CN104928456A - Manufacturing method for improving extensibility of commonly-cooled ferrite lightweight steel - Google Patents
Manufacturing method for improving extensibility of commonly-cooled ferrite lightweight steel Download PDFInfo
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Abstract
The invention discloses a manufacturing method for improving extensibility of commonly-cooled ferrite lightweight steel. The manufacturing method includes: performing pretreatment before cold rolling, cold rolling and continuous-annealing thermal treatment on thermally-rolled plates, wherein pretreatment before cold rolling includes cold-rolling pre-deformation and recrystallizing annealing. The thermally-rolled steel plates are pretreated before cold rolling to refine high-temperature delta ferrite and improve tissue uniformity of the steel plates after being annealed. By the manufacturing method, high strength of the steel plates is guaranteed while extensibility and strength and elongation product are improved remarkably.
Description
Technical field
The invention belongs to ferrite lightweight rings territory, be specifically related to a kind of manufacture method improving general chill ferritic lightweight steel ductility.
Background technology
Application high-strength steel and advanced high-strength steel substitute traditional low strength rank steel, can improve the specific tenacity ratio of density (intensity with) of automobile steel and reduce the thickness of structural part, realizing vehicle structure lightweight.The another kind of effective way improving automobile steel specific tenacity is on the basis maintaining the excellent mechanical property of above-mentioned high-strength steel, reduce the density of steel.Therefore, low density, high-strong toughness steel plate is developed just in order to tackle the active demand of further automobile lightweight.
Low density steel generally realizes the reduction of carbon steel density by adding more alloy element Al.At present, researchist is just being devoted to develop based on phase-change induced plastic (Transformation-inducedplasticity is called for short TRIP) strengthening mechanism and is being rich in the ferrite low density steel of Al.The alloy content of this kind of ferritic steel is compared low with the alloy content of other low density steel grade (as ferritic-austenitic duplex steel and austenitic steel), thus it not only has low density, high strength characteristics, and it also has good manufacturability simultaneously.Based on the microstructure of the ferrite low density steel of phase-change induced plastic mechanism primarily of the metastable state residual austenite composition of ferrite (comprising high temperature delta ferrite and the alpha ferrite through being deformed into mutually) and appropriate volume mark.It is martensite that metastable state residual austenite is induced progressive transitions under subsequent external deformation effect, to improve the deformation processing sclerosis of steel plate, and then improves armor plate strength and improves ductility.
In prior art, the main manufacturing processes flow process of low-density and high-strength ferrite steel plate is followed successively by smelting and continuous casting, hot rolling, cold rolling and continuous annealing.High temperature iron ferritic (i.e. delta ferrite) is the main composition phase of ferrite lightweight steel.After molten steel solidification process completes, delta ferrite retains all the time in subsequent thermal processing and heat treatment process, and it has following two characteristics: delta ferrite can not obtain structure refinement by solid-state phase changes; In actual production process, delta ferrite also not easily passs through hot rolling, cold rolling and continuous annealing process abundant dynamic and static state recrystallize occurs and refinement.
In the low density ferrite steel plate of high Mn, high Al content, although hot rolling can make delta ferrite microtexture occur to reply and partial, re-crystallization with connecting to move back, but strip delta ferrite still can exist in a large number in the matrix of steel, and these strip delta ferrites often have lower distortion plasticity.So, although annealed sheet steel matrix is dispersed with abundant metastable state residual austenite, because the distortion plasticity of delta ferrite is poor, the delta ferrite under external force in annealed sheet steel mostly occurs the failure mode of cleavage fracture, correspondingly, the integral extension of annealed sheet steel also can reduce.In addition, the existence of a large amount of ribbon delta ferrite also can reduce the bending property of steel plate.
Therefore, in the urgent need to refinement delta ferrite tissue to improve the distortion plasticity of delta ferrite, the plasticity based on the ferrite low density steel of phase-change induced plastic strengthening mechanism is obtained and significantly improves.
