CN104561827A - High strength steel with yield strength to be 900-1000MPa grade and production method of high strength steel - Google Patents
High strength steel with yield strength to be 900-1000MPa grade and production method of high strength steel Download PDFInfo
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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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- 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
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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- 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
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- 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
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- 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
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- 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
Abstract
The invention discloses a high strength steel with yield strength to be 900-1000MPa grade and a production method of the high strength steel. The high strength steel is prepared from the following components in percentage by weight: 0.07-0.15 percent of C, 0.10-0.30 percent of Si, 0.80-1.60 percent of Mn, 0.20-0.70 percent of Cr, 0.10-0.45 percent of Mo, 0.10-0.50 percent of Ni, 0.010-0.030 percent of Nb, 0.010-0.030 percent of Ti, 0.010-0.050 percent of V, 0.0005-0.0030 percent of B, 0.02-0.06 percent of Al, 0.001-0.004 percent of Ca, 0.002-0.005 percent of N, P no larger than 0.020 percent, S no larger than 0.010 percent, O no larger than 0.008 percent and the balance of Fe and inevitable impurities, wherein Ceq accounts for 0.42-0.52 percent and is equal to C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15; Mo+0.8Ni+0.4Cr+6V is no less than 0.8 percent and no larger than 1.3 percent; Ti/N is no less than 3.7 and no larger than 7.0, and Ca/S is no less than 1.0 and no larger than 3.0. According to the production method disclosed by the invention, processes of online quenching and tempering are adopted, so that the yield strength of the produced steel plate is 900-1080MPa, the tensile strength is 950-1200MPa, the elongation is larger than 10 percent, and the impact energy at the temperature of 40 DEG C below zero is larger than 27J.
Description
Technical field
The present invention relates to a kind of yield strength 900 ~ 1000MPa level high-strength steel and production method thereof, the high-strength steel obtained, its yield strength is 900 ~ 1080MPa, tensile strength is 950 ~ 1200MPa, unit elongation >10%,-40 DEG C of ballistic work >40J, microstructure is tempered martensite.
Background technology
Adopt the component of the mobile equipments such as the girder construction of high strength easy Welded Structural Steel manufacturing engineering machinery, the arm of lifting machine and the car body of wagon tremie, all can alleviate equipment self-weight, reduce fuel consumption, increase work efficiency.Along with the aggravation of international competition, the component of the mobile equipments such as the car body of high strength easy welded construction steel making harbour machinery, mining machinery, excavator, the girder construction of shovel loader, the arm of lifting machine and wagon tremie is adopted to become trend.Due to engineering machinery high-performance, maximization, light-weighted demand for development, the intensity rank of steel for engineering machinery constantly rises, and is climbed to 700MPa, 900MPa, 1000MPa and even 1100MPa from 500 ~ 600MPa level.Engineering machinery super-high strength steel, due to the environment for use of its harshness and stress condition, has strict requirement to steel product quality, comprises strength property, impact property, buckling performance, welding property and plate shape etc.
The enterprise of the high tensile steel plate of current domestic production surrender 900 ~ 1000MPa rank is little, Chinese patent CN102560274A describes a kind of production method of surrendering 1000MPa grade high-strength degree Plate Steel, what adopt is quench in furnace+tempering process, opens flat equipment requirements high to steel plate.Chinese patent CN102134680A describes a kind of production method of yield strength 960MPa level high-strength steel, adopt lower carbon content design and higher Cr content, C:0.07% ~ 0.09%, Cr:1.05 ~ 1.15%, this patent is not containing Nb, Ti, V microalloy element, Cr content is higher, is unfavorable for welding.Chinese patent CN101397640A describes a kind of production method of surrendering 960Mpa grade high-strength steel plate, adopts higher Mo content design and higher tempering temperature, Mo content 0.45 ~ 0.57%, tempering temperature 550 ~ 600 DEG C.
