.0 mass % of Cu
  • Cu is the most important element in the inventive alloy system. Within a temperature range which the inventors have researched and examined, most of Cu is dissolved in an annealed steel matrix and precipitated during heat-treatment. Cu precipitates exhibits the same strengthening effect as Mo at the beginning of heating, but the strengthening effect gradually becomes weaker as the lapse of heating time. At least 0.8 mass % of Cu is necessary in order to gain high-temperature strength suitable for the purpose, as noted in Fig. 1. However, formability, low-temperature toughness and weldability are degraded as increase of a Cu content. The unfavorable effect of Cu on formability, low-temperature toughness and weldability is suppressed by controlling an upper limit of the Cu content at 2.0 mass %. The Cu content is preferably determined within a range of 1.0-1.7 mass %. Al up to 0.03 mass %
  • Al is added as a deoxidizing element in a steel making process. But, excess Al degrades an external appearance of a stainless steel sheet and also puts harmful effects on formability, low-temperature toughness and weldability. In this sense, an Al content is preferably controlled at a lowest possible level, so that its upper limit is determined at 0.03 mass %. 0.03-0.20 mass % of V
  • the additive V improves high-temperature strength of a ferritic stainless steel in co-presence of Nb and Cu. Addition of V together with Nb is also effective for formability, low-temperature toughness, intergranular corrosion-resistance and toughness at a weld heat affected-zone. These effects are noted at 0.03 mass % or more of V, but excess V above 0.20 mass % is rather unfavorable for formability and low-temperature toughness. In this sense, a V content is determined within a range of 0.03-0.20 mass % (preferably 0.04-0.15 mass %). 0.05-0.30 mass % of Ti
  • Ti is an optional element, which raises Lankford value (r) and improves formability of a ferritic stainless steel, and its effect is noted at 0.05 mass % or more of Ti.
  • excess Ti promotes formation of TiN harmful on external appearance of a stainless steel and also degrades formability and low-temperature toughness.
  • Ti shall be held at a smallest possible ratio, even when Ti is added for improvement of formability. Therefore, an upper limit of a Ti content is determined at 0.30 mass % (preferably 0.20 mass %). 0.0005-0.02 mass % of B
  • B is another optional element for improving secondary formability of a stainless steel and suppressing cracking during multi-stepped forming.
  • the effect on formability is noted at 0.0005 mass % or more of B, but excess B causes degradation of productivity and weldability.
  • a B content is determined within a range of 0.0005-0.02 mass % (preferably 0.001-0.01 mass %).
  • the inventive alloy system is designed on the assumption that expensive Mo is not added as an alloying element, but Mo is likely to be included as an impurity during steel making. Since inclusion of Mo at a relatively high ratio is harmful on formability, low-temperature toughness and weldability, it shall be controlled at a ratio less than 0.10 mass %.
  • P, S and O are preferably controlled at lowest possible levels. Accounting hot-workability, oxidation-resistance and so on, upper limits of P, S and O are preferably determined at 0.04 mass %, 0.03 mass % and 0.02 mass %, respectively. At least one of W, Zr, Y and REM (rare earth metals) may be added for heat-resistance, or at least one of Ca, Mg and Co may be added for hot-workability.
  • W, Zr, Y and REM rare earth metals
  • Table 1 Each ferritic stainless steel with chemical composition shown in Table 1 or 2 was melted in a vacuum furnace and cast to a 30 kg ingot. The ingot was forged, hot-rolled, annealed, cold-rolled to thickness of 2.0 mm or 1.2 mm, and finish-annealed.
  • Table 1 shows compositions according to the present invention, while Table 2 shows comparative compositions.
  • a steel No. 11 corresponds to SUS430J1l
  • a steel No. 15 corresponds to SUH409L
  • a steel No. 16 corresponds to a 14Cr-Si-Nb steel
  • a steel No. 17 corresponds to SUS444. Any of these steels has been used so far as a material for an exhaust manifold.
  • Each annealed cold-rolled steel sheet of 2.0 mm in thickness was examined by a high-temperature tensile test, a high-temperature oxidation test, a room-temperature tensile test and Charpy impact test.
  • Each annealed cold-rolled steel sheet of 1.2 mm in thickness was examined by a tensile type hot-cracking test.
  • a test piece was heated at each temperature of 850°C, 900°C, 950°C, 1000°C and 1100°C for 200 hours under conditions regulated in JIS Z2281.
  • the heated test piece was observed by naked eyes to detect occurrence of abnormal oxidation (i.e. growth of knobby thick oxide through a steel sheet).
  • a critical temperature, at which the test piece was heated without abnormal oxidation, was determined from the observation results.
  • each annealed cold-rolled steel sheet of 2.0 mm in thickness was shaped to a test piece No. 13B and stretched under conditions regulated in JIS Z2241 to measure its elongation after fracture.
  • any of the inventive steels Nos. 1-10 has 0.2%-proof stress at 800°C, fairly higher than the Nb, Si-alloyed steel No. 16 and similar or superior to the Nb, Mo-alloyed steel No. 17.
  • Values of elongation by the room-temperature tensile test, a ductile-brittle transition temperature by Charpy impact test and a critical strain by the tensile type hot-cracking test were also similar or superior to the Nb, Mo-alloyed steel No. 17.
  • the Mo-containing comparative steel No. 17 had the same properties as the inventive steels Nos. 1-10, but its low-temperature toughness was relatively inferior. A cost of the steel No. 17 is inevitably higher than the inventive steels Nos. 1-10, due to consumption of Mo at approximately 2 mass %.
  • a ferritic stainless steel is improved in formability, low-temperature toughness and weldability without degradation of heat-resistant by specified alloying design, especially control of V and Cu contents, without necessity of expensive Mo.
  • the newly proposed stainless steel is useful as members or parts for automotive engines or conduit members, e.g. exhaust manifolds, front pipes, center pipes, outer casings of catalytic converters for emission of exhaust gas.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
EP02743819A 2001-07-05 2002-07-04 Ferritischer nichtrostender stahl für ein element einer abgasstrompassage Expired - Lifetime EP1413640B1 (de)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
JP2001204444 2001-07-05
JP2001204444 2001-07-05
PCT/JP2002/006768 WO2003004714A1 (fr) 2001-07-05 2002-07-04 Acier inoxydable ferritique pour element de debit de gaz d'echappement

