CN105018843A - Q&P steel with vanadium and titanium added in compounded manner and manufacturing method of Q&P steel - Google Patents
Q&P steel with vanadium and titanium added in compounded manner and manufacturing method of Q&P steel Download PDFInfo
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Abstract
The invention discloses Q&P steel with vanadium and titanium added in a compounded manner and a manufacturing method of the Q&P steel and belongs to the field of third-generation automobile steel research. The Q&P steel with vanadium and titanium added in the compounded manner is capable of saving energy and efficient and comprises the components of, by weight, 0.17% to 0.22% of C, 1.3% to 1.6% of Si, 1.5% to 2.2% of Mn, not larger than 0.010% of P, not larger than 0.008% of S, 0.03% to 0.070% of V, 0.02% to 0.04% of Ti, the balance being Fe and inevitable impurities. The grain refinement effect is achieved through Ti in the steel and the precipitation strengthening effect is achieved through V. The manufactured energy-saving efficient Q&P steel is of a polygonal ferrite structure, a martensite structure and a retained austenite structure, the yield strength ranges from 550 MPa to 650 MPa, the tensile strength ranges from 1350 MPa to 1450 MPa, the percentage elongation after fracture is larger than or equal to 15.0%, and the product of strength and elongation is larger than or equal to 22.0 GPa*%.
Description
Technical field
The invention belongs to the Q & P steel PRODUCTION TRAITS field of third generation automobile steel, particularly relate to a kind of have energy-conservation, efficient vanadium, titanium compound add Q & P steel and manufacture method.
Background technology
Since the eighties in 19th century first-generation automobile come out, especially from since 20th century six the seventies, the automotive industry in North America, Japan and West Europe obtains develop rapidly.Automobile is one of mainstay industry of Chinese national economy, to pulling national economy and ensureing that employment etc. has a very important role.In recent years, China's automobile volume of production and marketing increases year by year, 2013, China's auto output 2211.68 ten thousand, sales volume 2198.41 ten thousand; 2014, China's automobile volume of production and marketing broke through 2,300 ten thousand in pairs; 2015, the expectation of automobile volume of production and marketing can continue to increase, and reaches 2,500 ten thousand.In the past ten years, the auto output of China rises to breakthrough 2,300 ten thousand from 2,000,000, within continuous 7 years, keep the speedup of about 25%, if country controls automobile market year speedup 8.5% in 10 years from now on, will more than 300,000,000 to the year two thousand twenty China automobile pollution; If year, speedup was low to moderate 5.5%, estimate the year two thousand twenty sales volume about more than 3,000 ten thousand, recoverable amount will more than 2.6 hundred million.In view of above-mentioned development trend, the fast development of automobile industry will inevitably driving automobile steel new theory, the appearance of new technology, development and application.
New automobile steel not only can strengthen by height the lightweight reaching automobile, and needs higher plasticity to improve the crystallized ability of steel and the collision safety performance of automobile.In order to intuitively and exactly describe this High-strength high-plasticity steel, American scholar Krupitzer and Heimbuch take the lead in proposing have high strength and ductility performance (i.e. the product of tensile strength Rm and plasticity A) the 3rd generation automobile steel concept, as the R&D direction of following new automobile steel.Because automobile steel has a large capacity and a wide range and with high content of technology, the developmental level of High-quality automobile steel is also the important symbol of a whole steel research of country and production level.Q & P steel is the representative of third generation automobile steel, by Q & P technique, can realize high intensity and the combination of plasticity.Q & P steel because of the combination of the obdurability of excellence, and does not need add alloying element and have broad application prospects.At present to the research of Q & P steel more be two-step approach thermal treatment process, one-step technology is studied less.One step thermal treatment process is comparatively simple production technique, is also more efficient and energy-conservation heat treatment process, is easy to realize actual industrial production.Herein by experiment, determine the industrial Composition Control scope of single stage method, and rolling and thermal treatment optimal processing parameter,
In the published patent about third generation automobile Q & P steel, Chinese patent application CN201310051807.3, describe a kind of method utilizing alloying element partition to prepare silicomanganese system Q & P steel, it adopts rational chemical composition design, utilizes alloying element in the two-phase region partition mechanism of action, prepares low carbon high-strength Q & P steel.Chinese patent application CN201310520580.2, openly describe a kind of two-step approach Q & P980 Heat Treatment Of Steel technique, wherein tensile strength reaches 1000MPa, and strength and ductility product reaches more than 25GPa%.Above two inventions are produced mainly through two-step approach Q & P technique, compared to single stage method, power consumption, efficiency is low, and two-step approach produces the heat-treatment production line that cannot meet some enterprise, and although single stage method plasticity is high less than two-step approach, its tensile strength is than two-step approach height 200-400MPa, and strength and ductility product also can reach the level of more than 20GPa%.After the present invention adds titanium and vanadium, make its intensity higher, and plasticity does not almost reduce.So single stage method Q & P technique herein has energy-conservation, efficient manufacture method.
