CN107002192B - High-strength high-tractility steel plate - Google Patents

High-strength high-tractility steel plate Download PDF

Info

Publication number
CN107002192B
CN107002192B CN201580061877.4A CN201580061877A CN107002192B CN 107002192 B CN107002192 B CN 107002192B CN 201580061877 A CN201580061877 A CN 201580061877A CN 107002192 B CN107002192 B CN 107002192B
Authority
CN
China
Prior art keywords
steel plate
carbon
steel
strength
retained austenite
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.)
Expired - Fee Related
Application number
CN201580061877.4A
Other languages
Chinese (zh)
Other versions
CN107002192A (en
Inventor
村上俊夫
大谷茂生
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.)
Kobe Steel Ltd
Original Assignee
Kobe Steel Ltd
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 Kobe Steel Ltd filed Critical Kobe Steel Ltd
Publication of CN107002192A publication Critical patent/CN107002192A/en
Application granted granted Critical
Publication of CN107002192B publication Critical patent/CN107002192B/en
Expired - Fee Related legal-status Critical Current
Anticipated expiration legal-status Critical

Links

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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C21D1/20—Isothermal quenching, e.g. bainitic hardening
    • 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
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment 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
    • C21D8/0205—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
    • 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
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0405—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • 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
    • C22C38/002—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
    • C22C38/02—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
    • C22C38/06—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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing 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
    • 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
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • 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
    • C21D2211/002—Bainite
    • 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
    • C21D2211/008—Martensite
    • 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
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0426—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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0436—Cold rolling

Abstract

A kind of high-strength high-tractility steel plate, it contains individual alloying component, in structure of steel, retained austenite is 8 area % or more in all tissues, surplus is the one or more of bainite, martensite, tempering bainite and tempered martensite, and the average carbon density of the concentration of carbon in retained austenite and the standard deviation of carbon content distribution are respectively at specific range.

