US20140023550A1 - Ferritic stainless steel sheet excellent in heat resistance and workability and method of production of same - Google Patents

Ferritic stainless steel sheet excellent in heat resistance and workability and method of production of same Download PDF

Info

Publication number
US20140023550A1
US20140023550A1 US14/008,406 US201214008406A US2014023550A1 US 20140023550 A1 US20140023550 A1 US 20140023550A1 US 201214008406 A US201214008406 A US 201214008406A US 2014023550 A1 US2014023550 A1 US 2014023550A1
Authority
US
United States
Prior art keywords
steel sheet
stainless steel
ferritic stainless
workability
high temperature
Prior art date
Legal status (The legal status 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 status listed.)
Abandoned
Application number
US14/008,406
Other languages
English (en)
Inventor
Junichi Hamada
Norihiro Kanno
Yoshiharu Inoue
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Nippon Steel Stainless Steel Corp
Original Assignee
Individual
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 Individual filed Critical Individual
Assigned to NIPPON STEEL & SUMIKIN STAINLESS STEEL CORPORATION reassignment NIPPON STEEL & SUMIKIN STAINLESS STEEL CORPORATION ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: HAMADA, JUNICHI, INOUE, YOSHIHARU, KANNO, NORIHIRO
Publication of US20140023550A1 publication Critical patent/US20140023550A1/en
Abandoned legal-status Critical Current

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B21B1/24—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process
    • B21B1/26—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process by hot-rolling, e.g. Steckel hot mill
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing
    • 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
    • C22C38/004—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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/28—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
    • C22C38/40—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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • 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
    • F01N13/08—Other arrangements or adaptations of exhaust conduits
    • F01N13/10—Other arrangements or adaptations of exhaust conduits of exhaust manifolds
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01N—GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR MACHINES OR ENGINES IN GENERAL; GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR INTERNAL COMBUSTION ENGINES
    • F01N2530/00—Selection of materials for tubes, chambers or housings
    • F01N2530/02—Corrosion resistive metals
    • F01N2530/04—Steel alloys, e.g. stainless steel

