CN102337482A - Bainite high strength and toughness steel plate with yield strength of 900 MPa and its manufacture method - Google Patents
Bainite high strength and toughness steel plate with yield strength of 900 MPa and its manufacture method Download PDFInfo
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Abstract
The invention relates to a bainite high strength and toughness steel plate with the yield strength of 900 MPa and its manufacture method. The chemical composition of the steel plate (weight percent wt.%) comprises: 0.07-0.14% of C, 0.25-0.50% of Si, 1.70-2.20% of Mn, 0.05-0.50% of Cr, 0.20-0.50% of Ni, 0.03-0.10% of Nb, 0.03-0.10% of V, 0.01-0.04% of Ti, 0.02-0.04% of Al, 0.0006-0.0025% of B, the balance of Fe and inevitable impurity. The method adopts a thermo-mechanical controlled rolling technology and a cooling technology to obtain an organization with an ultra-fine bainite lath as a matrix, the yield strength of the steel plate is greater than or equal to 900 MPa, the tensile strength is greater than or equal to 980 MPa, the Charpy impact energy Akv (20 DEG C below zero) is more than 150 J, the weld crack sensitivity index Pcm is less than or equal to 0.25%, the steel plate has good welding performance.
Description
Technical field
The present invention relates to HS low-temperature high-toughness steel plate, specifically, the present invention relates to ys 900MPa level bainite type high strength steel plate and method of manufacture thereof.
Background technology
The hot treat mechanically of steel plate adopts controlled rolling and controlled cooling mode (TMCP) usually.Realize the refinement of microtexture or form HS tissue such as ultra-fine bainite, the ys of raising steel through controlled deformation rate and speed of cooling.
Prior art has the document of introducing bainite high-strength steel, being prone to welding high-strength steel and high strength steel plate.Publication number is that the one Chinese patent application of CN1786246 discloses " high tensile strength high toughness low yield ratio bainite steel and working method thereof "; This steel plate has 800MPa tensile strength; Ductile-brittle transition temperature is below-60 ℃, and its chemical ingredients (wt.%) is C:0.08～0.15%, Si:0.26～0.46%, Mn:1.5～1.7%, Nb:0.015～0.060%, Ti:0.005～0.03%, B:0.0005～0.003%, Mo:0.2～0.5%, Cu:0.4～0.6%, Ni:0.26～0.40%, Al:0.015～0.05%.It is a kind of with the low-alloy high-strength steel of two temperature stages with the TMCP explained hereafter that publication number is that the international application of WO99/05335 discloses; Tensile strength with 930MPa;-20 ℃ of ballistic works are 120J, and its chemical ingredients (wt.%) is: C:0.05～0.10%, Mn:1.7～2.1%, Ni:0.2～1.0%, Mo:0.25～0.6%, Nb:0.01～0.10%, Ti:0.005～0.03%, P≤0.015%, S≤0.003%.
The alloying element design of above-mentioned disclosed two kinds of steel grades is respectively Mn-Ni-Nb-Mo-Ti and Mn-Mo-Ni-Cu-Nb-Ti system; Because Mo is valuable alloy; Therefore analyze from the kind of the alloying element that adds and the total amount of adding, it is higher to prepare this type of steel grade cost.
Summary of the invention
In order to overcome the above problems; It is steel grade that the present inventor adopts Si-Mn-Cr-Ni-Nb-V-Ti-Al-B; Through control thermo-mechanical rolling and cooling technology; And do not have modifier treatment, prepared the low-carbon (LC) that a kind of ys reaches the 900MPa level and had low temperature superhigh tenacity and the low steel plate of welding crack sensibility index, this steel plate has good low-temperature flexibility and weldableness.
One object of the present invention is to provide a kind of ys 900MPa level bainite type high strength steel plate.
Another object of the present invention is to provide the method for manufacture of said superstrength, H.T., the low steel plate of welding crack sensibility index.