Description

High-strength high-tractility steel plate
Technical field
It is in detail to be related to the present invention relates to the high-strength high-tractility steel plate useful as thin steel sheet for automobile etc. The strength ductile balance of steel plate develops skill.
Background technique
Such as in the steel plate used in frame part of automobile etc., with crashworthiness and it is based on the light-weighted drop of car body For the purpose of low oil consumption etc., and further high intensity is required, and in order to be processed into complex-shaped frame part, in addition to requiring Have other than excellent shaping processability, also requires weldability when will engage between component and being assembled into component.It is therefore desirable for opening Send out steel plate such a, the mechanical property as specific requirement is (hereinafter, be also only called " characteristic ".), carbon amounts can be pressed down on one side System in 0.3 mass % hereinafter, ensure on one side yield tensile ratio (YR) be 0.7 or more, tensile strength (TS) × elongation percentage (EL) × extension Flange performance (λ) is 1000000MPa%% or more.
In 980MPa grades or more of high-strength steel sheet, in order to ensure high intensity and high ductibility are existed side by side, effectively Use the TRIP steel and TBF steel etc. that retained austenite bring TRIP effect is utilized.In order to make intensity-extension of these steel Sexual balance further increases, and has carried out various researchs for the amount, average carbon density, form of retained austenite, proposes have more The steel plate of good characteristic (for example, referring to Patent Documents 1 to 3).
For example, in patent document 1, propose there is a kind of thin steel of the high intensity of elongation percentage and stamping excellent in stability Plate, be by the typoiogical classification of the retained austenite in structure of steel at lath-shaped and island when, by the retained austenite of island Ratio is controlled in certain range.Although, can also be real in the art, it is contemplated that other than good elongation percentage at room temperature Good elongation percentage under existing 100~200 DEG C of warm state, but cannot but be substantially ensured effectively as material as collision characteristic The YR of material factor and strength-ductility balanced can not think that it meets above-mentioned requirements level.
In addition, in patent document 2, proposition has a kind of high strength cold rolled steel plate, by improving the Ovshinsky in structure of steel The aggregation degree of the crystalline orientation of body phase significantly improves the uniform elongation relative to rolling direction for 45 ° of directions.But make It is not write out especially for the rolling direction of general ductility evaluation of orientations and the characteristic of rolling right angle orientation, can not think that it is full Sufficient above-mentioned requirements are horizontal.
In addition, propose there is a kind of high-strength steel sheet in patent document 3, it is brilliant by the retained austenite into structure of steel The surface of grain and it is internal assign C concentration difference, so as to improve coating baking hardening and strength-ductility balanced.But this In a little technologies, assign C concentration difference to retained austenite crystal grain, but be with the improvement of coating baking hardening as the main purpose, It is not as the present invention in this way, it, which is intended to, improves stability of retained austenite, improves ductility, and to retained austenite Body assigns the carbon content distribution needed, entirely different in technical idea with the present application.
[existing technical literature]
[patent document]
[patent document 1] Japanese Laid-Open 2012-41573 bulletin
[patent document 2] Japanese Laid-Open 2012-21225 bulletin
[patent document 3] Japanese Laid-Open 2012-31505 bulletin
Summary of the invention
Therefore the object of the present invention is to provide a kind of strength-ductility balanced excellent high-strength high-tractility steel Plate can ensure that yield tensile ratio (YR) is 0.7 or more, and tensile strength (TS) × elongation percentage (EL) × Extending flange Perfor (λ) is 1000000MPa%% or more.
The high-strength high-tractility steel plate of first invention of the invention, which is characterized in that at being grouped as, in terms of quality %, For
C:0.10% or more and lower than 0.35%,
Si+Al:0.5~2.0%,
Mn:1.0~4.0%,
P:0~0.05%,
S:0~0.01%,
Surplus is made of iron and inevitable impurity,
In structure of steel, retained austenite to be calculated as 8% or more relative to the area ratio all organized, surplus by bainite, One or more of martensite, tempering bainite and tempered martensite are constituted, also,
About the concentration of carbon in the retained austenite,
Its average carbon density is 0.9~1.2 mass %,
The standard deviation of its carbon content distribution is 0.35 mass % or more,
Its concentration of carbon is the region of 1.5 mass % or more, to be calculated as 1.0% or more relative to the area ratio all organized.
The high-strength high-tractility steel plate of second invention of the invention, according to above-mentioned first invention, at being grouped as with matter % meter is measured, also the one or more containing Cu, Ni, Mo, Cr and B add up to 1.0% or less.
The high-strength high-tractility steel plate of third invention of the invention, is invented according to the above-mentioned first or second, at being grouped as In terms of quality %, 0.2% or less also is added up to containing one or more of V, Nb, Ti, Zr and Hf.
The high-strength high-tractility steel plate of 4th invention of the invention, according to any one of above-mentioned first~third invention Invention also adds up to 0.01% or less containing one or more of Ca, Mg and REM at being grouped as in terms of quality %.
According to the present invention, not only provide retained austenite amount (the area ratio) and average concentration of carbon, but also control carbon The distribution of concentration shows TRIP phenomenon from the initial stage of deformation to the later period, to realize high work hardening rate, thus, it is possible to provide Strength-ductility balanced excellent high-strength high-tractility steel plate can ensure that yield tensile ratio (YR) is 0.7 or more, and tension is strong Spending (TS) × elongation percentage (EL) × Extending flange Perfor (λ) is 1000000MPa%% or more.
Detailed description of the invention
Fig. 1 is the figure for schematically showing the diffraction peak of the residual γ measured by X-ray diffraction method.
Fig. 2 is the figure for schematically showing the heat treatment condition of high-strength high-tractility steel plate for manufacturing the present invention.
Specific embodiment
In order to solve the above problems, in the steel plate being made of TBF steel, the characteristic mechanical as it is right by the present inventors In that can ensure that yield tensile ratio (YR) is 0.7 or more, tensile strength (TS) × elongation percentage (EL) × Extending flange Perfor (λ) is Various researchs have been repeated in the method for 1000000MPa%% or more.Its result is expected, is studied by thinking below, It can ensure above-mentioned desired characteristic.
That is, in order to make it is strength-ductility balanced further increased than the prior art, need more effectively using promote The retained austenite of TRIP phenomenon is (hereinafter, be also expressed as " residual γ ".).But, go out from the viewpoint for the weldability for ensuring steel plate Hair, because the C content in steel plate there are upper limit restriction, increases the average carbon density for remaining γ amount and remaining in γ by presence Limitation.
Therefore, the present inventors are conceived to the carbon content distribution in residual γ.That is, reaching height to utilize TRIP phenomenon Intensity and high ductibility, it is important that high work hardening rate is realized from the initial stage of deformation to mid-term, for this reason, it may be necessary to which concentration of carbon is low Unstable residual gamma portion exists.On the other hand, when deflection becomes larger, in order to still maintain high processing in the later period of deformation Hardening ratio needs to create the high stable residual γ of concentration of carbon.
