CN102912219A - TRIP steel plate with high product of strength and elongation and preparation method thereof - Google Patents
TRIP steel plate with high product of strength and elongation and preparation method thereof Download PDFInfo
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- CN102912219A CN102912219A CN2012104113207A CN201210411320A CN102912219A CN 102912219 A CN102912219 A CN 102912219A CN 2012104113207 A CN2012104113207 A CN 2012104113207A CN 201210411320 A CN201210411320 A CN 201210411320A CN 102912219 A CN102912219 A CN 102912219A
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- 229910000794 TRIP steel Inorganic materials 0.000 title claims abstract description 25
- 238000002360 preparation method Methods 0.000 title claims description 9
- 238000001816 cooling Methods 0.000 claims abstract description 26
- 238000000137 annealing Methods 0.000 claims abstract description 17
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 14
- 238000005096 rolling process Methods 0.000 claims abstract description 14
- 238000005098 hot rolling Methods 0.000 claims abstract description 10
- 238000010438 heat treatment Methods 0.000 claims abstract description 9
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 9
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 8
- 229910001567 cementite Inorganic materials 0.000 claims abstract description 4
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 claims abstract description 4
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 3
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 3
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 3
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 3
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 3
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 3
- 238000005097 cold rolling Methods 0.000 claims description 11
- 238000000034 method Methods 0.000 claims description 10
- 238000009749 continuous casting Methods 0.000 claims description 8
- 238000002791 soaking Methods 0.000 claims description 8
- 239000000203 mixture Substances 0.000 claims description 7
- 239000000126 substance Substances 0.000 claims description 5
- 238000003723 Smelting Methods 0.000 claims description 4
- 229910052782 aluminium Inorganic materials 0.000 claims description 3
- 238000009825 accumulation Methods 0.000 claims description 2
- 229910052758 niobium Inorganic materials 0.000 claims description 2
- 238000005554 pickling Methods 0.000 claims description 2
- 238000004321 preservation Methods 0.000 abstract 3
- 229910052742 iron Inorganic materials 0.000 abstract 1
- 229910000831 Steel Inorganic materials 0.000 description 49
- 239000010959 steel Substances 0.000 description 49
- 239000011572 manganese Substances 0.000 description 10
- 230000000694 effects Effects 0.000 description 9
- 238000004519 manufacturing process Methods 0.000 description 6
- 238000003466 welding Methods 0.000 description 5
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 4
- 238000012545 processing Methods 0.000 description 4
- 229910000937 TWIP steel Inorganic materials 0.000 description 3
- 229910052799 carbon Inorganic materials 0.000 description 3
- 239000000470 constituent Substances 0.000 description 3
- 239000013078 crystal Substances 0.000 description 3
- 230000002349 favourable effect Effects 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 230000005540 biological transmission Effects 0.000 description 2
- 238000004134 energy conservation Methods 0.000 description 2
- 230000007613 environmental effect Effects 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 241001417490 Sillaginidae Species 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 239000004411 aluminium Substances 0.000 description 1
- 229910001563 bainite Inorganic materials 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 239000010960 cold rolled steel Substances 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 208000020442 loss of weight Diseases 0.000 description 1
- 238000012423 maintenance Methods 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 description 1
- 238000004080 punching Methods 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 238000011105 stabilization Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 238000010301 surface-oxidation reaction Methods 0.000 description 1
- 150000003568 thioethers Chemical class 0.000 description 1
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Abstract
The invention discloses a TRIP steel plate with high product of strength and elongation, C: 0.08-0.5%, Si: 0.4% -2.0%, Mn: 3% -8%, P: less than or equal to 0.10 percent, S: less than or equal to 0.02 percent, Al: 0.02% -4%, N: less than or equal to 0.01 percent, Nb: 0-0.5%, V: 0-0.5%, Ti: 0-0.5%, Cr: 0-2%, Mo: 0-1%, and the remainder consisting of Fe and unavoidable impurities; in the microstructure, the area ratio of martensite is 30-90%, the volume ratio of austenite is 5-30%, and the balance is a small amount of ferrite and cementite. Hot rolling heating temperature: 1100-1250 ℃, the heat preservation time is more than or equal to 2h, the initial rolling temperature is more than or equal to 1100 ℃, the final rolling temperature is 850-950 ℃, and the coiling temperature is less than 720 ℃; the thickness of the hot rolled plate is 2-4 mm; the bell-type furnace annealing is furnace heating, the heat preservation temperature is 550-750 ℃, the heat preservation time is 1-20 hours, and furnace cooling is carried out.
