CN104513936B - A kind of yield strength 1100MPa grades of quenching and tempering, highs and its production method - Google Patents

A kind of yield strength 1100MPa grades of quenching and tempering, highs and its production method Download PDF

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CN104513936B
CN104513936B CN201410810279.XA CN201410810279A CN104513936B CN 104513936 B CN104513936 B CN 104513936B CN 201410810279 A CN201410810279 A CN 201410810279A CN 104513936 B CN104513936 B CN 104513936B
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tempering
quenching
steel
yield strength
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CN104513936A (en
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李自刚
杨阿娜
刘刚
杜林�
刘运华
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Baoshan Iron and Steel Co Ltd
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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Abstract

A kind of yield strength 1100MPa grades of quenching and tempering, highs and its production method, its chemical component weight percentage are as follows: C 0.17~0.21%, Si 0.10~0.30%, Mn 0.80~1.60%, Cr0.20~0.70%, Mo 0.10~0.45%, Ni 0.30~1.50%, Nb 0.010~0.030%, Ti0.010~0.030%, V 0.020~0.060%, B 0.0005~0.0030%, Al 0.02~0.06%, Ca0.001~0.004%, N 0.002~0.005%, P≤0.020%, S≤0.010%, O≤0.008%, remaining For Fe and inevitable impurity, and, Ceq 0.53~0.62%, Ceq=C+Mn/6+ (Cr+Mo+V)/5+ (Ni+Cu)/15；3.7≤Ti/N≤7.0；1.0≤Ca/S≤3.0；1.0%≤Mo+0.8Ni+0.4Cr+6V≤1.6%.The present invention uses out-line quenching+tempering process, and the steel plate yield strength produced is 1100~1200MPa, and tensile strength is >=1250MPa, and elongation percentage > 8%, -40 DEG C of ballistic works are in 40J or more.

Description

A kind of yield strength 1100MPa grades of quenching and tempering, highs and its production method
Technical field
The present invention relates to a kind of yield strength 1100MPa grades of quenching and tempering, highs and its production method, yield strength to be 1100~1200MPa, tensile strength are >=1250MPa, and elongation percentage > 8%, -40 DEG C of ballistic works are in 40J or more, microscopic structure Tempered martensite.
Background technique
Using the girder construction of high strength easy welded structural steel manufacturing engineering machinery, the boom of crane and the car body of dumper Etc. mobile devices component, can all mitigate equipment self-weight, reduce fuel consumption, improve working efficiency.With adding for international competition Play, using high strength easy welding structure steel making harbour machinery, mining machinery, excavator, the girder construction of loading machine, crane The component of the mobile devices such as the car body of boom and dumper has become trend.Due to engineering machinery high-performance, enlargement, light weight The demand for development of change, the intensity rank of steel for engineering machinery is constantly soaring, be climbed to from 500~600MPa grades 700MPa, 900MPa, 1000MPa or even 1100MPa.Engineering machinery super-high strength steel is right due to its harsh use environment and stress condition Steel product quality has strict requirements, including strength character, impact property, buckling performance, welding performance and plate shape etc..
The enterprise that the high-strength steel sheet of 1100MPa rank is surrendered in domestic production at present is seldom, Chinese patent CN102560274A describes a kind of production method for surrendering 1000MPa grade high-strength degree thick steel plate, quenches using reheating It is high to open flat equipment requirement to steel plate for fire+tempering process.Chinese patent CN102134680A describes a kind of yield strength The production method of 960MPa grades of high-strength steel, using lower carbon content design and higher Cr content, C:0.07%~0.09%, Cr:1.05~1.15%, the patent are free of Nb, Ti, V microalloy element, and Cr content is higher, is unfavorable for welding.Chinese patent CN101397640A describe it is a kind of surrender 960Mpa grade high-strength steel plate production method, using higher Mo content design and Higher tempering temperature, Mo content 0.45~0.57%, 550~600 DEG C of tempering temperature.
Ingredient in the prior art designs no control joint plasticity and toughness comprehensive performance, does not also account for through field trash control System, the control of structure property heredity improve the intensity and toughness of finished steel plate.
Summary of the invention
The purpose of the present invention is to provide a kind of yield strength 1100MPa grades of quenching and tempering, highs and its production method, the height The yield strength of strong steel is 1100~1200MPa, and tensile strength is >=1250MPa, and elongation percentage > 8%, -40 DEG C of ballistic works are in 40J More than, microscopic structure is tempered martensite.
