CN102605252A - Steel plate with yield strength grade of 1030MPa and manufacturing method thereof - Google Patents
Steel plate with yield strength grade of 1030MPa and manufacturing method thereof Download PDFInfo
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The invention discloses a steel plate with yield strength grade of 1030MPa, which comprises the chemical components in percentage by weight: 0.115-0.165% of C, 0.10-0.40% of Si, 0.80-2.00% of Mn, less than or equal to 0.015% of P, less than or equal to 0.03% of S, less than or equal to 0.70% of Cr, 0.30-0.80% of Mo, 0.20-1.00% of Ni, 0.01-0.06% of Nb, less than or equal to 0.03% of V, 0.003-0.04% of Ti, 0.02-0.07% of Al, 0.0006-0.0020% of B, and the balance of Fe and other inevitable impurities. The steel plate with yield strength grade of 1030MPa further meets the conditions that Mn is more than or equal to 7.01-30.13 C-7.58 Si-6.38 Mo-3.93 Cr-0.63 Ni and less than or equal to 42.73-30.62 C-11.25 Si-18.69 Mo-10.97 Cr-8.23Ni, and 1n(km) is more than or equal to 3.83 and less than or equal to 4.97. For the steel plate, the yield strength is more than or equal to 1030MPa, the tensile strength is more than or equal to 1100MPa, charpy impact energy Akv (minus 40 DEG C) is more than or equal to 60J, and the carbon equivalent CEV is less than or equal to 0.60%, so that the steel plate has excellent 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 widely used in the large-sized structural parts of engineering machinery, mining machinery and harbour machinery.Along with social demand and scientific-technical progress, the intensity of high tensile steel plate constantly increases, thereby alleviates the weight of equipment, realizes energy-saving and cost-reducing target.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.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; S960QL satisfies-40 ℃ of impact of collision merit>=30J in addition, and 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%.
Ys 1030MPa grade high-strength steel plate has wide practical use as the substitute products of ys 900/960MPa grade steel plate.At present domestic and international standard is not stipulated the mechanical property and the carbon equivalent of ys 1030MPa grade high-strength steel plate as yet.
The manufacturing technology of high strength steel plate mainly is controlled rolling and controlled cooling+tempering (TMCP+T) and quenching+tempering (Q+T).Adopt cooling controlling and rolling controlling process (TMCP:Thermo Mechanical Control Process) can through defect concentration in control austenite grain size, the austenite, carbonitride fault location separate out with process of cooling in the type etc. of phase transformation realize the purpose of organizational controls and Properties Control.Quenching+tempering process is to separate out etc. through the diffusion of carbon in the ferritic that contains supersaturation carbon after reheat austenitizing control austenite grain size, carbonitride dissolving, the tempering and carbonitride to realize organizational controls and Properties Control.Get into thermal treatment unit after the steel plate of above-mentioned two kinds of explained hereafter all need roll off the production line, quench or temper.About 0.1～0.3 ℃/s of the heating rate of prior heat treatment device, the generation carbonitride is separated out during tempering, dislocation desity reduces and the residual austenite decomposition course.Because tempering time is longer, the time of growing up that carbonitride is separated out is longer, so can form thicker precipitate after the tempering, reduces the low temperature impact properties of steel plate.
The online thermal treatment of recent development (HOP:heat treatment online process) technology is that steel plate direct induction heater that gets into behind controlled rolling and controlled chilling carries out tempering heat treatment.Electromagnetic induction heating furnace makes the temperature rise rate of steel plate with 2～20 ℃/s, is warming up to the appointment tempering temperature very soon, comes out of the stove after insulation for some time.Rapid heating can make carbonitride separate out has bigger forming core motivating force, and soaking time is shorter simultaneously, can form the carbide tissue of refinement.Residual austenite part in the rapid heating process is transformed into ferritic, forms the residual austenite tissue that disperse distributes.
