CN103045941B - A kind of heat treating method of high-strong toughness Multiphase Steel - Google Patents
A kind of heat treating method of high-strong toughness Multiphase Steel Download PDFInfo
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Abstract
A kind of high-strong toughness Multiphase Steel of the present invention and heat treating method thereof belong to steel alloy technical field of producing; Technical problem to be solved realizes utilizing deformation induced ferrite district to be out of shape to carry out crystal grain thinning, utilize the regulation and control that Q & P technique realizes hard phase martensite and soft phase residual austenite, while increasing the intensity of steel, ensure that again it has good toughness; The technical scheme adopted is: a kind of high-strong toughness Multiphase Steel, and the component comprised and weight percent content are: C:0.10%-0.25%, Si:0.5%-1.0%, Mn:1.2%-1.8%, Ti:0.01%-0.05%, B:0.001%-0.003%, S :≤0.01%, P :≤0.01%, all the other are Fe; Its heat treating method is: the first step, and steel is heated to austenitizing temperature, and is incubated 3-30min; Second step, is cooled fast to critical temperature by steel, in this temperature range, carry out deformation induced trans-formation; 3rd step, quenches steel in the quenchant of 50-370 DEG C, and is incubated 5-600s; 4th step, quenches steel in room temperature water; Relative to Q & P steel, the steel good combination property that the present invention obtains, cost is low.
Description
Technical field
The invention belongs to steel alloy technical field of producing, be specifically related to a kind of low-alloy ultra-high strength and toughness Multiphase Steel and production technique thereof.
Background technology
At present, the first-generation automobile steel (as DP steel, TRIP steel) with lower strength and ductility product can not meet the double requirements of automotive industry future development to lightweight and high safety.The strength and ductility product of s-generation automobile steel (as TWIP steel), far away higher than first-generation automobile steel, has very high collision energy-absorbing ability and good forming ability.But be less than the first-generation automobile steel of 5% compared to alloy content, its total alloy content, up to more than 25%, causes that its cost is higher, processing performance is poor and metallurgical production is difficult larger.Economize on resources to meet, reduce costs, the requirement of automotive light weight technology and raising security, in the urgent need to research and development have cost close to the first-generation automobile steel performance close to the high strength and low cost high-ductility third generation automobile steel of s-generation automobile steel.
Q & P steel is the third generation automobile steel with higher-strength and toughness grown up in recent years.Its ultimate principle is: containing Si or (with) first after austenitizing, to be quenched to Ms ~ Mf(Ms be Ms (martensite start) point for the steel part of Al, Mf is martensitic transformation end temp) between a certain temperature, namely martensite and the residual austenite of some amount is formed, stay for some time in this initial quench temperature or a certain temperature of more than Ms again, carbon is distributed to residual austenite by martensite, carbon content now in martensite declines, carbon content in austenite raises, thus make the rich carbon of residual austenite and can stablize to room temperature, finally obtain the complex tissue be made up of martensite and residual austenite, thus obtain higher intensity and toughness, namely good comprehensive mechanical property.
But, along with the development of automotive industry, more and more higher requirement is proposed to the intensity of advanced high-strength steel and toughness.Although the Q & P steel intensity obtained is higher, its plasticity is poor.In addition, because its intensity is higher, largely reducing its welding property.Therefore, from the obdurability and the weldability that improve steel, and the angle consideration economizing on resources, reduce costs, the over-all properties improving Q & P steel is further significant.
Through finding the literature search of prior art, Xu ancestral shines academician at International Heat Treatment and Surface Engineering, 2008,2 (2), 64-68. delivers " Quenching-partitioning-tempering (Q-P-T) process for ultra-high strength steel " civilian, set forth the principle of quenching-carbon distribution-tempering (Q-P-T) technique, what utilize is that Carbide Precipitation strengthening improves the intensity of steel, finally obtains the heterogeneous structure of martensite, residual austenite and carbide.Also find in retrieval, the patent No. is the Chinese patent of 200810033295.7, this patent obtains the three-phase contexture of martensite, residual austenite and nanometer bainite, and the nanometer bainite utilizing low temperature long time treatment to obtain improves the comprehensive mechanical property of steel further.Recently, J. G. Speer etc. are at Metallurgical and Materials Transactions A, 2011,42 (12), 3652-3659. delivers " Quenched and Partitioned Microstructures Produced via Gleeble Simulations of Hot-Strip Mill Cooling Practices " civilian, point out that the obdurability by improving Q & P steel in high temperature hot rolling is effective, but do not introduce ferritic structure.In a word, above research is not all introduced ferritic structure and is made structure refinement to improve the obdurability of steel simultaneously.
