CN102925802A - Method for producing ultrahigh strength steel plate - Google Patents
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- CN102925802A CN102925802A CN2012104299831A CN201210429983A CN102925802A CN 102925802 A CN102925802 A CN 102925802A CN 2012104299831 A CN2012104299831 A CN 2012104299831A CN 201210429983 A CN201210429983 A CN 201210429983A CN 102925802 A CN102925802 A CN 102925802A
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Abstract
A method for producing an ultrahigh strength steel plate includes: steelmaking, refining, continuous casting, heating, rolling, cooling and thermal treatment. The steel comprises the follow components by mass: 0.18-0.20 of C, 0.35-0.42 of Si, 1.30-1.40 of Mn, less than or equal to 0.015 of P, less than or equal to 0.010 of S, 0.03-0.06 of Al, 0.02-0.03 of Nb, 0.05-0.06 of V, 0.035-0.045 of Ti, 0.25-0.35 of Mo and 0.0017-0.0022 of B. The steel plate is concise in component design and does not contain a large number of alloying elements, and production cost of the ultrahigh strength steel plate is reduced; Ti is added in the steel plate, so that the welding performance of the steel plate is improved; after Q+P treatment on the steel plate, the tissue of the steel plate contains superfine lath martensite, nanoscale plate retained austenite and deposited composite carbide, and the comprehensive performance of steel plate strength and plasticity is superior to double-phase steel, transformation-induced plasticity (TRIP) steel and common martensitic steel; the steel plate is good in shape after quenched through a roller type quenching machine; and the method is simple in process, easy to achieve, and capable of solving the puzzle that ultrahigh strength steel plates cannot be produced through traditional quenching and tempering, and volume production of 1100MPa level ultrahigh strength steel plates can be achieved.
Description
Technical field
The invention belongs to steel-smelting technology, is a kind of production method of super-high strength steel plate.
Technical background
Ultrahigh-strength steel refers to its tensile strength more than 1000MPa, approaches or surpasses 2000MPa, percentage of total elongation〉10 %, and the more honest and cleaner structure iron of price.Traditional quenching-tempering process can not satisfy high-strength steel and have certain toughness and cheap requirement concurrently.At present, general high-strength steel all is to make the steel grade performance up to standard by adding alloying element basically, and the high-strength steel cost that obtains like this is higher, is unfavorable for saving energy and reduce the cost.In order to reduce production costs, increase economic benefit, must be constantly to novel process, new technology research experiment.
The difficult tensile strength that makes steel of perlite (non-deformation attitude) and bainite structure is up to 2000MPa, and martensitic stucture is when being competent at.For having certain toughness concurrently, should make the tissue of steel be dislocation strip martensitic stucture.Have recognized that in the past that the residual austenite physical efficiency in the hardened steel improved plasticity and the toughness of steel half century, surrounded by the residual austenite of several nanometer thickness such as strip martensite, increased toughness; Utilize austenitic thermostabilization phenomenon, propose tool steel without being out of shape quenching and rapid steel workpiece without the distortion tempering heat treatment process.Experiment showed, that the hydrogen embrittlement crackle is hampered by the fcc austenite, contain 300M steel (residual austenite is 3 % approximately) contrast 4340 steel (paralympic＜2 %) of 1.3 % Si through 300 ℃ of tempering, separate out equally ε-carbide, but the slow order of magnitude of stress corrosion speed.Xu Zuyao once tentatively set forth the vital role of residual austenite in the soft steel.Utilize the electron microscope experiment results such as Thomas, Xu Zuyao calculates proof: carbon diffused to residual austenite by martensite when soft steel quenched.Speer etc. propose the Q+P thermal treatment process of steel, namely quench (Q) after between Ms～Mf, through the certain temperature insulation, make carbon distribute (partition) to austenite from martensite, make a certain amount of austenite stable to room temperature to guarantee toughness.For hindering separating out of Fe3C, contain 1%～2 %Si in their the designed Q+P steel.Xu Zuyao introduces precipitation hardening mechanism on the Q+P technique bases such as Speer, tentatively propose Q+P+T technique, namely in steel, add the carbon compound forming element, outside quenching distributes by carbon, and make diffusion-precipitation complicated carbide in the martensite, obtain higher-strength and toughness and cooperate.