Definitions

  • the present invention relates to ferritic stainless steel sheet excellent in heat resistance which is optimal for use for an exhaust system member etc. which requires high temperature strength and oxidation resistance and a method of production of the same.
  • Exhaust manifolds, front pipes, center pipes, and other exhaust system members of automobiles carry high temperature exhaust gas which is exhausted from the engine, so the materials forming the exhaust members are required to offer oxidation resistance, high temperature strength, heat fatigue characteristics, and diverse other characteristics.
  • austenitic stainless steel is excellent in heat resistance and workability, but it has a large heat expansion coefficient, so if used for members which are repeatedly heated and cooled such as exhaust manifolds, heat fatigue fracture easily occurs.
  • ferritic stainless steel has a smaller heat expansion coefficient compared with austenitic stainless steel, so is excellent in heat fatigue characteristics and scale spalling resistance. Further, it does not contain Ni, so compared with austenitic stainless steel, the cost of material is low. Therefore, this is being used for general applications.
  • ferritic stainless steel is lower in high temperature strength compared with austenitic stainless steel, so art for improving the high temperature strength has been developed. For example, there are SUS430J1 (Nb steel), Nb—Si steel, and SUS444 (Nb—Mo steel) of the Japan Industrial Standard (JIS). These all are predicated on addition of Nb. This uses solution strengthening or precipitation strengthening by Nb so as to raise the high temperature strength.
  • PLTs 1 to 4 disclose the art of composite addition of Cu or Cu—V.
  • PLT 1 to improve low temperature toughness, addition of 0.5% or less of Cu is being studied. It is not addition from the viewpoint of heat resistance.
  • PLTs 2 to 4 disclose the art which utilizes precipitation strengthening by Cu precipitates to improve the high temperature strength in the 600° C. or 700 to 800° C. temperature range.
  • PLTs 1 to 2 and PLTs 5 to 7 disclose steel containing B as ferritic stainless steel excellent in high temperature characteristics.
  • PLTs 8 to 13 disclose arts relating to ferritic stainless steel containing W.
  • W is known as an element which improves the high temperature strength, but addition of W causes the workability (elongation) to worsen and gives rise to the problem of the difficulty of forming the parts and issues in terms of costs. Further, at a high temperature, it bonds with Fe and precipitates as the later explained Laves phases, so there was the issue that when the Laves phases coarsened, it was not possible to effectively improve the heat resistance.
  • PLTs 14 and 15 disclose to define the sum of the Mo and W added, that is, Mo+W, to secure the high temperature strength of the ferritic stainless steel, but again concern over coarsening of the Laves phases was unavoidable. That is, when, like with exhaust manifolds, being subjected to thermal cycles along with starting and stopping of the engine, at the stage of long term use, the high temperature strength would fall and there would be the danger of heat fatigue breakage. That is, in existing materials, even if the high temperature strength is excellent, there was a concern that with long term use, coarsening of the Laves phases and ⁇ -Cu and other precipitates would cause deterioration of the heat fatigue characteristics.
  • PLT 16 describes that inclusion of P causes FeTiP to precipitate which has a detrimental effect, so the content of P has to be kept low.
  • PLT 17 prescribes that in ferritic stainless steel, P is useful for increasing the high temperature strength (solution strengthening) and prescribes that P be included up to 0.1 wt %, but examples including high P contents are not disclosed.
  • the present invention provides ferritic stainless steel which is used in a hot environment of a maximum temperature of exhaust gas of 950° C. and which is excellent heat resistance and workability.
  • the present invention has as its object to solve the above problem by balancing the various dissolved elements including P and dispersing the various precipitates so as to improve the high temperature characteristics and providing ferritic stainless steel sheet for exhaust manifold use which is excellent in ordinary temperature workability. That is, the present invention provides new ferritic stainless steel sheet which is balanced in precipitate refinement and solution strengthening and a method of production of the same.
  • intermetallic compounds called “Laves phases” formed by composite addition of Nb, Mo, and W and ⁇ -Cu which is formed by addition of Cu are actively utilized for high temperature precipitation strengthening.
  • the precipitates coarsen, so the precipitation strengthening ability only acts for an extremely short time.
  • the steel material is not improved in heat fatigue life and ends up breaking in a short time. Therefore, the inventors discovered that by utilizing compounds of Fe and P as precipitation sites, the above-mentioned Laves phases and ⁇ -Cu uniformly finely precipitate in the grains and as a result the precipitation strengthening becomes stable for a long period of time and the heat fatigue life is improved.
  • the inventors discovered that by utilizing solution strengthening by the dissolved Nb, Mo, and W, the high temperature characteristics are improved much more.
  • the inventors discovered that by defining Mo+W and the amount of addition of Cu as predetermined ranges, it is possible to improve both the heat fatigue life and the ordinary temperature ductility. Due to this, it was made possible to provide highly reliable ferritic stainless steel sheet which has a high heat resistance and freedom of working of parts at a temperature region of exhaust gas with a maximum temperature of 950° C. Note that, Mo+W is the sum, by mass %, of the amount of addition of Mo and the amount of addition of W.
  • the gist of the present invention is as follows:
  • Ferritic stainless steel sheet excellent in heat resistance and workability characterized by containing, by mass %, C: 0.02% or less, N: 0.02% or less, Si: over 0.1 to 1.0%, Mn: 0.5% or less, P: 0.02 to 0.10%, Cr: 13.0 to 20.0%, Nb: 0.5 to 1.0%, Cu: 1.0 to 3.0%, Mo: 1.5 to 3.5%, W: 2.0% or less, B: 0.0001 to 0.0010%, and Al: 0.01 to 1.0% and having a balance of Fe and unavoidable impurities, where Mo+W is 2.0 to 3.5%.
  • Ferritic stainless steel sheet excellent in heat resistance and workability of (1) characterized by further containing, by mass %, one or more of Ti: 0.05 to 0.4%, V: 0.05 to 1.0%, Zr: 0.05 to 1.0%, Sn: 0.05 to 0.5%, and Ni: 0.05 to 1.0%.
