CN103882320A - High-strength cold-rolled steel sheet having excellent stretch flangeability and spot welding property and manufacturing method of the steel sheet - Google Patents
High-strength cold-rolled steel sheet having excellent stretch flangeability and spot welding property and manufacturing method of the steel sheet Download PDFInfo
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Abstract
The invention provides a high-strength cold-rolled steel sheet having excellent stretch flangeability and spot welding property and a manufacturing method of the steel sheet. The steel sheet comprises 0.03-0.15% of C, 0.30-0.10% of Si, 1.20-2.20% of Mn, not more than 0.015% of P, not more than 0.010% of S, 0.02-0.15% of Al, not more than 0.005% of N, 0.20-0.60% of Cr, 0.010-0.060% of Nb, 0.030-0.100% of V and 0.0007-0.0050% of Ca, with the balance being Fe and unavoidable impurities, and with the (Mn+2Nb+V) being not more than 2.3% and not less than 1.6%. In the manufacturing method, the start rolling temperature of hot continuous rolling precision rolling is 1000-1100 DEG C, the finish rolling temperature is 890-950 DEG C, the acid-washing cold rolling rate is 60-80%, and two-stage cooling, namely slow cooling firstly and rapid cooling secondly, are adopted after annealing and temperature maintaining steps. The tensile strength of the finally obtained steel sheet is higher than 800 MPa. The obtained steel sheet is good in strength ductility matching, and excellent in stretch flangeability and spot welding property.
Description
Technical field
The invention belongs to automobile cold-rolled high strength thin slab technique field, relate in particular to the good high strength cold rolled steel plate of a kind of stretch flangeability and spot weldability and manufacture method thereof.
Background technology
In recent years, along with the fast development of automotive industry, automobile brings easily simultaneously to people as the daily vehicles, also becomes and produces CO
2, NOx and noise primary pollution source, its consequent environment and energy problem are also subject to people's great attention day by day.In order to reduce oil consumption, save energy, realizes Sustainable development, impels automobile to environment-friendly type, lightweight future development.Developed at present two-phase (DP) steel, phase change induction plasticity (DP) steel, complex phase (CP) steel and twin crystal inducing plasticity (TWIP) steel, for frame member, stiffener and the anti-collision energy absorption member of automobile.High Strength Steel Plate needs spot welding to assemble after machine-shaping, but because the raising of armor plate strength must cause the reduction of Extending flange Perfor (reaming performance) and spot welding characteristics, has limited the widespread use of these high tensile steel plates.Therefore, expect that these high tensile steel plates have the high-intensity while, have good higher ream forming and spot welding characteristics concurrently.
A kind of high-elongation that patent " twin crystal induction plastic steel of a kind of high-elongation and high hole expansibility and manufacture method thereof " (publication number CN102400036A) is announced and the twin crystal inducing plasticity steel of high hole expansibility, in steel, Mn content is 10% ~ 20%, carbon content is 0.3% ~ 0.7%, steel thermal conductivity and the magnetic difference of this composition, continuous casting and subsequent production difficulty are large, production cost is high, after cold rolling by hot-rolled sheet in patent in static furnace after 600 ~ 1000 ℃ of insulations to be greater than the cooling rate solution treatment of 20 ℃/s, unit elongation and the hole expansibility of the steel plate obtaining are high, but can not get good spot welding characteristics.
Korean Patent " have high strength cold rolled steel plate and the steel plate galvanized of superior workability and manufacture its method " (PCT/KR2008/004642), in steel except basal component and Sb element, also need to add in all multielements of Co, Mo, Ti, Nb, V and Ca one or both and more than, in addition, the N that also contains 70 ~ 300PPm in steel, this alloy system has increased smelting difficulty and product cost undoubtedly.This steel obtains the complex tissue of ferrite, bainite and residual austenite by annealing or hot dip galvanizing annealing process, the excellent processability of steel but not necessarily have good spot welding characteristics.
Patent " high strength cold rolled steel plate of excellent in bending workability " (publication number CN102260821A) has announced that a kind of steel plate is organized as full martensite or martensite adds minute quantity ferrite, tensile strength is greater than the cold-rolled steel sheet of the excellent in bending workability of 880MPa, but does not do to consider for hole expandability and the spot weldability of steel plate.