It in short, residual γ is only stability height, or is only that stability is low all not all right, it is important that stability, i.e. concentration of carbon Widely distributed presence.
The present inventors are based on above-mentioned cognition further progress research as a result, completing the present invention.
Hereinafter, high-strength high-tractility steel plate of the invention to imparting first is (hereinafter also referred to as " steel plate of the present invention ".) with The structure of steel (hereinafter simply referred to as " tissue " of feature.) be illustrated.
(structure of steel of steel plate of the present invention)
As above-mentioned, steel plate of the present invention contains defined concentration of carbon in specified amount based on the tissue of TBF steel, but especially On this point of remaining γ aspect, controlling the carbon content distribution in residual γ, it is different from the above-mentioned prior art.
< retained austenite: being 8% or more > relative to the area ratio all organized
It is useful for the raising of ductility to remain γ, in order to effectively play such effect, needs to be allowed to relative to complete There are 8% or more, preferably 9% or more, more preferably 10% or more for the area ratio of portion's tissue.In addition, the area ratio of residual γ Preferably 20% hereinafter, more preferably 18% hereinafter, particularly preferably 16% or less.
< surplus: bainite, martensite, tempering bainite and tempered martensite one or more kinds of >
Ferritic generation is prevented, using as fine and the bainite and martensite uniformly organized, and/or its tempering group Texture builds parent phase, using the miniaturization of parent phase tissue, it is possible thereby to which anti-deformation when by low load realizes that yield strength YS's is upper It rises.
< remains the average carbon density (%C in γγR): 0.9~1.2 mass % >
%CγRResidual γ phase is influenced when being deformation becomes the index of stability of martensite.If %CγRIt is too low, then remain γ It is unstable, therefore after application stress, processing strain induced martensite phase transformation occurs before plastic deformation, therefore what cannot be required prolongs Stretch rate.On the other hand, if %CγRExcessively high, then remaining γ becomes excessively stable, even if applying processing, processing will not occur and lure Send out martensitic traoformation, therefore the Extending flange Perfor that still cannot be required.Required elongation percentage in order to obtain, %CγRIt needs It to be 0.9~1.2 mass %.%CγRPreferred lower limit be 1.0 mass %.
< remains the standard deviation of the carbon content distribution in γ: the 0.35 above > of mass %
This is the concentration of carbon point in order to maintain work hardening rate from the initial stage of deformation to later period height, in extension residual γ Cloth, to create the different residual γ of stability.In order to effectively play such effect, need to remain the concentration of carbon point in γ The standard deviation of cloth is 0.35 mass % or more, preferably 0.40 mass % or more, more preferably 0.45 mass % or more.Also Have, in high-strength high-tractility steel plate of the invention, remains the standard deviation of the carbon content distribution in γ actually with 0.70 Quality % or so is the upper limit, preferably 0.65 mass % or less.
< remains the region that the concentration of carbon in γ is 1.5 mass % or more: being 1.0% relative to the area ratio all organized The above >
In order to improve elongation percentage, it is important that the stability of residual γ when dependent variable increases is high, for this purpose, the carbon that is only averaged Concentration is high simultaneously insufficient, but needs stability high, i.e. there are more than a certain amount of by the high residual γ of concentration of carbon.Specifically, The region of 1.5 mass % of concentration of carbon Ga or more in residual γ is needed relative to the area ratio all organized there are 1.0% or more, Preferably 1.5% or more, more preferably 2.0% or more.In addition, remaining γ in high-strength high-tractility steel plate of the invention In concentration of carbon be 1.5 mass % or more region relative to the area ratio all organized, it is left with all remain γ areas 1/2 The right side is the upper limit, and preferably 2/5 hereinafter, more preferably 1/3 or less.
(the area ratio of residual γ, remains the average carbon density (%C in γγR) and the carbon content distribution each measurement side Method)
Here, for the area ratio, the average carbon density (%C that remain γγR) and carbon content distribution each measurement method carry out Explanation.
The area ratio (V about residual γγR) and average carbon density (%CγR), after being ground to 1/4 thickness of steel plate, Through after chemical grinding No.7, p.776 by X-ray diffraction method measurement (ISIJ Int.Vol.33, (1933)).In addition, at this In invention, as X-ray diffraction device, use (strain) リ ガ Network two dimension zone X ray detecting diffraction device (RINT-RAPIDII), Co-K alpha ray is used as X-ray.
In addition, nital corrosion is carried out to steel plate, about the tissue other than residual γ with optical microscopy (400 times of multiplying power) observation distinguishes the tissue other than residual γ.
Then, the distribution about the concentration of carbon in residual γ, uses (200) measured by above-mentioned X-ray diffraction device γ, (220) γ and this 3 diffraction peaks of (311) γ, are acquired as follows.
Firstly, as shown in the schematic of Figure 1, in (200) γ, (220) γ and this 3 diffraction peaks of (311) γ, respectively Acquire maximum 2 θ (2 θ of diffracted intensityavgAnd its 2 θ of half breadth Δ (hkl) (hkl)).Here, (hkl) mean (200), (220) or (311) (similarly hereinafter.).
Secondly, by above-mentioned 2 θavg(hkl), using Bragg condition: λ=2dsin θ (d: diffraction lattice constant, λ: Co-K α The wavelength of ray), according to the following formula (1), acquire d (hkl).
D (hkl)=λ/{ 2sin (2 θavg(hkl)/2) } ... formula (1)
Then, according to the following formula (3), crystal lattice constant a is acquired0(hkl), by this 3 crystal lattice constant a0(hkl) make Crystal lattice constant a is acquired for arithmetic average0。
Then, using formula (Dyson D.J., the Holmes B. (1970), " Effect of of Dyson shown in following formula (3) Alloying additions on the lattice parameter austenite ", J.Iron Steel Inst., 208:469-474.), acquire concentration of carbon %Cavg(unit: quality %).(in addition, concentration of carbon %CavgIt is only used as providing The index of carbon content distribution uses, the above-mentioned average carbon density %C for annotating and separately measuring in advanceγRIt strictly speaking may not one It causes.)
%Cavg=(1/0.033) (a0- 0.0012%Mn+0.00157%Si-0.0056%Al) ... formula (3)
Here, %Mn, %Si, %Al are the content (quality %) of Mn, Si, Al in steel plate respectively.
Next, acquiring the half breadth Δ %C of the carbon content distribution in residual γ according to the following steps.
Firstly, following formula (4) and (5), acquire the upper of 2 θ of half breadth Δ (hkl) of 2 θ of angle of diffraction (hkl) at each peak The angle of diffraction (referring to Fig.1) of lower limit.
2θL(hkl)=2 θavg(hkl)-Δ 2 θ (hkl)/2 ... formula (4)
2θH(hkl)=2 θavg(hkl)+Δ 2 θ (hkl)/2 ... formula (5)
Therefore, above-mentioned 2 θ is used respectivelyL(hkl) and 2 θH(hkl), with above-mentioned same step, using Bragg condition and Above-mentioned formula (1)~(3), acquire the upper lower limit value %C of the half breadth of carbon content distributionLAnd %CH.Then, (6) are asked according to the following formula Obtain the half breadth Δ %C of carbon content distribution.
Δ %C=%CH- %CL... formula (6)
Then, it is assumed that carbon content distribution is normal distribution, as follows, calculates standard by above-mentioned half breadth Δ %C Deviations %C.
That is, the probability density function f (x) of normal distribution is indicated according to average value u and standard deviation by following formula (7).
Probability f (u) in average value is that x=u is substituted into above-mentioned formula (7), is acquired by following formula (8).
