WO2003004714A1 - Ferritic stainless steel for member of exhaust gas flow passage - Google Patents

Ferritic stainless steel for member of exhaust gas flow passage 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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mass
nb
ferritic stainless
stainless steel
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PCT/JP2002/006768
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French (fr)
Japanese (ja)
Inventor
Manabu Oku
Yoshitomo Fujimura
Toshirou Nagoya
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Nisshin Steel Co., Ltd.
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Priority to JP2001204444 priority Critical
Priority to JP2001-204444 priority
Application filed by Nisshin Steel Co., Ltd. filed Critical Nisshin Steel Co., Ltd.
Publication of WO2003004714A1 publication Critical patent/WO2003004714A1/en
Priority claimed from US13/632,418 external-priority patent/US20130263979A1/en

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    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/02Ferrous alloys, e.g. steel alloys containing silicon
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/004Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/04Ferrous alloys, e.g. steel alloys containing manganese
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/18Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/18Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/18Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/18Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/18Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE BY DECARBURISATION, TEMPERING OR OTHER TREATMENTS
    • C21D2211/00Microstructure comprising significant phases
    • C21D2211/005Ferrite
    • FMECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01NGAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR MACHINES OR ENGINES IN GENERAL; GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR INTERNAL COMBUSTION ENGINES
    • F01N2530/00Selection of materials for tubes, chambers or housings
    • F01N2530/02Corrosion resistive metals
    • F01N2530/04Steel alloys, e.g. stainless steel

Abstract

A ferritic stainless steel for use in a member of an exhaust gas flow passage, which has a chemical composition, in mass %: C: 0.03 % or less, Si: 1.0 % or less, Mn: 1.5 % or less, Ni: 0.6 % or less, Cr: 10 to 20 %, Nb: 0.50 % or less, Cu: 0.8 to 2.0 %, Al: 0.03 % or less, V: 0.03 to 0.20 %, N: 0.03 % or less, provided that Nb ≥ 8(C+N) is satisfied, and balance: Fe and inevitable impurities. The Mo content of the ferritic stainless steel as an impurity is preferably controlled to 0.10 mass % or less, and Ti and B may be optionally contained in amounts of 0.05 to 0.30 and 0.0005 to 0.02 mass %, respectively. The ferritic stainless steel exhibits a thermal resistance comparable to that of a ferritic stainless steel containing Nb and Mo added thereto, and also is excellent in formability, the toughness at a low temperature and weldability.

Description

Ferritic stainless steels art for bright fine manual exhaust gas passage member

The present invention Ekizo one stoma two hold, front pipes, center first pipe, catalytic compactors one coater outer cylinder or the like, is used as the exhaust gas flow path member for various internal combustion engine, including automobile, heat resistance, low temperature toughness, about the excellent ferritic stainless steel weldability. BACKGROUND

Exhaust gas flow path member of an automobile is exposed to a high temperature atmosphere touching the exhaust gas is directly during operation, operation, vibration of the engine thermal stress or during operation due to the repetition of stopping applied. In cold climates, also applied mechanical stress at low temperatures during the winter of start-up. Therefore, the materials used in the exhaust system member is required durability in very harsh environments. If the plate material Ya pipe stainless steel for use in exhaust gas passage member, Rukoto excellent heat resistance as well, because it is assembled in the product shape by welding and machining, weldability, also an important requirement to have excellent processability it is a characteristic. Toughness to withstand the mechanical load at low temperature during secondary processing or use in molding (low temperature toughness) is also required.

Ferritic stainless steels, Netsu膨 Zhang compared to Osutenaito stainless steel is small, thermal fatigue resistance, has excellent resistance to scale peeling resistance. Steel because costs were low, in many cases ferritic stainless steel is used in the exhaust gas line members. Ferritic stainless steels, high-temperature strength than austenitic stainless steel because inherently low, improvements to improve the high temperature strength have been subjected. For example, SUS430J11 system Nb-added steel, Nb, Si composite-added steel (JP-3 274 245 JP), there is Nb, Mo composite-added steel (JP-A 5-125491 JP) or the like. Among them, Nb, Mo double if added steel, high-temperature strength is the highest, are used in the site to be required to have excellent thermal fatigue resistance. However, Nb, Mo composite addition steel is in the workability and tend to low temperature toughness is inferior to other Me steels. Workability, although cases having improved low-temperature toughness is scattered, difficult always also sufficient to say. It is also a disadvantage that high steel costs for containing a large amount of expensive elements Mo.