Welding property is the important use properties of engineering machinery 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/T16270, carbon equivalent ce V all is not more than 0.82%.
Publication number is CN101497971; Open day is on August 5th, 2009; The Chinese patent that name is called " a kind of high-strength hardened and tempered steel and working method thereof " discloses a kind of high-strength hardened and tempered steel and working method thereof; The said steel plate of this patent adopts that roughing, finish rolling, control are cold, quenching furnance austenitizing, quenching press shrend and tempering stove tempering production technique, and the steel plate ys of production is more than or equal to 690MPa, and tensile strength is more than or equal to 770MPa.
Publication number is CN1786245; Open day is on June 14th, 2006; The Chinese patent that name is called " high tensile strength low carbon bainite thick steel plate and working method thereof " discloses a kind of high tensile strength low carbon bainite thick steel plate and working method thereof, and the said steel plate of this patent adopts TMCP+RPC+T technology can obtain the above level steel plate of tensile strength 900MPa.
Summary of the invention
The object of the present invention is to provide a kind of ys 1030MPa grade steel plate, this steel plate not only has higher intensity and toughness, also has good welding property.In addition, the present invention also aims to provide this kind ys 1030MPa method of manufacture of grade steel plate.
The principle of design of composition system of the present invention is in the related scope of composition, the low Mn of low high Mn of C or high C, and in conjunction with compositions such as Mo, Ni, Nb, B, suitably selectivity is added Cr or V, and wherein the Mn constituent content is confirmed through the addition of other element.Alloying element such as Si, Cr, Mo and Ni equal size increase, and then Mn content adjusts accordingly.Water malleableize coefficient is that C, Si, Mn, Mo, Cr, Ni and B element are to the tough sex comprehensive embodiment of back steel plate of quenching.Constant term coefficient before the alloying element content has embodied when quenching heat treatment, and different elements are to the influence degree of steel plate obdurability.
According to the foregoing invention purpose, the invention provides a kind of ys 1030MPa grade steel plate, its chemical ingredients quality per distribution ratio is:
C:0.115～0.165wt%; Si:0.10～0.40wt%; Mn:0.80～2.00wt%; P :≤0.015wt%; S :≤0.003wt%, Cr :≤0.70wt%; Mo:0.30～0.80wt%; Ni:0.20～1.00wt%; Nb:0.01～0.06wt%; V :≤0.03wt%; Ti:0.003～0.04wt%; A1:0.02～0.07wt%; B:0.0006～0.0020wt%; Surplus is Fe and other unavoidable impurities;
This ys 1030MPa grade steel plate also should satisfy:
7.01-30.13C-7.58Si-6.38Mo-3.93Cr-0.63Ni≤Mn≤
42.73-30.62C-11.25Si-18.69Mo-10.97Cr-8.23Ni；
And
3.83≤ln(km)≤4.97；
In the formula, km is a water malleableize coefficient, and it satisfies:
km＝33.15C+8.33Si+27.99Mn+58.62Mo+10.52Cr+15.41Ni+2512B。
The interpolation principle of chemical element is following among the present invention:
The C:C element adds in the steel, improves the hardening capacity of steel plate, forms higher low temperature bainite or the martensitic stucture of intensity, thereby improves the intensity of steel plate.C content is higher, can cause the steel plate low temperature impact properties to descend, and steel plate can take place when receiving shock action along the crystalline substance fracture of dissociating.For guaranteeing higher intensity and low-temperature impact toughness, C content of the present invention is controlled in 0.115～0.165wt% scope.
The increase of Si:Si content can make the welding crack sensibility of steel plate improve, and promptly increases steel plate produces cold crack after welding trend.Si is solid-solubilized in the steel, improves the intensity of steel plate.In conjunction with armor plate strength performance and welding property, the Si content among the present invention is controlled in 0.10～0.40wt% scope.
