CN102174685A - 800 MPa grade cold-rolling dual-phase steel and manufacturing method thereof - Google Patents
800 MPa grade cold-rolling dual-phase steel and manufacturing method thereof Download PDFInfo
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Abstract
The invention discloses 800 MPa grade cold-rolling dual-phase steel and a manufacturing method thereof. The steel contains the following chemical compositions in percentage by weight: 0.10-0.18% of C, 0.03-0.19% of Si, 2.6-3.0% of Mn, 0.01-0.04% of Als, 0.15-0.9% of Cr, and the balance of Fe and other inevitable impurities. The manufacturing method for the steel comprises the following steps sequentially: heating billet steel to 1150-1250 DEG C along with a furnace and preserving the temperature for 1.5-3 hours under heat insulation condition, then performing hot rolling, wherein the rough rolling start rolling temperature is controlled within the range from 1050 DEG C to 1110 DEG C, the precision rolling finish rolling temperature is controlled within the range from 860 DEG C to 900 DEG C, and the simulation curling temperature is controlled within the range from 560 to 600 DEG C; washing a hot rolled plate with acid and then carrying out cold rolling; wherein the cold rolling pressing rate is controlled to be 45-75%, then performing the annealing treatment, wherein the annealing temperature is controlled within the range from 760 DEG C to 860 DEG C; and slowly cooling the hot rolled plate to 630-680 DEG C after keeping for 1-5 minutes under heat preservation condition and then rapidly cooling to be below 350 DEG C at a speed more than 25 DEG C/s for ageing treatment lasting for 5-10 minutes. The practice proves that the steel has the advantages of low yield strength, low yield ratio, high coefficient of elongation, and excellent forming property, and the manufacturing method has simple process and low cost.
Description
Technical field
The invention belongs to the high-strength steel production technical field, refer to a kind of 800MPa level cold-rolled biphase steel and manufacture method thereof particularly.
Background technology
Along with improving constantly that light-weighted continuous development of body of a motor car and passenger safety require, other ultrahigh-strength steel of 800MPa and higher level more and more is applied in intermediate car structural part and the stiffener, to reach energy-saving and emission-reduction and to improve car load crashworthiness effect.In recent years, international automobile manufacturer is on vehicle newly developed, the ratio of using the super-high strength steel plate has reached about 20%, the vehicle of winning international prize high tensile steel plate usage ratio is generally about 70%, and domestic Europe, the United States, Japanese and independent brand new model high tensile steel plate employing rate also increase year by year.And cold-rolled biphase steel is because of it has that yield strength is low, tensile strength is high, work hardening capacity is strong, breaking elongation and plurality of advantages such as uniform elongation is big, easily drawing, good plasticity and toughness coupling, the extremely favor of automotive industry circle.
The principal feature of 800MPa level cold-rolled biphase steel on chemical ingredients is low-carbon and low-alloy both at home and abroad at present.Main alloy element is based on Si, Mn, in order to obtain duplex structure, according to production technique and service requirements difference, also add elements such as proper C r, Mo, V, Nb, having formed with Si-Mn system, Mn-Mo system, Si-Mn-Cr-V system and Mn-Si-Cr-Mo is main dual phase steel series.But the Mo element costs an arm and a leg, the production cost height, and the adding of microalloy elements such as Nb, V has increased the difficulty of technology controlling and process in the production process, capacity of equipment and controlled levels are had relatively high expectations, and the fluctuation of technology is bigger to final Effect on Performance, the precipitation strength effect of adding Nb, V simultaneously and being produced, when increasing tensile strength, yield strength also significantly increases, and this is disadvantageous to impact briquetting, is unfavorable for suitability for industrialized production.
Summary of the invention
The object of the present invention is to provide a kind of low cost, low yield strength, low yield strength ratio, high-elongation and forming property good 800MPa level cold-rolled biphase steel and manufacture method thereof.
For achieving the above object, the 800MPa level cold-rolled biphase steel that the present invention is designed, its chemical ingredients percentage ratio is by weight counted:
C:0.10～0.18%, Si:0.03～0.19%, Mn:2.6～3.0%, Als:0.01～0.04%, Cr:0.15～0.9%, all the other are Fe and other inevitable impurity.