However, looking at the correlation between the high-temperature strength of the exhaust gas passage components are most important in an environment exposed (resistance to thermal fatigue fracture) and the high-temperature oxidation properties (abnormal oxidation limit temperature), high-temperature strength, high temperature oxidation characteristics necessarily some sites do not need to be compatible at a high level. Specifically, in very complex sites even structure is no exhaust gas temperature is too high, high temperature strength is more important than the high-temperature oxidation properties, workability and low-temperature toughness to accommodate the complexity of the structure is emphasized that. Even for such sites, at present Nb, without the Ru seat the use of Mo composite addition steel, even if the heat resistance is a sufficient workability, low-temperature toughness, there is room for improvement in terms of cost. Disclosure of the Invention

The present invention has been devised to solve such problems, without the use of expensive Mo as an alloy component, have heat resistance comparable Nb, the Mo composite addition steel, formability, low temperature toughness, and to provide an excellent exhaust gas passage member for ferritic stainless steels weldability.

Exhaust gas flow path member for ferritic stainless steel of the present invention in order to achieve its objectives, C: 0.03 wt% or less, Si: 1.0 wt% or less, Mn: 1.5 wt% or less, Ni: 0.6 wt% or less, Cr : 10 to 20 mass%, Nb: 0.50 mass% or less, Cu: 0.8 to 2.0 mass%, A1: 0.03% by mass or less, V: 0.03-0.20 wt%, N: see contains 0.03 mass% or less, and Nb characterized in that it satisfies the ≥8 (C + N).

The ferritic stainless steel does not contain Mo as an alloying element, further comprising a β of 0.0005 to 0.02 mass% for increasing the i and Z or secondary workability from 0.05 to 0.30 wt% to further improve the moldability it is also possible. BRIEF DESCRIPTION OF THE DRAWINGS

Figure 1 is a conventional or et SUH409L system as a material satisfying heat resistance in an environment in which the best mode exhaust gas passage member for carrying out the graph invention showing the effect of Cu on 0.2% yield strength at high temperature are exposed, SUS430J11 system, although SUS429-based stainless steel is used, there is also a site where much higher hot strength of the conventional steels but the maximum temperature remains about 800 to 900 ° C is required. Site high-temperature strength is required, the structure is very complex and also a thermal fatigue fracture easily occurs place since the thermal stress is applied repeatedly. Moreover, the constituent material of the portion, workability and low-temperature toughness and the like which can not be obtained in the Mo-added steel is required.

The present inventors have, in order to satisfy the required play characteristics the material of such sites were investigated the effects of various alloying elements. As a result, V, high-temperature strength below 900 ° C by the combined addition of Cu, processability, low-temperature toughness is improved, it found that Nb, the Mo-added steel at the same level is obtained.

It was added V traces, with the Nb-containing ferritic stainless steels with varying Cu content was measured with 0.2% 耐Ka in Oyobi 800 high temperature tensile test at 700. As a result, the regulation of dopants and the Cu content of V, 900 ° C or less in high-temperature strength is above the temperature dramatically was found that Nb, high-temperature strength comparable to Mo composite addition steel is obtained.

Figure 1 is a tensile test results of the steel added with Cu at various content to the basic composition of 17Cr- 0.4Nb- 0.1V steel. 1 shows also to intensity levels of SUS444-based steel Nb, a 18Cr-2Mo-0.4Nb a Mo composite-added steel as a basic component for comparison.

As it is clear from the results shown in FIG. 1, 0.2% 耐Ka at 700 a and 80CTC is increased sharply with increasing Cu content. When the Cu content more than 0.8 mass%, SUS444 series which is equal to or more than the 0.2% yield containing Mo about 2% by weight is obtained. For the 0.2% 耐Ka in 900 ° C, V, although not reach the level of SUS444 steels in increasing the Cu, sure to improve 0.2% 耐Ka than Nb-containing ferritic stainless steel in a separate experiment ing. That, combined addition V, of Cu in a temperature range of below 900 is effective in improving high-temperature strength, does not appear significant adverse effect even more than 900.

Nb, Cu, a composite addition and V, but why the high-temperature strength is secured at a high level is not fully understood, Nb-based precipitates in either after brief heating and long, Cu-based precipitates Nb added alone was compared to finely dispersed in steel structure is observed. This observation, by V is preferentially deposited on the state or heating the initial as-annealed, Nb-based precipitates, the formation of Cu-based precipitates is suppressed, resulting in fine Nb-based precipitates, the Cu-based precipitates dispersed precipitation is inferred to contribute to precipitation strengthening. It does not aggregate by finely dispersed precipitates prolonged heating to heat the initial, it is inferred that contribute to precipitation strengthening is acting effect until a long time.