Studies show that, plasticity and the toughness of residual austenite physical efficiency Effective Raise material, for in hardened steel, obtaining a certain amount of stable retained austenite, adopt (the Quenching)-carbon that quenches to distribute (Partitioning)-tempering (Tempering) technique when proposing thermal treatment, be called for short Q-P-T technique, be that steel plate quenching is incubated certain hour after certain temperature, carbon is dispensed to retained austenite from martensite, then after suitable time of certain temperature tempering, make it separate out complicated carbide, to increase strengthening effect.0.2%C-Mn-Ti-B has been carried out the thermal modeling test of similar Q-P-T technique, and the sample after the thermal analogy has been carried out structure observation, organizing of obtaining is lath martensite tissue and a certain amount of residual austenite basically.
Adopt Q-P-T technique that 0.2%C-Mn-Ti-B has been carried out experimental study, then cut two tension specimens, two groups of impact specimens, a metallographic specimen and a hardness sample, the performance such as the table 1 that obtain at each motherboard.Can find out from table, not only strength ratio increased originally, and all increased before impact, unit elongation, the test of hardness geometric ratio.
The performance test results that table 1 adopts Q-P-T technique that 0.2%C-Mn-Ti-B is tested
By above-mentioned experimental study as can be known, adopt Q-P-T technique really can improve the performance of high-strength steel, but also can reduce the alloying element addition.Therefore, can be by the trial-production of the carbon content high-strength steel of Q-P-T technique about 0.15%, optimization reaches the super-high strength steel chemical composition more than the 1100MPa level on the basis of few addition element, to reduce the production cost of high-strength steel, improve simultaneously plasticity and the toughness of high-strength steel.
Chinese patent application 200610018011.8 " easy-weld hardening high-strength steel plate and production method thereof ", Chinese patent application 200710193023.9 " a kind of high tensile steel plate and preparation method thereof ", Chinese patent application 200710193027.7 " high tensile steel plate and preparation method thereof ", be respectively 80kg, 100kg, 110kg level High Strength Steel Plate production technology, adopt off-line quenching+tempering technique (Q+T), steel plate finally is organized as tempered martensite.Above patent light plate composition has added the precious alloys such as Mo, Ni, V, Ti, the Nb of high-content, and to guarantee the adaptability of plate property and technique, production cost is high.
So the problem that High Strength Steel Plate production exists in the prior art is: added the precious alloys such as Mo, Ni, V, Ti, Nb of high-content in a. High Strength Steel Plate composition, to guarantee the adaptability of plate property and technique, the Plate Production cost is high; When b. High Strength Steel Plate intensity reaches 1000MPa, steel plate plasticity and poor toughness, its unit elongation is less than 10%; C. (Q+T) and TMCP production technique can not have been produced the demand that the above high tensile steel plate of 1100MPa satisfies manufacturing at present; D.1200Mpa above superstrength Wide and Thick Slab does not have maturation process and the production method of batch production at present.
Summary of the invention
It is the low-cost superstrength structural steel and iron of 8～60mm intensity 1100MPa level that the present invention is intended to produce thickness, satisfies the demand of manufacturing, realizes theory energy-saving and cost-reducing, green iron and steel.Its characteristics are succinct Composition Design, and yield strength is not less than 1100Mpa, and tensile strength is not less than 1200 Mpa, and unit elongation is greater than 10%, and-20 ℃ of impacts of collision are not less than 47J; Steel plate is organized as stable tiny lath martensite and residual austenite, and is distributed with the carbide of coherence and half coherence, to improve the reasonable coordination of armor plate strength and obdurability.
Technical solution of the present invention:
A kind of production technique of super-high strength steel plate, adopting process route are steel-making → refining → continuous casting → heating → rolling → cooling → thermal treatment.