800MPa level cold-rolled biphase steel of the present invention adopts vacuum induction furnace smelting, and its manufacture method may further comprise the steps successively:
Steel billet is heated to 1150～1250 ℃ with stove, insulation 1.5～3h, rolling on hot rolls subsequently, the roughing start rolling temperature is controlled at 1050～1110 ℃, finish rolling finishing temperature and is controlled at 860～900 ℃, the simulation temperature of curling and is controlled at 560～600 ℃;
Hot-rolled sheet carries out cold rolling after pickling, cold rolling draft is controlled at 45～75%, carries out anneal subsequently, 760～860 ℃, and after being incubated 1～5min, slowly be cooled to 630～680 ℃, be quickly cooled to the above speed of 25 ℃/s again and carry out overaging processing 5～10min below 350 ℃.
Further, described annealing temperature is controlled to be 780～830 ℃.
Further, described quick refrigerative speed control is 25～50 ℃/s.
Chemical ingredients and manufacture method to 800MPa level cold-rolled biphase steel of the present invention describes below.
(1) chemical ingredients
C is a kind of effective and cheap strengthening element, directly influence the critical zone and handle fraction of martensite volume and martensite carbon content in the dual phase steel of back, if carbon content is too low, though can obtain duplex structure, but strengthening effect is not obvious, need to increase Mn, the content of alloying elements such as Cr comes proof strength, thereby cause cost to increase, carbon content too Gao Ze under same critical Heating temperature, the austenite that has more volume fractions forms Cr in the austenite island, alloying element contents such as Mn reduce relatively, and hardening capacity reduces, be unfavorable for forming martensitic stucture, so among the present invention the weight percentage of carbon be controlled in 0.10～0.18% scope.
Si is ferritic solution strengthening element, and its acceleration carbon has " removing " and " purification " effect to austenitic poly-partially to the solid solution carbon in the ferrite, the generation of thick carbide when reduction gap solution strengthening also can suppress to cool off, the ductility of raising dual phase steel.Yet, the Si too high levels makes troubles for the hot rolling surface quality, as when homogenizing is handled, may form some low-melting complex oxides, and Si content height easy surface enrichment in annealing process, influence zinc-plated performance, so the present invention is controlled at Si content 0.03～0.19% scope.
Mn is typical austenite stabilizer element, significantly improves the hardening capacity of steel, and plays the effect of solution strengthening and refinement ferrite crystal grain, can significantly postpone perlitic transformation and bainite transformation.Mn can reduce A3, A1 stagnation point as the element that enlarges the γ phase region, and the too low perlitic transformation that easily causes of Mn content is difficult to form the martensite of q.s in the tissue; If but too high levels is also postponed ferritic separating out when can postpone perlitic transformation, and " velocity window " diminished, the bainite district moves to right, and makes steel become big to the susceptibility of processing condition, is unfavorable for stable batch process.Therefore, the present invention is controlled at Mn content 2.6～3.0% scope.
Als adds for deoxidation, when Als contains quantity not sufficient 0.010%, can not bring into play its effect; On the other hand, form the aluminum oxide agglomerate easily owing to add the aluminium of volume, so Als content is controlled at 0.01～0.04% scope.
The hardening capacity on the austenite island that Cr forms in the time of can improving intercritical annealing, the dual phase steel that does not contain chromium is compared, contain the chromium dual phase steel and can under lower cooling rate, obtain higher martensite volume fraction, simultaneously, chromium and carbon have stronger avidity, hinder the long-range diffusion of carbon atom, cause the difference of martensite pattern and the variation of distribution, and can reduce ferritic yield strength, more help obtaining the dual phase steel of low yield strength.If chromium content is too low, then solution strengthening and to improve the effect of hardening capacity not remarkable too highly then can increase smelting cost.The present invention is controlled at 0.15～0.9% scope with chromium content.
Cold-rolled biphase steel of the present invention passes through suitably to increase cheap C in the composition design, Si, the Mn constituent content is to improve the intensity and the hardening capacity of steel, reduce and the loss of strength of generation in order to remedy other valuable alloying elements, simultaneously by adding suitable alloying elements cr to promote that carbon spreads to austenite, reduce ferritic yield strength, and guarantee under low cooling rate, to obtain higher martensite volume fraction, to reduce the susceptibility of this steel to technology, be convenient to suitability for industrialized production, simultaneously, steel of the present invention obtains under the prerequisite of duplex structure in assurance, made full use of carbon, the strengthening effect of element silicon, manganese, the raising hardening capacity effect of chromium element.Owing to do not add alloying elements such as Mo, Nb, V, the smelting cost of this steel has obtained effective control.
