CN102618793A - Steel plate with yield strength of 960MPa and manufacturing method thereof - Google Patents
Steel plate with yield strength of 960MPa and manufacturing method thereof Download PDFInfo
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Abstract
The invention discloses a steel plate with yield strength of 960MPa, which comprises the following chemical components in weight percent: 0.07-0.11 percent of C, 0.10-0.50 percent of Si, 1.60-2.20 percent of Mn, not greater than 0.015 percent of P, not greater than 0.003 percent of S, 0.10-0.35 percent of Cr, 0.20-0.50 percent of Mo, 0.02-0.06 percent of Nb, 0.02-0.06 percent of V, 0.003-0.04 percent of Ti, 0.02-0.07 percent of Al, 0.0006-0.0025 percent of B and the balance of Fe and other inevitable impurities. The steel plate with the yield strength of 960MPa also meets the following relational expressions: C+Mn is not less than 1.853Si+2.078Cr+3.112Mo-1298.532B but is not greater than 5.891Si+4.115Cr+4.797Mo-398.532B, and ln(AEQ) is not less than 2.08 but is not greater than 3.41. The invention also discloses a manufacturing method for the steel plate. The tensile strength of the obtained steel plate is not less than 980MPa, the Charpy impact power Akv (-40 DEG C) is not less than 80J, and the carbon equivalent (CEV) is not greater than 0.58 percent. The steel plate is excellent in welding property.
Description
Technical field
The present invention relates to a kind of alloy and method of manufacture thereof, relate in particular to a kind of steel plate and method of manufacture thereof.
Background technology
High tensile steel plate is applied to engineering machinery such as structural parts such as crawler mounted crane, crane and truck.The maximization of engineering machinery has proposed to strengthen the demand of loss of weight to high tensile steel plate.Ys 960MPa grade high-strength steel plate has been widely used in the structural part of large-scale engineering machinery.The mechanical property and the carbon equivalent standard of ys 960MPa level high-strength steel have been stipulated among Europe superscript 10025-6:2004 and the GB GB/T16270-2009.Wherein, S960Q that stipulates in the Europe superscript and S960QL, ys >=960MPa, tensile strength 980～1150MPa, unit elongation >=10%, wherein S960Q satisfies-20 ℃ of impact of collision merit >=30J, and S960QL satisfies-40 ℃ of impact of collision merit >=30J.In addition, the carbon equivalent of S960Q and S960QL satisfies CEV≤0.82%, and its calculation formula is:
CEV＝C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15
Ys>=960MPa of GB GB/T16270-2009 regulation Q960E, tensile strength 980～1150MPa, unit elongation>=10% ,-40 ℃ of impact of collision merit>=27J, carbon equivalent satisfies CEV≤0.82%.
The manufacturing technology of high strength steel plate mainly is controlled rolling and controlled cooling+tempering (TMCP+T) and modified (Q+T).TMCP (Thermo-Mechanical Control Process) forms specific microtexture through two stage rolling temperature, draught and the process for cooling of control steel plate, to obtain the favorable mechanical performance.The fs of TMCP technology is during rolling deformation, processes such as austenite generation dynamic recrystallization, static recrystallize and dynamic recovery, refinement austenite crystal; In austenite, accumulated a large amount of dislocations during the subordinate phase distortion, the process for cooling of optimizing is adopted in rolling back, has formed tiny bainite or bainite+martensitic stucture.Steel plate behind the TMCP is through the reheat tempering, and carbonitride is separated out in the drawing process, and unlike dislocation is buried in oblivion, and the internal stress of improving steel plate distributes, and forms the microtexture with fine obdurability coupling.To be steel plate get into rolling technology to hardening and tempering process after heating austenite homogenizing, is rolled down to air cooling after the appointed thickness.The steel plate of air cooling after the room temperature gets into process furnace, and behind the assigned temperature austenitizing, quenching is cooled to room temperature.Steel plate after the quenching gets into tempering stove again and reheats assigned temperature, the air cooling of coming out of the stove behind the insulation certain hour.It is through the final martensitic stucture of quenching process refinement behind the austenitizing that hardening and tempering process is produced high tensile steel plate, through tempering process carbon is discharged from the supersaturation ferritic again, forms tiny carbide simultaneously, improves the internal stress and the low-temperature impact toughness of steel plate.