Description
Technical field
The invention belongs to automobile steel and make the field, relate to high strength and ductility TRIP steel plate of a kind of strength and ductility product 〉=30GPa% and preparation method thereof.
Background technology
Along with people's improving constantly automobile environment-protection, safety, energy-conservation requirement, automobile industry is had higher requirement to automobile steel, not only require automobile steel that high strength is arranged, require simultaneously automobile steel to have good unit elongation to satisfy the stamping requirement of auto parts.In order to satisfy the requirement of automobile industry fast development, each big steel company of the world successively developed take DP, TRIP steel as the advanced high-strength steel of the first-generation of representative, take the TWIP steel as representative the advanced high-strength steel of the s-generation and take QP steel and high manganese TRIP steel as the advanced high-strength steel of the third generation of representative.
The advanced high-strength steel of the first-generation take DP and TRIP steel as representative is developed successfully and the extensive application on automobile industry, has played great promoter action for the raising of vehicle energy saving, environmental protection, safety performance.Its weak point is, the strength and ductility product of DP steel and TRIP steel is difficult to satisfy that automotive industry improves constantly is energy-conservation, the standard of safety and environmental protection about 20GPa%.
The advanced high-strength steel of the s-generation take the TWIP steel as representative, than the advanced high-strength steel of the first-generation, its strength and ductility product increases substantially, and TWIP steel strength and ductility product reaches 60GPa%, shows extraordinary intensity and plasticity.Weak point is, manganese content is higher, and between 15 ~ 24%, cost is high, and is expensive.Organization of production is difficult simultaneously.
The advanced high-strength steel of the third generation with respect to the advanced high-strength steel of the s-generation, adopts the Composition Design of low-alloy content, has the low characteristics of cost, and its performance index are significantly improved than the advanced high-strength steel of the first-generation simultaneously, and target is that strength and ductility product is greater than 30GPa%.
As one of advanced high-strength steel of the third generation, the QP steel, it has good intensity and plasticity, and weak point is complex process, need special company to move back line and could realize its processing requirement, so cost is high, and stability is poor.
Than other each steel grade, it is simple that high manganese TRIP steel has technique, can produce on traditional production line, do not need the special characteristics such as equipment, and the strength and ductility product of steel plate can reach 30GPa%, can satisfy punching press and the loss of weight needs of most of automobile structures.
Patent CN 102304664A provides a kind of high-strength high-plasticity to contain manganese TRIP cold-rolled steel sheet and preparation method in the aluminium, and its advantage is that the tensile strength of steel plate reaches 900 ~ 1210MPa, and unit elongation reaches 17 ~ 30%, shows good intensity and plasticity.Weak point is that Al content is higher in (1) steel, in 1 ~ 8% scope, and the continuous casting difficulty; (2) annealing time is short between 2 ~ 20 minutes the steel plate annealing time, is difficult to play the purpose that makes the Mn enrichment.
Patent CN 102321854A provides a kind of low-carbon high-manganese TRIP steel and production method thereof, and its advantage is that tensile strength reaches 1000 ~ 1500MPa, and weak point is to have added a large amount of alloys in the steel, causes cost high.Si element and Al constituent content are very low, are difficult to play the effect that carbon is separated out that suppresses.Simultaneously, the curling temperature of hot rolling is 580 degree, and curling temperature is lower, causes cold rolling difficulty.
Summary of the invention
In order to overcome the shortcoming of above-mentioned prior art, purpose of the present invention the object of the present invention is to provide a kind of high strength and ductility TRIP steel plate and manufacture method thereof.
For reaching above purpose, the technical solution used in the present invention is:
(1) a kind of high strength and ductility TRIP steel plate, the chemical composition that it is characterized in that the TRIP steel plate is by percentage to the quality: C:0.08%～0.5%, Si:0.4%～2.0%, Mn:3%～8%, P :≤0.10%, S :≤0.02%, Al:0.02%～4%, N :≤0.01%, Nb:0 ~ 0.5%, V:0 ~ 0.5%, Ti:0 ~ 0.5%, Cr:0 ~ 2%, Mo:0 ~ 1%, and remainder is comprised of Fe and inevitable impurity; Martensite counts 30% ~ 90% with area occupation ratio in the microstructure, and austenite counts 5 ~ 30% with volume fraction, and all the other are a small amount of ferrite and cementite.