Summary of the invention
The present invention overcomes the deficiency that prior art exists, technical problem to be solved is for providing a kind of low-alloy ultra-high strength and toughness Multiphase Steel and heat treating method thereof, achieve distortion, phase transformation and carbon and distribute the high-strength steel design philosophy combined, utilize deformation induced ferrite district to be out of shape and carry out crystal grain thinning, utilize the regulation and control that Q & P technique realizes hard phase martensite and soft phase residual austenite, ensure that again it has good toughness while increasing the intensity of steel, and achieve low alloying, with low cost.
In order to solve the problems of the technologies described above, the technical solution used in the present invention is: a kind of heat treating method of high-strong toughness Multiphase Steel, and the component that described high-strong toughness Multiphase Steel comprises and weight percent content are: C:0.10%-0.25%, Si:0.5%-1.0%, Mn:1.2%-1.8%, Ti:0.01%-0.05%, B:0.001%-0.003%, S :≤0.01%, P :≤0.01%, all the other are Fe, it is characterized in that, mainly comprise the following steps:
The first step, by steel with the heating rate of 30 DEG C/s to austenitizing temperature 860-1000 DEG C, and be incubated 3-30min;
Second step, the steel the first step obtained is cooled fast to critical temperature 700-800 DEG C with the speed of 80 DEG C/s, and carries out deformation induced trans-formation in this temperature range, and strain rate is 0.6-5s
-1, reduction in pass is 51-80%, makes grain refining and generates deformation induced ferrite;
3rd step, the steel obtained by second step is quenched in the liquid quenching medium of 50-370 DEG C, to obtain martensite and residual austenite body tissue, and realizes carbon distribution at this temperature range inside holding 5-600s, carbon atom is fully spread, with stable austenite from supersaturation martensite to not changing austenite;
4th step, quenches in room temperature water by the steel that the 3rd step obtains, and obtains the heterogeneous structure of thin lath dislocation type martensite+thin thin residual austenite+deformation induced ferrite.
Temperature in the described the first step is 900 DEG C, and soaking time is 5min.
In described second step, strain rate is 1s
-1, reduction in pass is 60%.
In described 3rd step, quenching temperature is 300 DEG C, and soaking time is 60s.
The present invention compared with prior art has following beneficial effect.
The present invention is not using in expensive alloy element situation, is improved toughness and the plasticity of steel by tissue modulation further.This is because: for ensureing the high strength of steel, its matrix need select martensitic stucture, and this martensitic stucture based on the thin lath martensite containing high density dislocation, secondly, should will have retained austenitic film between martensite lath.On this basis, allowed in tissue by tissue modulation and there are some ferrites, and allow grain refining simultaneously, obtain a kind of martensite of refinement, residual austenite and ferritic heterogeneous structure.The retained austenitic film that will exist between martensite lath, mainly in order to make steel residual austenite when being subject to External Force Acting that TRIP effect occur, improves the plasticity of steel.Ferritic introducing not only to improving the intensity of steel and plasticity has contribution, and to the coordination between hard phase martensite and soft phase austenite, play vital effect for the stability of residual austenite.Structure refinement is this is because close grain is subject to external force generation viscous deformation dispersibles and carry out in more crystal grain, and viscous deformation is comparatively even, and stress concentration is less.In addition, crystal grain is thinner, and grain boundary area is larger, and crystal boundary is more tortuous, is more unfavorable for the expansion of crackle.
The present invention is at high temperature thermal deformation generation deformation-induced ferrite transformation, then makes it quench and carries out carbon distribution, finally obtains the martensite of certain volume mark, residual austenite and ferritic three-phase composite tissue.Thus making steel have excellent mechanical property, tensile strength is 1500-1900MPa, and unit elongation is 15-30%.Relative to Q & P steel, the steel good combination property that the present invention obtains, cost is low.
Accompanying drawing explanation
Below in conjunction with accompanying drawing, the present invention will be further described in detail.
Fig. 1 is thermal treatment process schematic diagram of the present invention.
The microstructure picture of the ultra-high strength and toughness Multiphase Steel that Fig. 2 obtains for the embodiment of the present invention 1.
Embodiment
A kind of high-strong toughness Multiphase Steel of the present invention, the component comprised and weight percent content are: C:0.10%-0.25%, Si:0.5%-1.0%, Mn:1.2%-1.8%, Ti:0.01%-0.05%, B:0.001%-0.003%, S :≤0.01%, P :≤0.01%, all the other are Fe.
