EP2412837B1 - Ferritisches edelstahlblech mit hervorragender wärmebeständigkeit und hervorragender verarbeitbarkeit - Google Patents

Ferritisches edelstahlblech mit hervorragender wärmebeständigkeit und hervorragender verarbeitbarkeit Download PDF

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EP2412837B1
EP2412837B1 EP10756261.3A EP10756261A EP2412837B1 EP 2412837 B1 EP2412837 B1 EP 2412837B1 EP 10756261 A EP10756261 A EP 10756261A EP 2412837 B1 EP2412837 B1 EP 2412837B1
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Prior art keywords
high temperature
steel
content
stainless steel
less
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English (en)
French (fr)
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EP2412837A4 (de
EP2412837B8 (de
EP2412837A1 (de
Inventor
Junichi Hamada
Norihiro Kanno
Akihiko Takahashi
Yoshiharu Inoue
Shinichi Teraoka
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Nippon Steel Stainless Steel Corp
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Nippon Steel and Sumikin Stainless Steel Corp
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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
    • C22C38/38—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
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C22C38/02—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/28—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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • 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
    • F01N13/00—Exhaust or silencing apparatus characterised by constructional features ; Exhaust or silencing apparatus, or parts thereof, having pertinent characteristics not provided for in, or of interest apart from, groups F01N1/00 - F01N5/00, F01N9/00, F01N11/00
    • F01N13/08—Other arrangements or adaptations of exhaust conduits
    • F01N13/10—Other arrangements or adaptations of exhaust conduits of exhaust manifolds
    • 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
    • F01N13/00—Exhaust or silencing apparatus characterised by constructional features ; Exhaust or silencing apparatus, or parts thereof, having pertinent characteristics not provided for in, or of interest apart from, groups F01N1/00 - F01N5/00, F01N9/00, F01N11/00
    • F01N13/16—Selection of particular materials

Definitions

  • the present invention relates to a ferritic stainless steel sheet excellent in heat resistance which is optimal for use in particular for an exhaust system member in which high temperature strength or oxidation resistance is required.
  • An exhaust manifold, front pipe, center pipe, or other exhaust system member of an automobile carries high temperature exhaust gas which is exhausted from the engine. For this reason, the material forming the exhaust system member requires oxidation resistance, high temperature strength, heat fatigue characteristics, and other various characteristics.
  • the exhaust gas temperature differs depending on the car model or engine structure, but usually is 600 to 800°C or so. A material which has an excellent high temperature strength and oxidation resistance in an environment of long term use in such a temperature region has been demanded.
  • austenitic stainless steel is excellent in heat resistance and workability.
  • austenitic stainless steel has a large coefficient of heat expansion, so when applied to a member like an exhaust manifold which is repeatedly subjected to heating and cooling, thermal fatigue failure easily occurs.
  • Ferritic stainless steel is smaller in coefficient of heat expansion compared with austenitic stainless steel, so is better in heat fatigue characteristics and scale peeling resistance. It does not contain Ni, so is also lower in material cost compared with austenitic stainless steel and is being generally used.
  • Ferritic stainless steel is lower than high temperature strength compared with austenitic stainless steel. For this reason, the art of improving the high temperature strength has been developed. For example, there are SUS430J1 (Nb steel), Nb-Si steel, and SUS444 (Nb-Mo steel). In each case, Nb is added. These use solution strengthening or precipitation strengthening by Nb for raising the high temperature strength.
  • Stainless steel becomes harder due to the addition of Nb, so after hot rolling, it is necessary to anneal the hot rolled sheet to soften it, then cold roll it.
  • the product sheet In Nb steel, the product sheet easily becomes harder and easily falls in elongation and, furthermore, the r-value, an indicator of deep drawability, is low. This is because due to the presence of the solute Nb and precipitated Nb, the hardening at ordinary temperature and growth of the recrystallized texture are suppressed. For this reason, the press formability when forming exhaust parts falls and the freedom of shape becomes smaller.
  • Nb steel is inferior in productivity, manufacturability, and workability of the steel sheet.
  • Nb is high in alloy cost, so addition of Nb also results in higher production costs.
  • PLT 1 discloses addition of 0.5% or less of Cu for improvement of the low temperature toughness. This is not addition of Cu from the viewpoint of heat resistance.
