CN110312812A - Ferrite-group stainless steel and automobile exhaust path components ferrite-group stainless steel - Google Patents
Ferrite-group stainless steel and automobile exhaust path components ferrite-group stainless steel Download PDFInfo
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- CN110312812A CN110312812A CN201780083889.6A CN201780083889A CN110312812A CN 110312812 A CN110312812 A CN 110312812A CN 201780083889 A CN201780083889 A CN 201780083889A CN 110312812 A CN110312812 A CN 110312812A
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- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 51
- 239000010935 stainless steel Substances 0.000 title claims description 48
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 22
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 20
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 17
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 17
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 13
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 13
- 229910052802 copper Inorganic materials 0.000 claims abstract description 12
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 12
- 239000012535 impurity Substances 0.000 claims abstract description 7
- 229910052750 molybdenum Inorganic materials 0.000 claims description 8
- 229910052719 titanium Inorganic materials 0.000 claims description 6
- 239000004615 ingredient Substances 0.000 claims description 4
- 229910052698 phosphorus Inorganic materials 0.000 abstract description 6
- 229910052717 sulfur Inorganic materials 0.000 abstract description 6
- 238000007254 oxidation reaction Methods 0.000 description 23
- 229910000831 Steel Inorganic materials 0.000 description 21
- 239000010959 steel Substances 0.000 description 21
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 16
- 238000000034 method Methods 0.000 description 16
- 238000012360 testing method Methods 0.000 description 16
- 230000007423 decrease Effects 0.000 description 15
- 238000010438 heat treatment Methods 0.000 description 15
- 229910000734 martensite Inorganic materials 0.000 description 13
- 230000003647 oxidation Effects 0.000 description 13
- 230000000052 comparative effect Effects 0.000 description 11
- 238000005098 hot rolling Methods 0.000 description 11
- 230000000694 effects Effects 0.000 description 8
- 230000008569 process Effects 0.000 description 6
- 238000009661 fatigue test Methods 0.000 description 5
- 239000000463 material Substances 0.000 description 5
- 229910001566 austenite Inorganic materials 0.000 description 4
- 239000003054 catalyst Substances 0.000 description 4
- 230000008859 change Effects 0.000 description 4
- 238000011156 evaluation Methods 0.000 description 4
- 238000004519 manufacturing process Methods 0.000 description 4
- 230000002411 adverse Effects 0.000 description 3
- 238000000137 annealing Methods 0.000 description 3
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 3
- 230000033228 biological regulation Effects 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 229910052758 niobium Inorganic materials 0.000 description 3
- 229910052760 oxygen Inorganic materials 0.000 description 3
- 239000001301 oxygen Substances 0.000 description 3
- 230000037361 pathway Effects 0.000 description 3
- 230000009467 reduction Effects 0.000 description 3
- 229910052721 tungsten Inorganic materials 0.000 description 3
- 229910052726 zirconium Inorganic materials 0.000 description 3
- 229910000859 α-Fe Inorganic materials 0.000 description 3
- 208000025599 Heat Stress disease Diseases 0.000 description 2
- 239000000654 additive Substances 0.000 description 2
- 230000000996 additive effect Effects 0.000 description 2
- 238000005275 alloying Methods 0.000 description 2
- 238000005097 cold rolling Methods 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 238000000227 grinding Methods 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 238000000465 moulding Methods 0.000 description 2
- 238000005554 pickling Methods 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 238000003825 pressing Methods 0.000 description 2
- 230000002829 reductive effect Effects 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 230000000087 stabilizing effect Effects 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 230000002159 abnormal effect Effects 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 230000002929 anti-fatigue Effects 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 238000002485 combustion reaction Methods 0.000 description 1
- 238000012790 confirmation Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 210000000981 epithelium Anatomy 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 230000014759 maintenance of location Effects 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 238000000746 purification Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 230000002441 reversible effect Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
-
- 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
- C21D8/0221—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
- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—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
- 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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—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
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- 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
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Combustion & Propulsion (AREA)
- General Engineering & Computer Science (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
The present invention relates to a kind of ferrite-group stainless steels, it contains 0.03 mass % C below, the Si of 0.1~0.8 mass %, 1.0 mass % Mn below, 0.04 mass % P below, 0.01 mass % S below, 0.5 mass % Ni below, the Cr of 12.0~15.0 mass %, 0.03 mass % N below, the Nb of 0.1~0.5 mass %, the Cu of 0.8~1.5 mass %, 0.1 mass % Al below, remainder is made of Fe and inevitable impurity, and γ max shown in following formula (1) is 55 or less.γ max=420C-11.5Si+7Mn+23Ni-11.5Cr+470N+9Cu-52Al+189 (1), C, Si, Mn, Ni, Cr, N, Cu and Al refer to the quality % of the element in formula.