TMCP+T and Q+T explained hereafter high tensile steel plate all have its advantage separately, and wherein the TMCP+T technical process is short, can fully use alloying element to effects of phase transition; Q+T technology simple controllable, steel plate less to performance difference in length and breadth.Be shortened process, recent development direct quenching (DQ:direct quenching) and online thermal treatment (HOP:heat treatment online process).Direct quenching technology is directly to get into cooling facility for laminar flow after controlled rolling finishes to be cooled to room temperature; Online thermal treatment process is that the steel plate after the direct quenching gets into induction heater, is warming up to the appointment tempering temperature, the air cooling of coming out of the stove after insulation for some time with the rate of heating of 2～20 ℃/s.
With respect to traditional process for cooling, direct quenching technology stops that cold temperature is lower, and speed of cooling is very fast, can form the microtexture of refinement.Tradition tempering process temperature rise rate is slower, and soaking time is longer, and the carbide particle of formation is thick.Online thermal treatment process heats up with fast speeds, and the carbide that forms refinement is separated out, and improves the low-temperature impact toughness of steel plate.The residual austenite tissue that steel plate forms in the direct quenching process can part decompose in the HOP process, has finally formed the equally distributed residual austenite of disperse.Adopt the high tensile steel plate of DQ+HOP explained hereafter, have good obdurability.
Engineering machinery also must have good welding property with high tensile steel plate.Carbon equivalent is to weigh the important indicator of steel plate welding property.Carbon equivalent is low more, and the welding property of steel plate is good more.The ys 960MPa grade steel plate of stipulating among Europe superscript 10025-6 and the GB GB/T16270, carbon equivalent ce V all is not more than 0.82%.
Publication number is WO2000040764; Open day is on July 13rd, 2000; The patent that name is called " ULTRA-HIGH STRENGTH AUSAGED STEELS WITH EXCELLENT CRYOGENIC TEMPERATURE TOUGHNESS " discloses a kind of ultrahigh-strength steel plates; Its tensile strength is 830MPa, and contains more valuable alloying element Ni (>=1%).
Publication number is WO1999005335; Open day is on February 4th, 1999; The patent that name is called " ULTRA-HIGH STRENGTH, WELDABLE STEELS WITH EXCELLENT ULTRA-LOW TEMPERATURE TOUGHNESS " discloses a kind of ultrahigh-strength steel plates, and it adopts the method for two stage rolling and controlled chilling; And contain noble elements such as Ni, Cu, its steel plate tensile strength >=930MPa.
Summary of the invention
The object of the present invention is to provide a kind of ys 960MPa grade steel plate, this steel plate not only has higher intensity, also has good welding property.In addition, the present invention also aims to provide a kind of method of manufacture of this ys 960MPa grade steel plate.
The whole thinking of the present invention's design is to adopt the composition system of the low high Mn of C (carbon content is not more than 0.11%) (Mn content 1.60～2.20%); And the process system of controlled rolling and controlled cooling and prompt tempering; Through the optimization between the alloying element proportioning; Make full use of the raising effect of technology to the steel plate obdurability, manufacturing has the high strength steel plate than low-carbon-equivalent (CEV≤0.58%).Alloying element C and Mn are austenizer, add in the steel to improve the intensity of steel plate, but have best proportion relation between the content of C+Mn and other constituent content.For optimizing C, Mn and other constituent content, the relation that the present invention has set between C+Mn and other element obtains excellent performance to guarantee employing appropriate ingredients proportioning.Alloying equivalent AEQ has considered under the condition of suitable carbon equivalent, the influence of different-alloy element and interaction partners obdurability thereof.Constant term before the alloying element is relevant to the influence of obdurability with this alloying element.The alloying equivalent has been considered Cr and the compound interpolation of Mo, Nb and the V influence to the steel plate mechanical property simultaneously.Simultaneously, the alloying equivalent is crossed to hang down and then can't be produced the steel plate that satisfies mechanical property requirements, and the too high carbon equivalent that then can cause improves, and welding property worsens.
