CN108950405A - A kind of 800MPa grade multi-phase Steels and production method with good flange performance - Google Patents
A kind of 800MPa grade multi-phase Steels and production method with good flange performance Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- 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
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- 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
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- 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0273—Final recrystallisation annealing
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium 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
- C21D2211/002—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
- C21D2211/005—Ferrite
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
A kind of 800MPa grade multi-phase Steels with good flange performance, its component and wt% are as follows: C:0.075~0.100%, Si:0.41~0.52%, Mn:1.60~2.00%, P:0.0120% or less, S:0.010% or less, Als:0.015~0.070%, Cr:0.25~0.45%, Ti:0.036~0.055%, Nb:0.036~0.050%, N:0.005% or less；Production technology: slab after routine is smelted is set according to ingredient；Carry out hot rolling technology；Carry out cold-rolling process；Cooled to room temperature, for use.Yield strength of the present invention reaches 500~650MPa, 780~900MPa of tensile strength, 13% or more elongation, 35% or more hole expansibility；Its microstructure is bainite, ferrite, pearlite, a small amount of martensite and retained austenite, to ensure that while having higher-strength, also has preferable forming property, flange performance and collision energy-absorbing performance.
Description
Technical field
The present invention relates to a kind of automotive safety structure steel and production method, definitely belong to good flange performance
800MPa grade tissue automotive safety structure steel and the production methods of carrying out more.
Background technique
Auto industry is pillar industry and the maximum user of iron and steel enterprise in industrially developed country, in energy conservation, ring
Under the requirement of guarantor, safety and sustainable development, high-strength and unimach becomes the mainstream of body of a motor car steel, to reach
The purpose of lightness of automobile, safety, in order to develop high Strength Steel for Motor Vehicles, promote automotive light weight technology, it is alive in recent years
The research of a large amount of associated vehicle lightweight project is started within the scope of boundary, the common ground of research is to reduce car mass
20%~40%.
Advanced high-strength steel is the new type steel occurred in recent years, and the main distinction with common high-strength steel is the micro- of them
Tissue is different.Common high-strength steel is single phase ferrite, and advanced high-strength steel is substantially heterogeneous structure, including ferrite F
(Ferrite), martensite M (Martensite), bainite B (Bainite) and retained austenite (Retained
Austenite).Its schedule of reinforcement is other than solution strengthening, precipitation strength, refined crystalline strengthening, and there are also phase transformation strengthenings, and wherein phase transformation is strong
Change is the main schedule of reinforcement of advanced high-strength steel.Compared with common high-strength steel, advanced high-strength steel formability is good, S. E. A.
The advantages that height, dent resistance is good, and baking and hardening performance, yield strength, work hardening rate are high, good fatigue behaviour, in auto industry
Show good application prospect.
Multi-phase Steels Main Tissues are a high proportion of hard phase (such as bainite, martensite) and tiny ferrite.Pass through geneva
The intensity of the compound action of body and bainite and precipitation strength, Multiphase Steel can reach 800MPa or more, the Series Steel have compared with
High collision energy-absorbing and flange performance, the safety members such as side door beams, bumper and B column particularly suitable for production automobile
And structural member.
Through retrieving:
China Patent Publication No. is the document of CN103290320A, discloses " a kind of hot rolling Multiphase Steel and its producer
Method " is designed using the ingredient of the low manganese of high silicon, and in 880-900 DEG C of finish to gauge, the 590-620 DEG C of technique batched.Though it is bent
Intensity is taken in 750-800MPa, for tensile strength in 820-950MPa, elongation is Multiphase Steel in 14-20%, but document due to
It is not directed to assess flange performance with hole expansibility data, and the elongation index for characterizing plasticity is relatively low, in punching press
Easily occurs problem of Cracking in forming process.In addition, its intensity is higher, therefore the hard Phase Proportion in its tissue is higher, formability and
Flange performance also can be relatively low, while compared with cold rolling Multiphase Steel proposed by the present invention, and surface quality is opposite to want poor.