Summary of the invention
The object of the present invention is to provide a kind of manufacture method improving general chill ferritic lightweight steel ductility, on the basis keeping higher-strength, significantly improve ductility and the strength and ductility product (i.e. the product of intensity and ductility) of ferrite lightweight steel.
For achieving the above object, technical scheme of the present invention is:
Improve a manufacture method for general chill ferritic lightweight steel ductility, it comprises the steps:
1) cold rolling predeformation
Carry out cold rolling predeformation to hot-rolled sheet, deflection is 30 ~ 80%; The main chemical compositions weight percent of hot-rolled sheet is: C:0.05 ~ 0.50%, Mn:0.25 ~ 12.0%, Al:3.0 ~ 7.0%, also contain: more than one in Si:0.01 ~ 1.5%, Ti:0.005 ~ 0.6%, Nb:0.005 ~ 0.2%, V:0.005 ~ 0.5%, Cr:0.01 ~ 0.5%, Mo:0.01 ~ 0.5%, Ni:0.05 ~ 2.0%, Cu:0.05 ~ 1.0%, all the other are Fe and inevitable impurity;
2) recrystallization annealing
Adopt cover annealing, soaking temperature is 660 ~ 850 DEG C, and soaking time is 0.5 ~ 48h;
3) cold rolling
Cold rolling deflection is 30 ~ 90%;
4) continuous annealing thermal treatment
Be incubated 30 ~ 600s after cold-reduced sheet being heated to soaking temperature 750 ~ 950 DEG C, be first cooled to medium temperature, then be cooled to partition stabilization temperature 200 ~ 500 DEG C, insulation 0 ~ 600s, wherein, the heating rate of cold-rolled steel sheet is 1 ~ 20 DEG C/s; 650 DEG C≤medium temperature < 950 DEG C; The rate of cooling that steel plate after equal thermal treatment is cooled to medium temperature from soaking temperature is 1 ~ 10 DEG C/s; The rate of cooling that steel plate after equal thermal treatment is cooled to partition stabilization temperature from medium temperature is 1 ~ 150 DEG C/s, and this rate of cooling is not less than steel plate is cooled to medium temperature rate of cooling from soaking temperature.After partition stabilization treatment terminates, by steel plate with the rate of cooling slow cooling of 1 ~ 20 DEG C/s to room temperature.
Further, step 1) in, hot-rolled sheet rolling: Heating temperature 1000 ~ 1250 DEG C, soaking time is 0.5 ~ 3h, finishing temperature >=800 DEG C, gets hot-rolled sheet at 300 ~ 750 DEG C of last volumes; After cooling, pickling.
Preferably, step 3) in, the deflection of cold rolling predeformation is 40 ~ 60%.
Preferably, step 5) in, cold rolling deflection is 50 ~ 70%.
The microstructure of the ferrite lightweight steel prepared by the present invention is mainly made up of the ferrite of abundant recrystallize and metastable state residual austenite.
The reason of design and manufacture technology of the present invention is as follows:
(1) cold rolling front pretreatment technology
Cold rolling front pretreatment technology comprises cold rolling predeformation and recrystallization annealing successively, its objective is high temperature delta ferrite in refinement steel, increases the rear steel plate homogeneity of structure of annealing.
Carry out cold rolling predeformation to the hot-rolled steel sheet after pickling, deflection is 30 ~ 80%, preferably 40 ~ 60%.Cold rolling predeformation stores deformation energy at steel matrix, provides motivating force for high temperature delta ferrite is organized in the recrystallize carried out in follow-up bell furnace recrystallization annealing process.Increase the deflection of cold rolling predeformation, contribute to improving deformation energy storage and recrystallize motivating force, thus increase the degree of refinement of deformation delta ferrite and improve the homogeneity of structure of annealed sheet steel.If but the deflection of cold rolling predeformation is excessive, because work hardening causes the resistance to deformation of material very high.
