WO2013179616A1 - フェライト系ステンレス鋼 - Google Patents
フェライト系ステンレス鋼 Download PDFInfo
- Publication number
- WO2013179616A1 WO2013179616A1 PCT/JP2013/003282 JP2013003282W WO2013179616A1 WO 2013179616 A1 WO2013179616 A1 WO 2013179616A1 JP 2013003282 W JP2013003282 W JP 2013003282W WO 2013179616 A1 WO2013179616 A1 WO 2013179616A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- less
- steel
- stainless steel
- ferritic stainless
- thermal fatigue
- Prior art date
Links
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
-
- 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
-
- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
- C22C38/02—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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
-
- 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
-
- 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
-
- G—PHYSICS
- G01—MEASURING; TESTING
- G01N—INVESTIGATING OR ANALYSING MATERIALS BY DETERMINING THEIR CHEMICAL OR PHYSICAL PROPERTIES
- G01N3/00—Investigating strength properties of solid materials by application of mechanical stress
- G01N3/32—Investigating strength properties of solid materials by application of mechanical stress by applying repeated or pulsating forces
-
- 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
- C21D7/00—Modifying the physical properties of iron or steel by deformation
- C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
-
- 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
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- 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
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
-
- 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
-
- G—PHYSICS
- G01—MEASURING; TESTING
- G01N—INVESTIGATING OR ANALYSING MATERIALS BY DETERMINING THEIR CHEMICAL OR PHYSICAL PROPERTIES
- G01N2203/00—Investigating strength properties of solid materials by application of mechanical stress
- G01N2203/0014—Type of force applied
- G01N2203/0016—Tensile or compressive
-
- G—PHYSICS
- G01—MEASURING; TESTING
- G01N—INVESTIGATING OR ANALYSING MATERIALS BY DETERMINING THEIR CHEMICAL OR PHYSICAL PROPERTIES
- G01N2203/00—Investigating strength properties of solid materials by application of mechanical stress
- G01N2203/0058—Kind of property studied
- G01N2203/0069—Fatigue, creep, strain-stress relations or elastic constants
- G01N2203/0073—Fatigue
-
- G—PHYSICS
- G01—MEASURING; TESTING
- G01N—INVESTIGATING OR ANALYSING MATERIALS BY DETERMINING THEIR CHEMICAL OR PHYSICAL PROPERTIES
- G01N2203/00—Investigating strength properties of solid materials by application of mechanical stress
- G01N2203/02—Details not specific for a particular testing method
- G01N2203/022—Environment of the test
- G01N2203/0222—Temperature
-
- G—PHYSICS
- G01—MEASURING; TESTING
- G01N—INVESTIGATING OR ANALYSING MATERIALS BY DETERMINING THEIR CHEMICAL OR PHYSICAL PROPERTIES
- G01N2203/00—Investigating strength properties of solid materials by application of mechanical stress
- G01N2203/02—Details not specific for a particular testing method
- G01N2203/026—Specifications of the specimen
- G01N2203/0262—Shape of the specimen
- G01N2203/0268—Dumb-bell specimens
Definitions
- the present invention relates to a ferritic stainless steel excellent in scale adhesion and thermal fatigue characteristics.
- Nb added to ferritic stainless steel increases the high temperature strength and improves thermal fatigue properties by dissolving in the steel.
- Nb is likely to combine with C and N in the steel to become carbonitride, and the amount of solid solution Nb may be reduced to deteriorate the thermal fatigue characteristics.
- a typical example of this Nb-Ti composite added steel is Type 441 ferritic stainless steel (18% Cr-0.5% Nb-0.2% Ti) (EN10088-2: EN1.4509). Widely used in automobile exhaust manifolds.
- Nb—Ti composite-added ferritic stainless steel has a problem that scale (oxide film) tends to peel off when it is repeatedly heated to a high temperature and cooled, so-called repeated oxidation. Since the exhaust manifold is used in a severe and repeated oxidation environment that is repeatedly heated and cooled each time the engine is started and stopped, if the scale peels off, the iron will be directly exposed to high-temperature exhaust gas and oxidation will proceed. As a result, the plate thickness decreases, and in some cases, holes may be formed or deformed. In addition, cracks may occur starting from the point where the scale peels off. Therefore, the Nb—Ti composite-added ferritic stainless steel is also required to have excellent scale adhesion that does not cause the scale to peel off.
- Patent Documents 1 and 2 disclose the addition of Mo as a method for improving the high temperature strength and thermal fatigue characteristics of Nb—Ti composite added ferritic stainless steel.
- Patent Documents 3 to 5 disclose the addition of Mo, Cu, and W.
- Patent Document 3 discloses the addition of REM, Ca, Y, and Zr.
- Patent Document 5 discloses the addition of REM and Ca.
- Mo and W are expensive and have not only an increase in the surface defects (so-called scabs and the like) of the steel sheet, but also have the disadvantage of reducing workability.
- Cu not only greatly reduces the workability at room temperature, but also has the disadvantage of reducing oxidation resistance.
- REM, Ca, Y, and Zr also have a drawback of increasing the surface defects of the steel sheet.
- the present invention has been made to solve the above-described problems, and an object of the present invention is to provide a ferritic stainless steel excellent in scale adhesion and thermal fatigue characteristics without impairing surface properties.
- the inventors have conducted research on the scale adhesion of Nb—Ti composite-added ferritic stainless steel, and found that adding a suitable amount of Ni can improve the scale adhesion and prevent scale peeling.
- the present invention has been made based on the above findings, and the gist thereof is as follows.