Then, from average value u=%CavgOnly move up and down the 1/2 value (%C of half breadth Δ %Cavg± Δ %C/2) Probability density f (%Cavg± Δ %C/2), become average value u=%CavgProbability density f (u)=f (%Cavg) 1/2, Therefore by formula (7) and (8), the relationship of following formula (9) can be obtained.
As above-mentioned formula (9) is deformed, to acquire standard deviation by half breadth Δ %C%CFormula, following formula can be imported (10), half breadth Δ %C is substituted into the formula (10), calculates standard deviation%C。
Then, using the average value %C of the carbon content distribution in the residual γ acquired as described soavgAnd σ%C, utilize Cumulative distribution function g (x) shown in following formula (11) acquires the region that concentration of carbon is 1.5 mass % or more, relative to whole tissues The area ratio VγR(C >=1.5%) exports following formula (12) as its formula, calculates V using the formula (12)γR(C >=1.5%).
Here, VγRIt is the area ratio of all residual γ.
Next, for constituting being illustrated at being grouped as steel plate of the present invention.Hereinafter, the unit of chemical component is entirely Quality %.In addition, it is " amount " that " content " of each ingredient, which also only describes,.
(steel plate of the present invention at be grouped as)
C:0.10% or more is simultaneously lower than 0.35%
C facilitates the amount (the area ratio) for ensuring retained austenite, is for ensuring that intensity and the necessary element of ductility.For Such effect is effectively played, needs C is made to contain 0.10% or more, preferably 0.12% or more, more preferably 0.14% More than.But if C amount becomes superfluous, deteriorate weldability, therefore C amount is lower than 0.35%, preferably 0.32% hereinafter, more Preferably 0.30% hereinafter, further preferably 0.28% or less.
Si+Al:0.5~2.0%
Si and Al is to effectively inhibit retained austenite decomposition, the element that carbide generates.In order to effectively play in this way Effect, need to make Si and Al total containing 0.5% or more, preferably 0.7% or more, more preferably 0.9% or more.But Even if excessively containing Si and Al, said effect is also saturation, not only economically causes to waste, but also cause red brittleness, Sl It is 2.0% hereinafter, preferably 1.9% hereinafter, more preferably 1.8% or less with the total amount of Al.
Mn:1.0~4.0%
Mn makes stabilization of austenite, is element required for for obtaining desired retained austenite.In order to effectively send out Such effect is waved, needs that Mn is made to contain 1.0% or more, preferably 1.3% or more, more preferably 1.6% or more.But if Mn amount becomes superfluous, then, it is seen that adverse effect occurs etc. for slab crackle, therefore Mn amount for 4.0% hereinafter, preferably 3.5% with Under, more preferably 3.0% or less.
P:0~0.05%
P is inevitably present as impurity element, but in order to ensure desired residual γ, can also be allowed to containing Element.But if containing P excessively, secondary workability deterioration, therefore P amount for 0.05% hereinafter, preferably 0.03% with Under, more preferably 0.02% or less.
S:0~0.01%
S is also inevitably present as impurity element, forms the sulfide-based field trash of MnS etc., is to become crackle Starting point and make processability deteriorate element, therefore S amount be 0.01% hereinafter, preferably 0.005% hereinafter, be more preferably 0.003% or less.
Steel of the invention contains using above-mentioned element as necessary ingredient, and surplus is iron and inevitable impurity, in addition, In the range for not damaging effect of the invention, permission ingredient below can be made to contain.
The one or more of Cu, Ni, Mo, Cr and B: total 1.0% or less
These elements are useful as the intensified element of steel, and ensure it is to have for the stabilisation and specified amount that remain γ The element of effect.In order to effectively play such effect, recommending these element total amounts is 0.001% or more, more recommends to be allowed to Contain 0.01% or more.But even if these elements excessively contain, said effect is also saturation, economically causes to waste, Therefore preferably these element total amounts are 1.0% hereinafter, more preferably 0.5% or less.
V, the one or more of Nb, Ti, Zr and Hf: total 0.2% or less
These yuan are known as the effect of precipitation strength and tissue miniaturization, are useful elements to high intensity.In order to effective Ground plays such effect, and recommendation makes these 0.01% or more element total amounts, more recommends to be allowed to containing 0.02% or more.But It is that, even if these elements excessively contain, said effect is also saturation, economically causes to waste, therefore these elements are total Amount preferably 0.2% is hereinafter, more preferably 0.1% or less.
The one or more of Ca, Mg and REM: total 0.01% or less
The form of sulfide in these control of element steel is effective element for improving processability.Here, as being used for REM (rare earth element) of the invention, can enumerate Sc, Y, lanthanide series etc..In order to effectively play above-mentioned effect, recommendation makes this A little element total amounts are 0.001% or more, more recommend to be allowed to containing 0.002% or more.But even if these elements excessively contain Have, said effect is also saturation, economically causes to waste, therefore preferably these element total amounts are 0.01% hereinafter, more excellent It is selected as 0.005% or less.
Then, illustrate the preferred manufacturing condition for obtaining aforementioned present invention steel plate below.
(the preferred manufacturing method of steel plate of the present invention)
Steel plate of the present invention can carry out hot rolling to the steel for meeting mentioned component composition, then after cold rolling, such as with following Process (1)~(4) condition be heat-treated and manufacture (referring to Fig. 2).
[heat treatment condition]
(1) cold-reduced sheet is heated to second heating temperature T2:[0.7 × Ac1+0.3 × Ac3]~[0.2 × Ac1+0.8 × Ac3], the second retention time t2:5s or more is kept at this temperature, alternatively, with 4 DEG C/s average heating rate below in equality of temperature After spending range heating,
(2) it is again heated to T3:[Ac3+10 DEG C of third heating temperature]~950 DEG C, when keeping third to keep at this temperature Between after t3:180s or less,
(3) with CR1:20 DEG C/s or more of average cooling rate, after being cooled to 500 DEG C from above-mentioned third heating temperature T3,
(4) cold after keeping austempering retention time t4:10s or more with austempering temperature T4:350~480 DEG C But to room temperature.
Hereinafter, being illustrated for the rationale for the recommendation of above-mentioned heat treatment condition.
< (1) is with second heating temperature T2:[0.7 × Ac1+0.3 × Ac3]~[0.2 × Ac1+0.8 × Ac3] keep the Two retention time t2:5s or more, alternatively, heating > in synthermal range with 4 DEG C/s average heating rate below
It is kept in two phase region temperature region of ferrite/austenite with the stipulated time or delays heating, in the two phase regions temperature Region occurs that the distribution of Mn concentration in reverse transformation, this is to increase when the austempering in above-mentioned operation (4) is handled The speed difference of the part of bainitic transformation, extension remain the carbon content distribution in γ.
The retention time t2 of the temperature range is more preferably 10s or more, further preferably 20s or more, from productivity Viewpoint, which is set out, is recommended as 200s or less.
In addition, Ac1 and Ac3 can be write according to the chemical component of steel plate using Lesley, and " iron Steel material science ", good fortune field Cheng Jingyi, Wan Shan Co., Ltd., 1985, p.273 the formula acquired.
< (2) is heated with third keep T3:[Ac3+10 DEG C of temperature again]~950 DEG C of holding third retention time t3:180s Following >
This be in order to by austenite one phase domain temperature region keep, make tissue become austenite one phase tissue, thus Remaining ferrite when preventing cooling later.