Description
Technical field
The present invention relates to a kind of ferrite-group stainless steels and automobile exhaust path components ferrite-group stainless steel.
Background technique
Compared with austenite stainless steel, the thermal expansion coefficient of ferrite-group stainless steel is small, thermal fatigue characteristics and high temperature oxygen
Change excellent, therefore is used for heat-resisting purposes of the thermal deformation as problem.As its representative purposes, exhaust can be enumerated
The automobile exhausts path components such as manifold, front tube, catalyst carrier outer cylinder, central tube, muffler, tail pipe.
Recently, automobile engine is in order to improve exhaust gas purification efficiency and output power, in raising exhaust gas temperature
The trend of degree is (high close to the component special requirement high-fire resistance of engine to exhaust manifold, front tube, catalyst carrier outer cylinder etc.
Warm intensity, high-temperature oxidation).In addition, in recent years, the shape of exhaust pathway component has the tendency that complication.In particular, exhaust
Manifold and catalyst carrier outer cylinder pass through the various method moldings such as mechanical pressing, servo punch forming, rotary pressing processing, hydro-forming
At complicated shape.When shape becomes complexity, the thermal deformation that the starting and stopping of engine are adjoint is concentrated at one, is easy
Under Thermal Fatigue Damage occurs, while the material temperature of part rises, and is also easy to be abnormal oxidation.Therefore, seeking to improve molding
Property aspect, heat resistance cannot be sacrificed.
The ferrite-group stainless steel high as heat resistance, it is known that SUH409L and SUS430J1L.The processability of SUH409L is good
It is good, it is also a large amount of in exhaust pathway component to use.However, not preferably being more than in material temperature if considering its heat resistance level
800 DEG C with using on the way.On the other hand, SUS430J1L has the excellent heat resistance that can also be used at 900 DEG C.So
And since SUS430J1L is hard, it is possible to be difficult to apply in terms of processability.
Therefore, ferrite-group stainless steel as described below is developed.
Patent document 1 proposes following technology: based on the steel of SUS429 system composition, being improved and is added by not adding Nb
Work, while inhibiting the reduction of thermal fatigue characteristics by adding Cu.However, if being kept for a long time in Cu Precipitation Temperature range,
Then the precipitate of Cu can be assembled and become thick, and the improvement effect of elevated temperature strength becomes smaller.Therefore, the heat of the ferrite-group stainless steel is tired
Labor characteristic is likely to decrease.
Patent document 2 proposes following technology: based on the steel of SUS429 system composition, being improved by addition Nb and Cu
Thermal fatigue characteristics, while by improving γ max retained martensitic in slab, to improve slab toughness.However, due to the iron
The γ max high of plain system stainless steel can generate martensitic phase when so such as welding being heated to high temperature, and thermal fatigue characteristics are possible to
Decline.
Existing technical literature
Patent document
Patent document 1: Japanese Unexamined Patent Publication 2012-188748 bulletin
Patent document 2: Japanese Unexamined Patent Publication 2012-007195 bulletin
Summary of the invention
Technical problems to be solved by the inivention
As described above, to the ferrite-group stainless steel for purposes such as automobile exhaust path components, can by it is various at
Type method is processed into complicated shape, it is desirable that can aid in the excellent processability of the design freedom of enlargement part.In addition, right
For the ferrite-group stainless steel of the purposes such as automobile exhaust path components, need that there is excellent heat fatigue at high temperature
Characteristic and oxidation characteristic, therefore it is not intended to heat resistance reduction.However, from above patent document: status is not obtain also
The ferrite-group stainless steel of excellent processability and excellent heat resistance is improved simultaneously.
In addition, as improve processability means, have as general means reduced for the purpose of low alloying Cr and
The method of Si.However, in the method, since γ max rises, so being easy to generate martensitic phase, heat when using at high temperature
Fatigue properties reduce.In addition, high-temperature oxydation characteristic also reduces if reducing Cr and Si.