Recrystallization annealing adopts cover annealing, and cover annealing process is mainly incubated after being heated to soaking temperature through the coil of strip of cold rolling predeformation, and this process is used for the homogeneity of structure of high temperature delta ferrite tissue and raising steel plate in refinement steel.In addition, the delta ferrite of refinement can provide more Recrystallization nucleation point for follow-up through the further refinement of delta ferrite in continuous annealing heat treatment process of cold roller and deformed steel plate.The soaking temperature of cover annealing is 660 ~ 850 DEG C.When soaking temperature is lower than 660 DEG C, it is insufficient that the recrystallize of delta ferrite tissue carries out; When soaking temperature is higher than 850 DEG C, after recrystallize, delta ferrite crystal grain can occur excessive coarsening.Soaking time can be regulated by appropriate change soaking temperature, and long soaking time affects production efficiency, and therefore, the soaking time that the present invention controls cover annealing is no more than 48 hours.
Use neutrality or restitutive protection's atmosphere (as N in recrystallization annealing process
2gas or N
2+ H
2mixed gas), be oxidized and decarburization to prevent surface of steel plate.After recrystallization annealing terminates, steel plate is cooled to room temperature.
(2) cold-rolling process
Carry out cold roller and deformed to specific thickness to the steel plate after recrystallization annealing, cold rolling reduction is 30 ~ 90%, preferably 50 ~ 70%.Increase cold rolling reduction, austenitic formation speed can be improved and promote the further refinement of high temperature delta ferrite in follow-up continuous annealing process.If but cold rolling reduction is excessive, because work hardening causes the resistance to deformation of material very high, the cold-rolled steel sheet preparing specific thickness and good profile becomes abnormal difficult.
(3) continuous annealing process
Adopt continuous annealing process thermal treatment cold-rolled steel sheet, make delta ferrite that further recrystallization softening occur and obtain appropriate metastable state residual austenite.Continuous annealing process of the present invention mainly comprises equal thermal process and partition stabilization procedures, as shown in Figure 1.
See Fig. 1, by cold-rolled steel sheet with heating rate v
0t1 (soaking time) time period is incubated after being heated to soaking temperature T1.Choosing of soaking temperature T1 needs to ensure that the recrystallization softening of deformation delta ferrite and austenite phase transformation occur simultaneously, therefore chooses v
0=1 ~ 20 DEG C/s; T1=750 ~ 950 DEG C; T1=30 ~ 600s.When soaking temperature T1 is less than 30s lower than 750 DEG C and soaking time t1, not yet fully there is austenitizing in cold-rolled steel sheet matrix, comprise carbide in matrix to dissolve generate austenite grains not yet completely, and ribbon deformation delta ferrite fully cannot carry out recrystallize and refinement.
When soaking temperature T1 is longer than 600s higher than 950 DEG C and soaking time t1, after equal thermal treatment, in steel matrix tissue, AUSTENITE GRAIN COARSENING and austenite C content reduce, both all make stabilization of austenite in steel reduce, thus residual austenite content minimizing in steel matrix after causing annealing cooling, and residual austenite mechanical stability also can reduce.Correspondingly, the mechanical property of annealed sheet steel worsens.
See Fig. 1, by the steel plate after equal thermal treatment first with slow cooling speed v
2immediately with rapid cooling speed v after slow cooling to medium temperature T2
3t3 (partition stabilizing take) time period is incubated after being cooled to partition stabilization temperature T3.Slow cooling speed v
2mainly consider with choosing of medium temperature T2: the austenite avoiding equal thermal treatment to be formed decomposes Formed compound in the slow cooling section being cooled to medium temperature by soaking temperature, easy handling controls to make annealing thermal treatment be transitioned into rapid cooling section from soaking zone smoothly and maintain the plate shape of cold-rolled steel sheet.The present invention chooses v
2=1 ~ 10 DEG C/s, 650 DEG C≤T2 < 950 DEG C; In rapid cooling section, v
3=1 ~ 150 DEG C/s, and v
3>=v
2, be that the austenite formed after guaranteeing equal thermal treatment does not decompose when rapid cooling section experience differing temps equally.