To achieve these goals; The chemical ingredients (weight percentage wt.%) of ys 900MPa level bainite type high strength steel plate of the present invention comprises: C:0.07～0.14%, Si:0.25～0.50%, Mn:1.70～2.20%, Cr:0.05～0.50%, Ni:0.20～0.50%, Nb:0.03～0.10%, V:0.03～0.10%, Ti:0.01～0.04%, Al:0.02～0.04%, B:0.0006～0.0025%, surplus are Fe and unavoidable impurities.
Ys>=the 900MPa of steel plate, tensile strength>=980MPa, Xia Shi ballistic work Akv (20 ℃) be greater than 150J, welding crack sensibility indices P cm≤0.25%.
The method of manufacture of above-mentioned ys 900MPa level bainite type high strength steel plate comprises:
Smelting, casting, heating, rolling, cooling and tempering process;
In the heat-processed, heating and temperature control is at 1080～1280 ℃;
Rollingly be divided into the fs and subordinate phase is rolling; Fs is rolling carries out more than recrystallization temperature, and it is rolling that rolling back of fs treats that on roller-way temperature is carried out subordinate phase to 770～860 ℃, and finishing temperature is 760～840 ℃;
Cool off after rolling, preferably, steel plate with the speed of 12～45 ℃/s be cooled to≤400 ℃, air cooling after the water outlet;
Carry out tempering heat treatment behind the cool to room temperature, tempering temperature is 350～500 ℃, air cooling after the tempering.Preferably, air cooling adopts stacking or cold bed cooling.
Adopted the control of improved TMCP and relaxation to separate out (RPC) technology during thermal treatment of the present invention, rolling back air cooling relaxation for some time, make carbonitride in dislocation with the formation disperse of subgrain boundary place and tiny separating out.It is rolling to carry out subordinate phase behind the relaxation, the rolling after-acceleration cooling of subordinate phase.The ultimate principle of technological process is:
Steel plate fully is out of shape in the recrystallization zone, and the dislocation desity in the austenite increases.Dynamic recovery that takes place in the operation of rolling and recrystallize refinement original austenite grain.There is the hydrostaticpressure field of force in edge dislocation, and interstitial atom such as B etc. can dispiration place's enrichments.Subgrain boundary can be described with dislocation model, and interstitial atom can be to the enrichment of subgrain boundary place.The enrichment of interstitial atom makes the dislocation place form the Cottrell air mass, has hindered high density dislocation process evolution in Recovery Process that distortion causes, and has formed the stable network of dislocation.In the relaxation process, microalloy elements such as Nb, V, Ti are so that (Ti) x (C, N) separate out at crystal boundary, subgrain boundary and dislocation place by the carbonitride of different chemical such as y metering ratio for Nb, V.Two-phase particles such as the carbonitride of separating out, pinning dislocation and the subgrain boundary in the crystal grain, stablized like substructures such as dislocation walls.
It is rolling to carry out subordinate phase behind the relaxation, and the dislocation desity in the steel is further increased.Relaxation after strain steel plate gets into accelerated cooling device, and cooling rate has been avoided ferritic and pearlitic C curve among the CCT figure faster, directly gets into the bainite transformation district.The nucleation rate process of bainite has received the influence of following factor:
(1) learn angle analysis from thermodynamics, austenite has bigger condensate depression, and has a large amount of defectives, defective that the defective ability can be provided in the austenite, and the two all can increase phase driving force, and the bainite nucleation rate is increased;
(2) from the crystallography angle analysis, a large amount of defectives in the austenite cause the zone that exists a lot of mismatch higher in the lattice, and bainite is the forming core in the sub-region more easily;
(3) from the crystalline structure angle analysis, separate out in the relaxation process a large amount of tiny and carbonitride of disperse provides a large amount of potential nucleation site.
Owing to the influence of above-mentioned three reasons, bainite has very high nucleation rate.Growing up of bainite lamella receives the influence of following reason:
(1) from the thermodynamics angle analysis, the interface of alloying element atom pairs scattering nature moves through solute effect of dragging dissipation free energy, has reduced the bainite coarsening rate;
(2) from the kinetics angle analysis, lower transition temperature has reduced the velocity of diffusion of carbon atom and iron atom, the coarsening rate of having slowed down bainite ferrite;
(3) from the crystalline structure angle analysis, bainite receives the obstruction of the place ahead subgrain boundary in the growth process behind the subgrain boundary forming core.In the austenite Recovery Process, the motion of dislocation receives the pinning of the second phase particle, has therefore formed a large amount of subgrain boundaries.Subgrain boundary through developing has restraining effect to growing up of bainite.
