CN103882335A - Hot-rolled high-strength steel with yield strength of 800 MPa and production method thereof - Google Patents
Hot-rolled high-strength steel with yield strength of 800 MPa and production method thereof Download PDFInfo
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Abstract
The invention provides hot-rolled high-strength steel with yield strength of 800 MPa and a production method thereof. The steel plate comprises the following components by weight: 0.04%-0.07% of C, 0.20%-0.30% of Si, 1.65%-1.85% of Mn, 0-0.015% of P, 0-0.003% of S, 0.25%-0.35% of Ni, 0.20%-0.30% of Cr, 0.20%-0.30% of Cu, 0.20%-0.30% of Mo, 0.05%-0.07% of Nb, 0.010%-0.020% of Ti, 0.03%-0.06% of Als, and the balance of Fe and inevitable impurities. The production method comprises: reheating a casting blank at a temperature of 1200-1250 DEG C, performing rough rolling with a finishing temperature of 1010-980 DEG C; when the rough rolling is finished and the temperature returns to 930 DEG C-950 DEG C, performing finish rolling with a finishing temperature of 830-805 DEG C; cooling after rolling, wherein the cooling is divided into two phases: 1) in the first phase, performing quenching cooling to 300-150 DEG C with a cooling speed of more than 20 DEG C/s; 2) in the second phase, performing slow cooling to room temperature with a cooling speed of less than 30 DEG C/h. The high-strength steel has high yield strength, plasticity, toughness and good weldability; off-line heat treatment after rolling is canceled, which reduces the production cost.
Description
Technical field
The invention belongs to metal material field, to relate in particular to a kind of yield strength be 800MPa level and have excellent toughness and the hot-rolled high-strength steel of welding property and production method thereof.
Background technology
Along with the development of world economy, the pressure of resource, environment and the energy strengthens day by day, environmental protection and the energy-conservation attention that is more and more subject to steel industry.Exploitation has the high-strength steel of energy-conservation, efficient, longevity and excellent performance, and the needs that meet the crucial industry developments of the national economy such as oil, coal, chemical industry, electric power, traffic are also the important channels that Iron And Steel Industry realizes Sustainable development.
The current high-strength steel for industries such as shipbuilding, pressurized vessel, offshore platform, oil and natural gas line of pipes, transportation by railroad and engineering machinery, not only need to there is higher tensile strength and yield strength, and need good toughness and welding property, also wish in addition to obtain this type of high-strength steel under lower manufacturing cost condition.A lot of steel research personnel have carried out the development of a large amount of high-strength steels in the world at present, the main thought of these work is by suitable alloy designs and rolling technology (and rolling postheat treatment), obtain desirable tissue morphology and Organization Matching, to reach the good over-all properties of high-strength steel.
Publication number is the disclosed patent of CN 101928873 A " working method of a kind of high strength and ultrahigh-strength steel plates ", adopt the alloy designs of C-Mn-Cr-Ni-Nb-B, after hot rolling, carry out by induction heating method the high tensile steel plate that the method production yield strength of preheating, quenching and tempering is 710～1550MPa.Publication number is the CN disclosed patent of 1390972 A " ultrahigh-strength low-alloy steel ", adopt the alloy designs of C-Mn-Cr-Mo-V, after hot rolling, process by modifier treatment (quenching+high tempering) high tensile steel plate that production yield strength is 797～1260MPa.
Although above-mentioned patent can production yield strength be 800MPa grade steel plate, be all the method for having utilized hot rolling+off-line thermal treatment (modified, tempering etc.), therefore production cost is higher.In order to reduce production costs, publication number is the disclosed patent of CN 101932745 A " high tensile steel plate and manufacture method thereof ", by hot rolling with roll rear self-tempering processing and obtain the automobile high-strength steel that yield strength is 817MPa, but it has adopted higher carbon content (0.33%), higher silicone content (1.52%) and higher manganese content (2.3%), its unit elongation is 7.5%, and strength and ductility product (TS × EL) is 11408MPa.%.The carbon equivalent higher (Ceq=0.713) of this steel, welding property is poor.This patent does not provide low-temperature flexibility in addition, but its higher carbon content and silicone content show that its low-temperature flexibility is also poor.