  • PLT 2 discloses the art for utilizing the action of steel in improving the corrosion resistance and weatherability. This is not addition of Cu from the viewpoint of heat resistance.
  • PLT's 3 to 6 discloses the art of precipitation hardening by Cu precipitates to improve the high temperature strength in a 600°C or 700 to 800°C temperature region.
  • these are all composite addition with Nb, are inferior in manufacturability and workability, and are high in cost.
  • the prior art for improvement of the high temperature strength by addition of Cu utilizes Cu precipitates.
  • Cu precipitates When Cu precipitates are exposed to a high temperature for a long time, aggregation and combination of the precipitates rapidly occur, so the precipitation strengthening ability remarkably falls.
  • PLT 6 discloses the art of using composite addition of Nb-Cu-B to cause precipitation of fine Cu. However, even with this method, composite precipitation with the Laves phases cannot be avoided. Further, it adds a fine amount of Mo, so the workability becomes inferior and the cost becomes high.
  • PLT's 7 to 9 disclose ferritic stainless steel excellent in high temperature characteristics. These all add B for improving the workability and do not disclose addition from the viewpoint of the heat resistance.
  • PLT 10 discloses a ferritic stainless steel, which has a composition containing, by weight, ⁇ 0.02% C, 0.01-1.00% Si, 0.01-1.00% Mn, 7.0-15.0% Cr, 0.02-0.25% Ti, 0.0002-0.01% B, and ⁇ 0.02% N.
  • PLT11 discloses a ferritic stainless steel sheet comprising (by mass): C: 0.01% or less, N: 0.02% or less, Si: 0.05-1%, Mn: 0.1-2%, Cr: 10-30%, Mo: 0.1-1%, Cu: 1-2%, Nb: 0.2-0.7%, Ti: 0.01-0.3% and B: 0.0002-0.0050%, with the remainder being Fe and unavoidable impurities.
  • the present invention has as its object the inexpensive provision of ferritic stainless steel excellent in heat resistance and workability which may be used in particular under a heat environment of a maximum temperature of the exhaust gas of 600 to 800°C.
  • the object is to improve the high temperature characteristics of ferritic stainless steel sheet by adding Cu in steel ingredients not including Nb and causing the fine dispersion of Cu precipitates.
  • the inventors focused on the use of composite addition of Ti-Cu-B and resultant increased fineness of precipitates.
  • the inventors investigated in detail the strength at 500°C to 800°C or so and the ordinary temperature ductility of steel to which no Nb is added (or a small amount is added) and obtained the following discoveries.
  • the Cu precipitates uniformly finely form and it becomes possible to utilize precipitation strengthening and suppress a drop in strength due to aging heat treatment. This is effective for the durable stability of parts such- as exhaust members which are repeatedly subjected to a heat cycle and are used over long periods of time.
  • the inventors caused the sole formation of fine Cu precipitates so as to obtain the effect of precipitation strengthening and suppressed the coarsening of Cu precipitates by using the art of fine precipitation where composite precipitation of the Laves phases and Cu does not occur so as to provide ferritic stainless steel sheet which is inexpensive and exhibits heat resistance.
  • the gist of the present invention is as follows:
  • ferritic stainless steel sheet excellent in high temperature strength and workability is obtained.
  • the ferritic stainless steel sheet of the present invention gives a large effect in environmental protection and lowering cost of parts upon application in particular to an exhaust system member of an automobile etc.
  • FIG. 1 is a view showing the 0.2% yield strength in a high temperature tensile test of invention steel and comparative steel.
  • the content of C causes deterioration of the formability and corrosion resistance and causes a drop in the high temperature strength, so the smaller the content, the better. For this reason, the content of C is made 0.02% or less, more preferably 0.009% or less.
  • the lower limit of the content of C is not particularly provided, but excessive reduction leads to an increase in the refining cost, so the content is preferably made 0.001% or more.
  • N like C, causes deterioration of the formability and corrosion resistance and causes a drop in the high temperature strength, so the smaller the content, the better.
  • the content of N is made 0.02% or less, more preferably 0.015% or less.
  • the lower limit of the content of N is not particularly provided, but excessive reduction leads to an increase in the refining cost, so the content is preferably made 0.003% or more.