Publications (3)

Publication Number Publication Date
EP1413640A1 true EP1413640A1 (de) 2004-04-28
EP1413640A4 EP1413640A4 (de) 2004-12-15
EP1413640B1 EP1413640B1 (de) 2005-05-25

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EP02743819A Expired - Lifetime EP1413640B1 (de) 2001-07-05 2002-07-04 Ferritischer nichtrostender stahl für ein element einer abgasstrompassage

Country Status (8)

Country Link
US (4) US20040170518A1 (de)
EP (1) EP1413640B1 (de)
JP (2) JP4197492B2 (de)
KR (1) KR20040007764A (de)
CN (1) CN1225566C (de)
DE (1) DE60204323T2 (de)
ES (1) ES2240764T3 (de)
WO (1) WO2003004714A1 (de)

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EP1930461A1 (de) * 2006-12-07 2008-06-11 Nisshin Steel Co., Ltd. Ferritischer Edelstahl für Abgasleitungskomponenten eines Fahrzeuges und geschweißtes Stahlrohr
EP2767605A4 (de) * 2011-10-14 2015-06-03 Jfe Steel Corp Ferritischer edelstahl
EP2058413A4 (de) * 2007-02-26 2016-04-20 Nippon Steel & Sumikin Sst Ferretisches edelstahlblech mit hervorragender hitzeresistenz
US9365915B2 (en) 2011-10-14 2016-06-14 Jfe Steel Corporation Ferritic stainless steel
US9399809B2 (en) 2011-02-08 2016-07-26 Nippon Steel & Sumikin Stainless Steel Corporation Hot rolled ferritic stainless steel sheet, method for producing same, and method for producing ferritic stainless steel sheet
EP2351868A4 (de) * 2008-10-24 2016-11-30 Nippon Steel & Sumikin Sst Ferritisches edelstahlblech für agr-kühlgeräte
EP3231883A4 (de) * 2014-12-11 2017-10-18 JFE Steel Corporation Ferritischer edelstahl und verfahren zur herstellung davon
EP2617854A4 (de) * 2010-09-16 2018-01-10 Nippon Steel & Sumikin Stainless Steel Corporation Hitzebeständige ferrit-edelstahlplatte mit hervorragender oxidierungsfestigkeit
EP3508598A4 (de) * 2016-09-02 2019-08-28 JFE Steel Corporation Ferritischer edelstahl
EP3572544A4 (de) * 2017-01-19 2020-05-20 Nippon Steel Stainless Steel Corporation Ferritischer edelstahl und ferritischer edelstahl für autogaswegelemente

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JP5274074B2 (ja) * 2008-03-28 2013-08-28 新日鐵住金ステンレス株式会社 耐酸化性に優れた耐熱性フェライト系ステンレス鋼板
JP5239643B2 (ja) * 2008-08-29 2013-07-17 Ｊｆｅスチール株式会社 熱疲労特性、高温疲労特性、耐酸化性および加工性に優れるフェライト系ステンレス鋼
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JP5609571B2 (ja) 2010-11-11 2014-10-22 Ｊｆｅスチール株式会社 耐酸化性に優れたフェライト系ステンレス鋼
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EP2617854A4 (de) * 2010-09-16 2018-01-10 Nippon Steel & Sumikin Stainless Steel Corporation Hitzebeständige ferrit-edelstahlplatte mit hervorragender oxidierungsfestigkeit
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EP3572544A4 (de) * 2017-01-19 2020-05-20 Nippon Steel Stainless Steel Corporation Ferritischer edelstahl und ferritischer edelstahl für autogaswegelemente

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DE60204323D1 (de) 2005-06-30
CN1225566C (zh) 2005-11-02
US20040170518A1 (en) 2004-09-02
KR20040007764A (ko) 2004-01-24
US20090053093A1 (en) 2009-02-26
CN1524130A (zh) 2004-08-25
ES2240764T3 (es) 2005-10-16
EP1413640B1 (de) 2005-05-25
US20100119404A1 (en) 2010-05-13
JP5138504B2 (ja) 2013-02-06
WO2003004714A1 (fr) 2003-01-16
JP2008297631A (ja) 2008-12-11
JPWO2003004714A1 (ja) 2004-10-28
JP4197492B2 (ja) 2008-12-17
EP1413640A4 (de) 2004-12-15
US20110176954A1 (en) 2011-07-21

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