Publication number is the disclosed patent of CN 101041879A " hot-rolled super-strength martensitic steel and manufacture method thereof ", a kind of method that hot rolling production yield strength is 860MPa hot-rolled coil of utilizing is provided, but this high-strength steel adopts very low temperature to batch to produce by powerful reeling machine after hot rolling, and can only produce the hot-rolled coil that thickness is 1-4mm.
Can find out, in original technology, utilize hot rolling and roll rear off-line heat-treating methods and produce 800MPa high-strength steel, production cost is higher; The 800MPa grade steel plate that adopts the alloy designs of higher carbon, high silicon and Gao Meng to obtain, toughness and welding property are poor; And utilize the method that very low temperature batches to produce or thin size hot-rolled roll bending, need high-power reeling machine and can only produce thin specification roll bending.Therefore need a kind of method of utilizing hot-rolling method to produce the 800MPa grade high-strength steel plate with excellent toughness and welding property.
Summary of the invention
The object of the invention is to overcome the problems referred to above and deficiency and a kind of yield strength is provided is 800MPa level hot-rolled high-strength steel and production method thereof, this high-strength steel not only has higher yield strength, and has higher plasticity, toughness and good welding property; Employing is rolled and is chilled to soon 250～150 ℃ and slowly cool to the technique of room temperature afterwards, has cancelled and has rolled rear off-line thermal treatment, has reduced production cost.
The present invention is achieved in that the composition of this yield strength of 800 MPa grade hot-rolled high-strength steel plate is as follows by weight percentage: C:0.04%～0.07%, Si:0.20%～0.30%, Mn:1.65%～1.85%, P:0～0.015%, S:0～0.003%, Ni:0.25% ~ 0.35%, Cr:0.20%～0.30%, Cu:0.20%～0.30%, Mo:0.20%～0.30%, Nb:0.05%～0.07%, Ti:0.010%～0.020%, all the other are Fe and inevitable impurity for Als:0.03%～0.06%.
The alloy designs that the present invention adopts low C and low Si and adds Ni, Cr, Mo, Cu, Nb, Ti, has reduced the carbon equivalent of steel significantly, is not only conducive to low-temperature flexibility, and guarantees that steel plate has good welding property and low-temperature flexibility.
Composition Design of the present invention be the reasons are as follows:
C: form interstitial solid solution in steel, play solution strengthening effect, can improve significantly the intensity of steel and with low cost.But carbon content is too high, unfavorable to low-temperature flexibility and welding property.In the present invention, carbon content is 0.04%～0.07%.
Si: be deoxidant element in the time of steel-making, play solution strengthening effect in steel, can improve significantly the intensity of steel, but add unit elongation, toughness and the welding property that too much can damage steel, silicone content of the present invention is 0.20%～0.30%.
Mn: improve the hardening capacity of steel, reduce the transition temperature of steel, there is solution strengthening effect simultaneously.But when manganese content is too much, can produce segregation in strand heart portion on the one hand, affect the homogeneity of organizing after hot rolling, unfavorable to low-temperature flexibility, can make on the other hand martensite transformation temperature decline, cause there is certain residual austenite in room temperature texture, affect the intensity of steel.When manganese content is higher in steel, can increase the weight of the segregation of strand heart portion and loose.Manganese content in the present invention is 1.65%～1.85%.
P: as the harmful element in steel, unit elongation, low-temperature impact toughness and welding property to steel all have infringement, and its content should be controlled at lower level as far as possible.Therefore in the present invention, the content of P is≤0.015%.
S: as the harmful element in steel, the low-temperature flexibility of steel is had to very large infringement.Sulphur forms manganese sulfide inclusion with manganese in steel, not only affects toughness, unit elongation, Z-direction performance, the welding property of steel, but also can affect anti-hydrogen induced cracking (HIC) performance of petroleum natural gas pipeline steel.Its content should be controlled at lower level as far as possible.Therefore in the present invention, the content of S is≤0.003%.