If third heating temperature T3 is lower than [Ac3+10 DEG C], ferrite remaining, the cooling of above-mentioned operation (3) behind It cannot inhibit ferritic growth in the process, ferrite is excessively formed.On the other hand, if third heating temperature T3 is higher than 950 DEG C or third retention time t3 be higher than 180s, then with above-mentioned operation (1) two phase regions heat when be distributed Mn homogenization, cannot Carbon content distribution in extension residual γ.
< (3) is cooled to 500 DEG C of > with HR1:20 DEG C/s or more of average cooling rate, from third heating temperature T3
This is ferritic formation in order to prevent, becomes the tissue of bayesian phosphor bodies.
The average cooling rate HR3 of the temperature range, more preferably 25 DEG C/s or more, further preferably 30 DEG C/s with On.
After < (4) keeps austempering retention time t4:10s or more with austempering temperature T4:350~480 DEG C, It is cooled to room temperature >
This is to be thickened carbon to non-transformed austenite to promote bainitic transformation, to obtain stable residual γ.
[variation of heat treatment condition]
In addition, above-mentioned operation (1) can also be constituted in the way of following processes (1a).
Cold-reduced sheet is heated to T1:[Ac1-100 DEG C of the first heating temperature by (1a)]~[Ac1-30 DEG C], at this temperature Kept for the first retention time: 10s or more, alternatively, after synthermal range is with 2 DEG C/s average heating rate's heating below, with Second heating temperature T2:[0.7 × Ac1+0.3 × Ac3]~the second retention time t2:5s of [0.2 × Ac1+0.8 × Ac3] holding More than.
In this way, being kept for stipulated time or slow heating in two phase region temperature region of ferrite/cementite in advance, first make Mn to infiltration It being thickened in carbon body, two phase region of ferrite/austenite behind promotes the Mn concentration distribution between ferrite/austenite when heating, So as to increase the local speed difference of the bainitic transformation when processing of the austempering in above-mentioned operation (4), further Carbon content distribution in extension residual γ.
In addition, above-mentioned operation (4) can also be constituted in the way of following processes (4a).
After (4a) keeps austempering retention time t4:10s or more with austempering temperature T4:350~480 DEG C, Relation reheating temperature T5:500~600 DEG C are again heated to, are kept after reheating retention time t5:30s or less with this temperature, cooling chamber Temperature.
In this way, steel plate of the present invention, it is again heated to the residual not resolvent temperature field of γ and makes coating alloying, it also can be at For plated steel sheet.
Hereinafter, enumerating embodiment further illustrates the present invention, but the present invention is not limited certainly by following embodiments, in energy Before enough meeting in the range of aftermentioned objective, naturally it is also possible to suitably be changed implementation, these are all contained in of the invention In technical scope.
[embodiment]
After the steel of ingredient shown in vacuum melting manufacture following table 1, become the steel plate of plate thickness 30mm through being hot-forged, then Implement hot rolling.Although the condition of hot rolling will not cause influence substantially to the final tissue and characteristic of steel plate of the present invention, at this It in embodiment, after being heated to 1200 DEG C, is rolled by multistage, plate thickness is become with 880 DEG C of end temperature of condition of hot rolling 2.5mm.Thereafter, 500 DEG C are cooled to the cooling velocity of 30 DEG C/s and stop cooling down, after being inserted into the furnace for be heated to 500 DEG C Holding 30min, followed by furnace are cold and become hot rolled plate.To hot rolled plate implementation pickling, after the oxide skin for removing surface, implement 1.4mm is cold-rolled to as cold-reduced sheet.
Then, using above-mentioned cold-reduced sheet as raw material, implement to be heat-treated by condition shown in following table 2.In addition, from room temperature Average heating rate to initial heating temperature (keeping temperature) is fixed as 10 DEG C/s, until subsequent heating temperature (keeps temperature Degree) average heating rate be fixed as 20 DEG C/s, to followed by the average heating rate of heating temperature (holding temperature) fix For 10 DEG C/s.In addition, 10 DEG C/s is fixed as from austempering temperature T4 to the average heating rate of relation reheating temperature T5, from Austria Family name body tempering temperature T4 or the average cooling rate of relation reheating temperature T5 to room temperature are fixed as 10 DEG C/s.
[table 1]
(underscore: outside the scope of the present invention-: it is no added)
[table 2]
(outside underscore=the scope of the present invention, outside *=recommended range ,-: it is not applicable)
For each steel plate after above-mentioned heat treatment, by the measurement method illustrated in above-mentioned [specific embodiment] one, The area ratio of measurement residual γ, average carbon density (C γ R) and its carbon content distribution in residual γ.
In addition, the tissue of the steel plate used in the present embodiment, the surplus in addition to retained austenite and ferrite, all It is to be made of one or more of bainite, martensite, tempering bainite and tempered martensite, therefore in following tables In 3, retained austenite and ferritic the area ratio are only described.
In addition, evaluation is strength-ductility balanced in order to for each steel plate after above-mentioned heat treatment, pass through tension test, surveys Measure yield strength YS, tensile strength TS and elongation percentage (breaking elongation) EL.In addition, making JIS 5 tests in tension test Piece, it then follows JIS Z 2241 is implemented.In addition, in order to evaluate the Extending flange Perfor λ of each steel plate, according to Tie Gang alliance, Japan specification JFST1001 measures hole expansibility.
Measurement result is shown in following Table 3.In same table, in the characteristic of the steel plate after above-mentioned heat treatment, yield tensile ratio (YR) be 0.7 or more, tensile strength (TS) × elongation percentage (EL) × Extending flange Perfor (λ) be 1000000MPa%% with On qualification (zero), herein other than unqualified (×).
(outside underscore=the scope of the present invention, *=refined is recommended outside range, α=ferrite)
[table 3]
As shown in Table 3 above, steel No.3,4,9~11,14,18~27 as invention steel (being evaluated as zero), using full The steel grade of important document as defined in foot ingredient of the invention, is heat-treated, as a result, making tissue of the invention with the condition of recommendation The invention steel of defined important document abundance is able to confirm that its mechanical characteristic meets criterion of acceptability, can obtain strength-ductility The strong ductile steel sheet of high intensity of balancing good.
In contrast, as steel No.1,2,5~8,12,13,15~17 of comparing steel (being evaluated as ×), it is of the invention Ingredient provide and the important document of organization prescribed at least any one is inadequate, characteristic is unsatisfactory for criterion of acceptability.
That is, steel No.1,2,5~8,12, although using the steel grade for meeting important document as defined in ingredient of the invention, It is manufactured under conditions of being partially disengaged the manufacturing condition of recommendation, therefore the important document of organization prescribed is inadequate, characteristic is poor.
On the other hand, although steel No.13,15~17 are with the manufacturing condition manufacture of recommendation, use is partially disengaged this hair The steel grade of important document as defined in bright ingredient, therefore the important document of organization prescribed is inadequate, characteristic is poor.
By that can confirm applicability of the invention above.
In detail and the present invention is illustrated referring to specific embodiment, but do not depart from the spirit and scope of the present invention to add With various changes and modifications, this will be apparent that for practitioner.
The application based on Japanese patent application (patent application 2014-238710) filed on November 26th, 2014, in Hold in this as reference and is incorporated into.
[industrial availability]
About steel plate of the invention, intensity and ductility balanced excellent is useful to automobile sheet metal etc..

