CN101008066B - Hot rolling martensite steel plate with tensile strength higher than 1000Mpa and its production method - Google Patents
Hot rolling martensite steel plate with tensile strength higher than 1000Mpa and its production method Download PDFInfo
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Abstract
The invention relates to a hot- roled martensite steel with strength for extension higher than 1000 Mpa, the component (with percent by weight) comprises: C 0.08-0.20, Si<=0.8, Mn 0.5-2.0, Al 0.010-0.060, N<=0.008, P<= 0.020, S<=0.005, one or more than one of Ti 0.01-0.03, V<=0.10 and Nb 0.01-0.05; Ca 0.001%-0.005%, added when sulfur content >=0.003; left is Fe and inavoidable foreigh matter. Themain process parameters are as follows: cooling said steel with speed not less than 20 degree/ s to cooling temeprature between 150 Deg. C to Ms, stopping cooling and batching to make metallic band; or cooling with speed not less than 20 degree/ s to 650- 750 Deg. C, setting for 2- 10 seconds, and cooling with speed not less than 50 degree/ s to cooling stop temperature of 150 Deg. C- Ms, and batching to make metallic band.
Description
Technical field
The present invention relates to the manufacture method of ferrous materials, particularly hot-rolled super-strength martensitic steel plate and manufacture method thereof.
Background technology
Automobile steel has a large amount in variety.Traditional low strength steel (LSS) and high-strength steel (HSS) mainly contain the part low strength rank kind of gapless atomic steel (IF), high strength gapless atomic steel (IF-HS), general carbon soft steel (MILD), isotropy steel (IS), baking hardened steel (BH), carbon manganese steel (C-Mn) and Hi-Stren steel (HSLA), dual phase steel (DP), phase change induction plasticity steel three kinds such as (TRIP).Development along with automobile industry, requirement to vehicle safety is more and more higher, and light weight also requires more and more gentlier to improve fuel economy, requirement to the intensity aspect of vehicles steel plate improves constantly, also more and more, thin more to the performance requriements division of labor of different sites steel plate simultaneously, so advanced high-strength steel (AHSS) or ultrahigh-strength steel (Ultra-HSS) arise at the historic moment.Usually tensile strength for ultrahigh-strength steel, mainly contains following five big classes: Hi-Stren steel (HSLA), dual phase steel (DP), phase change induction plasticity steel (TRIP), complex phase steel (CP), martensitic steel (MP) greater than the steel grade rule of 700MPa.According to the different qualities of these a few class steel plates, they are widely used in the different sites of automobile.
The manufacture method of relevant hot-rolled high-strength steel plate has formed multinomial patent in the world, mainly concentrates on Hi-Stren steel (HSLA), dual phase steel (DP) and phase change induction plasticity steel (TRIP).But, automobile hot-rolled super-strength steel plate (thickness of slab 1.5mm～6mm) seek unity of standard as yet with martensitic stucture, especially yield strength is higher than 750MPa, and tensile strength is not appeared in the newspapers as yet greater than the technology of the hot-rolled super-strength martensitic steel plate this respect of 1000MPa.
Have following for finding the close patent relevant at present with high-strength steel:
U.S.'s " hot-rolled high-strength structure iron " patent US 5704998 (open day: 1998.01.06), " hot rolling high-tensile-strength steel " US 95532534 (open day: 1995.09.22) belong to hot-rolled high-strength structural steel and iron, yield strength 630MPa tensile strength 840MPa.
(contriver: tool is grown flourish, N-RV and is added Shandong, the fertile root of GA at the Chinese patent ZL98812446.7 of " ultra-high strength Ausaged steels with excellent low-temperature flexibility " of Exxon Mobil; Open day: 2001.01.31), it need be in the district's controlled rolling of austenite non-recrystallization, the hot rolling postcooling is to Ms～Ms+100 ℃, do not adopt tempering, the tensile strength grade is 830MPa, and its normal temperature is organized as the micro-lamellar structure based on the lath of fine-grained martensitic and close grain lower bainite of 2-10% austenite film layer and about 90-98%.
