CN103805851A - Ultrahigh strength low-cost hot rolling Q and P (quenching and partitioning) steel and production method thereof - Google Patents

Ultrahigh strength low-cost hot rolling Q and P (quenching and partitioning) steel and production method thereof Download PDF

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CN103805851A
CN103805851A CN201210461655.XA CN201210461655A CN103805851A CN 103805851 A CN103805851 A CN 103805851A CN 201210461655 A CN201210461655 A CN 201210461655A CN 103805851 A CN103805851 A CN 103805851A
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CN103805851B (en
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李自刚
王焕荣
王巍
胡晓萍
李建业
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Baoshan Iron and Steel Co Ltd
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Abstract

The invention provides ultrahigh strength low-cost hot rolling Q and P (quenching and partitioning) steel and a production method thereof. The ultrahigh strength low-cost hot rolling Q and P steel comprises the following components in percentage by weight: 0.20-0.40% of C, 0.8-2.0% of Si, 1.5-3.0% of Mn, less than or equal to 0.015% of P, less than or equal to 0.005% of S, 0.02-0.08% of Al, less than or equal to 0.006% of N, 0.005-0.015% of Ti, less than or equal to 30ppm of O and the balance of Fe and inevitable impurities. The production method is characterized in that the low-cost component design is adopted, on the basis of conventional C-Mn steel components, the Si content is increased so as to inhibit precipitation of cementite, meanwhile, a trace amount of Ti is added so as to control the size of austenite crystals during heating, so that tiny lath martensite is obtained during quenching, thus the low-cost manufacturing of the ultrahigh strength hot rolling wear-resistant steel is realized. The microstructure of the ultrahigh strength hot rolling Q and P steel is martensite plus retained austenite, the tensile strength of the steel is greater than or equal to 1400 Mpa, and the elongation percentage of the steel is greater than 10%.

Description

A kind of superstrength low cost hot rolling Q & P steel and production method thereof
Technical field
The invention belongs to wear resisting steel field, particularly a kind of superstrength low cost hot rolling Q & P steel and production method thereof, tensile strength >=1400MPa, unit elongation >10%.
Background technology
From professor John.G.Speer of Colorade USA mining institute in 2003, quenching+partition (Quenching and Partitioning is proposed first, Q & P) concept since, Q & P steel has been acknowledged as the advanced high-strength steel of the automobile steel field third generation.
The main technique of Q & P steel is: steel is heated to complete austenitic area or part austenitic area, after insulation for some time, is quenched into rapidly M sand M f(M sand M frepresent respectively Ms (martensite start) point and end temp) between a certain temperature there is martensite+residual austenite body tissue of a certain amount of residual austenite to obtain, stop cold temperature or make carbon atom spread enrichment from oversaturated martensite to residual austenite a little more than stopping being incubated at cold temperature certain hour in quenching subsequently, thereby the at room temperature stable existence of residual austenite that makes rich carbon, is then cooled to room temperature.
The steel obtaining by this technique has very high intensity and plasticity, more than its tensile strength can reach 2000MPa, and unit elongation >=10%.The typical organization of Q & P steel in the time of room temperature is lath martensite and film like residual austenite, sometimes may contain a small amount of plate martensite.Q & P steel mechanical property is mainly to be determined by lath martensite and the width of sheet of film like residual austenite and the percent by volume of residual austenite.
The concept of Q & P steel is after the people such as Speer propose, and many research groups have all carried out detailed and deep research to this class new steel grade from theoretical and test aspect in the world.Comprehensive these achievements in research are not difficult to find, operational path in process of the test is substantially all to adopt heat-treating methods or two-step approach, be that steel is through after austenitizing, first quench and then steel is reheated to stopping a little more than quenching and is incubated after for some time at cold temperature, be finally quenched to again room temperature.This operational path is proper concerning the production of cold rolling or pot galvanize product.For during Hot Strip Rolling, due to cooling at laminar flow and batch between do not reheat fast process or batch after ability that entire volume is reheated, therefore, produce on line and cannot realize according to two-step approach production Q & P steel at hot continuous rolling, the one-step technology route that can only adopt laminar flow Cooling Quenching to certain temperature then to batch.
