CN1840724A - Superhigh strength steel plate with yield strength more than 960Mpa and method for producing same - Google Patents
Superhigh strength steel plate with yield strength more than 960Mpa and method for producing same Download PDFInfo
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Abstract
The invention provides a super-strength steel plate comprising the following constituents (by weight percent): C 0.08-0.18%, Si<=0.6%, Mn 0.5-2.0%, Al <=0.018%, N<=0.008%, B<=0.0025%, Ca 0-0.006%, P<=0.015%, S<=0.005%, Ni <=1.0%, Cr<=0.8%, Cu<=0.5%, Mo<=0.6%, Ti 0.01-0.03%, V<=0.1%, Nb 0.01-0.1%, balancing Fe and unavoidable foreign substance. The invention also provides the preparing process.
Description
Technical field
The present invention relates to the manufacture method of ferrous materials, particularly ultrahigh-strength steel plates and manufacture method thereof.
Background technology
The manufacture method of the relevant ultrahigh-strength steel plates of yield strength more than 700MPa has formed multinomial patent in the world, among the patent JP 60121219 and JP 89025371 as Sumitomo Metal Industries, silicone content is≤0.015% in employing tempering process production high-strength steel and the steel, nickel content is 1.00%～3.50%, chromium content 0.40%～1.20%.
The patent WO 200039352 of Exxonmobil Upstream Res company application 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.In the low-alloy super-strength steel plate patent WO 9905335 of Exxonmobil Upstream Res and Nippon Steel's cooperation application, though adopt the not tempering of after hot rolling, only quenching, but carbon content is hanged down and is 0.05-0.10% in its composition, the this patent carbon content is 0.08%～0.18%, roll the back and directly quicken cooling, can not tempering, notable difference is arranged.
In the high tensile steel plate patent of Sumitomo Metal Industries (JP 59159932), employing direct quenching after hot rolling adds the tempered method, and in its composition design, the scope of the titanium of employing is low to be 0.003-0.010%.
In " production of high-strength steel plate " patent (GB 2132225) of NIPPON KOKAN KK, control the speed of direct quenching after the hot rolling by control discharge, the thickness of production is greater than 25mm, and needs tempering.Carbon in its composition (0.04%～0.16%), manganese (0.40～1.20%), chromium (0.20～1.50%), nickel (0.20～5.00%), molybdenum (0.20～1.00%), aluminium (0.01～0.10%).
In the patent (98812446.7) of " the ultra-high strength Ausaged steels " of Exxon Mobil with excellent low-temperature flexibility, 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, tensile strength has only more than the 830MPa, and its normal temperature is organized the micro-lamellar structure based on the lath of fine-grained martensitic and close grain lower bainite of 2-10vol% austenite film layer and about 90-98vol%.
Unite in the Chinese patent 98802878.6 of " high-tensile-strength steel and production method thereof " of application in Exxon Mobil and Sumitomo Metal Industries, the carbon content of steel plate is 0.02-0.10%, and manganese is 0.2-2.5%, more than the tensile strength 900MPa.
In the Dillimax series high-strength steel of the Weldox960 of the correspondence that Sweden SSAB company produces series and Dillingen, Germany production, all adopt the method for high alumina (being not less than 0.018%) to rely on the aluminium crystal grain thinning to improve the obdurability of steel.
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 high level, the steel product cost height.Nickel as adding among JP 60121219 and the JP 89025371 is 1.00%～3.50%, chromium content 0.40%～1.20%; Nickel content is not less than 1.0% among the WO 200039352; 2. complex process, the process cost height.Low as carbon content among the patent WO 9905335 is 0.05-0.10%, carbon 0.04%～0.16% among the patent GB 2132225, carbon content is 0.02-0.10% in the patent 98802878.6, and decarburization time was long when low excessively carbon content caused steel-making, and steel melting furnace labour productivity is low; Patent JP 60121219, JP 89025371, JP 59159932 and GB 2132225 have all adopted tempering process, have increased by a procedure, have improved process cost.In the Dillimax series high-strength steel that Weldox960 series that Sweden SSAB company produces and Dillingen, Germany are produced, all adopt high aluminium content (being not less than 0.018%), following some shortcomings are arranged: high aluminum steel molten steel is the easy dross in the mouth of a river when cast, brings the anti-material of ladle nozzle into molten steel easily; Too much aluminium can cause that alumina inclusion significantly increases in the steel, needs long argon blowing time impel inclusion floating; The tiny precipitate of the aluminium nitride of aluminium crystal grain thinning dissolves when steel plate welds fully, thereby makes welded heat affecting zone crystal grain thick.3. the armor plate strength rank is low.As patent WO 200039352 and patent 98812446.7, tensile strength can only reach more than the 830MPa, and patent 98802878.6 tensile strength can only reach more than the 900MPa.
