CN103805869A - High-strength hot-rolled Q and P steel and manufacturing method thereof - Google Patents
High-strength hot-rolled Q and P steel and manufacturing method thereof Download PDFInfo
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Abstract
The invention discloses a high-strength hot-rolled Q and P steel and a manufacturing method thereof. The high-strength hot-rolled Q and P steel contains the chemical components in percentage by weight: 0.20-0.50% 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, 0.5-1.5% of Cr and the balance of Fe and unavoidable impurities. On the basis of the traditional C-Mn steel components, the content of Si is increased to inhibit the separation of a cementite, a trace of Ti is added to control the size of an austenite grain during heating, so that fine lath martensite is obtained during quenching; and a certain quantity of Cr element is added to improve the hardenability of a steel plate and delay the conversion from a residual austenite to a bainite at a distribution stage, so that the high-strength hot-rolled wear-resistant steel is manufactured at low cost, and the steel has the tensile strength of greater than 1500MPa and favorable elongation of greater than 10% and is excellent in strength and plasticity matching.
Description
Technical field
The invention belongs to wear resisting steel and manufacture field, particularly a kind of high-strength hot-rolled Q & P steel and manufacture method thereof, its tensile strength >1500MPa, unit elongation >10%.
Background technology
Quenching-partition steel is that Q & P steel is the study hotspot in last decade high-strength steel field.
At present, 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, and homogenizing was processed after for some time, was 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 in residual austenite, spread enrichment from oversaturated martensite a little more than stopping being incubated certain hour at cold temperature in quenching subsequently, thereby stable residual austenite, and then be quenched to room temperature.The relative content of martensite and residual austenite has determined the final performance of steel conventionally, and can be quenched and be stopped cold temperature and adjusted by control.Conventionally there is very high intensity and good plasticity by the steel after this art breading, there is very high strength and ductility product.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 and massive martensite.Q & P steel mechanical property is mainly determined by the carbon content in width of sheet, the martensite of lath martensite and film like residual austenite and residual austenite percent by volume.
The concept of Q & P steel is once proposition, 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, and wherein the most famous is the Speer seminar of Colorade USA mining industry university.
Comprehensive existing achievement in research is not difficult to find, the operational path of test is substantially all to adopt heat-treating methods or two-step approach, be steel 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.But 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 under line equipment condition at current domestic hot continuous rolling, producing Q & P steel according to two-step approach is almost impossible realize, the one-step technology route that can only adopt laminar flow Cooling Quenching to certain temperature then to batch.
Chinese patent CN102226248A has introduced a kind of carbon silicomanganese hot rolling Q & P steel, but in design of alloy, does not carry out micro-Ti processing and add Cr element, and the tensile strength of steel plate is starkly lower than 1400MPa.Chinese patent CN101775470A has introduced a kind of production technique of complex phase Q & P steel, is 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, but intensity is lower.
Summary of the invention
The object of this invention is to provide a kind of high-strength hot-rolled Q & P steel and manufacture method thereof, design by reasonable component, adopt hot continuous rolling process can produce the grade high-strength hot-rolled wear resisting steel of tensile strength >1500MPa, there is good unit elongation (>10%) simultaneously, show excellent strong plasticity coupling.
For achieving the above object, technical scheme of the present invention is:
The present invention is 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, add a certain amount of Cr element improve the hardening capacity of steel plate and postpone the transformation of allocated phase residual austenite to bainite, go out high-strength hot-rolled wear resisting steel thereby realize low cost fabrication.
Particularly, the high-strength hot-rolled Q & of one of the present invention P steel, its chemical component weight per-cent is: C 0.20% ~ 0.50%, 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%, Cr 0.5% ~ 1.5%, all the other are Fe and inevitable impurity.
In the Composition Design of steel of the present invention:
Carbon, 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 0.5%, 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 0.20-0.50% steel plate has good high strength and good plasticity coupling.
Silicon, 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%.
Manganese, 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%.
Phosphorus is the impurity element in steel.In steel, when the content of phosphorus higher (>=0.1%), form Fe2P and separate out crystal grain around, plasticity and the toughness of reduction steel, therefore its content is more low better, general control better and not improves steel-making cost in 0.015%.
