CN102618793B - 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 manufacture method thereof, relate in particular to a kind of steel plate and manufacture method thereof.
Background technology
High tensile steel plate is applied to engineering machinery such as the structural parts such as crawler mounted crane, crane and truckmounted concrete pump.The maximization of engineering machinery has proposed to strengthen the demand of loss of weight to high tensile steel plate.Yield strength 960MPa grade high-strength steel plate has been widely used in the structural part of large-scale engineering machinery.Mechanical property and the carbon equivalent standard of yield strength 960MPa level high-strength steel in Europe superscript 10025-6:2004 and GB GB/T16270-2009, have been stipulated.Wherein, the S960Q that stipulates in Europe superscript and S960QL, yield strength >=960MPa, tensile strength 980～1150MPa, unit elongation >=10%, wherein S960Q meets-20 ℃ of impact of collision merit >=30J, and S960QL meets-40 ℃ of impact of collision merit >=30J.In addition, the carbon equivalent of S960Q and S960QL meets CEV≤0.82%, and its calculation formula is:
CEV＝C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15
Yield strength >=960MPa of GB GB/T16270-2009 regulation Q960E, tensile strength 980～1150MPa, unit elongation >=10% ,-40 ℃ of impact of collision merit >=27J, carbon equivalent meets CEV≤0.82%.
The manufacturing technology of high strength steel plate is mainly controlled rolling and controlled cooling+tempering (TMCP+T) and modified (Q+T).TMCP (Thermo-Mechanical Control Process), by controlling two stage rolling temperature, draught and the process for cooling of steel plate, forms specific microtexture, to obtain good mechanical property.The first stage of TMCP technique is during rolling deformation, the processes such as austenite generation dynamic recrystallization, Static Recrystallization and dynamic recovery, refinement austenite crystal; During the subordinate phase distortion, in austenite, accumulate a large amount of dislocations, after rolling, adopted the process for cooling of optimizing, formed tiny bainite or bainite+martensitic stucture.Steel plate process after TMCP reheats tempering, Carbonitride Precipitation in 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 enter rolling technology to hardening and tempering process after heating austenite homogenizing, is rolled down to air cooling after appointed thickness.Air cooling enters process furnace to the steel plate after room temperature, after the assigned temperature austenitizing, quenches and is cooled to room temperature.Steel plate after quenching enters tempering stove again and reheats assigned temperature, the air cooling of coming out of the stove after the insulation certain hour.It is by the final martensitic stucture of quenching process refinement after austenitizing that hardening and tempering process is produced high tensile steel plate, then makes carbon from the supersaturation ferrite, discharging through tempering process, forms simultaneously tiny carbide, improves 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 apply the impact of alloying element on phase transformation; Q+T technique is simply controlled, and the vertical lateral performance difference of steel plate is less.For shortened process, recent development direct quenching (DQ:direct quenching) and online thermal treatment (HOP:heat treatment online process).Direct quenching technique is after controlled rolling finishes, directly to enter cooling facility for laminar flow to be cooled to room temperature; Online thermal treatment process is that the steel plate after direct quenching enters induction heater, with the rate of heating of 2～20 ℃/s, is warming up to the appointment tempering temperature, the air cooling of coming out of the stove after insulation for some time.
With respect to traditional process for cooling, direct quenching technique 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, with speed intensification faster, forms the Carbide Precipitation of refinement, improves the low-temperature impact toughness of steel plate.Steel plate forms in the direct quenching process residual austenite body tissue, the meeting decomposed, finally formed the equally distributed residual austenite of disperse in the HOP process.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 Plate Welding performance.Carbon equivalent is lower, and the welding property of steel plate is better.The yield strength 960MPa grade steel plate of stipulating in Europe superscript 10025-6 and 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 precious alloy 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, it adopts two stage rolling and controls cooling method, and contain the 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 yield strength 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 manufacture method of this yield strength 960MPa grade steel plate.