The quality percentage composition of steel is C=0.18～0.20, Si=0.35～0.42, Mn=1.30～1.40, P≤0.015, S≤0.010, Al=0.03～0.06, Nb=0.02～0.03, V=0.05～0.06, Ti=0.035～0.045, Mo=0.25～0.35, B=0.0017～0.0022;
Processing step is:
A. steel-making: molten steel sulfur content S≤0.010% after the hot metal pretreatment, temperature 〉=1250 ℃, molten iron is taken off slag totally before entering converter; Converter terminal control C-T coordinates tapping, P≤0.012%, S≤0.015%, pushing off the slag go out slag thick≤50mm, tapping time 4 ~ 7min, 1/5～2/5 o'clock adding alloy of tapping; Squeeze into the deoxidation of Al line after the tapping and be no less than 250m;
B. refining: the refining of LF stove is made white slag and deoxidation operation to molten steel; The refining later stage according to LF stove molten steel sample composition add V-Fe, Nb-Fe, the Ti-Fe alloy carries out trimming; An amount of Si-Ca line of feeding adds 0.018 ~ 0.020B-Fe after blowing Ar5min before the departures; In the front 5min after the VD extracting vacuum begins, ladle bottom Ar is stirred gas flow be reduced to zero; After extracting vacuum began 3min, gas clean-up was to keeping carrying out circulating degasification more than the 15min below the 0.5tor;
C. continuous casting: 1511 ℃ of liquidus lines, 5～15 ℃ of middle bag superheating temperature; Plate strand production allusion quotation pulling rate was carried out during pulling speed of continuous casting adopted, and produced thickness of strand 300mm;
D. heating: 1180～1200 ℃ of Heating temperatures, the slab heart section temperature of coming out of the stove be greater than 1150 ℃, rate of heating 9～11min/cm, and total time inside furnace is greater than 5h;
E. rolling: roughing adopts high temperature, depresses greatly, rolling technique at a slow speed, and maximum percentage pass reduction is more than 15%, 1040～1060 ℃ of start rolling temperatures, 950～970 ℃ of finishing temperatures; Finish rolling accumulative total draft is greater than 60%, and last three percentage pass reductions are greater than 12%, 830～820 ℃ of start rolling temperatures, 780～810 ℃ of finishing temperatures;
F. cooling: roll rear ACC cooling, open 760～780 ℃ of cold temperature, be cooled to 580～630 ℃ of air coolings, 6～15 ℃/S of speed of cooling;
G. thermal treatment: 890～910 ℃ of quenching temperatures, time inside furnace calculates by 1.4～1.6min/mm * thickness of slab min, quenching press speed 20～40m/min, temperature is 240～300 ℃ after quenching, and sends into fast tempering stove after the quenching and carries out the carbon distribution; 180～200 ℃ of carbon dispense temperature, time inside furnace are pressed 0.8min/mm * thickness of slab min and are calculated, the rear air cooling of coming out of the stove.
Steel plate by this technical scheme is produced detects performance actual achievement such as table 2.
Table 2 1100MPa super-high strength steel plate service check actual achievement
Know-why of the present invention:
The present invention possesses tissue characteristic and the requirement of super-high strength steel: the fine strip shape martensite of (1) tool high dislocation density, lath thickness are tens nanometer; (2) separate out tiny coherence complicated carbide on the martensite further to gain in strength; (3) avoid cementite Fe3C to separate out; (4) contain the residual austenite of proper amt (thickness), certain carbon content between the martensite bar to improve toughness and the plasticity of steel; (5) original austenite is answered tool fine grained texture.
The high manganese Composition Design of carbon during 1100MPa level super-high strength steel plate of the present invention uses, the intensity of assurance steel plate; High Si composition suppresses the formation of Fe3C, stablizes ε-carbide, and makes steel can carry out carbon distribution (Partitioning) processing; Contain the stable austenite elements such as Mn, Ms is descended; Contain complicated carbide forming element such as Nb, V, Ti, the Mo element descends Ms, is precipitation hardening and refine austenite crystal grain; The adding of Ti has improved the welding property of super-high strength steel plate.