  • Si is an element which is useful as a deoxidizing agent and an element which improves the high temperature strength and oxidation resistance.
  • the high temperature strength up to 800°C or so is improved along with an increase in the amount of Si.
  • the content of Si is made 0.2% or more.
  • the upper limit of the content of Si is made 1.0%.
  • the content of Si is 0.2 to 1.0%.
  • Mn is an element which is added as a deoxidizing agent and contributes to the rise in the high temperature strength in the medium temperature region of 600 to 800°C or so. Further, during long term use, it forms Mn-based oxides at the surface layer and thereby contributes to improvement of scale adhesion and suppression of abnormal oxidation. If the content of Mn is over 2%, the ordinary temperature ductility falls and, furthermore, MnS is formed and thereby the corrosion resistance falls, so the upper limit of content of Mn is made 2%. If considering the high temperature ductility and scale adhesion, the content of Mn is preferably 0.1 to 1.0%.
  • Cr is an element essential in the present invention for securing oxidation resistance and corrosion resistance. If the content of Cr is less than 10%, that effect cannot be obtained. If the content of Cr is over 20%, a drop in workability and deterioration of the toughness are caused. For this reason, the content of Cr is made 10 to 20%. If considering the manufacturability and the high temperature ductility, 10 to 18% is preferable.
  • Cu in particular is an element which is effective for improvement of the high temperature strength in the medium temperature region of 600 to 800°C or so. This is due to the precipitation strengthening due to the Cu precipitates in the medium temperature region.
  • FIG. 1 shows the 0.2% yield strength in a high temperature tensile test of steels of the present invention (steel A, steel B, and steel C) and comparative steels (SUH409L and Nb-Si steel).
  • composition of ingredients of the steel A is 0.005%C-0.007%N-0.41%Si-0.45%Mn-10.5%Cr-1.25%Cu-0.15%Ti-0.0009%B.
  • composition of ingredients of the steel B is 0.006%C-0.009%N-0.88%Si-0.31%Mn-13.9%Cr-1.42%Cu-0.11%.Ti-0.0005%B.
  • composition of ingredients of the steel C is 0.004%C-0.011%N-0.11%Si-0.13%Mn-17.5%Cr-1.36%Cu-0.19%Ti-0.0004%B.
  • the comparative steels are steels which are used for general purposes.
  • composition of ingredients of the SUH409L is 0.005%C-0.007%N-0.35%Si-0.50%Mn-10.5%Cr-0.15%Ti.
  • composition of ingredients of the Nb-Si steel is 0.006%C-0.009%N-0.90%Si-0.35%Mn-13.8%Cr-0.45%Nb.
  • the high temperature tensile test was performed based on JISG0567 by running a tensile test in the rolling direction and measuring the 0.2% yield strength.
  • the steel of the present invention is high in strength in the 600°C or so temperature region and is particularly effective when used in an environment with a low exhaust gas temperature.
  • the steel of the present invention can be applied even in an environment less than 600°C.
  • a 600°C yield strength of 150 MPa or more and a 800°C yield strength of 30 MPa or more are made the required properties of the high temperature strength.
  • the content of Cu exceeds 3%, the ordinary temperature ductility and oxidation resistance deteriorate. Further, the edge cracking in the hot rolling process becomes remarkable and the manufacturability deteriorates. For this reason, the upper limit of the content of Cu is made 3%. If considering the manufacturability, scale adhesion, weldability, etc., the content of Cu is preferably 0.5 to 2.5%.
  • Ti is an element which bonds with C, N, and S and improves the corrosion resistance, grain boundary corrosion resistance, ordinary temperature ductility, and deep drawability. Further, by addition of a suitable quantity in composition addition with Cu, it gives rise to uniform formation of the Cu precipitates and improves the high temperature strength and heat fatigue characteristics.
  • the content of Ti is made 0.01% or more. If the content of Ti is over 0.5%, the amount of solute Ti increases, the ordinary temperature ductility falls, further, coarse Ti-based precipitates are formed and become starting points of cracking at the time of hole enlargement, and the press formability deteriorates. Furthermore, the oxidation resistance deteriorates. For this reason, the content of Ti is made 0.5% or less. If considering the formation of surface flaws or toughness, the content of Ti is preferably 0.05 to 0.3%.