In addition, as the general means for improving processability, answering when having the heating temperature for reducing slab to increase hot rolling
The method of change, but in this case, it is known that surface quality decline.Moreover, its reason and countermeasure not yet determine.
It is an object of the invention to: a kind of processability and excellent heat resistance, simultaneously surface quality also good iron element are provided
System stainless steel and automobile exhaust path components ferrite-group stainless steel.
The means used to solve the problem
In ferrite-group stainless steel, when reducing Cr and Si to improve processability, γ max can rise, and be easy to generate
Martensitic phase, therefore thermal fatigue characteristics decline.Therefore, in the present invention, generation and the heat for having inquired into γ max and martensitic phase are tired
The relationship of labor characteristic, as a result, it has been found that: if γ max is 55 hereinafter, martensitic phase will not be generated, to thermal fatigue characteristics also without shadow
It rings.
In addition, surface quality can decline in order to improve processability in hot rolling when the heating temperature of reduction slab.Cause
This is conceived to the generation state of the oxide skin when reducing the heating temperature of slab, has carried out various researchs in the present invention.Its
As a result, it has been found that: there is no the oxide skin for equably generating Fe main body in heating of plate blank but be locally generated, this is surface quality
One of the reason of decline.Think in the case where being locally generated the oxide skin of Fe main body, due to Fe main body oxide skin it is thin
Part is contacted with the roller of hot-rolling mill, generates surface defect.Therefore, present inventor has performed further investigations, as a result, it has been found that: it is reducing
In the case where slab heating temperature when hot rolling, Si and Cr have larger impact to the generation of the oxide skin of part.And it is also found that:
By providing the additive amount of Si and Cr, even if reducing the heating temperature of slab, the oxide skin of Fe main body is also equably generated, it can
Improve surface quality when hot rolling.
That is, containing 0.03 mass % C below, 0.1~0.8 matter the present invention relates to a kind of ferrite-group stainless steel
Measure Si, 1.0 mass % Mn below, 0.04 mass % P below, the 0.01 mass % S below, 0.5 mass % or less of %
Ni, 12.0~15.0 mass % Cr, 0.03 mass % N below, the Nb of 0.1~0.5 mass %, 0.8~1.5 mass %
Cu, 0.1 mass % Al below, remainder is made of Fe and inevitable impurity, and γ shown in following (1) formulas
Max is 55 or less.
γ max=420C-11.5Si+7Mn+23Ni-11.5Cr+470N+9Cu-52Al+189 (1)
In formula, C, Si, Mn, Ni, Cr, N, Cu and Al refer to the quality % of the element.
In addition, containing 0.03 matter the invention further relates to a kind of automobile exhaust path components ferrite-group stainless steel
Measure % C below, the Si of 0.1~0.8 mass %, 1.0 mass % Mn below, 0.04 mass % P below, 0.01 mass %
S below, 0.5 mass % Ni below, the Cr of 12.0~15.0 mass %, 0.03 mass % N below, 0.1~0.5 matter
The Nb of %, the Cu of 0.8~1.5 mass %, 0.1 mass % Al below are measured, remainder is by Fe and inevitable impurity structure
At, and γ max shown in following (1) formulas is 55 or less.
γ max=420C-11.5Si+7Mn+23Ni-11.5Cr+470N+9Cu-52Al+189 (1)
In formula, C, Si, Mn, Ni, Cr, N, Cu and Al refer to the quality % of the element.
The effect of invention
According to the present invention it is possible to provide a kind of processability and excellent heat resistance, simultaneously surface quality also good ferrite
It is stainless steel and automobile exhaust path components ferrite-group stainless steel.
Specific embodiment
Ferrite-group stainless steel of the invention contains C, Si, Mn, P, S, Ni, Cr, N, Nb, Cu and Al, and remainder is by Fe
It is constituted with inevitable impurity.In addition, the ferrite-group stainless steel can be also containing in Ti, Mo, V, Zr, W, Co and B
More than one as any ingredient.
Here, in the present specification, for not providing the content of the element of lower limit, indicating that its content can achieve can not be kept away
The impurity level exempted from.
In the following, the restriction reason to each element is illustrated.