  • a method of production of ferritic stainless steel sheet excellent in heat resistance and workability characterized by producing ferritic stainless steel sheet as set forth in the above (1) or (2) during which water cooling a steel sheet within one hour after hot rolling and coiling and cold rolling and annealing the cold rolled steel sheet while omitting annealing of hot rolled steel sheet.
  • cases where no lower limit is defined means inclusion up to the level of unavoidable impurities.
  • ferritic stainless steel sheet excellent in heat resistance and workability is obtained which is suitable for exhaust system parts which are exposed to an atmosphere of 950° C. for which use of ferritic stainless steel sheet had been difficult in the past.
  • FIG. 1 is a view which shows the effects of Mo+W on the heat fatigue characteristics in the case of a maximum temperature of 950° C.
  • FIG. 2 is a view which shows the effects of Mo+W on the elongation at break at ordinary temperature.
  • FIG. 3 is a view which shows the effects of Mo+W on the oxidation resistance in a continuous oxidation test at 950° C.
  • 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. Accordingly, the content of C is made 0.02% or less. However, excessive reduction leads to an increase in the refining costs, so 0.002 to 0.009% is preferable.
  • N in the same way as C, degrades the formability and corrosion resistance and causes a drop in the high temperature strength, so the smaller the content, the better. Accordingly, the amount of N is made 0.02% or less. However, excessive reduction leads to an increase in the refining costs, so 0.003 to 0.015% is preferable.
  • Si is an element useful as a deoxidizing agent and is an element which improves the high temperature strength and the oxidation resistance.
  • the high temperature strength and the oxidation resistance are improved along with the increase in the amount of Si.
  • the effect is manifested at over 0.1%. In particular, this effect becomes remarkable when compositely adding Mo and W.
  • the upper limit is made 1.0%. Further, if considering the manufacturability, 0.2 to 0.5% is preferable.
  • Mn is an element which is added as a deoxidizing agent and contributes to the rise in high temperature strength in the 600 to 800° C. or so temperature region (medium temperature region).
  • Mn-based oxide surface layer at high temperatures and easily causes scale adhesion or abnormal oxidation.
  • the upper limit was made 0.5% or less. Further, if considering the pickling ability at the time of production of steel sheet and the ordinary temperature ductility, 0.05 to 0.2% is preferable.
  • P controls the precipitation of the Laves phases and ⁇ -Cu, so is an important element. Usually, it is considered that P should be reduced as much as possible from the viewpoint of the workability.
  • compounds of Fe and P are formed and these compounds are used as nuclei for fine dispersion and precipitation of Laves phases and ⁇ -Cu at 950° C. Even if held at a high temperature for a long period of time, coarsening of these precipitates is prevented. If the Laves phases and ⁇ -Cu independently precipitate in the ferrite grains and at the grain boundaries in the matrix, they will coarsen early and the precipitation strengthening ability will fall. In addition, in the process of heat fatigue, they will form starting points of cracks and will end up accelerating crack propagation.
  • the refining of the precipitates by P is manifested from 0.02%, so the lower limit of P was made 0.02%. Further, by addition of over 0.10%, the ordinary temperature ductility dropped sharply, so the upper limit was made 0.10%. Further, if considering the pickling ability at the time of production of steel sheet, 0.028 to 0.080% is preferable.
  • Cr is an element which is essential for securing oxidation resistance and corrosion resistance. If less than 13%, the oxidation resistance cannot be secured, while if over 20%, a drop in workability and deterioration of the toughness are caused, so the content was made 13 to 20%. Further, if considering the manufacturability and high temperature ductility, 16 to 18% is preferable.
  • Nb is an element necessary for improving the high temperature strength by solution strengthening and precipitate refining strengthening. Further, it also has the role of fixing the C and N as carbonitrides and contributing to the growth of a recrystallized structure having an effect on the corrosion resistance and r value of the product sheet.
  • the strength at 950° C. is mainly solution strengthening, but when compositely adding Mo and W, they also have the effect of contributing to fine precipitation of Laves phases and promoting formation of compounds of Fe and P acting as sites for precipitation of Laves phases. This is believed to be because FeNbP precipitates in the grains at the product stage which serve as nuclei for fine precipitation of the Laves phases and suppresses coarsening of the Laves phases.
  • Fine Laves phases are effective for improvement of the high temperature strength and heat fatigue life.
  • the effects are manifested with addition of 0.5% or more.
  • excessive addition causes a drop in uniform elongation, so the content was made 0.5 to 1.0%.
  • 0.5 to 0.6% is preferable.
  • Cu contributes to precipitation strengthening by precipitation of ⁇ -Cu, but to secure the amount of precipitation which contributes to high temperature strength at 950° C., addition of 1.0% or more is necessary, so the lower limit was made 1.0%.
  • ⁇ -Cu precipitates as explained above, interact with Fe—P-based precipitates and finely disperse with each other. This point is greatly different from PLT 16.
  • Cu is an element which remarkably lowers the ordinary temperature ductility. If adding over 3.0%, the total elongation of the steel sheet does not reach the 30% required for ordinary press-forming, so the upper limit was made 3.0%. Furthermore, if considering the manufacturability and oxidation resistance, 1.2 to 2.0% is preferable.
  • Mo is an element which is effective for solution strengthening at 950° C. and forms Laves phases (Fe 2 Mo) to give rise to a precipitation strengthening action. These effects are manifested at 1.5% or more, but excessive addition raises the alloy cost. With addition of over 3.5%, the ordinary temperature ductility and the oxidation resistance are remarkably degraded, so the content was made 1.5 to 3.5%. Furthermore, if considering the manufacturability, 1.5 to 2.7% is preferable.
  • W is an element which is effective for solution strengthening at 950° C. and forms Laves phases (Fe 2 W) to give rise to a precipitation strengthening action.
  • Laves phases of Fe 2 (Nb,Mo,W) precipitate, but if adding W, coarsening of the Laves phases is suppressed and the precipitation strengthening ability is improved.
  • the reason is believed to be dispersion of W and the interaction between the FeP compounds which form precipitation sites for Fe 2 (Nb,Mo,W) and W.
  • these Laves phases tend to become finer.