Composition Design of the prior art does not control joint plasticity and toughness over-all properties, does not consider intensity and the toughness of being improved finished steel plate by control inclusion and structure property heredity yet.
Summary of the invention
The object of the present invention is to provide a kind of yield strength 900 ~ 1000MPa grade high-strength steel and production method thereof, the microstructure of this high-strength steel is tempered martensite, yield strength is 900 ~ 1080MPa, tensile strength is 950 ~ 1200MPa, unit elongation >10% ,-40 DEG C of ballistic work >40J.
In order to achieve the above object, technical scheme provided by the invention is:
A kind of yield strength 900 ~ 1000MPa level high-strength steel, its chemical component weight per-cent is: C:0.07 ~ 0.15%, Si:0.10 ~ 0.30%, Mn:0.80 ~ 1.60%, Cr:0.20 ~ 0.70%, Mo:0.10 ~ 0.45%, Ni:0.10 ~ 0.50%, Nb:0.010 ~ 0.030%, Ti:0.010 ~ 0.030%, V:0.010 ~ 0.050%, 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%, all the other are Fe and inevitable impurity, above-mentioned element must meet following relational expression simultaneously: Ceq 0.42 ~ 0.52%, Ceq=C+Mn/6+ (Cr+Mo+V)/5+ (Ni+Cu)/15, 0.8%≤Mo+0.8Ni+0.4Cr+6V≤1.3%, 3.7≤Ti/N≤7.0, 1.0≤Ca/S≤3.0.
Further, the yield strength of described yield strength 900 ~ 1000MPa level high-strength steel is 900 ~ 1080MPa, and tensile strength is 950 ~ 1200MPa, unit elongation >10%,-40 DEG C of ballistic work >40J, microstructure is tempered martensite.
In Composition Design of the present invention:
Carbon: solution strengthening, the intensity of adjustment martensitic stucture and plasticity and toughness, the press quenching state tensile strength of low carbon martensite of the present invention and the relation of C content are following relation: Rm=2940C (%)+820 (MPa), Rm is press quenching state tensile strength, C content just can ensure that more than 0.07% quenching state tensile strength is greater than 1000MPa, adjust intensity further by tempering again, improve toughness; The higher meeting of C content causes the raising of overall carbon equivalent, easily cracks during welding, and C content scope of the present invention is 0.07 ~ 0.15%.
Silicon: can play good desoxydatoin when Si content is more than 0.10%, Si content easily produces red iron sheet more than 0.30%, and easily worsen the toughness of martensite high-strength steel when Si content is higher, silicone content scope of the present invention is 0.10 ~ 0.30%.
Manganese: Mn element is more than 0.8% hardening capacity that can improve steel, Mn content easily produces the inclusion such as segregation and MnS more than 1.6%, and worsen the toughness of martensite high-strength steel, Mn content range of the present invention is 0.80 ~ 1.60%.
Chromium: Cr element can improve the hardening capacity of steel more than 0.2%, be conducive to forming full martensitic stucture when quenching, Cr can form the carbide of Cr in about 400 ~ 500 DEG C tempering ranges, there is the effect that anti-average tempering is softening, Cr content there will be larger spark more than 0.70% when welding, affect welding quality, Cr content range of the present invention is 0.20 ~ 0.70%.
Molybdenum: the Mo element of more than 0.10% has the hardening capacity improving steel, is conducive to forming full martensitic stucture when quenching; Can react with C under the high temperature of Mo more than 400 DEG C and form compound particle, there is the high-temperature resistant tempered softening effect softening with welding joint, the too high meeting of Mo content causes carbon equivalent to improve, worsen welding property, Mo belongs to precious metal simultaneously, can raise the cost, Mo content range of the present invention is 0.10 ~ 0.45%.
Nickel: the Ni element of more than 0.10% has refinement martensitic stucture, improves the effect of the low-temperature impact toughness of steel, the too high meeting of Ni content causes carbon equivalent to improve, worsen welding property, Ni belongs to precious metal simultaneously, and can raise the cost, Ni content range of the present invention is 0.10 ~ 0.50%.