Adopt the production method of Clean Steel to produce high-quality continuously cast bloom; Tissue before TMCP rolling technology refinement steel plate hot is processed; The lesser temps austenitizing can obtain thin brilliant austenite structure; Be quenched to 240～300 ℃ of (Ms～Mf) to obtain an amount of martensite, improve armor plate strength; Carry out carbon at 180～200 ℃ and distribute, the rich carbon of more residual austenites is also stable to room temperature; Dispense temperature complicated carbide coherence and half coherent precipitate can improve the intensity of steel and plasticity, toughness; The complicated carbide that steel plate is organized as lath martensite+lath residual austenite and is settled out after Q+P processes, the over-all properties of armor plate strength and plasticity are better than dual phase steel, TRIP steel, general martensite steel sections.
The present invention includes steel-making, refining, continuous casting, heating, rolling, accelerate the operations compositions such as cooling, Q+P thermal treatment.Succinct steel grades designs, and has reduced the production cost of steel plate; Adopt the high-quality continuously cast bloom of the aquatic product of Clean Steel; Low temperature long-time heating slab acquisition crystal grain is tiny, the austenite crystal of homogeneous chemical composition; Roughing high temperature depresses greatly, rolling abundant refinement strand central tissue at a slow speed, and finish rolling accumulative total draft guarantees that austenite has enough deformation bands, accelerates to change after the cooling and organizes crystal grain tiny, even; Q technique guarantees to be martensite and enough residual austenites behind the steel plate quenching, guarantees the stable of residual austenite after P processes, and has improved plasticity and the toughness of steel plate.
Therefore, compared with prior art, the present invention has the following advantages: a. steel plate Composition Design is succinct, does not add a large amount of alloying elements, has reduced the production cost of super-high strength steel plate; B. add Ti in the steel plate composition, improved the welding property of steel plate; C. the steel plate complicated carbide that after Q+P processes, is organized as ultra-fine lath martensite+nano level lath residual austenite and is settled out, the over-all properties of armor plate strength and plasticity is better than dual phase steel, TRIP steel and general martensite steel sections; D. steel plate is after roller quenching machine quenches, and template is good; E. operation simple, easily realize, solved the difficult problem that traditional quenching, tempering can not be produced the super-high strength steel plate, realize the batch production of 1100MPa level super-high strength steel plate.
Description of drawings
Accompanying drawing is that the present invention produces the rear organization chart of steel plate Q+P processing.
Embodiment
Embodiment 1:
Enter the stove molten iron and carry out first hot metal pretreatment, molten steel sulfur content S after processing≤0.010%, temperature 〉=1250 ℃, molten iron must be taken off slag totally before entering converter.Converter steelmaking process adds molten iron and steel scrap, and molten iron and steel scrap proportioning are molten iron about 85%, steel scrap about 15%.Converter terminal control C-T coordinates tapping, P≤0.012%, S≤0.015%; Strict pushing off the slag tapping, slag is thick≤50mm, tapping time 4 ~ 7min, tapping 1/5 adds alloy, and tapping 2/5 adds alloy; Squeeze into the deoxidation of Al line after the tapping and be no less than 250m, and the variation of looking Intake Quantity, terminal point C, molten steel oxidation is suitably adjusted.Then molten steel is transported to the LF refining furnace and carries out refining operation.
The LF refining is made white slag and deoxidation operation to molten steel, guarantees that the content of the element such as oxygen, sulphur in the steel is controlled at lower level; The refining later stage is added an amount of alloy such as V-Fe, Nb-Fe, Ti-Fe according to LF stove molten steel sample composition and carries out trimming, guarantees that composition all hits; An amount of Si-Ca line of feeding before the departures adds B-Fe after blowing Ar5min, and the add-on of B-Fe is according to 0.018 ~ 0.020 control.Then molten steel is transported to the VD stove and carries out vacuum-treat.In the front 5min after the VD extracting vacuum begins, ladle bottom Ar is stirred gas flow be reduced to zero, prevent from before vacuum chamber reaches vacuum, molten steel not being stirred, cause the molten steel oxidation; After extracting vacuum begins 3min, require the Quick condition of high vacuum degree to 0.5tor, and under this vacuum tightness the empty 15min of fidelity; During the RH vacuum-treat, vacuum keep is below 0.5tor, and more than circulating degasification 15min under this vacuum tightness.The soft blow of after vacuum-treat finishes molten steel being carried out more than the 15min is processed, and then molten steel is transported to continuous casting and casts.