C and N is usually seen as to effective elements of elevated temperature strengths such as raising creep strengths.However, if it is superfluous containing C and
N is then easy to generate martensitic phase, and thermal fatigue characteristics, oxidation characteristic and processability can decline.It is used as C and N in addition Nb with carbon
In the steel composition of the fixed element of the form of nitride, need to add the Nb for the amount for meeting C and N concentration, therefore ferrite is not
The cost increase of rust steel.On the other hand, if seeking that C and N is greatly decreased, the burden made steel is excessive, leads to increased costs.Due to
These reasons, in the present invention, C and N provide below 0.03 mass %.In addition, it is contemplated that oxidation characteristic and processability, are wished
Hope C and N below 0.015 mass %.
Si and Cr has larger impact to high-temperature oxydation characteristic and processability.The additive amount of Si and Cr is more, then high temperature oxygen
Changing characteristic becomes better, but processability declines.In addition, become good reverse side in high-temperature oxydation characteristic, when reducing hot rolling
In the case where slab heating temperature, locally generated without equably generating the oxide skin of Fe main body, therefore surface quality
Decline.In order to assign surface quality, it is also desirable to the addition range of strict regulations Si and Cr.Therefore, in order to have both processability, resistance to height
Surface quality when warm oxidation characteristic and hot rolling, Si are defined as 0.1~0.8 mass %, preferably 0.2~0.6 mass %.In addition,
For the same reason, Cr is defined as 12.0~15.0 mass %.
Although Mn is the alloying element for the high-temperature oxydation characteristic, particularly epithelium fissility for improving ferrite-group stainless steel,
If but superfluous addition Mn, processability can be made to deteriorate.In addition, since Mn is austenite phase stabilizing element, in adding for Cr
It in the few steel grade of dosage when superfluous addition Mn, is easy to generate martensitic phase, thermal fatigue characteristics and processability is caused to deteriorate.Therefore,
Mn is defined as 1.0 mass % or less, preferably 0.8 mass % or less.
Since P and S can generate adverse effect to the toughness of high-temperature oxidation and hot rolled plate, it is advantageous to reduce as far as possible
P and S.Therefore, P is defined as 0.04 mass % hereinafter, S is defined as 0.01 mass % or less.
Ni is to the improvement effective element of low-temperature flexibility.However, since Ni is austenite phase stabilizing element, in Cr
Martensitic phase can be generated as Mn when superfluous addition Ni in poor steel grade, decline thermal fatigue characteristics and processability.Separately
Outside, since the price of Ni is high, so should also avoid superfluous addition Ni.Therefore, Ni content regulation is below 0.5 mass %.It is right
The lower limit of Ni content is not particularly limited, but preferably greater than 0 mass %, more preferably 0.01 mass % or more.
Nb fixes C and N in the form of carbonitride, and the remaining solid solution Nb for being fixed with carbonitride shows to improve high
The effect of warm intensity.However, if the Nb of addition excess quantity, processability decline.Therefore, Nb content is defined as 0.1~0.5 matter
Measure %, preferably 0.2~0.4 mass %.
Cu is the element for improving elevated temperature strength.In order to obtain necessary elevated temperature strength, Cu content need 0.8 mass % with
On.However, processability and high temperature oxidation resisting characteristic can decline with the increase of Cu content.Therefore, Cu content be defined as 0.8~
1.5 mass %, preferably 0.9~1.3 mass %.
Al is added in steel-making as deacidification agent, also shows the effect for improving high-temperature oxidation.However, Al
Surplus addition can be such that surface texture declines, and generate adverse effect to processability.Therefore, it is intended that the fewer Al content the better, it is specified that being
0.1 mass % or less, preferably 0.05 mass % or less.
Ti is fixed the solid solution C and N in steel in the form of carbonitride to improve the element of ductility and processability.Separately
Outside, Ti inhibits the intergranular of Cr carbide to be precipitated, also it can be expected that improving corrosion proof effect.However, if the Ti of addition excess quantity,
Cause the surface texture of steel to deteriorate because generating TiN, adverse effect is generated to weldability and low-temperature flexibility.Therefore, according to need
It wants, Ti can be added according to 0.20 mass % or less, preferably 0.1 mass % or less.