  • B is an element which improves the secondary workability at the time of press-forming a product.
  • Cu precipitates finely form and the high temperature strength is improved.
  • Cu precipitates usually form extremely finely at the initial stage of precipitation.
  • the effect of improvement of strength is large, but coarsening occurs due to aging heat treatment and the strength greatly falls after aging.
  • coarsening of the Cu precipitates is suppressed and the stability of strength becomes higher at the time of use.
  • the content of B is made 0.0002% or more. If the content of B is over 0.0030%, the steel hardens, the grain boundary corrosion and oxidation resistance deteriorate, and, furthermore, weld cracking easily occurs. For this reason, the content of B is made 0.0002 to 0.0015%. If considering the corrosion resistance and production costs, 0.0003 to 0.0015% is preferable.
  • Nb, Mo, Al, V, and Zr may be added.
  • Nb may be added in accordance with need so as to improve the high temperature strength or heat fatigue characteristics. If the content of Nb is less than 0.01%, the effect of addition cannot be obtained. If adding Nb, formation of Laves phases occurs and the effect of precipitation of Cu on precipitation strengthening is suppressed, so addition of a large amount is not preferred. Further, the workability is inhibited and the elongation at break at ordinary temperature deteriorates. Therefore, the upper limit of the content of Nb is made 0.3%. From the viewpoint of productivity and manufacturability, the content of Nb is preferably 0.01 to 0.2%.
  • Mo is an element which further improves the high temperature strength and heat fatigue characteristics. If the content of Mo is less than 0.01%, the effect of addition cannot be obtained. If adding Mo, formation of the Laves phases occurs, the effect of precipitation of Cu on precipitation strengthening is suppressed, and, further, the ordinary temperature ductility falls, so addition of a large amount is not preferred. For this reason, the content of Mo is made 0.3% or less. The more preferable content of Mo is 0.01% to 0.2%.
  • Al is an element which is added in accordance with need as a deoxidizing element or for improving the oxidation resistance. Furthermore, it is useful for improving the strength at 600 to 700°C as a solution strengthening element. To stably obtain this effect, the content of Al is preferably made 0.01% or more. If excessively adding Al, the steel hardens, uniform elongation remarkably falls, and, furthermore, the toughness remarkably falls. For this reason, the upper limit of the content of Al is made 2.5%. If considering the occurrence of surface flaws and weldability and manufacturability, the content of Al is preferably 0.01 to 2.0%.
  • V forms fine carbonitrides and contributes to the improvement of the high temperature strength by the precipitation strengthening action, so is an element which is added in accordance with need:
  • the content of V is preferably made 0.01% or more. If the content of V is over 1%, the precipitates coarsen, the high temperature strength falls, and the heat fatigue life falls. For this reason, the upper limit of content of V is made 1%. If considering the production cost and manufacturability, the content of V is preferably 0.08 to 0.5%.
  • Zr is carbonitride-forming element. It contributes to the improvement of the high temperature strength and improvement of the oxidation resistance by the increase of the amounts of solute Ti and Nb. To stably obtain this effect, the content of Zr is preferably made 0.2% or more. If the content of Zr is over 1%, the manufacturability remarkably deteriorates. For this reason, the upper limit of the content of Zr is made 1%. If considering the cost and surface quality, 0.2 to 0.6% is preferable.
  • Sn is an element which is large in atomic radius and which is effective for solution strengthening. It does not cause major deterioration of the mechanical properties at ordinary temperature, so is an element which is added according to need. To stably obtain this effect, the content of Sn is preferably made 0.1% or more. If the content of Sn is over 1%, the manufacturability and the weldability remarkably deteriorate. For this reason, the upper limit of the content of Sn is made 1%. If considering the oxidation resistance etc., the content of Sn is preferably 0.2 to 0.5%.
  • the steel of the present invention either does not have any Nb and Mo added or contains them in low concentrations and thereby secures high temperature strength. As a result, it is possible to realize improvement of the ordinary temperature elongation.
  • the process of production of the steel sheet of the present invention is comprised of the steps of steelmaking, hot rolling, pickling, cold rolling, annealing, and pickling.
  • the method of smelting steel containing the above essential ingredients and ingredients which are added in accordance with need in a converter, then performing secondary refining is preferable.
