WO2003004714A1 - Acier inoxydable ferritique pour element de debit de gaz d'echappement - Google Patents

Acier inoxydable ferritique pour element de debit de gaz d'echappement Download PDF

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Publication number
WO2003004714A1
WO2003004714A1 PCT/JP2002/006768 JP0206768W WO03004714A1 WO 2003004714 A1 WO2003004714 A1 WO 2003004714A1 JP 0206768 W JP0206768 W JP 0206768W WO 03004714 A1 WO03004714 A1 WO 03004714A1
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Prior art keywords
mass
less
steel
stainless steel
temperature
Prior art date
Application number
PCT/JP2002/006768
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English (en)
Japanese (ja)
Inventor
Manabu Oku
Yoshitomo Fujimura
Toshirou Nagoya
Original Assignee
Nisshin Steel Co., Ltd.
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
Application filed by Nisshin Steel Co., Ltd. filed Critical Nisshin Steel Co., Ltd.
Priority to EP02743819A priority Critical patent/EP1413640B1/fr
Priority to KR10-2004-7000076A priority patent/KR20040007764A/ko
Priority to US10/482,718 priority patent/US20040170518A1/en
Priority to JP2003510470A priority patent/JP4197492B2/ja
Priority to DE60204323T priority patent/DE60204323T2/de
Publication of WO2003004714A1 publication Critical patent/WO2003004714A1/fr
Priority to US13/042,542 priority patent/US20110176954A1/en
Priority to US13/632,418 priority patent/US20130263979A1/en

