CN107002192A - High-strength high-tractility steel plate - Google Patents

High-strength high-tractility steel plate Download PDF

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CN107002192A
CN107002192A CN201580061877.4A CN201580061877A CN107002192A CN 107002192 A CN107002192 A CN 107002192A CN 201580061877 A CN201580061877 A CN 201580061877A CN 107002192 A CN107002192 A CN 107002192A
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steel plate
carbon
steel
strength
temperature
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CN107002192B (en
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村上俊夫
大谷茂生
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Kobe Steel Ltd
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Kobe Steel Ltd
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    • 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
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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Abstract

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

Description

High-strength high-tractility steel plate
Technical field
It is to be related in detail the present invention relates to as the useful high-strength high-tractility steel plate such as thin steel sheet for automobile The strength ductile balance of steel plate develops skill.
Background technology
In the steel plate such as used in the frame part in automobile, with crashworthiness and 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, except requiring Have beyond excellent shaping processability, weldability when also requiring to engage between part and be assembled into component.It is therefore desirable for opening Send out steel plate such a, as specific requirement mechanical property (it is following, be also only called " characteristic ".), can be while carbon amounts be pressed down System is in below 0.3 mass %, while ensuring that yield tensile ratio (YR) is more than 0.7, tensile strength (TS) × elongation percentage (EL) × extension Flange performance (λ) is more than 1000000MPa%%.
In high-strength steel sheet more than 980MPa grades, in order to ensure high intensity and high ductibility are existed side by side, effectively Use TRIP steel and TBF steel that make use of TRIP effects that retained austenite brings etc..In order that intensity-extension of these steel Sexual balance is further improved, and the amount, average carbon density, form for retained austenite have carried out various researchs, proposes have more The steel plate of good characteristic (for example, referring to patent document 1~3).
For example, in patent document 1, propose there is the thin steel of high intensity of a kind of elongation percentage and stamping excellent in stability Plate, its be by the typoiogical classification of the retained austenite in structure of steel into lath-shaped and island when, by the retained austenite of island Ratio is controlled in certain scope.In the art it is contemplated that, although, can also be real in addition to elongation percentage good at room temperature Good elongation percentage under existing 100~200 DEG C warm state, but can not but be substantially ensured that effectively as material as collision characteristic The YR of material factor and strength-ductility balanced, it is impossible to 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, and it is by improving the Ovshinsky in structure of steel The aggregation degree of the crystalline orientation of body phase, is significantly improved relative to the uniform elongation that rolling direction is 45 ° of directions.But, make The characteristic of rolling direction and rolling right angle orientation for general ductility evaluation of orientations is not write out especially, it is impossible to think that it is expired Sufficient above-mentioned requirements level.
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 differences, so as to improve coating baking hardening and strength-ductility balanced.But, this In a little technologies, C concentration differences are assigned to retained austenite crystal grain, but are that main purpose is improved as with coating baking hardening, It is not that as the present invention, it is intended to improve the stability of retained austenite, improves ductility, and to retained austenite Body assign need carbon content distribution, with the present application on technological thought it is entirely different.
【Prior art literature】
【Patent document】
【Patent document 1】Japanese Laid-Open 2012-41573 publications
【Patent document 2】Japanese Laid-Open 2012-21225 publications
【Patent document 3】Japanese Laid-Open 2012-31505 publications
The content of the invention
Therefore it is an object of the present invention to provide a kind of strength-ductility balanced excellent high-strength high-tractility steel Plate, it is able to ensure that yield tensile ratio (YR) is more than 0.7, and tensile strength (TS) × elongation percentage (EL) × Extending flange Perfor (λ) is More than 1000000MPa%%.
The high-strength high-tractility steel plate of the first invention of the present invention, it is characterised in that composition is constituted, in terms of quality %, For
C：More than 0.10% and less 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 up of iron and inevitable impurity,
In structure of steel, retained austenite is calculated as more than 8% with the area occupation ratios relative to all tissues, surplus by bainite, More than one or both of martensite, tempering bainite and tempered martensite constitute, also,
On 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 more than 0.35 mass %,
Its concentration of carbon is more than 1.5 mass % region, and more than 1.0% is calculated as with the area occupation ratio relative to all tissues.