1511 ℃ of the liquidus lines of this steel grade, 5～15 ℃ of middle bag superheating temperature controls; Plate strand production allusion quotation pulling rate was carried out during pulling speed of continuous casting adopted, the casting of strict implement stable state; Produce thickness of strand 300mm(casting machine and produce maximum ga(u)ge); The strict protective casting of the omnidistance implementation of continuous casting prevents molten steel secondary oxidation and nitrogen pick-up.The strand that rolls off the production line carries out the cooling in heap more than 24 hours.The finished product composition sees Table 3.
Strand is 1180～1200 ℃ of the Heating temperatures of process furnace, and the slab heart section temperature of coming out of the stove is greater than 1150 ℃; Rate of heating 9～11min/cm, total time inside furnace is greater than 5h.Come out of the stove and carry out the high pressure dephosphorization, then enter roughing." high temperature, depress greatly, at a slow speed " rolling technique is adopted in roughing, does not use automatic rolling, and is manually rolling; The reduction schedule establishment is selected maximum reduction in pass by the ability of milling train, and maximum percentage pass reduction reaches more than 15%; 1040～1060 ℃ of start rolling temperatures, 950～970 ℃ of finishing temperatures.Finish rolling accumulative total draft is greater than 60%, and last three percentage pass reductions are greater than 12%; 830～820 ℃ of start rolling temperatures, 780～810 ℃ of finishing temperatures.Roll rear ACC cooling and select strong cold technique, open 760～780 ℃ of cold temperature, be cooled to 580～630 ℃ of air coolings, 6～15 ℃/s of speed of cooling.
The heat treatment mode that steel plate adopts quenching+carbon to distribute.The temperature of austenitizing is 890～910 ℃; Time inside furnace calculates by (1.4～1.6min/mm * thickness of slab) min; Quenching press speed 20～40m/min; Temperature is 240～300 ℃ behind the steel plate quenching, sends into fast tempering stove behind the steel plate quenching and carries out the carbon distribution.180～200 ℃ of carbon dispense temperature; Time inside furnace calculates by (0.8min/mm * thickness of slab) min; The rear air cooling of coming out of the stove.
The finished steel plate performance test results is: thickness is that the steel plate yield strength of 20mm is 1271MPa, and tensile strength is 1379MPa, and unit elongation is 12.6%, and normal temperature impacts and is 97/100/94J, and 0 ℃ of impact is 78/77/126J, and-20 ℃ of impacts are 61/63/70J.Thickness is that the steel plate yield strength of 40mm is 1164MPa, and tensile strength is 1394MPa, and unit elongation is 11.5%, and normal temperature impacts and is 137/173/136J, and 0 ℃ of impact is 78/85/88J, and-20 ℃ of impacts are 81/78/75J.
Embodiment 2:
Enter the stove molten iron and carry out first hot metal pretreatment, molten steel sulfur content S after processing≤0.010%, temperature 〉=1250 ℃, molten iron must be taken off slag totally before entering converter.Converter steelmaking process adds molten iron and steel scrap, and molten iron and steel scrap proportioning are molten iron about 85%, steel scrap about 15%.Converter terminal control C-T coordinates tapping, P≤0.012%, S≤0.015%; Strict pushing off the slag tapping, slag is thick≤50mm, tapping time 4 ~ 7min, tapping 1/5 adds alloy, and tapping 2/5 adds alloy; Squeeze into the deoxidation of Al line after the tapping and be no less than 250m, and the variation of looking Intake Quantity, terminal point C, molten steel oxidation is suitably adjusted.Then molten steel is transported to the LF refining furnace and carries out refining operation.
The LF refining is made white slag and deoxidation operation to molten steel, guarantees that the content of the element such as oxygen, sulphur in the steel is controlled at lower level; The refining later stage is added an amount of alloy such as V-Fe, Nb-Fe, Ti-Fe according to LF stove molten steel sample composition and carries out trimming, guarantees that composition all hits; An amount of Si-Ca line of feeding before the departures adds B-Fe after blowing Ar5min, and the add-on of B-Fe is according to 0.018 ~ 0.020 control.Then molten steel is transported to the VD stove and carries out vacuum-treat.In the front 5min after the VD extracting vacuum begins, ladle bottom Ar is stirred gas flow be reduced to zero, prevent from before vacuum chamber reaches vacuum, molten steel not being stirred, cause the molten steel oxidation; After extracting vacuum begins 3min, require the Quick condition of high vacuum degree to 0.5tor, and under this vacuum tightness the empty 15min of fidelity; During the RH vacuum-treat, vacuum keep is below 0.5tor, and more than circulating degasification 15min under this vacuum tightness.The soft blow of after vacuum-treat finishes molten steel being carried out more than the 15min is processed, and then molten steel is transported to continuous casting and casts.