Patent " high strength cold rolled steel plate of excellent in workability and manufacture method thereof " (publication number CN102140608A) has proposed a kind of high strength cold rolled steel plate of excellent in workability, and the microstructure of its steel plate is bainite, residual austenite and tempered martensite.For obtaining this complex tissue, patent has adopted 930 ~ 960 ℃ of soaking, two-stage cooling adds the operational path of tempering, this technique needs the multiple spot plate temperature control of 4 temperature spots, actual operation complexity, in addition, high temperature soaking has also approached the limit of existing cold rolled continuous annealing stove, realizes industrial quantity-produced possibility very little and the spot welding characteristics of steel plate is not done to consider.
Japanese Patent " high-strength hot-dip zinc-coated steel sheet of excellent processability and manufacture method thereof " (PCT/JP2008/069699) provides a kind of processibility and good high-strength hot-dip zinc-coated steel sheet and manufacture method thereof of shock resistance that is organized as ferrite, martensite and residual austenite and tempered martensite, does not relate to the spot welding characteristics that finished product is cold rolled annealed plate and steel plate.
In view of the requirement to High Strength Steel Plate Extending flange Perfor (reaming performance) and spot welding characteristics, should be by effectively controlling in the smelting composition of steel and production technique, realizing ferrite and tempered martensite and a small amount of bainite structure in steel plate coexists, and coordinate the difference of hardness of soft phase and hard phase in steel plate tissue, to obtain High Strength Steel Plate good high ream forming performance and spot welding characteristics.
Summary of the invention
The object of the invention is to overcome the problems referred to above and deficiency and provide one can on industrial continuous annealing production line, easily manufacture tensile strength more than 800Mpa, the high strength cold rolled steel plate that stretch flangeability and spot weldability are good and manufacture method thereof.
The present invention to achieve these goals, control and smelt composition, hot rolling, cold rolling and continuous annealing process parameter, the high strength that guarantees steel plate, microstructure is the heterogeneous structure that ferrite, tempered martensite add a small amount of bainite, and good stretch flangeability and spot weldability.
The present invention is achieved in that
The good high strength cold rolled steel plate composition of stretch flangeability and spot weldability is as follows by weight percentage: C:0.03% ~ 0.15%, Si:0.30% ~ 0.10%, Mn:1.20% ~ 2.20%, P :≤0.015%, S :≤0.010%, Al:0.02% ~ 0.15%, N :≤0.005%, Cr:0.20% ~ 0.60%, Nb:0.010% ~ 0.060%, V:0.030% ~ 0.100%, Ca:0.0007% ~ 0.0050%, and meet 1.6%≤Mn+2Nb+V≤2.3%, surplus is Fe and some other inevitable impurity.
As to further improvement of the present invention, its moiety is preferably as follows by weight percentage: C:0.06% ~ 0.11%, Si:0.50 ~ 0.70%, Mn:1.60% ~ 2.00%, P :≤0.010%, S :≤0.008%, Al:0.050% ~ 0.100%, N :≤0.0035%, Cr:0.30% ~ 0.50%, Nb:0.020% ~ 0.050%, V:0.050% ~ 0.080%, Ca:0.0010% ~ 0.0030%, and meet 1.8%≤Mn+2Nb+V≤2.1%, surplus is Fe and some other inevitable impurity.
Steel grades control principle of the present invention is as follows:
C: being austenite generting element, is to organize Composite, improves intensity and ductility balanced effective element.For guaranteeing have a certain amount of austenitic transformation to become bainite and martensite after low-temperature transformation in steel plate, and do not reduce spot welding characteristics, in the present invention carbon content control 0.03% ~ 0.15%, more preferably 0.06% ~ 0.11%.
Si: the element that is reinforced ferrite, impel carbon to austenite segregation, solid solution carbon in ferrite is had and removed and cleaning action, to avoid gap solution strengthening and the generation of thick carbide when cooling, contribute to improve the ductility of steel, but for avoiding Si too high levels to cause that surface of steel plate produces red rust, Si of the present invention is controlled at 0.30% ~ 0.10%, more preferably 0.50% ~ 0.70%.
Mn: belong to and expand austenite phase region, the element of stable austenite, can effectively improve the hardening capacity on austenite island, thereby after can reducing steel plate middle temperature transformation, remaining austenitic transformation becomes the necessary rate of cooling of martensite, and play the effect of solution strengthening and refinement ferrite crystal grain.High Mn content easily causes that cementite, perlite and bainite are main banded structure, and affects the spot welding characteristics of steel plate.Mn content of the present invention is controlled at 1.20% ~ 2.20%, and more preferably 1.60% ~ 2.00%.