The high-strength high-tractility steel plate of the second invention of the present invention, according to above-mentioned first invention, composition is constituted with matter % meters are measured, also the one or more containing Cu, Ni, Mo, Cr and B add up to less than 1.0%.
The high-strength high-tractility steel plate of the 3rd invention of the present invention, according to the above-mentioned first or second invention, composition composition In terms of quality %, also less than 0.2% is added up to above containing one or both of V, Nb, Ti, Zr and Hf.
The high-strength high-tractility steel plate of the 4th invention of the present invention, according to any one of the above-mentioned first~the 3rd invention Invention, composition is constituted in terms of quality %, also adds up to less than 0.01% above containing one or both of Ca, Mg and REM.
According to the present invention, the amount (area occupation ratio) and average concentration of carbon of retained austenite are not only provided, but also controls carbon The distribution of concentration, shows TRIP phenomenons from the initial stage of deformation to the later stage, so that high work hardening rate is realized, thus, it is possible to provide Strength-ductility balanced excellent high-strength high-tractility steel plate, it is able to ensure that yield tensile ratio (YR) is more than 0.7, and tension is strong It is more than 1000000MPa%% to spend (TS) × elongation percentage (EL) × Extending flange Perfor (λ).
Brief description of the drawings
Fig. 1 is the figure for the diffraction peak for schematically showing the residual γ measured by X-ray diffraction method.
Fig. 2 is the figure for the heat treatment condition for schematically showing the high-strength high-tractility steel plate for manufacturing the present invention.
Embodiment
The present inventors are in order to solve above-mentioned problem, in the steel plate being made up of TBF steel, right as its mechanical characteristic In being able to ensure that yield tensile ratio (YR) is more than 0.7, tensile strength (TS) × elongation percentage (EL) × Extending flange Perfor (λ) is Various researchs have been repeated in more than 1000000MPa%% method.Its result is expected, is studied by following thinking, It is able to ensure that above-mentioned desired characteristic.
That is, in order that strength-ductility balanced improve further than prior art promotes, it is necessary to more effectively utilize The retained austenite of TRIP phenomenons (below, is also expressed as " residual γ ".).But, the viewpoint from the weldability for ensuring steel plate goes out , because the C content in steel plate has upper limit restriction, there is the average carbon density increase in residual γ amounts and residual γ in hair Limitation.
Therefore, the present inventors are conceived to the carbon content distribution in residual γ.That is, in order to utilize TRIP phenomenons, height is reached 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 is present.On the other hand, when deformation quantitative change is big, i.e., in order to still maintain high processing in the later stage of deformation Hardening ratio is, it is necessary to create the residual γ of the high stabilization of concentration of carbon.
In a word, residual γ is only that stability is high, or is only that stability is low all not all right, it is important that stability, i.e. concentration of carbon It is widely distributed to exist.
The present inventors complete the present invention based on the above-mentioned cognitive result further studied.
Hereinafter, first to assigning the high-strength high-tractility steel plate of the present invention (hereinafter also referred to as " steel plate of the present invention ".) with The structure of steel of feature is (hereinafter simply referred to as " tissue ".) illustrate.
(structure of steel of steel plate of the present invention)
As described above, steel plate of the present invention is based on the tissue of TBF steel, but especially contains defined concentration of carbon in ormal weight In terms of remaining γ, on this point of controlling the carbon content distribution in residual γ is different from above-mentioned prior art.
＜ retained austenites：Area occupation ratio relative to all tissues is more than 8% ＞
γ is remained useful for the raising of ductility, in order to effectively play such effect, it is necessary to be allowed to relative to complete There is more than 8%, preferably more than 9%, more preferably more than 10% in the area occupation ratio of portion's tissue.Further, γ area occupation ratio is remained Preferably less than 20%, more preferably less than 18%, particularly preferably less than 16%.
＜ surpluses：Bainite, martensite, one or more kinds of ＞ of tempering bainite and tempered martensite
Ferritic generation is prevented, to be used 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 by low load when anti-deformation realize that yield strength YS's is upper Rise.