1511 ℃ of the liquidus lines of this steel grade, 5～15 ℃ of middle bag superheating temperature controls; Plate strand production allusion quotation pulling rate was carried out during pulling speed of continuous casting adopted, the casting of strict implement stable state; Produce thickness of strand 300mm(casting machine and produce maximum ga(u)ge); The strict protective casting of the omnidistance implementation of continuous casting prevents molten steel secondary oxidation and nitrogen pick-up.The strand that rolls off the production line carries out the cooling in heap more than 24 hours.The finished product composition sees Table 3.
Strand is 1180～1200 ℃ of the Heating temperatures of process furnace, and the slab heart section temperature of coming out of the stove is greater than 1150 ℃; Rate of heating 9～11min/cm, total time inside furnace is greater than 5h.Come out of the stove and carry out the high pressure dephosphorization, then enter roughing." high temperature, depress greatly, at a slow speed " rolling technique is adopted in roughing, does not use automatic rolling, and is manually rolling; The reduction schedule establishment is selected maximum reduction in pass by the ability of milling train, and maximum percentage pass reduction reaches more than 15%; 1040～1060 ℃ of start rolling temperatures, 950～970 ℃ of finishing temperatures.Finish rolling accumulative total draft is greater than 60%, and last three percentage pass reductions are greater than 12%; 830～820 ℃ of start rolling temperatures, 780～810 ℃ of finishing temperatures.Roll rear ACC cooling and select strong cold technique, open 760～780 ℃ of cold temperature, be cooled to 580～630 ℃ of air coolings, 6～15 ℃/s of speed of cooling.
The heat treatment mode that steel plate adopts quenching+carbon to distribute.The temperature of austenitizing is 890～910 ℃; Time inside furnace calculates by (1.4～1.6min/mm * thickness of slab) min; Quenching press speed 20～40m/min; Temperature is 240～300 ℃ behind the steel plate quenching, sends into fast tempering stove behind the steel plate quenching and carries out the carbon distribution.180～200 ℃ of carbon dispense temperature; Time inside furnace calculates by (0.8min/mm * thickness of slab) min; The rear air cooling of coming out of the stove.
The finished steel plate performance test results is: thickness is that the steel plate yield strength of 60mm is 1185MPa, and tensile strength is 1429MPa, and unit elongation is 12.6%, and normal temperature impacts and is 115/109/105J, and 0 ℃ of impact is 78/107/87J, and-20 ℃ of impacts are 71/63/66J.