Niobium, titanium and vanadium: Nb, Ti and V are microalloy element, form nano level precipitate with the element such as C, N, suppresses growing up of austenite crystal when heating; Nb can improve non-recrystallization critical temperature Tnr, expanding production window; The tiny precipitate particle of Ti can improving welding property; V reacts with N and C and separates out nano level V (C, N) particle in drawing process, can improve the intensity of steel; Content of niobium scope of the present invention is 0.010 ~ 0.030%, and titanium content scope is 0.010 ~ 0.030%, and content of vanadium scope is 0.010 ~ 0.050%.
Boron: the B of trace can improve the hardening capacity of steel, and improve the intensity of steel, the B more than 0.0030% easily produces segregation, and form carbon-boron compound, the toughness of severe exacerbation steel, therefore, Boron contents scope of the present invention is 0.0005 ~ 0.0030%.
Aluminium: Al is used as reductor, and the Al adding more than 0.02% in steel can crystal grain thinning, improves impelling strength, and Al content easily produces the oxide inclusion defect of Al more than 0.06%, Al content range of the present invention is 0.02 ~ 0.06%.
Calcium: the micro-Ca element more than 0.001% can the effect playing scavenging agent d in smelting steel process, improves the toughness of steel; Ca content easily forms the compound of larger-size Ca more than 0.004%, can worsen toughness on the contrary, Ca content range of the present invention is 0.001 ~ 0.004%.
Nitrogen: application claims strictly controls the scope of N element, the N element of more than 0.002% can be reacted with V and C and be formed nano level V (C in drawing process, N) particle, plays the effect of precipitation strength, in welding process, also can resist heat-affected zone softened by precipitation strength; N content easily causes more than 0.005% forming thick precipitate particle, worsens toughness.N content scope of the present invention is 0.002 ~ 0.005%.
Phosphorus, sulphur and oxygen: P, S and O affect the moulding of steel, toughness as impurity element, and the present invention controls its scope and is respectively P≤0.020%, S≤0.010%, O≤0.008%.
Press quenching type yield strength of the present invention is the high-strength steel of 900 ~ 1000MPa level, carbon equivalent Ceq need meet: Ceq 0.42 ~ 0.52%, Ceq=C+Mn/6+ (Cr+Mo+V)/5+ (Ni+Cu)/150, Ceq is too low easily occurs that welding joint softens, the too high easy appearance welding tiny crack of Ceq.
The present invention is by control 0.8%≤Mo+0.8Ni+0.4Cr+6V≤1.3%, the grade being mainly used in guarantee 900 ~ 1000MPa high-strength steel mates welding by force, regulate intensity and the low-temperature flexibility of welded heat affecting zone, reach the optimum matching with mother metal armor plate strength and low-temperature flexibility.Wherein Mo, Ni and Cr element can reduce the critical cooling velocity of steel, improves the hardening capacity of steel, improves the intensity of welding joint; Mo at high temperature reacts with C and forms compound, has the effect that opposing welding joint is softening; Mo and Ni element all has thinning microstructure, improves the effect of toughness; V and N reaction generates nano level V (C, N) particle can resist welding joint softened; The collocation of Mo, Ni, Cr and V element can regulate intensity and the toughness of welded heat affecting zone according to strength of parent, lower than the intensity of 0.8% welding joint and low-temperature flexibility all lower; Higher higher than 1.3% strength of welded joint, easily produce welding crack.
B atom in steel can be protected by controlling 3.7≤Ti/N≤7.0, making the abundant solid solution of B, improving hardening capacity.
The sulfide nodularization of steel grade can be made by controlling 1.0≤Ca/S≤3.0, improving low-temperature flexibility and the welding property of steel.