Average carbon density (%C in ＜ residuals γγR)：0.9~1.2 mass % ＞
%CγRInfluence residual γ phases are changed into the index of the stability of martensite when being deformation.If %CγRIt is too low, then remain γ It is unstable, therefore apply after stress, processing strain induced martensite phase transformation, therefore prolonging of cannot requiring occur before plastic deformation Stretch rate.On the other hand, if %CγRToo high, then remaining γ becomes excessively to stablize, even if applying processing, will not also occur processing and lure Send out martensitic traoformation, therefore the Extending flange Perfor that still cannot be required.In order to obtain required elongation percentage, %CγRNeed To be 0.9~1.2 mass %.%CγRPreferred lower limit be 1.0 mass %.
The standard deviation of carbon content distribution in ＜ residuals γ：0.35 mass % above ＞
This is that extension remains the concentration of carbon point in γ in order to highly maintain work hardening rate from the initial stage of deformation to the later stage Cloth, so as to create the different residual γ of stability.In order to effectively play such effect, it is necessary to remain the concentration of carbon point in γ The standard deviation of cloth is more than 0.35 mass %, more preferably preferably more than 0.40 mass %, more than 0.45 mass %.Also Have, in the high-strength high-tractility steel plate of the present invention, the standard deviation of the carbon content distribution in residual γ is actually with 0.70 Quality % or so is the upper limit, preferably below 0.65 mass %.
The region that concentration of carbon in ＜ residuals γ is more than 1.5 mass %：Area occupation ratio relative to all tissues is 1.0% Above ＞
In order to improve elongation percentage, it is important that the stability of residual γ during dependent variable increase is high, therefore, the carbon that is only averaged Concentration is high and insufficient, but needs stability high, i.e. the high residual γ of concentration of carbon is present more than a certain amount of.Specifically, The region of more than the mass % of concentration of carbon Ga 1.5 in residual γ needs have more than 1.0% relative to the area occupation ratio of all tissues, Preferably more than 1.5%, more preferably more than 2.0%.Further, in the high-strength high-tractility steel plate of the present invention, γ is remained In concentration of carbon for more than 1.5 mass % area occupation ratios of the region relative to all tissues, it is left with all remain γ areas 1/2 The right side is the upper limit, preferably less than 2/5, more preferably less than 1/3.
(average carbon density (the %C in residual γ area occupation ratio, residual γγR), and the carbon content distribution each measurement side Method)
Here, area occupation ratio, average carbon density (%C for remaining γγR) and carbon content distribution each measuring method carry out Explanation.
Area occupation ratio (V on remaining γγR) and average carbon density (%CγR), after 1/4 thickness of steel plate is ground to, Measured after chemical grinding by X-ray diffraction method (ISIJ Int.Vol.33, (1933), No.7, p.776).Further, at this In invention, as X-ray diffraction device, the two-dimentional zone X ray detecting diffraction instrument (RINT-RAPIDII) of (strain) リ ガ Network systems is used, Co-K alpha rays are used as X-ray.
Further, on the tissue beyond residual γ, nital corrosion is carried out to steel plate, with light microscope (400 times of multiplying power) is observed, and distinguishes the tissue beyond residual γ.
Then, the distribution on the concentration of carbon in residual γ, uses (200) gone out by above-mentioned X-ray diffraction measurement device γ, (220) γ and this 3 diffraction peaks of (311) γ, are tried to achieve as follows.
First, as shown in the schematic of Figure 1, in (200) γ, (220) γ and (311) γ this 3 diffraction peaks, respectively Try to achieve maximum 2 θ (2 θ of diffracted intensityavg) and its θ of half breadth Δ 2 (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 following formula (1), try to achieve d (hkl).