The Integral Thought of the present invention's design is the composition system that adopts 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, by the optimization between the alloying element proportioning, take full advantage of the raising effect of technique to the steel plate obdurability, manufacture and have than the high strength steel plate of low-carbon-equivalent (CEV≤0.58%).Alloying element C and Mn are austenizer, add the intensity that can improve steel plate in steel, 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 the suitable composition proportion of employing.Alloyingequivalent AEQ has considered under the condition of suitable carbon equivalent, different-alloy element and interaction thereof the impact on obdurability.Constant term before alloying element is relevant on the impact of obdurability to this alloying element.Alloyingequivalent has been considered Cr and Mo, Nb and the compound interpolation of the V impact on mechanical property of steel plate simultaneously.Simultaneously, alloyingequivalent is too low can't produce the steel plate that meets mechanical property requirements, and the too high carbon equivalent that can cause improves, and welding property worsens.
According to the foregoing invention purpose, the invention provides a kind of yield strength 960MPa grade steel plate, chemical composition 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 inevitable impurity;
Described yield strength 960MPa grade steel plate also should meet:
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 formula, AEQ is alloyingequivalent, and it meets:
AEQ＝25.66C+9.36Si+11.88Cr+17.95Mo+1152.21B+31.58×Cr×Mo+91.14×Nb×V。
In the present invention, the interpolation principle of chemical element is as follows:
C:C content difference has important impact on steel plate in the phase transformation of process of cooling.The steel grade that C content is higher, under same cooling conditions, in process of cooling, easily form bainite or the higher tissue of martensite equal strength, but C content is too high, can form more crisp tissue, reduces the low-temperature impact toughness of steel plate.In drawing process, the steel plate that C content is higher can form thicker carbide, thereby worsens the impact property of steel plate.On the other hand, C content is too low, easily forms the tissue that the ferrite equal strength is lower.For reaching yield strength 960MPa, tensile strength 980MPa, comprehensive several respects factor consideration, the present invention is controlled at C content in 0.07～0.11wt% scope.
The Si:Si element solid solution, in steel, improves the intensity of steel plate.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 in the present invention is controlled to be 0.10～0.50wt%.
Mn:Mn is weak carbide forming element, usually is solid-solubilized in steel, plays the effect of solution strengthening.The high tensile steel plate that employing controlled rolling and controlled cooling mode is produced, Mn element, by crossing over diffuse interface dissipation free energy, suppress the diffusion control of sheet phase end face and grow up, and form the sheet lath of bainite of refinement, thus the 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 easily in the slab production process, forms the defects such as lobe.Mn content is low less to the contribution of intensity, therefore must add C element or other precious alloy element such as Mo element etc. to guarantee the intensity of steel plate.Add the C element and can worsen the Plate Welding performance, add other precious alloy element and can improve the steel plate cost.Therefore, in the present invention, add the Mn element of 1.60～2.20wt%, thereby be conducive to form 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.The Fe element that the Cr element can replace in cementite forms M
3C, and can form M
7C
3And M
23C
6.The carbide that is solid-solubilized in Cr element in steel and Cr 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% in the present invention, to guarantee intensity and the ballistic work of steel plate.
The Mo:Mo element is solid-solubilized in steel when austenitizing in, in process of cooling, by suppressing the diffuse interface motion, realize that refinement finally organizes.The free energy that the Mo element dissipates to the diffuse interface effect of dragging is approximately 3 times of Mn element, therefore adds the Mo element and can suppress sheet phase end face and grow up, and forms bainite or the bainite+martensitic stucture of refinement.The Mo element is the precious alloy element simultaneously, for guaranteeing plate property and cost, in the present invention, adds the Mo element of 0.20～0.50wt% to guarantee the mechanical property of steel plate, and has both the market competitiveness.