The production method of yield strength 900 ~ 1000MPa level high-strength steel of the present invention, comprises the steps:
1) smelt, cast
Adopt converter or Electric furnace steel making by following chemical composition, refining, casting forms strand; Chemical component weight per-cent is: C:0.07 ~ 0.15%, Si:0.10 ~ 0.30%, Mn:0.80 ~ 1.60%, Cr:0.20 ~ 0.70%, Mo:0.10 ~ 0.45%, Ni:0.10 ~ 0.50%, Nb:0 ~ 0.030%, Ti::0.010 ~ 0.030%, V:0.010 ~ 0.050%, 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%, all the other are Fe and inevitable impurity; Above-mentioned element must meet following relational expression simultaneously:
Ceq 0.42～0.52％，Ceq＝C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15；0.8％≤Mo+0.8Ni+0.4Cr+6V≤1.3％；3.7≤Ti/N≤7.0；1.0≤Ca/S≤3.0；
2) heat
Strand is heated to 1150 ~ 1270 DEG C, after strand heart portion temperature reaches furnace temperature, starts insulation, soaking time >1.5h;
3) rolling
The reciprocal rolling of single chassis or multi-frame hot continuous rolling is adopted strand to be rolled to target thickness, last passes draft of rolling >15%; Finishing temperature is 820 ~ 920 DEG C, and finishing temperature Tf meets simultaneously: Ar3<Tf<Tnr; Wherein, Ar3 is that hypoeutectoid steel austenite starts temperature to ferritic transformation; Tnr is non-recrystallization critical temperature; Ar
3=901-325C-92Mn-126Cr-67Ni-149Mo; Tnr=887+464C+ (6445Nb-644sqrt (Nb))+(732V-230sqrt (V))+890Ti+363Al-357Si;
4) press quenching
By step 3) rolled piece that obtains carries out section cooling online, is quenched to final cooling temperature, and final cooling temperature is, below (Ms-150) DEG C, form the steel plate of full martensitic stucture; Wherein, Ms is Ms (martensite start) point, Ms=539-423C-30.4Mn-17.7Ni-12.1Cr-11.0Si-7.0Mo; Speed of cooling is V>e
(5.3-2.53C-0.16Si-0.82Mn-0.95Cr-1.87Mo-160B)dEG C/s;
5) tempering heat treatment
By step 4) steel plate that obtains carries out tempering heat treatment, and tempering temperature is 400 ~ 550 DEG C, starts insulation after steel plate heart portion reaches tempering temperature, and insulation 20 ~ 180min, namely obtains the High Strength Steel Plate of yield strength 900 ~ 1000MPa rank.
Further, the yield strength of the high-strength steel of the yield strength 900 ~ 1000MPa rank obtained is 900 ~ 1080MPa, and tensile strength is 950 ~ 1200MPa, unit elongation >10%,-40 DEG C of ballistic work >40J, microstructure is tempered martensite.
In the following relational expression that the present invention relates to: Ceq=C+Mn/6+ (Cr+Mo+V)/5+ (Ni+Cu)/15, Mo+0.8Ni+0.4Cr+6V, Ti/N, Ca/S, each symbol of element represents the weight percentage of corresponding element; The following calculation formula related to: Ar
3=901-325C-92Mn-126Cr-67Ni-149Mo, Tnr=887+464C+ (6445Nb-644sqrt (Nb))+(732V-230sqrt (V))+890Ti+363Al-357Si, Ms=539-423C-30.4Mn-17.7Ni-12.1Cr-11.0Si-7.0Mo, and V>e
(5.3-2.53C-0.16Si-0.82Mn-0.95Cr-1.87Mo-160B)in each symbol of element represent weight percentage × 100 of corresponding element.
In the production method of yield strength 900 ~ 1000MPa level high-strength steel of the present invention:
In strand heating process, control that Heating temperature is greater than 1150 DEG C, heart portion soaking time >1.5h can ensure the abundant solid solution of alloying element; When Heating temperature is more than 1270 DEG C, austenite crystal is excessively grown up, and causes intergranular bonding force to weaken, easily cracks when rolling; Heating temperature easily causes billet surface decarburization more than 1270 DEG C in addition, impacts finished product mechanical property.