At present, relevant hot rolling Q & P steel is a kind of carbon silicomanganese hot rolling Q & P steel as Chinese patent CN102226248A has introduced, but do not adopt micro-Ti to control austenite grain size in design of alloy, and the highest 1400MPa that is no more than of the tensile strength of steel plate.Also introduce a kind of production technique of complex phase Q & P steel just like Chinese patent CN101775470A, be actually a kind of technique of two-step approach production Q & P steel; It is Q & P steel that Chinese patent CN101487096A has introduced a kind of use two step heat treating process production C-Mn-Al, and its principal feature is that unit elongation is very high, is mainly used in automotive field.
Summary of the invention
The object of this invention is to provide a kind of superstrength low cost hot rolling Q & P steel and production method thereof, the microtexture of the super high strength hot rolled Q & P steel obtaining is martensite+residual austenite, its tensile strength >=1400MPa, unit elongation >10%.
For achieving the above object, technical scheme of the present invention is:
The present invention is by low cost Composition Design, adopt hot continuous rolling process, on the composition basis of traditional C-Mn steel, separate out by carrying high Si content inhibition cementite, austenite grain size while simultaneously adding micro-Ti to control heating tiny lath martensite while quenching to obtain, thus low cost fabrication goes out super high strength hot rolled wear resisting steel.
Particularly, a kind of superstrength low cost hot rolling Q & P steel of the present invention, its composition weight percent is: C 0.20% ~ 0.40%, Si 0.8% ~ 2.0%, Mn 1.5% ~ 3.0%, P≤0.015%, S≤0.005%, Al 0.02 ~ 0.08%, N≤0.006%, Ti 0.005% ~ 0.015%, O≤30ppm, all the other are Fe and inevitable impurity; The microtexture of super high strength hot rolled Q & P steel is martensite+residual austenite, its tensile strength >=1400MPa, unit elongation >10%.
In Composition Design of the present invention:
C, is element the most basic in steel, is also one of most important element in the present invention simultaneously.Carbon, as the interstitial atom in steel, plays very important effect to the intensity that improves steel, and yield strength and tensile strength to steel have the greatest impact.If the content of carbon is lower than 0.2% in steel, in the situation that not adding other alloying elements, the intensity of hot rolling Q & P steel is difficult to reach very high intensity as more than 1500MPa; And in the process of batching isothermal, the degree that carbon spreads enrichment from martensite to austenite is not enough to guarantee the stability of residual austenite in the time of room temperature.If the carbon content in steel is greater than 0.4%, although can guarantee there are enough carbon atoms in isothermal process to enrichment in austenite batching, cause M because carbon content is high sand M fpoint reduces, and under identical processing condition, the content of residual austenite increases, and the carbon concentration in corresponding residual austenite also can reduce, and stability reduces.In addition, too high impelling strength and the weldability etc. to steel plate of carbon content has disadvantageous effect.Therefore, in steel, carbon content control can guarantee that in the scope of 0.20-0.40% steel plate has good high strength and high-ductility coupling;
Si, is element the most basic in steel, is also one of most important element in the present invention simultaneously.Compared with traditional hot-rolling high-strength steel, high strength Q & P steel is substantially all at present the Composition Design principle that adopts high silicon.The main purpose that adds high silicon in Q & P steel is to batch separating out of slow cooling stage inhibition cementite, promoting carbon enrichment in residual austenite, stable austenite.If the add-on of silicon in steel is lower than 0.8%, steel is being quenched into M s-M fbetween batch in annealing process carbide precipitate as cementite, reduced the carbon content in residual austenite, make residual austenite become unstable.At continuation Slow cooling, in the process of room temperature, residual austenite is likely decomposed, and the performance of steel is caused to disadvantageous effect; On the other hand, the content of silicon in steel can not be too high, if silicone content exceedes 2.0%, easily forms the oxide compound of silicon in steel, makes steel generation brittle rupture.Therefore, in steel, the content of silicon is controlled at 0.8 ~ 2.0%, and preferable range is between 1.2 ~ 1.8%;
Mn, is the element that expands austenite phase region, can reduce the critical cooling velocity of steel, and stable austenite is postponed austenite to pearlitic transformation.In the present invention, for guaranteeing the intensity of steel plate, the content of manganese generally should be controlled at more than 1.5%; On the other hand, manganese content can not be too high, as exceed 3.0%, and the intensity of steel plate easily reduces on the contrary, and this is mainly to improve austenitic stability because manganese content increases, and is quenched into M sand M fbetween obtain many residual austenites, reduced the intensity of steel plate.Therefore, in the present invention, the content general control of manganese can obtain the good steel plate of over-all properties between 1.5-3.0%.