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Classifications

    • 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 is used as an exhaust gas flow path member of various internal combustion engines such as automobiles, such as an exhaust manifold, a front pipe, a center pipe, a catalytic converter outer cylinder, etc., and has heat resistance, low temperature toughness, Related to ferritic stainless steel with excellent weldability. Background art
  • Exhaust gas flow path members of automobiles are exposed to a high-temperature atmosphere that is in direct contact with the exhaust gas during operation, and are subjected to thermal stress due to repeated operation and shutdown and vibration of the engine during operation. In cold climates, cold winters are also subject to mechanical stress at low temperatures. Therefore, the materials used for exhaust system components must be durable in extremely harsh environments.
  • a stainless steel plate or pipe is used as an exhaust gas flow path member, it is important to have excellent heat resistance, as well as excellent weldability and workability because it can be assembled into a product shape by welding and processing. It is a characteristic. Toughness (low-temperature toughness) that can withstand secondary processing during molding and mechanical load at low temperature during use is also required.
  • Ferritic stainless steel has a smaller thermal expansion than austenitic stainless steel, and is superior in thermal fatigue properties and scale peel resistance. Since the cost of steel is low, ferrite stainless steel is often used for exhaust gas flow passage members. Ferritic stainless steels have inherently lower high-temperature strength than austenitic stainless steels, and improvements have been made to improve high-temperature strength. For example, there are SUS430J11-based Nb-added steel, Nb / Si composite-added steel (JP-A-3-274245), and Nb / Mo composite-added steel (JP-A-5-125491). Of these, Nb and Mo complex addition steels have the highest high-temperature strength and are used in places where excellent thermal fatigue properties are required.
  • Nb and Mo composite additive steels tend to have lower workability and lower temperature toughness than other steel types. Cases of improved workability and low-temperature toughness are occasionally seen, Is not enough. Another disadvantage is the high cost of steel because it contains a large amount of expensive elemental Mo.
  • the present invention has been devised to solve such a problem, and does not use expensive Mo as an alloy component, has heat resistance comparable to that of Nb and Mo composite added steel,
  • An object of the present invention is to provide a ferritic stainless steel having excellent low-temperature toughness and weldability for exhaust gas flow path members.
  • the ferritic stainless steel for exhaust gas flow passage members of the present invention has the following characteristics: C: 0.03% by mass, Si: 1.0% by mass, Mn: 1.5% by mass, Ni: 0.6% by mass, Cr: : 10 to 20% by mass, Nb: 0.50% by mass or less, Cu: 0.8 to 2.0% by mass, A1: 0.03% by mass or less, V: 0.03 to 0.20% by mass, N: 0.03% by mass or less, and Nb ⁇ 8 (C + N).
  • This ferritic stainless steel does not contain Mo as an alloying component and contains 0.05 to 0.30% by mass of i and Z to further enhance formability or 0.0005 to 0.02% by mass ⁇ to further enhance secondary workability. You can also. BRIEF DESCRIPTION OF THE FIGURES
  • Fig. 1 is a graph showing the effect of Cu on 0.2% proof stress at high temperatures.
  • SUH409L, SUS430J11, and SUS429 stainless steels have been used as materials that satisfy the heat resistance characteristics in the environment where the exhaust gas flow path members are exposed, but although the maximum temperature remains at about 800 to 900 ° C.
  • Some parts require significantly higher high-temperature strength than conventional steel grades. Areas requiring high-temperature strength are also places where the structure is extremely complex and thermal fatigue is likely to occur due to repeated application of thermal stress.
  • the constituent material of the relevant part is required to have workability and low-temperature toughness that cannot be obtained with Mo-added steel.
  • the present inventors have investigated the effects of various alloying elements in order to satisfy the characteristics required for the constituent material of such a portion. As a result, it was found that the combined addition of V and Cu improved the high-temperature strength below 900 ° C, workability, and low-temperature toughness, and achieved the same level as Nb and Mo-added steel.
  • Figure 1 shows the results of a tensile test of steels with various contents of Cu added to the basic composition of 17Cr-0.4Nb-0.1V steel.
  • Fig. 1 also shows the strength level of SUS444-based steel containing 18Cr-2Mo-0.4Nb, which is a Nb and Mo composite added steel, as a basic component for comparison.
  • the 0.2% resistance at 700 and 80 CTC increases sharply with increasing Cu content.
  • the Cu content is 0.8% by mass or more, a 0.2% proof stress equivalent to or higher than the SUS444 system containing about 2% by mass of Mo is obtained.
  • the 0.2% resistance to heat at 900 ° C it was confirmed by another experiment that the increase in V and Cu did not reach the level of SUS444 steel, but the 0.2% resistance was improved more than the Nb-containing ferritic stainless steel. ing.
  • the combined addition of V and Cu is effective in improving the high-temperature strength in a temperature range of 900 or less, and no significant adverse effect appears at 900 or more.
  • Nb-based precipitates A structure in which Cu-based precipitates are finely dispersed compared to the steel with Nb added alone is observed. From these observation results, it is found that V preferentially precipitates in the as-annealed state or in the early stage of heating, thereby suppressing the formation of Nb-based precipitates and Cu-based precipitates. As a result, fine Nb-based precipitates and Cu-based precipitates It is presumed that they are dispersed and contribute to precipitation strengthening. Presumably, this is because the finely dispersed precipitates do not agglomerate even after heating for a long time in the early stage of heating, and the precipitation strengthening works effectively for a long time.
  • V which is a strong carbonitride forming element
  • bonds with N more solid-solution Nb effective for improving high-temperature strength can be secured than V-free steel when the amount of Nb added is the same.
  • the same high-temperature strength as V-free steel can be achieved with a reduced Nb content, and as a result, contributes to the improvement of workability and low-temperature toughness.
  • the amount of Nb and V carbonitrides in the as-annealed state increases.
  • the grain size of the weld heat affected zone becomes less likely to become coarse and the toughness is improved. Since the generation of Cr-based carbides is also suppressed, the intergranular corrosion resistance is also improved.
  • C and N are generally considered to be effective elements for improving high-temperature strength such as creep strength, but if they are contained excessively, oxidation properties, workability, low-temperature toughness, and weldability are reduced.
  • V and Nb are added as elements that fix C and N as carbonitrides, it is necessary to add V and Nb in amounts corresponding to the C and ⁇ concentrations.
  • both C and N were regulated to 0.03% by mass or less (preferably 0.015% by mass or less).