D (hkl)=λ/{ 2sin (2 θavg(hkl)/2) } ... formula (1)
Then, according to following formula (3), crystal lattice constant a is tried to achieve0(hkl), by this 3 crystal lattice constant a0(hkl) make Crystal lattice constant a is tried to achieve for arithmetic average0。
Then, using formula (Dyson D.J., the Holmes B. (1970), " Effect of of the Dyson shown in following formula (3) Alloying additions on the lattice parameter austenite ", J.Iron Steel Inst., 208：469-474.), try to achieve concentration of carbon %Cavg(unit：Quality %).(also have, concentration of carbon %CavgIt is only used as being used to provide The index of carbon content distribution is used, and the above-mentioned average carbon density %C with separately measuring is annotated in advanceγRStrictly speaking may not one Cause.)
%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, trying to achieve the half breadth Δ %C of the carbon content distribution in residual γ according to the following steps.
First, with following formula (4) and (5), try to achieve the θ of angle of diffraction 2 (hkl) at each peak the θ of half breadth Δ 2 (hkl) it is upper The angle of diffraction (reference picture 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, respectively using above-mentioned 2 θLAnd 2 θ (hkl)H(hkl), with above-mentioned same step, using Bragg condition and Above-mentioned formula (1)~(3), try to achieve the upper lower limit value %C of the half breadth of carbon content distributionLAnd %CH.Then, asked according to following formula (6) 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, standard is calculated by above-mentioned half breadth Δ %C Deviations %C.
That is, the probability density function f (x) of normal distribution, according to average value u and standard deviation, is represented by following formula (7).
Probability f (u) in average value, is that x=u is substituted into above-mentioned formula (7), is tried to achieve by following formula (8).
Then, from average value u=%CavgOnly move up and down half breadth Δ %C 1/2 value (%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 relation of following formula (9) can be obtained.
As above-mentioned formula (9) is deformed, so as to try to achieve standard deviation by half breadth Δ %C%CFormula, following formula can be imported (10) half breadth Δ %C, is substituted into the formula (10), standard deviation is calculated%C。
Then, using the average value %C of the carbon content distribution in the residual γ tried to achieve as described soavgAnd σ%C, utilize Cumulative distribution function g (x) shown in following formula (11), tries to achieve the region that concentration of carbon is more than 1.5 mass %, relative to whole tissues Area occupation ratio VγR(C >=1.5%), as its formula, export following formula (12) calculates V using the formula (12)γR(C >=1.5%).
Here, VγRIt is all residual γ area occupation ratio.
Next, being illustrated for the composition composition for constituting steel plate of the present invention.Hereinafter, the unit of chemical composition is entirely Quality %.In addition, it is " amount " that " content " of each composition, which is also only described,.
(the composition composition of steel plate of the present invention)
C：More than 0.10% and less than 0.35%
C helps to ensure the amount (area occupation ratio) of retained austenite, is for ensuring that intensity and the necessary element of ductility.For Such effect is effectively played, it is necessary to make C contain more than 0.10%, preferably more than 0.12%, more preferably 0.14% More than.But, if C amounts become superfluous, deteriorate weldability, therefore C amounts are less than 0.35%, preferably less than 0.32%, more Preferably less than 0.30%, more preferably less than 0.28%.
Si+Al：0.5~2.0%
Si and Al are effectively to suppress retained austenite to decompose, the element of carbide generation.In order to effectively play so Effect, it is necessary to make Si and Al is total to contain more than 0.5%, preferably more than 0.7%, more preferably more than 0.9%.But, Even if containing Si and Al superfluously, the effect above is also saturation, not only economically causes to waste, and cause red brittleness, Sl Total amount with Al is less than 2.0%, preferably less than 1.9%, more preferably less than 1.8%.
Mn：1.0~4.0%
Mn makes stabilization of austenite, is for obtaining the element required for desired retained austenite.In order to effectively send out Such effect is waved, it is necessary to make Mn contain more than 1.0%, preferably more than 1.3%, more preferably more than 1.6%.But, if Mn amounts become superfluous, then, it is seen that adverse effect occurs etc. for slab crackle, therefore Mn amounts are less than 4.0%, preferably 3.5% with Under, more preferably less than 3.0%.
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 make P contain superfluously, secondary workability deterioration, therefore P amounts be less than 0.05%, preferably 0.03% with Under, more preferably less than 0.02%.
