CN106636925A - High-strength-and ductility-product cold-rolled TRIP steel and preparing method thereof - Google Patents
High-strength-and ductility-product cold-rolled TRIP steel and preparing method thereof Download PDFInfo
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- CN106636925A CN106636925A CN201611262468.3A CN201611262468A CN106636925A CN 106636925 A CN106636925 A CN 106636925A CN 201611262468 A CN201611262468 A CN 201611262468A CN 106636925 A CN106636925 A CN 106636925A
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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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
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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
- 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
- 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
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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Abstract
The invention discloses high-strength-and ductility-product cold-rolled TRIP steel and a preparing method thereof and belongs to the technical field of high-strength-and ductility-product cold-rolled automobile steel. The high-strength-and ductility-product cold-rolled TRIP steel comprises, by mass percent, 0.20%-0.23% of C, 0.35%-0.50% of Si, 2.0%-2.4% of Mn, 1.6%-2.5% of Al, smaller than or equal to 0.01% of P, smaller than or equal to 0.005% of S and the balance Fe and inevitable impurities. The preparing method includes smelting, hot rolling, cold rolling, pre-quenching and annealing. The high-strength-and ductility-product cold-rolled TRIP steel is high in strength, large in elongation rate, high in strength and ductility product and good in strength and ductility matching, and the forming performance and collision absorbing energy of the steel are greatly improved. Alloys of the steel grade are low in cost, the steel plate welding performance is good, the coating performance is good, the surface quality is good, and the strength and ductility product of the steel can reach 25 GPa.% to 33 GPa.%.
Description
Technical field
The invention belongs to high strength and ductility cold rolled automobile steel technical field, more particularly to a kind of high strength and ductility Cold-Rolled TRIP Steel
And preparation method thereof,
Background technology
In recent years, advanced high-strength steel is developed rapidly.First generation high-strength steel such as two-phase of the strength and ductility product in 15-20GPa%
(DP) steel, phase-change induced plastic (TRIP) steel, complex phase (CP) steel, martensite steel etc. are applied in the car, to automobile
Lightweight serves very important effect.But the formability of the advanced high-strength steel of the first generation has much room for improvement to meet what is increasingly lifted
Automobile Design demand.Used as the twin crystal inducing plasticity (TWIP) of the advanced high-strength steel of the second generation, its strength and ductility product can reach
60GPa%, but because it has relatively low yield strength in performance, alloy content is high in production causes production difficulty
Greatly, the series of factors such as cost height fails to be used widely.The current advanced high-strength steel desired strength of the third generation developed
It is substantially improved compared with first generation AHSS with matching for ductility, to give punching component more preferable formability, gives peace
The complete higher energy-absorbing of part or anticollision deformability, so as to meet the requirement of auto industry technological progress.Therefore, high intensity, height
Formability, high performance-price ratio, the high strength and ductility high-strength steel of stable performance become pursuing a goal for third generation high-strength steel.
In the R＆D process of the first generation high-strength TRIP steel early stage, Ni, Cr of more costliness etc. are added in chemical composition
Alloying element, application is subject to a definite limitation.The TRIP steel researched and developed in recent years mostly is C-Si-Mn systems, and add a certain amount of Nb,
The elements such as V, although with excellent mechanical property, strength and ductility product matching is still unreasonable, and formability has much room for improvement, weldability compared with
Difference, and Si contents are high, not only cause hot rolling to show that oxidation is serious, and also Si aoxidizes the SiO to be formed in galvanizing process2With
Mn2SiO3Cause wettability of the surface of steel plate in liquid Zn to deteriorate, cause coating difficult, poor surface quality.
The content of the invention
To solve above-mentioned technical problem, the present invention passes through to improve Al content, reduces Si contents, optimized production process scheme,
There is provided a kind of intensity height, ductility is big, strength and ductility product is high, the Cold-Rolled TRIP Steel that weldability is excellent.Meanwhile, present invention also offers this is cold
The preparation method of TRIP steel is rolled, preparation method adopts prequenching+annealing process, prequenching to make all horses of the tissue of steel before annealing
Family name's body, so that in annealing process, be more conducive to form substantial amounts of, film-form, stable retained austenite, with this retained austenite
The TRIP effects of family name's body obtain more preferable intensity ductility matching improving the elongation percentage of steel.