Partition stabilization treatment section, partition stabilization temperature T3=200 ~ 500 DEG C; Partition stabilizing take t3=0 ~ 600s.The present invention adopts partition stabilization treatment (i.e. austempering), to improve stabilization of austenite further.In partition stabilization procedures, partial austenitic can be converted into bainite ferrite, and carbide is formed and is suppressed simultaneously, and C atom spreads from bainite ferrite thus improves C content and the stability of residual austenite to remaining austenite.
Partition stabilization temperature T3 can cause austenite decomposition higher than when 500 DEG C, thus consumes C and reduction stability of retained austenite in austenite; And partition stabilization temperature T3 temperature is lower than 200 DEG C, then delay the generation of partition process.For avoiding austenite to decompose in long-time partition stabilization procedures, and considering from effective and economy, choosing partition stabilizing take t3 and being no more than 600s.After partition stabilization treatment terminates, steel plate is cooled to room temperature with rate of cooling v4, v4=1 ~ 20 DEG C/s.
(4) hot-rolled sheet rolling technology
Heating temperature 1000 ~ 1250 DEG C in the hot-rolled sheet operation of rolling of the present invention, can cause strand burning when Heating temperature is more than 1250 DEG C, strand internal grain is organized thick and hot workability is reduced, and ultrahigh-temperature can cause blank surface decarburization serious.When Heating temperature is lower than 1000 DEG C, strand is after high-pressure water descaling and breaking down, and finishing temperature is too low and cause the resistance to deformation of material excessive, thus cannot produce not only free of surface defects but also have the hot-rolled steel sheet of specific thickness.
The present invention needs to control finishing temperature more than 800 DEG C, completes hot rolling to strand.The too low meeting of finishing temperature causes casting blank deformation drag too high, is difficult to produce desired thickness specification and without the cold-rolled steel sheet of edge fault; In addition, for component system of the present invention, finishing temperature, higher than 800 DEG C, contributes to strand internal heat kicker shape high temperature iron ferritic (also claiming delta ferrite) and Recovery and recrystallization occurs.
The present invention gets hot-rolled sheet at 300 ~ 750 DEG C of last volumes, if coiling temperature is higher than 750 DEG C, can cause κ carbide or the excessive nodularization of cementite and alligatoring, obtains the residual austenite of even small stable after being unfavorable for the annealing of follow-up cold-rolled steel sheet.In addition, coiling temperature is too high, easily causes flat volume, and the head of hot rolled coil, middle part and afterbody material microstructure ununiformity increase, so cause annealing coil head, in, afterbody microstructure and performance uneven.In addition, coiling temperature is at least 300 DEG C, to suppress to form too much martensitic stucture in hot-rolled steel sheet, guarantees that hot-rolled steel sheet has good cold roller and deformed ability.
Compared with prior art, by optimizing manufacturing process, the unit elongation of steel plate prepared by the present invention and strength and ductility product all can improve more than 20%.Manufacturing process of the present invention is applicable to and manufactures all and be rich in Al and be the general cold TRIP steel plate mainly forming phase with ferrite, and being applicable to the baseplate material producing band Coated Steel, coating can be selected from the one in Zn, Zn-Fe, Zn-Al, Zn-Mg, Zn-Al-Mg, Al-Si and Al-Mg-Si.
Beneficial effect of the present invention:
1. hot-rolled steel sheet is carried out pre-treatment by the present invention before cold rolling, cold rolling front pre-treatment comprises cold rolling predeformation and recrystallization annealing successively, cold rolling front pretreatment technology obviously makes high temperature delta ferrite generation recrystallize in annealed sheet steel and refinement, streaky structure obviously reduces, and the homogeneity of structure of annealed sheet steel is improved.
2. the present invention is through cold rolling front pretreated annealed sheet steel while maintenance high intensity level, and its ductility and strength and ductility product significantly improve.
3. the present invention can complete on existing advanced high-strength steel production line, and without the need to doing larger adjustment, has good popularizing application prospect.
Accompanying drawing explanation
Fig. 1 is the process curve schematic diagram of the cold rolling rear continuous annealing process of the present invention.