  • the smelted molten steel is made into a slab by continuous casting or another known casting method.
  • the slab is heated to a predetermined temperature and is hot rolled to a predetermined sheet thickness by continuous rolling.
  • the cold rolling of stainless steel sheet is usually reverse rolling by a Sendimir rolling mill with a roll diameter of 60 to 100 mm or so or one-directional rolling by a tandem rolling mill with a roll diameter of 400 mm or more. In each case, the slab is rolled by several passes.
  • the slab is preferably cold rolled by a tandem rolling mill with roll diameters of 400 mm or more. If the roll diameters are 100 mm or less, a large amount of shear strain is introduced near the surface layer at the time of cold rolling, ⁇ 111> and ⁇ 554> crystal orientation growth is suppressed at the time of recrystallization annealing, and improvement of the r-value becomes difficult.
  • shear strain is suppressed, the above crystal orientation remarkably grows, and improvement of the r-value is contributed to.
  • Tandem rolling is one-directional rolling and has fewer rolling passes compared with Sendimir rolling, so is also better in productivity. If the reduction rate in the cold rolling process is low, after annealing, a recrystallized microstructure will not be obtained or excessive grain coarsening will occur causing degraded mechanical properties, so the reduction rate at the cold rolling process is preferably 30% or more.
  • the other steps of the method of production are not particularly limited.
  • the hot rolling conditions, hot rolled sheet thickness, cold rolled sheet annealing temperature, atmosphere, etc. may be suitably selected. It is also possible to impart temper rolling and a tension leveler after cold rolling and annealing. Furthermore, the product sheet thickness may also be selected in accordance with the required member thickness.
  • the steel of the present invention has no Nb added or is low in Nb content, so the annealing temperature after cold rolling is made a low temperature of 850 to 970°C. Due to this, the high temperature yield strength is improved compared to when the annealing temperature is over 970°C.
  • a rolling mill having large sized rolls (diameter 450 mm) was used for one-directional multipass rolling.
  • a rolling mill having small sized rolls was used for reverse type multipass rolling.
  • the annealing temperature of the cold rolled sheet was made 850 to 970°C so as to make the crystal grain size number 6 to 8 or so.
  • the annealing temperature of the cold rolled sheet was made 1000 to 1050°C.
  • Nos. 1 to 17 and 37 are invention steels, while Nos. 18 to 36 are comparative steels.
  • Comparative Steel No. 18 is SUH409L, while Nos. 19 and 20 are steels with goods records of use as Nb-Si steels.
  • test pieces for high temperature tensile tests were obtained, tensile tests were run at 600°C and 800°C, and the 0.2% yield strength was measured (based on JISG0567). The tensile tests which gave a 600°C yield strength of 150 MPa or more and a 800°C yield strength of 30 MPa or more were judged passing.
  • a JIS No. 13B test piece was prepared and a tensile test was performed in a direction parallel to the rolling direction and the elongation at break measured. If the elongation at break at ordinary temperature is 35% or more, working into complicated parts becomes possible, so an elongation at break of 35% or more was judged passing.
  • the average r-value was calculated by obtaining a JIS No. 13B tensile test piece, giving 15% strain in the rolling direction, direction 45° from the rolling direction, and direction 90° from the rolling direction, then using formula (1) and formula (2).
  • r ln W 0 / W ln t 0 / t where, W 0 is the sheet width before tension, W is the sheet width after tension, t 0 is the sheet thickness before tension, and "t" is the sheet thickness after tension.
  • Average r-value r 0 + 2 r 45 + r 90 / 4
  • r 0 is the r-value in the rolling direction
  • r 45 is the r-value in the direction 45° from the rolling direction
  • r 90 is the r-value in the direction 90° from the rolling direction. If the average r-value is 1.3 or more, working into complicated parts becomes possible, so an average r-value of 1.3 or more is preferable.
  • Comparative Steel Nos. 18, 19, and 20 are existing steels, but have high temperature strengths lower than the requested values. Comparative Steel Nos. 19 and 20 to which Nb is added in excess also have low r-values.
  • Nos. 21 and 22 have C and N which are over the upper limits and are inferior in high temperature strength, oxidation resistance, and workability.
  • No. 23 has excessively added Si and is inferior in workability.