P, is the impurity element in steel, in steel, when the content of phosphorus higher (>=0.1%), forms Fe 2p separates out around crystal grain, reduces plasticity and the toughness of steel, therefore its content is more low better, general control better and not improves steel-making cost in 0.015%.
S, is present in around the crystal grain of steel with the eutectiferous form of FeS-Fe when in steel, sulphur content is higher, reduces the mechanical property of steel, and its content and seemingly Phosphorus, is also more low better, when actual production, is conventionally controlled in 0.005%.
Al, the effect of aluminium in steel is mainly in steelmaking process, to carry out deoxidation.In addition, aluminium also can the nitrogen in steel be combined and be formed AlN, if the content of nitrogen in steel is higher, the titanium adding is not enough to the fixed nitrogen atomic time, aluminium but also can play the effect of fixed nitrogen.Therefore, in steel, the content of aluminium will be controlled in suitable scope, is conventionally controlled at 0.02-0.08%, and preferable range is 0.03-0.06%.
Ti, add-on is corresponding with the add-on of nitrogen in steel.The stoichiometric ratio that in steel, Ti/N is controlled at TiN is advisable below 3.42.If Ti/N is greater than 3.42, in steel, easily form thicker TiN particle, the impelling strength of steel plate is caused to disadvantageous effect, thick TiN particle can become the formation of crack of fracture.On the other hand, the content of Ti can not be too low, otherwise the TiN quantity forming very little, do not have the effect of refine austenite crystal grain.Therefore, in steel, the content of titanium will be controlled at suitable scope, and the add-on of titanium is controlled between 0.005-0.015% conventionally, and preferable range is controlled at 0.008-0.012%.
N, belongs to impurity element in the present invention, and its content is more low better.Nitrogen is also inevitable element in steel, and under normal circumstances, the residual content of nitrogen in steel is between 0.002-0.004%, and these nitrogen elements can be by being combined and fixing with acid-soluble aluminium and Ti.In order not improve steel-making cost, the content of nitrogen is controlled at 0.006% with interior, and preferable range is for being less than 0.004%.
O, is inevitable element in steelmaking process, and for the purpose of the present invention, in steel, the content of oxygen generally can reach below 30ppm by after aluminium deoxidation, can not cause significant adverse impact to the performance of steel plate.Therefore, by the Control for Oxygen Content in steel in 30ppm.
The production method of superstrength low cost hot rolling Q & P steel of the present invention, comprises the steps:
1) smelt, cast
Press mentioned component converter or electrosmelting+vacuum oven secondary refining, be cast as strand or ingot;
2) heating
Strand or ingot heating, 1100 ~ 1200 ℃ of Heating temperatures, soaking time 1 ~ 2 hour;
3) hot rolling
1000 ~ 1070 ℃ of start rolling temperatures, more than 950 ℃, multi-pass is depressed greatly and accumulative total deflection >=50%, and main purpose is refine austenite crystal grain; Subsequently intermediate blank treat temperature to 800 ~ 850 ℃, then carry out last 3 ~ 6 passage rollings;
4) press quenching
Finish to gauge finishes rear steel plate and is cooled to 150 ~ 250 ℃ with the cooling rate of >50 ℃/s, obtains martensite+residual austenite body tissue, after finally batching, slowly cools to room temperature.