Finishing temperature is greater than Ar
3be to ensure in austenitic area rolling, it is to ensure in the rolling of austenite Unhydrated cement that finishing temperature is less than Tnr, can martensitic stucture after fining austenite grains and quenching in the rolling of austenite Unhydrated cement, thus improves the obdurability of steel.
In the operation of rolling, carrying out aximal deformation value rolling is to form enough energy of deformation at Unhydrated cement, at Ar
3austenite recrystallization is brought out, crystal grain thinning in ~ Tnr temperature range.
The steel tempering temperature of component system of the present invention is more than 400 DEG C, and when being incubated more than 20min after steel plate heart portion reaches tempering temperature, the supersaturation carbon atom precipitation in quenched martensite forms spherical Fe
3c cementite, alloy Mo and V can react with C and form tiny alloy carbide at such a temperature, can improve plasticity and the toughness of steel, effectively removes the internal stress of steel simultaneously.Tempering temperature is more than 550 DEG C or the long spherical Fe of high soaking time
3c cementite and alloy carbide generation alligatoring, can worsen the toughness of steel on the contrary, and reduce the intensity of steel; By adjustment tempering temperature and tempering time can ensure by force, toughness realizes optimum matching.
Beneficial effect of the present invention:
The present invention adopts controlled rolling and controlled cooling and press quenching+tempering process, chemically Composition Design, mother metal tissue, quenching temperature, tempering Heating temperature angularly control, ensure that the yield strength 900 ~ 1000MPa level high-strength steel produced is while having superstrength, also has good unit elongation, low-temperature impact toughness.
The present invention is by the content of element and the obdurabilities of match control mother metal welding joint such as control Mo, Ni, Cr, V, and by control Ti, N ratio, Ca, S are than the toughness improving mother metal steel plate and welding joint.Utilize structure property hereditary property by the obdurability of process improving finished steel plate.
Accompanying drawing explanation
Fig. 1 is that the 1# of the embodiment of the present invention 1 tests steel typical gold phase constitution figure.
Fig. 2 is that the 5# of the embodiment of the present invention 5 tests steel typical gold phase constitution figure.
Fig. 3 is that the 8# of the embodiment of the present invention 8 tests steel typical gold phase constitution figure.
Embodiment
Below in conjunction with embodiment, the present invention will be further described.
The technological process of production of super-high strength steel of the present invention is: converter or Electric furnace steel making → external refining → continuous casting → heating → rolling → cooling → thermal treatment.
The production method of 900 ~ 1000MPa level high-strength steel of the embodiment of the present invention 1 ~ 10, comprises the steps:
1) adopt 50kg vacuum electric furnace to smelt, composition is as shown in table 1, by the strand that the pouring molten steel of smelting becomes 120mm thick, puts into electric furnace and heats.
2) adopt multi-pass strand to be rolled into the steel plate of target thickness 10mm, finishing temperature is 820 ~ 920 DEG C, and finishing temperature Tf meets simultaneously: Ar
3<Tf<Tnr; End percentage pass reduction setting 17%.
3) to the rolled piece after rolling, section cooling is carried out online; Laminar cooling system controlled cooling model speed V>e
(5.3-2.53C-0.16Si-0.82Mn-0.95Cr-1.87Mo-160B)dEG C/s; Final cooling temperature is below (Ms-150) DEG C.
4) tempering heat treatment: tempering temperature is 400 ~ 550 DEG C, tempering time is 20 ~ 180min behind steel plate heart portion to furnace temperature, obtains 900 ~ 1000MPa level high-strength steel of the present invention.
5) steel plate after press quenching+tempering is carried out longitudinal stretching and impact of collision test.
Concrete composition, processing parameter are as shown in table 1, table 2.The performance that each embodiment model is corresponding is as shown in table 3.