- C 0.020% or less, Si: 1.0% or less, Mn: 1.0% or less, P: 0.040% or less, S: 0.030% or less, Cr: 16 0.0% to 20.0%, N: 0.020% or less, Nb: 0.30% to 0.80%, Ti: 4 ⁇ (C% + N%)% to 0.50%, Al : Less than 0.20%, Ni: 0.05% or more and 0.40% or less, Co: 0.01% or more and 0.30% or less, with the balance being Fe and inevitable impurities Ferritic stainless steel.
- the C% and the N% represent C and N contents (% by mass), respectively.
- a ferritic stainless steel having excellent scale adhesion and thermal fatigue characteristics can be obtained. Also, the surface properties are excellent. Since the ferritic stainless steel of the present invention is excellent in scale adhesion and thermal fatigue characteristics, it can be suitably used for an exhaust system member of an automobile.
- FIG. 1 is a diagram for explaining a thermal fatigue test piece.
- FIG. 2 is a diagram for explaining temperature and restraint conditions in a thermal fatigue test.
- composition of the steel of the present invention is specified.
- component% means the mass% unless there is particular notice.
- C 0.020% or less C is an element effective for increasing the strength of steel, and since the effect is obtained with a content of 0.001% or more, 0.001% or more is preferable. On the other hand, if the content exceeds 0.020%, scale peeling occurs, so the content is made 0.020% or less. From the viewpoint of ensuring workability, a smaller amount is desirable, and it is preferably 0.015% or less. More preferably, it is 0.004% or more and 0.008% or less of range.
- Si 1.0% or less Si is an element effective for improving oxidation resistance, and the effect is obtained by addition of 0.01% or more, so 0.01% or more is preferable. On the other hand, if over 1.0% is added, the workability deteriorates. In addition, Preferably it is the range of more than 0.3% and 0.6% or less.
- Mn 1.0% or less Mn is an element that increases the strength of steel and also has an action as a deoxidizer. Since the effect is obtained by addition of 0.01% or more, 0.01% or more is preferable. On the other hand, if added over 1.0%, the amount of increase in oxidation is remarkably increased and the oxidation resistance is lowered, so the content is made 1.0% or less. Preferably, it is 0.2 to 0.6% of range.
- P 0.040% or less
- P is an element that lowers toughness, and is desirably reduced, and is 0.040% or less. Preferably, it is 0.035% or less. More preferably, it is 0.030% or less.
- S 0.030% or less S is desirable because it lowers moldability and corrosion resistance, and is preferably 0.030% or less. Preferably, it is 0.006% or less. More preferably, it is 0.003% or less.
- Cr 16.0% or more and 20.0% or less Cr is an element necessary for improving oxidation resistance, and in order to obtain good oxidation resistance, addition of 16.0% or more is necessary. . On the other hand, if added over 20.0%, the steel hardens and the productivity and workability deteriorate, so the content is made 20.0% or less. Preferably, it is 17.0% or more and 19.0% or less of range.
- N 0.020% or less N is preferable because it lowers the toughness and formability of steel, and is preferably 0.020% or less. Preferably, it is 0.015% or less. More preferably, it is 0.012% or less.
- Nb 0.30% or more and 0.80% or less
- Nb is an element having an effect of remarkably increasing high-temperature strength by solid solution strengthening and improving thermal fatigue characteristics. The effect appears with addition of 0.30% or more.
- excessive addition exceeding 0.80% not only lowers the toughness of the steel, but also forms a Laves phase (Fe 2 Nb) at a high temperature and lowers the high temperature strength, so it is made 0.80% or less.
- it is 0.40% or more and 0.60% or less of range.
- C% and N% represent the contents (mass%) of C and N, respectively.
- Ti preferentially combines with C and N to produce carbonitride, thereby preventing the formation of Nb carbonitride and improving corrosion resistance, formability, and intergranular corrosion of welds.
- 4 ⁇ (C% + N%)% or more is necessary. If it is less than this, C and N cannot be produced completely as Ti carbonitrides, Nb carbonitrides are formed, the amount of Nb solid solution is reduced, and thermal fatigue properties are deteriorated.
- excessive addition reduces the toughness of the steel, so it is made 0.50% or less.
- they are 5 * (C% + N%)% or more and 0.30% or less. More preferably, it is 0.10% or more and 0.25% or less.
- Al less than 0.20%
- Al is an element effective for deoxidation, and the effect is obtained by addition of 0.01% or more, so 0.01% or more is preferable.
- the content is made less than 0.20%.
- they are 0.01% or more and 0.10% or less. More preferably, it is 0.02% or more and 0.06% or less.
- Ni 0.05% or more and 0.40% or less Ni is an important element for securing scale adhesion in the present invention, and for that purpose it is necessary to add 0.05% or more. Further, as will be described later, since the thermal expansion coefficient of the steel of the present invention is reduced by the addition of an appropriate amount of Co, a smaller amount of Ni is added compared to steel containing no Co or steel lacking the amount of Co. The above effect can be obtained. On the other hand, in addition to being an expensive element, Ni is added in excess of 0.40%, thereby generating a ⁇ phase at a high temperature and reducing scale adhesion. Therefore, the amount of Ni added is in the range of 0.05% to 0.40%. Preferably, it is 0.10% or more and 0.30% or less of range. More preferably, it is 0.20% or more and 0.30% or less of range.
- Co 0.01% or more and 0.30% or less
- Co is an important element in the present invention. It is an element necessary for improving thermal fatigue characteristics, and for that purpose, at least 0.01% or more must be added. Co can improve the thermal fatigue characteristics by reducing the thermal expansion coefficient of the steel to reduce the amount of expansion at the time of temperature rise and by reducing the amount of strain generated at the time of temperature rise and cooling. Furthermore, by reducing the thermal expansion coefficient of the steel, the difference between the thermal expansion coefficient of the steel and the scale is reduced, and the scale is difficult to peel off during cooling. Therefore, there is an effect that scale peeling can be prevented by adding a smaller amount of Ni.