Claims (2)

1. a kind of high-strength high-tractility steel plate, which is characterized in that be calculated as at being grouped as with quality %
C:0.10% or more and lower than 0.35%,
Si+Al:0.5~2.0%,
Mn:1.0~4.0%,
P:0~0.05%,
S:0~0.01%,
Surplus is made of iron and inevitable impurity,
In structure of steel, retained austenite be calculated as relative to the area ratio all organized 8% or more 20% hereinafter, surplus by bayesian One or more of body, martensite, tempering bainite and tempered martensite are constituted, also,
About the concentration of carbon in the retained austenite,
Its average carbon density is 0.9~1.2 mass %,
The standard deviation of its carbon content distribution be 0.35 mass % or more, 0.70 mass % hereinafter,
Its concentration of carbon is the region of 1.5 mass % or more to be calculated as 1.0% or more relative to the area ratio all organized and with complete The 1/2 of portion's retained austenite bulk area is the upper limit.
2. high-strength high-tractility steel plate according to claim 1, wherein at being grouped as in terms of quality %, under also containing State any one in (a)~(c):
(a) one or more of Cu, Ni, Mo, Cr and B add up to 1.0% or less；
(b) one or more of V, Nb, Ti, Zr and Hf add up to 0.2% or less；
(c) one or more of Ca, Mg and REM add up to 0.01% or less.
CN201580061877.4A 2014-11-26 2015-11-25 High-strength high-tractility steel plate Expired - Fee Related CN107002192B (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
JP2014238710A JP6282577B2 (en) 2014-11-26 2014-11-26 High strength high ductility steel sheet
JP2014-238710 2014-11-26
PCT/JP2015/083078 WO2016084847A1 (en) 2014-11-26 2015-11-25 High-strength high-ductility steel sheet