When sulphur content is higher in steel, be present in around the crystal grain of steel with the eutectiferous form of FeS-Fe, reduce the mechanical property of steel, its content and seemingly Phosphorus, is also more low better, when actual production, is conventionally controlled in 0.005%;
Aluminium, 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, and aluminium 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%.
Titanium, 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%.
Chromium is the important element in the present invention.Chromium adds in steel the hardening capacity that improves on the one hand steel, and chromium can greatly reduce the spread coefficient of carbon in austenite on the other hand, can significantly postpone steel in quenching-distribution process residual austenite to the transformation of bainite.If the content of chromium, need not be not obvious to the transformation postponement of bainite to postponing residual austenite lower than 0.5%; If the content of chromium is higher than 1.5%, it is substantially saturated to the effect of bainite transformation that chromium is postponed residual austenite, therefore the content of chromium is controlled between 0.5-1.5% in steel;
Nitrogen, 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%.
Oxygen, 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 manufacture method of a kind of high-strength hot-rolled Q & P steel of the present invention, it comprises the steps:
1) smelt, cast
Adopt converter or electrosmelting by following compositions, chemical component weight per-cent is: C 0.20 ~ 0.50%, Si 0.8 ~ 2.0%, Mn 1.5 ~ 3.0%, P≤0.015%, S≤0.005%, Al0.02 ~ 0.08%, N≤0.006%, Ti 0.005 ~ 0.015%, Cr 0.5 ~ 1.5%, all the other are Fe and inevitable impurity; Through vacuum oven secondary refining, be cast as steel billet or steel ingot;
2) heating
Steel billet or Heating Steel Ingots temperature: 1100 ~ 1200 ℃, soaking time: 1 ~ 2 hour;
3) rolling
Start rolling temperature: 1000 ~ 1100 ℃, more than 950 ℃ multi-pass depress greatly and accumulative total deflection >=50%, subsequently intermediate blank treat temperature to 900 ~ 950 ℃, then carry out last 3 ~ 5 passage rollings;
4) cooling
Separate out and start on temperature, between 850 ~ 900 ℃, to be cooled to 100 ~ 300 ℃ with the cooling rate of >50 ℃/s at ferrite, obtain martensite+residual austenite body tissue, after finally batching, slowly cool to room temperature.
In manufacture method of the present invention:
Steel billet (ingot) Heating temperature: 1100 ~ 1200 ℃, soaking time: 1 ~ 2 hour, start rolling temperature: 1000 ~ 1100 ℃, multi-pass is depressed greatly and accumulative total deflection>=50% more than 950 ℃, and main purpose is refine austenite crystal grain; Subsequently intermediate blank treat temperature to 900-950 ℃, then carry out last 3-5 passage rolling; Separate out and start between 850-900 ℃, to be cooled to 100-300 ℃ of (M with the cooling rate of >50 ℃/s on temperature at ferrite
s-M
fbetween) a certain temperature to be to obtain martensite+a certain amount of residual austenite body tissue, after finally batching, slowly cools to room temperature.
Preferably, the Thickness Ratio of the thickness of intermediate blank and final steel plate generally, more than 3.0, can guarantee deformation uniformity.
If the Heating temperature of steel billet 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, the Heating temperature general control of steel billet 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 Si, and the diffusion of Mn etc. is abundant not, 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.
Beneficial effect of the present invention:
1. the 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 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.Although alloying elements cr add-on is more, Cr is compared with above-mentioned several alloying elements, and price is still very low.In addition, 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 is very low.
2. the mechanical property of steel plate of the present invention significantly improves, and customer using cost reduces, and the tensile strength of steel plate and unit elongation are significantly improved 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. the steel plate that adopts the present invention to produce has low cost superstrength and high rigidity advantage, be particularly suitable for improving the field of wear resistance, the residual austenite (more than 5%) particularly retaining in steel, under the conditions such as abrasive wear, can change martensite into, further improve the wear resistance of steel plate.
Accompanying drawing explanation
Fig. 1 is process flow sheet 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.