In sum, be in developmental stage for third generation automobile Q & P steel at present, the single stage method Q & P technique for titaniferous and vanadium at home and abroad have not been reported.Because the single stage method Q & P technique of titaniferous and vanadium and two-step approach have bigger difference, the mainly more difficult control of quenching temperature in process of production.Therefore need the research of experimentally room, new design and processes route is taked in metallurgically design and technology controlling and process, meets the third generation automobile steel of performance requriements with low cost, less energy-consumption and high efficiency production, to meet the need of market.
Summary of the invention
In order to solve the problem, the object of the present invention is to provide a kind of production cost low, the time is short, and efficiency is high, energy-conservation, and the Q & P steel of the vanadium of stable performance and the interpolation of titanium compound and manufacture method thereof.
Present invention employs following technical scheme: the Q & P steel that vanadium and titanium compound are added, main component and the weight percent content of this Q & P steel are: C 0.17 ~ 0.22%, Si 1.3 ~ 1.6%, Mn 1.5 ~ 2.2%, P≤0.010%, S≤0.008%, V 0.03 ~ 0.07%, Ti 0.02 ~ 0.04%, and surplus is Fe and inevitable impurity.
Another object of the present invention is to provide the manufacture method of the Q & P steel of above-mentioned vanadium and the interpolation of titanium compound, specifically comprises the following steps:
1. prepare burden: take each raw material respectively according to design mix, mix, carry out melting strand, obtain slab;
Step 2. hot rolling technology: slab step 1 prepared is heated to 1170 ~ 1220 DEG C from room temperature, be incubated 1.5 ~ 2 hours, be 1150 DEG C of open rollings in temperature, hot rolling finishing temperature is 890 ~ 920 DEG C, section cooling line starts water-cooled by during slab air cooling to 780 ~ 820 DEG C after hot rolling, and cooling rate controls at 15-25 DEG C/s, is chilled to and starts to batch lower than when 200 DEG C, what make hot-rolled sheet is organized as ferrite+martensite+bainite, hot rolling thickness of slab 3.5-4.5mm;
Step 3. cold-rolling process: step 2 is obtained hot-rolled sheet and carry out cold rolling after overpickling, cold rolling draft 50 ~ 70%, cold rolling thickness of slab 1.4-1.7mm;
Step 4. continuous annealing process: step 3 is obtained cold-reduced sheet and be heated to 780 ~ 820 DEG C with 10 DEG C/s from room temperature, soaking time is 120 ~ 150s, is cooled to 170 ~ 210 DEG C with 30 ~ 50 DEG C/s, insulation 100 ~ 150s, after be cooled to room temperature, namely obtain automobile steel.
C: be soft steel tradition, economic strengthening element, the increase of the intensity carbon content of steel and improving.In the partition process of single stage method Q & P steel, C spreads to austenite from martensite, plays the effect of stable austenite, and the residual austenite in steel is increased, and the strength and ductility product of steel is improved.
Si: be the fundamental element in steel, play desoxydatoin in steelmaking process, in the partition process of Q & P steel, Si plays the formation stoping cementite, makes C not form cementite when partition and fully spread in austenite.
Mn: as the essentially consist element of low alloy steel, Mn plays solution strengthening in steel, in Q & P steel, Mn can play the effect of stable austenite.