Table 3 1100MPa level super-high strength steel plate composition (%)
Claims (1)
1. the production technique of a super-high strength steel plate, the adopting process route is steel-making → refining → continuous casting → heating → rolling → cooling → thermal treatment, it is characterized in that:
The quality percentage composition of steel is C=0.18～0.20, Si=0.35～0.42, Mn=1.30～1.40, P≤.015, S≤.010, Al=0.03～0.06, Nb=0.02～0.03, V=0.05～0.06, Ti=0.035～0.045, Mo=0.25～0.35, B=0.0017～0.0022;
Processing step is:
A. steel-making: molten steel sulfur content S≤0.010% after the hot metal pretreatment, temperature 〉=1250 ℃, molten iron is taken off slag totally before entering converter; Converter terminal control C-T coordinates tapping, P≤0.012%, S≤0.015%, pushing off the slag go out slag thick≤50mm, tapping time 4 ~ 7min, 1/5～2/5 o'clock adding alloy of tapping; Squeeze into the deoxidation of Al line after the tapping and be no less than 250m;
B. refining: the refining of LF stove is made white slag and deoxidation operation to molten steel; The refining later stage according to LF stove molten steel sample composition add V-Fe, Nb-Fe, the Ti-Fe alloy carries out trimming; An amount of Si-Ca line of feeding adds 0.018 ~ 0.020B-Fe after blowing Ar5min before the departures; In the front 5min after the VD extracting vacuum begins, ladle bottom Ar is stirred gas flow be reduced to zero; After extracting vacuum began 3min, gas clean-up was to keeping carrying out circulating degasification more than the 15min below the 0.5tor;
C. continuous casting: 1511 ℃ of liquidus lines, 5～15 ℃ of middle bag superheating temperature; Plate strand production allusion quotation pulling rate was carried out during pulling speed of continuous casting adopted, and produced thickness of strand 300mm;
D. heating: 1180～1200 ℃ of Heating temperatures, the slab heart section temperature of coming out of the stove be greater than 1150 ℃, rate of heating 9～11min/cm, and total time inside furnace is greater than 5h;
E. rolling: roughing adopts high temperature, depresses greatly, rolling technique at a slow speed, and maximum percentage pass reduction is more than 15%, 1040～1060 ℃ of start rolling temperatures, 950～970 ℃ of finishing temperatures; Finish rolling accumulative total draft is greater than 60%, and last three percentage pass reductions are greater than 12%, 830～820 ℃ of start rolling temperatures, 780～810 ℃ of finishing temperatures;
F. cooling: roll rear ACC cooling, open 760～780 ℃ of cold temperature, be cooled to 580～630 ℃ of air coolings, 6～15 ℃/S of speed of cooling;
G. thermal treatment: 890～910 ℃ of quenching temperatures, time inside furnace calculates by 1.4～1.6min/mm * thickness of slab min, quenching press speed 20～40m/min, temperature is 240～300 ℃ after quenching, and sends into fast tempering stove after the quenching and carries out the carbon distribution; 180～200 ℃ of carbon dispense temperature, time inside furnace are pressed 0.8min/mm * thickness of slab min and are calculated, the rear air cooling of coming out of the stove.
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
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| WO2014154104A1 (en) * | 2013-03-28 | 2014-10-02 | 宝山钢铁股份有限公司 | Low alloy high toughness wear-resistant steel plate and manufacturing method thereof |
| CN113637900A (en) * | 2021-07-27 | 2021-11-12 | 包头钢铁（集团）有限责任公司 | Production method of thick steel plate for 1100 MPa-level heavy machinery suspension arm |
| CN116926427A (en) * | 2023-07-28 | 2023-10-24 | 湖南华菱湘潭钢铁有限公司 | Q1300 steel plate for high-strength structure and preparation method and application thereof |
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| JP2011111674A (en) * | 2009-11-30 | 2011-06-09 | Nippon Steel Corp | HIGH STRENGTH COLD ROLLED STEEL SHEET EXCELLENT IN FATIGUE DURABILITY AND HAVING THE MAXIMUM TENSILE STRENGTH OF >=900 MPa AND METHOD FOR PRODUCING THE SAME, AND HIGH STRENGTH GALVANIZED STEEL SHEET AND METHOD FOR PRODUCING THE SAME |
| CN102363859A (en) * | 2011-11-14 | 2012-02-29 | 湖南华菱湘潭钢铁有限公司 | Method for producing wear-resisting steel plate |
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| WO2014154104A1 (en) * | 2013-03-28 | 2014-10-02 | 宝山钢铁股份有限公司 | Low alloy high toughness wear-resistant steel plate and manufacturing method thereof |
| US10494706B2 (en) | 2013-03-28 | 2019-12-03 | Baoshan Iron & Steel Co., Ltd. | High-toughness low alloy wear-resistant steel sheet and method of manufacturing method thereof the same |
| CN113637900A (en) * | 2021-07-27 | 2021-11-12 | 包头钢铁（集团）有限责任公司 | Production method of thick steel plate for 1100 MPa-level heavy machinery suspension arm |
| CN116926427A (en) * | 2023-07-28 | 2023-10-24 | 湖南华菱湘潭钢铁有限公司 | Q1300 steel plate for high-strength structure and preparation method and application thereof |
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