Exxon Mobil and Sumitomo Metal Industries unite " high-tensile-strength steel and the production method thereof " of application Chinese patent 98802878.6 (contriver: tool grows that honor, N-RV spot loud, high-pitched sound Shandong, MJ Luton, CW Peter are gloomy, rattan former know, Gang Kouxiu controls, shore Tian Changyan; Open day: 2000.03.29), composition C:0.02～0.10% of steel plate, Mn:0.2～2.5%, the tensile strength grade is 900MPa.
Japan " high strength has excellent welding performance hot-strip and line bar " patent JP 10053814A is hot-rolled high-strength steel plate and wire rod, good welding performance. bainite+perlite accounts for 10～95%, other also has ferrite, martensite and paralympic, yield strength of 800 MPa; Composition: 0.05～0.22%C, 0.5～2.0%Si, 0.5～2.0%Mn; Can be descended one or more elements :≤1.5%Cr ,≤1.0%Mo ,≤0.5%Ti ,≤0.5%V ,≤0.01%B ,≤0.1%Nb.
Japan's " have excellence is drawn, flange processability Automobile Frame Parts hot-rolled high-strength steel plate " patent JP 4176822A belongs to hot-rolled high-strength steel, is used for automotive frame, draws and the flange good processability; Be organized as 〉=97% ferrite and≤2% perlite or martensite; 1000 ℃～1150 ℃ of Heating temperatures, finishing temperature is not less than Ar3,500 ℃～700 ℃ of coiling temperatures, tensile strength 〉=450MPa; Chemical ingredients: C≤0.01%, Si≤0.01%, Mn 0.1～1%, and Cu 0.5～2%.
Japan " hot-rolled high-strength steel plate production " patent JP 2038525A is a hot-rolled dual-phase steel, and the rolling processing performance is good, pickling and heat-treats; The final rolling temperature of the wide middle part of plate 〉=800 ℃, than temperature height 〉=40 of limit portion ℃, being cooled to 400 ℃～650 ℃ (the wide centres of plate) with the cooling rate of 〉=30 ℃/s batches, after the pickling, carrying out continuous annealing handles, be heated to Acl to 900 ℃, be incubated 1 to 5 minute, with the cooling rate of≤50 ℃/s be cooled to 〉=400 ℃.Be organized as the martensite of ferrite and 〉=30%, transition temperature is lower, and tensile strength can reach more than the 700MPa; C:0.10～0.25%, Si :≤2.0%, Mn:1.0～3.0%, Als:0.01～0.10%, 0.015～0.10%Nb or Ti (as needs).
Japan " the plastic hot-rolled steel sheet of high-tensile " patent JP 2003321738A is a hot-rolling phase change induction plasticity steel, is used for trolley part.Be organized as ferrite, bainite, paralympic (three-phase), or four phases (containing martensite).C：0.1～0.2％，Si：0.5～2.0％，Mn：0.5～1.7％，Al：≤0.06％，N：≤0.006％，Mo：0.1～0.5％，Ti：0.05～0.2％。
Among the patent of Sumitomo Metal Industries " production of tempering high tensile steel plate " JP 60121219 (announcing time 1985.06.28) and the JP 89025371 (announcing time 1989.05.17), adopt tempering process to produce high-strength steel, and Si in the steel :≤0.015%, Ni:1.00%～3.50%, Cr:0.40%～1.20%.
" comprising heat again; twice compression; Q-tempering; tissue comprises the thin brilliant lath martensite tissue of tempering; the Hi-Stren steel production that the low temperature of low-carbon bainite and tempering FGB uses " patent WO 200039352 of Exxonmobil Upstream Res company application (announces time 2000.07.06, inventor: AYER R, BANGARU N V, KOO J) is a kind of Cryogenic Steel, with the good high-strength steel of method production low-temperature flexibility than low carbon content (0.03%～0.12%) and high nickel content (being not less than 1.0%), its adopt lower rate of cooling (10 ℃/s), its tensile strength can only reach more than the 830MPa.