  • the three Cu precipitates, Laves phases, and Fe—P-based precipitates affect each other and finely disperse and precipitate whereby coarsening is inhibited and improvement of the high temperature fatigue characteristics is contributed to. That is, the composite addition of Mo, W, and P is also a great difference from PLT 16.
  • FIG. 1 shows the influence of the addition of Mo and W on the heat fatigue life of a steel material which has a chemical composition of 17.3% Cr-0.005% C-0.010% N-0.03% P-0.55% Nb-1.5% Cu-0.0004% B-0.03% Al.
  • the heat fatigue life was measured using a welded pipe of ⁇ 38.1 ⁇ 2 mm thickness which was prepared from 2 mm thick steel sheet as a test piece. The test conditions were made a constraining rate (ratio of amount of deformation to free heat expansion) held at 20% while giving a thermal cycle (minimum temperature 200° C., maximum temperature 950° C., holding time at maximum temperature 2 minutes). Further, the number of cycles when the cracks passed through the test piece was measured. In this test, the life was illustrated assuming 2000 cycles or more as passing (in figure, o) and less than 2000 cycles as failing (in figure, x).
  • FIG. 2 shows the influence of the addition of Mo and W on the total elongation at ordinary temperature of the same system of chemical compositions.
  • the elongation at break has to be 30% or more. Therefore, the case giving an elongation at break of 30% or more was shown as “o” and the case of less than 30% was shown as “x”.
  • FIG. 3 shows the effects of the addition of Mo and W on the oxidation resistance at 950° C. for the same system of chemical compositions. The case where no abnormal oxidation and scale spalling occurred was shown as “o”, while the case where they occurred was shown as “x”.
  • B is an element which improves the secondary workability at the time of press-forming a product. Further, in the present invention, addition of B suppresses coarsening of the Cu precipitates, Laves phases, and FeP compounds and raises the stability of strength at the time of use in a high temperature environment. This is believed to be because the B segregates at the crystal grain boundaries at the time of recrystallization treatment in the cold rolled sheet annealing step whereby it becomes harder for the above precipitates which precipitate when exposed to a high temperature environment after that to precipitate at the crystal grain boundaries and fine precipitation in the grains is promoted. Due to this, long term stability of precipitation strengthening is expressed, the drop in strength is suppressed, and the heat fatigue life is improved.
  • Al is an element which is added as a deoxidizing element and also improves the oxidation resistance. Further, it is useful for improvement of strength at 600 to 700° C. as a solution strengthening element. Its action is stably expressed from 0.01%, but excessive addition causes the steel to harden, uniform elongation to be remarkably degraded, and, furthermore, the toughness to remarkably fall, so the upper limit was made 1.0%. If considering the occurrence of surface defects and the weldability and manufacturability, 0.01 to 0.2% is preferable.
  • Ti is an element which bonds with C, N, and S to improve the corrosion resistance, intergranular corrosion resistance, ordinary temperature ductility, and deep drawability and is added in accordance with need. These effects are manifested at 0.05% or more, but addition of over 0.4% causes the amount of dissolved Ti to increase and the ordinary temperature ductility to fall and further causes coarse Ti-based precipitates to form and act as starting points of cracking at the time of hole enlargement and thereby degrades the press formability. Further, the oxidation resistance is also degraded, so the amount of addition of Ti was made 0.4% or less. Furthermore, if considering the formation of surface flaws and the toughness, 0.05 to 0.2% is preferable.
  • V is an element which improves the corrosion resistance and is added in accordance with need. This effect is stably manifested by addition of 0.05% or more, but if adding over 1%, the precipitates coarsen and the high temperature strength falls and, in addition, the oxidation resistance deteriorates, so the upper limit was made 1%. Furthermore, if considering the manufacturing cost and manufacturability, 0.08 to 0.5% is preferable.
  • Zr is a carbonitride-forming element in the same way as Ti and Nb and is an element which improves the corrosion resistance and deep drawability, so is added in accordance with need. These effects are manifested at 0.05% or more, but adding over 1.0% causes the manufacturability to remarkably deteriorate, so the content was made 0.05 to 1.0%. Furthermore, if considering the cost and surface quality, 0.1 to 0.6% is preferable.
  • Sn is an element which improves the corrosion resistance. It improves the high temperature strength in the medium temperature region, so is added in accordance with need. These effects are manifested at 0.05% or more, but if adding over 0.5%, the manufacturability remarkably falls, so the content was made 0.05 to 0.5%. Furthermore, if considering the oxidation resistance and production costs, 0.1 to 0.5% is preferable.
  • Ni is an element which improves the oxidation resistance and toughness and is added in accordance with need. These effects are manifested at 0.05% or more, but if adding over 1.0%, the cost becomes high, so the content was made 0.05 to 1.0%. Furthermore, if considering the manufacturability, 0.1 to 0.5% is preferable.
  • the method of production of steel sheet of the present invention has the steps of steelmaking, hot rolling, pickling, cold rolling, annealing, and pickling.
  • steelmaking the method of melting steel which contains the above essential elements and optional elements which are added in accordance with need in a converter, then performing secondary refining is preferable.
  • the melted steel is made into a slab in accordance with a known casting method (continuous casting).
  • the slab is heated by an ordinary method to a predetermined temperature and is hot rolled to a predetermined sheet thickness by continuous rolling.
  • the hot rolling is performed by a hot rolling mill comprised of a plurality of stands, then the sheet is coiled.
  • the coil is water cooled after coiling.
  • the steel of the present invention has various alloy elements added to it, so the hot rolled sheet easily falls in toughness and the steel sheet sometimes breaks in the next step or other trouble occurs.
  • the causes coarsening of the crystal grains, formation of Cu clusters, and two-phase separation of Cr may be mentioned. Therefore, to reliably eliminate these causes, the coil is immersed as is into a pool for water cooling.
  • the time from coiling to water cooling is over 1 hour, there is no effect of improvement of the toughness, so the time from coiling to water cooling is made within 1 hour. This time is preferably within 20 minutes.