Publications (2)

Publication Number Publication Date
CN107002192A CN107002192A (en) 2017-08-01
CN107002192B true CN107002192B (en) 2019-03-08

Family

ID=56074399

Family Applications (1)

Application Number Title Priority Date Filing Date
CN201580061877.4A Expired - Fee Related CN107002192B (en) 2014-11-26 2015-11-25 High-strength high-tractility steel plate

Country Status (6)

Country Link
US (1) US20170268077A1 (en)
EP (1) EP3225708A4 (en)
JP (1) JP6282577B2 (en)
KR (1) KR102111921B1 (en)
CN (1) CN107002192B (en)
WO (1) WO2016084847A1 (en)

Families Citing this family (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2017208763A1 (en) * 2016-05-30 2017-12-07 株式会社神戸製鋼所 High-strength steel sheet and method for producing same
CN108018484B (en) * 2016-10-31 2020-01-31 宝山钢铁股份有限公司 Cold-rolled high-strength steel having tensile strength of 1500MPa or more and excellent formability, and method for producing same
WO2018115936A1 (en) * 2016-12-21 2018-06-28 Arcelormittal Tempered and coated steel sheet having excellent formability and a method of manufacturing the same
WO2018115933A1 (en) 2016-12-21 2018-06-28 Arcelormittal High-strength cold rolled steel sheet having high formability and a method of manufacturing thereof
JP6860420B2 (en) * 2017-05-24 2021-04-14 株式会社神戸製鋼所 High-strength steel sheet and its manufacturing method
JP6849536B2 (en) * 2017-05-31 2021-03-24 株式会社神戸製鋼所 High-strength steel sheet and its manufacturing method
ES2921013T3 (en) * 2017-09-28 2022-08-16 Thyssenkrupp Steel Europe Ag Flat steel product and process for its manufacture
CN113316656B (en) * 2019-01-18 2022-11-04 杰富意钢铁株式会社 High-strength hot-dip galvanized steel sheet and method for producing same
CN114746584A (en) * 2019-12-20 2022-07-12 日本制铁株式会社 Ni-plated steel sheet and method for producing Ni-plated steel sheet
CN113308593B (en) * 2021-05-28 2022-08-09 四川大学 Carbon distribution and two-step isothermal quenching based medium carbon silicon manganese low alloy steel heat treatment process
CN114908287B (en) * 2022-04-11 2023-04-14 武汉科技大学 Low-alloy lightweight high-strength automobile steel and production method thereof

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101155940A (en) * 2005-03-30 2008-04-02 株式会社神户制钢所 High strength cold rolled steel sheet and plated steel sheet excellent in the balance of strength and workability
JP2010065272A (en) * 2008-09-10 2010-03-25 Jfe Steel Corp High-strength steel sheet and method for manufacturing the same
JP2010285636A (en) * 2009-06-09 2010-12-24 Kobe Steel Ltd High-strength cold-rolled steel sheet having elongation, stretch-flange formability and weldability
CN102149840A (en) * 2008-09-10 2011-08-10 杰富意钢铁株式会社 High-strength steel plate and manufacturing method thereof
JP2011157583A (en) * 2010-01-29 2011-08-18 Kobe Steel Ltd High-strength cold-rolled steel sheet excellent in workability and method for manufacturing the same
CN102770571A (en) * 2010-01-29 2012-11-07 新日本制铁株式会社 Steel sheet and process for producing steel sheet