Nb: steel plate can form a large amount of defects such as dislocation in the operation of rolling.Recrystallize occurs in austenite under the effect of defect energy.Recrystallization process comprises the nucleation and growth process of the new crystal grain of austenite.The Nb element improves the recrystallization temperature of steel plate by suppressing the Austenite Interfacial motion.Add a certain amount of Nb, can realize two stage rolling, i.e. non-recrystallization zone lesser temps rolling, to improve the inner dislocation desity of austenite, forms the tissue of refinement in process of cooling subsequently.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, in the present invention, add 0.02～0.06wt%Nb to control steel plate microtexture and mechanical property.
V:V is ferritisey, strongly dwindles austenitic area.High temperature dissolves in the hardening capacity that V element in austenite can increase steel.The carbide V of V element in steel
4C
3More stable, can suppress that crystal boundary moves and grain growth.V element and Cu element have been all the precipitation strength effects in steel, but relative Cu element, only need add the V element of minute quantity, can reach equal precipitation strength effect.In addition, the Cu element easily causes grain-boundary crack in steel, thereby must add the Ni element that reaches at least its half content, the ability Crack prevention, and the Ni element is very expensive alloying element equally.Therefore, with V element, replace the manufacturing cost that the Cu element can the decrease steel.Therefore, in the present invention, add the V element of 0.02～0.06wt% 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 steel, forms bainite or martensitic stucture.When B content was higher, the B atom can be in the crystal boundary enrichment, reduced crystal boundary in conjunction with energy, thereby when being subject to shock action, can occur along the crystalline substance fracture of dissociating.Therefore, in the present invention, the add-on of B element is 0.0006～0.0025wt%.
The Al:Al element forms tiny AlN and separates out when high temperature, when the heating of plate blank austenitizing, suppress Austenite Grain Growth, reaches the purpose of austenite crystal grain thinning, raising steel toughness at low temperatures.The Al too high levels can cause the oxide compound of larger Al to form, and reduces low temperature impact properties and the detection capability of steel plate.Therefore, in the present invention, add the Al crystal grain thinning of 0.02～0.07wt%, with the toughness that improves steel plate and guarantee its welding property.
Ti:Ti and N form TiN when high temperature, during the heating of plate blank austenitizing, TiN can suppress Austenite Grain Growth.Ti and C are at the interval TiC that forms of lesser temps, and tiny TiC particle is conducive to improve the low temperature impact properties of steel plate.The Ti too high levels, 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.The impact of comprehensive Ti element on mechanical property and fatigue property, the Ti content in 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 the suitable composition proportion of employing.Alloyingequivalent AEQ has considered under the condition of suitable carbon equivalent, different-alloy element and interaction thereof the impact on obdurability.Constant term before alloying element is relevant on the impact of obdurability to this alloying element.Alloyingequivalent has been considered Cr and Mo, Nb and the compound interpolation of the V impact on mechanical property of steel plate simultaneously.Simultaneously, alloyingequivalent is too low can't produce the steel plate that meets mechanical property requirements, and the too high carbon equivalent that can cause improves, and welding property worsens.
In addition, in order to realize purpose of the present invention, the present invention also provides a kind of manufacture method of yield strength 960MPa grade steel plate, and it comprises the following steps:
(1) smelt;
(2) casting;
(3) heating: after heating steel billet to core temperature reaches 1050～1280 ℃, more than insulation 15min;
(4) rolling:
A) first stage: higher than recrystallization temperature, steel billet is rolled, after rolling completes, steel billet is placed on roller-way and treats temperature;
B) subordinate phase: when steel billet during to 760～850 ℃, starts the subordinate phase rolling until temperature, its finishing temperature is 740～830 ℃;
The present invention adopts the two-stage control rolling technology.The temperature of first stage rolling is on steel plate recrystallization temperature, and recrystallization process can occur operation of rolling light plate.Forming core growth process by austenite recrystallization crystal grain, reduced grain-size.After the first stage rolling, intermediate blank treats that temperature, to 760～850 ℃, starts to carry out the subordinate phase rolling.The subordinate phase rolling is under the recrystallization temperature of steel plate, and finishing temperature is 740～830 ℃.The cold zone rolling makes in austenite to have added up a large amount of dislocations, and carbonitride fault in place is separated out, pinning the motion of dislocation.In follow-up process of cooling, bainite, at dislocation and fault location forming core, forms tiny bainite lamella, and bainite sheet interlayer has a small amount of horse constituent element difficult to understand.The bainite structure of refinement and tiny Carbide Precipitation are conducive to steel plate obdurability coupling.