In order to achieve the above object, present invention provide the technical scheme that
A kind of yield strength 1100MPa grades of quenching and tempering, highs, chemical component weight percentage are as follows: C:0.17~ 0.21%, Si:0.10~0.30%, Mn:0.80~1.60%, Cr:0.20~0.70%, Mo:0.10~0.45%, Ni: 0.30~1.50%, Nb:0.010~0.030%, Ti:0.010~0.030%, V:0.020~0.060%, B:0.0005~ 0.0030%, Al:0.02~0.06%, Ca:0.001~0.004%, N:0.002~0.005%, P≤0.020%, S≤ 0.010%, O≤0.008%, remaining is Fe and inevitable impurity；Above-mentioned element need to meet following relational expression: Ceq simultaneously 0.53~0.62%, Ceq=C+Mn/6+ (Cr+Mo+V)/5+ (Ni+Cu)/15；
1.0%≤Mo+0.8Ni+0.4Cr+6V≤1.6%；3.7≤Ti/N≤7.0；1.0≤Ca/S≤3.0.
Further, the yield strength of 1100MPa grade quenching and tempering, high is 1100~1200MPa, and tensile strength is >=1250MPa, elongation percentage > 8%, -40 DEG C of ballistic works are in 40J or more, microscopic structure tempered martensite.
In ingredient design of the invention:
Carbon: solution strengthening adjusts the intensity and plasticity and toughness of martensitic structure, is tested, and reheats low-carbon geneva after quenching The tensile strength of body and the relationship of C content are in following relationship: Rm=2510C (%)+790 (MPa), Rm are tensile strength, C content It can just guarantee that quenching state tensile strength is greater than 1200MPa 0.17% or more, then intensity is further adjusted by tempering, improve Toughness；The higher raising that will lead to whole C equivalent of C content, when welding, are easy to produce crackle, and C content range of the invention is 0.17~0.21%.
Silicon: 0.10% or more Si can play preferable deoxidation, and Si is more than 0.30% to be easy to produce red iron sheet, Si It is easy to deteriorate the toughness of martensite high-strength steel when content is higher, silicone content range of the invention is 0.10~0.30%.
Manganese: the harden ability that steel can be improved 0.8% or more in Mn element, Mn content be more than 1.6% be easy to produce segregation and The field trashes such as MnS, deteriorate the toughness of martensite high-strength steel, and Mn content range of the invention is 0.80~1.60%.
Chromium: the harden ability that steel can be improved 0.2% or more in Cr element is conducive to form full martensite group in quenching It knits, Cr will form the carbide of Cr in 150~350 DEG C of tempering ranges, have the function of that low-temperature resistance temper softening, Cr contain Amount will appear biggish spark in welding more than 0.70%, influence welding quality, Cr content range of the invention for 0.20~ 0.70%.
Molybdenum: 0.10% or more Mo element has the harden ability for improving steel, is conducive to form full martensite group in quenching It knits；It can react to form compound particle with C under Mo high temperature, have the function of anti-welding point softening, Mo content is too high to be will lead to Carbon equivalent improves, and deteriorates welding performance, while Mo belongs to noble metal, can improve cost, and Mo content range of the invention is 0.10 ~0.45%.
Nickel: for martensite steel when intensity is improved to 1000MPa or more, the toughness of steel is decreased obviously, and Ni makes dislocation Commutative Banach aglebra becomes easy, and has the function of refining martensitic structure, and the low-temperature flexibility of steel, 0.30% or more Ni can be improved Element can improve the low-temperature flexibility and welding point toughness of 1100MPa grades of martensite super-high strength steels, and Ni content is too high to be will lead to Carbon equivalent improves, and deteriorates welding performance, while Ni belongs to noble metal, can improve cost, and Ni content range of the invention is 0.30 ~1.50%.
Niobium, titanium and vanadium: Nb, Ti and V are microalloy element, form nanoscale precipitate with elements such as C, N, press down when heated Austenite grain processed is grown up；Non-recrystallization critical-temperature Tnr, expanding production window can be improved in Nb；The tiny precipitate of Ti Particle can be with improving welding property；V, which reacts in drawing process with N and C, is precipitated nanoscale V (C, N) particle, and steel can be improved Intensity；Content of niobium range of the invention is 0.010~0.030%, and Ti content range is 0.010~0.030%, content of vanadium range It is 0.020~0.060%.