More than three reasons cause the coarsening rate of bainite ferrite and the final lengths of bainite ferrite to be suppressed.This technology to promote forming core with the combined action refinement that suppresses to grow up the bainite ferrite lath of final tissue.
For physical construction and the employed high-strength steel of engineering construction, need before the weldering not preheating or preheating and not cracking a little, mainly be the welding procedure problem that has solved large-scale steel structure members.The only resource that reduces Pcm is exactly the add-on that reduces carbon and alloying element; And for the high-strength steel that adopts quenching+tempering process to produce; The reduction that the add-on of minimizing carbon and alloying element will be brought hardness of steel inevitably; Adopt improved TMCP+RPC technology among the present invention, then can remedy this defective.The welding crack sensibility indices P cm of steel plate can confirm by following formula
Pcm＝C+Si/30+Ni/60+(Mn+Cr+Cu)/20+Mo/15+V/10+5B
Welding crack sensibility indices P cm is the judgement index of the welding cold cracking tendency of reflection steel, and Pcm is low more, and weldableness is good more.The steel of weldableness difference is easy to generate crackle after welding, for fear of the generation of crackle, must before welding, carry out preheating to steel, and weldableness is good more, and then required preheating temperature is low more, otherwise then needs higher preheating temperature.According to the ferrous metallurgy industry standard YB/T 4137-2005 of the People's Republic of China regulation, the trade mark is the steel grade of Q800CF, and the Pcm value need be lower than 0.28%.Ys 900MPa grade steel plate involved in the present invention, microtexture is ultra-fine lath of bainite, has characteristics such as H.T. and welding crack sensibility index are low, its welding crack sensibility is lower than 0.25%.
The composition system that the present invention adopts guarantees that steel plate has HS and low-temperature flexibility, and welding crack sensibility indices P cm≤0.25% has good welding property simultaneously.
The composition of steel of the present invention designs as follows:
C: for the bainitic steel that adopts the TMCP explained hereafter; When carbon content is low; The diffusion phase transformation of bainite ferrite lath is easier to, and the bainite ferrite lath width of formation is bigger, when carbon content is higher; Need more carbon atom diffusion during bainitic transformation, the width of bainite ferrite lath reduces.The impelling strength of low-carbon bainite steel is by following controlling factors: the pattern and the distribution of the oversaturated carbon content in the bainite ferrite, the width of lath of bainite and pattern, participation horse constituent element difficult to understand.Comprehensive several respects factor considers and combines experimental result that C content of the present invention is controlled to be 0.07～0.14%.
Si:Si does not form carbide, is present in the steel with the solid solution form, hinders the motion of dislocation in the steel, improves the intensity of steel.Si can change the free energy that cementite is separated out simultaneously, and the Si of high level can suppress cementite and form.When Si content is higher, can increase the welding crack sensibility index, reduce the welding property of steel.Si content among the present invention is controlled to be 0.25～0.50%.
Mn:Mn enlarges the austenitic area in the carbon iron balance phasor.Mn and Fe can form sosoloid; The Mn that is solid-solubilized in the austenite passes through the solute drageffect; Reduce the phase driving force of diffusion phase transformation, suppressed ferrite transformation on the one hand, suppressed the end face diffusion control of lath of bainite on the other hand and grown up; Refinement lath of bainite, improved the intensity and the toughness of steel plate.Usually add valuable Alloy Elements Mo in the steel, suppress the diffusion phase transformation, the refinement lath of bainite.Higher Mn can realize improving intensity through the final tissue of refinement, guarantees that simultaneously steel plate has high toughness.Add 1.70～2.20% Mn among the present invention, help forming the bainite structure of refinement, make steel have good obdurability.