China Patent Publication No. is the document of CN103131946A, disclose " a kind of phosphorous cold rolling Multiphase Steel of low-carbon and its
Preparation method ", which employs C:0.08-0.12%, the ingredient of P:0.02-0.06% is designed.Its cold-rolled steel sheet need to be in 940-980
DEG C heat preservation 2-8min, is quickly cooled to 350-500 DEG C, keeps the temperature 2-8min, water cooling to room temperature.Tensile strength can reach 840MPa with
On, 12% or more elongation.The document is equally not directed to assess important flange performance to hole expansibility data, and the invention is
Bainite isothermal phase change occurs by the way that bainite point will be cooled fast to after steel austenitizing, then obtains horse to room temperature in water quenching
The method of family name's body obtains superhigh intensity, therefore its intensity is high, but its forming property is poor, easily occurs cracking, zero in forming process
The problems such as part rebound is serious, while biggish limitation is had according to its production technology, be not suitable for industrialized production.
Summary of the invention
The invention reside in the shortcomings of the prior art is overcome, a kind of 500~650MPa of yield strength, tensile strength are provided
780~900MPa, elongation >=13%, the 800MPa grade multi-phase Steels with good flange performance of hole expansibility >=35% and production
Method.
Realize the technical measures of above-mentioned purpose:
A kind of 800MPa grade multi-phase Steels with good flange performance, component and weight percent content are as follows: C:0.075
~0.100%, Si:0.41~0.52%, Mn:1.60~2.00%, P:0.0120% hereinafter, S:0.010% hereinafter, Als:
0.015~0.070%, Cr:0.25~0.45%, Ti:0.036~0.055%, Nb:0.036~0.050%, N:0.005%
Hereinafter, surplus is Fe and inevitable impurity；Its mechanical property are as follows: 500~650MPa of yield strength, tensile strength 780~
900MPa, 13% or more elongation, 35% or more hole expansibility, microstructure are that bainite volume ratio is 45~65%, ferrite
Volume ratio is 20~40%, remaining is pearlite, martensite and retained austenite.
It is: the addition weight percent content of V is no more than 0.05%.
Preferably: the weight percent content of Cr is 0.29~0.41%%.
Preferably: the weight percent content of Ti is 0.39~0.52%%.
Preferably: the weight percent content of Nb is 0.38~0.47%%.
A kind of method for producing 800MPa grade multi-phase Steels with good flange performance, step:
1) slab after routine is smelted is set according to ingredient, and controls 25~40 DEG C again of the packet degree of superheat in slab；
2) hot rolling technology is carried out:
A, slab is heated first, controls heating temperature at 1230~1280 DEG C；
B, roughing is carried out, control roughing dephosphorization passage is not less than 3 times, and roughing outlet temperature is at 1090~1130 DEG C；
C, finish rolling is carried out, controls finishing temperature at 870~910 DEG C；
D, it is cooled down, is cooled to using the leading portion type of cooling to coiling temperature；
E, it is batched, controls coiling temperature at 530~570 DEG C；
3) cold-rolling process is carried out:
A, pickling is carried out to strip, and controls pickling solution temperature at 70~90 DEG C；
B, carry out cold rolling, control steel strip thickness of the cold rolling total reduction after 58%~72%, cold rolling 0.70~
2.5mm；
C, carry out continuous annealing: therebetween, control soaking section temperature at 800~820 DEG C, slow cooling section terminate temperature 650~
670 DEG C, rapid cooling section terminates temperature at 350~375 DEG C；Overaging temperature is at 280~330 DEG C, and cold section of temperature is 100~160 eventually
℃。
4) cooled to room temperature, for use.
The effect and mechanism of each element grade master operation in the present invention:
C:C is gap intensified element, its main feature is that strengthening effect is obvious, cost of material is low.It is directly affected at critical zone
After reason in Multiphase Steel bainite, martensite etc. volume fraction, but carbon content low (< 0.06%) is difficult to obtain hard phase constitution,
Carbon content is too high, and the harden ability enhancing of steel can obtain a large amount of martensitic structure under lower cooling velocity, and cannot get
Bainite structure, therefore carbon content requires control 0.075~0.100%%, if exceeding this range, the intensity of material is held
It is easily relatively low or higher.