Boron: the harden ability of steel can be improved in micro B, improves the intensity of steel, and the B more than 0.0030% is easy to produce partially Analysis, forms carbon-boron compound, the toughness of severe exacerbation steel, and boron content range of the invention is 0.0005~0.0030%.
Aluminium: Al is used as deoxidier, and 0.02% or more Al is added in steel and can refine crystal grain, improves impact flexibility, AL content The oxide inclusion defect of Al is easy to produce more than 0.06%, Al content range of the invention is 0.02~0.06%.
Calcium: the micro Ca element more than 0.001% can play the role of cleanser during steel smelting, improve steel Toughness；Ca content is more than the compound of 0.004% larger-size Ca easy to form, can deteriorate toughness instead, and Ca of the present invention contains Measuring range is 0.001~0.004%.
Nitrogen: the present invention claims the range of strict control N element, 0.002% or more N element can be in drawing process V and C, which reacts, to be formed nanoscale V (C, N) particle and plays the role of precipitation strength, can also pass through precipitation in the welding process Strengthen and resists heat-affected zone softened；N content is more than 0.005% to be easy to cause to form coarse precipitation composition granule, deteriorates toughness, this Invention N content range is 0.002~0.005%.
Phosphorus, sulphur and oxygen: P, S and O influence the modeling of steel, toughness, the control model of four kinds of elements of the invention as impurity element It encloses for P≤0.020%, S≤0.010%, O≤0.008%.
Out-line quenching+tempering type surrender 1100MPa high-strength steel carbon equivalent Ceq is needed to meet: Ceq0.53~0.62%, Ceq=C+Mn/6+ (Cr+Mo+V)/5+ (Ni+Cu)/150, Ceq is too low to be easy to appear welding point softening, and Ceq is too high to be easy Now weld micro-crack.
By control 1.0%≤Mo+0.8Ni+0.4Cr+6V≤1.6% mainly serve for ensuring 1100MPa high-strength steel etc. Strong matching welding, adjusts the intensity and low-temperature flexibility of welding heat affected zone, reaches with base material armor plate strength and low-temperature flexibility most Good matching.Wherein Mo, Ni and Cr element can reduce the critical cooling rate of steel, improve the harden ability of steel, and raising connects The intensity of head；Mo reacts to form compound with C at high temperature, has the function of resisting welding point softening；Mo and Ni element is all With thinning microstructure, improve the effect of toughness；V, which reacts generation nanoscale V (C, N) particle with N, can resist welding joint softened；Mo, The collocation of Ni, Cr and V element can adjust the intensity and toughness of welding heat affected zone according to strength of parent.Lower than 1.0% welding The intensity and low-temperature flexibility of connector are all lower；It is higher higher than 1.6% strength of welded joint, it is easy to produce weld crack.
It can protect the B atom in steel by controlling 3.7≤Ti/N≤7.0, so that B is sufficiently dissolved, improve harden ability, close Suitable Ti, N ratio is conducive to control the intensity and toughness of composition granule is precipitated in Ti size improvement base material and connector.
It can make the sulfide nodularization of steel grade by controlling 1.0≤Ca/S≤3.0, improve the low-temperature flexibility and weldability of steel Energy.