(2) a kind of preparation method of high strength and ductility TRIP steel plate, its preparation process comprises the processes such as smelting, continuous casting, hot rolling, pickling, cold rolling, cover annealing, it is characterized in that: (a) rolling: the hot rolling Heating temperature: 1100～1250 ℃, soaking time is 〉=2h, start rolling temperature is 〉=1100 ℃, 850～950 ℃ of finishing temperatures, coiling temperature＜720 ℃; Hot-rolled sheet thickness is 2 ~ 4mm; If the customer requirement steel plate thickness between 2 ~ 4mm, also can not carry out cold rolling; Cold rolling accumulation draught 40%～80%; (b) cover annealing: with the stove heating, holding temperature is: 550～750 ℃, soaking time is: 1 ~ 20h, furnace cooling.Namely obtain high strength and ductility Cold-Rolled TRIP Steel plate.
The below will describe the restriction of chemical composition of the present invention:
C: being used for the reinforcement of steel and the important element that improves stability of retained austenite, is to produce the indispensable element of TRIP steel.In order to obtain strength and ductility product greater than the TRIP steel of 30GPa%, C content is being necessary more than 0.08%.Simultaneously, if C content is too much, easily cause forming property and welding property to descend, therefore 0.5% is its upper limit.
Si: be to improving intensity and the favourable element of unit elongation of TRIP steel.The interpolation of Si element can suppress separating out of cementite, plays simultaneously the effect of solution strengthening.Therefore the lower of Si element is limited to 0.4%.Yet, if the too high decline that will cause surface quality, coating performance and the welding property of TRIP steel of Si constituent content, so the upper limit would be defined as 2.0%.
Mn: be intensity and the favourable element of maintenance stabilization of austenite to improving the TRIP steel.When being lower than 3%, intensity can not meet the demands.When surpassing 8%, will cause continuous casting and rolling difficulty, be limited to 8% on therefore, be limited to 3% down.
P: be to separate out the element that stable austenite is favourable to suppressing C.When P content surpasses 0.10%, will cause the P element on crystal boundary segregation so that worsen its processing characteristics, be limited to 0.10% on therefore.
S: being that the inclusion form is residual with the Mn sulfides, is harmful element.Particularly the intensity of steel plate is higher, affects greatlyr, so its content must be controlled at below 0.02%.
Al: be deoxidant element necessary in the steel and suppress the element that C separates out from austenite, when the Al constituent content is lower than 0.02%, does not have deoxidation effect and suppress the effect that C separates out, when Al content is higher than 3%, to cause the inclusion increases such as aluminum oxide, cause the continuous casting difficulty.
N: when surpassing 0.01%, will cause the ageing and poor processability of steel plate, so be limited to 0.01% on it.
Nb: Main Function is the effect of crystal grain thinning and precipitation strength, improves simultaneously welding property.The Nb too high levels can cause the poor processability of steel plate.Therefore be limited to 0.5% on it.
V: mainly play precipitation strength and improve the effect of welding property.The V too high levels can cause the poor processability of steel plate.Therefore be limited to 0.5% on it.
Ti: Main Function is the effect of crystal grain thinning and precipitation strength, improves simultaneously welding property.The Ti too high levels causes the poor processability of steel plate.Therefore be limited to 0.5% on it.
Cr: mainly play the effect that improves armor plate strength and hardening capacity.The Cr too high levels can cause steel plate plasticity variation, so is limited to 2% on it.
Mo: mainly play the effect that improves armor plate strength and hardening capacity, promote to form bainite structure in the steel plate.The Mo too high levels can cause the steel plate cost to rise and processing characteristics descends.Therefore be limited to 1% on it.
Manufacture method of the present invention comprises that (1) smelts, continuous casting working procedure; (2) rolling process (comprising hot rolling and cold rolling); (3) cover annealing operation.In order to obtain steel plate of the present invention, rolling process and cover annealing operation are even more important.