Si:Si is ferritic solution strengthening element, and the main function that silicon is added in multi-phase Steels is to expand Fe-Fe3C phasor
In the area (α+γ), the temperature range for handling critical zone widens, and improves the processing performance of multi-phase Steels, and increase A3 line in phasor
Gradient, the flexibility of heat treatment process is thus increased, to be conducive to keep the stabilization of the performances such as multiphase hardness of steel
Property.Therefore carbon content requires control 0.41~0.52%, and silicone content is too high or too low to be not achieved said effect.
Mn: manganese is typical austenite stabilizer element, significantly improves the harden ability of steel, reduces bainite and martensite shape
At critical cooling rate, to effectively reduce the cooling velocity of rapid cooling section in annealing process, and then be conducive to obtain bayesian
Body or martensitic structure.It is simultaneously also a kind of cheap stable austenite and reinforced alloys element.But high manganese content (>
2.0%) while postponing perlitic transformation, bainite transformation also to be postponed, " process window " is made to become smaller, Bainite Region moves to right,
So that steel is become larger the sensibility of process conditions, is unfavorable for stably producing.Manganese content is too low easily to cause perlitic transformation, tissue
In be difficult to form the bainite of sufficient amount.Therefore manganese content requires control 1.60~2.00%.
Als: aluminium is strong deoxidant element, in order to guarantee that the oxygen content in steel is low as far as possible, needs to add a certain amount of aluminium,
Meanwhile soluble aluminum is commonly used for microalloy element to combine the nitrogen in steel, the very thin AlN of disperse prevents growing up for austenite grain.
In γ-α transition process, AlN plays nucleation, so that austenite be accelerated to change.The most important effect of AlN is to refine crystal grain simultaneously
Obtain aging resistance.When Als content is less than 0.010%, its effect cannot be played；But add the aluminium oxidation easy to form of volume
Aluminium agglomerate.Therefore aluminium content requires control 0.015~0.070%.
Cr: effect of the chromium in multi-phase Steels is mainly reflected in the harden ability of its stability that can increase austenite and steel, this
Two adverse effect joint effects restrict the volume fraction of martensite in chrome-bearing steel.Chromium is under lower cooling velocity to influence
Based on the stability of overcooling austenite；In higher cooling velocity chromium to influence based on the volume fraction of austenite.But chromium is
The most effective element of bainite transformation is postponed, the effect of its postponement bainitic transformation is bigger than the effect for postponing pearlitic transformation to be obtained
It is more.Therefore chromium content requires control 0.25~0.45% in steel.
Ti, Nb, V: titanium, niobium and vanadium are all carbides, and the effect being added in multi-phase Steels is and carbon, nitrogen shape
At the Second Phase Particle of small and dispersed, Grain refinement is played.Its additional amount can excessively consume the carbon in steel, reduce bayesian
The generation of the hard phase such as body, martensite, addition cannot play Grain refinement very little.Therefore titanium, niobium and content of vanadium requirement in steel
Control is in Ti:0.036~0.055%, Nb:0.036~0.050%, V: being no more than 0.050%.
P, S, N: phosphorus, sulphur, nitrogen belong to control element in steel, should control in minimum level, produce reality according to steel mill,
P:0.012% hereinafter, S:0.010% hereinafter, N:0.005% or less.
The present invention why control in the packet degree of superheat at 25~40 DEG C, be for guarantee pouring temperature stablize, thus reasonable
With continuous casting cooling water, good slab quality is obtained.
Why the present invention controls slab heating temperature at 1230~1280 DEG C, is since excessively high heating temperature will lead to
Continuous casting billet structure is excessively coarse, thus the organizational controls after influence of rolled, too low temperature cannot be such that alloying component is sufficiently dissolved.