The invention provides a kind of high strength and ductility Cold-Rolled TRIP Steel, its chemical composition mass percent is：
C 0.20-0.23%, Si 0.35-0.50%, Mn 2.0-2.4%, Al 1.6-2.5%, P≤0.01%, S≤
0.005%, remaining is Fe and inevitable impurity.
The invention provides a kind of preparation method of high strength and ductility Cold-Rolled TRIP Steel：
Chemical Composition in Cast Billet mass percent be C 0.20-0.23%, Si 0.35-0.50%, Mn 2.0-2.4%,
Al1.6-2.5%, P≤0.01%, S≤0.005%, remaining is Fe and inevitable impurity, and the strand of this chemical composition enters
Row following steps：
1) strand forging, heating, hot rolling, water-cooled are batched, obtains hot rolled strip；
2) hot rolled strip is carried out into pickling, cold rolling, makes cold-rolled strip；
3) cold-rolled strip is carried out into prequenching process, specially：The cold-rolled strip is reheated and is incubated certain
Time, then water quenching obtains the steel band of full martensitic structure to room temperature；
4) by the quenching after full martensitic structure cleaning steel after annealed, rapid water is cooled to necessarily after annealing
Temperature is simultaneously incubated the regular hour, and then rapid water is cooled to room temperature, makes finished product steel belt.
The preparation method of this high strength and ductility Cold-Rolled TRIP Steel, it is characterised in that：
Step 1) described in strand forging after heat, heating-up temperature be 1150-1250 DEG C, temperature retention time 1-3h, four rollings
The passes of machine 6, every time reduction ratio is 30-45%, and 1050 DEG C of hot rolling start rolling temperature, finishing temperature is 800-900 DEG C, then
Water-cooled to 600-680 DEG C and be incubated 0.5-2h simulation batch, subsequent along with the furnace cooling, obtain thickness be 4.8mm hot rolled strip.
Step 2) described in cold rolling step carry out 6 passes and 1 passage skin pass rolling in two cold mills, obtain thickness
For the cold-rolled strip of 1.5mm.
Step 3) described in prequenching processing procedure in, the relation reheating temperature of the cold-rolled strip is 1050-1250 DEG C, is protected
The warm time is 4-10min.
Preferably, step 3) described in prequenching processing procedure in, the relation reheating temperature of the cold-rolled strip is 1080-
1150 DEG C, temperature retention time is 5min.
Step 4) described in annealing temperature be 750-950 DEG C, annealing temperature retention time be 3-7min, be quickly cooled to after annealing
380-480 DEG C, it is incubated 3-7min.
Preferably, step 4) described in annealing temperature be 780-900 DEG C, annealing temperature retention time is 5min, after annealing quickly
400 DEG C are cooled to, 5min is incubated.
The Cold-Rolled TRIP Steel mechanical property that the present invention is produced meets tensile strength 869-977MPa, yield strength 572-
658MPa, elongation percentage 29.3-33.6%, strength and ductility product 25.5-32.8GPa%, the film-form containing 15.7-20.2% in tissue
Retained austenite.
The Cold-Rolled TRIP Steel that the present invention is provided has following features：(1) without the elements such as Ni, Cr, Nb, V, cost of alloy
It is low.(2) employing reduces Si contents and improves the scheme of Al content improving the welding performance of steel plate, and due to Si contents it is low,
The coating of steel plate becomes very excellent, so as to substantially improve surface quality.(3) hardness of steel of the present invention is high, elongation percentage is big, strong
Modeling product is high, intensity and ductility are matched, and substantially increases the formability and impact absorption energy of steel.(4) in cold rolling TRIP of the invention
In the preparation process of steel, all lath martensites of tissue of steel before heat treatment are conducive to forming substantial amounts of, thin-film state during annealing
Retained austenite.The retained austenite of this thin-film state can not only improve steel compared with equiaxial state, block retained austenite
Elongation percentage, and its stability in steel is very high, is applied to after prepared by auto parts and components, such as vehicle collision,
There is martensite transfor mation in a large amount of thin-film state retained austenites, instantaneous induced plastic increases, and effectively carries out crash energy absorption, and then
Substantially increase automotive crash safety coefficient.