Mn: the Mn content in the steel increases, and can improve the tendency that slab produces longitudinal crack.C and the increase of Mn content can cause the slab segregation serious, reduce the steel plate internal soundness, also can in the controlled rolling and controlled cooling process, form the higher tissue of hardenability simultaneously, thereby reduce the low-temperature impact work of steel plate.Under the C content condition with higher,, can adopt lower Mn content for guaranteeing slab quality and steel plate mechanical property; C content is lower, can adopt higher Mn content to guarantee the obdurability of steel plate.In conjunction with the carbon content scope among the present invention, add the Mn element of 0.80～2.00wt% among the present invention, to form the bainite structure of refinement, make steel have good obdurability.
The Cr:Cr element can improve the hardening capacity of steel plate, forms the higher tissue of intensity.The Cr element can form different carbide in the drawing process with the C in the steel, is unfavorable for low temperature impact properties.In conjunction with other alloying element content among the present invention, Cr element add-on is no more than 0.70wt% in the steel, to guarantee the intensity and the ballistic work of steel plate.
The Mo:Mo element solid solution improves the intensity of steel plate through solution strengthening in steel.The Mo element can suppress to spread phase transformation, and refinement is finally organized, and improves the intensity of steel plate through refined crystalline strengthening.The Mo element improves the resistance to tempering of steel plate, expansion tempering platform, thus make steel plate tempering in awide temperature range obtain excellent performance.Mo content increases can improve the manufacturing cost of steel plate, so adds the Mo element of 0.30～0.80wt% among the present invention, with the mechanical property of assurance steel plate and suitable manufacturing cost.
The Nb:Nb element adds in the steel, improves steel plate recrystallization temperature, in conjunction with two stage controlled rolling process refine austenite crystal grain.The Nb element can form carbonitride in the online tempering heat treatment process, thereby improves the low-temperature impact toughness of steel plate.The higher meeting of Nb content causes steel plate in drawing process, to form thick carbonitride separating out, thereby worsens low-temperature impact toughness.Therefore, add the Nb element of 0.01～0.06wt% among the present invention, to obtain the good mechanical performance.
The Ni:Ni element adds in the steel, can reduce stacking fault energy, improves the low-temperature impact toughness of steel plate.The Ni element in steel, understands and Fe, Mn form face-centred cubic structure.Ni content increases, though the low-temperature impact work of steel plate can increase, the manufacturing cost of steel plate also can improve.Therefore, add the Ni element of 0.20～1.00wt% among the present invention, with the mechanical property that guarantees steel plate and have the market competitiveness.
The V:V element forms VC and separates out in steel, thus in drawing process, improve steel plate strength property.The V too high levels can form thick precipitate, thereby reduces the ballistic work of steel plate.Content in conjunction with other alloying element such as Mn, Mo, Cr is controlled at V content≤0.03wt% among the present invention, to guarantee that steel plate has higher yield strength after tempering.
The B:B element adds in the steel, can improve the hardening capacity of steel plate.After quickening cooling, steel plate can form the microtexture of refinement, thereby improves the mechanical property of steel plate.B content improves the low-temperature impact work that can reduce steel plate.Therefore, the add-on of B element is 0.0006～0.0020wt% among the present invention.
The Al:Al element adds in the steel as reductor, and the oxide compound of Al and nitride can be realized the effect of refine austenite crystal grain, but the Al too high levels then can form thick inclusion, reduces fatigue property, low-temperature impact toughness and the 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 combines with N in steel, when high temperature, forms TiN, and the content TiN then capable of using of control Ti separates out the inhibition austenite crystal and grows up, and avoids the thick mechanical property that influences steel plate of TiN particle simultaneously.Ti content among the present invention is controlled at 0.003～0.04wt%.