A kind of production method of 1100MPa grades of quenching and tempering, highs of the invention, includes the following steps:
1) it smelts, cast
Converter or electric furnace steel making are used by following chemical components, and using refining further fine tuning, casting forms slab；Change Learn composition by weight percent are as follows: C:0.17~0.21%, Si:0.10~0.30%, Mn:0.80~1.60%, Cr:0.20~ 0.70%, Mo:0.10~0.45%, Ni:0.30~1.50%, Nb:0.010~0.030%, Ti:0.010~0.030%, V: 0.020~0.060%, B:0.0005~0.0030%, Al:0.02~0.06%, Ca:0.001~0.004%, N:0.002~ 0.005%, P≤0.020%, S≤0.010%, O≤0.008%, remaining is Fe and inevitable impurity；Above-mentioned element is same When need to meet following relational expression:
Ceq 0.53~0.62%, Ceq=C+Mn/6+ (Cr+Mo+V)/5+ (Ni+Cu)/15；
1.0%≤Mo+0.8Ni+0.4Cr+6V≤1.6%；3.7≤Ti/N≤7.0；1.0≤Ca/S≤3.0；
2) it heats
Slab is heated in 1150~1270 DEG C of furnace, starts to keep the temperature after slab center portion to temperature, soaking time > 1.5h；
3) it rolls
It is back and forth rolled using single chassis or slab is rolled to target thickness by multi-frame hot continuous rolling, roll last passes Reduction ratio > 15%；Finishing temperature is 820~920 DEG C, meanwhile, finishing temperature Tf meets: Ar3< Tf < Tnr, wherein Ar3Altogether for Asia Steel austenite is analysed to ferritic transformation start temperature, Tnr is non-recrystallization critical-temperature；Ar3=901-325C-92Mn- 126Cr-67Ni-149Mo, Tnr=887+464C+ (6445Nb-644sqrt (Nb))+(732V-230sqrt (V))+890Ti+ 363Al-357Si；
4) cooling
Rolled piece after hot rolling is batched in 450~Bs DEG C of temperature range, is then air-cooled to room temperature；Bs=630-45Mn- 40V-35Si-30Cr-25Mo-20Ni；
5) it is heat-treated
Quenching, quenching temperature Ac3+ (30~80) DEG C, steel plate center portion start to be kept the temperature after reaching furnace temperature, heat preservation 5~40min；Quenching cooling velocity is,
V>e(5.3-2.53C-0.16Si-0.82Mn-0.95Cr-1.87Mo-160B)℃/s；
Wherein, Ac3Changing for austenite terminates temperature, DEG C；
Ac3=955-350C-25Mn+51Si+106Nb+100Ti+68Al-11Cr-33Ni-16Cu+67Mo；
Tempering, tempering temperature are 150~350 DEG C, keep the temperature 20~180min after steel plate center portion to tempering temperature, are surrendered 1100MPa grades of quenching and tempering, highs of intensity.
Further, the yield strength of the 1100MPa grades of quenching and tempering, highs of yield strength obtained is 1100~1200MPa, is resisted Tensile strength is >=1250MPa, and elongation percentage > 8%, for -40 DEG C of ballistic works in 40J or more, microscopic structure is tempered martensite.
Following relational expression of the present invention: Ceq=C+Mn/6+ (Cr+Mo+V)/5+ (Ni+Cu)/15, Mo+0.8Ni+ Each element symbol indicates the weight percentage of corresponding element in 0.4Cr+6V, Ti/N, Ca/S；The following calculation formula being related to: Ar3=901-325C-92Mn-126Cr-67Ni-149Mo, Tnr=887+464C+ (6445Nb-644sqrt (Nb))+ (732V-230sqrt (V))+890Ti+363Al-357Si, Bs=630-45Mn-40V-35Si-30Cr-25Mo-20Ni,
Ac3=955-350C-25Mn+51Si+106Nb+100Ti+68Al-11Cr-33Ni-16Cu+67Mo and V > e(5.3-2.53C-0.16Si-0.82Mn-0.95Cr-1.87Mo-160B)Middle each element symbol indicates weight percentage × 100 of corresponding element.
In the production method of 1100MPa grades of quenching and tempering, highs of yield strength of the invention:
In slab heating process, control heating temperature can guarantee alloy greater than 1150 DEG C, center portion soaking time > 1.5h Element is sufficiently dissolved；Austenite grain is excessively grown up when heating temperature is more than 1270 DEG C, is caused intergranular binding force to weaken, is being rolled When be easy to produce crackle；In addition heating temperature is more than 1270 DEG C and easily causes billet surface decarburization, causes to finished product mechanical property It influences.
In rolling mill practice, finishing temperature is greater than Ar3It is to guarantee to roll in austenitic area, finishing temperature is less than Tnr In order to guarantee to roll in austenite Unhydrated cement, rolling in austenite Unhydrated cement can be with fining austenite grains and cooling Martensitic structure afterwards, then after subsequent heat treatment, the grain size and toughness of steel have certain heredity, therefore can improve hot place The intensity and toughness of steel after reason.
During the rolling process, carrying out aximal deformation value rolling is in order to form enough deformation energy in Unhydrated cement, in Ar3 Austenite recrystallization is induced in~Tnr temperature range, refines crystal grain.