Al:Al is main reductor, and while Al can also form AlN and separate out, and plays certain Grain refinement.When in steel, Al is added for deoxidation, unsuitable too low, otherwise the oxide compound that Mn, Si etc. are thick disperses in a large number in steel, deteriorated steel, but inclusion increases in too much bunch of shape aluminum oxide, makes ductility and the weldability variation of steel, can affect again steelmaking and continuous casting and produce, in the present invention, Al content is controlled at 0.02% ~ 0.15%, and more preferably 0.050% ~ 0.100%.
Cr: middle carbide, significantly improve the hardening capacity of steel, can strongly postpone perlitic transformation and bainite transformation, increase and austeniticly cross cold energy power, thereby thinning microstructure plays strengthening effect.In addition, the solution strengthening ability of Cr element in steel is little, too much adds and can reduce spot welding characteristics.The content of Cr of the present invention is controlled at 0.20% ~ 0.60%, and more preferably 0.30% ~ 0.50%.
Nb, V: for improving the element of intensity crystal grain thinning.In steel, add Nb and V element, N can form precipitated phase prior to C in steel, makes the effect that has refining grain size and keep carbon.Ferrite matrix has been strengthened in the compound interpolation of Nb and V, reduces and the difference of hardness of bainite and martensite phase, can effectively improve the stretch flangeability of steel plate.For avoiding excessive precipitated phase to reduce ferritic ductility, Nb of the present invention, the content of V is controlled at 0.010% ~ 0.060% and 0.030% ~ 0.100%, and more preferably 0.020% ~ 0.050% and 0.050% ~ 0.080%.
Ca: there is the effect of improving ductility and hole expandability by oxide morphology control and raising grain-boundary strength, suitably add as required.But, in too much interpolation steel, be mingled with and can increase, reduce on the contrary the processing characteristics of steel.The content of Ca of the present invention is controlled at 0.0007% ~ 0.0050%, and more preferably 0.0010% ~ 0.0030%.
N: make nitride separate out in steel plate, contribute to strengthen steel plate, but superfluous, nitride is separated out in a large number, causes that unit elongation, stretch flangeability and spot weldability are deteriorated, and in the present invention, N content is controlled at below 0.005%, more preferably below 0.0035%.
P, S: be the harmful element in steel.P easily on crystal boundary segregation cause embrittlement, make deterioration of impact resistance, and unfavorable to spot welding.S easily forms the inclusiones such as MnS in steel, and it is hot-short that heat causes, and S is larger on spot weldability impact.P in the present invention, S content is controlled at respectively below 0.015% and 0.010%, more preferably below 0.010% and 0.008%.
The high strength cold rolled steel plate manufacture method that stretch flangeability and spot weldability are good, comprises smelting, refining, hot continuous rolling, pickling and cold-rolling, continuous annealing, smooth curling;
Undertaken, after converter smelting, external refining, being cast into the slab that 170 ~ 230mm is thick by said ratio;
In hot continuous rolling production process, be save energy, reduce costs, slab can hot delivery and hot charging after continuous casting, carries out hot continuous rolling after heating and thermal insulation.When hot continuous rolling, by heating of plate blank to 1200 ~ 1300 ℃, insulation 120-180min, prevents that excess Temperature from causing the burning of slab and overheated, and makes the microstructure and composition homogenizing of slab; Finish rolling start rolling temperature is 1000 ~ 1100 ℃, and before object makes finish rolling, several frames realize recrystallization zone rolling, the rolling load before reducing under several frame heavy reductions; Finishing temperature is 890 ~ 950 ℃, and object, for alloying element solid solution, is separated out with crystal grain thinning in annealing, and, at the above high-temperature final rolling of Ar3, be conducive to homogeneity of structure, prevent the generation of deformation texture, anisotropy and banded structure, improve the stretch flangeability of steel plate; Finishing temperature should not exceed 950 ℃, otherwise recrystallize has excessive abnormal growth tendency, simultaneously, too high finishing temperature causes the growing amount of oxide compound sharply to increase, plate surface quality variation after pickling (oxide skin that pickling does not eliminate is owed in existence) is cold rolling, has reduced stretch flangeability