Furthermore, a potent carbonitride forming element V is for coupling to N, when the amount of Nb added was the same can be increased secure than V not added steel effective solute Nb to improve high-temperature strength. In other words, it can be achieved in Nb content high temperature strength of the V-free steels the same level is reduced, resulting in processability, contribute to the improvement of low temperature toughness.

Moreover, Nb, in a system V coexist, becomes large amounts of Nb-based, V-based carbonitride in a state annealing. Nb-based, grain HAZ with increasing V based carbonitrides hardly coarsened toughness is improved. Generation of Cr carbide also being suppressed, thereby improving grain boundary corrosion susceptibility.

Hereinafter, the alloy components of the ferritic stainless steel to which the present invention is directed, the content and the like will be described.

C: 0.03 wt% or less

N: 0.03% by mass or less

C and N are generally have been effective element for improving the high temperature strength such as creep strength, oxidation properties to be included in excess, processability, low-temperature toughness, weldability decreases. C, and this component system is added V, and Nb to N as an element for fixing a carbonitride, C, V in an amount commensurate with the Ν concentration, required is the addition of Nb. V, in order to suppress an increase in raw material costs due to the increase of Nb, C, N together 0.03 wt% or less (preferably, 0.015 wt% or less) was regulated.

Si: 1.0 wt% or less

A very effective element for improving the high temperature oxidation properties, not very effective in raising the top of the high-temperature strength below 900. Excessive addition of Si to the contrary, increases the hardness, processability, low-temperature toughness is lowered. Therefore, the Si content of 1.0 mass% or less (preferably, 0.:!~ 0.5 wt%) was regulated. Mn: 1.5 mass% or less

High temperature oxidation characteristics of ferritic stainless steel, an alloy element particularly improve the scale peelability, excessive addition of Mn workability degrades the weldability. Moreover, Orth since Tenaito phase is stabilizing element, apt to generate the Ka剩 added Then martensite phase Mn in amount less steels Cr, causing thermal fatigue resistance, the workability occurs. Accordingly, 1.5 wt% or less of Mn content (preferably 0.5 mass% or less) won Tadashi on.

Ni: 0.6 mass% or less

An austenite phase stabilizing elements, the Ni creating excessive added pressure to the Mn as well as the martensite phase to the low grades of C r content, causes decreased thermal fatigue resistance, processability. Also because of high raw material prices, excessive addition of Ni should be avoided. Wherein, the Ni content 0.6 wt% or less (preferably 0.5 mass% or less) was regulated. Cr: 10 ~ 20 mass%

Ferrite phase with stabilizing an essential element for improvement of oxidation resistance is important to the high temperature material. Is preferably larger the Cr content from the viewpoint of oxidation resistance, an excessive addition of steel is embrittled to degrade workability by increasing the hardness. Therefore, selecting the Cr content in the range of 10 to 20 wt%. Cr content is preferably adjusted according to the operating temperature of the material. For example, the high-temperature oxidation resistance up to 950 ° C 16~: 19 mass% is preferred, the high-temperature oxidation resistance of below 900 ° C 12~; 16 wt% is sufficient.

Nb: 8 (C + N~0.50 wt%

C, to secure the N as carbonitrides, the remainder of the solid solution Nb fixed carbonitrides exhibits an effect of increasing the high temperature strength of. However, the addition of an excess amount of Nb, formability, low temperature toughness is degraded, weld hot cracking susceptibility increases. C, and the fixation of N is required Nb content satisfies Nb≥8 (C + N), processability, the upper limit of the Nb content to suppress the adverse effect the low-temperature toughness, the weld hot cracking sense susceptibility setting to 0.5 wt%. good Mashiku is chosen is Nb content satisfies 8 (C + N) + 0.10≤Nb≤0.45. Cu: 0.8~2.0 mass%

In the present component system, it is a very important element for improving the high temperature strength. In the temperature range of the onset bright and others were investigated, almost all of the Cu has been solid solution in the matrix of the annealed condition, precipitated during heating. Precipitated Cu exerts strengthening effect on early as well as Mo-added steel, but reinforced action by prolonged heating gradually disappears. In order to obtain a high temperature strength required degree, it is necessary to Cu content of 0.8 wt% As is clear from FIG. However, with the increase of the Cu content, processability, low-temperature toughness, it decreases weldability. Processability, in order to suppress the adverse effect the low-temperature toughness, weldability, to restrict the upper limit of the Cu content to 2.0 mass%. Preferred Cu content is in the range of 1.0-1.7 wt%. A1: 0.03% by mass or less

