CN106636925B - A kind of high strength and ductility Cold-Rolled TRIP Steel and preparation method thereof - Google Patents
A kind of high strength and ductility Cold-Rolled TRIP Steel and preparation method thereof 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
- C22C38/04—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
Abstract
The invention discloses a kind of high strength and ductility Cold-Rolled TRIP Steels and preparation method thereof, belong to high strength and ductility cold rolled automobile steel technical field.The chemical composition mass percent of the high strength and ductility Cold-Rolled TRIP Steel is：C0.20 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.Preparation method includes smelting, hot rolling, cold rolling, prequenching, annealing.Hardness of steel of the present invention is high, elongation percentage is big, strength and ductility product is high, intensity and ductility match, and substantially increases the formability of steel and impact absorption energy.This steel grade cost of alloy is low, and the good welding performance of steel plate, coating are excellent, and surface quality is good, and the strength and ductility product of steel is up to 25 33GPa%.
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 rapidly develops.Strength and ductility product is in the first generation high-strength steel such as two-phase of 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 plays the role of very important.But the formability of the advanced high-strength steel of the first generation has much room for improvement to meet what is increasingly promoted
Automobile Design demand.As the twinning induced plasticity (TWIP) of the advanced high-strength steel of the second generation, strength and ductility product can reach
60GPa%, but since it has relatively low yield strength in performance, alloy content is high so that production difficulty in production
Greatly, the series of factors such as of high cost fail to be used widely.The current advanced high-strength steel desired strength of the third generation being developed
Matching with ductility is substantially improved compared with first generation advanced high-strength steel, to assign punching component better formability, assigns 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
The high strength and ductility high-strength steel that formability, high performance-price ratio, performance are stablized becomes 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, using being subject to certain restrictions.The TRIP steel researched and developed in recent years is mostly C-Si-Mn systems, and add in 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, and not only so that hot rolling shows that oxidation is serious, but also Si aoxidizes the SiO to be formed in galvanizing process2With
Mn2SiO3Wettability of the surface of steel plate in liquid Zn is caused to deteriorate, causes coating difficult, poor surface quality.
The content of the invention
In order to solve the above technical problems, it is of the invention by improving Al content, reducing Si contents, optimized production process scheme,
Provide the Cold-Rolled TRIP Steel that a kind of intensity is high, ductility is big, strength and ductility product is high, weldability is excellent.It is meanwhile cold the present invention also provides this
The preparation method of TRIP steel is rolled, preparation method uses prequenching+annealing process, and prequenching makes all horses of tissue of steel before annealing
Family name's body so that in annealing process, more conducively forms retained austenite substantial amounts of, film-form, stablizing, with this retained austenite
The TRIP effects of family name's body improve the elongation percentage of steel, obtain better intensity ductility matching.
The present invention provides a kind of high strength and ductility Cold-Rolled TRIP Steel, 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 present invention provides a kind of preparation methods of high strength and ductility Cold-Rolled TRIP Steel：
Chemical Composition in Cast Billet mass percent is 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, the strand of this chemical composition into
Row following steps：
1) strand forging, heating, hot rolling, water cooling are batched, obtains hot rolled strip；
2) hot rolled strip is subjected to pickling, cold rolling, cold-rolled strip is made；
3) cold-rolled strip is subjected to prequenching processing, is specially：The cold-rolled strip is reheated and kept the temperature certain
Time, then water quenching to room temperature obtains the steel band of full martensitic structure；
4) will anneal after the cleaning steel of the quenched full martensitic structure, quick water cooling is to certain after annealing
Temperature simultaneously keeps the temperature the regular hour, and then quick water cooling to room temperature, is made finished product steel belt.
The preparation method of this high strength and ductility Cold-Rolled TRIP Steel, it is characterised in that：
It is heated after strand forging described in step 1), heating temperature is 1150-1250 DEG C, soaking time 1-3h, four rollings
6 passes of machine, every time reduction ratio are 30-45%, and 1050 DEG C of hot rolling start rolling temperature, finishing temperature is 800-900 DEG C, then
Water cooling to 600-680 DEG C and keep the temperature 0.5-2h simulation batch, subsequent furnace cooling, obtain thickness be 4.8mm hot rolled strip.
Cold rolling step described in step 2) carries out 6 passes and 1 passage skin pass rolling in two cold mills, obtains thickness
For the cold-rolled strip of 1.5mm.
In prequenching processing procedure described in step 3), the relation reheating temperature of the cold-rolled strip is 1050-1250 DEG C, is protected
The warm time is 4-10min.
Preferably, in the prequenching processing procedure described in step 3), the relation reheating temperature of the cold-rolled strip is 1080-
1150 DEG C, soaking time 5min.
Annealing temperature described in step 4) is 750-950 DEG C, and annealing soaking time is 3-7min, is quickly cooled to after annealing
380-480 DEG C, keep the temperature 3-7min.
Preferably, the annealing temperature described in step 4) is 780-900 DEG C, and annealing soaking time is 5min, quick after annealing
400 DEG C are cooled to, keeps the temperature 5min.
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.