and the spot weldability of steel plate; Coiling temperature is 650 ~ 700 ℃, high temperature coiling under this temperature range, in eutectoid transformation subsequently, easily generate compared with carbide thick and that disperse distributes, and the element such as C, Mn is obviously enrichment in perlite, the critical cooling rate of austenite in the time of middle low temperature phase change can reduce annealing time, simultaneously, high temperature coiling can make precipitate separate out and grow up, recrystallization temperature is reduced, while being conducive to alleviate steel plate annealing, soaking temperature, the cooling harsh requirement to continuous annealing furnace fast.After hot continuous rolling, obtain the hot-rolled coil that microstructure is ferrite and pearlite, hot-rolled coil thickness is 2.0 ~ 6.5mm;
In pickling and cold-rolling production process, hot-rolled coil is cold rolling one-tenth cold rolled sheet after pickling, cold rolling draft is 60 ~ 80%, cold rolling coil plate thickness is 0.5 ~ 2.5mm, and cold rolling draft is lower than 60%, and cold rolling efficiency is low, cold rolling draft is higher than 80%, work hardening is strengthened, and cold roller and deformed drag increases, and easily causes cold rolling unit load to transfinite.In addition, the pearlite colony spacing under this draft in structure of steel reduces to be broken more fully with perlite, for the grain refining in annealing process provides condition;
In continuous annealing operation, steel band is 790 ~ 850 ℃ in the holding-zone temperature of annealing furnace, soaking time is 90 ~ 260s, makes perlite in steel all change the alloying element such as austenitizing and C, Mn into and in austenite, spreads from ferrite, improves austenitic stability.Soaking temperature is lower than 790 ℃, steel organize austenitizing degree inadequate, when cooling, can not obtain suitable bainite and martensite content.Soaking temperature is higher than 850 ℃, and the Ovshinsky scale of construction is many but the alloy amount wherein of dissolving in is relatively less, and the lower transformation Critical cooling speed of the Critical cooling speed of martensitic transformation and bainite transformation improves, and is difficult for obtaining bainite and martensite connecting moving back under the limited rate of cooling of stove.After steel band insulation, adopt quick cooling two-stage cooling after first Slow cooling, slow cooling section is cooled to 670-700 ℃ by steel band from holding temperature, and rate of cooling is 1 ~ 10 ℃/s, for regulating austenitic quantity and distribution in steel, improving the distributional pattern of alloying element in austenite and ferrite; Rapid cooling section is cooled to 280 ~ 330 ℃ with the rate of cooling of 25 ~ 50 ℃/s by steel band, is for avoiding perlitic transformation, and in assurance, the bainite and martensite of low temperature changes; Cooling rear steel band carries out overaging processing at 280 ~ 330 ℃, and overaging time 350 ~ 950s is air-cooled after timeliness, makes martensite self-tempering, coordinates and ferritic difference of hardness, improves the stretch flangeability of steel plate.
Beneficial effect of the present invention: when smelting, by controlling the content of C element, add a certain amount of Cr, Ca element, and compound interpolation Nb, V element, the controlled rolling and controlled cooling during by hot rolling obtains rational hot rolling microstructure and surface and the good hot-rolled substrate of plate shape; In the time of continuous annealing, adopt slow cooling and twice type of cooling of rapid cooling section after soaking, finally obtain tensile strength more than 800MPa, strength and ductility coupling is good, and stretch flangeability and spot weldability are good, thickness, between 0.5 ~ 2.5mm, can be used as the cold-rolled steel sheet of automobile stiffener and structural part etc.
Accompanying drawing explanation
Fig. 1 is the hot-rolled sheet microstructure of embodiment 1.
Fig. 2 is the cold rolled annealed plate microstructure of embodiment 1.
Fig. 3 is the transmission electron microscope photo of embodiment 1 cold rolled annealed plate.
Fig. 4 is the transmission electron microscope photo of embodiment 1 cold rolled annealed plate.
The tensile stress-strain curve of the cold rolled annealed plate of Fig. 5.
Embodiment
By embodiment, the present invention is further described.
The composition of embodiment steel is in table 1, and hot-rolled process parameter is in table 2, and continuous annealing process parameter is in table 3, and the mechanical property of continuous annealing steel plate and characteristic are in table 4.