Cr: increase the hardening capacity of steel, improve the intensity of steel, Cr too high levels, easily forms the multiple carbide containing Cr in steel, although the intensity of steel and hardness improve, but makes the toughness of steel decline.Therefore in the present invention, the content of Cr is 0.20%～0.30%.
Ni: improve hardening capacity and reduce Cold Brittleness Transition Temperature.But Ni too high levels, not only makes cost of alloy increase, and can reduce martensite transformation temperature, increase the ratio of twin crystal martensite and be unfavorable for the toughness of steel.Therefore in the present invention, the content of Ni is 0.25% ~ 0.35%.
Cu: be the anti-corrosion element of one in steel, and can play solution strengthening effect in steel.But hot-short for preventing that it from causing in steel, its content should be too not high, and add certain nickel.In the present invention, the content of Cu is 0.20%～0.30%.
Mo: postpone proeutectoid ferrite and change in steel, increase the hardening capacity of steel, crystal grain thinning, intensity and the toughness of raising steel.In the present invention, the content of Mo is 0.20%～0.30%.
Nb: Nb(solid solution Nb or strain inducing in steel are separated out Nb) can suppress significantly austenitic recrystallize, improve austenitic recrystallization temperature, hot rolling is rolled, by the microstructure of controlled rolling refinement steel in recrystallization temperature interval and two temperature sections of non-recrystallization temperature range.In the present invention, changing Nb content into is 0.05%～0.07%.
Ti: form carbide, nitride or carbonitride with C, N in steel, suppress growing up of austenite crystal in the time reheating and weld preheating, crystal grain thinning, significantly improves armor plate strength, toughness and welding property.Because the avidity of titanium and nitrogen in steel is stronger, in steel, easily form titanium nitride, therefore titanium also has the effect of fixed nitrogen, eliminates the free nitrogen in steel.But higher titanium content can form thick titanium nitride granular in steel, affects intensity and the toughness of steel.Therefore in the present invention, the content of Ti is 0.010%～0.020%.
Yield strength of 800 MPa grade hot-rolled high-strength steel production method of the present invention comprises the following steps: smelting → continuous casting → reheating → roughing → treat temperature → finish rolling → cooling.It is characterized in that:
It is 1200～1250 ℃ that strand reheats temperature, promotes the abundant dissolving of the carbide of Nb, V in steel, and the partly soluble Ti carbide that contains can effectively suppress growing up of austenite crystal.Temperature range at austenite recrystallization is carried out roughing, and roughing finishing temperature is 1010～980 ℃, austenite crystal by recrystallize by passage refinement; After roughing finishes, treat temperature to 930～950 ℃ of temperature ranges, carry out finish rolling, the finishing temperature of finish rolling is 830～805 ℃, temperature range at austenitic non-recrystallization temperature～Ar3 is carried out finish rolling, though there is not recrystallize in austenite, but its shape becomes pie, there is a large amount of deformation bands in its inside, has promoted structure refinement after phase transformation; Roll that rear cooling to be divided into two stages cooling: 1) first stage, to be greater than cooling rate quench cooled to 300～150 ℃ of 20 ℃/s, obtains the tiny martensite lath that width is about 80～240nm; 2) subordinate phase slowly cools to room temperature with the cooling rate of 30 ℃/h of <, when martensite is produced, the martensite after phase transformation is carried out to self-tempering.
Basic ideas of the present invention: the alloy designs that adopts low C and low Si and add Ni, Cr, Mo, Cu, Nb, Ti, adopt austenite recrystallization and non-recrystallization two stage rolling, be quickly cooled to the following also technique of the room temperature of slow cooling of Ms point after rolling, to produce yield strength be 800MPa level and have good low-temperature toughness and the high-strength steel of welding property.