V:V can improve the hardening capacity of steel, dissolves in ferrite and has strengthening effect, can form stable carbide, crystal grain thinning, and N can strengthen the effect of V.The method that the precipitation strength of V and the grain refining of Ti can be utilized to combine obtains larger strengthening effect.
Ti: be micro alloying element, adds the intensity that a small amount of Ti can improve steel, plays the effect of precipitation strength and grain refining in steel.Wherein TiN effectively can stop austenite crystal growing up in heat-processed, plays the effect of fining austenite grains, and can improve the toughness of steel.
The present invention, owing to have employed above technical scheme, makes it, compared with two step method Q & P technique and prior art, to have the following advantages and positively effect:
(1) the invention provides a kind of Q & P steel can produced under traditional continuous annealing process and preparation method thereof, this method does not need through second-heating partition process when connecting and moving back, direct quenching carries out insulation partition to certain stablizing, by means of only suitable Composition Design and technology controlling and process, yield strength is made to reach 550 ~ 650MPa, tensile strength is 1350 ~ 1450MPa, elongation after fracture >=15.0%, strength and ductility product >=22.0GPa%;
(2) the produced autobody sheet organization type of the present invention is polygonal ferrite, martensite and residual austenite body tissue, and the precipitate containing V, Ti, play the effect of precipitation strength, compared to two step method Q & P technique, its armor plate strength produced is high, and there is certain plasticity, meet the standard of automobile steel high-strong toughness;
(3) the present invention's produced Plate Production cost is low, and the time is short, and efficiency is high, energy-conservation, and stable performance, there is excellent obdurability coupling.By composition and technique adjustment, can can not promoting single stage method Q & P steel in the enterprise of production two step method Q & P steel at some, laying the foundation to the transformation of high-performance, low cost, less energy-consumption and high efficiency production line for realizing enterprise's production line.
Accompanying drawing explanation
Fig. 1 be vanadium of the present invention and titanium compound add there is energy-conservation, the efficient quenching temperature of Q & P steel and the graph of a relation of performance.Wherein X-coordinate is temperature, and ordinate zou is tensile strength and strength and ductility product.
Fig. 2 is the hot rolling metallograph with energy-conservation, efficient Q & P steel that vanadium of the present invention and titanium compound are added.
Fig. 3 is the metallographic had after energy-conservation, efficient Q & P Heat Treatment Of Steel that vanadium of the present invention and titanium compound are added
Photo; (a) partition temperature 190 DEG C, (b) partition temperature 200 DEG C, (c) partition temperature 210 DEG C.
Fig. 4 is the transmission electron microscope photo of different austenite pattern after thermal treatment.
Embodiment
With the drawings and specific embodiments, the present invention is further detailed explanation below.
Embodiment 1:
First carry out smelting according to mentioned component scope, continuous casting, then detect the composition of strand, see the following form 1.
The composition (wt.%) of table 1 strand
Hot rolling adopts following technique: the strand of preparation is heated to 1200 DEG C from room temperature, be incubated 2 hours, start rolling temperature is 1150 DEG C, hot rolling finishing temperature is 900 DEG C, section cooling line starts water-cooled by during slab air cooling to 800 DEG C after hot rolling, cooling rate is at 20 DEG C/s, is chilled to and starts to batch lower than when 190 DEG C.At this moment hot-rolled sheet be organized as ferrite+martensite+bainite, see Fig. 2, hot rolling thickness of slab is 3.6mm.Cold-rolling process is as follows: carry out cold rolling after overpickling by hot-rolled sheet, cold rolling draft 58%, cold rolling thickness of slab 1.5mm.Take 3 examples below, be different partition temperature, then carry out Performance Detection.
Cold-reduced sheet is heated to 800 DEG C with 10 DEG C/s from room temperature, and soaking time is 150s, is cooled to 190 DEG C with 50 DEG C/s, insulation 100s, after be cooled to room temperature, performance is in table 2.
The performance of Q & P steel when table 2 partition temperature is 190 DEG C
Each mechanical property all reaches required performance index as can be seen from the above table, and tensile strength is 1389MPa, and elongation is 17.5%, strength and ductility product 24.3GPa%.Wherein tensile strength wants high about 200MPa compared to two-step approach.Metallograph, as shown in Fig. 3 (a), is made up of ferrite, martensite and residual austenite.