Mo, V, Zr, W and Co are the members for improving elevated temperature strength and heat-resistant anti-fatigue characteristic by solution strengthening or precipitation strength
Element.However, the addition of excess quantity can make steel overvulcanization, therefore, as needed, Mo, Zr, W and Co respectively can be according to 0.5
Quality % or less is added, and V is added according to 0.1 mass % or less.
The element of cracking when B is the secondary workability for improving steel, multistage is inhibited to form.However, if superfluous addition B,
Manufacturing and weldability can deteriorate.Therefore, as needed, B can be added according to 0.01 mass % or less.
(1) formula and (2) formula indicate that γ max, γ max are that austenite phase generates index.If γ max is too high, it is easy to generate
Martensitic phase, martensitic phase if it exists, then thermal fatigue characteristics can decline.Therefore, in order not to generating martensitic phase, it is specified that γ max
It is 55 or less.In addition, γ max when (1) formula is without Mo or Ti as any ingredient, and (2) formula is comprising as any
γ max when Mo or Ti of ingredient.
γ max=420C-11.5Si+7Mn+23Ni-11.5Cr+470N+9Cu-52Al+189 (1)
γ max=420C-11.5Si+7Mn+23Ni-11.5Cr+470N+9Cu-12Mo-49Ti-52Al+
189···(2)
Here, in (1) formula and (2) formula, C, Si, Mn, Ni, Cr, N, Cu, Al, Mo and Ti refer to the quality % of the element.
The manufacturing method of ferrite-group stainless steel of the invention is not particularly limited, as long as by successively carrying out following processes
To manufacture: the process that 1~3 hour will be heated at 1000~1250 DEG C according to the slab of regulation method casting；According to rule
Determine the process that method carries out hot rolling；In 900~1100 DEG C of the at a temperature of process annealed；Pickling is carried out, according still further to prescriptive procedure
The process for carrying out cold rolling；And 900~1100 DEG C at a temperature of anneal, then the process for carrying out pickling.
So ferrite-group stainless steel of the invention prepared by operation also can be equal even if reducing the heating temperature of slab
Generate the oxide skin of Fe main body evenly, surface quality when hot rolling is good.In addition, the processability of the ferrite-group stainless steel and resistance to
It is hot also excellent.Therefore, ferrite-group stainless steel of the invention is suitable as heat-resisting ferrite-group stainless steel, particularly automobile
Exhaust pathway component ferrite-group stainless steel.
Embodiment
In the following, further illustrate the present invention by embodiment, but the present invention and it is not limited to the examples restriction.
The various ferrite-group stainless steels melting in steel vacuum melting stoves that will be formed with the steel of table 1, is cast as 30kg's
Steel ingot.Hot rolling, annealing, cold rolling and finishing annealing are successively carried out after steel ingot (slab) to be carried out to heating in 1100 DEG C × 2 hours,
To manufacture the cold rolled annealed plate that plate thickness is 1.5mm.In addition, being forged and being annealed steel ingot, pole annealing has also been manufactured
Material.In table, No.1~No.20 is steel of the present invention, and No.21~No.30 is to compare steel.Wherein, No.21 is comparable to patent
The steel of document 1, and No.22 is comparable to the steel of patent document 2.
Table 1
The confirmation method of the generation state of oxide skin when reducing slab heating temperature is illustrated.
Steel ingot is cut into thick 5mm × wide 25mm × long 35mm, with its surface of the grinding belt grinding of #120, using reappeared with
Pass through observation section after heating in the furnace of the electric furnace of the identical oxygen amount of hot-rolling heating furnace and water vapour amount progress 1000 DEG C × 2 hours
Face confirms the generation state of oxide skin.To equably generate the oxide skin of Fe main body state evaluation be it is good (zero: under
Together), will be locally generated or without generate Fe main body oxide skin state evaluation be it is bad (×: similarly hereinafter).
High-temperature oxidation test and processability evaluation are carried out to the cold rolled annealed plate that plate thickness is 1.5mm.
About high-temperature oxidation test, the test film that size is 25mm × 35mm is made, it is real using electric furnace under air atmosphere
The continuous oxidation test heated in 875 DEG C × 200 hours furnaces is applied, later the weight of measurement test piece.The measurement of oxidation increment
As a result: compared with the weight before test, by weight change in 5mg/cm2Test film below is evaluated as zero, will have and be more than
5mg/cm2Weight change test film be evaluated as ×.