  • Si is a very effective element for improving high temperature oxidation characteristics, but is not so effective for increasing the high temperature strength below 900.
  • Si content was regulated to 1.0% by mass or less (preferably, 0 :! to 0.5% by mass).
  • Mn 1.5 mass% or less
  • Mn content was regulated to 1.5% by mass or less (preferably 0.5% by mass or less).
  • Ni 0.6 mass% or less
  • Ni is excessively added to a steel type with a low Cr content, a martensitic phase is formed similarly to Mn, and the thermal fatigue properties and workability are reduced. Due to the high price of raw materials, excessive addition of Ni should be avoided. Therefore, the Ni content was regulated to 0.6% by mass or less (preferably 0.5% by mass or less). Cr: 10-20% by mass
  • the Cr content is selected in the range of 10 to 20% by mass.
  • the Cr content is preferably adjusted to the working temperature of the material. For example, for high-temperature oxidation resistance up to 950 ° C, 16 to 19% by mass is preferable, and for high-temperature oxidation resistance at 900 ° C or lower, 12 to 16% by mass is sufficient.
  • Nb the remaining solid solution Nb to which the carbonitrides are fixed has the effect of increasing the high-temperature strength.
  • the Nb content that satisfies Nb ⁇ 8 (C + N) is required for fixing C and N, but the upper limit of the Nb content is set to suppress adverse effects on workability, low-temperature toughness, and susceptibility to welding hot cracking. Is set to 0.5% by mass.
  • an Nb content satisfying 8 (C + N) + 0.10 ⁇ Nb ⁇ 0.45 is selected.
  • the high-temperature strength of ferritic stainless steel improves.
  • coexistence with Nb improves workability, low-temperature toughness, intergranular corrosion susceptibility, and toughness of the heat affected zone.
  • These effects appear at a V content of 0.03% by mass or more, but an excessive addition exceeding 0.20% by mass causes deterioration in workability and low-temperature toughness. Therefore, the V content is selected in the range of 0.03 to 0.20 mass% (preferably 0.04 to 0.15 mass).
  • the r-value (Rankford value) of steel It is an element that improves the r-value (Rankford value) of steel to improve formability.
  • the effect of addition becomes significant at 0.05% by mass or more.
  • the surface properties of the steel material deteriorate due to the formation of TiN, and the weldability and low-temperature toughness are adversely affected. Therefore, it is desired to reduce the Ti content as much as possible even when Ti is added for improving formability. Therefore, the upper limit of the Ti content is restricted to 0.30% by mass (preferably 0.20% by mass).
  • the B content is selected in the range of 0.0005 to 0.02% by mass (preferably 0.001 to 0.01% by mass).
  • the ferritic stainless steel of the present invention is based on the premise that expensive Mo is not added, but is an element that is easily mixed as an inevitable impurity during the production of stainless steel. If a large amount of Mo is mixed in, it will adversely affect workability, low-temperature toughness, and weldability, etc. Therefore, it is desirable to limit the amount of Mo mixed to less than 0.10% by mass.
  • P, S, 0, etc. which are common impurities, as much as possible.
  • the upper limits of P, S, and 0 be 0.04 mass%, 0.03 mass%, and 0.02 mass%, respectively.
  • W, Zr, Y, REM (rare earth element), which is effective for improving heat resistance, and Ca, Mg, Co, which is effective for improving hot workability, can be added as needed.
  • Table 2 Composition and composition of test material (comparative steel)
  • a 2.0-mm-thick cold-rolled annealed plate was subjected to a high-temperature tensile test, a high-temperature oxidation test, a room-temperature tensile test, and a Charpy impact test, and a 1.2-mm-thick cold-rolled annealed plate was subjected to a weld hot cracking test.
  • test piece was pulled at 800 ° C in accordance with JISG0567, and 0.2% resistance was measured.
  • the test piece was continuously heated at 850 ° C, 900 ° C, 950 ° C, 1000 ° C, and 1100 ° C for 200 hours in accordance with JISZ2281.
  • the heated test specimens were visually observed for the occurrence of abnormal oxidation (thick oxide penetrating in the plate thickness direction), and the critical temperature at which abnormal oxidation did not occur was determined.
  • a test piece was used at a temperature of -75 ° C, -50t, -25, 0 ° C, and 25 ° C using a subsize test piece with a thickness of 2.0 nm in accordance with JISZ2242.
  • a shock was applied to the steel to determine the ductility-toughness transition temperature.
  • TIG welding was performed with both ends of a 40 mm X 20 mm test piece held and tensile stress applied in the longitudinal direction, and the minimum strain at which cracking began to occur was determined. The obtained critical strain amount was used as an index of the hot cracking susceptibility.
  • Each of the steels Nos. 1 to 10 of the present invention has a much higher 0.2% proof stress at 800 compared to the Ti-added steel (No. 15), Nb, and Si-added steel (No. 16). It had a 0.2% power resistance comparable to or surpassed that of the Mo-added steel (No. 17). Elongation by room-temperature tensile test, ductile-brittle transition temperature by Charpy impact test, and critical strain by welding hot cracking test have properties equal to or higher than those of Nb and Mo composite-added steel (No. 17). It was confirmed that the target performance could be obtained without doing so. As for abnormal oxidation, as can be seen from the results of Nos. 4, 5, and 12, the lower the Cr content, the lower the critical temperature. From the effect of Cr content on abnormal oxidation, it can be understood that it is necessary to set an appropriate amount of Cr content according to the temperature of the application site.
  • Comparative steels No.11, No.15, No.16 and No.19 which lack V and Cu, have sufficient workability, low-temperature toughness and weldability, but inferior high-temperature strength at 800 ° C. ing.
  • comparative steel No. 12 which contains an excessive amount of steel, has excellent high-temperature strength, its workability and weldability are inferior to those of Nb and Mo composite-added steels, and it hinders processing into product shapes and welding.
  • the comparative steel No. 13 containing too much Si and the comparative steel No. 14 containing too much Nb have excellent workability and low-temperature toughness even if they have excellent high-temperature strength.
  • the weldability was inferior to the steel of the present invention.
  • Comparative steel No. 17 containing Mo has the same performance as the steel of the present invention, but has a slightly lower low-temperature toughness. Moreover, since Mo is contained at about 2% by mass, it is inevitable that the material cost will be higher than that of the steel of the present invention.
  • Critical strain 3% by mass or more is indicated by ⁇ , and less than 3% by mass is indicated by X.
  • the underline indicates that the property does not satisfy the purpose of the present invention.
  • ferritic stainless steel As described above, by strictly controlling the content of various alloying elements contained in ferritic stainless steel, especially the range of V and Cu, high heat resistance is secured without the need for expensive Mo. While improving workability, low-temperature toughness, and weldability, ferritic stainless steel suitable for exhaust gas path members can be obtained. This ferritic stainless steel is used in exhaust gas flow passage members, such as automobile engines, exhaust pipes, front pipes, center pipes, and outer tubes of catalytic converters, utilizing its excellent properties.