(1) smelting, continuous casting working procedure
Smelting, continuous casting working procedure are not specially limited, and adopt usual method to produce the molten steel that satisfies the composition requirement, obtain continuously cast bloom through continuous caster.
(2) rolling process
Rolling process is very important for obtaining high strength and ductility TRIP steel plate of the present invention, its processing requirement is: continuous blank heating temperature: 1100～1250 ℃, soaking time is 〉=2h, start rolling temperature is 〉=1100 ℃, 850～950 ℃ of finishing temperatures, coiling temperature＜720 ℃ are when curling temperature is higher than 720 ℃, can cause the coil of strip surface oxidation serious, be difficult to satisfy the user to the specification of quality of surface of steel plate.After obtaining thickness and being 2 ~ 4mm hot-rolled sheet, according to customer need, can carry out draft and be 40%～80% cold rolling, obtain cold-reduced sheet.If hot-rolled sheet thickness has satisfied customer requirement, also can not carry out cold rolling.
(3) cover annealing operation
Annealing temperature is extremely important for obtaining high strength and ductility steel plate of the present invention, when temperature is lower than 550 ℃, can't obtain austenite structure.Temperature is higher than 750 ℃, can cause martensite lath thick, reduces the intensity of steel plate.Therefore annealing temperature is suitable temperature between 550～750 ℃.
Annealing time is also very important for obtaining steel plate of the present invention, if soaking time less than 1 hour, Mn element enrichment degree in austenite is not enough, can't obtain stable austenite structure in room temperature.If soaking time is higher than 20 hours, can cause martensite lath thick, reduce the intensity of steel plate.Therefore suitable time range is 1 ~ 20 hour.
After finishing annealing, with the steel plate furnace cooling, can obtain high strength and ductility TRIP steel plate.
The present invention has good performance, and the steel plate strength and ductility product is greater than 30GPa%.The preparation method is simple, can utilize traditional production line to produce the steel plate of excellent property.Product application is in extensive range, can be used for a plurality of industries such as automobile, machinery.
Description of drawings
The metallographic structure of Fig. 1: embodiment 3 steel plates, martensite and austenite structure;
Fig. 2: embodiment 3 transmission electron microscope film photo, martensite and austenite structures.
Embodiment
The invention will be further described below in conjunction with accompanying drawing:
The embodiment chemical composition is as shown in table 1:
Table 1 chemical composition (wt%)
The embodiment rolling technological parameter is as shown in table 2:
Table 2 rolling technological parameter
| Embodiment | The hot rolling start rolling temperature (℃) | Hot rolling finishing temperature (℃) | Coiling temperature (℃) | Cold rolling draft (%) |
| 1 | 1128 | 923 | 560 | 0 |
| 2 | 1108 | 885 | 642 | 64 |
| 3 | 1086 | 921 | 504 | 58 |
| 4 | 1075 | 897 | 650 | 57 |
| 5 | 1104 | 909 | 569 | 67 |
| 6 | 1121 | 908 | 681 | 68 |
| 7 | 1054 | 917 | 502 | 0 |
| 8 | 1107 | 907 | 687 | 62 |
| 9 | 1092 | 882 | 521 | 60 |
| 10 | 1121 | 878 | 578 | 65 |
| 11 | 1057 | 882 | 612 | 55 |
| 12 | 1064 | 878 | 634 | 58 |
| 13 | 1078 | 868 | 642 | 52 |
| 14 | 1096 | 897 | 538 | 55 |
| 15 | 1109 | 902 | 567 | 58 |
| 16 | 1136 | 913 | 579 | 57 |
| 17 | 1123 | 922 | 582 | 52 |
| 18 | 1142 | 905 | 622 | 55 |
| 19 | 1114 | 909 | 634 | 67 |
| 20 | 1108 | 915 | 642 | 63 |
| 21 | 1104 | 904 | 628 | 61 |