The principle of design of composition system of the present invention is in the related scope of composition, the low Mn of low high Mn of C or high C, and in conjunction with compositions such as Mo, Ni, Nb, B, suitably selectivity is added Cr or V, and wherein the Mn constituent content is confirmed through the addition of other element.Alloying element such as Si, Cr, Mo and Ni equal size increase, and then Mn content adjusts accordingly.Water malleableize coefficient is that C, Si, Mn, Mo, Cr, Ni and B element are to the tough sex comprehensive embodiment of back steel plate of quenching.Constant term coefficient before the alloying element content has embodied when quenching heat treatment, and different elements are to the influence degree of steel plate obdurability.
In addition, in order to realize the object of the invention, the present invention also provides a kind of method of manufacture of ys 1030MPa grade steel plate, and it comprises the following steps:
(1) smelts;
(2) casting;
(3) heating: steel billet is heated to core temperature and reaches 1050～1250 ℃;
(4) rolling:
A) fs: steel billet is rolled being higher than under the recrystallization temperature, 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 800～860 ℃, the beginning subordinate phase was rolling, and its finishing temperature is 780～840 ℃;
Steel plate adopts two stage rolling behind the heating austenitizing, rolling distortion of fs in the recrystallization zone, and rolling back intermediate blank is treated temperature to 800～860 ℃, it is rolling to begin to carry out subordinate phase.Subordinate phase is rolling below the recrystallization temperature of steel plate, and finishing temperature is 780～840 ℃.The subordinate phase rolling deformation fully provides the accumulation of defective in austenite, thereby for process of cooling forms thinning microstructure favourable original structure is provided.
(5) cooling: the speed with 15～45 ℃/s is cooled to steel plate≤and 300 ℃;
Steel plate gets into refrigerating unit after controlled rolling, speed of cooling is 15～45 ℃/s, stops cold temperature and is≤300 ℃.In process of cooling, can form supercooled austenite.Because speed of cooling is very fast, austenitic condensate depression is bigger, and bainite or martensitic phase have bigger forming core motivating force.Speed of cooling makes steel plate get into low-temperature region fast soon, and C atom and alloying element atomic diffusivity reduce, so steel plate forms tiny bainite or bainite+martensitic stucture.
(6) online tempering heat treatment: the speed with 3～15 ℃/s is warming up to 200～580 ℃ of tempering temperatures with steel plate, behind insulation 5～120s, and air cooling.
Steel plate cooling back gets into the tempering heat treatment stove of online induction heating, and 3～15 ℃/s of heat-up rate is warming up to 200～580 ℃ of tempering temperatures, insulation 5～120s, air cooling after the tempering.The temperature rise rate of conventional tempering stove is 0.1～0.3 ℃/s, and the temperature rise rate of steel plate of the present invention is 3～15 ℃/s.Online tempering process can form the horse constituent element difficult to understand that tiny carbonitride and disperse distribute, and improves the mechanical property of steel plate.Online thermal treatment process makes steel plate after rolling, cooling, directly carry out tempering, has shortened technical process and delivery cycle, thereby has reduced the production cost of steel plate.
In conjunction with steel grades of the present invention and ME, steel billet is at 1050～1250 ℃ of austenitizings, and the middle Ti of steel plate and the nitride of Al can hinder austenite grain boundary and grow up, and the carbonitride of Nb and V is partly dissolved.Can obtain the suitable austenite crystal of size at TR internal heating according to the invention, avoid austenite crystal thick, also can make Nb and the solid solution of V part in steel, avoid temperature to cross the low-carbon (LC) nitride and dissolve insufficient.The rolling beginning temperature of subordinate phase is 800～860 ℃; Finishing temperature is 780～840 ℃; Carry out in this temperature range that subordinate phase is rolling can accumulate dislocation in austenite, avoid crossing the low ferritic that forms and reduce armor plate strength because of rolling temperature too high reduction steel plate low-temperature impact work and rolling temperature.Steel plate with the speed of 15～45 ℃/s be cooled to≤300 ℃, can form lath of bainite or bainite+martensite and along the horse of lath interface distributions constituent element difficult to understand, this type of tissue has characteristics such as high-strong toughness.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 200～580 ℃ of tempering temperatures, insulation 5～120s, air cooling after the tempering.Temperature rise rate and short soaking time can form tiny carbide and separate out and equally distributed residual austenite faster, thereby improve the mechanical property of steel plate.