- Co is made 0.30% or less. More preferably, it is 0.02% or more and 0.10% or less of range. More preferably, it is 0.03% or more and 0.110% or less of range.
- the present invention is a ferritic stainless steel excellent in scale adhesion and thermal fatigue characteristics, characterized in that it contains the above-mentioned essential components and the balance consists of Fe and inevitable impurities. Furthermore, if necessary, one or more selected from Ca, Mg and B, or one or more selected from Mo, Cu, V and W within the following ranges. Can be added.
- Ca 0.0005% or more and 0.0030% or less
- Ca is an effective component for preventing nozzle clogging due to precipitation of Ti-based inclusions that are likely to occur during continuous casting. The effect is obtained by adding 0.0005% or more.
- it is necessary to be 0.0030% or less. Therefore, when adding Ca, it is set as 0.0005% or more and 0.0030% or less. More preferably, it is 0.0005% or more and 0.0020% or less of range. More preferably, it is 0.0005% or more and 0.0015% or less of range.
- Mg 0.0002% or more and 0.0020% or less
- Mg is an element effective for improving the equiaxed crystal ratio of the slab and improving workability and toughness. Furthermore, it is an element effective for suppressing the coarsening of Nb and Ti carbonitrides. When the Ti carbonitride becomes coarse, it becomes a starting point for brittle cracks, so that toughness decreases. Further, when the Nb carbonitride is coarsened, the amount of Nb solid solution in the steel is reduced, which leads to a decrease in thermal fatigue characteristics. The above effect can be obtained by adding 0.0002% or more. On the other hand, if the amount of Mg added exceeds 0.0020%, the surface properties of the steel are deteriorated.
- Mg when adding Mg, it is set as 0.0002% or more and 0.0020% or less of range. Preferably it is 0.0002% or more and 0.0015% or less of range. More preferably, it is 0.0004% or more and 0.0010% or less of range.
- B 0.0002% or more and 0.0020% or less B is an element effective for improving workability, particularly secondary workability. These effects can be obtained by adding 0.0002% or more. On the other hand, if added over 0.0020%, the workability and toughness of the steel decrease, so 0.0020% or less. Therefore, when adding B, it is set as 0.0002% or more and 0.0020% or less of range. Preferably it is 0.0003% or more and 0.0010% or less of range.
- Mo 0.02% or more and less than 0.10%
- Mo is an element that increases the strength of the steel by solid solution strengthening and improves the thermal fatigue characteristics, and the effect is obtained by adding 0.02% or more.
- it is an expensive element, and when it is added in a large amount, not only surface defects are generated, but also workability is lowered.
- it is necessary to be less than 0.10%. Therefore, when adding, it is made into the range of 0.02% or more and less than 0.10%.
- it is 0.04% or more and less than 0.10%.
- Cu 0.01% or more and less than 0.20%
- Cu precipitates as ⁇ -Cu, strengthens the steel and improves thermal fatigue properties. Moreover, in order to acquire the effect, it is necessary to add 0.01% or more. On the other hand, if 0.20% or more is added, the steel becomes hard and the workability is lowered. Therefore, in order to obtain good workability, the content is made less than 0.20%. Therefore, when adding Cu, it is set as 0.01% or more and less than 0.20% of range. Preferably it is 0.01% or more and less than 0.10%.
- V 0.01% or more and less than 0.50%
- V is an element effective for improving high-temperature strength. The effect is obtained at 0.01% or more.
- coarse V (C, N) precipitates and the toughness decreases. Therefore, when adding V, it is made into the range of 0.01% or more and less than 0.50%. Preferably, it is 0.02% or more and less than 0.20%.
- W 0.02% or more and less than 0.30%
- W is an element that increases the strength of steel by solid solution strengthening, and the effect is obtained by adding 0.02% or more.
- it is an expensive element, and if it is added in a large amount, it not only causes surface defects, but also greatly reduces workability. In order to obtain good surface properties and good workability, the content is made less than 0.30%. Therefore, when adding W, it is set as 0.02% or more and less than 0.30%.
- an ordinary method for producing stainless steel can be used.
- Steel with the above composition is melted in a melting furnace such as a converter or electric furnace, and further subjected to secondary refining such as ladle refining, vacuum refining, etc., and then a steel slab by continuous casting or ingot-bundling rolling (Slab), hot-rolled, hot-rolled sheet annealed and pickled to give a hot-rolled annealed pickled sheet.
- a method of forming a cold-rolled annealed plate through each process such as cold rolling, finish annealing, pickling and the like is recommended.
- An example is as follows.
- this hot-rolled annealed pickled plate is for the purpose of the present invention, such as an exhaust manifold, but further, cold-rolled and annealed / pickled to obtain a cold-rolled annealed pickled plate. You can also.
- two or more cold rolling processes including intermediate annealing may be performed as necessary.
- the total rolling reduction in the cold rolling process comprising one or more cold rollings is 60% or more, preferably 70% or more.
- the cold-rolled sheet annealing temperature is 900 to 1150 ° C, preferably 950 to 1100 ° C.
- the shape and quality of the steel sheet can be adjusted by adding mild rolling (skin pass rolling or the like) after pickling.
- it can also be set to BA finishing which annealed in the reducing atmosphere containing hydrogen and abbreviated the pickling.
- the hot-rolled annealed sheet product or cold-rolled annealed sheet product obtained in this way bending is performed according to the respective use, and the exhaust pipe, catalyst outer cylinder material, and thermal power plant for automobiles and motorcycles. It is formed into an exhaust duct or a fuel cell related member.