Why the present invention controls roughing outlet temperature at 1090~1130 DEG C, is since too low roughing temperature cannot protect
The temperature that card strip is exported in finish rolling.
Why the present invention controls exit temperature at finishing at 870~910 DEG C, is since finishing stands to be guaranteed are in single-phase Austria
The area Shi Ti completes, and mixed crystal problem is avoided to occur.
Why the present invention controls coiling temperature at 530~570 DEG C, is due to that can guarantee hot rolled plate in this temperature range
Tissue be ferrite and pearlite, avoid generating martensite and bainite and causing the intensity of hot-strip higher.
Why the present invention controls cold rolling total reduction 58%~72%, is due to can guarantee under the conditions of following rate herein
Strip can be made to complete sufficiently recrystallization during subsequent anneal, and can guarantee that cold-strip steel smoothly completes cold rolling.
Why the present invention controls continuous annealing process soaking section temperature at 800~820 DEG C, and slow cooling section terminates temperature and exists
650~670 DEG C, rapid cooling section terminates temperature at 350~375 DEG C；Overaging temperature is at 280~330 DEG C, and cold section of temperature is 100 eventually
~160 DEG C, while can be protected due to can guarantee that strip can anneal in the two-phase section of ferrite and austenite under this soaking temperature
A certain proportion of austenite content is demonstrate,proved, by control slow cooling section and rapid cooling section outlet temperature, the cooling velocity for controlling strip guarantees
The ratio of each phase of final products, reaches design requirement.
Compared with prior art, the present invention having good reaming flange performance and collision energy-absorbing performance, yield strength to reach
500~650MPa, 780~900MPa of tensile strength, 13% or more elongation, 35% or more hole expansibility；Its microstructure is shellfish
Family name's body, ferrite, pearlite, a small amount of martensite and retained austenite also have to ensure that while having higher-strength
Preferable forming property, flange performance and collision energy-absorbing performance.
Detailed description of the invention
Fig. 1 is the metallographic structure figure of steel plate of the present invention.
Specific embodiment
The present invention is described in detail below:
Table 1 is the chemical component comparative example of various embodiments of the present invention and comparative example；
Table 2 is the main technologic parameters comparative example of various embodiments of the present invention and comparative example；
Table 3 is the performance text list of various embodiments of the present invention and comparative example.
Various embodiments of the present invention follow the steps below production:
1) slab after routine is smelted is set according to ingredient, and controls 25~40 DEG C again of the packet degree of superheat in slab；
2) hot rolling technology is carried out:
A, slab is heated first, controls heating temperature at 1230~1280 DEG C；
B, roughing is carried out, control roughing dephosphorization passage is not less than 3 times, and roughing outlet temperature is at 1090~1130 DEG C；
C, finish rolling is carried out, controls finishing temperature at 870~910 DEG C；
D, it is cooled down, is cooled to using the leading portion type of cooling to coiling temperature；
E, it is batched, controls coiling temperature at 530~570 DEG C；
3) cold-rolling process is carried out:
A, pickling is carried out to strip, and controls pickling solution temperature at 70~90 DEG C；
B, carry out cold rolling, control steel strip thickness of the cold rolling total reduction after 58%~72%, cold rolling 0.70~
2.5mm；
C, carry out continuous annealing: therebetween, control soaking section temperature at 800~820 DEG C, slow cooling section terminate temperature 650~
670 DEG C, rapid cooling section terminates temperature at 350~375 DEG C；Overaging temperature is at 280~330 DEG C, and cold section of temperature is 100~160 eventually
℃。
4) cooled to room temperature, for use.
The chemical component (wt.%) of 1 various embodiments of the present invention of table and comparative example
The main technologic parameters comparative example of 2 various embodiments of the present invention of table and comparative example
The performance text list of 3 various embodiments of the present invention of table and comparative example
From table 3 it can be seen that steel of the present invention is matched with reasonable heterogeneous structure, it both ensure that invention steel was with higher
Intensity, and there is good forming property and reaming performance, it can satisfy the requirement of bodywork parts forming flange and energy-absorbing.