Embodiment 2:
First carry out smelting according to mentioned component scope, continuous casting, then detect the composition of strand, see the following form 3.
The composition (wt.%) of table 3 strand
Hot rolling adopts following technique: the strand of preparation is heated to 1170 DEG C from room temperature, be incubated 1.7 hours, start rolling temperature is 1150 DEG C, hot rolling finishing temperature is 920 DEG C, section cooling line starts water-cooled by during slab air cooling to 820 DEG C after hot rolling, cooling rate is at 25 DEG C/s, is chilled to and starts to batch lower than when 190 DEG C.At this moment hot-rolled sheet be organized as ferrite+martensite+bainite, see Fig. 2, hot rolling thickness of slab is 3.5mm.Cold-rolling process is as follows: carry out cold rolling after overpickling by hot-rolled sheet, cold rolling draft 70%, cold rolling thickness of slab 2.45mm.Take 3 examples below, be different partition temperature, then carry out Performance Detection.
Cold-reduced sheet is heated to 780 DEG C with 10 DEG C/s from room temperature, and soaking time is 135s, is cooled to 200 DEG C with 40 DEG C/s, insulation 130s, after be cooled to room temperature, performance is in table 4.
The performance of Q & P steel when table 4 partition temperature is 200 DEG C
Each mechanical property all reaches required performance index as can be seen from the above table, and tensile strength is 1364MPa, and elongation is 19.7%, strength and ductility product 26.9GPa%.Wherein tensile strength wants high about 200MPa compared to two-step approach.Metallograph, as shown in Fig. 3 (b), is made up of ferrite, martensite and residual austenite.
Embodiment 3:
First carry out smelting according to mentioned component scope, continuous casting, then detect the composition of strand, see the following form 5.
The composition (wt.%) of table 5 strand
Hot rolling adopts following technique: the strand of preparation is heated to 1220 DEG C from room temperature, be incubated 1.5 hours, start rolling temperature is 1150 DEG C, hot rolling finishing temperature is 890 DEG C, section cooling line starts water-cooled by during slab air cooling to 780 DEG C after hot rolling, cooling rate is at 15 DEG C/s, is chilled to and starts to batch lower than when 190 DEG C.At this moment hot-rolled sheet be organized as ferrite+martensite+bainite, see Fig. 2, hot rolling thickness of slab is 4.5mm.Cold-rolling process is as follows: carry out cold rolling after overpickling by hot-rolled sheet, cold rolling draft 50%, cold rolling thickness of slab 2.1mm.Take 3 examples below, be different partition temperature, then carry out Performance Detection.
Cold-reduced sheet is heated to 820 DEG C with 10 DEG C/s from room temperature, and soaking time is 120s, is cooled to 210 DEG C with 30 DEG C/s, insulation 100s, after be cooled to room temperature, performance is in table 6.
The performance of Q & P steel when table 6 partition temperature is 210 DEG C
Each mechanical property all reaches required performance index as can be seen from the above table, and tensile strength is 1351MPa, and elongation is 17.6%, strength and ductility product 23.8GPa%.Wherein tensile strength wants high about 200MPa compared to two-step approach.Metallograph, as shown in Fig. 3 (c), is made up of ferrite, martensite and residual austenite.
The transmission electron microscope photo of above-mentioned three kinds of different partition temperature is as Fig. 4, wherein all comprise the photo of different austenite pattern, wherein (a) is the film like austenite between martensite lath, the block austenite that (b) is intracrystalline, and (c) is intracrystalline strip austenite.There is portion of residual austenite in steel, makes steel, when being out of shape, TRIP effect occur, increasing the strong plasticity of steel.As fully visible, the steel plate in the present invention has excellent toughness and tenacity.
It should be noted last that, above embodiment is only in order to illustrate technical scheme of the present invention and unrestricted.Although with reference to embodiment to invention has been detailed description, will be understood by those skilled in the art that, modify to technical scheme of the present invention or equivalent replacement, do not depart from the spirit and scope of technical solution of the present invention, it all should be encompassed in the middle of right of the present invention.