  • No. 24 has excessively added Mn and is inferior in oxidation resistance and workability.
  • No. 25 has a small amount of Cr, so is low in high temperature strength and is also inferior in oxidation resistance.
  • No. 26 has a small amount of Cu, so is low in 0.2% yield strengths at 600°C and 800°C.
  • No. 27 has an amount of Ti which is over the upper limit, so is inferior in oxidation resistance and workability.
  • No. 28 has an amount of Ti which is less than the lower limit and has excessively added Nb, so is low in ductility.
  • No. 29 has excessively added Nb, so is low in ductility and r-value.
  • No. 30 has B which is over the upper limit, so is low in oxidation resistance and workability.
  • No. 31 has an amount of addition of B of 0.0001% or less than the lower limit, so at 800°C the Cu precipitate coarsens, the effect of the precipitation strengthening falls, and the yield strength is low.
  • Nos. 32 to 36 has Mo, Al, V, Zr, and Sn which are over the upper limit, the ordinary temperature ductility is low, and working into a part is hindered.
  • Nos. 1 to 17 which use large sized rolls for cold rolling exhibited average r-values of 1.3 or more, that is, good values.
  • the Invention Steel No. 37 is excellent in high temperature yield strength and ordinary temperature elongation at break. However, the cold rolling roll size is small, so the r-value is a value lower than the preferable range.
  • the present invention it is possible to provide a stainless steel sheet excellent in high temperature characteristics and workability without addition of large amounts of expensive alloy elements such as Nb and Mo.
  • this for an exhaust member the reduction of the parts costs, reduction of weight, and resultant contributions to environment protection and social contributions are remarkably great.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Combustion & Propulsion (AREA)
  • General Engineering & Computer Science (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Claims (2)

  1. Ferritisches Edelstahlblech mit hervorragender Wärmebeständigkeit und Bearbeitbarkeit, das in Masse-% enthält,
    C: 0,02% oder weniger,
    N: 0,02% oder weniger,
    Si: 0,2 bis 1,0%,
    Mn: 2% oder weniger,
    Cr: 10 bis 20%,
    Cu: 0,4 bis 3%,
    Ti: 0,01 bis 0,5%,
    B: 0,0002 bis 0,0015%,
    gegebenenfalls einen oder mehrere aus
    Nb: 0,01 bis 0,3%,
    Mo: 0,01 bis 0,3%,
    Al: 2,5% oder weniger,
    V: 1% oder weniger,
    Zr: 1% oder weniger und
    Sn: 1% oder weniger, und
    einen Rest von Fe und unvermeidbaren Verunreinigungen, wobei die Gesamtmenge von Nb und Mo weniger als 0,2% beträgt.
  2. Das Verfahren zur Herstellung des ferritischen Edelstahlblechs, das eine hervorragende Wärmebeständigkeit und Bearbeitbarkeit aufweist, gekennzeichnet durch das Warmwalzen des ferritischen Edelstahls, das eine Zusammensetzung von Bestandteilen gemäß Anspruch 1 aufweist, um ein warmgewalztes Blech zu erhalten, dann das Weglassen des Glühens des warmgewalzten Blechs, das Beizen des warmgewalzten Blechs, das Kaltwalzen mittels Walzen mit einem Durchmesser von 400 mm oder mehr, dann das Durchführen des Endglühens bei 850 bis 970°C.
EP10756261.3A 2009-03-24 2010-03-23 Ferritisches edelstahlblech mit hervorragender wärmebeständigkeit und hervorragender bearbeitbarkeit Active EP2412837B8 (de)

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JP2009072320 2009-03-24
JP2010055944A JP5546911B2 (ja) 2009-03-24 2010-03-12 耐熱性と加工性に優れたフェライト系ステンレス鋼板
PCT/JP2010/055488 WO2010110466A1 (ja) 2009-03-24 2010-03-23 耐熱性と加工性に優れたフェライト系ステンレス鋼板

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KR20110120352A (ko) 2011-11-03
CN102361999A (zh) 2012-02-22
EP2412837A4 (de) 2014-04-09
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EP2412837B8 (de) 2020-04-29
EP2412837A1 (de) 2012-02-01
JP5546911B2 (ja) 2014-07-09

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