Wherein lower C content can ensure that steel alloy has good plasticity, reduce its carbon equivalent as far as possible again simultaneously, make it have certain weldability, Si is mainly used for suppressing the precipitation of cementite, Mn is used for increasing austenitic area and reduces austenitizing temperature, Ti is mainly used for fining austenite grains, and a small amount of B ensures enough good hardening capacity.
A heat treating method for high-strong toughness Multiphase Steel, mainly comprises the following steps:
The first step, is heated to austenitizing temperature 860-1000 DEG C, and is incubated 3-30min by steel;
Second step, the steel the first step obtained is cooled fast to critical temperature 700-850 DEG C with the speed of 50-100 DEG C/s, and carries out deformation induced trans-formation in this temperature range, and strain rate is 0.6-5s
-1, reduction in pass is 51-80%, makes grain refining and generates deformation induced ferrite;
3rd step, the steel obtained by second step is quenched in the liquid quenching medium of 50-370 DEG C, to obtain martensite and residual austenite body tissue, and realize carbon distribution at this temperature range inside holding 5-600s, carbon atom is fully spread from supersaturation martensite to not changing austenite, with stable austenite, concurrent deformation ferrite due to carbon concentration higher, can increase austenitic stability, high density dislocation provides favourable diffusion admittance for carbon atom;
4th step, quenches in room temperature water by the steel that the 3rd step obtains, and obtains the heterogeneous structure of thin lath dislocation type martensite+thin thin residual austenite+deformation induced ferrite.
The present invention is to pricking the not requirement of how many passages in second step during deformation induced trans-formation, and general bundle 1 passage, also can prick repeatedly, when pricking repeatedly, passage is greater than 5s interval time.
Below in conjunction with specific embodiment, the present invention will be further described.
Embodiment 1
The component of high-strong toughness Multiphase Steel and weight percent content are: C:0.21%, Si:0.81%, Mn:1.58%, Ti:0.022%, B:0.0024%, S:0.0014%, P:0.0064%, and all the other are Fe.Steel is incubated 5min with the heating rate of 10 DEG C/s to austenitizing temperature 900 DEG C, and be then cooled fast to 800 DEG C with the speed of 50 DEG C/s, strain rate is 1s
-1, reduction in pass is 65%, is then quenched into 310 DEG C of isothermal 20s, is finally quenched into room temperature.After tested, the tensile strength Rm of steel is 1523MPa, yield strength Rp0.2 is 850MPa, and breaking elongation is 12.6%, and ferrite content is 48%, and average grain size is 1.1 μm.
Embodiment 2
The component of high-strong toughness Multiphase Steel and weight percent content are: C:0.21%, Si:0.81%, Mn:1.58%, Ti:0.022%, B:0.0024%, S:0.0014%, P:0.0064%, and all the other are Fe.Steel is incubated 10min with the heating rate of 10 DEG C/s to austenitizing temperature 950 DEG C, and be then cooled fast to 750 DEG C with the speed of 70 DEG C/s, strain rate is 1s
-1, reduction in pass is 60%, is then quenched into 300 DEG C of isothermal 30s, is finally quenched into room temperature.After tested, the tensile strength Rm of steel is 1688MPa, yield strength Rp0.2 is 922MPa, and breaking elongation is 15.6%.Ferrite content is 45%, and average grain size is 1.2 μm.
Embodiment 3
The component of high-strong toughness Multiphase Steel and weight percent content are: C:0.21%, Si:0.81%, Mn:1.58%, Ti:0.022%, B:0.0024%, S:0.0014%, P:0.0064%, and all the other are Fe.Steel is incubated 3min with the heating rate of 10 DEG C/s to austenitizing temperature 900 DEG C, and be then cooled fast to 700 DEG C with the speed of 60 DEG C/s, strain rate is 1s
-1, reduction in pass is 60%, is then quenched into 290 DEG C of isothermal 60s, is finally quenched into room temperature.After tested, the tensile strength Rm of steel is 1702MPa, yield strength Rp0.2 is 885MPa, and breaking elongation is 16.5%.Ferrite content is 50%, and average grain size is 1.0 μm.
Embodiment 4
The component of high-strong toughness Multiphase Steel and weight percent content are: C:0.21%, Si:0.81%, Mn:1.58%, Ti:0.022%, B:0.0024%, S:0.0014%, P:0.0064%, and all the other are Fe.Steel is incubated 20min with the heating rate of 10 DEG C/s to austenitizing temperature 900 DEG C, and be then cooled fast to 750 DEG C with the speed of 50 DEG C/s, strain rate is 1s
-1, reduction in pass is 60%, is then quenched into 300 DEG C of isothermal 120s, is finally quenched into room temperature.After tested, the tensile strength Rm of steel is 1413MPa, yield strength Rp0.2 is 819MPa, and breaking elongation is 17.2%.Ferrite content is 52%, and average grain size is 0.9 μm.