According to the foregoing invention purpose, the invention provides a kind of ys 960MPa grade steel plate, chemical ingredients quality per distribution ratio is:
C:0.07～0.11wt%; Si:0.10～0.50wt%; Mn:1.60～2.20wt%; P :≤0.015wt%; S :≤0.003wt%; Cr:0.10～0.35wt%; Mo:0.20～0.50wt%; Nb:0.02～0.06wt%; V:0.02～0.06wt%; Ti:0.003～0.04wt%; Al:0.02～0.07wt%; B:0.0006～0.0025wt%; Surplus is Fe and other unavoidable impurities;
Said ys 960MPa grade steel plate also should satisfy:
1.853Si+2.078Cr+3.112Mo-1298.532B≤C+Mn≤5.891Si+4.115Cr+4.797Mo-398.532B；
And
2.08≤ln(AEQ)≤3.41；
In the formula, AEQ is the alloying equivalent, and it satisfies:
AEQ＝25.66C+9.36Si+11.88Cr+17.95Mo+1152.21B+31.58×Cr×Mo+91.14×Nb×V。
The interpolation principle of chemical element is following among the present invention:
C:C content difference is to the phase transformation important influence of steel plate in process of cooling.The steel grade that C content is higher under same cooling conditions, form bainite or the higher tissue of martensite equal strength in the process of cooling easily, but C content is too high, then can form more crisp tissue, reduces the low-temperature impact toughness of steel plate.In the drawing process, the higher steel plate of C content can form thicker carbide, thereby worsens the impact property of steel plate.On the other hand, C content is too low, forms the lower tissue of ferritic equal strength easily.For reaching ys 960MPa, tensile strength 980MPa, comprehensive several respects factor considers that the present invention is controlled at C content in 0.07～0.11wt% scope.
The Si:Si element solid solution improves the intensity of steel plate in steel.The Si too high levels can suppress the formation of cementite, and higher Si content can worsen the welding property of steel plate simultaneously.Therefore, the Si content among the present invention is controlled to be 0.10～0.50wt%.
Mn:Mn is weak carbide forming element, is solid-solubilized in usually in the steel, plays the effect of solution strengthening.The high tensile steel plate that employing controlled rolling and controlled cooling mode is produced, Mn element suppress the diffusion control of sheet phase end face and grow up through crossing over diffuse interface dissipation free energy, form the sheet lath of bainite of refinement, thus over-all propertieies such as the intensity of raising steel plate and toughness.The Mn too high levels can cause the slab tearing tendency to strengthen, and in the slab production process, forms defectives such as lobe easily.Mn content is low then less to the contribution of intensity, therefore must add C element or other valuable alloying element such as Mo element etc. to guarantee the intensity of steel plate.Add the C element and can worsen the steel plate welding property, add other valuable alloying element and can improve the steel plate cost.Therefore, add the Mn element of 1.60～2.20wt% among the present invention, thereby help forming the bainite structure of refinement, make steel have good obdurability.
Cr:Cr element and Fe element form continuous solid solution, and form multiple carbide with the C element.Fe element in the Cr element instead cementite forms M
3C, and can form M
7C
3And M
23C
6The carbide that is solid-solubilized in Cr element and Cr in the steel can improve the intensity of steel plate.Cr content increases, and can form thicker carbide, thereby worsens the impact property of steel plate.The Cr that adds 0.10～0.35wt% among the present invention is to guarantee the intensity and the ballistic work of steel plate.
The Mo:Mo element is solid-solubilized in the steel when austenitizing, finally organizes through suppressing the refinement of diffuse interface motion realization in the process of cooling.The free energy that the Mo element dissipates to the diffuse interface effect of dragging is 3 times of Mn element approximately, therefore adds the Mo element and can suppress sheet phase end face and grow up, and forms the bainite or the bainite+martensitic stucture of refinement.The Mo element is valuable alloying element simultaneously, for guaranteeing plate property and cost, adds the mechanical property of the Mo element of 0.20～0.50wt% with the assurance steel plate among the present invention, and has both the market competitiveness.