In manufacture method of the present invention:
If slab heating temperature lower than 1100 ℃ and soaking time too short, be unfavorable for the homogenizing of alloying element; And when temperature is during higher than 1200 ℃, not only improve manufacturing cost, and the heating quality of steel billet is declined to some extent.Therefore, slab heating temperature general control is proper at 1100 ~ 1200 ℃.
Similarly, soaking time also needs to control within the specific limits.Soaking time is too short, and solute atoms is as abundant not in the diffusion of Si, Mn etc., and the heating quality of steel billet can not be guaranteed; Soaking time is long makes austenite crystal thick and improved manufacturing cost, therefore soaking time should be controlled between 1 ~ 2 hour.Heating temperature is higher, and corresponding soaking time can suitably shorten.
The present invention adopts higher carbon content (0.2-0.4%), make after steel plate press quenching (quenching stops cold temperature 150-250 ℃) to batch to have in annealing process more carbon atom from martensite to residual austenite diffusion with stable residual austenite; And higher Si content can reduce steel plate the separating out of carbide in annealing process, reduce the consumption of carbon atom, stable residual austenite; In addition, higher Mn content is on the basis of carbon atom raising stability of retained austenite, further to improve its stability.
Technology provided by the present invention can be used for manufacturing tensile strength >=1400MPa, and thickness is at the hot rolling super intensified abrasion-proof steel plate of 4-12mm, has good unit elongation (>10%) simultaneously, shows excellent strong plasticity coupling.
Beneficial effect of the present invention:
1) cost of alloy of steel plate of the present invention significantly reduces.The present invention, compared with traditional low-alloy high-strength steel, does not add any noble metal element as Nb, V, Cu, Ni, Mo etc., and the trace alloying element Ti of interpolation is not only cheap, and add-on is very low.Adopt hot continuous rolling process to produce than producing and also can further reduce production costs with slab line.Therefore, the production cost of steel plate significantly reduces.
2) mechanical property of steel plate of the present invention significantly improves, and customer using cost reduces.Although cost of alloy significantly reduces, the tensile strength of steel plate and unit elongation are largely increased compared with traditional low-alloy high-strength steel.Therefore, use the field of slab wear resisting steel can use the ultrahigh-strength wear-resistant steel of thinner specification at some, weight reduction, reduces costs.
3) steel plate that adopts the present invention to produce has low cost superstrength and high rigidity advantage, the field that is particularly suitable for improving wear resistance.
Accompanying drawing explanation
Fig. 1 is artwork of the present invention.
Fig. 2 is the metallographic microstructure photo of the embodiment of the present invention 2 steel plates.
Fig. 3 is the metallographic microstructure photo of the embodiment of the present invention 4 steel plates.
Embodiment
Below in conjunction with embodiment and accompanying drawing, the present invention will be further described.
Referring to Fig. 1, technical process of the present invention: adopt converter or electrosmelting, through vacuum oven secondary refining, be cast as steel billet or steel ingot; Heating, steel billet or Heating Steel Ingots temperature: 1100 ~ 1200 ℃, soaking time: 1 ~ 2 hour; Rolling, start rolling temperature: 1000 ~ 1070 ℃, more than 950 ℃ multi-pass depress greatly and accumulative total deflection >=50%, subsequently intermediate blank treat temperature to 800 ~ 850 ℃, then carry out last 3 ~ 6 passage rollings; Press quenching, is cooled to 150 ~ 250 ℃ with the cooling rate of >50 ℃/s, obtains martensite+residual austenite body tissue, after finally batching, slowly cools to room temperature.
The embodiment of the present invention is referring to table 1.Table 2 is production method and the performance of the embodiment of the present invention.