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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)

Abstract

L'invention concerne un acier inoxydable ferritique pour élément de débit de gaz d'échappement, présentant la composition chimique suivante ( % de masse) : C : 0,03 % ou moins, Si : 1,0 % ou moins, Mn : 1,5 % ou moins, Ni : 0,6 % ou moins, Cr : 10 à 20 %, Nb : 0,50 % ou moins, Cu :0,8 à 2,0 %, Al : 0,03 % ou moins, à condition que Nb ≥ 8 (C+N), le reste étant constitué de Fe et des impuretés inévitables. Le contenu en Mo de l'acier inoxydable ferritique, constituant une impureté, représente, de préférence, 0,10 % de masse ou moins, et le contenu en Ti et B peut éventuellement varier de 0,05 à 0,30 et de 0,0005 à 0,02 % de masse, respectivement. L'acier inoxydable ferritique présente une résistance thermique comparable à celle d'un acier inoxydable ferritique auquel on a rajouté Nb et Mo, ainsi qu'une formabilité, une résistance à faible température et une soudabilité excellentes.
PCT/JP2002/006768 2001-07-05 2002-07-04 Acier inoxydable ferritique pour element de debit de gaz d'echappement WO2003004714A1 (fr)

Priority Applications (7)

Application Number Priority Date Filing Date Title
EP02743819A EP1413640B1 (fr) 2001-07-05 2002-07-04 Acier inoxydable ferritique pour element de debit de gaz d'echappement
KR10-2004-7000076A KR20040007764A (ko) 2001-07-05 2002-07-04 배기가스 유로 부재용 페라이트계 스테인레스 강
US10/482,718 US20040170518A1 (en) 2001-07-05 2002-07-04 Ferritic stainless steel for member of exhaust gas flow passage
JP2003510470A JP4197492B2 (ja) 2001-07-05 2002-07-04 排ガス流路部材用フェライト系ステンレス鋼
DE60204323T DE60204323T2 (de) 2001-07-05 2002-07-04 Ferritischer nichtrostender stahl für ein element einer abgasstrompassage
US13/042,542 US20110176954A1 (en) 2001-07-05 2011-03-08 Ferritic Stainless Steel for Use as Conduit Members for Emission of Automotive Exhaust Gas
US13/632,418 US20130263979A1 (en) 2001-07-05 2012-10-01 Ferritic Stainless Steel for Use as Conduit Members for Emission of Automotive Exhaust Gas