Nb: steel plate can form a large amount of defectives such as dislocation in the operation of rolling.Recrystallize takes place in austenite under the effect of defective ability.Recrystallization process comprises the forming core and the growth process of the new crystal grain of austenite.The Nb element is through suppressing the recrystallization temperature that the motion of austenite interface improves steel plate.Add a certain amount of Nb, can realize two stage rolling, promptly non-recrystallization zone lesser temps is rolling to improve the inner dislocation desity of austenite, in process of cooling subsequently, forms the tissue of refinement.The higher meeting of Nb content forms thicker NbC and separates out in drawing process, thereby reduces the low-temperature impact work of steel plate.Therefore, add 0.02～0.06wt%Nb among the present invention with control steel plate microtexture and mechanical property.
V:V is a ferritisey, dwindles the austenitic area strongly.High temperature dissolves in the hardening capacity that V element in the austenite can increase steel.The carbide V of V element in the steel
4C
3More stable, can suppress that crystal boundary moves and grain growth.V element and Cu element all have been the precipitation strength effect in steel, but relative Cu element, only need to add the V element of minute quantity, can reach equal precipitation strength effect.In addition, the Cu element causes grain-boundary crack easily in steel, thereby must adding reaches the Ni element of its half content at least, just can avoid crackle, and the Ni element is very expensive alloying element equally.Therefore, can reduce the manufacturing cost of steel significantly with V element replaced C u element.Therefore, the V element that adds 0.02～0.06wt% among the present invention is to guarantee that steel plate has higher yield strength after tempering.
The B:B element is added on the hardening capacity that can improve steel plate in the steel, forms bainite or martensitic stucture.When B content was higher, the B atom can be in the crystal boundary enrichment, reduced the crystal boundary bound energy, thereby when receiving shock action, can take place along the crystalline substance fracture of dissociating.Therefore, the add-on of B element is 0.0006～0.0025wt% among the present invention.
The Al:Al element forms tiny AlN and separates out when high temperature, when slab heating austenitizing, suppress austenite crystal and grow up, and reaches the austenite crystal grain thinning, improves steel flexible purpose at low temperatures.The Al too high levels can cause the oxide compound of bigger Al to form, and reduces the low temperature impact properties and flaw detection performance of steel plate.Therefore, add the Al crystal grain thinning of 0.02～0.07wt% among the present invention, with the toughness that improves steel plate and guarantee its welding property.
Ti:Ti and N form TiN when high temperature, during slab heating austenitizing, TiN can suppress austenite crystal and grow up.Ti and C are at the interval TiC that forms of lesser temps, and tiny TiC particle helps improving the low temperature impact properties of steel plate.The Ti too high levels then can form thick square TiN and separate out, and steel plate stress when stressed is concentrated near the TiN particle, and the forming core that the becomes tiny crack source of growing up reduces the fatigue property of steel plate.Comprehensive Ti element is to the influence of mechanical property and fatigue property, and the Ti content among the present invention is controlled in 0.003～0.04wt% scope.
For optimizing C, Mn and other constituent content, the relation that the present invention has set between C+Mn and other element obtains excellent performance to guarantee employing appropriate ingredients proportioning.Alloying equivalent AEQ has considered under the condition of suitable carbon equivalent, the influence of different-alloy element and interaction partners obdurability thereof.Constant term before the alloying element is relevant to the influence of obdurability with this alloying element.The alloying equivalent has been considered Cr and the compound interpolation of Mo, Nb and the V influence to the steel plate mechanical property simultaneously.Simultaneously, the alloying equivalent is crossed to hang down and then can't be produced the steel plate that satisfies mechanical property requirements, and the too high carbon equivalent that then can cause improves, and welding property worsens.