Fig. 1 ~ Fig. 3 gives the metallographic structure figure that embodiment 1,5,8 tests steel.As can be seen from Fig. 1 ~ Fig. 3 metallograph, the metallographic structure of finished steel plate is homogeneous lath-shaped tempered martensite, and organizes fine and closely woven.
The present invention adopts press quenching+tempering process, chemically Composition Design, mother metal tissue, quenching temperature, tempering Heating temperature angularly control, ensure that the 900 ~ 1000MPa level high-strength steel produced is while having superstrength, also has good unit elongation, low-temperature impact toughness.
Table 1 unit: weight percent
| Embodiment | C | Si | Mn | Cr | Mo | V | Ni | Nb | Ti | B | Al | Ca | P | S | N | O |
| 1 | 0.08 | 0.1 | 1.12 | 0.7 | 0.37 | 0.05 | 0.43 | 0.01 | 0.01 | 0.0015 | 0.06 | 0.0016 | 0.012 | 0.0013 | 0.0027 | 0.0026 |
| 2 | 0.08 | 0.1 | 1.12 | 0.7 | 0.37 | 0.05 | 0.43 | 0.01 | 0.01 | 0.0015 | 0.06 | 0.0016 | 0.012 | 0.0013 | 0.0027 | 0.0026 |
| 3 | 0.07 | 0.29 | 1.6 | 0.55 | 0.2 | 0.05 | 0.1 | 0.012 | 0.015 | 0.0005 | 0.023 | 0.0039 | 0.016 | 0.0016 | 0.0028 | 0.0063 |
| 4 | 0.07 | 0.29 | 1.6 | 0.55 | 0.2 | 0.05 | 0.1 | 0.012 | 0.015 | 0.0005 | 0.023 | 0.0039 | 0.016 | 0.0016 | 0.0028 | 0.0063 |
| 5 | 0.15 | 0.25 | 0.8 | 0.22 | 0.4 | 0.035 | 0.16 | 0.02 | 0.029 | 0.002 | 0.05 | 0.0026 | 0.017 | 0.0016 | 0.0042 | 0.0054 |
| 6 | 0.15 | 0.25 | 0.8 | 0.22 | 0.4 | 0.035 | 0.16 | 0.02 | 0.029 | 0.002 | 0.05 | 0.0026 | 0.017 | 0.0016 | 0.0042 | 0.0054 |
| 7 | 0.13 | 0.22 | 1.1 | 0.2 | 0.45 | 0.01 | 0.28 | 0.03 | 0.02 | 0.0016 | 0.035 | 0.004 | 0.011 | 0.0014 | 0.0036 | 0.0071 |
| 8 | 0.13 | 0.22 | 1.1 | 0.2 | 0.45 | 0.01 | 0.28 | 0.03 | 0.02 | 0.0016 | 0.035 | 0.004 | 0.011 | 0.0014 | 0.0036 | 0.0071 |
| 9 | 0.086 | 0.21 | 0.95 | 0.63 | 0.1 | 0.048 | 0.49 | 0.018 | 0.019 | 0.003 | 0.025 | 0.0024 | 0.008 | 0.0023 | 0.0049 | 0.0021 |
| 10 | 0.086 | 0.21 | 0.95 | 0.63 | 0.1 | 0.048 | 0.49 | 0.018 | 0.019 | 0.003 | 0.025 | 0.0024 | 0.008 | 0.0023 | 0.0049 | 0.0021 |
Table 2
Table 3
Note: in-40 DEG C of ballistic work test-results, three row represent the test result of three parallel samples respectively.