Table 1 unit: weight percent
Embodiment C Si Mn P S Al N Ti O
1 0.20 1.95 2.95 0.009 0.0027 0.020 0.0044 0.015 0.0025
2 0.25 1.66 2.55 0.007 0.0034 0.067 0.0058 0.008 0.0028
3 0.29 1.54 2.24 0.007 0.0023 0.036 0.0033 0.006 0.0024
4 0.35 0.83 1.85 0.013 0.0031 0.078 0.0041 0.011 0.0030
5 0.39 1.22 1.53 0.011 0.0033 0.050 0.0046 0.013 0.0027
Table 2
Figure BDA00002411911500061
Fig. 2 and Fig. 3 have provided the typical metallograph of embodiment 2,4 steel.From metallograph, can find out, the tissue of steel plate is mainly lath martensite.Known according to X-ray diffraction result, the content of embodiment 2,4 detecting residual austenite in steel plates is respectively 6.19% and 9.76%.Therefore, the microtexture of light plate of the present invention is lath martensite+a small amount of residual austenite.Due to the existence of more residual austenite, make steel plate in tensile deformation process, undergo phase transition induced plastic (TRIP) effect, improve tensile strength and the plasticity of steel plate, make steel plate there is good wear resistance.

Claims (6)

1. a superstrength low cost hot rolling Q & P steel, its composition weight percent is: C0.20% ~ 0.40%, Si 0.8% ~ 2.0%, Mn 1.5% ~ 3.0%, P≤0.015%, S≤0.005%, Al 0.02 ~ 0.08%, N≤0.006%, Ti 0.005% ~ 0.015%, O≤30ppm, all the other are Fe and inevitable impurity; The microtexture of super high strength hot rolled Q & P steel is martensite+residual austenite, its tensile strength >=1400MPa, unit elongation >10%.
2. superstrength low cost hot rolling Q & P steel as claimed in claim 1, is characterized in that, described Si content is 1.2 ~ 1.8%, weight percent meter.
3. superstrength low cost hot rolling Q & P steel as claimed in claim 1, is characterized in that, described Al content is 0.03 ~ 0.06%, weight percent meter.
4. superstrength low cost hot rolling Q & P steel as claimed in claim 1, is characterized in that, described Ti content is 0.008 ~ 0.012%, weight percent meter.
5. superstrength low cost hot rolling Q & P steel as claimed in claim 1, is characterized in that described N content≤0.004%, weight percent meter.
6. as the production method of the superstrength low cost hot rolling Q & P steel as described in any one in claim 1 ~ 5, comprise the steps:
1) smelt, cast
Press mentioned component converter or electrosmelting+vacuum oven secondary refining, be cast as strand or ingot;
2) heating
Strand or ingot heating, 1100 ~ 1200 ℃ of Heating temperatures, soaking time 1 ~ 2 hour;
3) hot rolling
1000 ~ 1070 ℃ of start rolling temperatures, more than 950 ℃ multi-pass depress greatly and accumulative total deflection >=50%, subsequently intermediate blank treat temperature to 800 ~ 850 ℃, then carry out last 3 ~ 6 passage rollings;
4) press quenching
Finish to gauge finishes rear steel plate and is cooled to 150 ~ 250 ℃ with the cooling rate of >50 ℃/s, obtain martensite+residual austenite body tissue, after finally batching, slowly cool to room temperature, tensile strength >=the 1400MPa of final hot-rolled super-strength Q & P steel plate, unit elongation >10%.