" thin brilliant lower bainite and lath martensite are organized low-cost low-alloy super-strength steel plate " patent WO 9905335 of Exxonmobil Upstream Res and Nippon Steel's cooperation application (inventor: ASAHI H, BANGARU N V, HARA T, KOO J, LUTON M J, PETERSENC W, TAMEHIRO H, TERADA Y, announcement time 1999.02.04) in, though adopt the not tempering of only quenching after hot rolling, C:0.05 in its composition～0.10% is lower.
European patent " has high strength and excellent moldability hot-rolled steel sheet ", and EP 295500A1 belongs to the hot-rolled high-strength thin plate, and plasticity is good, is organized as ferrite, bainite and paralympic; Composition C:0.15～0.40%, Si:0.5～2.0%, Mn:0.5～2.0%.
European patent " has good formability and sticking power high tensile steel plate and manufacture method thereof ", and EP1170391 is a hot-rolling phase change induction plasticity steel, be organized as ferrite, bainite and paralympic, composition C:0.07～0.40%, Si:0.3～2.0%, Mn:0.2～2.5%, tensile strength 〉=580MPa, unit elongation 〉=30%.
By above contrast patent as can be known, there are following one or more deficiencies in these patents: 1. added the expensive alloy element of certain content, as Cu, Ni, Cr, Mo etc., steel product cost height.As adding 1.00～3.50%Ni, 0.40～1.20%Cr among JP60121219 and the JP 89025371; Nickel content is not less than 1.0% among the WO200039352; Copper content is 0.5～2% among the Japanese Patent JP 4176822A; 2. complex process, the process cost height.Carbon content is≤0.01% among the Japanese Patent JP 4176822A, belong to ultra low-carbon steel, crossing low carbon content causes when steel-making decarburization time long, steel melting furnace labour productivity is low, and the carbon in the iron alloy material that adds in the steelmaking process is also corresponding low, and the iron alloy material cost of low-carbon (LC) is also higher, will also increase smelting cost with special ladle and anti-material when smelting low carbon, ultra low-carbon steel in addition; Patent JP 60121219, JP 89025371 have all adopted tempering process, have increased by a procedure, have improved process cost.3. the armor plate strength rank is low.As patent WO 200039352 and patent 98812446.7, tensile strength can only reach the rank of 830MPa; U.S. Pat 5704998, US 95532534 belong to hot-rolled high-strength structural steel and iron, yield strength 630MPa, tensile strength 840MPa; Japanese Patent JP 4176822A belongs to hot-rolled high-strength steel, tensile strength 〉=450MPa; EP1170391 is a hot-rolling phase change induction plasticity steel, tensile strength 〉=580MPa.
Because the development of automobile industry, requirement to vehicle safety is more and more higher, and light weight also requires more and more gentlier to improve fuel economy, so the requirement to some parts of vehicle such as the stiffener and the intensity of the used steel plate of security personnel's part improves constantly, do not need very high unit elongation at some specific use positions, a kind of like this automobile based on martensitic stucture arises at the historic moment with the hot-rolled super-strength steel.Simultaneously, from utilizing resource most effectively, ultrahigh-strength steel newly developed requires to have the least possible alloying element.
Summary of the invention
The purpose of this invention is to provide have certain plasticity and plasticity with martensitic stucture (martensite＞90%, all the other are bainite) be main hot-rolled super-strength steel plate (composition design and the manufacture method of thickness of slab 1.5mm～6.0mm), design of alloy and the special follow-up process for cooling control of strict control by reasonable cheapness, the direct cooling (DQ) fast in back is rolled in employing or two kinds of technologies of segmentation cooling reach more than or equal to 1000MPa the tensile strength of thickness of slab 1.5mm～6.0mm hot-rolled steel sheet, yield strength is more than or equal to 750MPa, unit elongation A
80(JIS13A gauge length 80mm sample) is more than or equal to 7%.And have good cold-bending property, be stiffener and safety member that steel plate of the present invention can be used for automobile.