In cooling technique, batching in 450~Bs DEG C of temperature range is bainite structure tiny in order to obtain, improves steel Toughness.After subsequent heat treatment, the grain size and toughness of steel have certain heredity, therefore can improve steel after heat treatment Intensity and toughness.
In quenching heat treatment technique, heating temperature is lower than Ac3If+30 DEG C, soaking time reach heating lower than steel plate center portion 5min after temperature, alloy are difficult to sufficiently be dissolved, and heating temperature is greater than Ac3+ 80 DEG C, soaking time be greater than steel plate center portion reach heating After temperature when 40min, austenite grain is easy to grow up, by control quenching temperature and Quench heating time certain narrow In range, it is ensured that obtain tiny austenite grain, to refine quenched martensitic structure, improve the tough of steel Property.
In tempering heat treatment process, the steel of chemical component system of the invention is tempered and keeps at 150~350 DEG C Supersaturated carbon atom precipitation when 20min or more in quenched martensite forms tiny carbide particle, and alloy V is at such a temperature Tiny alloy cpd can be reacted and formed with C and N, the yield strength of steel can be improved, and improve the plasticity and toughness of steel, The internal stress of steel is effectively removed simultaneously.Tempering temperature is more than 350 DEG C or the too long carbide particle fast growth of high soaking time, meeting Significantly reduce the tensile strength of steel；It can guarantee that strong, toughness realizes best match by adjusting tempering temperature and tempering time.
Beneficial effects of the present invention:
The present invention uses controlled rolling and controlled cooling and out-line quenching+tempering process, and chemically ingredient design, base material tissue, quenching add Hot temperature, tempering heating-up temperature are angularly controlled, and are guaranteed while realizing superhigh intensity, the elongation percentage of steel, low temperature punching It is functional to hit toughness etc..
Compared with existing invention, content and the welding of match control base material that the present invention passes through the elements such as control Mo, Ni, Cr, V The obdurability of connector, by controlling Ti, N ratio, Ca, S ratio improve the toughness of base material steel plate and welding point.It is lost using structure property Pass the obdurability that characteristic passes through process improving finished steel plate.
Detailed description of the invention
Fig. 1 is test steel typical case's metallographic structure figure of the embodiment of the present invention 1.
Fig. 2 is test steel typical case's metallographic structure figure of the embodiment of the present invention 3.
Fig. 3 is test steel typical case's metallographic structure figure of the embodiment of the present invention 7.
Specific embodiment
Below with reference to embodiment, the present invention will be further described.
The technological process of production of super-high strength steel of the invention are as follows: converter or electric furnace steel making → external refining → continuous casting → heating → rolling → cooling → heat treatment.
The production method of the 1100MPa grade quenching and tempering, high of the embodiment of the present invention 1~10, includes the following steps:
1) smelt, cast: smelted using 50kg vacuum electric furnace, ingredient is as shown in table 1, by the pouring molten steel of smelting at The slab of 120mm thickness, is put into electric furnace and heats.
2) it rolling: slab is rolled into the steel plate of target thickness 10mm using multi-pass, finishing temperature is 820~920 DEG C, Finishing temperature Tf meets simultaneously: Ar3<Tf<Tnr；Final reduction rate setting 17%.
3) cooling: to the rolled piece after rolling, to carry out section cooling online；Final cooling temperature control range is 450~Bs DEG C, Bs For bainite start temperature.
4) quenching heat treatment technique: quenching temperature uses: austenite transformation terminates temperature Ac3+ (30~80) DEG C, quench Fiery heating time is 5~40min after steel plate center portion to temperature.
5) tempering heat treatment process: tempering temperature is 150~350 DEG C, and tempering time is steel plate center portion to 150~350 DEG C 20~180min afterwards obtains 1100MPa grade quenching and tempering, high of the invention.
6) steel plate after modifier treatment will be subjected to longitudinal stretching and impact of collision is tested.
Specific ingredient, technological parameter are as shown in table 1, table 2.The corresponding performance of each embodiment template is as shown in table 3.
FIG. 1 to FIG. 3 gives the metallographic structure photo that embodiment 1,3,7 tests steel.It can from FIG. 1 to FIG. 3 metallograph To find out, the metallographic structure of finished steel plate is the shaft-like tempered martensite such as uniform, and is organized fine and closely woven.
The present invention uses controlled rolling and controlled cooling and out-line quenching+tempering process, and chemically ingredient design, base material tissue, quenching add Hot temperature, tempering heating-up temperature are angularly controlled, and are guaranteed while realizing superhigh intensity, the elongation percentage of steel, low temperature punching It is functional to hit toughness etc..