Fig. 2 is the manufacturing process flow diagram of the embodiment of the present invention.
Fig. 3 is the representative microstructure photo of ferrite lightweight steel prepared by existing manufacturing process.
Fig. 4 is the representative microstructure photo of ferrite lightweight steel prepared by the present invention.
Embodiment
Below in conjunction with embodiment and accompanying drawing, the present invention will be further described.
Table 1 is the hot rolling of the embodiment of the present invention, cold rolling front pre-treatment and cold-rolling process parameter, and table 2 is the continuous annealing process parameter of the embodiment of the present invention, and table 3 is the mechanical property of the embodiment of the present invention and comparative example steel.
The manufacturing process of the embodiment of the present invention mainly comprises: smelt and continuous casting, hot rolling, cold rolling front pre-treatment, cold rolling and continuous annealing thermal treatment.Cold rolling front pre-treatment comprises cold rolling predeformation and bell furnace recrystallization annealing successively, technical process as shown in Figure 2:
Comparative example 1: do not carry out cold rolling front pre-treatment (i.e. cold rolling predeformation and the process of bell furnace recrystallization annealing process) before cold rolling, steel grade and other manufacturing process are with embodiment 1.
Comparative example 2: do not carry out cold rolling front pre-treatment (i.e. cold rolling predeformation and the process of bell furnace recrystallization annealing process) before cold rolling, steel grade and other manufacturing process are with embodiment 2.
Comparative example 3: do not carry out cold rolling front pre-treatment (i.e. cold rolling predeformation and the process of bell furnace recrystallization annealing process) before cold rolling, steel grade and other manufacturing process are with embodiment 3.
Comparative example 4: do not carry out cold rolling front pre-treatment (i.e. cold rolling predeformation and the process of bell furnace recrystallization annealing process) before cold rolling, steel grade and other manufacturing process are with embodiment 4.
As shown in Table 4, embodiment 1 is compared with comparative example 1, and the unit elongation of embodiment 1 annealed sheet steel improves 30.2%, and strength and ductility product improves 26.7%.Embodiment 2 is compared with comparative example 2, and the unit elongation of embodiment 2 annealed sheet steel improves 28.9%, and strength and ductility product improves 24.1%.Embodiment 3 is compared with comparative example 3, and the unit elongation of embodiment 3 annealed sheet steel improves 30.3%, and strength and ductility product improves 21.2%.Embodiment 4 is compared with comparative example 4, and the unit elongation of embodiment 4 annealed sheet steel improves 27.5%, and strength and ductility product improves 21%.Therefore, the present invention is by the manufacturing process of hot-rolled steel sheet in the cold rolling predeformation of cold rolling advance and bell furnace recrystallization annealing, and ensure that ferrite lightweight steel is while maintenance high intensity level, its ductility and strength and ductility product significantly improve.
Fig. 3 is the representative microstructure photo of ferrite lightweight steel prepared by existing manufacturing process, Fig. 4 is the representative microstructure photo of ferrite lightweight steel prepared by the present invention, in Fig. 3,4, δ represents high temperature delta ferrite, and α+RA represents the mixture of phase transformation alpha ferrite and residual austenite RA.
See Fig. 3 and Fig. 4, the cold rolling front pretreatment technology of the invention process obviously makes high temperature delta ferrite generation recrystallize in annealed sheet steel and refinement, and streaky structure obviously reduces, and the homogeneity of structure of annealed sheet steel is improved, and then can significantly improve the ductility of steel.