It evaluates about processability, is evaluated by room temperature tension test.JIS13 B test film is made, rolling side is measured
To elongation at break.The test film that elongation at break is 35% or more is evaluated as zero, and by elongation at break less than 35%
Test film be evaluated as ×.
Thermal fatigue test piece is made by pole annealed material, supplies thermal fatigue test.Here, thermal fatigue test piece, which uses, incites somebody to action
The pole annealed material that diameter is 10mm carries out machining, the notch that R=2.83mm is arranged in central portion between datum mark makes directly
Diameter has reached the pole test film of 7mm (length is 15mm between datum mark).In thermal fatigue test, using thermatron,
Heating cooling is carried out with 3 DEG C/sec in the range of 200 DEG C of minimum temperature, 750 DEG C of maximum temperature, while in the minimum and highest temperature
Retention time under degree is set to 30 seconds, recycles in this, as 1.In addition, constraint rate is set as 25% in thermal fatigue test
And implement.25% recurring number is reduced as thermal fatigue life using value of the maximum stress of each circulation when more constant, it will be hot
Fatigue life be 1600 circulation more than test film be evaluated as zero, by less than 1600 recycle test film be evaluated as ×.
Table 2
Evaluation test result
It is as shown in table 2: the ferrite-group stainless steel of example of the present invention the generation state of oxide skin, high-temperature oxydation characteristic,
It is excellent in terms of processability and thermal fatigue characteristics.
In contrast, comparative example 21, Nb without Nb are lower than the comparison of lower limit value lower than the comparative example 24 and Cu of lower limit value
The elevated temperature strength of the ferrite-group stainless steel of example 28 is insufficient, therefore thermal fatigue characteristics decline.Moreover, the ferrite of comparative example 28
It is stainless steel since Cr content is superfluous, so processability declines, while is unevenly generated in heating in 1000 DEG C × 2 hours
The oxide skin of Fe main body.
The ferrite-group stainless steel of comparative example 22 and 23 is since γ max is more than upper limit value, so be easy to generate martensitic phase,
Thermal fatigue characteristics decline.Moreover, the ferrite-group stainless steel of comparative example 23 is since the content of C is more, so processability is also insufficient.
The ferrite-group stainless steel of comparative example 27 is since Ni content and γ max are more than upper limit value, so under thermal fatigue characteristics
Drop, simultaneously because Cr content is few, so high-temperature oxydation characteristic is also insufficient.
The ferrite-group stainless steel of comparative example 25 is since the content of Si is more, so not having in heating in 1000 DEG C × 2 hours
There is the oxide skin for uniformly generating Fe main body, it is more additionally, due to the content of Si and Nb, so processability also declines.
The ferrite-group stainless steel of comparative example 26 is since N and Al is superfluous, so processability declines.
The ferrite-group stainless steel of comparative example 29 is since Si content is few, so high-temperature oxydation characteristic reduces.
The ferrite-group stainless steel of comparative example 30 is since the content of Mn and Cu is superfluous, so high-temperature oxydation characteristic and processability
Decline.
As described above, in the ferrite-group stainless steel of comparative example, the generation state of oxide skin, adds high-temperature oxydation characteristic
Have in work and thermal fatigue characteristics one it is insufficient.
This application claims the priority based on Japanese patent application filed on January 19th, 2017 the 2017-7842nd,
The all content of these Japanese patent applications is quoted in the application.
Practicability in industry
Surface quality, high-temperature oxydation characteristic, processability and the heat fatigue of ferrite-group stainless steel according to the present invention are special
Excellent, the row suitable for the various internal combustion engines headed by automobile such as exhaust manifold, front tube, central tube, catalyst outer cylinder of property
Air-flow circuit unit.
Claims (5)
1. a kind of ferrite-group stainless steel, contains:
C:0.03 mass % or less,
The mass of Si:0.1~0.8 %,
Mn:1.0 mass % or less,
P:0.04 mass % or less,
S:0.01 mass % or less,
Ni:0.5 mass % or less,
The mass of Cr:12.0~15.0 %,
N:0.03 mass % or less,
The mass of Nb:0.1~0.5 %,
The mass of Cu:0.8~1.5 %,
Al:0.1 mass % hereinafter,
Remainder is made of Fe and inevitable impurity, and γ max shown in following (1) formulas be 55 hereinafter,
γ max=420C-11.5Si+7Mn+23Ni-11.5Cr+470N+9Cu-52Al+189 (1)
In formula, C, Si, Mn, Ni, Cr, N, Cu and Al refer to the quality % of the element.