- the welding method for welding these members is not particularly limited, and various arc welding methods such as TIG, MIG, and MAG, resistance welding methods such as spot welding and seam welding, and electric resistance welding methods, etc. High frequency resistance welding and high frequency induction welding can be applied.
- the sheet bar was heated to 1050 ° C. and hot-rolled to obtain a hot-rolled sheet having a thickness of 5 mm. Thereafter, hot-rolled sheet annealing was performed in a temperature range of 900 to 1050 ° C., and pickled to produce a hot-rolled annealed sheet. At this stage, the surface properties of the steel sheet were observed with the naked eye. This was cold-rolled to a thickness of 2 mm and finish-annealed in a temperature range of 900 to 1050 ° C. to obtain a cold-rolled annealed plate. This was subjected to the following repeated oxidation test.
- the test piece for thermal fatigue test was repeatedly heated and cooled between 100 ° C. and 900 ° C., and at the same time, strain was repeatedly given at a constraint factor of 0.6 as shown in FIG. 2, and the thermal fatigue life was measured.
- the measurement method was in accordance with the Japan Society of Materials Standard High Temperature Low Cycle Test Method (JSMS-SD-7-03).
- JSMS-SD-7-03 Japan Society of Materials Standard High Temperature Low Cycle Test Method
- Comparative Example No. 1 with Cr of 14.5% which is low outside the scope of the present invention.
- Comparative Example No. C is 0.023%, which is high outside the scope of the present invention.
- scale peeling occurred and scale adhesion was unacceptable.
- Comparative Example No. No. 20 is a steel equivalent to Type 441, but Co is less than 0.01%, which is low outside the scope of the present invention, so the thermal fatigue characteristics are unacceptable, and even though 0.05% Ni is added. The scale adhesion was also unacceptable.
- Ni is as low as 0.04% or 0.02% outside the scope of the present invention. Nos. 22 and 23, and Ni is 0.45%, which is high outside the scope of the present invention. Comparative Example No. 29, in which 24 and Co were 0.32%, which were high outside the scope of the present invention, failed in scale adhesion.
- the ferritic stainless steel of the present invention is suitable for exhaust system members such as exhaust manifolds, various exhaust pipes, converter cases, and mufflers because it has excellent scale adhesion and thermal fatigue characteristics. Furthermore, it is also suitable as an exhaust system member or a fuel cell member of a thermal power generation system.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Combustion & Propulsion (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- General Engineering & Computer Science (AREA)
- Life Sciences & Earth Sciences (AREA)
- Biochemistry (AREA)
- General Health & Medical Sciences (AREA)
- General Physics & Mathematics (AREA)
- Immunology (AREA)
- Pathology (AREA)
- Analytical Chemistry (AREA)
- Health & Medical Sciences (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
[1]質量%で、C:0.020%以下、Si:1.0%以下、Mn:1.0%以下、P:0.040%以下、S:0.030%以下、Cr:16.0%以上20.0%以下、N:0.020%以下、Nb:0.30%以上0.80%以下、Ti:4×(C%+N%)%以上0.50%以下、Al:0.20%未満、Ni:0.05%以上0.40%以下、Co:0.01%以上0.30%以下を含有し、残部がFeおよび不可避的不純物からなることを特徴とするフェライト系ステンレス鋼。なお、前記C%、前記N%はそれぞれC、Nの含有量(質量%)を表す。
[2] 質量%で、さらに、Ca:0.0005%以上0.0030%以下、Mg:0.0002%以上0.0020%以下、B:0.0002%以上0.0020%以下の中から1種または2種以上を含有することを特徴とする前記[1]に記載のフェライト系ステンレス鋼。