For achieving the above object, the invention provides the hot rolling martensite steel plate that a kind of tensile strength is higher than 1000Mpa, its composition is (weight percent):
C 0.08～0.20；
Si ≤0.8；
Mn 0.5～2.0；
Al 0.010～0.060；
N ≤0.008；
P ≤0.020；
S ≤0.005；
More than among Ti 0.01～0.03, V≤0.10 and the Nb 0.01～0.05 one or more;
Ca:0.001～0.005, some adding in sulphur content 〉=0.003;
All the other are iron and unavoidable impurities.
Below be the effect and the qualification explanation thereof of patent principal element of the present invention:
Carbon: the height of carbon content has determined the intensity rank of steel plate largely, becomes the requisite element of strengthening phase in the steel such as martensite, bainite because carbon is austenitic transformation.Carbon is the topmost element of decision carbon equivalent size, and carbon equivalent is the important indicator that influences the intensity of steel and weldability etc.The span of control of carbon of the present invention is 0.08%～0.20%, be based on the coupling of the obdurability of steel, carbon is lower than does not have enough carbide and solid solution carbon in 0.08% steel, thereby is can not produce enough distortion in the martensite process to strengthen the intensity that martensitic stucture obtains steel plate at austenitic transformation; Otherwise carbon content is higher than at 0.20% o'clock, and then the plasticity of steel and toughness reduce, and weldability is variation also.
Silicon: silicon plays the solution strengthening effect in steel, and content can suppress separating out of carbide more for a long time, promotes ferrite to form, thereby carbon is diffused in the residual austenite.Silicon or analogous element serve as the ferrite function of stabilizer, not only quicken the formation of proeutectoid ferrite, and hinder separating out of cementite during bainite forms, quicken carbon be diffused into austenite mutually in.Silicon helps to increase the stability of residual austenite, and concerning martensitic stucture was the hot-rolled super-strength steel plate of leading, silicon mainly act as solution strengthening.The interpolation of silicon also cooperates the segmentation process for cooling can promote ferrite to separate out, and helps reducing the yield strength of steel and reduces the yield tensile ratio that contains niobium controlled rolling steel.Add silicon in the steel and can improve purity of steel and deoxidation.But too high silicon can make troubles to hot rolling heating and subsequent product coating, influences the surface quality of steel plate.So the control silicone content is not more than 0.8% among the present invention.
Manganese: manganese plays the solution strengthening effect in steel, can improve the intensity of the back steel plate that quenches.Manganese is the element of stable austenite, can reduce austenitic transformation temperature, promote the dissolving of carbon in austenite, manganese has also increased the possibility of carbon enrichment, thereby owing to has postponed the range of application that pearlitic formation has enlarged the rate of cooling that is quenched to martensitic stucture.Too high manganese contents level must be avoided, because manganese reduces the activity of carbon in the austenite, has promoted the formation of carbide like this, must pay attention to the inhibition of ferrite transformation, because it can drop to the enrichment of carbon in process of cooling minimum.Too high manganese also is easy to segregation, worsens the performance of steel.About silicon and manganese, must adjust distribution and the volume fraction of the relative quantity of interpolation with the control phase.
Nitrogen: in adding the steel of titanium, an amount of nitrogen and titanium form titanium nitride, thisly easily second help strengthening matrix mutually, the undissolved particle energy of part refinement original austenite grains when slab heat what high temperature was separated out, as a same reason, when welding, can improve steel plate the welding property of steel plate.If but nitrogen is too high, as be higher than 0.010%, can in steel, form thick titanium nitride, perhaps too much solid solution nitrogen, this will seriously damage the plasticity and the toughness of steel.