  • the coiling temperature is not particularly defined, but is preferably 400 to 750° C. from the viewpoint of refinement of the structure.
  • the hot rolled sheet is annealed by heating until the recrystallization temperature from the viewpoint of homogenizing and softening the structure.
  • the recrystallized structure becomes coarse in crystal grains, so sometimes the toughness of the hot rolled annealed sheet becomes an issue. Therefore, in the present invention, preferably, the annealing of the hot rolled sheet is omitted or heat treatment is performed at a temperature not causing recrystallization so as to refine the structure and thereby secure toughness.
  • the recrystallization temperature of the present invention is 1000° C. or more, but when obtaining a recrystallized structure, the crystal grains end up coarsening, the toughness falls, and the steel sheet sometimes breaks when running the coil.
  • the sheet is cold rolled while having nonuniformity of the structure, but in such a case as well, a regular grain structure is obtained after the annealing of the cold rolled sheet. Further, even if the cold rolled material is hard, cold rolling is possible. Finely worked grains can be obtained at the hot rolling stage, so the toughness is not a problem. Further, in the present invention, sub grains are formed, so it is possible to remove the working strain and obtain a sub grain structure to prevent a drop in toughness due to formation of deformed twin crystals. This effect is obtained by heat treatment at 700 to 950° C. in temperature region, so the hot rolled sheet annealing temperature is preferably 700 to 950° C.
  • the holding time and the cooling rate are not particularly prescribed, but from the viewpoint of productivity, the holding time is within 20 seconds and the cooling rate is preferably 10° C./sec or more.
  • the annealing after cold rolling was performed for obtaining a recrystallized structure.
  • the recrystallization temperature of the steel having the chemical composition of the present invention is 1000 to 1100° C., so the sheet was heated to this temperature range, then cooled.
  • Cu, Nb, Mo, and W form ⁇ -Cu and Laves phases in the cooling process, but if the cooling rate is slow, the ⁇ -Cu and Laves phases are sometimes made to excessively precipitate and a drop is caused in the high temperature strength and ordinary temperature ductility, so the solid solution state is preferably held as much as possible.
  • the cooling rate until 400° C. where a salt treatment or neutral salt electrolysis treatment is performed is preferably made 10° C./sec or more. If considering the productivity and the pickling ability, the cooling rate is preferably 20 to 100° C./sec. Further, as the cooling method, mist cooling, water cooling, etc. may be suitably selected.
  • the conditions of the other steps are not particularly defined, but the thickness of the hot rolled sheet, the annealing atmosphere of the cold rolled sheet, etc. may be suitably selected. Further, after cold rolling and annealing, at least one of temper rolling and a tension leveler may be applied. Furthermore, the thickness of the product sheet may be selected in accordance with the required thickness of the member.
  • the sheet was cooled by a cooling rate until 400° C. of 20 to 100° C./sec to obtain the product sheet. From the thus obtained product sheet, the above-mentioned methods were used to run heat fatigue tests and measure the ordinary temperature elongation at break and continuous oxidation test. The results were judged in the same way as FIGS. 1 to 3 .
  • Table 1 for “good” and “poor”, judgment criteria similar to those of FIGS. 1 to 3 are shown for “o” and “x”. Namely, “good” is corresponding to “o”, and “poor” is corresponding to “x”. Note that the crystal grain size numbers are the austenite crystal granularity defined in JIS G 0551.
  • Nb is off from the lower limit, so the high temperature strength is insufficient and the heat fatigue life is short.
  • Nb is off from the upper limit, so the Laves phases coarsely precipitate and therefore the heat fatigue characteristics and workability are inferior.
  • Cu is off from the lower limit, so the high temperature strength is insufficient and the heat fatigue life is short.
  • Cu is excessively added.
  • the heat fatigue characteristics are good, but the ordinary temperature ductility and oxidation resistance are inferior.
  • Mo is off from the lower limit, so the high temperature strength is insufficient and the heat fatigue life is short and the oxidation resistance is also inferior.
  • Mo is excessively added, so the workability and oxidation resistance are inferior.
  • W is off from the upper limit, so the elongation is insufficient and the oxidation resistance is also inferior.
  • B is off from the upper limit, so all characteristics are inferior.
  • Al and Ti are off from the upper limit, so the workability is inferior.
  • V and Sn are off from the upper limit, so the workability and oxidation resistance are inferior.
  • Zr and Ni are off from the upper limit, so the workability is inferior.
  • Steel Nos. 1 to 6 were produced by changing the time after coiling in hot rolling until water cooling of the coil, the hot rolled sheet annealing temperature, and the cooling rate until 400° C. at the time of annealing the cold rolled sheet.
  • the hot rolled sheet or hot rolled sheet toughness was evaluated and the cold rolled annealed sheet was measured for ordinary temperature elongation.
  • the heating temperature in the hot rolling was made 1250° C.
  • the finishing temperature was made 900° C.
  • the time after coiling to water cooling of the coil was changed in the range of 400 to 750° C.
  • the annealing temperature of the hot rolled sheet was changed, then the sheet was cold rolled to a 2 mm thickness and the cold rolled sheet was annealed. At this time, at the time of cooling, the cooling rate was changed from the maximum temperature to 400° C.
  • the hot rolled sheet or the hot rolled annealed sheet was evaluated for toughness by preparing a V-notch Charpy test piece notched in the width direction, running a Charpy impact test at ordinary temperature, judging the case where an impact value or 20 J/cm 2 or more as passing (in figure, A), and judging the case where it less than this as somewhat unpreferable (in figure, B). Further, the ordinary temperature elongation of the cold rolled annealed sheet was evaluated by the above-mentioned method. The results are shown in Table 2, Nos. 41 to 50.
  • the present invention it is possible to provide ferritic stainless steel sheet excellent in heat resistance and workability which is suitable for exhaust gas system parts which are exposed to an atmosphere of 950° C. Therefore, the present invention is useful for environmental measures, reducing the cost of exhaust gas system parts, etc. and is therefore industrially useful.