(5) cooling: the speed with 12～45 ℃/s is cooled to steel plate≤and 350 ℃;
Steel plate enters 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, quick when cooling in lesser temps generation bainite transformation.Speed of cooling makes austenite have larger condensate depression faster, even bainite transformation has larger nuclear driving 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 cold temperature condition faster, bainite forms with very high nucleation rate and slower coarsening rate, the MA constituent element of the austenitic formation small and dispersed that does not change is distributed on the bainite matrix, thereby has improved 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 by steel plate, after insulation 5～90s, and air cooling.
After steel plate of the present invention is cooling, enter the tempering heat treatment stove of online induction heating, temperature rise rate is 3～15 ℃/s, is warming up to 470～550 ℃ of tempering temperatures, insulation 5～90s, air cooling after 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 of the temperature rise rate of a common tempering stove order of magnitude.In the prompt tempering process, the motivating force of Carbonitride Precipitation is larger, and the carbonitride of therefore separating out is tiny.Online equipment for Heating Processing tempering time is shorter, and soaking time is 5～90s, thereby improves the production efficiency of steel plate.Traditional tempering process light plate operation such as cooling that rolls off the production line has been avoided in online tempering, thereby shortens the production cycle, reduces the production cost of steel plate.The present invention is preferred, and tempering temperature is 470～550 ℃, consider that the strengthening effect of Carbonitride Precipitation and unlike dislocation buries in oblivion the bating effect that causes, thereby guarantee that steel plate yield strength in drawing process is significantly improved, and that tensile strength descends is not obvious.
In conjunction with steel grades of the present invention and manufacturing process, the steel billet of composition system of the present invention is at 1050～1280 ℃ of lower austenitizings, and the carbonitride of Nb and V can be partially dissolved in austenite, in the operation of rolling subsequently, can form tiny carbonitride.Heating temperature is low can cause the carbonitride of Nb and V in austenite to dissolve insufficient; The higher meeting of Heating temperature causes austenite crystal thick, reduces the steel plate ballistic work.It is 760～850 ℃ that the subordinate phase rolling starts temperature, and finishing temperature is 740～830 ℃.Lower rolling temperature interval, can form the austenite that contains more dislocation, the final bainite structure of refinement, 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 in the present invention very fast speed of cooling to stop cold temperature and make austenitic transformation become the lath of bainite of refinement or bainite+martensite and along the horse of lath interface distributions constituent element difficult to understand, this type of tissue has the characteristics such as high-strong toughness with lower.Steel plate of the present invention stops after cold to need to enter online tempering heat treatment, and temperature rise rate is 3～15 ℃/s, is warming up to 470～550 ℃ of tempering temperatures, insulation 5～90s, air cooling after tempering.Temperature rise rate and shorter soaking time, can make the carbonitride of tiny V or the Carbide Precipitation of Cr faster, is conducive to improve the low-temperature impact toughness of steel plate.
The present invention is by optimization design composition system, adopt online thermal treatment process, can produce the yield strength 960MPa level high strength steel plate of carbon equivalent ce V≤0.58%, far below what in Europe superscript 10025-6:2004 and GB GB/T16270:2009, stipulate, the carbon equivalent ce V of yield strength 960MPa grade steel plate is≤0.82%.
Preferably, in the manufacture method of above-mentioned yield strength 960MPa grade steel plate, air cooling adopts cold bed cooling.