Family Cites Families (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20060011274A1 (en) * 2002-09-04 2006-01-19 Colorado School Of Mines Method for producing steel with retained austenite
JP4109619B2 (en) * 2003-12-16 2008-07-02 株式会社神戸製鋼所 High strength steel plate with excellent elongation and stretch flangeability
JP2005336526A (en) * 2004-05-25 2005-12-08 Kobe Steel Ltd High strength steel sheet having excellent workability and its production method
JP5365112B2 (en) * 2008-09-10 2013-12-11 Ｊｆｅスチール株式会社 High strength steel plate and manufacturing method thereof
JP5807368B2 (en) 2010-06-16 2015-11-10 新日鐵住金株式会社 High-strength cold-rolled steel sheet having a very high uniform elongation in the direction of 45 ° with respect to the rolling direction and a method for producing the same
JP5589925B2 (en) 2010-06-28 2014-09-17 新日鐵住金株式会社 High-strength thin steel sheet with excellent elongation and uniform paint bake-hardening performance and method for producing the same
JP5719545B2 (en) 2010-08-13 2015-05-20 新日鐵住金株式会社 High strength thin steel sheet with excellent elongation and press forming stability
JP5825205B2 (en) * 2011-07-06 2015-12-02 新日鐵住金株式会社 Cold rolled steel sheet manufacturing method
JP5632904B2 (en) * 2012-03-29 2014-11-26 株式会社神戸製鋼所 Manufacturing method of high-strength cold-rolled steel sheet with excellent workability

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101155940A (en) * 2005-03-30 2008-04-02 株式会社神户制钢所 High strength cold rolled steel sheet and plated steel sheet excellent in the balance of strength and workability
JP2010065272A (en) * 2008-09-10 2010-03-25 Jfe Steel Corp High-strength steel sheet and method for manufacturing the same
CN102149840A (en) * 2008-09-10 2011-08-10 杰富意钢铁株式会社 High-strength steel plate and manufacturing method thereof
JP2010285636A (en) * 2009-06-09 2010-12-24 Kobe Steel Ltd High-strength cold-rolled steel sheet having elongation, stretch-flange formability and weldability
JP2011157583A (en) * 2010-01-29 2011-08-18 Kobe Steel Ltd High-strength cold-rolled steel sheet excellent in workability and method for manufacturing the same
CN102770571A (en) * 2010-01-29 2012-11-07 新日本制铁株式会社 Steel sheet and process for producing steel sheet

Also Published As

Publication number Publication date
EP3225708A1 (en) 2017-10-04
JP2016098427A (en) 2016-05-30
KR102111921B1 (en) 2020-05-18
US20170268077A1 (en) 2017-09-21
CN107002192A (en) 2017-08-01
EP3225708A4 (en) 2018-05-02
KR20170070230A (en) 2017-06-21
WO2016084847A1 (en) 2016-06-02
JP6282577B2 (en) 2018-02-21

Similar Documents

Publication Publication Date Title
CN107002192B (en) High-strength high-tractility steel plate
CN105492643B (en) High strength cold rolled steel plate and its manufacture method
CN103403210B (en) The high tensile steel plate of the deep drawing quality excellence under room temperature and warm state and warm working method thereof
US11193180B2 (en) High-strength steel sheet and method for manufacturing the same
JP5860308B2 (en) High strength steel plate with excellent warm formability and method for producing the same
CN105940134B (en) High strength cold rolled steel plate and its manufacture method
CN101460647B (en) High-strength steel sheets and processes for production of the same
CN106574319B (en) High-strength steel sheet and its manufacturing method
CN104736736B (en) High strength cold rolled steel plate and its manufacture method
CN104471093B (en) Yield strength and the high strength hot dip galvanized steel sheet having excellent formability and manufacture method thereof
US10590504B2 (en) High-strength cold-rolled steel sheet and method for manufacturing the same
KR101532492B1 (en) High-strength steel plate with excellent formability, warm working method, and warm-worked automotive part
US9914988B2 (en) High-strength cold-rolled steel sheet with high yield ratio having excellent formability and method for producing the same
CN107532266A (en) Coated steel sheet
US10253387B2 (en) Hot-pressed steel sheet member, method of manufacturing the same, and steel sheet for hot pressing
CN106574342A (en) High-strength steel sheet and production method for same, and production method for high-strength galvanized steel sheet
JP2018500465A (en) Method for producing high-strength steel product and steel product obtained thereby
WO2017026125A1 (en) Material for high-strength steel sheet, hot rolled material for high-strength steel sheet, material annealed after hot rolling and for high-strength steel sheet, high-strength steel sheet, high-strength hot-dip plated steel sheet, high-strength electroplated steel sheet, and manufacturing method for same
MX2014008429A (en) Hot stamp molded article and method for producing same.
CN107109557A (en) High-strength high-tractility steel plate
CN103732778B (en) The high tensile steel plate had excellent formability under room temperature and warm state and warm state manufacturing process thereof
US20130259734A1 (en) Highly formable high-strength steel sheet, warm working method, and warm-worked automobile part
CN108699660A (en) High-strength steel sheet and its manufacturing method
CN108884538A (en) The manufacturing method of sheet metal and coated steel sheet and hot rolled steel plate, manufacturing method, the manufacturing method of heat treatment plate, the manufacturing method of the manufacturing method of sheet metal and coated steel sheet of cold rolling is fully hard steel plate
CN110475892A (en) High strength cold rolled steel plate and its manufacturing method

Legal Events

Date Code Title Description
PB01 Publication
PB01 Publication
SE01 Entry into force of request for substantive examination
SE01 Entry into force of request for substantive examination
GR01 Patent grant
GR01 Patent grant
CF01 Termination of patent right due to non-payment of annual fee
CF01 Termination of patent right due to non-payment of annual fee

Granted publication date: 20190308