The present invention adopts the composition design and processes system of optimization, can produce the ys 1030MPa level high strength steel plate of carbon equivalent ce V≤0.60%.Carbon equivalent is the important parameter of influence welding.The welding property of steel plate that it has been generally acknowledged that carbon equivalent＞0.60% is poor, is difficult to realize adopting weldprocedure johning knot member.The steel plate of carbon equivalent≤0.60% can connect through the welding means.Carbon equivalent is low more, and it is easy more to weld.The carbon equivalent ce V that Europe superscript 10025-6:2004 and GB GB/T16270:2009 limit ys 960MPa steel plate is≤0.82%; And ys of the present invention is 1030MPa; And carbon equivalent ce V≤0.60%, not only ys is higher than standard, and carbon equivalent ce V is also far below standard.
Preferably, in the method for manufacture of above-mentioned ys 1030MPa grade steel plate, air cooling adopts the cold bed cooling.
Adopt technical scheme of the present invention to have the following advantages:
(1) ys>=1030MPa of ys 1030MPa grade steel plate of the present invention, tensile strength>=1100MPa, Xia Shi ballistic work Akv (40 ℃)>=60J, carbon equivalent ce V≤0.60% has good welding property;
(2) method of manufacture of ys 1030MPa 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 1030MPa 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 1030MPa grade steel plate of the present invention under a kind of embodiment.
Fig. 2 is the transmission electron microscope photo of ys 1030MPa grade steel plate of the present invention under a kind of embodiment.
Embodiment
Embodiment 1-6
The concrete steps of making ys 1030MPa 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: billet heating temperature is 1050～1250 ℃;
(4) rolling:
A) fs: steel billet is rolled being higher than under the recrystallization temperature, 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 800～860 ℃, the beginning subordinate phase was rolling, and its finishing temperature is 780～840 ℃;
(5) cooling: the speed with 15～45 ℃/s is cooled to steel plate≤and 300 ℃;
(6) online tempering heat treatment: the speed with 3～15 ℃/s is warming up to 200～580 ℃ of tempering temperatures with steel plate, behind insulation 5～120s, and the cold bed cooling.
(surplus is Fe and other unavoidable impurities to table 1., wt%)
| Embodiment | C | Si | Mn | P | S | Cr | Mo | Nb | Ni | V | B | Al | Ti | km | In(km) |
| 1 | 0.115 | 0.4 | 2 | 0.015 | 0.003 | 0 | 0.45 | 0.06 | 0.65 | 0.03 | 0.002 | 0.07 | 0.003 | 104.54 | 4.65 |
| 2 | 0.12 | 0.3 | 1.8 | 0.013 | 0.002 | 0.1 | 0.6 | 0.04 | 0.2 | 0.02 | 0.0015 | 0.06 | 0.008 | 99.93 | 4.60 |
| 3 | 0.13 | 0.3 | 1.65 | 0.01 | 0.002 | 0.2 | 0.5 | 0.03 | 0.6 | 0.01 | 0.0012 | 0.05 | 0.01 | 96.67 | 4.57 |
| 4 | 0.14 | 0.2 | 1.2 | 0.011 | 0.002 | 0.7 | 0.3 | 0.02 | 0.8 | 0.03 | 0.001 | 0.04 | 0.02 | 78.69 | 4.38 |
| 5 | 0.15 | 0.2 | 1 | 0.008 | 0.001 | 0.5 | 0.8 | 0.01 | 0.2 | 0.02 | 0.001 | 0.03 | 0.04 | 92.38 | 4.53 |
| 6 | 0.165 | 0.1 | 0.8 | 0.006 | 0.001 | 0.4 | 0.7 | 0.01 | 1.0 | 0 | 0.0006 | 0.02 | 0.03 | 90.85 | 4.51 |
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 | 1090 | 1350 | 12 | 82 | 0.59 |
| 2 | 1105 | 1370 | 10 | 79 | 0.58 |
| 3 | 1145 | 1270 | 11 | 81 | 0.59 |
| 4 | 1170 | 1230 | 12 | 78 | 0.60 |
| 5 | 1165 | 1210 | 12 | 76 | 0.59 |
| 6 | 1150 | 1210 | 12 | 83 | 0.59 |
Can find out from table 3, the ys of this case embodiment 1-6 all>=1030MPa, tensile strength all>=1100MPa, Xia Shi ballistic work Akv (40 ℃) all>=60J, carbon equivalent ce V is all≤0.60%.