In addition, in order to realize the object of the invention, the present invention also provides a kind of method of manufacture of ys 960MPa grade steel plate, and it comprises the following steps:
(1) smelts;
(2) casting;
(3) heating: steel billet is heated to after core temperature reaches 1050～1280 ℃, more than the insulation 15min;
(4) rolling:
A) fs: to be higher than recrystallization temperature steel billet is rolled, after the rolling completion, steel billet is placed in treats temperature on the roller-way;
B) subordinate phase: when steel billet was treated temperature to 760～850 ℃, the beginning subordinate phase was rolling, and its finishing temperature is 740～830 ℃;
The present invention adopts two stages controlled rolling technology.Rolling temperature of fs is on steel plate recrystallization temperature, and recrystallization process can take place operation of rolling light plate.Forming core growth process through austenite recrystallization crystal grain has reduced grain-size.Fs rolling back intermediate blank is treated temperature to 760～850 ℃, and it is rolling to begin to carry out subordinate phase.Subordinate phase is rolling under the recrystallization temperature of steel plate, and finishing temperature is 740～830 ℃.Rolling the making of cold zone added up a large amount of dislocations in the austenite, carbonitride fault on the throne is separated out, pinning the motion of dislocation.In follow-up process of cooling, bainite forms tiny bainite lamella at dislocation and fault location forming core, and bainite sheet interlayer has a spot of horse constituent element difficult to understand.The bainite structure of refinement and tiny carbide are separated out and are helped steel plate obdurability coupling.
(5) cooling: the speed with 12～45 ℃/s is cooled to steel plate≤and 350 ℃;
Steel plate gets into refrigerating unit after controlled rolling, speed of cooling is 12～45 ℃/s, stops cold temperature and is≤350 ℃.Rolling deformation contains the austenite of a large amount of dislocations, when cooling off fast in lesser temps generation bainite transformation.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.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 the austenite that does not change forms small and dispersed is distributed on the bainite matrix, thereby has improved the intensity and the toughness of steel plate.
(6) online tempering heat treatment: the speed with 3～15 ℃/s is warming up to 470～550 ℃ of tempering temperatures with steel plate, behind insulation 5～90s, and air cooling.
Steel plate cooling of the present invention back gets into the tempering heat treatment stove of online induction heating, and temperature rise rate is 3～15 ℃/s, is warming up to 470～550 ℃ of tempering temperatures, insulation 5～90s, air cooling after the tempering.Usually the temperature rise rate of tempering stove is 0.1～0.3 ℃/s, and the temperature rise rate of induction heating tempering stove is 3～15 ℃/s, than the high 1-2 one magnitude of temperature rise rate of common tempering stove.In the prompt tempering process, the motivating force that carbonitride is separated out is bigger, and the carbonitride of therefore separating out is tiny.Online HTFX tempering time is shorter, and soaking time is 5～90s, thereby improves the production efficiency of steel plate.Traditional tempering process light plate operations such as cooling that roll off the production line have been avoided in online tempering, thereby shorten the production cycle, reduce the production cost of steel plate.The present invention is preferred, and tempering temperature is 470～550 ℃, consider that strengthening effect and unlike dislocation that carbonitride is separated out buries in oblivion the bating effect that causes, thereby guarantee that steel plate ys in drawing process is significantly improved, and that tensile strength descends is not obvious.
In conjunction with steel grades of the present invention and ME, the steel billet of composition system according to the invention is at 1050～1280 ℃ of following austenitizings, and the carbonitride of Nb and V can be partially dissolved in the austenite, in the operation of rolling subsequently, can form tiny carbonitride.Heating temperature is low can to cause that the carbonitride of Nb and V dissolves insufficient in the austenite; The higher meeting of Heating temperature causes austenite crystal thick, reduces the steel plate ballistic work.The rolling beginning temperature of subordinate phase is 760～850 ℃, and finishing temperature is 740～830 ℃.Lower rolling temperature is interval, can form the austenite that contains more dislocation, the final bainite structure of refinement, the intensity and the low temperature impact properties of raising steel plate.Steel plate with the speed of 12～45 ℃/s be cooled to≤350 ℃.Alloying element C, Mn and Mo can suppress to spread phase transformation; Adopt very fast speed of cooling to stop cold temperature and make austenitic transformation become lath of bainite or the bainite+martensite 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 present invention with lower.Steel plate according to the invention stops need getting into online tempering heat treatment after cold, and temperature rise rate is 3～15 ℃/s, is warming up to 470～550 ℃ of tempering temperatures, insulation 5～90s, air cooling after the tempering.Temperature rise rate and short soaking time can make the carbonitride of tiny V or the carbide of Cr separate out faster, help improving the low-temperature impact toughness of steel plate.