Description of the drawings：
Fig. 1 is the SEM-EBSD photos of the comparative example 3 of strength and ductility product 25.5GPa% of the present invention
Fig. 2 is the SEM-EBSD photos of the embodiment 1 of strength and ductility product 32.8GPa% of the present invention
Specific embodiment
The invention provides a kind of high strength and ductility Cold-Rolled TRIP Steel, its chemical composition mass percent is：C 0.20-
0.23%, Si 0.35-0.50%, Mn 2.0-2.4%, Al 1.6-2.5%, P≤0.01%, S≤0.005%, remaining is Fe
With inevitable impurity.
The invention provides a kind of preparation method of high strength and ductility Cold-Rolled TRIP Steel, Chemical Composition in Cast Billet amount percentage is C
0.20-0.23%, Si 0.35-0.50%, Mn 2.0-2.4%, Alt 1.6-2.5%, P≤0.01%, S≤0.005%,
Remaining is Fe and inevitable impurity, and the strand for meeting this chemical composition is carried out into following preparation process：
1) strand forging, heating, hot rolling, water-cooled are batched, obtains hot rolled strip；
2) hot rolled strip is carried out into pickling, cold rolling, makes cold-rolled strip；
3) cold-rolled strip is carried out into prequenching process, specially：The cold-rolled strip is reheated and is incubated certain
Time, then water quenching obtains the steel band of full martensitic structure to room temperature；
4) by the quenching after full martensitic structure cleaning steel after annealed, rapid water is cooled to necessarily after annealing
Temperature is simultaneously incubated the regular hour, and then rapid water is cooled to room temperature, makes finished product steel belt.
The preparation method of this high strength and ductility Cold-Rolled TRIP Steel, it is characterised in that：
Step 1) described in strand forging after heat, heating-up temperature be 1150-1250 DEG C, temperature retention time 1-3h, four rollings
The passes of machine 6, every time reduction ratio is 30-45%, and 1050 DEG C of hot rolling start rolling temperature, finishing temperature is 800-900 DEG C, then
Water-cooled to 600-680 DEG C and be incubated 0.5-2h simulation batch, subsequent along with the furnace cooling, obtain thickness be 4.8mm hot rolled strip.
Step 2) described in cold rolling step carry out 6 passes and 1 passage skin pass rolling in two cold mills, obtain thickness
For the cold-rolled strip of 1.5mm.
Step 3) described in prequenching processing procedure in, the relation reheating temperature of the cold-rolled strip is 1050-1250 DEG C, is protected
The warm time is 4-10min.
Preferably, step 3) described in prequenching processing procedure in, the relation reheating temperature of the cold-rolled strip is 1080-
1150 DEG C, temperature retention time is 5min.
Step 4) described in annealing temperature be 750-950 DEG C, annealing temperature retention time be 3-7min, be quickly cooled to after annealing
380-480 DEG C, it is incubated 3-7min.
Preferably, step 4) described in annealing temperature be 780-900 DEG C, annealing temperature retention time is 5min, after annealing quickly
400 DEG C are cooled to, 5min is incubated.
The Cold-Rolled TRIP Steel mechanical property that the present invention is produced meets tensile strength 869-977MPa, yield strength 572-
658MPa, elongation percentage 29.3-33.6%, strength and ductility product 25.5-32.8GPa%, the film-form containing 15.7-20.2% in tissue
Retained austenite.
In order to understand the present invention in depth, below in conjunction with the accompanying drawings, specific embodiment and comparative example carried out in detail to the present invention
Describe in detail bright.