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2001204444 2001-07-05
JP2001-204444 2001-07-05

Related Child Applications (1)

Application Number Title Priority Date Filing Date
US12/233,122 Continuation US20090053093A1 (en) 2001-07-05 2008-11-06 Ferritic Stainless Steel for Use as Conduit Members For Emission of Automotive Exhaust Gas

Publications (1)

Publication Number Publication Date
WO2003004714A1 true WO2003004714A1 (fr) 2003-01-16

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

Cited By (29)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1930461A1 (fr) 2006-12-07 2008-06-11 Nisshin Steel Co., Ltd. Acier inoxydable ferritique pour composants de conduit de gaz d'échappement d'automobile et tuyau soudé en acier
JP2008138270A (ja) * 2006-12-05 2008-06-19 Nippon Steel & Sumikin Stainless Steel Corp 加工性に優れた高強度ステンレス鋼板およびその製造方法
WO2008093888A1 (fr) 2007-02-02 2008-08-07 Nisshin Steel Co., Ltd. Acier inoxydable ferritique pour un élément de passage de gaz d'échappement
WO2008105134A1 (fr) 2007-02-26 2008-09-04 Nippon Steel & Sumikin Stainless Steel Corporation Tôle d'acier inoxydable ferritique ayant une excellente résistance à la chaleur
WO2009110641A1 (fr) 2008-03-07 2009-09-11 Ｊｆｅスチール株式会社 Acier inoxydable ferritique ayant d'excellentes résistance à la chaleur et ténacité
WO2009110640A1 (fr) 2008-03-07 2009-09-11 Ｊｆｅスチール株式会社 Acier inoxydable ferritique ayant une excellente résistance à la chaleur
JP2009235555A (ja) * 2008-03-28 2009-10-15 Nippon Steel & Sumikin Stainless Steel Corp 耐酸化性に優れた耐熱性フェライト系ステンレス鋼板
JP2010053417A (ja) * 2008-08-29 2010-03-11 Jfe Steel Corp 熱疲労特性、高温疲労特性および耐酸化性に優れるフェライト系ステンレス鋼
JP2010053418A (ja) * 2008-08-29 2010-03-11 Jfe Steel Corp 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
JP2010053420A (ja) * 2008-08-29 2010-03-11 Jfe Steel Corp 熱疲労特性、高温疲労特性、耐酸化性および靭性に優れるフェライト系ステンレス鋼
WO2010110466A1 (fr) 2009-03-24 2010-09-30 新日鐵住金ステンレス株式会社 Plaque en acier inoxydable ferritique ayant une excellente résistance à la chaleur et une excellente aptitude au façonnage
JP2010236001A (ja) * 2009-03-31 2010-10-21 Nisshin Steel Co Ltd フェライト系ステンレス鋼
WO2011024568A1 (fr) 2009-08-31 2011-03-03 Ｊｆｅスチール株式会社 Acier inoxydable ferritique ayant une excellente résistance à la chaleur
WO2011068328A2 (fr) * 2009-12-04 2011-06-09 주식회사 포스코 Tôle d'acier laminée à froid à traiter présentant une excellente résistance à la chaleur, et procédé de production de celle-ci
WO2011118854A1 (fr) 2010-03-26 2011-09-29 新日鐵住金ステンレス株式会社 Plaque d'acier inoxydable ferritique ayant une excellente résistance à la chaleur et une excellente aptitude au façonnage, et procédé de fabrication de celle-ci
JP2012007195A (ja) * 2010-06-22 2012-01-12 Nisshin Steel Co Ltd 耐熱性および時効硬化特性に優れた低Ｃｒステンレス鋼およびその鋼からなる自動車排ガス経路部材
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KR20040007764A (ko) 2004-01-24
US20090053093A1 (en) 2009-02-26
US20040170518A1 (en) 2004-09-02
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CN1225566C (zh) 2005-11-02
CN1524130A (zh) 2004-08-25
ES2240764T3 (es) 2005-10-16
DE60204323T2 (de) 2006-01-26
JPWO2003004714A1 (ja) 2004-10-28
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