Embodiment batch annealing parameter is as shown in table 3:
Table 3 batch annealing parameter
| Embodiment | Type of heating | Heating temperature (℃) | Soaking time (h) | The type of cooling |
| 1 | Heat with stove | 640 | 8 | Furnace cooling |
| 2 | Heat with stove | 650 | 10 | Furnace cooling |
| 3 | Heat with stove | 660 | 12 | Furnace cooling |
| 4 | Heat with stove | 630 | 14 | Furnace cooling |
| 5 | Heat with stove | 645 | 15 | Furnace cooling |
| 6 | Heat with stove | 625 | 16 | Furnace cooling |
| 7 | Heat with stove | 620 | 17 | Furnace cooling |
| 8 | Heat with stove | 650 | 11 | Furnace cooling |
| 9 | Heat with stove | 647 | 20 | Furnace cooling |
| 10 | Heat with stove | 640 | 18 | Furnace cooling |
| 11 | Heat with stove | 610 | 4 | Furnace cooling |
| 12 | Heat with stove | 630 | 6 | Furnace cooling |
| 13 | Heat with stove | 660 | 8 | Furnace cooling |
| 14 | Heat with stove | 634 | 12 | Furnace cooling |
| 15 | Heat with stove | 624 | 9 | Furnace cooling |
| 16 | Heat with stove | 654 | 10 | Furnace cooling |
| 17 | Heat with stove | 647 | 11 | Furnace cooling |
| 18 | Heat with stove | 623 | 16 | Furnace cooling |
| 19 | Heat with stove | 657 | 14 | Furnace cooling |
| 20 | Heat with stove | 667 | 13 | Furnace cooling |
| 21 | Heat with stove | 647 | 11 | Furnace cooling |
The mechanical property of embodiment steel plate is as shown in table 4:
The mechanical property of table 4 steel plate
| Embodiment | Rp 0.2（MPa） | Rm（MPa） | A（%） |
| 1 | 617 | 1042 | 31 |
| 2 | 647 | 1087 | 33 |
| 3 | 608 | 1079 | 32 |
| 4 | 626 | 1104 | 35 |
| 5 | 634 | 1089 | 32 |
| 6 | 627 | 1048 | 33 |
| 7 | 645 | 1027 | 34 |
| 8 | 638 | 1123 | 30 |
| 9 | 598 | 1088 | 36 |
| 10 | 616 | 1076 | 33 |
| 11 | 587 | 1120 | 32 |
| 12 | 624 | 1108 | 33 |
| 13 | 633 | 1098 | 34 |
| 14 | 621 | 1112 | 31 |
| 15 | 595 | 1087 | 32 |
| 16 | 587 | 1089 | 34 |
| 17 | 588 | 1114 | 33 |
| 18 | 604 | 1109 | 31 |
| 19 | 637 | 1186 | 30 |
| 20 | 657 | 1204 | 31 |
| 21 | 627 | 1198 | 30 |
The metallographic structure of embodiment 3 can find out clearly that steel plate contains martensite, austenite structure as shown in Figure 1.The transmission electron microscope photo of embodiment 3 can be seen clearly martensite lath pattern and austenite structure as shown in Figure 2.
Claims (3)
1. high strength and ductility TRIP steel plate, it is characterized in that its chemical composition is by percentage to the quality: C:0.08%～0.5%, Si:0.4%～2.0%, Mn:3%～8%, P :≤0.10%, S :≤0.02%, Al:0.02%～4%, N :≤0.01%, Nb:0 ~ 0.5%, V:0 ~ 0.5%, Ti:0 ~ 0.5%, Cr:0 ~ 2%, Mo:0 ~ 1%, and remainder is comprised of Fe and inevitable impurity; Martensite counts 30% ~ 90% with area occupation ratio in the microstructure, and austenite counts 5% ~ 30% with volume fraction, and all the other are a small amount of ferrite and cementite.
2. the preparation method of a high strength and ductility TRIP steel plate according to claim 1, comprise smelting, continuous casting, hot rolling, cover annealing process, it is characterized in that: the hot rolling Heating temperature: 1100～1250 ℃, soaking time is 〉=2h, start rolling temperature is 〉=1100 ℃, 850～950 ℃ of finishing temperatures, coiling temperature＜720 ℃; Hot-rolled sheet thickness is 2 ~ 4mm; Cover annealing is that holding temperature is: 550～750 ℃, soaking time is 1 ~ 20h, furnace cooling with the stove heating.
3. the preparation method of high strength and ductility TRIP steel plate according to claim 2 is characterized in that: carry out pickling and cold rolling after the hot rolling, cold rolling accumulation draught 40%～80%, cold rolling rear cover annealing.
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