Fig. 1 has shown the microtexture of ys 1030MPa grade steel plate among the embodiment 5.As shown in Figure 1, the microtexture of ys 1030MPa grade steel plate is the bainite or the bainite+martensitic stucture of refinement among the embodiment 5.
Fig. 2 is the transmission electron microscope photo of ys 1030MPa grade steel plate among the embodiment 5.As shown in Figure 2, the carbide of ys 1030MPa grade steel plate is separated out tiny and disperse among the embodiment 5, and is evenly distributed on the matrix, thereby improves the obdurability coupling of steel plate.
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 1030MPa grade steel plate is characterized in that, chemical ingredients quality per distribution ratio is:
C:0.115～0.165wt%; Si:0.10～0.40wt%; Mn:0.80～2.00wt%; P :≤0.015wt%; S :≤0.003wt%, Cr :≤0.70wt%; Mo:0.30～0.80wt%; Ni:0.20～1.00wt%; Nb:0.01～0.06wt%; V :≤0.03wt%; Ti:0.003～0.04wt%; Al:0.02～0.07wt%; B:0.0006～0.0020wt%; Surplus is Fe and other unavoidable impurities;
Said ys 1030MPa grade steel plate also should satisfy:
7.01-30.13C-7.58Si-6.38Mo-3.93Cr-0.63Ni≤Mn≤
42.73-30.62C-11.25Si-18.69Mo-10.97Cr-8.23Ni；
And
3.83≤ln(km)≤4.97；
In the formula, km is a water malleableize coefficient, and it satisfies:
km＝33.15C+8.33Si+27.99Mn+58.62Mo+10.52Cr+15.41Ni+2512B。
2. the method for manufacture of ys 1030MPa 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 1050～1250 ℃;
(4) rolling:
A) fs: steel billet is rolled being higher than under the recrystallization temperature, 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 800～860 ℃, the beginning subordinate phase was rolling, and its finishing temperature is 780～840 ℃;
(5) cooling: the speed with 15～45 ℃/s is cooled to steel plate≤and 300 ℃;
(6) online tempering heat treatment: the speed with 3～15 ℃/s is warming up to 200～580 ℃ of tempering temperatures with steel plate, behind insulation 5～120s, and air cooling.
3. the method for manufacture of ys 1030MPa grade steel plate as claimed in claim 2 is characterized in that, said air cooling adopts the cold bed cooling.