Titanium: titanium can form the compound of titanium with nitrogen, carbon and sulphur.The content of titanium in the control steel makes that titanium is main to form the titanium nitride of small and dispersed, remaining titanium and sulphur, carbon formation compound with nitrification.Therefore, the fixing nitrogen in the steel and form tiny titanium nitride particles of an amount of titanium.Be unfavorable for obtaining good obdurability coupling but titanium content is too high.Titanium content is crossed low less than 0.005% effect that does not have crystal grain thinning.Therefore an amount of titanium (0.005%～0.03%) is crystal grain thinning and improve the weldability of steel plate significantly significantly.Ti/N is generally 3.42, also will see the sulphur content in the steel simultaneously, and this steel grade wishes that sulphur is few more good more.
Sulphur and phosphorus: sulphur forms the plastic occluded foreignsubstance manganese sulfide with chemical combination such as manganese in steel, especially unfavorable to the horizontal plastic property and the toughness of steel, so the content of sulphur should be low as much as possible.Phosphorus also is the harmful element in the steel, the plasticity of grievous injury steel plate and toughness.More than or equal to 0.003% o'clock, be the detrimentally affect of the inclusion of avoiding the MnS class as sulphur content, need when smelting, to adopt Ca treatment process, the span of control of Ca: 0.0010～0.0050% lateral performance.
Niobium and vanadium: niobium and vanadium are strong carbon and nitrogen compound forming element.Because add an amount of titanium in the steel, the formation temperature of titanium and nitrogen is higher,, make the main carburet of niobium and vanadium therefore by controlling the content of titanium, nitrogen.Vanadium carbide and niobium carbide to separate out temperature low than titanium nitride and titanium carbide, when hot rolling and the hot rolling technology coupling, separating out thinning microstructure and improving intensity and toughness by control niobium carbide and vanadium carbide.The niobium of solid solution condition has postponed static state and dynamic recrystallization in the thermal deformation process, improves non-recrystallization temperature, helps the austenitic phase-change product of refinement deformation.
Aluminium: it is 0.010～0.060% that steel of the present invention adds aluminium content.Aluminium is the main deoxidant element in the steel, helps crystal grain thinning, all contains a certain amount of in the general steel.The aluminium that adds among the present invention is mainly used to deoxidation and crystal grain thinning.
The present invention has composition economy, do not contain such as valuable alloying elements such as Cr, Ni, Mo, hot rolling technology is simple, characteristics such as the intensity height of steel plate, adopt the more moderate carbon content (0.08% to 0.20%) of other patent relatively, this carbon content neither very low neither be very high, can satisfy the requirement of steel making working procedure, can guarantee that also steel plate is follow-up to the welding performance demands. wherein the niobium that adds in carbon content and the steel plate guarantees as far as possible by solubility product formula Lg[Nb] T of [C]=2.96-7510/T calculating is less than 1473K (1200 ℃); If add V, the T that also will guarantee to calculate by similar formula is less than 1473K, and this is that all carbonitrides dissolve fully in the time of will guaranteeing the steel billet reheat, so that the effect of each element is given full play in precipitation strength in follow-up rolling and process of cooling; Heating temperature can not be too high when will guarantee to contain in the steel higher element silicon simultaneously, otherwise the scale on surface of steel is too sticking, is difficult for removing, and influences surface quality. the element titanium of adding and nitrogen content guarantee Ti/N 〉=3.42 as far as possible, allow titanium be completely fixed nitrogen, make niobium can form enough NbC and strengthen; Sulphur content in the steel is low as far as possible, meeting the demands with the horizontal cold-bending property that guarantees steel plate. the C in the steel, Si, Mn content can not be simultaneously near the upper limit or lower limits, the purpose of doing like this is proof strength and carbon equivalent. to the suitable control of the above element, purpose is with lower cost of alloy, accurate composition proportion, simple steel-making, rolling and process for cooling obtain over-all propertieies such as mechanics, clod wash, welding preferably.