Is added to the steel making as a deoxidizer also exhibit effects of improving high-temperature oxidation resistance. However, excessive addition of A1 is the surface properties degrade workability, weldability, adversely affect the low-temperature toughness. Thus, A1 content is preferably as small, the upper limit 0.03% by weight

(Preferably 0.02 mass%) for regulating the.

V: 0.03~0.20 mass%

Nb, Cu and the composite addition, improved high-temperature strength of the ferritic stainless steel. Further, the coexistence with Nb, formability, low-temperature toughness, and improves grain boundary corrosion susceptibility, is also improved toughness of the heat affected zone. These effects appear in V content of not less than 0.03 mass%, the excessive addition of more than 0.20 mass% workability, lowering the low temperature toughness. Therefore, the V content 0.03 to 0.20% by weight (preferably, 0.04 to 0.15 wt) is selected in the range of.

Ti: 0.05~0.30 mass%

r value of the steel is an element for improving the moldability by improving the (Lankford value), the addition effect becomes significant at 0.05 mass% or more. However, the addition of an excess amount of Ti, due to the generation of TiN surface properties of the steel is deteriorated, weldability, also adversely appears in the low-temperature toughness. Therefore, it is desirable to reduce as much as possible Ti content even when adding Ti to the improvement of formability. Therefore, the upper limit of the Ti content 0.30% by weight (preferably, 0.20 wt%) was regulated.

B: 0.0005 ~ 0.02 mass%

To improve secondary workability of the steel, a element for suppressing cracking during multi-stage molding, the effect of adding B is remarkable at 0.0005 mass% or more. However, if the addition of a large amount B, manufacturability and weldability are degraded. Therefore, 0.0005-0.02 wt% (preferably, 0.001 to 0.01 mass%) for selecting a B content in the range of.

Mo: less than 0.10 wt%

The ferritic stainless steel of the present invention, although the assumption that no addition of expensive Mo, a mixed easily element as inevitable impurities in the production of stainless steel. Workability Mo is a large amount of contamination, low temperature toughness, since there is Hay harm such degrading weldability, it is desirable to regulate the mixing amount less than 0.10 wt%.

Although not particularly restricted except for the elements listed above, a typical non-pure product P, it is preferable to reduce S, 0, etc. as much as possible. Hot workability, considering the oxidation resistance and the like, P, S, the upper limit of each 0.04 mass% of 0, 0.03 wt%, it is preferable that 0.02 wt%. Effective W to improve the heat resistance, Zr, Y, REM (rare earth element) and, effective for improvement of hot workability Ca, Mg, may be added as necessary is also Co and the like.

The production conditions of ferritic stainless steels are not intended to otherwise constrained is applied, as long as allowed to advance solid solution Cu, excellent heat resistance remain hot rolled annealed sheet is obtained. If the steel sheet of the desired thickness by hot rolling can not be prepared, by to repeat one or more times cold rolling and annealing, can produce a steel sheet having the same heat resistance and hot-rolled annealed sheets. When the C u is finely dispersed at any stage of the manufacturing process as necessary, better high-temperature strength. Excellent properties, hot-rolled annealed sheet is maintained cold-rolled annealed 扳等 even after pressurization E or welded into a desired shape (including molding tubes). Next, examples illustrate the present invention more specifically.

Table 1, various ferritic stainless steels having the second composition was melted in a vacuum melting furnace, and 铸造 the ingot 30k. Forging an ingot, hot rolling, annealing to produce a cold-rolled annealed sheet of thickness 2.0mm and 1.2mm through Hiyakan圧 rolled, final annealed. In the table, No; ~ 10 steel of the present invention, No.ll~:.! 19 are comparative steels. Among the comparative steels, No.Ll the SUS430JU equivalent steel, No.15 is SUH409L equivalent steel, No.16 is 14Cr- Si- Nb steel, No.17 is SUS444 equivalent steel, Ekizo one stoma two none of the steels there is actually used as a for hold. Table 1: Ingredients of test materials' compositions (invention steels)

B: Roupushironpaiiota single [Nb] = Nb - 8 [C + N] one: less than the detection limit

Table 2: Ingredients of test materials, the composition (comparative steels)

B: ppm Unit [Nb〗 = Nb - 8 [C + N] one: less than the detection limit

Underline indicates that outside the range specified in the present invention.