Because the development of industries such as heavy load truck, engineering machinery, the requirement of the intensity of the load-carrying of vehicle and machinery is improved constantly, also require to alleviate deadweight simultaneously, require therefore to adopt that cost is lower, the intensity rank good ultrahigh-strength steel plates of high and low temperature impelling strength more.
Summary of the invention
The object of the present invention is to provide a kind of manufacture method with ultrahigh strength hot-rolled steel plate of good low-temperature toughness, by rational design of alloy and technology controlling and process, employing is rolled after-acceleration cooling (ACC) technology and is reached the yield strength of steel plate more than 960MPa, its low-temperature impact toughness reaches E level above (ballistic work that promptly satisfies-40 ℃ is not less than 27J), and has good plasticity and weldability.
For achieving the above object, the above ultrahigh-strength steel plates of technical solution of the present invention: yield strength 960MPa, its composition are (weight percent):
C 0.08％～0.18％；
Si≤0.6％；
Mn 0.5％～2.0％；
Al≤0.018％；
N≤0.008％；
B≤0.0025％；
Ca 0％～0.006％；
P≤0.015％；
S≤0.005％；
More than in Ni≤1.0%, Cr≤0.8%, Cu≤0.5% and Mo≤0.6% one or more;
More than among Ti 0.01%～0.03%, V≤0.1% and the Nb 0.01%～0.1% one or more;
Yu Tie and inevitable impurity.
The production method of ultrahigh-strength steel plates of the present invention comprises the steps:
1) smelts, casts the formation steel billet;
2) steel billet is heated to 1100～1250 ℃;
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 860～920 ℃;
5) with the speed of cooling that is not less than about 5 ℃/s online being cooled to of described steel plate is lower than Ms～Ms+100 ℃ cooling termination temperature;
Further, in the step 3, draft rolling in the temperature range of recrystallize can take place austenite is not less than 60%.
In the step 4, be lower than austenite generation recrystallize but be higher than Ar
3Rolling draft is not less than 50% in the temperature range of transition point
Can carry out tempering to improve performance to cooled steel plate, tempering temperature is 350～550 ℃.
The course of hot rolling hot rolling is at the end carried out water-cooled after advanced line space is cold, and the final temperature scope of air cooling is: 750～920 ℃.
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% to 0.18%, 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 unfavorable for forming the intensity that enough strengthening phases obtain steel plate in the austenitic transformation process; Otherwise carbon content is higher than at 0.18% o'clock, and then the plasticity of steel and toughness reduce, and weldability is variation also.
Silicon: the stability influence to supercooled austenite is little.Silicon plays the solution strengthening effect in steel, and content can suppress separating out of carbide, raising toughness more for a long time.Add silicon in the steel and can improve purity of steel and deoxidation.
Manganese: improve the principal element of bainitic steel hardening capacity, reduce the transformation temperature of bainitic steel, the thinning microstructure substructure, the degree of supersaturation of carbon helps the raising of intensity in the increase bainite ferrite.
Nitrogen: in adding the steel of titanium, an amount of nitrogen and titanium form titanium nitride, thisly easily second help strengthening matrix mutually what high temperature was separated out, and improve the welding property of steel plate.If but nitrogen is too high, as be higher than 0.0060%, 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, an amount of titanium has not only been fixed the nitrogen in the steel but also has been fixed sulphur and the part carbon in the steel.But titanium content is too high greater than 0.03%, can cause that titanium nitride is thick to be mingled with, and worsens the performance of steel, and the carbon of solid solution in the steel reduces, and is unfavorable for obtaining good obdurability coupling.Titanium content is crossed low less than 0.01% effect that does not have crystal grain thinning.Therefore an amount of titanium (0.01%～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.
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.
Molybdenum: perlite is separated with the bainite transformation curve, and move to right effectively ferrite and perlite begin to separate out line, to bainite begin that to separate out line influence little, help the acquisition of bainite structure, improve bainite hardening capacity.Add molybdenum, can refinement microstructure, improve toughness.
Nickel: improve the toughness of steel, the steel that especially has low-temperature flexibility to require.Adding nickel can increase bainite or martensite border residual austenite film, improves plasticity and toughness.And help the structure refinement after the tempering.
Copper: solution strengthening, amount more for a long time can be after the proper temperature tempering secondary hardening, improve intensity.Not high for the general content of non-hardened steel.
Chromium: perlite is separated with the bainite transformation curve, in, under the condition of low-carbon (LC), can obviously move to right proeutectoid ferrite and perlite begin to separate out line, but instead of part manganese and molybdenum.Thinning microstructure reduces ductile-brittle transition temperature.It is bigger than manganese that chromium reduces the Bs/Ms value, helps reducing the welding crack tendency.Chromium and manganese element cooperate, and can obtain higher hardenability and full hardening deepness, improve the mechanical property of steel.Chromium is littler than the segregation of manganese tendency, helps reducing the core segregation of steel, raising mechanical property homogeneity with chromium for manganese.