[3] 質量%で、さらに、Mo:0.02%以上0.10%未満、Cu:0.01%以上0.20%未満、V:0.01%以上0.50%未満およびW:0.02%以上0.30%未満のうちから選ばれる1種または2種以上を含有することを特徴とする前記[1]または[2]に記載のフェライト系ステンレス鋼。
Cは、鋼の強度を高めるのに有効な元素であり、その効果は0.001%以上の含有で得られるため、0.001%以上が好ましい。一方、0.020%を超えて含有すると、スケール剥離が起こるので、0.020%以下とする。なお、加工性を確保する観点からは少ない方が望ましく、0.015%以下とするのが好ましい。より好ましくは、0.004%以上0.008%以下の範囲である。
Siは、耐酸化性向上のために有効な元素であり、その効果は0.01%以上の添加で得られるため、0.01%以上が好ましい。一方、1.0%を超えて添加すると加工性が低下するので、1.0%以下とする。なお、好ましくは0.3%超0.6%以下の範囲である。
Mnは、鋼の強度を高める元素であり、また、脱酸剤としての作用も有する。その効果は0.01%以上の添加で得られるため、0.01%以上が好ましい。一方、1.0%を超えて添加すると、酸化増量を著しく増加させて耐酸化性を低下させてしまうので、1.0%以下とする。好ましくは、0.2%以上0.6%以下の範囲である。
Pは、靭性を低下させる元素であり、低減するのが望ましく、0.040%以下とする。好ましくは、0.035%以下である。より好ましくは0.030%以下である。
Sは、成形性と耐食性を低下させるので少ないほうが望ましく、0.030%以下とする。好ましくは、0.006%以下である。より好ましくは、0.003%以下である。
Crは、耐酸化性を向上させるために必要な元素であり、良好な耐酸化性を得るために、16.0%以上の添加が必要である。一方、20.0%を超えて添加すると鋼が硬質化して製造性や加工性が低下するので20.0%以下とする。好ましくは、17.0%以上19.0%以下の範囲である。
Nは、鋼の靭性および成形性を低下させるので少ないほうが望ましく、0.020%以下とする。好ましくは、0.015%以下である。より好ましくは、0.012%以下である。
Nbは、固溶強化により高温強度を著しく上昇させて熱疲労特性を向上させる効果を有する元素である。その効果は0.30%以上の添加で現れる。一方、0.80%を超える過剰な添加は鋼の靭性を低下させるのみならず、高温においてLaves相(Fe2Nb)を形成して却って高温強度を低下させるので0.80%以下とする。好ましくは0.40%以上0.60%以下の範囲である。
Tiは、優先的にC、Nと結びついて炭窒化物を生成することで、Nb炭窒化物の生成を防ぐとともに、耐食性、成形性および溶接部の粒界腐食性を向上させる。これらの効果を得るためには4×(C%+N%)%以上の添加が必要である。これより少ないと、C、Nを完全にTi炭窒化物として生成させることができず、Nb炭窒化物が形成してNb固溶量が減少して熱疲労特性が低下する。一方で、過剰な添加は鋼の靭性が低下するので、0.50%以下とする。好ましくは5×(C%+N%)%以上0.30%以下である。さらに好ましくは0.10%以上0.25%以下である。
Alは脱酸に有効な元素であり、その効果は0.01%以上の添加で得られるため、0.01%以上が好ましい。一方、鋼を硬質化させて加工性を低下させるので、0.20%未満とする。好ましくは0.01%以上0.10%以下である。より好ましくは0.02%以上0.06%以下である。
Niは、本発明においてスケール密着性を確保するために重要な元素であり、そのためには0.05%以上添加することが必要である。また、後述のように、本発明の鋼は適量のCo添加によって熱膨張係数が低減されているため、Co無添加鋼あるいはCoの添加量が不足する鋼に比べて、より少量のNi添加量で上記効果が得られる。一方、Niは高価な元素であることに加えて、0.40%を超えて添加すると高温でγ相を生成し却ってスケール密着性を低下させる。従って、Ni添加量は、0.05%以上0.40%以下の範囲とする。好ましくは、0.10%以上0.30%以下の範囲である。さらに好ましくは、0.20%以上0.30%以下の範囲である。
Coは、本発明において重要な元素である。熱疲労特性を向上させるのに必要な元素であり、そのためには少なくとも0.01%以上の添加が必要である。Coは、鋼の熱膨張係数を低減して昇温時の膨張量を少なくして、昇温および冷却時に発生する歪量を小さくすることで熱疲労特性を向上させることができる。さらに、鋼の熱膨張係数を低減することにより、鋼とスケールの熱膨張係数の差が小さくなり、冷却時にスケールが剥離しにくくなる。そのため、より少量のNi添加によってスケールの剥離を防止することができる効果がある。一方、0.10%を超えて添加すると、酸化皮膜と地鉄の界面にCoが濃化し、スケール密着性が低下する。0.30%を超えて添加すると、この界面濃化の副作用が上記の熱膨張係数低減によるスケール剥離防止効果を打ち消し、冷却時にスケールが剥離する。このため、Coは0.30%以下とする。より好ましくは、0.02%以上0.10%以下の範囲である。さらに好ましくは、0.03%以上0.10%以下の範囲である。
Caは、連続鋳造の際に発生しやすいTi系介在物析出によるノズルの閉塞を防止するのに有効な成分である。その効果は0.0005%以上の添加で得られる。一方、表面欠陥を発生させず良好な表面性状を得るためには0.0030%以下とする必要がある。従って、Caを添加する場合は、0.0005%以上0.0030%以下の範囲とする。より好ましくは0.0005%以上0.0020%以下の範囲である。さらに好ましくは0.0005%以上0.0015%以下の範囲である。
Mgはスラブの等軸晶率を向上させ、加工性や靱性を向上させるのに有効な元素である。さらに、NbやTiの炭窒化物の粗大化を抑制するのに有効な元素である。Ti炭窒化物が粗大化すると、脆性割れの起点となるため靱性が低下する。また、Nb炭窒化物が粗大化すると、Nbの鋼中の固溶量が低下するため、熱疲労特性の低下につながる。上記効果は0.0002%以上の添加で得られる。一方、Mg添加量が0.0020%を超えると、鋼の表面性状を悪化させてしまう。従って、Mgを添加する場合は、0.0002%以上0.0020%以下の範囲とする。好ましくは0.0002%以上0.0015%以下の範囲である。さらに好ましくは0.0004%以上0.0010%以下の範囲である。
Bは、加工性、特に二次加工性を向上させるのに有効な元素である。それらの効果は0.0002%以上の添加で得られる。一方、0.0020%を超えて添加すると鋼の加工性、靭性が低下するため、0.0020%以下とする。従って、Bを添加する場合は、0.0002%以上0.0020%以下の範囲とする。好ましくは0.0003%以上0.0010%以下の範囲である。
Moは、固溶強化により鋼の強度を増加させて熱疲労特性を向上させる元素であり、その効果は0.02%以上の添加で得られる。しかし、高価な元素であるとともに、多量に添加すると表面欠陥が発生するのみならず、加工性が低下する。良好な表面性状および良好な加工性を得るために、0.10%未満とする必要がある。従って、添加する場合は、0.02%以上0.10%未満の範囲とする。好ましくは0.04%以上0.10%未満の範囲である。
Cuは、ε-Cuとして析出することで鋼を強化して熱疲労特性を向上させる。また、その効果を得るためには、0.01%以上添加することが必要である。一方、0.20%以上添加すると鋼が硬質化し加工性が低下するので良好な加工性を得るために0.20%未満とする。従って、Cuを添加する場合は、0.01%以上0.20%未満の範囲とする。好ましくは0.01%以上0.10%未満の範囲である。