Tensile test at a high temperature cold-rolled annealed sheet having a thickness of 2.0 mm, the high-temperature oxidation test, room temperature tensile tests were subjected to Charpy impact test was subjected to weld hot cracking test cold-rolled annealed sheet having a thickness of 1.2 mm.

The high temperature tensile test, a tensile test piece at 800 ° C in compliance with the JISG0567, was measured 0.2% 耐Ka.

The high temperature oxidation test was then 850 ° C, 900 ° C, 950 ° C, 1000 ° C, the 1100 test piece to each temperature ° C 200 hours continuous heating compliant JISZ2281. Occurrence of abnormal oxidation for heating specimens (hump thick oxide penetrating in the thickness direction) was visually observed to determine the limit temperature that does not cause abnormal oxidation.

At room temperature tensile test, and processed into 13B test piece No. cold-rolled annealed sheet of thickness 2.0mm in conformity with JISZ2241, he was determined breaking elongation after tensile test.

In Sharubi one impact test compliant with JISZ2242, using sub-size test piece having a thickness of 2.0nmi, -75 ° C, -50t, at -25, 0 ° C, the test piece at each temperature of 25 ° C pressure to give a shock to the ductility - was determined toughness transition temperature.

The weld hot cracking test, hold the ends of the 40 mm X 20 mm of the test piece, and TIG welding while applying a tensile stress in the longitudinal direction, determining the minimum of the amount of strain cracking starts to occur. The critical strain amount obtained was used as an index of the weld hot cracking susceptibility.

Table 3 shows the test results.

Both the steel of the present invention steels No.l ~ 10 are, Ti-added steel (No.l5), Nb, 0.2% proof stress is much greater at 800 compared to the Si-added steel (No.16), Nb, was 0.2% 耐Ka values ​​comparable or superior to Mo composite addition steel (No.17). Beauty Shin by room temperature tensile tests, ductile brittle transition temperature by Charpy impact test, the critical strain is also Nb by welding hot cracking test, has equivalent or more properties and Mo composite addition steel (No.17), it added pressure to Mo that the target performance can be obtained it has been confirmed without. Abnormal regard to oxidation, No.4, No.5, as can be seen from the results of No.12, the limit temperature as the Cr content is less that summer low. Abnormalities from the effects of Cr content on the oxidation, an appropriate amount of Cr content can understand the need to set according to the temperature of the application point.

Comparative Steel No.11 of V, Cu is insufficient, No.15, No.16, No.19 is processability, low-temperature toughness, although weldability is a sufficient level, poor high-temperature strength of 800 ° C ing. Comparative Steel No.12 containing Cu in excess, although excellent in high temperature strength, workability, weldability inferior Nb, than the Mo composite addition steel, went wrong in machining and welding to the product shape.

Cu content is in the specified range and the comparative steel No.13 Si content is too high also, Comparative Steel No.14 Nb containing Yuryou is too large, even though excellent high-temperature strength, workability, low-temperature toughness , weldability was inferior to the invention steels.

V content is less A1 content is more comparative steel No.18, although heat resistance and workability of the same order as the present invention steels, poor low-temperature toughness, caused to factors toughness shortage during product processing or during use the occurrence of trouble is expected. Comparative Steel No.19 which V is insufficient, the missing high-temperature strength.

Comparative Steel No.17 containing Mo has the present invention steel and comparable performance, low-temperature toughness is summer slightly lower. Moreover, since the amount of about 2% by weight of Mo, the material cost is inevitably be higher than the present invention steels.

Table 3: Evaluation test results

The critical strain 3 mass% or more 〇 shows less than 3% by mass X. Underline indicates that the characteristic does not satisfy the object of the present invention. Industrial Applicability

As described above, the content of various alloying elements contained in ferritic stainless steels, in particular V, by strictly restricting the scope of Cu, without the need for expensive Mo, ensuring excellent heat resistance processability while, low temperature toughness, improved weldability, suitable ferritic stainless steel is obtained as an exhaust gas passage components. The ferritic stainless steel, including the automotive engine by utilizing the excellent properties, Ekizo one stoma two hold, front pipe, center pipe, are used in the exhaust gas line members such catalyst compactors one coater outer cylinder or the like.