Fig. 4 is the metallographic microstructure photo of the embodiment of the present invention 6 steel plates.
Embodiment
Below in conjunction with 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 ~ 1100 ℃, more than 950 ℃ multi-pass depress greatly and accumulative total deflection >=50%, subsequently intermediate blank treat temperature to 900 ~ 950 ℃, then carry out last 3 ~ 5 passage rollings; Cooling, separate out and start on temperature, between 850 ~ 900 ℃, to be cooled to 100 ~ 300 ℃ with the cooling rate of >50 ℃/s at ferrite, obtain the above residual austenite of martensite+5% body tissue, after finally batching, slowly cool to room temperature.
Embodiment of the present invention composition is referring to table 1, and technique and performance are referring to table 2.
Table 1 unit: weight percent
Table 2
Fig. 2 and Fig. 3 have provided the typical metallograph of embodiment 2 and 4 test steel.Fig. 4 is the metallographic microstructure photo of the embodiment of the present invention 6 steel plates.
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 2,4,6 detecting residual austenite in steel plates is respectively 6.11%, 8.40% and 13.55%.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 (10)
1. a high-strength hot-rolled Q & P steel, its chemical component weight per-cent is: C 0.20 ~ 0.50%, 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%, Cr 0.5 ~ 1.5%, O≤30ppm, all the other are Fe and inevitable impurity; The microstructure of hot rolling Q & P steel is martensite+residual austenite body tissue, tensile strength >=1500MPa, unit elongation >10%.
2. high-strength hot-rolled Q & P steel as claimed in claim 1, is characterized in that, described Si content is 1.2 ~ 1.8%, weight percent meter.
3. high-strength hot-rolled Q & P steel as claimed in claim 1, is characterized in that, described Al content is 0.03 ~ 0.06%, weight percent meter.
4. high-strength hot-rolled Q & P steel as claimed in claim 1, is characterized in that described N content≤0.004%, weight percent meter.
5. high-strength hot-rolled Q & P steel as claimed in claim 1, is characterized in that, described Ti content is 0.008 ~ 0.012%, weight percent meter.
6. a manufacture method for high-strength hot-rolled Q & P steel, it comprises the steps:
1) smelt, cast
Adopt converter or electrosmelting by following compositions, chemical component weight per-cent is: C 0.20% ~ 0.50%, 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%, Cr 0.5% ~ 1.5%, all the other are Fe and inevitable impurity; Through vacuum oven secondary refining, be cast as steel billet or steel ingot;
2) heating
Steel billet or Heating Steel Ingots temperature: 1100 ~ 1200 ℃, soaking time: 1 ~ 2 hour;
3) rolling
Start rolling temperature: 1000 ~ 1100 ℃, more than 950 ℃ multi-pass depress greatly and accumulative total deflection >=50%, subsequently intermediate blank treat temperature to 900 ~ 950 ℃, then carry out finally at least 3 passage rollings; The Thickness Ratio of the thickness of intermediate blank and final steel plate is more than 3.0;
4) cooling
Separate out and start on temperature, between 850 ~ 900 ℃, to be cooled to 100 ~ 300 ℃ with the cooling rate of >50 ℃/s at ferrite, obtain martensite+residual austenite body tissue, after finally batching, slowly cool to room temperature; The hot rolling super intensified abrasion-proof steel plate tensile strength >=1500MPa obtaining, unit elongation >10%.
7. the manufacture method of high-strength hot-rolled Q & P steel as claimed in claim 6, is characterized in that, described Si content is 1.2 ~ 1.8%, weight percent meter.
8. the manufacture method of high-strength hot-rolled Q & P steel as claimed in claim 6, is characterized in that, described Al content is 0.03 ~ 0.06%, weight percent meter.
9. the manufacture method of high-strength hot-rolled Q & P steel as claimed in claim 6, is characterized in that, described N content≤0.004%, weight percent meter.
10. the manufacture method of high-strength hot-rolled Q & P steel as claimed in claim 6, is characterized in that, described Ti content is 0.008 ~ 0.012%, weight percent meter.
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