S：0~0.01%
S also serves as impurity element and is inevitably present, and forms MnS etc. sulfide-based field trash, is to turn into crackle Starting point and make processability deteriorate element, therefore S amounts be less than 0.01%, preferably less than 0.005%, be more preferably Less than 0.003%.
The steel of the present invention contains using above-mentioned element as necessary composition, and surplus is iron and inevitable impurity, in addition, It in the scope for the effect for not damaging the present invention, can contain following permission composition.
Cu, Ni, Mo, Cr and B one or more：Total less than 1.0%
These elements are useful as the intensified element of steel, and ensure to have for the stabilisation and ormal weight for remaining γ The element of effect.In order to effectively play such effect, it is more than 0.001% to recommend these element total amounts, more recommends to be allowed to Contain more than 0.01%.But, even if these elements contain superfluously, the effect above is also saturation, economically causes to waste, Therefore preferably these element total amounts are less than 1.0%, more preferably less than 0.5%.
V, Nb, Ti, Zr and Hf one or more：Total less than 0.2%
These yuan have the effect of precipitation strength and tissue miniaturization, are useful element to high intensity.In order to effective Ground plays such effect, and recommendation makes these element total amounts be more than 0.01%, more recommends to be allowed to containing more than 0.02%.But It is that, even if these elements contain superfluously, the effect above is also saturation, economically causes to waste, therefore these elements are total Amount is preferably less than 0.2%, more preferably less than 0.1%.
Ca, Mg and REM one or more：Total less than 0.01%
The form of sulfide in these control of element steel, is effective element for improving processability.Here, as being used for The REM (rare earth element) of the present 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 more than 0.001%, more recommend to be allowed to containing more than 0.002%.But, even if these elements contain superfluously Have, the effect above is also saturation, economically cause to waste, therefore preferably these element total amounts are less than 0.01%, it is more excellent Elect less than 0.005% as.
Then, the preferred manufacturing condition for obtaining the invention described above steel plate is illustrated below.
(the preferred manufacture method of steel plate of the present invention)
The steel for meeting mentioned component composition can be carried out hot rolling by steel plate of the present invention, it is then cold rolling after, such as with following The conditions of process (1)~(4) be heat-treated and manufactured (reference picture 2).
[heat treatment condition]
(1) cold-reduced sheet is heated to the second heating-up temperature T2：[0.7 × Ac1+0.3 × Ac3]~[0.2 × Ac1+0.8 × Ac3], the second retention time t2 is kept at this temperature：More than 5s, or, with 4 DEG C/below s average heating rate in equality of temperature Spend after scope heating,
(2) it is again heated to the 3rd heating-up temperature T3：[Ac3+10 DEG C]~950 DEG C, when keeping the 3rd holding at this temperature Between t3：After below 180s,
(3) with average cooling rate CR1：20 DEG C/more than s, it is cooled to from above-mentioned 3rd heating-up temperature T3 after 500 DEG C,
(4) with austempering temperature T4：350~480 DEG C of holding austempering retention times t4：It is cold after more than 10s But to room temperature.
Hereinafter, illustrated for the rationale for the recommendation of above-mentioned heat treatment condition.
＜ (1) is with the second heating-up temperature T2：[0.7 × Ac1+0.3 × Ac3]~[0.2 × Ac1+0.8 × Ac3] keeps the Two retention time t2：More than 5s, or, ＞ is heated in synthermal scope with 4 DEG C/below s average heating rate
Kept in two phase region temperature provinces of ferrite/austenite with the stipulated time or slow heating, in the two phase regions temperature Region, make Mn concentration distribution in reverse transformation occur, this be in order to increase the austempering in above-mentioned operation (4) processing when Carbon content distribution in the local speed difference of bainitic transformation, extension residual γ.
The retention time t2 of the temperature range is more preferably more than 10s, more preferably more than 20s, from productivity ratio Viewpoint, which is set out, is recommended as below 200s.
Further, Ac1 and Ac3 can be write, " iron Steel material science ", good fortune field according to the chemical composition of steel plate using Lesley Cheng Jingyi, Wan Shan Co., Ltd., 1985, p.273 described formula try to achieve.