Landscapes

  • 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)
US14/008,406 2011-03-29 2012-03-28 Ferritic stainless steel sheet excellent in heat resistance and workability and method of production of same Abandoned US20140023550A1 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
JP2011-072270 2011-03-29
JP2011072270A JP5659061B2 (ja) 2011-03-29 2011-03-29 耐熱性と加工性に優れたフェライト系ステンレス鋼板及びその製造方法
PCT/JP2012/058218 WO2012133573A1 (ja) 2011-03-29 2012-03-28 耐熱性と加工性に優れたフェライト系ステンレス鋼板及びその製造方法

Publications (1)

Publication Number Publication Date
US20140023550A1 true US20140023550A1 (en) 2014-01-23

Family

ID=46931280

Family Applications (1)

Application Number Title Priority Date Filing Date
US14/008,406 Abandoned US20140023550A1 (en) 2011-03-29 2012-03-28 Ferritic stainless steel sheet excellent in heat resistance and workability and method of production of same

Country Status (6)

Country Link
US (1) US20140023550A1 (ko)
EP (1) EP2692889B1 (ko)
JP (1) JP5659061B2 (ko)
KR (1) KR101557463B1 (ko)
CN (1) CN103459639A (ko)
WO (1) WO2012133573A1 (ko)

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3103889A4 (en) * 2014-02-05 2017-03-08 JFE Steel Corporation Hot-rolled and annealed ferritic stainless steel sheet, method for producing same, and cold-rolled and annealed ferritic stainless steel sheet
US9885099B2 (en) 2012-03-09 2018-02-06 Nippon Steel & Sumikin Stainless Steel Corporation Ferritic stainless steel sheet
US10358689B2 (en) 2013-02-04 2019-07-23 Nippon Steel & Sumikin Stainless Steel Corporation Method of producing ferritic stainless steel sheet
US10385429B2 (en) 2013-03-27 2019-08-20 Nippon Steel & Sumikin Stainless Steel Corporation Hot-rolled ferritic stainless-steel plate, process for producing same, and steel strip
US10450623B2 (en) 2013-03-06 2019-10-22 Nippon Steel & Sumikin Stainless Steel Corporation Ferritic stainless steel sheet having excellent heat resistance
EP3795711A4 (en) * 2018-06-26 2021-03-24 Posco STAINLESS FERRITIC STAINLESS STEEL WITH EXCELLENT DAMPING CAPACITY AND PROCESS FOR ITS MANUFACTURING
US10975459B2 (en) 2015-09-29 2021-04-13 Jfe Steel Corporation Ferritic stainless steel
US11242578B2 (en) 2017-03-30 2022-02-08 Nippon Steel Stainless Steel Corporation Ferrite-based stainless steel sheet having low specific gravity and production method therefor

Families Citing this family (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN104769144B (zh) * 2012-10-30 2017-10-10 新日铁住金不锈钢株式会社 耐热性优良的铁素体系不锈钢板
JP6093210B2 (ja) * 2013-03-13 2017-03-08 新日鐵住金ステンレス株式会社 低温靭性に優れた耐熱フェライト系ステンレス鋼板およびその製造方法
JP6425959B2 (ja) * 2014-10-14 2018-11-21 山陽特殊製鋼株式会社 耐高温酸化性、高温クリープ強度および高温引張強度に優れたフェライト系ステンレス鋼
DE102015102255A1 (de) * 2015-02-17 2016-08-18 Sandvik Materials Technology Deutschland Gmbh Verfahren zum Herstellen eines Strangs aus Edelstahl sowie Strang aus Edelstahl
JP6239192B2 (ja) 2015-03-31 2017-11-29 新日鐵住金ステンレス株式会社 排気系部品
US20180171430A1 (en) * 2015-07-02 2018-06-21 Jfe Steel Corporation Ferritic stainless steel sheet and method for manufacturing the same
MX2019011670A (es) * 2017-03-27 2019-12-19 Nippon Steel Stainless Steel Corp Lamina de acero inoxidable ferritico, metodo para producir la misma y miembro de escape.
KR102020513B1 (ko) 2017-12-11 2019-09-10 주식회사 포스코 고온 내산화성이 우수한 페라이트계 스테인리스강 및 그 제조방법
DE102020214688A1 (de) * 2020-11-23 2022-05-25 Robert Bosch Gesellschaft mit beschränkter Haftung Wasserstoffbeständiger ferritischer Stahl mit Laves-Phase
CN113249558B (zh) * 2021-04-15 2022-12-16 首钢集团有限公司 减少低碳铝镇静钢粗晶缺陷的方法及制得的低碳铝镇静钢