Present embodiment is only the best example, not to the restricted implementation of technical solution of the present invention.
Claims (6)
1. a kind of 800MPa grade multi-phase Steels with good flange performance, component and weight percent content are as follows: C:0.075~
0.100%, Si:0.41~0.52%, Mn:1.60~2.00%, P:0.0120% hereinafter, S:0.010% hereinafter, Als:0.015~
0.070%, Cr:0.25~0.45%, Ti:0.036~0.055%, Nb:0.036~0.050%, N:0.005% are hereinafter, surplus is
Fe and inevitable impurity；Its mechanical property are as follows: 500~650MPa of yield strength, 780~900MPa of tensile strength, elongation
13% or more rate, 35% or more hole expansibility, microstructure are that bainite volume ratio is 45~65%, ferrite ratio be 20~
40%, remaining is pearlite, martensite and retained austenite.
2. a kind of 800MPa grade multi-phase Steels with good flange performance as described in claim 1, it is characterised in that: V's adds
Add weight degree is no more than 0.05%.
3. a kind of 800MPa grade multi-phase Steels with good flange performance as described in claim 1, it is characterised in that: the weight of Cr
Degree is measured 0.29~0.41%%.
4. a kind of 800MPa grade multi-phase Steels with good flange performance as described in claim 1, it is characterised in that: the weight of Ti
Degree is measured 0.039~0.052%%.
5. a kind of 800MPa grade multi-phase Steels with good flange performance as described in claim 1, it is characterised in that: the weight of Nb
Degree is measured 0.038~0.047%%.
6. producing a kind of method of the 800MPa grade multi-phase Steels with good flange performance as described in claim 1, step:
1) slab after routine is smelted is set according to ingredient, and controls 25~40 DEG C again of the packet degree of superheat in slab；
2) hot rolling technology is carried out:
A, slab is heated first, controls heating temperature at 1230~1280 DEG C；
B, roughing is carried out, control roughing dephosphorization passage is not less than 3 times, and roughing outlet temperature is at 1090~1130 DEG C；
C, finish rolling is carried out, controls finishing temperature at 870~910 DEG C；
D, it is cooled down, is cooled to using the leading portion type of cooling to coiling temperature；
E, it is batched, controls coiling temperature at 530~570 DEG C；
3) cold-rolling process is carried out:
A, pickling is carried out to strip, and controls pickling solution temperature at 70~90 DEG C；
B, cold rolling is carried out, controls steel strip thickness of the cold rolling total reduction after 58%~72%, cold rolling in 0.70~2.5mm；
C, it carries out continuous annealing: therebetween, controlling soaking section temperature at 800~820 DEG C, slow cooling section terminates temperature 650~670
DEG C, rapid cooling section terminates temperature at 350~375 DEG C；Overaging temperature is at 280~330 DEG C, and cold section of temperature is at 100~160 DEG C eventually；
4) cooled to room temperature, for use.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810923080.6A CN108950405B (en) | 2018-08-14 | 2018-08-14 | 800 MPa-grade multi-phase steel with good flanging performance and production method thereof |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810923080.6A CN108950405B (en) | 2018-08-14 | 2018-08-14 | 800 MPa-grade multi-phase steel with good flanging performance and production method thereof |
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| CN108950405A true CN108950405A (en) | 2018-12-07 |
| CN108950405B CN108950405B (en) | 2020-02-18 |
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Cited By (7)
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|---|---|---|---|---|
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| CN110724877A (en) * | 2019-10-30 | 2020-01-24 | 鞍钢股份有限公司 | 1180MPa grade high-plasticity bainite complex phase steel plate for automobile and preparation method thereof |
| CN111979489A (en) * | 2020-09-07 | 2020-11-24 | 鞍钢股份有限公司 | 780 MPa-grade high-plasticity cold-rolled DH steel and preparation method thereof |
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| CN114540707A (en) * | 2022-02-11 | 2022-05-27 | 武汉钢铁有限公司 | 590 MPa-grade cold-rolled high-strength steel and production method thereof |
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