Table 2
Table 3
Note: three column respectively represent the test result of three parallel samples in -40 DEG C of ballistic work test results.

Claims (2)

1. a kind of yield strength 1100MPa grades of quenching and tempering, highs, chemical component weight percentage are as follows: C:0.17~0.21%, Si:0.10~0.30%, Mn:0.80~1.60%, Cr:0.20~0.70%, Mo:0.10~0.45%, Ni:0.30~ 1.50%, Nb:0.010~0.030%, Ti:0.010~0.030%, V:0.020~0.060%, B:0.0005~ 0.0030%, Al:0.02~0.06%, Ca:0.001~0.004%, N:0.002~0.005%, P≤0.020%, S≤ 0.010%, O≤0.008%, remaining is Fe and inevitable impurity；And above-mentioned element need to meet following relational expression simultaneously:
Ceq 0.53~0.62%, Ceq=C+Mn/6+ (Cr+Mo+V)/5+ (Ni+Cu)/15；
1.0%≤Mo+0.8Ni+0.4Cr+6V≤1.6%；3.7≤Ti/N≤7.0；1.0≤Ca/S≤3.0；
The microscopic structure of the quenching and tempering, high be tempered martensite, yield strength be 1100~1200MPa, tensile strength >= 1250MPa, elongation percentage > 8%, -40 DEG C of ballistic works are in 40J or more.
2. a kind of production method of yield strength 1100MPa grades of quenching and tempering, highs, which comprises the steps of:
1) it smelts, cast
Converter or electric furnace steel making are used by following chemical components, and using refining further fine tuning, casting forms slab；Chemistry at Divide weight percent are as follows: C:0.17~0.21%, Si:0.10~0.30%, Mn:0.80~1.60%, Cr:0.20~ 0.70%, Mo:0.10~0.45%, Ni:0.30~1.50%, Nb:0.010~0.030%, Ti:0.010~0.030%, V: 0.020~0.060%, B:0.0005~0.0030%, Al:0.02~0.06%, Ca:0.001~0.004%, N:0.002~ 0.005%, P≤0.020%, S≤0.010%, O≤0.008%, remaining is Fe and inevitable impurity；Above-mentioned element is same When need to meet following relational expression: Ceq 0.53~0.62%, Ceq=C+Mn/6+ (Cr+Mo+V)/5+ (Ni+Cu)/15；1.0% ≤ Mo+0.8Ni+0.4Cr+6V≤1.6%；3.7≤Ti/N≤7.0；1.0≤Ca/S≤3.0；
2) it heats
Slab is heated in 1150~1270 DEG C of furnace, starts to keep the temperature after slab center portion to temperature, soaking time > 1.5h；
3) it rolls
It is back and forth rolled using single chassis or slab is rolled to target thickness by multi-frame hot continuous rolling, roll the pressure of last passes Rate > 15%；Finishing temperature is 820~920 DEG C, meanwhile, finishing temperature Tf meets: Ar3< Tf < Tnr, wherein Ar3For sub-eutectoid steel For austenite to ferritic transformation start temperature, Tnr is non-recrystallization critical-temperature；
Ar3=901-325C-92Mn-126Cr-67Ni-149Mo,
Tnr=887+464C+ (6445Nb-644sqrt (Nb))+(732V-230sqrt (V))+890Ti+363Al-357Si；
4) cooling
Rolled piece after hot rolling is batched in 450~Bs DEG C of temperature range, is then air-cooled to room temperature；
Bs=630-45Mn-40V-35Si-30Cr-25Mo-20Ni；
5) it is heat-treated
Quenching, is heated to Ac3+ (30~80) DEG C, Ac3Changing for austenite terminates temperature；
Ac3=955-350C-25Mn+51Si+106Nb+100Ti+68Al-11Cr-33Ni-16Cu+67Mo；Steel plate center portion reaches 5~40min is kept the temperature after furnace temperature；Quench cooling velocity V > e(5.3-2.53C-0.16Si-0.82Mn-0.95Cr-1.87Mo-160B)℃/s；
Tempering, tempering temperature are 150~350 DEG C, and tempering time is 20~180min after steel plate center portion to temperature, obtains yield strength 1100MPa grades of quenching and tempering, highs.
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