＜ (2) is again with the 3rd heating keeping temperature T3：[Ac3+10 DEG C]~950 DEG C keep the 3rd retention time t3：180s Following ＞
This be in order to by austenite one phase domain temperature province keep, make tissue turn into austenite one phase tissue so that Remaining ferrite during cooling after preventing.
If the 3rd heating-up temperature T3 is less than [Ac3+10 DEG C], ferrite remaining, the cooling of above-mentioned operation (3) behind During can not suppress ferritic growth, ferrite is formed superfluously.On the other hand, if the 3rd heating-up temperature T3 is higher than 950 DEG C, or the 3rd retention time t3 is higher than 180s, then the Mn homogenization being distributed with above-mentioned operation (1) when two phase regions are heated, it is impossible to Carbon content distribution in extension residual γ.
＜ (3) is with average cooling rate HR1：20 DEG C/more than s, 500 DEG C of ＞ are cooled to from the 3rd heating-up temperature T3
This is the tissue as bayesian phosphor bodies in order to prevent ferritic formation.
The average cooling rate HR3 of the temperature range, more preferably 25 DEG C/more than s, more preferably 30 DEG C/s with On.
＜ (4) is with austempering temperature T4：350~480 DEG C of holding austempering retention times t4：After more than 10s, It is cooled to room temperature ＞
This is in order to promote bainitic transformation, carbon is thickened to non-transformed austenite, so that the residual γ stablized.
[variation of heat treatment condition]
Further, above-mentioned operation (1) can also be constituted in the way of following processes (1a).
Cold-reduced sheet is heated to the first heating-up temperature T1 by (1a)：[Ac1-100 DEG C]~[Ac1-30 DEG C], at this temperature Kept for the first retention time：More than 10s, or, after synthermal scope is with 2 DEG C/below s average heating rate's heating, with Second heating-up temperature T2：[0.7 × Ac1+0.3 × Ac3]~[0.2 × Ac1+0.8 × Ac3] keeps the second retention time t2：5s More than.
In this way, kept for stipulated time or slow heating in the phase region temperature province of ferrite/cementite two in advance, first make Mn to oozing It is thickened in carbon body, the phase region of ferrite/austenite two behind promotes the Mn concentration distribution between ferrite/austenite when heating, So as to increase the local speed difference of the bainitic transformation during 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).
(4a) is with austempering temperature T4：350~480 DEG C of holding austempering retention times t4：After more than 10s, It is again heated to relation reheating temperature T5：500~600 DEG C, keep reheating retention time t5 with this temperature：After below 30s, cooling chamber Temperature.
In this way, steel plate of the present invention, it is again heated to the residual not resolvent temperature fields of γ and makes coating alloying, also can be into For plated steel sheet.
Hereinafter, enumerate embodiment and further illustrate the present invention, but the present invention is not limited by following embodiments certainly, in energy Before enough meeting in the range of objective described later, naturally it is also possible to suitably changed implementation, these are all contained in the present invention's In technical scope.
【Embodiment】
After the steel that the composition shown in table 1 below is manufactured with vacuum melting, turn into thickness of slab 30mm steel plate through hot forging, 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 In embodiment, it is heated to after 1200 DEG C, by multistage rolling, thickness of slab is turned into the condition of 880 DEG C of the end temp of hot rolling 2.5mm.Thereafter, 500 DEG C are cooled to 30 DEG C/s cooling velocity and stop cooling, be inserted into after being heated in 500 DEG C of stove Holding 30min, followed by stove are cold and turn into hot rolled plate.Pickling is implemented to the hot rolled plate, after the oxide skin for removing surface, implemented 1.4mm is cold-rolled to as cold-reduced sheet.
Then, using above-mentioned cold-reduced sheet as raw material, the condition as shown in table 2 below implements heat treatment.Further, from room temperature Average heating rate to initial heating-up temperature (keeping temperature) is fixed as 10 DEG C/s, and (temperature is kept to heating-up temperature below Degree) average heating rate be fixed as 20 DEG C/s, to followed by the average heating rate of heating-up temperature (keeping temperature) fix For 10 DEG C/s.In addition, 10 DEG C/s is fixed as from austempering temperature T4 to relation reheating temperature T5 average heating rate, from Austria Family name body temperature T4 or relation reheating temperature T5 is fixed as 10 DEG C/s to the average cooling rate of room temperature.