Chemical composition (mass percent) % of table 1 embodiment steel
The rolling technological parameter of table 2 embodiment steel
The continuous annealing process parameter of table 3 embodiment steel
Mechanical property and the characteristic of table 4 embodiment steel annealed sheet
By the chemical composition of the present invention's design, the steel of embodiment is through smelting continuous casting, and according to the hot rolling technology controlled rolling and controlled cooling of setting, obtaining thickness is 2.0 ~ 6.5mm, the hot-rolled sheet that plate shape and surface quality are good, and hot-rolled sheet tissue is made up of ferrite and pearlite, as Fig. 1.Hot-rolled sheet becomes the substrate of 0.5 ~ 2.5mm through pickling and cold-rolling, then in continuous annealing, anneal, the steel plate finally obtaining is made up of ferrite and tempered martensite and a small amount of bainite, and after annealing, tissue is shown in Fig. 2,3,4, more than its tensile strength is reached for 800MPa, R
m× λ>=4500MPa%, strength and ductility coupling is good, and stretch flangeability and spot weldability are good.
Claims (3)
1. a stretch flangeability and the good high strength cold rolled steel plate of spot weldability, it is characterized in that its chemical component weight per-cent is: C:0.03% ~ 0.15%, Si:0.30 ~ 0.10%, Mn:1.20% ~ 2.20%, P :≤0.015%, S :≤0.010%, Al:0.02% ~ 0.15%, N :≤0.005%, Cr:0.20% ~ 0.60%, Nb:0.010% ~ 0.060%, V:0.030% ~ 0.100%, Ca:0.0007% ~ 0.0050%, and meet 1.6%≤Mn+2Nb+V≤2.3%, surplus is Fe and some other inevitable impurity.
2. stretch flangeability and the good high strength cold rolled steel plate of spot weldability described in a claim 1, it is characterized in that its chemical component weight per-cent is: C:0.06% ~ 0.11%, Si:0.50 ~ 0.70%, Mn:1.60% ~ 2.00%, P :≤0.010%, S :≤0.008%, Al:0.050% ~ 0.100%, N :≤0.0035%, Cr:0.30 ~ 0.50%, Nb:0.020 ~ 0.050%, V:0.050 ~ 0.080%, Ca:0.0010 ~ 0.0030%, and meet 1.8%≤Mn+2Nb+V≤2.1%, surplus is Fe and some other inevitable impurity.
3. stretch flangeability and the good high strength cold rolled steel plate manufacture method of spot weldability described in a claim 1, comprise smelting, refining, hot continuous rolling, pickling and cold-rolling, continuous annealing, smooth curling, it is characterized in that, undertaken, after converter smelting, external refining, being cast into the slab that 170 ~ 230mm is thick by said ratio; Hot continuous rolling: by heating of plate blank to 1200 ~ 1300 ℃, insulation 120-180min, finish rolling start rolling temperature is 1000 ~ 1100 ℃, finishing temperature is 890 ~ 950 ℃, 650 ~ 700 ℃ of coiling temperatures, obtain the hot-rolled coil that microstructure is ferrite and pearlite, and hot-rolled coil thickness is 2.0 ~ 6.5mm; Pickling and cold-rolling: hot-rolled coil is cold rolling one-tenth cold rolled sheet after pickling, cold rolling draft is 60 ~ 80%, cold rolling coil plate thickness is 0.5 ~ 2.5mm; Continuous annealing: steel band is 790 ~ 850 ℃ in the holding-zone temperature of annealing furnace, soaking time is 90 ~ 260s; After steel band insulation, adopt quick cooling two-stage cooling after first Slow cooling, slow cooling section is cooled to 670-700 ℃ by steel band from holding temperature, and rate of cooling is 1 ~ 10 ℃/s; Rapid cooling section is cooled to 280 ~ 330 ℃ with the rate of cooling of 25 ~ 50 ℃/s by steel band; After annealing, steel band carries out overaging processing at 280 ~ 330 ℃, and overaging time 350 ~ 950s is air-cooled after timeliness.
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| CN113403545B (en) * | 2021-05-21 | 2022-07-22 | 鞍钢股份有限公司 | High-hole-expansibility DH1180MPa cold-rolled continuous-annealing steel plate and preparation method thereof |
| CN113528932A (en) * | 2021-05-31 | 2021-10-22 | 唐山钢铁集团高强汽车板有限公司 | Martensite steel plate and preparation method thereof |
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