The present invention is through optimization design composition system; Adopt online thermal treatment process; Can produce the ys 960MPa level high strength steel plate of carbon equivalent ce V≤0.58%; Far below what stipulate among Europe superscript 10025-6:2004 and the GB GB/T16270:2009, the carbon equivalent ce V of ys 960MPa grade steel plate is≤0.82%.
Preferably, in the method for manufacture of above-mentioned ys 960MPa grade steel plate, air cooling adopts the cold bed cooling.
Adopt technical scheme of the present invention to have the following advantages:
(1) ys>=960MPa of ys 960MPa grade steel plate of the present invention, tensile strength>=980MPa, Xia Shi ballistic work Akv (40 ℃)>=80J, carbon equivalent ce V≤0.58% has good welding property;
(2) method of manufacture of ys 960MPa grade steel plate of the present invention adopts controlled rolling, controlled chilling and online tempering heat treatment process, and technical process is short, thereby has practiced thrift the steel plate production cost;
(3) because composition and the technological design of ys 960MPa grade steel plate of the present invention is reasonable, and from implementation result, process system is looser, can be equipped with induction heater in, stably manufactured on the Plate Steel product line.
Description of drawings
Fig. 1 is the optical microscope photograph of ys 960MPa grade steel plate of the present invention under a kind of embodiment.
Embodiment
Embodiment 1-6
The concrete steps of making ys 960MPa grade steel plate of the present invention are (each steel grade chemical ingredients is seen table 1 among this case embodiment 1-6) as follows:
(1) smelts: adopt vacuum induction furnace, converter or electrosmelting, smelt the back and handle through the refining and the degassing.It should be noted that to smelt to include but are not limited to above-mentioned smelting process and treatment process, this case embodiment adopts vacuum induction furnace smelting, and chemical spectroscopy is measured the ultimate constituent;
(2) casting: adopt modes such as vertical continuous casting, vertical bending type continuous casting, arc continuous casting, die casting, directional freeze or esr.It should be noted that casting includes but are not limited to above-mentioned casting mode, this case embodiment adopts the die casting mode to cast in the ingot mold of anti-the material, and the casting superheating temperature is 25 ± 20 ℃;
(3) heating: steel billet is heated to after core temperature reaches 1050～1280 ℃, more than the insulation 15min;
(4) rolling:
A) fs: to be higher than recrystallization temperature steel billet is rolled, after the rolling completion, steel billet is placed in treats temperature on the roller-way;
B) subordinate phase: when steel billet was treated temperature to 760～850 ℃, the beginning subordinate phase was rolling, and its finishing temperature is 740～830 ℃;
(5) cooling: the speed with 12～45 ℃/s is cooled to steel plate≤and 350 ℃;
(6) online tempering heat treatment: the speed with 3～15 ℃/s is warming up to 470～550 ℃ of tempering temperatures with steel plate, behind insulation 5～90s, and the cold bed cooling.
(surplus is Fe and other unavoidable impurities to table 1., wt%)
The detailed process parameter of each step is referring to table 2 among this case embodiment 1-6.
Table 2.
Table 3 has been listed the mechanical property of this case embodiment 1-6.
Table 3.
| Embodiment | Ys, MPa | Tensile strength, MPa | Unit elongation, % | -40 ℃ of impact of collision merits, J | CEV |
| 1 | ?1010 | ?1070 | 14 | 152 | 0.56 |
| 2 | ?1005 | ?1070 | 13 | 125 | 0.56 |
| 3 | ?980 | ?1020 | 13 | 121 | 0.54 |
| 4 | 985 | 1050 | 13 | 132 | 0.55 |
| 5 | 975 | 1010 | 14 | 118 | 0.52 |
| 6 | 1005 | 1065 | 13 | 105 | 0.55 |
Can find out from table 3, the ys of this case embodiment 1-6 all>=960MPa, tensile strength all>=980MPa, Xia Shi ballistic work Akv (40 ℃) all>=80J, carbon equivalent ce V is all≤0.58%.