【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 inapplicable)
For each steel plate after above-mentioned heat treatment, by the measuring method illustrated in above-mentioned [embodiment] one, Measurement residual γ area occupation ratio, the average carbon density (C γ R) in residual γ and its carbon content distribution.
Further, the tissue of the steel plate used in the present embodiment, the surplus in addition to retained austenite and ferrite, all Constituted more than one or both of bainite, martensite, tempering bainite and tempered martensite, therefore in following tables In 3, retained austenite and ferritic area occupation ratio are only described.
In addition, in order to which for each steel plate after above-mentioned heat treatment, valence-ductility balanced, by tension test, is surveyed Measure yield strength YS, tensile strength TS and elongation percentage (breaking elongation) EL.Further, in tension test, No. 5 experiments of JIS are made Piece, it then follows JIS Z 2241 are implemented.In addition, the Extending flange Perfor λ in order to evaluate each steel plate, according to Tie Gang alliances of Japan specification JFST1001 measures hole expansibility.
Measurement result is shown in Table 3 below.In same table, in the characteristic of the steel plate after above-mentioned heat treatment, yield tensile ratio (YR) be more than 0.7, tensile strength (TS) × elongation percentage (EL) × Extending flange Perfor (λ) be 1000000MPa%% with On qualified (zero), herein beyond unqualified (×).
(outside underscore=the scope of the present invention, *=refined is recommended outside scope, α=ferrite)
【Table 3】
As shown in Table 3 above, as steel No.3,4,9~11,14,18~27 of invention steel (being evaluated as zero), using full The steel grade of important document, is heat-treated with the condition of recommendation as defined in the composition of the foot present invention, as a result, making the tissue of the present invention The sufficient invention steel of defined important document, 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 Composition provide and organization prescribed important document at least any one is inadequate, characteristic is unsatisfactory for criterion of acceptability.
That is, steel No.1,2,5~8,12, although use the steel grade of important document as defined in the composition for meeting the present invention, still Manufactured under conditions of the manufacturing condition of recommendation is partially disengaged, therefore the important document of organization prescribed is inadequate, characteristic is poor.
On the other hand, although steel No.13,15~17 being manufactured with the manufacturing condition of recommendation, using being partially disengaged this hair The steel grade of important document as defined in bright composition, therefore the important document of organization prescribed is inadequate, characteristic is poor.
The applicability of the present invention can be confirmed more than.
In detail and the present invention is illustrated with reference to specific embodiment, but do not depart from the spirit and scope of the present invention and can add With various changes and modifications, this will be apparent that for practitioner.
The application is based on Japanese patent application (patent application 2014-238710) filed in 26 days November in 2014, in it Hold and be incorporated into this as reference.
【Industrial applicability】
On the steel plate of the present 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, it is characterised in that composition composition is calculated as with quality %
C：More than 0.10% and less 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 up of iron and inevitable impurity,
In structure of steel, retained austenite is calculated as more than 8% with the area occupation ratio relative to all tissues, and surplus is by bainite, geneva More than one or both of body, tempering bainite and tempered martensite constitute, also,
On 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 more than 0.35 mass %,
Its concentration of carbon is calculated as more than 1.0% for more than 1.5 mass % region with the area occupation ratio relative to all tissues.
2. high-strength high-tractility steel plate according to claim 1, wherein, composition is constituted in terms of quality %, under also containing State any one in (a)~(c)：
(a) more than one or both of Cu, Ni, Mo, Cr and B less than 1.0% is added up to；
(b) more than one or both of V, Nb, Ti, Zr and Hf less than 0.2% is added up to；
(c) more than one or both of Ca, Mg and REM less than 0.01% is added up to.
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CN114908287A (en) * 2022-04-11 2022-08-16 武汉科技大学 Low-alloy lightweight high-strength automobile steel and production method thereof
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

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US20170268077A1 (en) 2017-09-21
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