The technological process of production of hot rolling martensite steel plate of the present invention is as follows:
Steel-making → continuous casting (perhaps die casting cogging) → heating → hot rolling (roughing, finish rolling) → control is cold → batches, and concrete steps are:
1) smelts, casts the formation steel billet;
2) steel billet is heated to 1150～1250 ℃, soaking time is pressed net thickness 1～1.5min/mm and is calculated;
3) in the temperature range of recrystallize can take place in austenite, adopt one or more passages, described billet rolling is become steel plate;
4) at austenite recrystallize not taking place promptly is lower than the Tnr temperature but is higher than Ar
3In the temperature range of transition point, adopt one or more passages, above-mentioned steel plate rolling is become the steel plate of final thickness, finishing temperature is between 750 ℃～900 ℃;
5) speed of cooling that is not less than about 20 ℃/s is quickly cooled to described steel plate between the cooling termination temperature of 150 ℃～Ms and coils into coil of strip;
6) can carry out tempering to improve performance and to eliminate stress to cooled coil of strip (steel plate), tempering temperature is 150 ℃～250 ℃.
Alternatively, in the step 5) of aforesaid method can also be: the medium temperature that is cooled to 650 ℃～750 ℃ with the cooling rate that is not less than 20 ℃/s earlier stops 2～10 seconds, was cooled to the cooling termination temperature of 150 ℃～Ms and coiled into coil of strip with the cooling rate that is not less than 50 ℃/s again;
Steel billet is heated to fully that high temperature (1150 ℃～1250 ℃) makes the austenite structure homogenizing, and the carbide of the niobium in the steel, vanadium and titanium etc. fully dissolves, and titanium nitride also have part not dissolved particles can stop growing up of original austenite grains.In the temperature range of recrystallize can take place in austenite, adopt the rolling steel billet of one or more passages, the draft of this temperature range is not less than 60%.Like this, the microalloy element of solid solution in steel plays a part retardance austenite dynamic recrystallization, and the austenite generation recrystallize of deformation also reaches the purpose of grain refining.
Be lower than austenite generation recrystallize but be higher than in the temperature range of Ar3 transition point, adopting one or more passages, above-mentioned steel plate rolling is become the steel plate of final thickness, the draft of this temperature range is not less than 60%.Finishing temperature is between 750 ℃～900 ℃.In this stage rolling process, recrystallize does not take place in austenite, and forms the extended austenite.Have a large amount of deformed belts in the extended austenite crystal, solid solution atoms such as niobium, vanadium and titanium are owing to deformation induced separating out is carbide and carbonitride.
After the finish to gauge of non-recrystallization district, the tissue of steel is made up of the austenite of distortion.Steel plate after the finish to gauge is quickly cooled to described steel plate between the cooling termination temperature of 150 ℃～Ms with the speed of cooling that is not less than about 20 ℃/s and coils into coil of strip; Perhaps be cooled to 650 ℃～750 ℃ temperature earlier and stopped 2～10 seconds, be cooled to the cooling termination temperature of 150 ℃～Ms and coil into coil of strip with the cooling rate that is not less than 50 ℃/s again with the cooling rate that is not less than 20 ℃/s; Can add 150 ℃～250 ℃ temper at last with the performance of improving steel and the stress of eliminating steel plate inside.
Beneficial effect of the present invention shows: composition design economical rationality helps resources effective utilization and recyclable, easy to implement and control, technology controlling and process is simple and easy to do, roll directly cooling or segmentation cooling fast of back owing to adopt, thereby the rolling cycle is short, the rolling efficiency height.The armor plate strength height has good clod wash and welding property.Through after above-mentioned described composition and the technological process, the tensile strength of thickness of slab 1.5mm～6mm hot-rolled steel sheet reaches 1000MPa～1100MPa, and yield strength is more than or equal to 750MPa, unit elongation A
80(JIS13A gauge length 80mm sample) more than or equal to 7%, to satisfying the indehiscent requirement of d=4t (flexual center diameter=4 * steel plate thickness), tissue is mainly martensite (greater than 90%) in length and breadth in clod wash.