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Cited By (12)

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CN104561790A (en) * 2015-01-23 2015-04-29 宝钢特钢有限公司 1500MPa-grade high-strength steel and production method thereof
CN105018843A (en) * 2015-08-03 2015-11-04 北京科技大学 Q&P steel with vanadium and titanium added in compounded manner and manufacturing method of Q&P steel
CN105886750A (en) * 2016-04-18 2016-08-24 河北钢铁股份有限公司 Continuous hot galvanizing method for 1180 MPa-grade Q&P steel
CN107127212A (en) * 2017-04-20 2017-09-05 北京科技大学 The method of manganese cold-rolled steel sheet in super rapid heating technique productions high strength and ductility
CN108368589A (en) * 2015-12-15 2018-08-03 株式会社Posco High hardness wear-resisting steel and its manufacturing method with excellent toughness and cut resistant cracking behavior
WO2019057114A1 (en) 2017-09-20 2019-03-28 宝钢湛江钢铁有限公司 Softening method for high-strength q＆p steel hot roll
CN110088326A (en) * 2016-12-14 2019-08-02 蒂森克虏伯钢铁欧洲股份公司 Flat hot rolled bar product and its production method
CN111593264A (en) * 2020-06-28 2020-08-28 武汉钢铁有限公司 Tempering-free wear-resistant hot-rolled strip steel and production method thereof
CN111607735A (en) * 2020-06-28 2020-09-01 武汉钢铁有限公司 Hot-rolled wear-resistant steel with Brinell hardness of more than or equal to 420 and production method thereof
CN111607741A (en) * 2020-06-28 2020-09-01 武汉钢铁有限公司 Hot-rolled wear-resistant steel with Brinell hardness of more than or equal to 370 and production method thereof
CN112921243A (en) * 2021-01-28 2021-06-08 西南交通大学 Low-hardness high-wear-resistance steel and heat treatment preparation method thereof
US11203796B2 (en) 2015-12-23 2021-12-21 Posco Ultra high strength hot-rolled steel sheet having excellent ductility and method for manufacturing same

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Publication number Priority date Publication date Assignee Title
CN104561790A (en) * 2015-01-23 2015-04-29 宝钢特钢有限公司 1500MPa-grade high-strength steel and production method thereof
CN105018843A (en) * 2015-08-03 2015-11-04 北京科技大学 Q&P steel with vanadium and titanium added in compounded manner and manufacturing method of Q&P steel
CN108368589B (en) * 2015-12-15 2020-10-20 株式会社Posco High hardness wear resistant steel having excellent toughness and cut crack resistance and method for manufacturing the same
CN108368589A (en) * 2015-12-15 2018-08-03 株式会社Posco High hardness wear-resisting steel and its manufacturing method with excellent toughness and cut resistant cracking behavior
US11203796B2 (en) 2015-12-23 2021-12-21 Posco Ultra high strength hot-rolled steel sheet having excellent ductility and method for manufacturing same
CN105886750A (en) * 2016-04-18 2016-08-24 河北钢铁股份有限公司 Continuous hot galvanizing method for 1180 MPa-grade Q&P steel
CN110088326A (en) * 2016-12-14 2019-08-02 蒂森克虏伯钢铁欧洲股份公司 Flat hot rolled bar product and its production method
CN107127212A (en) * 2017-04-20 2017-09-05 北京科技大学 The method of manganese cold-rolled steel sheet in super rapid heating technique productions high strength and ductility
CN107127212B (en) * 2017-04-20 2019-05-03 北京科技大学 The method that super rapid heating technique produces manganese cold-rolled steel sheet in high strength and ductility
WO2019057114A1 (en) 2017-09-20 2019-03-28 宝钢湛江钢铁有限公司 Softening method for high-strength q＆p steel hot roll
CN111593264A (en) * 2020-06-28 2020-08-28 武汉钢铁有限公司 Tempering-free wear-resistant hot-rolled strip steel and production method thereof
CN111607741A (en) * 2020-06-28 2020-09-01 武汉钢铁有限公司 Hot-rolled wear-resistant steel with Brinell hardness of more than or equal to 370 and production method thereof
CN111593264B (en) * 2020-06-28 2021-07-13 武汉钢铁有限公司 Tempering-free wear-resistant hot-rolled strip steel and production method thereof
CN111607735B (en) * 2020-06-28 2021-10-01 武汉钢铁有限公司 Hot-rolled wear-resistant steel with Brinell hardness of more than or equal to 420 and production method thereof
CN111607735A (en) * 2020-06-28 2020-09-01 武汉钢铁有限公司 Hot-rolled wear-resistant steel with Brinell hardness of more than or equal to 420 and production method thereof
WO2022001886A1 (en) * 2020-06-28 2022-01-06 武汉钢铁有限公司 Tempering-free wear-resistant hot-rolled strip steel and production method thereof
CN112921243A (en) * 2021-01-28 2021-06-08 西南交通大学 Low-hardness high-wear-resistance steel and heat treatment preparation method thereof

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