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2001303204A (ja) * 2000-04-19 2001-10-31 Sumitomo Metal Ind Ltd 耐熱性フェライト系ステンレス鋼とその鋼板
JP2009231149A (ja) * 2008-03-24 2009-10-08 Nisshin Steel Co Ltd セパレータ用フェライト系粗面化ステンレス鋼板およびセパレータ
JP2010156039A (ja) * 2008-12-04 2010-07-15 Jfe Steel Corp 耐熱性に優れるフェライト系ステンレス鋼

Family Cites Families (27)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP3021656B2 (ja) 1992-04-09 2000-03-15 新日本製鐵株式会社 耐高温塩害性及び高温強度に優れたフェライト系ステンレス鋼
JPH09279312A (ja) 1996-04-18 1997-10-28 Nippon Steel Corp 高温特性、耐食性及び加工性に優れたフェライト系ステンレス鋼
JP3536567B2 (ja) 1997-01-24 2004-06-14 Ｊｆｅスチール株式会社 耐熱性、加工性およびマフラー耐食性に優れるエンジン排気部材用フェライト系ステンレス鋼
JP2000169943A (ja) 1998-12-04 2000-06-20 Nippon Steel Corp 高温強度に優れたフェライト系ステンレス鋼及びその製造方法
JP3468156B2 (ja) 1999-04-13 2003-11-17 住友金属工業株式会社 自動車排気系部品用フェライト系ステンレス鋼
JP3397167B2 (ja) 1999-04-16 2003-04-14 住友金属工業株式会社 自動車排気系部品用フェライト系ステンレス鋼
JP4035919B2 (ja) * 1999-04-27 2008-01-23 住友金属工業株式会社 表面品質に優れたマルテンサイト系ステンレス鋼継目無鋼管
JP4301638B2 (ja) * 1999-05-27 2009-07-22 新日鐵住金ステンレス株式会社 高温強度に優れた高純度フェライト系ステンレス鋼
JP2001026826A (ja) * 1999-07-12 2001-01-30 Sumitomo Metal Ind Ltd ステンレス熱延鋼帯の製造方法
US6426039B2 (en) * 2000-07-04 2002-07-30 Kawasaki Steel Corporation Ferritic stainless steel
JP4197492B2 (ja) 2001-07-05 2008-12-17 日新製鋼株式会社 排ガス流路部材用フェライト系ステンレス鋼
CN1327009C (zh) * 2002-12-12 2007-07-18 新日铁住金不锈钢株式会社 加工性优良的含铬耐热钢板及其制造方法
JP4604714B2 (ja) 2003-12-26 2011-01-05 Ｊｆｅスチール株式会社 フェライト系Ｃｒ含有鋼材及びその製造方法
JP4519505B2 (ja) * 2004-04-07 2010-08-04 新日鐵住金ステンレス株式会社 成形性に優れるフェライト系ステンレス鋼板およびその製造方法
JP2006037176A (ja) 2004-07-28 2006-02-09 Nisshin Steel Co Ltd エキゾーストマニホールド用フェライト系ステンレス鋼
JP4498950B2 (ja) * 2005-02-25 2010-07-07 新日鐵住金ステンレス株式会社 加工性に優れた排気部品用フェライト系ステンレス鋼板およびその製造方法
JP5010301B2 (ja) 2007-02-02 2012-08-29 日新製鋼株式会社 排ガス経路部材用フェライト系ステンレス鋼および排ガス経路部材
JP5297630B2 (ja) * 2007-02-26 2013-09-25 新日鐵住金ステンレス株式会社 耐熱性に優れたフェライト系ステンレス鋼板
JP5012243B2 (ja) * 2007-06-19 2012-08-29 Ｊｆｅスチール株式会社 高温強度、耐熱性および加工性に優れるフェライト系ステンレス鋼
JP5396752B2 (ja) * 2007-10-02 2014-01-22 Ｊｆｅスチール株式会社 靭性に優れたフェライト系ステンレス鋼およびその製造方法
JP5178156B2 (ja) 2007-11-13 2013-04-10 日新製鋼株式会社 自動車排ガス経路部材用フェライト系ステンレス鋼材
JP5178157B2 (ja) 2007-11-13 2013-04-10 日新製鋼株式会社 自動車排ガス経路部材用フェライト系ステンレス鋼材
JP5025671B2 (ja) 2008-02-13 2012-09-12 新日鐵住金ステンレス株式会社 高温強度に優れたフェライト系ステンレス鋼板およびその製造方法
JP5125600B2 (ja) 2008-02-25 2013-01-23 Ｊｆｅスチール株式会社 高温強度、耐水蒸気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
JP5141296B2 (ja) 2008-02-25 2013-02-13 Ｊｆｅスチール株式会社 高温強度と靭性に優れるフェライト系ステンレス鋼
JP5274074B2 (ja) 2008-03-28 2013-08-28 新日鐵住金ステンレス株式会社 耐酸化性に優れた耐熱性フェライト系ステンレス鋼板
JP2010236001A (ja) * 2009-03-31 2010-10-21 Nisshin Steel Co Ltd フェライト系ステンレス鋼