2. ferrite-group stainless steel according to claim 1 also contains selected from one or more of following ingredient:
Ti:0.20 mass % or less,
Mo:0.5 mass % or less,
V:0.1 mass % or less,
Zr:0.5 mass % or less,
W:0.5 mass % or less,
Co:0.5 mass % or less,
B:0.01 mass % hereinafter,
And γ max shown in following (2) formulas be 55 hereinafter,
γ max=420C-11.5Si+7Mn+23Ni-11.5Cr+470N+9Cu-12Mo-49Ti-52Al+ 189
(2)
In formula, C, Si, Mn, Ni, Cr, N, Cu, Mo, Ti and Al refer to the quality % of the element.
3. ferrite-group stainless steel according to claim 1 or 2 uses ferrite-group stainless steel to be heat-resisting.
4. a kind of automobile exhaust path components ferrite-group stainless steel, contains:
C:0.03 mass % or less,
The mass of Si:0.1~0.8 %,
Mn:1.0 mass % or less,
P:0.04 mass % or less,
S:0.01 mass % or less,
Ni:0.5 mass % or less,
The mass of Cr:12.0~15.0 %,
N:0.03 mass % or less,
The mass of Nb:0.1~0.5 %,
The mass of Cu:0.8~1.5 %,
Al:0.1 mass % hereinafter,
Remainder is made of Fe and inevitable impurity, and γ max shown in following (1) formulas be 55 hereinafter,
γ max=420C-11.5Si+7Mn+23Ni-11.5Cr+470N+9Cu-52Al+189 (1)
In formula, C, Si, Mn, Ni, Cr, N, Cu and Al refer to the quality % of the element.
5. automobile exhaust path components ferrite-group stainless steel according to claim 4, also contain selected from as follows at
One or more of point:
Ti:0.20 mass % or less,
Mo:0.5 mass % or less,
V:0.1 mass % or less,
Zr:0.5 mass % or less,
W:0.5 mass % or less,
Co:0.5 mass % or less,
B:0.01 mass % hereinafter,
And γ max shown in following (2) formulas be 55 hereinafter,
γ max=420C-11.5Si+7Mn+23Ni-11.5Cr+470N+9Cu-12Mo-49Ti-52Al+ 189
(2)
In formula, C, Si, Mn, Ni, Cr, N, Cu, Mo, Ti and Al refer to the quality % of the element.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2017007842 | 2017-01-19 | ||
| JP2017-007842 | 2017-01-19 | ||
| PCT/JP2017/031988 WO2018135028A1 (en) | 2017-01-19 | 2017-09-05 | Ferritic stainless steel and ferritic stainless steel for car exhaust gas pathway member |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN110312812A true CN110312812A (en) | 2019-10-08 |
Family
ID=62907853
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201780083889.6A Pending CN110312812A (en) | 2017-01-19 | 2017-09-05 | Ferrite-group stainless steel and automobile exhaust path components ferrite-group stainless steel |
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| Country | Link |
|---|---|
| US (1) | US20190382874A1 (en) |
| EP (1) | EP3572544A4 (en) |
| JP (1) | JP6420494B1 (en) |
| KR (1) | KR20190109464A (en) |
| CN (1) | CN110312812A (en) |
| TW (1) | TWI667357B (en) |
| WO (1) | WO2018135028A1 (en) |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6721705B2 (en) | 2000-02-04 | 2004-04-13 | Webley Systems, Inc. | Robust voice browser system and voice activated device controller |
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Also Published As
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| TW201827623A (en) | 2018-08-01 |
| KR20190109464A (en) | 2019-09-25 |
| JPWO2018135028A1 (en) | 2019-01-24 |
| TWI667357B (en) | 2019-08-01 |
| US20190382874A1 (en) | 2019-12-19 |
| EP3572544A1 (en) | 2019-11-27 |
| EP3572544A4 (en) | 2020-05-20 |
| JP6420494B1 (en) | 2018-11-07 |
| WO2018135028A1 (en) | 2018-07-26 |
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