Cold-Rolled TRIP Steel provided by the invention has following features：(1) without the elements such as Ni, Cr, Nb, V, cost of alloy
It is low.(2) employing the scheme of reduction Si content raising Al contents improves the welding performance of steel plate, and since Si contents are 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 match, and substantially increases the formability of steel and impact absorption energy.(4) in cold rolling TRIP of the present invention
In the preparation process of steel, all lath martensites of the tissue of steel before heat treatment are conducive to form 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 isometric state, block-like 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,
Martensite transfor mation occurs for a large amount of thin-film state retained austenites, and 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 present invention provides a kind of high strength and ductility Cold-Rolled TRIP Steel, 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 present 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 following preparation process：
1) strand forging, heating, hot rolling, water cooling are batched, obtains hot rolled strip；
2) hot rolled strip is subjected to pickling, cold rolling, cold-rolled strip is made；
3) cold-rolled strip is subjected to prequenching processing, is specially：The cold-rolled strip is reheated and kept the temperature certain
Time, then water quenching to room temperature obtains the steel band of full martensitic structure；
4) will anneal after the cleaning steel of the quenched full martensitic structure, quick water cooling is to certain after annealing
Temperature simultaneously keeps the temperature the regular hour, and then quick water cooling to room temperature, is made finished product steel belt.
The preparation method of this high strength and ductility Cold-Rolled TRIP Steel, it is characterised in that：
It is heated after strand forging described in step 1), heating temperature is 1150-1250 DEG C, soaking time 1-3h, four rollings
6 passes of machine, every time reduction ratio are 30-45%, and 1050 DEG C of hot rolling start rolling temperature, finishing temperature is 800-900 DEG C, then
Water cooling to 600-680 DEG C and keep the temperature 0.5-2h simulation batch, subsequent furnace cooling, obtain thickness be 4.8mm hot rolled strip.
Cold rolling step described in step 2) carries out 6 passes and 1 passage skin pass rolling in two cold mills, obtains thickness
For the cold-rolled strip of 1.5mm.
In prequenching processing procedure described in step 3), the relation reheating temperature of the cold-rolled strip is 1050-1250 DEG C, is protected
The warm time is 4-10min.
Preferably, in the prequenching processing procedure described in step 3), the relation reheating temperature of the cold-rolled strip is 1080-
1150 DEG C, soaking time 5min.
Annealing temperature described in step 4) is 750-950 DEG C, and annealing soaking time is 3-7min, is quickly cooled to after annealing
380-480 DEG C, keep the temperature 3-7min.
Preferably, the annealing temperature described in step 4) is 780-900 DEG C, and annealing soaking time is 5min, quick after annealing
400 DEG C are cooled to, keeps the temperature 5min.
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 the present invention in detail
It describes 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, keeps the temperature 2h, four-roller rolling 6
Passes, 1050 DEG C of start rolling temperature, 850 DEG C of finishing temperature, water cooling to 640 DEG C and keep the temperature 1h simulation batch, then with furnace cooling
But, the hot rolled strip that thickness is 4.8mm is obtained.6 passes are carried out in two cold mills and 1 passage is put down after acid washing of hot rolled steel strip
Whole rolling obtains the cold-rolled strip of 1.5mm thickness.Cold-rolled strip is made annealing treatment, 800 DEG C of holding temperature of annealing, soaking time
5min is subsequently cooled to 420 DEG C of heat preservation 5min, cooled to room temperature after being subsequently cooled to less than 200 DEG C.The power of finished product steel belt
It is as shown in table 2 to learn performance.
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 and preparation method described in comparative example 1 are essentially identical, 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 and preparation method described in comparative example 1 are essentially identical, 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 obtained using the hot rolling identical with comparative example 1, cold rolling step
To cold-rolled strip；Then prequenching step is carried out, cold-rolled strip is again heated to 1100 DEG C, keeps the temperature 5min, subsequent water quenching to room
Temperature；Annealing steps are then carried out, room temperature steel band is heated to 950 DEG C of heat preservation 5min, is then quickly cooled to 400 DEG C of heat preservations
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 and comparative example 4 are essentially identical, only difference is that, implement
Room temperature steel band is separately heated to 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 obtained using the hot rolling identical with comparative example 1, cold rolling step
To cold-rolled strip；Then cold-rolled strip is again heated to 1150 DEG C, keeps the temperature 6min, subsequent water quenching to room temperature；Then anneal
Room temperature steel band is separately heated to 780 DEG C and 850 DEG C, and keeps the temperature 4min and 6min respectively by step, is then quickly cooled to respectively
425 DEG C of heat preservation 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 obtained using the hot rolling identical with comparative example 1, cold rolling step
To cold-rolled strip；Then cold-rolled strip is again heated to 1200 DEG C, keeps the temperature 8min, subsequent water quenching to room temperature；Then anneal
Room temperature steel band is separately heated to 850 DEG C and 900 DEG C, and keeps the temperature 6min and 7min respectively by step, is then quickly cooled to respectively
445 DEG C of heat preservation 7min, obtain finished product steel belt.Its mechanical property is as shown in table 2.
The chemical composition and annealing process of 1 embodiment of table and comparative example
2 finished product mechanical property of table and retained austenite quantify
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 ingredient obtains under different heat treatment technique have certain fluctuation, and have decline to become with the rise of Al content
Gesture, but property indices are above the comparative example 1, comparative example 2, comparative example 3 of conventional annealing technique.And combine the ingredient of table 1
It can be seen that comparative example 1 and comparative example 2 contain about 1.5% Si, finished surface degradation can be caused, coating is difficult.