Embodiment 5
The component of high-strong toughness Multiphase Steel and weight percent content are: C:0.15%, Si:0.6%, Mn:1.4%, Ti:0.035%, B:0.0016%, S:0.0065%, P:0.0028%, and all the other are Fe.Steel is incubated 30min with the heating rate of 20 DEG C/s to austenitizing temperature 1000 DEG C, and be then cooled fast to 850 DEG C with the speed of 100 DEG C/s, strain rate is 0.6s
-1, reduction in pass is 51%, is then quenched into 100 DEG C of isothermal 400s, is finally quenched into room temperature.After tested, the tensile strength Rm of steel is 1524MPa, yield strength Rp0.2 is 802MPa, and breaking elongation is 16.2%.Ferrite content is 49%, and average grain size is 1.1 μm.
Embodiment 6
The component of high-strong toughness Multiphase Steel and weight percent content are: C:0.10%, Si:0.5%, Mn:1.2%, Ti:0.01%, B:0.001%, S:0.01%, P:0.01%, and all the other are Fe.Steel is incubated 15min with the heating rate of 30 DEG C/s to austenitizing temperature 950 DEG C, and be then cooled fast to 700 DEG C with the speed of 80 DEG C/s, strain rate is 3s
-1, reduction in pass is 70%, is then quenched into 50 DEG C of isothermal 600s, is finally quenched into room temperature.After tested, the tensile strength Rm of steel is 1483MPa, yield strength Rp0.2 is 809MPa, and breaking elongation is 15.4%.Ferrite content is 46%, and average grain size is 1.05 μm.
Embodiment 7
The component of high-strong toughness Multiphase Steel and weight percent content are: C:0.25%, Si:1.0%, Mn:1.8%, Ti:0.05%, B:0.003%, S:0.01%, P:0.01%, and all the other are Fe.Steel is incubated 25min with the heating rate of 25 DEG C/s to austenitizing temperature 860 DEG C, and be then cooled fast to 750 DEG C with the speed of 50 DEG C/s, strain rate is 5s
-1, reduction in pass is 80%, is then quenched into 370 DEG C of isothermal 5s, is finally quenched into room temperature.After tested, the tensile strength Rm of steel is 1725MPa, yield strength Rp0.2 is 903MPa, and breaking elongation is 15.1%.Ferrite content is 47%, and average grain size is 1.2 μm.
Claims (4)
1. the heat treating method of a high-strong toughness Multiphase Steel, the component that described high-strong toughness Multiphase Steel comprises and weight percent content are: C:0.10%-0.25%, Si:0.5%-1.0%, Mn:1.2%-1.8%, Ti:0.01%-0.05%, B:0.001%-0.003%, S :≤0.01%, P :≤0.01%, all the other are Fe, it is characterized in that, mainly comprise the following steps:
The first step, by steel with the heating rate of 30 DEG C/s to austenitizing temperature 860-1000 DEG C, and be incubated 3-30min;
Second step, the steel the first step obtained is cooled fast to critical temperature 700-800 DEG C with the speed of 80 DEG C/s, and carries out deformation induced trans-formation in this temperature range, and strain rate is 0.6-5s
-1, reduction in pass is 51-80%, makes grain refining and generates deformation induced ferrite;
3rd step, the steel obtained by second step is quenched in the liquid quenching medium of 50-370 DEG C, to obtain martensite and residual austenite body tissue, and realizes carbon distribution at this temperature range inside holding 5-600s, carbon atom is fully spread, with stable austenite from supersaturation martensite to not changing austenite;
4th step, quenches in room temperature water by the steel that the 3rd step obtains, and obtains the heterogeneous structure of thin lath dislocation type martensite+thin thin residual austenite+deformation induced ferrite.
2. the heat treating method of a kind of high-strong toughness Multiphase Steel according to claim 1, it is characterized in that: the temperature in the described the first step is 900 DEG C, soaking time is 5min.
3. the heat treating method of a kind of high-strong toughness Multiphase Steel according to claim 1, is characterized in that: in described second step, and strain rate is 1s
-1, reduction in pass is 60%.
4. the heat treating method of a kind of high-strong toughness Multiphase Steel according to claim 1, is characterized in that: in described 3rd step, quenching temperature is 300 DEG C, and soaking time is 60s.
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| 刘和平.高强塑积热变形淬火碳分配钢的研究.《上海交通大学博士学位论文》.2011,第34,82-100页. * |
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