Comparative example 1
Chemical Composition in Cast Billet (mass percent %) is 0.20%C, 1.5%Si, 1.78%Mn, 0.035%Al, 0.01%
P, 0.005%S, remaining is Fe and inevitable impurity.1200 DEG C are heated to after strand is forged, 2h, four-roller rolling 6 is incubated
Passes, 1050 DEG C of start rolling temperature, 850 DEG C of finishing temperature, water-cooled to 640 DEG C and be incubated 1h simulation batch, it is subsequently cold with stove
But, the hot rolled strip that thickness is 4.8mm is obtained.It is flat 6 passes and 1 passage to be carried out after acid washing of hot rolled steel strip in two cold mills
Whole rolling, obtains the thick cold-rolled strips of 1.5mm.Cold-rolled strip is made annealing treatment, 800 DEG C of holding temperature of annealing, temperature retention time
5min, is subsequently cooled to 420 DEG C of insulation 5min, and after being subsequently cooled to less than 200 DEG C room temperature is naturally cooled to.The power of finished product steel belt
Learn performance as shown in table 2.
Comparative example 2
Strand main chemical compositions (mass percent %) as shown in table 1, also contain 0.01%P, 0.004%S,
0.005%N, remaining is Fe and inevitable impurity.Preparation process is essentially identical with preparation method described in comparative example 1, uniquely
It is distinguished as, the annealing holding temperature of comparative example 2 is 820 DEG C.The mechanical property for obtaining finished product steel belt is as shown in table 2.
Comparative example 3
Strand main chemical compositions (mass percent %) as shown in table 1, also contain 0.007%P, 0.006%S,
0.004%N, remaining is Fe and inevitable impurity.Preparation process is essentially identical with preparation method described in comparative example 1, uniquely
It is distinguished as, the annealing holding temperature of comparative example 3 is respectively 780 DEG C, 850 DEG C, 900 DEG C, is subsequently cooled to 400 DEG C.Obtain finished product
The mechanical property of steel band is as shown in table 2.
Comparative example 4
Strand main chemical compositions (mass percent %) as shown in table 1, also contain 0.009%P, 0.004%S,
0.005%N, remaining is Fe and inevitable impurity.Preparation process is adopted and obtained with the identical hot rolling of comparative example 1, cold rolling step
To cold-rolled strip；Then prequenching step is carried out, cold-rolled strip is again heated to into 1100 DEG C, be incubated 5min, subsequent water quenching is to room
Temperature；Annealing steps are subsequently carried out, room temperature steel band is heated to into 950 DEG C of insulation 5min, be then quickly cooled to 400 DEG C of insulations
5min, obtains finished product steel belt.Its mechanical property is as shown in table 2.
Embodiment 1
Strand main chemical compositions (mass percent %) as shown in table 1, also contain 0.006%P, 0.003%S,
0.004%N, remaining is Fe and inevitable impurity.Preparation process is essentially identical with comparative example 4, only difference is that, implements
Room temperature steel band is separately heated to into 780 DEG C, 850 DEG C, 900 DEG C in the annealing steps of example 1.Obtain the mechanical property of finished product steel belt such as
Shown in table 2.
Embodiment 2
Strand main chemical compositions (mass percent %) as shown in table 1, also contain 0.005%P, 0.004%S,
0.002%N, remaining is Fe and inevitable impurity.Preparation process is adopted and obtained with the identical hot rolling of comparative example 1, cold rolling step
To cold-rolled strip；Then cold-rolled strip is again heated to into 1150 DEG C, is incubated 6min, subsequent water quenching is to room temperature；Subsequently annealed
Step, by room temperature steel band 780 DEG C and 850 DEG C are separately heated to, and are incubated 4min and 6min respectively, are then quickly cooled to respectively
425 DEG C of insulation 6min, obtain finished product steel belt.Its mechanical property is as shown in table 2.
Embodiment 3
Strand main chemical compositions (mass percent %) as shown in table 1, also contain 0.007%P, 0.004%S,
0.003%N, remaining is Fe and inevitable impurity.Preparation process is adopted and obtained with the identical hot rolling of comparative example 1, cold rolling step
To cold-rolled strip；Then cold-rolled strip is again heated to into 1200 DEG C, is incubated 8min, subsequent water quenching is to room temperature；Subsequently annealed
Step, by room temperature steel band 850 DEG C and 900 DEG C are separately heated to, and are incubated 6min and 7min respectively, are then quickly cooled to respectively