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2001303204A (ja) * 2000-04-19 2001-10-31 Sumitomo Metal Ind Ltd 耐熱性フェライト系ステンレス鋼とその鋼板
JP2009231149A (ja) * 2008-03-24 2009-10-08 Nisshin Steel Co Ltd セパレータ用フェライト系粗面化ステンレス鋼板およびセパレータ
JP2010156039A (ja) * 2008-12-04 2010-07-15 Jfe Steel Corp 耐熱性に優れるフェライト系ステンレス鋼

Non-Patent Citations (3)

* Cited by examiner, † Cited by third party
Title
JP 2001-303204 machine translation and written English translation of Table 3 column 7-12 headings and footnotes 1-6 *
JP 2009-231149 machine translation *
JP2010156039 machine translation *

Cited By (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US9885099B2 (en) 2012-03-09 2018-02-06 Nippon Steel & Sumikin Stainless Steel Corporation Ferritic stainless steel sheet
US10358689B2 (en) 2013-02-04 2019-07-23 Nippon Steel & Sumikin Stainless Steel Corporation Method of producing ferritic stainless steel sheet
US10450623B2 (en) 2013-03-06 2019-10-22 Nippon Steel & Sumikin Stainless Steel Corporation Ferritic stainless steel sheet having excellent heat resistance
US10385429B2 (en) 2013-03-27 2019-08-20 Nippon Steel & Sumikin Stainless Steel Corporation Hot-rolled ferritic stainless-steel plate, process for producing same, and steel strip
EP3103889A4 (en) * 2014-02-05 2017-03-08 JFE Steel Corporation Hot-rolled and annealed ferritic stainless steel sheet, method for producing same, and cold-rolled and annealed ferritic stainless steel sheet
US10837075B2 (en) 2014-02-05 2020-11-17 Jfe Steel Corporation Hot rolled and annealed ferritic stainless steel sheet, method of producing same, and cold rolled and annealed ferritic stainless steel sheet
US10975459B2 (en) 2015-09-29 2021-04-13 Jfe Steel Corporation Ferritic stainless steel
US11242578B2 (en) 2017-03-30 2022-02-08 Nippon Steel Stainless Steel Corporation Ferrite-based stainless steel sheet having low specific gravity and production method therefor
EP3795711A4 (en) * 2018-06-26 2021-03-24 Posco STAINLESS FERRITIC STAINLESS STEEL WITH EXCELLENT DAMPING CAPACITY AND PROCESS FOR ITS MANUFACTURING

Also Published As

Publication number Publication date
KR20130107371A (ko) 2013-10-01
WO2012133573A1 (ja) 2012-10-04
KR101557463B1 (ko) 2015-10-06
EP2692889A1 (en) 2014-02-05
JP2012207252A (ja) 2012-10-25
JP5659061B2 (ja) 2015-01-28
EP2692889A4 (en) 2014-11-26
CN103459639A (zh) 2013-12-18
EP2692889B1 (en) 2017-06-21

Similar Documents

Publication Publication Date Title
EP2692889B1 (en) Ferritic stainless steel sheet having excellent heat resistance and processability, and method for producing same
JP5546911B2 (ja) 耐熱性と加工性に優れたフェライト系ステンレス鋼板
US8980018B2 (en) Ferritic stainless steel sheet excellent in heat resistance and workability and method of production of same
US8153055B2 (en) Ferritic stainless steel with excellent heat resistance
US8062584B2 (en) Ferritic stainless steel sheet superior in heat resistance
US9279172B2 (en) Heat-resistance ferritic stainless steel
US20150020933A1 (en) Heat-resistant cold rolled ferritic stainless steel sheet, hot rolled ferritic stainless steel sheet for cold rolling raw material, and methods for producing same
JP5025671B2 (ja) 高温強度に優れたフェライト系ステンレス鋼板およびその製造方法
US20130149187A1 (en) Heat-resistant ferritic stainless steel sheet having excellent oxidation resistance
US20140373980A1 (en) Ferrite-based stainless steel plate having excellent resistance against scale peeling, and method for manufacturing same
JP2013213279A (ja) 耐酸化性に優れたフェライト系ステンレス鋼板
JP4495064B2 (ja) 熱間プレス用鋼板
WO2015118855A1 (ja) フェライト系ステンレス熱延焼鈍鋼板、その製造方法およびフェライト系ステンレス冷延焼鈍鋼板
US20150139851A1 (en) Ferritic stainless steel
JP7009278B2 (ja) 耐熱性に優れたフェライト系ステンレス鋼板および排気部品とその製造方法
JP5937861B2 (ja) 溶接性に優れた耐熱フェライト系ステンレス鋼板
JP5208450B2 (ja) 熱疲労特性に優れたＣｒ含有鋼
JP5332894B2 (ja) 延性、疲労特性及び靭性に優れた低比重鋼板及びその製造方法

Legal Events

Date Code Title Description
AS Assignment

Owner name: NIPPON STEEL & SUMIKIN STAINLESS STEEL CORPORATION

Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNORS:HAMADA, JUNICHI;KANNO, NORIHIRO;INOUE, YOSHIHARU;REEL/FRAME:031302/0061

Effective date: 20130719

STCB Information on status: application discontinuation

Free format text: ABANDONED -- FAILURE TO RESPOND TO AN OFFICE ACTION