Table 3
| Tensile strength (MPa) | Unit elongation (%) | |
| Embodiment 1 | 817 | 32.8 |
| Embodiment 2 | 872 | 39.2 |
| Embodiment 3 | 854 | 32.7 |
| Embodiment 4 | 898 | 36.2 |
| Comparative example 1 | 839 | 25.2 |
| Comparative example 2 | 906 | 30.4 |
| Comparative example 3 | 918 | 25.1 |
| Comparative example 4 | 946 | 28.4 |
Claims (5)
1. improve a manufacture method for general chill ferritic lightweight steel ductility, it is characterized in that, it comprises the steps:
1) cold rolling predeformation
Carry out cold rolling predeformation to hot-rolled sheet, deflection is 30 ~ 80%; The main chemical compositions weight percent of hot-rolled sheet is: C:0.05 ~ 0.50%, Mn:0.25 ~ 12.0%, Al:3.0 ~ 7.0%, also contain: more than one in Si:0.01 ~ 1.5%, Ti:0.005 ~ 0.6%, Nb:0.005 ~ 0.2%, V:0.005 ~ 0.5%, Cr:0.01 ~ 0.5%, Mo:0.01 ~ 0.5%, Ni:0.05 ~ 2.0%, Cu:0.05 ~ 1.0%, all the other are Fe and inevitable impurity;
2) recrystallization annealing
Adopt cover annealing, soaking temperature is 660 ~ 850 DEG C, and soaking time is 0.5 ~ 48h;
3) cold rolling
Cold rolling deflection is 30 ~ 90%;
4) continuous annealing thermal treatment
Be incubated 30 ~ 600s after cold-reduced sheet being heated to soaking temperature 750 ~ 950 DEG C, be first cooled to medium temperature, then be cooled to partition stabilization temperature 200 ~ 500 DEG C, insulation 0 ~ 600s, wherein, the heating rate of cold-rolled steel sheet is 1 ~ 20 DEG C/s; 650 DEG C≤medium temperature < 950 DEG C; The rate of cooling that steel plate after equal thermal treatment is cooled to medium temperature from soaking temperature is 1 ~ 10 DEG C/s; The rate of cooling that steel plate after equal thermal treatment is cooled to partition stabilization temperature from medium temperature is 1 ~ 150 DEG C/s, and this rate of cooling is not less than steel plate is cooled to medium temperature rate of cooling from soaking temperature; After partition stabilization treatment terminates, by steel plate with the rate of cooling slow cooling of 1 ~ 20 DEG C/s to room temperature.
2. the manufacture method of the general chill ferritic of the raising according to any one of claim 1 lightweight steel ductility, it is characterized in that, step 1) in, hot-rolled sheet rolling: Heating temperature 1000 ~ 1250 DEG C, soaking time is 0.5 ~ 3h, finishing temperature >=800 DEG C, get hot-rolled sheet at 300 ~ 750 DEG C of last volumes; After cooling, pickling.
3. the manufacture method of raising according to claim 1 general chill ferritic lightweight steel ductility, is characterized in that, step 3) in, the deflection of cold rolling predeformation is 40 ~ 60%.
4. the manufacture method of raising according to claim 1 general chill ferritic lightweight steel ductility, is characterized in that, step 5) in, cold rolling deflection is 50 ~ 70%.
5. the manufacture method of the general chill ferritic of the raising according to any one of claim 1-4 lightweight steel ductility, is characterized in that, the microstructure of described ferrite lightweight steel is mainly made up of the ferrite of abundant recrystallize and metastable state residual austenite.
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| CN112226701B (en) * | 2020-09-11 | 2021-12-31 | 北京科技大学 | High-aluminum-content fine-grain low-density full-high-temperature ferrite steel and preparation method thereof |
| WO2022123299A1 (en) * | 2020-12-10 | 2022-06-16 | Arcelormittal | Low density cold rolled and annealed steel sheet, method of production thereof and use of such steel to produce vehicle parts |
| CN114086080A (en) * | 2021-11-15 | 2022-02-25 | 华北理工大学 | Dual-phase-isomerism light high-strength steel and preparation method thereof |
| CN115125442A (en) * | 2022-06-16 | 2022-09-30 | 首钢集团有限公司 | Low-density high-strength steel with low crack rate and preparation method thereof |
| CN115125442B (en) * | 2022-06-16 | 2023-11-10 | 首钢集团有限公司 | Low-density high-strength steel with low crack rate and preparation method thereof |
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