(2) manufacture method
Every technical parameter principle of design is as follows in the cold rolling two-way steel making method of the present invention:
Adopt the 50kg vacuum induction furnace smelting according to described composition, forge into little square billet, steel billet is heated to 1150～1250 ℃ comparatively high temps with stove can guarantees the equal solid solution of all alloying elements in the steel, and the long period that is incubated 1.5～3h helps enough diffusions of alloying element, promote the homogenizing of alloying element, finally help the homogenizing of organizing.
Rolling on hot rolls subsequently, the roughing start rolling temperature is controlled at 1050～1110 ℃, helps guaranteeing follow-up final rolling temperature requirement, avoid because of temperature after the roughing cross low cause steel billet melt down heating again.The finish rolling finishing temperature is controlled at 860～900 ℃, if finishing temperature is lower than below 860 ℃, proeutectoid ferrite and austenite are all extended along machine direction, finish and change back formation ferrite and the alternatively distributed banded structure pattern of perlite, banded structure has heredity, the hot rolling banded structure is serious, austenite preferentially formed at banded structure crystal boundary place when cold rolling back continuous annealing was heated, and grow up to perlite fast, in process of cooling subsequently, form banded martensite, cause the steel plate elongation to descend; The curling temperature of simulation is controlled at 560～600 ℃, by reducing the homogeneity that the temperature of curling can effectively improve the hot-rolled substrate tissue, make the crystal grain of hot-rolled substrate evenly fine and smooth, thereby improve the hot rolling banded structure, and then reduce cold rolling recrystallization crystal particle dimension, make cold rolled annealed organize more even.
Hot-rolled sheet is cold rolling through carrying out on cold-rolling mill behind the pickling and cold-rolling, cold rolling draft is controlled at 45～75%, deformation energy storage by cold-rolled steel sheet increases, crystal grain is crushed, crushes, and the ferrite and the perlite of elongation are interlaced, helps the recrystallize refinement and the austenitic formation of ferrite crystal grain, if but cold rolling draft is too big, resistance to deformation increases, and has increased the load of milling train, wastes energy.Annealing temperature is controlled at 760～860 ℃, is preferably 780～830 ℃ and through being incubated 1～5min, can control austenitic formation, thereby influence fraction of martensite volume, composition and ferrite composition, final control mechanics performance.
Carry out the two-phase region anneal subsequently, steel plate slowly is cooled to 630～680 ℃ of intervals below the Ar1 temperature, in order to regulating and controlling austenite and ferritic content, slowly in the process of cooling part austenitic transformation will be arranged is ferrite, remaining austenite helps all changing martensite in fast cold process subsequently because carbon concentration increases, and hardening capacity also increases under low cooling rate, and martensitic phase intensity is also higher, thereby guarantees final tensile strength height, yield strength is low, unit elongation is high.Be quickly cooled to the Ms temperature again and carry out overaging processing 5～10min below 350 ℃, can guarantee that austenite all changes martensite into, and can not produce bainite structure and intensity is reduced, 5～10min is handled in overaging can adjust martensite effectively with ferritic phase structure, dislocation with separate out and equate microstructure, finally improves comprehensive mechanical property.This quick refrigerative speed can not be lower than 25 ℃/s, preferred 25～50 ℃/s.
The present invention on the basis that composition of steel rationally is set in conjunction with suitable heat processing technique and annealing process to realize the performance of the finished product, reduce the content of alloying constituent, when reaching performance, reduce cost as much as possible, this rigidity can be stablized simultaneously, technological fluctuation is little to performance impact, helps suitability for industrialized production.Having made full use of Si, Cr acts on ferritic " purification ", promoted carbon to austenitic diffusion, effectively reduce ferritic yield strength, improved austenitic hardening capacity simultaneously, guarantee that dual phase steel of the present invention can obtain higher martensite content under lower cooling rate.Facts have proved that dual phase steel of the present invention is owing to have low yield strength, low yield tensile ratio, high unit elongation, forming property is good, can be widely used in the reinforcing structure spare such as B column reinforcement plate increasing the car load crashworthiness, and reach loss of weight, emission reduction effect.
Description of drawings
Fig. 1 is the metallographic microstructure structure iron of 800MPa level cold-rolled biphase steel of the present invention.