Nb:Nb has restraining effect to austenite one phase diffusion motion interface, thereby has improved the recrystallization temperature of steel.In the two stage rolling processes, higher recrystallization temperature can be after high temperature section be rolling, and recrystallize, crystal grain thinning fully take place austenite crystal.Nb can increase the hardening capacity of steel plate, and the Nb that adds certain content can produce the bigger steel plate of thickness.Strain inducing can take place in the subordinate phase operation of rolling carbide of Nb separates out; The Nb that separates out (CN) particle has the ability that hinders dislocation motion; Improve the dislocation desity in the austenite, suppress ferrite transformation, improve the nucleation rate of bainitic transformation; Refinement is finally organized, and improves the intensity and the toughness of steel plate.Add 0.03～0.10%Nb among the present invention with control steel plate microtexture and mechanical property.
V:V plays the effect of the carbonitride precipitation strength of solution strengthening and V in steel.The tiny ys that can improve steel plate of separating out of the disperse of V (CN) in drawing process, and not obvious to the flexible influence.Add 0.03～0.10% V among the present invention to guarantee that steel plate has higher yield strength after tempering.
Cr:Cr is solid-solubilized in the steel, improves the hardening capacity of steel plate.Cr is a carbide forming element, can form tiny carbide, improves the intensity of steel plate.Add 0.05～0.50% Cr among the present invention, guarantee the intensity and the ballistic work of steel plate.
Ni:Ni does not form carbide in being solid-solubilized in steel, can reduce ferritic stacking fault energy, improves the low-temperature impact toughness of steel plate.But Ni belongs to valuable alloying element, can cause the steel plate cost to raise when content is higher, and the market competitiveness descends, and adds 0.20～0.50% Ni among the present invention with the mechanical property that guarantees steel plate and have the market competitiveness.
C in Ti:Ti and the steel and N form compound.The formation temperature of TiN is more than 1400 ℃, in liquid phase or delta ferrite, separates out Ti usually
4C
2S
2Begin to separate out at 1260 ℃, TiC separates out about 1050 ℃, tiny precipitate meeting pinning crystal boundary, refine austenite size.Ti content among the present invention is controlled at 0.01～0.04%.
Al:Al when comparatively high temps and in the steel N form tiny and AlN disperse separates out, suppress grain growth, reach crystal grain thinning, improve steel flexible purpose at low temperatures.Add the Al crystal grain thinning that is no more than 0.04wt.% among the present invention, improve the toughness of steel plate and guarantee its welding property.
Dislocation and the fault location enrichment of B:B in steel reduces the crystal boundary energy, suppressed ferritic transformation, promoted the bainite transformation of steel at middle temperature area, increased armor plate strength.When B content was low, not obvious to the facilitation effect of bainitic transformation, the B element was too high, can cause grain-boundary strength significantly to reduce, and formed " boron is crisp " phenomenon.Therefore, the add-on of B is 0.0006～0.0025% among the present invention.
Adopt designed chemical composition of the present invention, meliority is to adopt Mn-Cr-Ni-Nb-V composition system, and high strength steel plate is produced in the effect of the alloying element that rationally utilizes.
In the method for manufacture of ys 900MPa level bainite type high strength steel plate of the present invention, rolling and principle and meliority process for cooling are:
Rolling technology
The present invention adopts two stages controlled rolling technology.Fs is out of shape on the non-recrystallization temperature.The dislocation of accumulative total can improve steel plate subsurface defect ability in the distortion, makes steel plate generation dynamic recrystallization, inferior dynamic recrystallization and static recrystallize, refine austenite crystal grain.When treating temperature to 770～860 ℃ after the fs is rolling, the beginning subordinate phase is rolling.Subordinate phase is rolling in the non-recrystallization district of steel plate, and finishing temperature is 760～840 ℃, and lower rolling temperature makes and added up a large amount of dislocations in the steel plate.Carbonitride fault generation on the throne strain inducing is separated out, pinning the motion of dislocation.In follow-up process of cooling, bainite can be at dislocation and fault location forming core, higher dislocation desity refinement final bainite structure.The precipitation strength effect of the carbonitride of small and dispersed and the refined crystalline strengthening effect of refinement lath of bainite make higher intensity of having of steel plate and toughness.