Vは、高温強度の向上に有効な元素である。その効果は、0.01%以上で得られる。一方、0.50%以上添加すると、粗大なV(C,N)が析出して靭性が低下する。従って、Vを添加する場合は、0.01%以上0.50%未満の範囲とする。好ましくは、0.02%以上0.20%未満の範囲である。
Wは、Moと同様に、固溶強化により鋼の強度を増加させる元素であり、その効果は0.02%以上添加することで得られる。しかし、高価な元素であり、また多量に添加すると表面欠陥が生じるのみならず、加工性が大きく低下する。良好な表面性状および良好な加工性を得るために、0.30%未満とする。従って、Wを添加する場合は、0.02%以上0.30%未満の範囲とする。
上記の冷延焼鈍板から20mm幅×30mm長さの寸法に切り出し、全6面を#320エメリー紙で研磨して試験に供した。酸化試験条件は、大気中において、1000℃で20min保持と100℃で1min保持を400サイクル繰り返した。加熱速度および冷却速度は、それぞれ5℃/sec、1.5℃/secで行った。試験後にスケールの剥離の有無を目視観察してスケール密着性を評価した。得られた結果を表1および表2に併せて示す。
上記熱疲労試験用試験片について、100℃-900℃間で加熱・冷却を繰り返すと同時に、図2に示したような拘束率0.6で歪を繰り返し付与し、熱疲労寿命を測定した。測定方法は、日本材料学会標準 高温低サイクル試験法(JSMS-SD-7-03)に準拠した。まず、各サイクルの100℃において検出された荷重を、図1に示した試験片均熱平行部の断面積(50.3mm2)で割って、そのサイクルの応力とした。そのサイクルにおける応力が初期(挙動が安定する5サイクル目)の応力に対して75%まで低下したサイクル数を熱疲労寿命とした。この寿命サイクル数で熱疲労特性を評価した。得られた結果を表1および表2に併せて示す。
(1)スケール密着性:繰り返し酸化試験後の試験片表面でスケールが剥離した面積が5%未満のものを○(合格)、5%以上を×(不合格)、異常酸化が生じたものを××(不合格)と判定した。
(2)熱疲労特性:熱疲労寿命が600サイクル以上のものを◎(合格、特に優れている)、540サイクル以上600サイクル未満を○(合格)、540サイクル未満を×(不合格)と判定した。
Claims (3)
- 質量%で、C:0.020%以下、Si:1.0%以下、Mn:1.0%以下、P:0.040%以下、S:0.030%以下、Cr:16.0%以上20.0%以下、N:0.020%以下、Nb:0.30%以上0.80%以下、Ti:4×(C%+N%)%以上0.50%以下、Al:0.20%未満、Ni:0.05%以上0.40%以下、Co:0.01%以上0.30%以下を含有し、残部がFeおよび不可避的不純物からなることを特徴とするフェライト系ステンレス鋼。なお、前記C%、前記N%はそれぞれC、Nの含有量(質量%)を表す。
- 質量%で、さらに、Ca:0.0005%以上0.0030%以下、Mg:0.0002%以上0.0020%以下、B:0.0002%以上0.0020%以下の中から1種または2種以上を含有することを特徴とする請求項1に記載のフェライト系ステンレス鋼。
- 質量%で、さらに、Mo:0.02%以上0.10%未満、Cu:0.01%以上0.20%未満、V:0.01%以上0.50%未満、W:0.02%以上0.30%未満のうちから選ばれる1種または2種以上を含有することを特徴とする請求項1または請求項2に記載のフェライト系ステンレス鋼。
Priority Applications (6)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP13796603.2A EP2857538B1 (en) | 2012-05-28 | 2013-05-23 | Ferritic stainless steel |
KR1020147032640A KR101956709B1 (ko) | 2012-05-28 | 2013-05-23 | 페라이트계 스테인리스강 |
ES13796603.2T ES2673216T3 (es) | 2012-05-28 | 2013-05-23 | Acero inoxidable ferrítico |
JP2013548673A JP5505570B1 (ja) | 2012-05-28 | 2013-05-23 | フェライト系ステンレス鋼 |
CN201380027852.3A CN104364404B (zh) | 2012-05-28 | 2013-05-23 | 铁素体系不锈钢 |
US14/403,687 US20150139851A1 (en) | 2012-05-28 | 2013-05-23 | Ferritic stainless steel |
Applications Claiming Priority (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2012120531 | 2012-05-28 | ||
JP2012-120531 | 2012-05-28 | ||
JP2012-209012 | 2012-09-24 | ||
JP2012209012 | 2012-09-24 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2013179616A1 true WO2013179616A1 (ja) | 2013-12-05 |
Family
ID=49672843
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2013/003282 WO2013179616A1 (ja) | 2012-05-28 | 2013-05-23 | フェライト系ステンレス鋼 |
Country Status (9)
Country | Link |
---|---|
US (1) | US20150139851A1 (ja) |
EP (1) | EP2857538B1 (ja) |
JP (1) | JP5505570B1 (ja) |
KR (1) | KR101956709B1 (ja) |
CN (1) | CN104364404B (ja) |
ES (1) | ES2673216T3 (ja) |
MY (1) | MY160980A (ja) |
TW (1) | TWI503424B (ja) |
WO (1) | WO2013179616A1 (ja) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2018116792A1 (ja) * | 2016-12-21 | 2018-06-28 | Jfeスチール株式会社 | フェライト系ステンレス鋼 |
Families Citing this family (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US20150323432A1 (en) * | 2014-05-09 | 2015-11-12 | Balhassn S. M. Ali | Pin loaded small one-bar specimen (OBS) |
US20150377757A1 (en) * | 2014-06-30 | 2015-12-31 | Balhassn S. M. Ali | Small Two bar specimen (TBS) |
DE102016112654B3 (de) * | 2016-07-11 | 2017-10-19 | Universität Siegen | Werkstoffprobe, Verfahren zum Festlegen einer Probengeometrie, Verfahren zum Ermitteln eines Werkstoffverhaltens und/oder von Werkstoffkennwerten, Spannungs-Dehnungs-Kurve eines Werkstoffs und Produkt |