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| CN104278206A (en) * | 2014-10-15 | 2015-01-14 | 山东钢铁股份有限公司 | Steel plate with thickness of smaller than 60mm and yield strength of 690MPa and preparation method of steel plate |
| CN104831185A (en) * | 2015-04-16 | 2015-08-12 | 河北钢铁股份有限公司 | Low-cost high-strength steel plate for engineering machinery, and production method thereof |
| CN104946997A (en) * | 2015-06-14 | 2015-09-30 | 秦皇岛首秦金属材料有限公司 | 1300MPa-level super-strength steel and preparation method thereof |
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| CN106498296A (en) * | 2016-11-30 | 2017-03-15 | 湖南华菱涟源钢铁有限公司 | A kind of manufacture method of yield strength 1100MPa level high-strength steel |
| CN111270166A (en) * | 2020-03-30 | 2020-06-12 | 武汉钢铁有限公司 | Non-quenched and tempered thin-gauge ultrahigh steel with yield strength greater than 830MPa and production method thereof |
| CN111748730A (en) * | 2019-03-28 | 2020-10-09 | 宝山钢铁股份有限公司 | 900 MPa-grade high-toughness high-magnetism hot-rolled magnetic yoke steel and production method thereof |
| WO2020253335A1 (en) * | 2019-06-20 | 2020-12-24 | 江阴兴澄特种钢铁有限公司 | Large-thickness lamellar tearing-resistant high-strength steel plate with 960 mpa-level yield strength, and production method therefor |
| CN112981230A (en) * | 2021-01-20 | 2021-06-18 | 江阴兴澄特种钢铁有限公司 | Steel for double-power-supply changeover switch gear shaft pin and manufacturing method thereof |
| CN114058793A (en) * | 2021-10-27 | 2022-02-18 | 舞阳钢铁有限责任公司 | Heat treatment method for reducing yield ratio of ultrahigh-strength marine steel EH890 |
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| CN104278206A (en) * | 2014-10-15 | 2015-01-14 | 山东钢铁股份有限公司 | Steel plate with thickness of smaller than 60mm and yield strength of 690MPa and preparation method of steel plate |
| CN104831185A (en) * | 2015-04-16 | 2015-08-12 | 河北钢铁股份有限公司 | Low-cost high-strength steel plate for engineering machinery, and production method thereof |
| CN104946997A (en) * | 2015-06-14 | 2015-09-30 | 秦皇岛首秦金属材料有限公司 | 1300MPa-level super-strength steel and preparation method thereof |
| CN105239017B (en) * | 2015-10-19 | 2017-04-12 | 燕山大学 | Carburization bearing steel and preparing method thereof |
| CN105239017A (en) * | 2015-10-19 | 2016-01-13 | 燕山大学 | Carburization bearing steel and preparing method thereof |
| CN106498296A (en) * | 2016-11-30 | 2017-03-15 | 湖南华菱涟源钢铁有限公司 | A kind of manufacture method of yield strength 1100MPa level high-strength steel |
| CN111748730A (en) * | 2019-03-28 | 2020-10-09 | 宝山钢铁股份有限公司 | 900 MPa-grade high-toughness high-magnetism hot-rolled magnetic yoke steel and production method thereof |
| CN111748730B (en) * | 2019-03-28 | 2022-06-21 | 宝山钢铁股份有限公司 | 900 MPa-grade high-toughness high-magnetism hot-rolled magnetic yoke steel and production method thereof |
| WO2020253335A1 (en) * | 2019-06-20 | 2020-12-24 | 江阴兴澄特种钢铁有限公司 | Large-thickness lamellar tearing-resistant high-strength steel plate with 960 mpa-level yield strength, and production method therefor |
| CN111270166A (en) * | 2020-03-30 | 2020-06-12 | 武汉钢铁有限公司 | Non-quenched and tempered thin-gauge ultrahigh steel with yield strength greater than 830MPa and production method thereof |
| CN111270166B (en) * | 2020-03-30 | 2021-05-28 | 武汉钢铁有限公司 | Non-quenched and tempered thin-gauge ultrahigh steel with yield strength greater than 830MPa and production method thereof |
| CN112981230A (en) * | 2021-01-20 | 2021-06-18 | 江阴兴澄特种钢铁有限公司 | Steel for double-power-supply changeover switch gear shaft pin and manufacturing method thereof |
| CN114058793A (en) * | 2021-10-27 | 2022-02-18 | 舞阳钢铁有限责任公司 | Heat treatment method for reducing yield ratio of ultrahigh-strength marine steel EH890 |
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