In addition, comparative example 3 is also containing Nb, V, cost of alloy height.
(2) comparative example 3 that ingredient is identical, annealing temperature is identical 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%, is less than embodiment 1 so as to cause its strength and ductility product.
(3) the identical comparative example 4 of ingredient 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 transformations being cooled to 400 DEG C
Divide the bainite of ratio, so as to reduce the ductility of steel.Therefore 950 DEG C are not preferable heat treatment heating temperatures.
It should be noted last that above-described specific embodiment, to the purpose of the present invention, technical solution and beneficial
Effect has been further described, it should be understood that the foregoing is merely the specific embodiment of the present invention, and
Be not intended to limit the invention, it is all within the spirit and principle of technical solution of the present invention, any modification for being made, equivalent substitution,
Improve etc., it should be included within the claims of the present invention.
Claims (4)
1. a kind of high strength and ductility Cold-Rolled TRIP Steel, which is characterized 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；
The Cold-Rolled TRIP Steel mechanical property 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 retained austenite containing 15.7-20.2% in tissue.
A kind of 2. preparation method of high strength and ductility Cold-Rolled TRIP Steel as described in claim 1, which is characterized in that preparation process bag
It includes：
1) the strand forging for meeting the Cold-Rolled TRIP Steel chemical composition, heating, hot rolling, water cooling are batched, obtains hot rolled strip；
2) hot rolled strip is subjected to pickling, cold rolling, cold-rolled strip is made；
3) cold-rolled strip is subjected to prequenching processing, is specially：When the cold-rolled strip is reheated and keeps the temperature certain
Between, room temperature is then quenched to, obtains the steel band of full martensitic structure；
4) it will anneal, quick water cooling and kept the temperature after annealing, so after the cleaning steel of the quenched full martensitic structure
Finished product steel belt is made to room temperature in quick water cooling afterwards；
It is heated after strand forging described in step 1), heating temperature is 1150-1250 DEG C, soaking time 1-3h, four-high mill 6
Secondary rolling, every time reduction ratio are 30-45%, and 1050 DEG C of hot rolling start rolling temperature, finishing temperature is 800-900 DEG C, then water cooling
To 600-680 DEG C and keep the temperature 0.5-2h simulation batch, subsequent furnace cooling, obtain thickness be 4.8mm hot rolled strip；
Cold rolling step described in step 2) carries out 6 passes and 1 passage skin pass rolling in two cold mills, and obtaining thickness is
The cold-rolled strip of 1.5mm；
In prequenching processing procedure described in step 3), the relation reheating temperature of the cold-rolled strip is 1050-1250 DEG C, during heat preservation
Between be 4-10min；
Annealing temperature described in step 4) is 750-950 DEG C, and annealing soaking time is 3-7min, and 380- is quickly cooled to after annealing
480 DEG C, keep the temperature 3-7min.
3. a kind of preparation method of high strength and ductility Cold-Rolled TRIP Steel as claimed in claim 2, which is characterized in that step 3) is described
Prequenching processing procedure in, the relation reheating temperature of the cold-rolled strip is 1080-1150 DEG C, soaking time 5min.
4. a kind of preparation method of high strength and ductility Cold-Rolled TRIP Steel as claimed in claim 2, which is characterized in that step 4) is described
Annealing temperature for 780-900 DEG C, annealing soaking time is 5min, 400 DEG C is quickly cooled to after annealing, heat preservation 5min.
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| CN107460408B (en) * | 2017-09-04 | 2019-04-30 | 东北大学 | Strong TRIP steel of a kind of 1.5GPa grades or more of superelevation and preparation method thereof |
| 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 |
| 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 |
| 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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| JP4288364B2 (en) * | 2004-12-21 | 2009-07-01 | 株式会社神戸製鋼所 | Composite structure cold-rolled steel sheet with excellent elongation and stretch flangeability |
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| US6328826B1 (en) * | 1999-07-30 | 2001-12-11 | Usinor | Method of fabricating “TRIP” steel in the form of thin strip, and thin strip obtained in this way |
| CN101058863A (en) * | 2007-06-11 | 2007-10-24 | 北京科技大学 | Hot-rolled low-silicon multiphase steel and preparation method thereof |
| CN105063311A (en) * | 2015-09-18 | 2015-11-18 | 东北大学 | Processing method for improving surface quality of TRIP steel |
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