445 DEG C of insulation 7min, obtain finished product steel belt.Its mechanical property is as shown in table 2.
The chemical composition and annealing process of the embodiment of table 1 and comparative example
The finished product mechanical property of table 2 and retained austenite are quantitative
As can be seen from Table 2：
(1) embodiment of the present invention 1, embodiment 2, embodiment 3 are bent using the Cold-Rolled TRIP Steel of prequenching+annealing process production
Intensity 527-658MPa, tensile strength 869-977MPa, elongation percentage 29.3-33.6%, strength and ductility product 25.5-32.8GPa% are taken,
Film-form retained austenite containing 15.7-20.2% in tissue.Although embodiment 1, embodiment 2,3 three kinds of embodiment are different
The end properties that composition is obtained under different heat treatment technique have certain fluctuation, and as the rising of Al content has decline to become
Gesture, but property indices are above comparative example 1, comparative example 2, the comparative example 3 of conventional annealing technique.And with reference to the composition of table 1
Can see, comparative example 1 and comparative example 2 can cause finished surface degradation containing about 1.5% Si, and coating is difficult.
In addition, comparative example 3 also contains Nb, V, cost of alloy is high.
(2) composition is identical, annealing temperature identical comparative example 3 is compared with embodiment 1, although the yield strength of comparative example 3
1005-1127MPa can be reached, but its elongation percentage is only 16.4-25.3%, so as to cause its strength and ductility product to be less than embodiment 1.
(3) composition identical comparative example 4 is compared with embodiment 1, and the elongation percentage of comparative example 4 declines clearly, illustrates 950
DEG C when, the austenitizing degree in steel is larger, carries out producing more volume hundred during bainite transformation being cooled to 400 DEG C
Divide the bainite of ratio, so as to reduce the ductility of steel.Therefore 950 DEG C is not preferably to be heat-treated heating-up temperature.
It should be noted last that, above-described specific embodiment, to the purpose of the present invention, technical scheme and beneficial
Effect is further described, and should be understood that the specific embodiment that the foregoing is only the present invention, and
It is non-for limiting the present invention, all any modifications within the spirit and principle of technical solution of the present invention, made, equivalent,
Improve etc., should be included within the claims of the present invention.
Claims (8)
1. a kind of high strength and ductility Cold-Rolled TRIP Steel, it is characterised in that the chemical composition mass percent of the Cold-Rolled TRIP Steel is：
C 0.20-0.23%, Si 0.35-0.50%, Mn 2.0-2.4%, Al 1.6-2.5%, P≤0.01%, S≤
0.005%, remaining is Fe and inevitable impurity.
2. a kind of preparation method of high strength and ductility Cold-Rolled TRIP Steel as claimed in claim 1, it is characterised in that preparation process bag
Include：
1) strand forging, heating, hot rolling, water-cooled are batched, obtains hot rolled strip；
2) hot rolled strip is carried out into pickling, cold rolling, makes cold-rolled strip；
3) cold-rolled strip is carried out into prequenching process, specially：When the cold-rolled strip being reheated and is incubated certain
Between, room temperature is then quenched to, obtain the steel band of full martensitic structure；
4) by the quenching after full martensitic structure cleaning steel after annealed, rapid water is cooled to uniform temperature after annealing
And the regular hour is incubated, then rapid water is cooled to room temperature, makes finished product steel belt.
3. a kind of preparation method of high strength and ductility Cold-Rolled TRIP Steel as claimed in claim 2, it is characterised in that step 1) it is described
Strand forging after heat, heating-up temperature be 1150-1250 DEG C, temperature retention time 1-3h, the passes of four-high mill 6, every time
Reduction ratio is 30-45%, 1050 DEG C of hot rolling start rolling temperature, and finishing temperature is 800-900 DEG C, then water-cooled to 600-680 DEG C simultaneously
Insulation 0.5-2h simulations are batched, and subsequent along with the furnace cooling obtains the hot rolled strip that thickness is 4.8mm.