Claims

The scope of the claims
1. C: 0.03 wt% or less, Si: 1.0 wt% or less, Mn: 1.5 wt% or less, Ni: 0.6 wt% or less, Cr: 10 to 20 mass%, Nb: 0.50 mass% or less, Cu: 0.8 to 2.0 mass%, A1: 0.03% by mass or less, V: 0.03 to 0.20 mass%, N: includes 0.03 wt% or less, and satisfy the Nb≥8 (C + N), the balance being Fe and unavoidable impurities automotive exhaust gas passage member for ferritic stainless steel, characterized in that.
2. unavoidable impurities as Mo automobile exhaust gas passage of regulated by that 請 Motomeko 1 described below 0.10 mass% member for ferritic stainless steel included.
3. Furthermore according to claim 1 or 2, wherein an automobile exhaust gas passage member for ferritic stainless steel containing 0.05 to 0.30 wt% of Ti.
4. Furthermore automobile exhaust gas channel member for ferritic stainless steel according to any one of claims 1 to 3 comprising from 0.0005 to 0.02% by weight of B.
PCT/JP2002/006768 2001-07-05 2002-07-04 Ferritic stainless steel for member of exhaust gas flow passage WO2003004714A1 (en)

Priority Applications (2)

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

Applications Claiming Priority (7)

Application Number Priority Date Filing Date Title
DE2002604323 DE60204323T2 (en) 2001-07-05 2002-07-04 Ferritic stainless steel for an element of an exhaust stream passage
US10/482,718 US20040170518A1 (en) 2001-07-05 2002-07-04 Ferritic stainless steel for member of exhaust gas flow passage
EP20020743819 EP1413640B1 (en) 2001-07-05 2002-07-04 Ferritic stainless steel for member of exhaust gas flow passage
KR10-2004-7000076A KR20040007764A (en) 2001-07-05 2002-07-04 Ferritic stainless steel for member of exhaust gas flow passage
JP2003510470A JP4197492B2 (en) 2001-07-05 2002-07-04 Ferritic stainless steel for exhaust gas passage member
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

Related Child Applications (1)

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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

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EP (1) EP1413640B1 (en)
JP (2) JP4197492B2 (en)
KR (1) KR20040007764A (en)
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DE (1) DE60204323T2 (en)
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Publication number Priority date Publication date Assignee Title
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Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0478790A1 (en) * 1990-03-24 1992-04-08 Nisshin Steel Co., Ltd. Heat-resistant ferritic stainless steel excellent in low-temperature toughness, weldability and heat resistance
JPH06279950A (en) * 1993-03-26 1994-10-04 Nisshin Steel Co Ltd Ferritic stainless steel for exhaust gas passage constituting member and its production
JPH10204591A (en) * 1997-01-24 1998-08-04 Kawasaki Steel Corp Ferritic stainless steel for engine exhaust member, excellent in muffler corrosion resistance in weld zone as well as in heat resistance
JPH10204590A (en) * 1997-01-24 1998-08-04 Kawasaki Steel Corp Ferritic stainless steel for engine exhaust member, excellent in heat resistance, workability, and muffler corrosion resistance

Family Cites Families (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH08144021A (en) * 1994-11-18 1996-06-04 Sumitomo Metal Ind Ltd Production of ferritic stainless steel and cold rolled sheet therefrom

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0478790A1 (en) * 1990-03-24 1992-04-08 Nisshin Steel Co., Ltd. Heat-resistant ferritic stainless steel excellent in low-temperature toughness, weldability and heat resistance
JPH06279950A (en) * 1993-03-26 1994-10-04 Nisshin Steel Co Ltd Ferritic stainless steel for exhaust gas passage constituting member and its production
JPH10204591A (en) * 1997-01-24 1998-08-04 Kawasaki Steel Corp Ferritic stainless steel for engine exhaust member, excellent in muffler corrosion resistance in weld zone as well as in heat resistance
JPH10204590A (en) * 1997-01-24 1998-08-04 Kawasaki Steel Corp Ferritic stainless steel for engine exhaust member, excellent in heat resistance, workability, and muffler corrosion resistance

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of EP1413640A4 *

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US20110176954A1 (en) 2011-07-21
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KR20040007764A (en) 2004-01-24
CN1225566C (en) 2005-11-02
US20100119404A1 (en) 2010-05-13
JP2008297631A (en) 2008-12-11
US20090053093A1 (en) 2009-02-26
CN1524130A (en) 2004-08-25
EP1413640B1 (en) 2005-05-25

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