Fig. 1 has shown the microtexture of ys 960MPa grade steel plate among the embodiment 2.As shown in Figure 1, the microtexture of ys 960MPa grade steel plate is the bainite or the bainite+martensitic stucture of refinement among the embodiment 2.
Be noted that above enumerate be merely specific embodiment of the present invention, obviously the invention is not restricted to above embodiment, many similar variations are arranged thereupon.If those skilled in the art all should belong to protection scope of the present invention from all distortion that content disclosed by the invention directly derives or associates.
Claims (3)
1. a ys 960MPa grade steel plate is characterized in that, chemical ingredients quality per distribution ratio is: C:0.07～0.11wt%; Si:0.10～0.50wt%; Mn:1.60～2.20wt%; P :≤0.015wt%; S :≤0.003wt%; Cr:0.10～0.35wt%; Mo:0.20～0.50wt%; Nb:0.02～0.06wt%; V:0.02～0.06wt%; Ti:0.003～0.04wt%; Al:0.02～0.07wt%; B:0.0006～0.0025wt%; Surplus is Fe and other unavoidable impurities;
Said ys 960MPa grade steel plate also should satisfy:
1.853Si+2.078Cr+3.112Mo-1298.532B≤C+Mn≤5.891Si+4.115Cr+4.797Mo-398.532B；
And
2.08≤ln(AEQ)≤3.41；
In the formula, AEQ is the alloying equivalent, and it satisfies:
AEQ＝25.66C+9.36Si+11.88Cr+17.95Mo+1152.21B+31.58×Cr×Mo+91.14×Nb×V。
2. the method for manufacture of ys 960MPa grade steel plate as claimed in claim 1 is characterized in that, comprises the following steps:
(1) smelts;
(2) casting;
(3) heating: steel billet is heated to core temperature and reaches 1050～1280 ℃;
(4) rolling:
A) fs: to be higher than recrystallization temperature steel billet is rolled, after the rolling completion, steel billet is placed in treats temperature on the roller-way;
B) subordinate phase: when steel billet was treated temperature to 760～850 ℃, the beginning subordinate phase was rolling, and its finishing temperature is 740～830 ℃;
(5) cooling: the speed with 12～45 ℃/s is cooled to steel plate≤and 350 ℃;
(6) online tempering heat treatment: the speed with 3～15 ℃/s is warming up to 470～550 ℃ of tempering temperatures with steel plate, behind insulation 5～90s, and air cooling.
3. the method for manufacture of ys 960MPa grade steel plate as claimed in claim 2 is characterized in that, said air cooling adopts the cold bed cooling.
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Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102851604A (en) * | 2012-09-22 | 2013-01-02 | 内蒙古包钢钢联股份有限公司 | Production method of high-strength steel plate with yield strength of 690MPa |
| CN102888565A (en) * | 2012-09-22 | 2013-01-23 | 内蒙古包钢钢联股份有限公司 | High-strength steel plate with yield strength at 690MPa level and manufacture method thereof |
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| CN106319350A (en) * | 2016-11-30 | 2017-01-11 | 湖南华菱涟源钢铁有限公司 | Rolling and heat treatment production method of high-strength steel 900MPa-grade in yield strength |
| CN109136737A (en) * | 2018-06-20 | 2019-01-04 | 宝山钢铁股份有限公司 | A kind of tensile strength 1100MPa grades of ultra-high strength and toughness steel and its manufacturing method |
| CN115298342A (en) * | 2020-03-19 | 2022-11-04 | 日本制铁株式会社 | Steel plate |
| CN115298342B (en) * | 2020-03-19 | 2023-11-17 | 日本制铁株式会社 | steel plate |
| CN115433872A (en) * | 2022-08-29 | 2022-12-06 | 包头钢铁（集团）有限责任公司 | Steel with yield strength of 800MPa grade for rare earth engineering machinery and preparation method thereof |
| CN115433872B (en) * | 2022-08-29 | 2024-01-30 | 包头钢铁（集团）有限责任公司 | Steel with yield strength of 800MPa grade for rare earth engineering machinery and preparation method thereof |
| CN116640998A (en) * | 2023-06-20 | 2023-08-25 | 南京钢铁股份有限公司 | Steel Q550GJ steel plate for high-rise building and manufacturing method thereof |
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