Process for cooling
Steel plate gets into refrigerating unit after controlled rolling, speed of cooling is 12～45 ℃/s, stops cold temperature and is≤400 ℃.The austenite that has a large amount of dislocations behind the rolling deformation is when cooling off, in lesser temps generation bainite transformation fast.Speed of cooling makes austenite have bigger condensate depression faster, even bainite transformation has bigger forming core motivating force, has improved the nucleation rate of bainite transformation.When lesser temps generation bainite transformation, the carbon atom diffusibility weakens, and bainite ferrite sheet end face is grown up and is suppressed, refinement the bainite ferrite lath.It is of the present invention that to stop cold temperature lower; In speed of cooling and lower stopping under the cold temperature condition faster; Bainite forms with very high nucleation rate and slower coarsening rate; The MA constituent element that forms small and dispersed for the austenite that changes is distributed on the bainite matrix, has improved the intensity and the toughness of steel plate.
Tempering process
Tempering temperature of the present invention is 350～500 ℃.The carbide of V is separated out at fault locations such as dislocation or crystal boundaries in the drawing process.Steel plate is in loading process, and the precipitate at dislocation or crystal boundary place has hindered the motion of mobile dislocation, has improved the ys of steel plate.In the drawing process, the motion of dislocation can take place simultaneously, unlike dislocation is buried in oblivion, and causes dislocation desity decline in the steel plate, and tensile strength reduces.Take all factors into consideration drawing process to ys and effects of tensile strength, the present invention is preferred, and tempering temperature is 350～500 ℃, guarantees that steel plate ys in drawing process is significantly improved, and that tensile strength descends is not obvious.
The steel billet of composition system according to the invention is at 1080～1280 ℃ of austenitizings; The carbonitride of Nb and V can be dissolved in the austenite more fully in the composition; In the operation of rolling subsequently, can form tiny carbonitride, pinning dislocation motion, refine austenite recrystal grain; Finally organize to reach refinement, improve the purpose of steel plate obdurability.Treat on roller-way after the rolling end of fs that temperature is rolling to 770～860 ℃ of beginning subordinate phase, finishing temperature is 760～840 ℃.The rolling temperature of subordinate phase is lower, can guarantee that TR has corresponding deflection to steel plate in the non-recrystallization district, in the steel plate enrichment a large amount of dislocations.Carbon atom can form horse constituent element difficult to understand to the edge dislocation enrichment in cooling phase-change process subsequently.
Steel plate with the speed of 12～45 ℃/s be cooled to≤400 ℃, air cooling after the water outlet.Steel plate adopts very fast speed of cooling and lower to stop cold temperature, and composition system according to the invention is at lower temperature range generation bainitic transformation, forms the lath of bainite of refinement and along the horse of lath interface distributions constituent element difficult to understand, this type of tissue has characteristics such as high-strong toughness.In the said system of composition of the present invention, need to adopt corresponding speed of cooling and stop cold temperature, just can obtain relevant mechanical properties.Steel plate according to the invention stops need carry out temper after cold, and the steel plate tempering temperature is 350～500 ℃, air cooling after the tempering.V separating out in ferritic in the drawing process in the composition system according to the invention can produce strengthening effect, improves the ys of steel plate, and the tempering time scope can guarantee that the carbonitride in the steel plate fully separates out, and realizes the purpose of precipitation strength.
Beneficial effect of the present invention
The present invention substitutes Mo through rational designing chemical composition with cheap alloying elements such as Mn, makes precipitation strength with C, the fine precipitation particles of N chemical combination of V; The precipitation strength effect of replaced C u, alloying element content is few, and raw materials cost is lower; Welding crack sensibility is less, need not preheating before the weldering.
Steel plate of the present invention need not carry out any extra modified thermal treatment, thereby has simplified manufacturing process, has reduced the manufacturing cost of steel.
The present invention is because composition and technological design are reasonable, and from implementation result, process system is looser, can in, stably manufactured on the Plate Steel product line.
Steel plate ys>=900MPa of the present invention, tensile strength>=980MPa, Xia Shi ballistic work Akv (20 ℃)>=150J, welding crack sensibility indices P cm≤0.25% has good welding property.