Embodiment
Below in conjunction with specific embodiments and the drawings 800MPa level cold-rolled biphase steel of the present invention and manufacture method thereof are described in further detail:
Adopt the 50kg vacuum induction furnace to smelt at pilot plant, each embodiment surveys chemical ingredients (surplus is Fe and unavoidable impurities) as shown in table 1.With steel billet with stove be heated to 1150～1250 ℃ and be incubated 1.5～3h after rolling on conventional hot rolls, the roughing start rolling temperature is controlled at 1050～1110 ℃, the finish rolling finishing temperature is controlled at 860～900 ℃, curling temperature is controlled at 560～600 ℃, with hot-rolled sheet through cold rolling on conventional cold-rolling mill after the pickling, cold rolling draft is controlled at 45～75%, obtain the thick chill attitude cold-reduced sheet of 1.5mm, the hot dip process simulation test machine of the German IWATANI company through introducing carries out anneal again, sample is quickly cooled to 250～350 ℃ of overaging of carrying out 5～10min and handles postcooling to room temperature behind 760～860 ℃ of insulation 60s～300s behind slow cooling to 600～700 ℃.
Table 1:
| Embodiment | C | Si | Mn | Als | Cr |
| 1 | 0.10 | 0.05 | 3.0 | 0.04 | 0.56 |
| 2 | 0.18 | 0.03 | 2.86 | 0.03 | 0.42 |
| 3 | 0.13 | 0.19 | 2.72 | 0.02 | 0.35 |
| 4 | 0.16 | 0.16 | 3.0 | 0.03 | 0.15 |
| 5 | 0.14 | 0.12 | 2.70 | 0.04 | 0.78 |
| 6 | 0.17 | 0.07 | 2.77 | 0.01 | 0.45 |
| 7 | 0.15 | 0.09 | 2.95 | 0.02 | 0.20 |
| 8 | 0.11 | 0.06 | 2061 | 0.04 | 0.90 |
| 9 | 0.15 | 0.13 | 2.62 | 0.02 | 0.65 |
Yield strength Rp0.2 (MPa), tensile strength Rm (MPa), uniform elongation (%), unit elongation A to the cold-rolled biphase steel product of this above-mentioned nine embodiment
80mm(%), mechanical property such as work hardening exponent n10-15 value detects, and the results are shown in Table 2.
Table 2:
The mechanical property of embodiment of the invention dual phase steel annealing sample: yield strength Rp0.2=339～396MPa, tensile strength Rm=833～872MPa, unit elongation A
80mm=16.5～18.2%, n=0.108～0.134, yield tensile ratio is all in 0.4 extremely low scope, and the fluctuation of the mechanical property of each embodiment steel is little, and annealing process susceptibility is not strong, is suitable for suitability for industrialized production.
Adopt opticmicroscope that the microstructure of embodiments of the invention cold-rolled biphase steel is observed discovery, the duplex structure that it is organized as typical ferrite+island martensite body, organizing grain fineness number is 11～12 grades.
Embodiment and accompanying drawing show, cold-rolled biphase steel of the present invention has initial manufacture cementation index height, no yield extension and avoids premium propertiess such as strain cracking and piece surface be wrinkling, can be applicable in the reinforcing structure spares such as car longeron stiffening plate, B column reinforcement plate increasing the car load crashworthiness, and reach loss of weight, reduce discharging energy-conservation effect.Can be widely used in vehicle body collision safety spare and inner structural members, along with the light-weighted development of automobile, this steel has good market outlook.
Claims (4)
1. 800MPa level cold-rolled biphase steel, its chemical ingredients percentage ratio is by weight counted: C:0.10～0.18%, Si:0.03～0.19%, Mn:2.6～3.0%, Als:0.01～0.04%, Cr:0.15～0.9%, all the other are Fe and other inevitable impurity.
2. the manufacture method of the described 800MPa level of claim 1 cold-rolled biphase steel may further comprise the steps successively:
Steel billet is heated to 1150～1250 with stove, and insulation 1.5～3h carries out hot rolling subsequently, and the roughing start rolling temperature is controlled to be 1050～1110, and the finish rolling finishing temperature is controlled to be 860～900, and the curling temperature of simulation is controlled to be 560～600; Hot-rolled sheet carries out cold rolling after pickling, cold rolling draft is controlled to be 45～75%, carry out anneal then, annealing temperature is controlled at 760～860, and after being incubated 1～5min, slowly be cooled to 630～680 ℃, be quickly cooled to the above speed of 25 ℃/s again and carry out overaging processing 5～10min below 350.
3. according to the manufacture method of the described 800MPa level of claim 2 cold-rolled biphase steel, it is characterized in that: described annealing temperature is controlled to be 780～830 ℃.