Description of drawings
Fig. 1 is TMCP (heating and controlled rolling and controlled cooling) synoptic diagram, is suitable for the segmentation cooling;
Fig. 2 is the TMCP synoptic diagram, is suitable for directly cooling fast;
Fig. 3 A-Fig. 3 D is respectively the typical gold phase constitution of the embodiment 1,3,6,9 with different thicknesss of slab, wherein, the metallograph of embodiment 1,3,6 is for implementing the metallographic structure of segmentation process for cooling thickness of slab from 1.5mm to 6mm, more than the minimum cooling rate of the present invention reaches, can make the martensitic stucture of tissue acquisition more than 90% of steel plate; The metallograph of embodiment 9 is the tissue of directly quick cooling, the medium cooling rate of 35 ℃/s, 3mm intermediate gauge steel plate, all is martensitic stucture basically.
Embodiment
Below be specifying of example 1-11 of the present invention.
The concrete chemical ingredients (Wt%) of example 1-11 sees Table 1:
Table 1
| Numbering | C | Si | Mn | P | S | T.Al | Nb | Ti | V | N | Ca |
| 1 | 0.08 | 0.25 | 2.00 | 0.013 | 0.004 | 0.010 | 0.045 | 0.030 | 0.0029 | 0.0010 | |
| 2 | 0.15 | 0.80 | 1.61 | 0.005 | 0.0029 | 0.027 | 0.031 | 0.017 | 0.0026 | ||
| 3 | 0.16 | 0.26 | 1.35 | 0.013 | 0.005 | 0.028 | 0.017 | 0.018 | 0.0034 | 0.0050 | |
| 4 | 0.19 | 0.28 | 1.05 | 0.013 | 0.0029 | 0.018 | 0.015 | 0.014 | 0.0039 | ||
| 5 | 0.15 | 0.26 | 0.85 | 0.013 | 0.0029 | 0.038 | 0.047 | 0.018 | 0.043 | 0.0035 | |
| 6 | 0.20 | 0.75 | 0.50 | 0.005 | 0.0029 | 0.025 | 0.027 | 0.018 | 0.050 | 0.0034 | |
| 7 | 0.10 | 0.27 | 2.00 | 0.013 | 0.0029 | 0.028 | 0.050 | 0.018 | 0.045 | 0.0035 | |
| 8 | 0.12 | 0.25 | 1.60 | 0.013 | 0.0029 | 0.060 | 0.010 | 0.010 | 0.080 | 0.0080 | |
| 9 | 0.15 | 0.79 | 0.50 | 0.012 | 0.0029 | 0.015 | 0.028 | 0.025 | 0.100 | 0.0058 |
| Numbering | C | Si | Mn | P | S | T.Al | Nb | Ti | V | N | Ca |
| 10 | 0.19 | 0.77 | 1.38 | 0.005 | 0.0029 | 0.028 | 0.026 | 0.022 | 0.0033 | ||
| 11 | 0.20 | 0.28 | 1.58 | 0.005 | 0.004 | 0.003 | 0.023 | 0.017 | 0.0022 | 0.0025 |
The concrete processing parameter of example 1-11 sees Table 2:
Table 2
| Numbering | Heating temperature ℃ | Finishing temperature ℃ | Finished product thickness of slab mm | Roll postcooling technology | Cold ℃ eventually | Remarks |
| 1 | 1150 | 750 | 1.5 | 20 ℃/s of leading portion, 650 ℃ stopped 50 ℃/s of back segment 2 seconds | 150 | The segmentation cooling |
| 2 | 1180 | 780 | 3 | 25 ℃/s of leading portion, 740 ℃ stopped 60 ℃/s of back segment 4 seconds | 200 | The segmentation cooling |
| 3 | 1200 | 800 | 3 | 30 ℃/s of leading portion, 710 ℃ stopped 70 ℃/s of back segment 4 seconds | 180 | The segmentation cooling |
| 4 | 1220 | 820 | 4 | 25 ℃/s of leading portion, 720 ℃ stopped 65 ℃/s of back segment 6 seconds | 200 | The segmentation cooling |
| 5 | 1220 | 850 | 4 | 20 ℃/s of leading portion, 700 ℃ stopped 60 ℃/s of back segment 8 seconds | 250 | The segmentation cooling |
| 6 | 1250 | 900 | 6 | 22 ℃/s of leading portion, 750 ℃ stopped 55 ℃/s of back segment 10 seconds | 300 | The segmentation cooling |