Description of drawings
Fig. 1 is the stereoscan photograph of the embodiment of the invention 2 steel plates, and this figure shows the refinement lath of bainite;
Fig. 2 is the transmission electron microscope photo of the embodiment of the invention 5 steel plates, and this figure shows the lath of bainite substructure of nano level superfine.
Embodiment
Embodiment 1
Press the chemical ingredients shown in the table 1 and smelt, and be cast into continuously cast bloom or steel ingot, Heating temperature is 1080 ℃; Treat after fs is rolling that temperature is rolling to 860 ℃ of beginning subordinate phase; Finishing temperature is 840 ℃, and the steel plate speed of cooling is 35 ℃/S, and final temperature is a room temperature; Tempering temperature is 500 ℃, the back air cooling of coming out of the stove.
Embodiment 2
Smelt according to the chemical ingredients shown in the table 1, and be cast into continuously cast bloom or steel ingot, Heating temperature is 1280 ℃; Treat after fs is rolling that temperature is rolling to 770 ℃ of beginning subordinate phase; Finishing temperature is 760 ℃, and the steel plate speed of cooling is 12 ℃/S, and final temperature is a room temperature; Tempering temperature is 450 ℃, the back air cooling of coming out of the stove.
Embodiment 3
Smelt according to the chemical ingredients shown in the table 1; And being cast into continuously cast bloom or steel ingot, Heating temperature is 1180 ℃, treats after the fs is rolling that temperature is rolling to 840 ℃ of beginning subordinate phase; Finishing temperature is 800 ℃; The steel plate speed of cooling is 45 ℃/S, and final temperature is 400 ℃, and air cooling is to room temperature after the water outlet.Tempering temperature is 500 ℃, the back air cooling of coming out of the stove.
Embodiment 4
Embodiment is with embodiment 1, and wherein Heating temperature is 1100 ℃, treats after the fs is rolling that temperature is rolling to 800 ℃ of beginning subordinate phase, and finishing temperature is 770 ℃, and the steel plate speed of cooling is 25 ℃/S, and final temperature is 350 ℃, and air cooling is to room temperature after the water outlet.Tempering temperature is 400 ℃, the back air cooling of coming out of the stove.
Embodiment 5
Smelt according to the chemical ingredients shown in the table 1, and be cast into continuously cast bloom or steel ingot, Heating temperature is 1180 ℃; Treat after fs is rolling that temperature is rolling to 790 ℃ of beginning subordinate phase, finishing temperature is 760 ℃, and the steel plate speed of cooling is 30 ℃/S; Final temperature is 250 ℃, and air cooling is to room temperature after the water outlet.Tempering temperature is 350 ℃, the back air cooling of coming out of the stove.
Embodiment 6
Smelt according to the chemical ingredients shown in the table 1, and be cast into continuously cast bloom or steel ingot, Heating temperature is 1200 ℃; Treat after fs is rolling that temperature is rolling to 820 ℃ of beginning subordinate phase, finishing temperature is 800 ℃, and the steel plate speed of cooling is 40 ℃/S; Final temperature is 200 ℃, and air cooling is to room temperature after the water outlet.Tempering temperature is 450 ℃, the back air cooling of coming out of the stove.
The composition of table 1 embodiment, wt%
Test Example 1
Ys 900MPa level bainite type high strength steel plate to embodiment of the invention 1-6 carries out Mechanics Performance Testing, and test result is seen table 2.
The mechanical property of the steel plate of table 2 embodiment of the invention 1-6
Can find out from table 1 and table 2, Pcm≤0.25% of the ys 900MPa level bainite type high strength steel plate that the present invention relates to, ys is all greater than 900MPa, and tensile strength is greater than 980MPa, Xia Shi ballistic work Akv (20 ℃)>=150J.
Test Example 2
Embodiment 2 and 5 is carried out microtexture research, and stereoscan photograph and transmission electron microscope photo are shown in Figure of description 1 and 2.Fig. 1 is the stereoscan photograph of embodiment 2 steel plates.As can be seen from the figure, carbide is not only separated out at superfine lath of bainite edge.Fig. 2 is the transmission electron microscope photo of embodiment 5.Lath of bainite is made up of meticulous nano level lath of bainite.The inner a lot of dislocations of nano level lath of bainite provide the dislocations strengthening effect.The superfine lath of bainite makes steel plate have high toughness at low temperatures.