Calcium: an amount of calcium can change the shape of sulfide, alleviates the disadvantageous effect of sulphur.When having excessive titanium in the steel, titanium can close with sulfuration and form titanium sulfide or carbon titanium sulfide, so whether the adding of calcium can be decided according to the add-on of titanium and the content of sulphur.
Boron: the trace B solid solution will make in all of steel warm structural transformation postpone strongly in matrix, it and the compound adding of molybdenum will make steel obtain bainite in very wide cooling rate scope, but when its content is too high, can form carbon (nitrogen) and change thing, so its content is generally less than 0.0025%.
Aluminium: steel of the present invention only contains on a small quantity or does not contain this element, adopts titanium and measures such as other element and processing method to come crystal grain thinning and raising weldability.Aluminium is the main deoxidant element in the steel, helps crystal grain thinning, all contains a certain amount of in the general steel.In the Dillimax series high-strength steel that Weldox960 series that Sweden SSAB company produces and Dillingen, Germany are produced, adopt the method for high alumina (being not less than 0.018%) to rely on the aluminium crystal grain thinning to improve the obdurability of steel.But the aluminium crystal grain thinning has many shortcomings (above stating).The present invention does not adopt aluminium, and aluminium can add other thin brilliant element ti, V, Nb etc. and utilize the means on the production technique to come thinning microstructure less than 0.018%, and this kind crystal grain thinning method helps follow-up steel plate welding.
The present invention adopts the relatively more moderate carbon content (0.08% to 0.18%) of other patent, 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 Nb content that adds in C content and the steel plate guarantees as far as possible by solubility product formula Lg[Nb] T that calculates of [C]=2.96-7510/T is less than 1523K (1250 ℃); If add V, the T that also will guarantee to calculate by similar formula is less than 1523K, 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.Element ti that adds and N content guarantee Ti/N 〉=3.42, allow Ti be completely fixed N, make Nb can form enough NbC and strengthen; Ca that adds and S content guarantee Ca/S 〉=0.5～2.0, make complete nodularization of sulfide or approximate fusiform, improve steel plate transverse impact, cold-bending property.If it is fashionable that the Cu in the steel, Ni, Cr, Mo add simultaneously, can not be simultaneously near the upper limit or lower limit, 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, and simple steel-making, rolling and process for cooling obtain over-all properties such as mechanics, welding preferably.
Steel billet is heated to fully that high temperature (1100～1250 ℃) makes the austenite structure homogenizing, and the carbide of the niobium in the steel, vanadium and titanium etc. fully dissolves, and titanium nitride also has and is partly dissolved to 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, during allow to adopt one or many to change steel to improve the horizontal plastic property and the toughness of finished product steel plate, 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 refinement.
Be lower than austenite generation recrystallize but be higher than Ar
3In the temperature range of transition point, adopt one or more passages and allow to adopt one or many to change steel, above-mentioned steel plate rolling is become the steel plate of final thickness, the draft of this temperature range is not less than 50%.Finishing temperature is between 860～920 ℃.In the operation of rolling, 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 with the online acceleration of the speed of cooling that is not less than about 5 ℃/s cooling to obtain bainite, martensite or bainite and martensite (may lingering section austenite) mixed structure.Can add 350～550 ℃ of temper to improve the toughness of steel.
Beneficial effect of the present invention
Easy to implement and the control of described composition design, technology controlling and process is simple and easy to do, rolls the after-acceleration cooling owing to adopt, thereby the rolling cycle is short, and steel plate deformed is little.Steel plate yield strength height has good low-temperature flexibility, can add tempering and improve plate property.
Embodiment
Specific embodiments of the invention are referring to table 1,2,3.