Claims (6)
1. yield strength 900 ~ 1000MPa level high-strength steel, its chemical component weight per-cent is: C:0.07 ~ 0.15%, Si:0.10 ~ 0.30%, Mn:0.80 ~ 1.60%, Cr:0.20 ~ 0.70%, Mo:0.10 ~ 0.45%, Ni:0.10 ~ 0.50%, Nb:0.010 ~ 0.030%, Ti:0.010 ~ 0.030%, V:0.010 ~ 0.050%, 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%, all the other are Fe and inevitable impurity, above-mentioned element must meet following relational expression simultaneously:
Ceq 0.42～0.52％，Ceq＝C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15；
0.8％≤Mo+0.8Ni+0.4Cr+6V≤1.3％；3.7≤Ti/N≤7.0；1.0≤Ca/S≤3.0。
2. yield strength 900 ~ 1000MPa level high-strength steel according to claim 1, it is characterized in that, its microstructure is tempered martensite.
3. yield strength 900 ~ 1000MPa level high-strength steel according to claim 1, it is characterized in that, its yield strength is 900 ~ 1080MPa, and tensile strength is 950 ~ 1200MPa, unit elongation >10% ,-40 DEG C of ballistic work >27J.
4. a production method for yield strength 900 ~ 1000MPa level high-strength steel, is characterized in that, comprise the steps:
1) smelt, cast
Adopt converter or Electric furnace steel making, refining by following chemical composition, casting forms strand; Its chemical component weight per-cent is: C:0.07 ~ 0.15%, Si:0.10 ~ 0.30%, Mn:0.80 ~ 1.60%, Cr:0.20 ~ 0.70%, Mo:0.10 ~ 0.45%, Ni:0.10 ~ 0.50%, Nb:0 ~ 0.030%, Ti:0.010 ~ 0.030%, V:0.010 ~ 0.050%, 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%, all the other are Fe and inevitable impurity; Above-mentioned alloying element must meet following relational expression simultaneously:
Ceq 0.42～0.52％，Ceq＝C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15；0.8％≤Mo+0.8Ni+0.4Cr+6V≤1.3％；3.7≤Ti/N≤7.0；1.0≤Ca/S≤3.0；
2) heat
Strand is heated to 1150 ~ 1270 DEG C, heart portion starts insulation after reaching furnace temperature, soaking time >1.5h;
3) rolling
The reciprocal rolling of single chassis or multi-frame hot continuous rolling is adopted strand to be rolled to target thickness, last passes draft of rolling >15%; Finishing temperature is 820 ~ 920 DEG C, and finishing temperature Tf meets simultaneously: Ar
3<Tf<Tnr; Wherein, Ar
3for hypoeutectoid steel austenite starts temperature to ferritic transformation, Tnr is non-recrystallization critical temperature;
Ar
3＝901-325C-92Mn-126Cr-67Ni-149Mo；
Tnr＝887+464C+(6445Nb-644sqrt(Nb))+(732V-230sqrt(V))+890Ti+363Al-357Si；
4) press quenching
By step 3) rolled piece that obtains carries out section cooling online, and be quenched to final cooling temperature, obtain steel plate; Final cooling temperature is that below (Ms-150) DEG C, Ms is Ms (martensite start) point, Ms=539-423C-30.4Mn-17.7Ni-12.1Cr-11.0Si-7.0Mo;
Wherein, speed of cooling V>e
(5.3-2.53C-0.16Si-0.82Mn-0.95Cr-1.87Mo-160B)dEG C/s;
5) tempering heat treatment
By step 4) steel plate that obtains carries out tempering heat treatment, and tempering temperature is 400 ~ 550 DEG C, and steel plate heart portion reaches insulation 20 ~ 180min after tempering temperature, namely obtains the High Strength Steel Plate of 900 ~ 1000MPa rank.
5. the production method of yield strength 900 ~ 1000MPa level high-strength steel according to claim 4, is characterized in that, its microstructure of High Strength Steel Plate that this production method obtains is tempered martensite.
6. the production method of yield strength 900 ~ 1000MPa level high-strength steel according to claim 4, it is characterized in that, the yield strength of the High Strength Steel Plate that this production method obtains is 900 ~ 1080MPa, tensile strength is 950 ~ 1200MPa, unit elongation >10% ,-40 DEG C of ballistic work >27J.
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