JP6418338B2 (ja) * | 2016-09-02 | 2018-11-07 | Jfeスチール株式会社 | フェライト系ステンレス鋼 |
EP3967857A1 (en) * | 2020-01-14 | 2022-03-16 | Hidria d.o.o. | Electrical connection |
FR3107959A1 (fr) * | 2020-03-05 | 2021-09-10 | Safran Aircraft Engines | Procede d’essai de caracterisation d’une eprouvette en materiau composite et installation correspondante |
Citations (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH04224657A (ja) | 1990-12-26 | 1992-08-13 | Kawasaki Steel Corp | 高温強度と溶接熱影響部の靱性に優れたフェライト系ステンレス鋼 |
JPH0570897A (ja) | 1991-09-13 | 1993-03-23 | Kawasaki Steel Corp | 高靱性高温高強度フエライト系ステンレス鋼 |
JPH08104950A (ja) * | 1994-10-04 | 1996-04-23 | Nippon Yakin Kogyo Co Ltd | 連続鋳造性に優れるフェライト系ステンレス鋼およびその製造方法 |
JPH10251759A (ja) * | 1997-03-18 | 1998-09-22 | Kawasaki Steel Corp | 冷間圧延性に優れたフェライト系ステンレス熱延鋼帯の製造方法 |
JP2004218013A (ja) | 2003-01-15 | 2004-08-05 | Sumitomo Metal Ind Ltd | 自動車排気系機器用フェライト系ステンレス鋼 |
JP2008240143A (ja) | 2007-02-26 | 2008-10-09 | Nippon Steel & Sumikin Stainless Steel Corp | 耐熱性に優れたフェライト系ステンレス鋼板 |
JP2009174040A (ja) | 2008-01-28 | 2009-08-06 | Nisshin Steel Co Ltd | Egrクーラー用フェライト系ステンレス鋼およびegrクーラー |
JP2010235994A (ja) * | 2009-03-31 | 2010-10-21 | Jfe Steel Corp | 加工性に優れたフェライト系ステンレス冷延鋼板及びその製造方法 |
JP2012102397A (ja) * | 2010-10-14 | 2012-05-31 | Jfe Steel Corp | 耐熱性と加工性に優れるフェライト系ステンレス鋼 |
Family Cites Families (16)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP3290751B2 (ja) * | 1992-05-21 | 2002-06-10 | 川崎製鉄株式会社 | 高加工性高温高強度フェライト系ステンレス鋼 |
CA2123470C (en) * | 1993-05-19 | 2001-07-03 | Yoshihiro Yazawa | Ferritic stainless steel exhibiting excellent atmospheric corrosion resistance and crevice corrosion resistance |
TW526281B (en) * | 1999-04-30 | 2003-04-01 | Kawasaki Steel Co | Stainless steel material with excellent antibacterial property and process for producing the same |
US6426039B2 (en) * | 2000-07-04 | 2002-07-30 | Kawasaki Steel Corporation | Ferritic stainless steel |
JP4562280B2 (ja) * | 2000-12-25 | 2010-10-13 | 日新製鋼株式会社 | 加工性に優れ面内異方性の小さいフェライト系ステンレス鋼及びその製造方法 |
JP2003313640A (ja) * | 2002-04-25 | 2003-11-06 | Jfe Steel Kk | 耐溶融亜鉛メッキ割れ特性に優れた高強度形鋼およびその製造方法 |
US7732733B2 (en) * | 2005-01-26 | 2010-06-08 | Nippon Welding Rod Co., Ltd. | Ferritic stainless steel welding wire and manufacturing method thereof |
EP1818421A1 (fr) * | 2006-02-08 | 2007-08-15 | UGINE & ALZ FRANCE | Acier inoxydable ferritique dit à 19% de chrome stabilisé au niobium |
JP2007247013A (ja) * | 2006-03-17 | 2007-09-27 | Jfe Steel Kk | 耐酸化性、加工性および高温強度に優れるフェライト系ステンレス鋼 |
JP5002991B2 (ja) * | 2006-03-20 | 2012-08-15 | Jfeスチール株式会社 | 耐面歪み性及び表面性状に優れたフェライト系ステンレス冷延鋼板の製造方法及び被膜鋼板 |
JP2009035756A (ja) * | 2007-07-31 | 2009-02-19 | Nisshin Steel Co Ltd | 高温強度に優れた二輪車排ガス経路部材用Al系めっき鋼板および部材 |
JP5274047B2 (ja) * | 2008-02-23 | 2013-08-28 | 日新製鋼株式会社 | フェライト系ステンレス鋼材およびその製造方法並びに自動車マフラー |
JP4386144B2 (ja) * | 2008-03-07 | 2009-12-16 | Jfeスチール株式会社 | 耐熱性に優れるフェライト系ステンレス鋼 |
JP5239642B2 (ja) * | 2008-08-29 | 2013-07-17 | Jfeスチール株式会社 | 熱疲労特性、高温疲労特性および耐酸化性に優れるフェライト系ステンレス鋼 |
EP2460899A4 (en) * | 2009-07-27 | 2014-07-09 | Nisshin Steel Co Ltd | FERRITIC STAINLESS STEEL FOR EGR COOLER AND EGR COOLER |
CN102234740B (zh) * | 2010-04-22 | 2013-07-17 | 宝山钢铁股份有限公司 | 一种铁素体不锈钢及其冷轧板的制造方法 |
-
2013
- 2013-05-23 MY MYPI2014703518A patent/MY160980A/en unknown
- 2013-05-23 JP JP2013548673A patent/JP5505570B1/ja active Active
- 2013-05-23 US US14/403,687 patent/US20150139851A1/en not_active Abandoned