Claims (8)
1. ys 900MPa level bainite type high strength steel plate; It is characterized in that; The chemical ingredients of percentage ratio meter is by weight: C:0.07～0.14%, Si:0.25～0.50%, Mn:1.70～2.20%, Cr:0.05～0.50%, Ni:0.20～0.50%, Nb:0.03～0.10%, V:0.03～0.10%, Ti:0.01～0.04%, Al:0.02～0.04%, B:0.0006～0.0025%, surplus are Fe and unavoidable impurities.
2. ys 900MPa level bainite type high strength steel plate as claimed in claim 1; It is characterized in that; Xia Shi ballistic work Akv under the ys>=900MPa of said steel plate, tensile strength>=980MPa ,-20 ℃ is greater than 150J, welding crack sensibility indices P cm≤0.25%.
3. according to claim 1 or claim 2 the method for manufacture of ys 900MPa level bainite type high strength steel plate comprises:
Smelting, casting, heating, rolling, cooling and tempering process;
In said heat-processed, Heating temperature is 1080～1280 ℃;
Rollingly be divided into the fs and subordinate phase is rolling, the said fs is rolling carries out more than recrystallization temperature, and rolling back of fs treats that on roller-way temperature is rolling to 770～860 ℃ of beginning subordinate phase, and the rolling finishing temperature of subordinate phase is 760～840 ℃.
4. the method for manufacture of ys 900MPa level bainite type high strength steel plate as claimed in claim 3 is characterized in that, in said process of cooling, steel plate with the speed of 12～45 ℃/S be cooled to≤400 ℃, air cooling after the water outlet.
5. like the method for manufacture of claim 3 or 4 described ys 900MPa level bainite type high strength steel plates, it is characterized in that in the said drawing process, tempering temperature is 350～500 ℃, air cooling after the tempering.
6. like the method for manufacture of the arbitrary described ys 900MPa level bainite type high strength steel plate of claim 3～5, it is characterized in that air cooling adopts stacking or cold bed cooling.
7. the ys 900MPa level bainite type high strength steel plate of making like the arbitrary described method of claim 3～6.
8. ys 900MPa level bainite type high strength steel plate as claimed in claim 7; It is characterized in that; Xia Shi ballistic work Akv under the ys>=900MPa, tensile strength>=980MPa ,-20 ℃ is greater than 150J, welding crack sensibility indices P cm≤0.25%.
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| CN102618800A (en) * | 2012-03-30 | 2012-08-01 | 宝山钢铁股份有限公司 | Steel plate with 115 MPa grade yield strength and manufacturing method thereof |
| CN104032237A (en) * | 2014-05-15 | 2014-09-10 | 合肥通用机械研究院 | Composite microalloyed high-strength steel forging with tensile strength of 700MPa and production method thereof |
| CN106917032A (en) * | 2015-12-25 | 2017-07-04 | 上海电气上重铸锻有限公司 | The method that reactor pressure vessel steels large thick-wall forging lifts low-temperature impact work |
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| CN102605252A (en) * | 2012-03-30 | 2012-07-25 | 宝山钢铁股份有限公司 | Steel plate with yield strength grade of 1030MPa and manufacturing method thereof |
| CN102618800A (en) * | 2012-03-30 | 2012-08-01 | 宝山钢铁股份有限公司 | Steel plate with 115 MPa grade yield strength and manufacturing method thereof |
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| CN106917032B (en) * | 2015-12-25 | 2018-11-02 | 上海电气上重铸锻有限公司 | The method that reactor pressure vessel steels large thick-wall forging promotes low-temperature impact work |
| CN114107785A (en) * | 2020-08-27 | 2022-03-01 | 宝山钢铁股份有限公司 | Gipa-grade bainite steel with ultrahigh yield ratio and manufacturing method thereof |
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| WO2023051668A1 (en) * | 2021-09-30 | 2023-04-06 | 宝山钢铁股份有限公司 | Bainite steel and preparation method therefor |
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