| 7 | 1150 | 750 | 1.5 | 20℃/s | 150 | Directly cooling fast |
| 8 | 1180 | 850 | 3 | 29℃/s | 200 | Directly cooling fast |
| 9 | 1200 | 880 | 3 | 35℃/s | 250 | Directly cooling fast |
| Numbering | Heating temperature ℃ | Finishing temperature ℃ | Finished product thickness of slab mm | Roll postcooling technology | Cold ℃ eventually | Remarks |
| 10 | 1220 | 890 | 4 | 50℃/s | 210 | Directly cooling fast |
| 11 | 1250 | 900 | 6 | 70℃/s | 350 | Directly cooling fast |
The mechanical property of example 1-11 sees Table 3.
Table 3
By table 3 as seen, vertical yield strength of 11 embodiment is all greater than 750MPa, and tensile strength is between 1000MPa～1100MPa, unit elongation A
80More than or equal to 7%, vertical and horizontal clod wash d=4t (flexual center diameter=4 * steel plate thickness) is all qualified, has reached the requirement of tensile strength 1000MPa level hot-rolled super-strength martensitic steel.
Claims (3)
1. a tensile strength is higher than the manufacture method of the hot rolling martensite steel plate of 1000MPa, and the martensite of described martensite steel plate is greater than 90%, and all the other are bainite, and its composition is (weight percent):
C 0.08～0.20；
Si ≤0.8；
Mn 0.5～2.0；
Al 0.010～0.060；
N ≤0.008；
P ≤0.020；
S ≤0.005；
Among Ti 0.01～0.03, V≤0.10 and the Nb 0.01～0.05 one or more;
Ca:0.001～0.005, some adding in sulphur content 〉=0.003;
Other is that Fe and inevitable impurity are formed;
It is characterized in that this manufacture method comprises the steps:
1) smelts, casts the formation steel billet;
2) steel billet is heated to 1150～1250 ℃, soaking time is pressed net thickness 1～1.5min/mm and is calculated;
3) in the temperature range of recrystallize can take place in austenite, adopt one or more passages, described billet rolling is become steel plate;
4) at austenite recrystallize not taking place promptly is lower than the Tnr temperature but is higher than Ar
3In the temperature range of transition point, adopt one or more passages, above-mentioned steel plate rolling is become the steel plate of final thickness, finishing temperature is between 750 ℃～900 ℃;
5) be quickly cooled to described steel plate between the cooling termination temperature of 150 ℃～Ms with the speed of cooling that is not less than 20 ℃/s and coil into coil of strip.
2. manufacture method according to claim 1 is characterized in that, also comprises step: cooled coil of strip is carried out tempering to improve performance and to eliminate stress, and tempering temperature is 150 ℃～250 ℃.
3. manufacture method according to claim 1, it is characterized in that, process of cooling in the described step 5 is: the medium temperature that is cooled to 650 ℃～750 ℃ with the cooling rate that is not less than 20 ℃/s earlier stopped 2～10 seconds, was cooled to the cooling termination temperature of 150 ℃～Ms and coiled into coil of strip with the cooling rate that is not less than 50 ℃/s again.
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