The beneficial effect of technical solution of the present invention is: adopt thermo-mechanical rolling+direct quenching+self-tempering technology, do not need off-line to quench and or tempering, simplified production technique, reduced the production cost of steel; Adopt low C design and TMCP technique, there is good low-temperature flexibility; Carbon equivalent is reduced to below 0.51, and welding property improves.From implementation result, high tensile steel plate yield strength of the present invention is 800～875MPa, and tensile strength is 960～1060MPa, and unit elongation is that 19～22% ,-20 ℃ of ballistic works are 60～90J.
Accompanying drawing explanation
Fig. 1 is the microstructure of the embodiment of the present invention 1 steel plate.
Fig. 2 is the microstructure of the embodiment of the present invention 2 steel plates.
Fig. 3 is the microstructure of the embodiment of the present invention 3 steel plates.
Fig. 4 is the microstructure of the embodiment of the present invention 4 steel plates.
Fig. 5 is the microstructure of the embodiment of the present invention 5 steel plates.
Fig. 6 is the microstructure of the embodiment of the present invention 6 steel plates.
Embodiment
Below by embodiment, the present invention is further illustrated.
The embodiment of the present invention, according to the component proportion of technical scheme, is smelted and rolling.The chemical composition of embodiment of the present invention steel is in table 1.The main technologic parameters of embodiment of the present invention steel is in table 2.The mechanical property of embodiment of the present invention steel is in table 3.
The chemical composition (%) of table 1 embodiment
The main technologic parameters of table 2 embodiment steel
The mechanical property of table 3 embodiment steel
Claims (2)
1. a yield strength of 800 MPa grade hot-rolled high-strength steel plate, it is characterized in that, the composition of this steel plate is as follows by weight percentage: C:0.04%～0.07%, Si:0.20%～0.30%, Mn:1.65%～1.85%, P:0～0.015%, S:0～0.003%, Ni:0.25% ~ 0.35%, Cr:0.20%～0.30%, Cu:0.20%～0.30%, Mo:0.20%～0.30%, Nb:0.05%～0.07%, Ti:0.010%～0.020%, all the other are Fe and inevitable impurity for Als:0.03%～0.06%.
2. a yield strength of 800 MPa grade hot-rolled high-strength steel production method of the present invention claimed in claim 1, comprise smelting, continuous casting, reheat, roughing, treat temperature, finish rolling, cooling, it is characterized in that: it is 1200～1250 ℃ that strand reheats temperature, the finishing temperature of roughing is 1010～980 ℃; After roughing finishes, treat that temperature carries out finish rolling to 930 ℃～950 ℃, the finishing temperature of finish rolling is 830～805 ℃; Roll rear cooling two stages that are divided into: 1) first stage is to be greater than cooling rate quench cooled to 300～150 ℃ of 20 ℃/s; 2) subordinate phase slowly cools to room temperature with the cooling rate of 30 ℃/h of <.
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Cited By (4)
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| CN106191408A (en) * | 2016-08-12 | 2016-12-07 | 武汉钢铁股份有限公司 | A kind of yield strength 530MPa level Thin Specs Hot Rolling Automobile chassis beam steel and production method |
| CN114752850A (en) * | 2021-01-12 | 2022-07-15 | 宝山钢铁股份有限公司 | High-strength steel plate with yield strength of 785MPa and manufacturing method thereof |
| CN115537675A (en) * | 2022-09-15 | 2022-12-30 | 武汉钢铁有限公司 | 800 MPa-grade surface treatment-free steel for commercial vehicles and production method thereof |
| CN116770198A (en) * | 2023-08-25 | 2023-09-19 | 张家港宏昌钢板有限公司 | Steel plate for low-compression-ratio hydropower and preparation method thereof |
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| CN116770198A (en) * | 2023-08-25 | 2023-09-19 | 张家港宏昌钢板有限公司 | Steel plate for low-compression-ratio hydropower and preparation method thereof |
| CN116770198B (en) * | 2023-08-25 | 2023-11-03 | 张家港宏昌钢板有限公司 | Steel plate for low-compression-ratio hydropower and preparation method thereof |
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