Table 1 embodiment chemical ingredients (wt%)
| Embodiment | C | Si | Mn | P | S | T.Al | Ni | Cr | Mo | Cu | Nb | V | Ti | B | N | Ca |
| 1 | 0.18 | 0.60 | 1.98 | 0.006 | 0.005 | 0.004 | 0 | 0.28 | 0.21 | 0 | 0 | 0.05 | 0.030 | 0.0020 | 0.0070 | 0.002 |
| 2 | 0.17 | 0.38 | 1.18 | 0.006 | 0.005 | 0.015 | 0.48 | 0.19 | 0.43 | 0 | 0.013 | 0.035 | 0.017 | 0.0017 | 0.0018 | 0 |
| 3 | 0.14 | 0.30 | 0.90 | 0.007 | 0.004 | 0.010 | 0.20 | 0.80 | 0.59 | 0.25 | 0.050 | 0.10 | 0.015 | 0.0018 | 0.0053 | 0.0018 |
| 4 | 0.11 | 0.29 | 1.15 | 0.005 | 0.005 | 0.007 | 0.48 | 0.19 | 0.46 | 0 | 0.013 | 0.041 | 0.011 | 0.0017 | 0.0024 | 0 |
| 5 | 0.08 | 0.03 | 0.52 | 0.008 | 0.005 | 0.018 | 1.00 | 0 | 0 | 0.50 | 0.071 | 0 | 0.010 | 0.0008 | 0.0035 | 0.0025 |
| 6 | 0.15 | 0.30 | 2.00 | 0.010 | 0.004 | 0.012 | 0.90 | 0.70 | 0.60 | 0.50 | 0.071 | 0 | 0.030 | 0.0025 | 0.008 | 0.006 |
Table 2
| Embodiment | The hot rolling Heating temperature | Finishing temperature | The finished product thickness of slab | Roll the after-acceleration rate of cooling | |
| 1 | 1250℃ | 920℃ | 16mm | 10℃/s | |
| 2 | 1200℃ | 880℃ | 16mm | 15℃/s | |
| 3 | 1200℃ | 900℃ | 16mm | 15℃/s | |
| 4 | 1200℃ | 860℃ | 16mm | 20℃/s | |
| 5 | 1200℃ | 860℃ | 16mm | 20℃/s | 550 ℃ of tempering 1.5 hours |
| 6 | 1200℃ | 860℃ | 16mm | 20℃/s | 550 ℃ of tempering 1.5 hours |
The horizontal mechanical property of the foregoing description sees Table 3.By table as seen, the yield strength of embodiment is all greater than 960MPa, and unit elongation is more than or equal to 12%, and-40 ℃ ballistic work has reached the requirement of 960E level all greater than 27J.
Table 3 embodiment mechanical property (laterally)
| Embodiment | Yield strength/MPa | Tensile strength | Unit elongation/% | Reduction of area/% | Akv | |
| -20℃ | -40℃ | |||||
| 1 | 975 | 1186 | 14.0 | 58.0 | 40 | 35 |
| 2 | 1073 | 1287 | 13.0 | 61.2 | 42 | 37 |
| 3 | 1060 | 1250 | 13.5 | 57.0 | 35 | 30 |
| 4 | 988 | 1177 | 15.0 | 55.8 | 38 | 33 |
| 5 | 965 | 1080 | 16.5 | 60.0 | 50 | 42 |
| 6 | 1050 | 1280 | 14.0 | 60.0 | 45 | 35 |
Claims (8)
1. the above ultrahigh-strength steel plates of yield strength 960MPa, its composition is (weight percent):
C 0.08％～0.18％；
Si≤0.6％；
Mn 0.5％～2.0％；
Al≤0.018％；
N≤0.008％；
B≤0.0025％；
Ca 0％～0.006％；
P≤0.015％；
S≤0.005％；
More than in Ni≤1.0%, Cr≤0.8%, Cu≤0.5% and Mo≤0.6% one or more;
More than among Ti 0.01%～0.03%, V≤0.1% and the Nb 0.01%～0.1% one or more;
Yu Tie and inevitable impurity.
2. the above ultrahigh-strength steel plates of yield strength 960MPa as claimed in claim 2 is characterized in that Ti/N 〉=3.42.
3. the above ultrahigh-strength steel plates of yield strength 960MPa as claimed in claim 2 is characterized in that Ca/S 〉=0.5～2.0.
4. the production method of the above ultrahigh-strength steel plates of yield strength 960MPa comprises the steps:
1) presses mentioned component and smelt, cast the formation steel billet;
2) steel billet is heated to 1100～1250 ℃;
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 the recrystallization zone 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 860～920 ℃;
5) with the speed of cooling that is not less than about 5 ℃/s online being cooled to of described steel plate is lower than Ms～Ms+100 ℃ cooling termination temperature.
5. the production method of ultrahigh-strength steel plates as claimed in claim 4 is characterized in that, in step 3, draft rolling in the temperature range of recrystallize can take place austenite is not less than 60%.
6. the production method of ultrahigh-strength steel plates as claimed in claim 4 is characterized in that, in step 4, is being lower than austenite generation recrystallize but is higher than Ar
3Rolling draft is not less than 50% in the temperature range of transition point.
7. the production method of ultrahigh-strength steel plates as claimed in claim 4 is characterized in that, cooled steel plate is carried out tempering, and tempering temperature is 350～550 ℃.
8. the production method of ultrahigh-strength steel plates as claimed in claim 4 is characterized in that, the course of hot rolling hot rolling is at the end carried out water-cooled, the final temperature of air cooling after advanced line space is cold: 750～920 ℃.
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