4. a kind of preparation method of high strength and ductility Cold-Rolled TRIP Steel as claimed in claim 2, it is characterised in that step 2) it is described
Cold rolling step carry out 6 passes and 1 passage skin pass rolling in two cold mills, obtain thickness be 1.5mm cold-rolled strip.
5. a kind of preparation method of high strength and ductility Cold-Rolled TRIP Steel as claimed in claim 2, it is characterised in that step 3) it is described
Prequenching processing procedure in, the relation reheating temperature of the cold-rolled strip is 1050-1250 DEG C, and temperature retention time is 4-10min.
6. a kind of preparation method of high strength and ductility Cold-Rolled TRIP Steel as claimed in claim 5, it is characterised in that step 3) it is described
Prequenching processing procedure in, the relation reheating temperature of the cold-rolled strip is 1080-1150 DEG C, and temperature retention time is 5min.
7. a kind of preparation method of high strength and ductility Cold-Rolled TRIP Steel as claimed in claim 2, it is characterised in that step 4) it is described
Annealing temperature be 750-950 DEG C, annealing temperature retention time is 3-7min, is quickly cooled to 380-480 DEG C after annealing, insulation 3-
7min。
8. a kind of preparation method of high strength and ductility Cold-Rolled TRIP Steel as claimed in claim 7, it is characterised in that step 4) it is described
Annealing temperature be 780-900 DEG C, annealing temperature retention time is 5min, is quickly cooled to 400 DEG C after annealing, insulation 5min.
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107460408A (en) * | 2017-09-04 | 2017-12-12 | 东北大学 | A kind of superelevation strong TRIP steel more than 1.5GPa levels and preparation method thereof |
| CN107794357A (en) * | 2017-10-26 | 2018-03-13 | 北京科技大学 | The method of super rapid heating technique productions superhigh intensity martensite cold-rolled steel sheet |
| CN108179256A (en) * | 2018-02-06 | 2018-06-19 | 东北大学 | A kind of heat treatment method for improving Cold-Rolled TRIP Steel strength and ductility product |
| CN109182923A (en) * | 2018-11-14 | 2019-01-11 | 东北大学 | A kind of low-carbon microalloyed high strength and ductility cold rolling TRIP980 Heat-Treatment of Steel method |
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| CN107460408A (en) * | 2017-09-04 | 2017-12-12 | 东北大学 | A kind of superelevation strong TRIP steel more than 1.5GPa levels and preparation method thereof |
| CN107794357A (en) * | 2017-10-26 | 2018-03-13 | 北京科技大学 | The method of super rapid heating technique productions superhigh intensity martensite cold-rolled steel sheet |
| CN107794357B (en) * | 2017-10-26 | 2018-09-14 | 北京科技大学 | The method of super rapid heating technique productions superhigh intensity martensite cold-rolled steel sheet |
| WO2019080659A1 (en) * | 2017-10-26 | 2019-05-02 | 北京科技大学 | Method for producing ultra high strength martensitic cold-rolled steel sheet by means of ultra fast heating process |
| EP3702477A4 (en) * | 2017-10-26 | 2021-03-31 | University Of Science And Technology Beijing | Method for producing ultra high strength martensitic cold-rolled steel sheet by means of ultra fast heating process |
| US11261504B2 (en) | 2017-10-26 | 2022-03-01 | University Of Science And Technology Beijing | Method for producing ultra-high-strength martensitic cold-rolled steel sheet by ultra rapid heating process |
| CN108179256A (en) * | 2018-02-06 | 2018-06-19 | 东北大学 | A kind of heat treatment method for improving Cold-Rolled TRIP Steel strength and ductility product |
| CN109182923A (en) * | 2018-11-14 | 2019-01-11 | 东北大学 | A kind of low-carbon microalloyed high strength and ductility cold rolling TRIP980 Heat-Treatment of Steel method |
| CN109182923B (en) * | 2018-11-14 | 2021-09-10 | 东北大学 | Heat treatment method of low-carbon microalloyed cold-rolled TRIP980 steel with high product of strength and elongation |
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