Claims (3)
1. the Q & P steel of a vanadium and the interpolation of titanium compound, it is characterized in that, the predominant quantity per-cent of described Q & P steel is: C 0.17 ~ 0.22%, Si 1.3 ~ 1.6%, Mn 1.5 ~ 2.1%, P≤0.010%, S≤0.008%, V 0.03 ~ 0.07%, Ti 0.02 ~ 0.04%, and surplus is Fe and inevitable impurity.
2. a manufacture method for the Q & P steel of vanadium as claimed in claim 1 and the interpolation of titanium compound, is characterized in that, specifically comprise the following steps:
Step 1. is prepared burden: take each raw material respectively according to design mix, mix, and carries out melting strand, obtains slab;
Step 2. hot rolling technology: slab step 1 prepared is heated to 1170 ~ 1220 DEG C from room temperature, be incubated 1.5 ~ 2 hours, be 1150 DEG C of open rollings in temperature, hot rolling finishing temperature is 890 ~ 920 DEG C, section cooling line starts water-cooled by during slab air cooling to 780 ~ 820 DEG C after hot rolling, and cooling rate controls at 15-25 DEG C/s, is chilled to and starts to batch lower than when 200 DEG C, what make hot-rolled sheet is organized as ferrite+martensite+bainite, hot rolling thickness of slab 3.5-4.5 mm;
Step 3. cold-rolling process: step 2 is obtained hot-rolled sheet and carry out cold rolling after overpickling, cold rolling draft 50 ~ 70%, cold rolling thickness of slab 1.4-1.7 mm;
Step 4. continuous annealing process: step 3 is obtained cold-reduced sheet and be heated to 780 ~ 820 DEG C with 10 DEG C/s from room temperature, soaking time is 120 ~ 150 s, is cooled to 170 ~ 210 DEG C with 30 ~ 50 DEG C/s, insulation 100 ~ 150 s, after be cooled to room temperature, namely obtain automobile steel.
3. the manufacture method according to claims 2, is characterized in that, the yield strength of described automobile steel is 550 ~ 650 MPa, and tensile strength is 1350 ~ 1450 MPa, elongation after fracture >=15.0%, strength and ductility product >=22.0 GPa%.
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| CN108486494A (en) * | 2018-06-05 | 2018-09-04 | 西北工业大学 | The production method of vanadium micro-alloying 1300MPa grade high-strengths hot rolled steel plate and cold-rolled biphase steel plate |
| CN109072374A (en) * | 2016-03-31 | 2018-12-21 | 杰富意钢铁株式会社 | The manufacturing method of sheet metal and coated steel sheet and hot rolled steel plate, manufacturing method, the manufacturing method of the manufacturing method of sheet metal and coated steel sheet of cold rolling is fully hard steel plate |
| CN111118397A (en) * | 2020-01-19 | 2020-05-08 | 攀钢集团攀枝花钢铁研究院有限公司 | 980 MPa-grade quenching distribution steel and preparation method thereof |
| CN111440987A (en) * | 2020-05-11 | 2020-07-24 | 武汉钢铁有限公司 | Quenching distribution steel with tensile strength of more than or equal to 980MPa produced by adopting short process and method |
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Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN109072374A (en) * | 2016-03-31 | 2018-12-21 | 杰富意钢铁株式会社 | The manufacturing method of sheet metal and coated steel sheet and hot rolled steel plate, manufacturing method, the manufacturing method of the manufacturing method of sheet metal and coated steel sheet of cold rolling is fully hard steel plate |
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| CN111118397A (en) * | 2020-01-19 | 2020-05-08 | 攀钢集团攀枝花钢铁研究院有限公司 | 980 MPa-grade quenching distribution steel and preparation method thereof |
| CN111440987A (en) * | 2020-05-11 | 2020-07-24 | 武汉钢铁有限公司 | Quenching distribution steel with tensile strength of more than or equal to 980MPa produced by adopting short process and method |
| CN111440987B (en) * | 2020-05-11 | 2021-03-02 | 武汉钢铁有限公司 | Quenching distribution steel with tensile strength of more than or equal to 980MPa produced by adopting short process and method |
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