- 2013-05-23 KR KR1020147032640A patent/KR101956709B1/ko active IP Right Grant
- 2013-05-23 WO PCT/JP2013/003282 patent/WO2013179616A1/ja active Application Filing
- 2013-05-23 ES ES13796603.2T patent/ES2673216T3/es active Active
- 2013-05-23 CN CN201380027852.3A patent/CN104364404B/zh active Active
- 2013-05-23 EP EP13796603.2A patent/EP2857538B1/en active Active
- 2013-05-27 TW TW102118656A patent/TWI503424B/zh not_active IP Right Cessation
Patent Citations (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH04224657A (ja) | 1990-12-26 | 1992-08-13 | Kawasaki Steel Corp | 高温強度と溶接熱影響部の靱性に優れたフェライト系ステンレス鋼 |
JPH0570897A (ja) | 1991-09-13 | 1993-03-23 | Kawasaki Steel Corp | 高靱性高温高強度フエライト系ステンレス鋼 |
JPH08104950A (ja) * | 1994-10-04 | 1996-04-23 | Nippon Yakin Kogyo Co Ltd | 連続鋳造性に優れるフェライト系ステンレス鋼およびその製造方法 |
JPH10251759A (ja) * | 1997-03-18 | 1998-09-22 | Kawasaki Steel Corp | 冷間圧延性に優れたフェライト系ステンレス熱延鋼帯の製造方法 |
JP2004218013A (ja) | 2003-01-15 | 2004-08-05 | Sumitomo Metal Ind Ltd | 自動車排気系機器用フェライト系ステンレス鋼 |
JP2008240143A (ja) | 2007-02-26 | 2008-10-09 | Nippon Steel & Sumikin Stainless Steel Corp | 耐熱性に優れたフェライト系ステンレス鋼板 |
JP2009174040A (ja) | 2008-01-28 | 2009-08-06 | Nisshin Steel Co Ltd | Egrクーラー用フェライト系ステンレス鋼およびegrクーラー |
JP2010235994A (ja) * | 2009-03-31 | 2010-10-21 | Jfe Steel Corp | 加工性に優れたフェライト系ステンレス冷延鋼板及びその製造方法 |
JP2012102397A (ja) * | 2010-10-14 | 2012-05-31 | Jfe Steel Corp | 耐熱性と加工性に優れるフェライト系ステンレス鋼 |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2018116792A1 (ja) * | 2016-12-21 | 2018-06-28 | Jfeスチール株式会社 | フェライト系ステンレス鋼 |
JPWO2018116792A1 (ja) * | 2016-12-21 | 2018-12-20 | Jfeスチール株式会社 | フェライト系ステンレス鋼 |
CN110088324A (zh) * | 2016-12-21 | 2019-08-02 | 杰富意钢铁株式会社 | 铁素体系不锈钢 |
Also Published As
Publication number | Publication date |
---|---|
CN104364404B (zh) | 2020-07-28 |
CN104364404A (zh) | 2015-02-18 |
JPWO2013179616A1 (ja) | 2016-01-18 |
TWI503424B (zh) | 2015-10-11 |
KR20150002872A (ko) | 2015-01-07 |
ES2673216T3 (es) | 2018-06-20 |
KR101956709B1 (ko) | 2019-03-11 |
US20150139851A1 (en) | 2015-05-21 |
EP2857538A4 (en) | 2016-03-23 |
EP2857538A1 (en) | 2015-04-08 |
MY160980A (en) | 2017-03-31 |
JP5505570B1 (ja) | 2014-05-28 |
EP2857538B1 (en) | 2018-04-18 |
TW201410884A (zh) | 2014-03-16 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP5700175B2 (ja) | フェライト系ステンレス鋼 | |
JP5609571B2 (ja) | 耐酸化性に優れたフェライト系ステンレス鋼 | |
JP5304935B2 (ja) | フェライト系ステンレス鋼 | |
JP6075349B2 (ja) | フェライト系ステンレス鋼 | |
TWI460292B (zh) | 肥粒鐵系不銹鋼 | |
JP5505570B1 (ja) | フェライト系ステンレス鋼 | |
JP5152387B2 (ja) | 耐熱性と加工性に優れるフェライト系ステンレス鋼 | |
WO2003106722A1 (ja) | 耐熱性フェライト系ステンレス鋼およびその製造方法 | |
JP6123964B1 (ja) | フェライト系ステンレス鋼 | |
JP6665936B2 (ja) | フェライト系ステンレス鋼 | |
JP5958412B2 (ja) | 熱疲労特性に優れたフェライト系ステンレス鋼 | |
JPWO2019151124A1 (ja) | フェライト系ステンレス鋼 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
ENP | Entry into the national phase |
Ref document number: 2013548673 Country of ref document: JP Kind code of ref document: A |
|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 13796603 Country of ref document: EP Kind code of ref document: A1 |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2013796603 Country of ref document: EP |
|
ENP | Entry into the national phase |
Ref document number: 20147032640 Country of ref document: KR Kind code of ref document: A |
|
WWE | Wipo information: entry into national phase |
Ref document number: 14403687 Country of ref document: US |
|
NENP | Non-entry into the national phase |
Ref country code: DE |