4. according to the manufacture method of claim 2 or 3 described 800MPa level cold-rolled biphase steels, it is characterized in that: the refrigerative speed control is 25～50 ℃/s fast.
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| CN102644021A (en) * | 2012-04-23 | 2012-08-22 | 武汉钢铁(集团)公司 | 600MPa-level cold rolling dual-phase steel with low process sensitivity and production method |
| CN103131843A (en) * | 2013-01-02 | 2013-06-05 | 河北钢铁股份有限公司邯郸分公司 | Stabilization continuous annealing process of low-alloy and high-strength steel cold-rolled sheet used for automobile structural components |
| CN104328349A (en) * | 2014-11-14 | 2015-02-04 | 武汉钢铁(集团)公司 | High-strength medium-carbon low-silicon aluminum cold-rolled dual-phase steel and production method |
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| CN104630641A (en) * | 2014-12-11 | 2015-05-20 | 武汉钢铁(集团)公司 | 800MPa-grade high-strength high-plasticity low-carbon medium-manganese steel and manufacturing method thereof |
| CN105543674A (en) * | 2015-12-18 | 2016-05-04 | 东北大学 | Method for manufacturing cold-rolled ultrahigh-strength dual-phase steel with high local forming performance |
| CN107916359A (en) * | 2017-10-31 | 2018-04-17 | 华晨汽车集团控股有限公司 | A kind of preparation method of the medium managese steel with favorable forming property |
| CN109898017A (en) * | 2019-03-01 | 2019-06-18 | 鞍钢股份有限公司 | 1000MPa grades of cold-bending properties excellent cold-rolled biphase steel and production method |
| CN110029269A (en) * | 2019-03-29 | 2019-07-19 | 本钢板材股份有限公司 | A kind of 800MPa grades of low cost tempering dual phase steel and preparation method thereof |
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| CN102644021B (en) * | 2012-04-23 | 2014-07-23 | 武汉钢铁(集团)公司 | 600MPa-level cold rolling dual-phase steel with low process sensitivity and production method |
| CN103131843A (en) * | 2013-01-02 | 2013-06-05 | 河北钢铁股份有限公司邯郸分公司 | Stabilization continuous annealing process of low-alloy and high-strength steel cold-rolled sheet used for automobile structural components |
| CN103131843B (en) * | 2013-01-02 | 2014-05-28 | 河北钢铁股份有限公司邯郸分公司 | Stabilization continuous annealing process of low-alloy and high-strength steel cold-rolled sheet used for automobile structural components |
| CN104328348B (en) * | 2014-10-13 | 2016-09-07 | 河北钢铁股份有限公司邯郸分公司 | 800MPa level cold-rolled biphase steel and production method thereof |
| CN104328348A (en) * | 2014-10-13 | 2015-02-04 | 河北钢铁股份有限公司邯郸分公司 | 800 MPa grade cold-rolled double-phase steel and production method thereof |
| CN104328349B (en) * | 2014-11-14 | 2016-08-17 | 武汉钢铁(集团)公司 | The carbon system cold-rolled dual phase steel of low sial and production method in a kind of high intensity |
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| CN105543674A (en) * | 2015-12-18 | 2016-05-04 | 东北大学 | Method for manufacturing cold-rolled ultrahigh-strength dual-phase steel with high local forming performance |
| CN107916359A (en) * | 2017-10-31 | 2018-04-17 | 华晨汽车集团控股有限公司 | A kind of preparation method of the medium managese steel with favorable forming property |
| CN110653267A (en) * | 2018-06-29 | 2020-01-07 | 宝山钢铁股份有限公司 | Control method for micro-opening welding seam of hot galvanizing unit leveling equipment |
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| CN109898017A (en) * | 2019-03-01 | 2019-06-18 | 鞍钢股份有限公司 | 1000MPa grades of cold-bending properties excellent cold-rolled biphase steel and production method |
| CN110029269A (en) * | 2019-03-29 | 2019-07-19 | 本钢板材股份有限公司 | A kind of 800MPa grades of low cost tempering dual phase steel and preparation method thereof |
| CN115181890A (en) * | 2021-04-02 | 2022-10-14 | 宝山钢铁股份有限公司 | 1180 MPa-grade low-carbon low-alloy dual-phase steel and rapid heat treatment manufacturing method |
| CN115181890B (en) * | 2021-04-02 | 2023-09-12 | 宝山钢铁股份有限公司 | 1180 MPa-level low-carbon low-alloy dual-phase steel and rapid heat treatment manufacturing method |
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