The employing technical solutions according to the invention have the following advantages:
(1) yield strength >=960MPa of yield strength 960MPa grade steel plate of the present invention, tensile strength >=980MPa, Xia Shi Impact energy Ak v (40 ℃) >=80J, carbon equivalent ce V≤0.58%, have good welding property;
(2) manufacture method of yield strength 960MPa grade steel plate of the present invention adopts controlled rolling, controls cooling and online tempering heat treatment process, and technical process is short, thereby has saved the cost of Plate Production;
(3) because composition and the technological design of yield strength 960MPa grade steel plate of the present invention are reasonable, from implementation result, process system is looser, can be equipped with induction heater in, Plate Steel produces stably manufactured on line.
The accompanying drawing explanation
Fig. 1 is the optical microscope photograph of yield strength 960MPa grade steel plate of the present invention under a kind of embodiment.
Embodiment
Embodiment 1-6
The concrete steps of manufacturing yield strength 960MPa grade steel plate of the present invention following (in this case embodiment 1-6, each steel grade chemical composition is in Table 1):
(1) smelt: adopt vacuum induction furnace, converter or electrosmelting, after smelting by refining and degassed processing.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 the 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: after heating steel billet to core temperature reaches 1050～1280 ℃, more than insulation 15min;
(4) rolling:
A) first stage: higher than recrystallization temperature, steel billet is rolled, after rolling completes, steel billet is placed on roller-way and treats temperature;
B) subordinate phase: when steel billet during to 760～850 ℃, starts the subordinate phase rolling until temperature, 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 by steel plate, and after insulation 5～90s, cold bed is cooling.
(surplus is Fe and other inevitable impurity to table 1., wt%)
In this case embodiment 1-6, the detailed process parameter of each step is referring to table 2.
Table 2.
Table 3 has been listed the mechanical property of this case embodiment 1-6.
Table 3.
| Embodiment | Yield strength, 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 |
As can be seen from Table 3, the yield strength of this case embodiment 1-6 all >=960MPa, tensile strength all >=980MPa, Xia Shi Impact energy Ak v (40 ℃) all >=80J, carbon equivalent ce V is all≤0.58%.
Fig. 1 has shown the microtexture of yield strength 960MPa grade steel plate in embodiment 2.As shown in Figure 1, in embodiment 2, the microtexture of yield strength 960MPa grade steel plate is bainite or the bainite+martensitic stucture of refinement.
Be noted that above enumerate only for specific embodiments of the invention, obviously the invention is not restricted to above embodiment, many similar variations are arranged thereupon.If those skilled in the art, from all distortion that content disclosed by the invention directly derives or associates, all should belong to protection scope of the present invention.
Claims (3)
1. a yield strength 960MPa grade steel plate, is characterized in that, the microtexture of described steel plate is bainite or the bainite+martensite of refinement, and its chemical composition 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 inevitable impurity;
Described yield strength 960MPa grade steel plate also should meet:
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 formula, AEQ is alloyingequivalent, and it meets:
AEQ＝25.66C+9.36Si+11.88Cr+17.95Mo+1152.21B+31.58×Cr×Mo+91.14×Nb×V。
2. the manufacture method of yield strength 960MPa grade steel plate as claimed in claim 1, is characterized in that, comprises the following steps:
(1) smelt;
(2) casting;
(3) heating: heating steel billet to core temperature reaches 1050～1280 ℃;
(4) rolling:
A) first stage: higher than recrystallization temperature, steel billet is rolled, after rolling completes, steel billet is placed on roller-way and treats temperature;
B) subordinate phase: when steel billet during to 760～850 ℃, starts the subordinate phase rolling until temperature, 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 by steel plate, after insulation 5～90s, and air cooling.
3. the manufacture method of yield strength 960MPa grade steel plate as claimed in claim 2, is characterized in that, described air cooling adopts cold bed cooling.
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| 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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