CN103589950B - The thermal treatment process of the boron micro-alloyed high-strength steel of vanadium - Google Patents
The thermal treatment process of the boron micro-alloyed high-strength steel of vanadium Download PDFInfo
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Abstract
The invention discloses the thermal treatment process of the boron micro-alloyed high-strength steel of a kind of vanadium, comprising: prequenching, intercritical hardening and low-temperaturetempering.The boron micro-alloyed high-strength steel of vanadium of the present invention has excellent mechanical property, can be applied on plate product, building material product and property product made from steel.Heat treating method of the present invention makes the intensity of steel significantly increase, and has good ductility simultaneously.
Description
Technical field
The present invention relates to ferrous materials technical field of heat treatment, specifically, relate to the thermal treatment process of the boron micro-alloyed high-strength steel of a kind of vanadium.
Background technology
In the production process of steel product, certain thermal treatment process is usually adopted to improve the performance of steel.Intercritical hardening is also known as critical area quenching, the hypoeutectoid structure iron with equilibrium state or nonequilibrium state original structure is heated to the two-phase region (namely intercritical temperature is interval) that ferrite and austenite coexist, held for some time, then carries out the thermal treatment process of quenching.Different from the complete quenching technology of routine, the Heating temperature of intercritical hardening between transformation temperature Ac1, Ac3, more conventional completely quench reduction by 50 ~ 100 DEG C.Intercritical hardening temperature is lower, but intercritical hardening can not obtain higher yield strength, and therefore the yield tensile ratio of steel is lower, and intensity is lower, and fatigue lifetime is lower.Therefore, need to adjust the composition of steel, adopt the thermal treatment process improved to improve the intensity of steel.
Summary of the invention
Technical problem to be solved by this invention is to provide the thermal treatment process of the boron micro-alloyed high-strength steel of a kind of vanadium, can produce the boron micro-alloyed high-strength steel of the vanadium with better mechanical property.
Technical solution of the present invention is as follows:
A thermal treatment process for the boron micro-alloyed high-strength steel of vanadium, comprising: prequenching, intercritical hardening and low-temperaturetempering, and the Heating temperature of described prequenching is 900-940 DEG C, 900-940 DEG C of insulation 60-180 minute, then shrend; The Heating temperature of described intercritical hardening is 780 DEG C-820 DEG C, is 30-120 minute 780 DEG C of-820 DEG C of soaking times, then shrend; The tempering temperature of described low-temperaturetempering is 200-240 DEG C, is 60-300 minute, then furnace cooling 200-240 DEG C of soaking time; The mass percentage of the chemical composition of the boron micro-alloyed high-strength steel of described vanadium obtained comprises: C≤0.25%, Mn≤1.7%, Si≤0.8%, S≤0.03%, P≤0.03%, V≤0.1%, B 0.001%-0.003%, and surplus is Fe and impurity.
Further, the mass percentage of the chemical composition of the boron micro-alloyed high-strength steel of described vanadium obtained comprises: C 0.21%, Mn 1.35%, Si 0.45%, S 0.02%, P 0.015%, V0.07%, B 0.0018%; Or, C 0.25%, Mn 1.50%, Si 0.45%, S 0.02%, P 0.015%, V0.09%, B 0.0025%; Or, C 0.24%, Mn 1.7%, Si 0.8%, S 0.03%, P 0.03%, V0.1%, B 0.003%; Or, C 0.22%, Mn 1.40%, Si 0.40%, S 0.01%, P 0.015%, V0.08%, B 0.001%.
Technique effect of the present invention is as follows:
1, the boron micro-alloyed high-strength steel of vanadium of the present invention has excellent mechanical property, and tensile strength reaches 1200-1320MPa, yield strength 950-1050MPa, unit elongation 19-24%.
2, the boron micro-alloyed high-strength steel of vanadium of the present invention can be applied on plate product, building material product and property product made from steel.
3, heat treating method of the present invention makes the intensity of steel significantly increase, and has good ductility simultaneously.
Accompanying drawing explanation
Fig. 1 is the schema of the boron micro-alloyed high-strength steel thermal treatment process of vanadium of the present invention;
Fig. 2 is the schematic diagram of the boron micro-alloyed high-strength steel thermal treatment process of vanadium of the present invention;
Fig. 3 is the metallographic structure figure of the embodiment of the present invention 1 round steel bar As rolled;
Fig. 4 is the metallographic structure figure of round steel bar after the embodiment of the present invention 1 prequenching;
Fig. 5 is the metallographic structure figure of round steel bar after the embodiment of the present invention 1 intercritical hardening;
Fig. 6 is the metallographic structure figure of round steel bar after the embodiment of the present invention 1 low-temperaturetempering.
Embodiment
The chemical composition mass percentage of the initial steel material of the present invention is C≤0.25%, Mn≤1.7%, Si≤0.8%, S≤0.03%, P≤0.03%, V≤0.1%, B 0.001%-0.003%, and surplus is Fe and impurity.The present invention is the mechanical property significantly improving steel, adds this high-hardenability element of boron.Form interrupted net to prevent boride from separating out along austenite grain boundary, in steel, the best retention amount of boron is 0.001% ~ 0.003%.The vanadium of solid solution can improve the hardening capacity of steel, and V (C, N) precipitate can significantly improve the resistance to elevated temperatures of steel.
As illustrated in fig. 1 and 2, schema and the schematic diagram of the boron micro-alloyed high-strength steel thermal treatment process of vanadium of the present invention is respectively.The step of thermal treatment process of the present invention is as follows:
Step S1: prequenching
The Heating temperature of prequenching is 900-940 DEG C, at 900-940 DEG C of insulation 60-180 minute, then carries out shrend.
Step S2: intercritical hardening
The Heating temperature of intercritical hardening is 780 DEG C-820 DEG C, at 780 DEG C-820 DEG C insulation 30-120 minute, then carries out shrend.
Step S3: low-temperaturetempering
The tempering temperature of low-temperaturetempering is 200-240 DEG C, at 200-240 DEG C of insulation 60-300 minute, then this high-strength steel furnace cooling.
The boron micro-alloyed high-strength steel of vanadium is obtained through above-mentioned thermal treatment process.The chemical composition mass percentage of the boron micro-alloyed high-strength steel material of the vanadium after above-mentioned thermal treatment is C≤0.25%, Mn≤1.7%, Si≤0.8%, S≤0.03%, P≤0.03%, V≤0.1%, B 0.001%-0.003%, and surplus is Fe and impurity.
Embodiment 1
Embodiment 1 is the round steel bar of Φ 18.The chemical composition mass percentage of this round steel bar is: C0.21%, Mn 1.35%, Si 0.45%, S 0.02%, P 0.015%, V0.07%, B 0.0018%, and surplus is Fe and inevitable impurity.As shown in Figure 3, be the metallographic structure figure of the embodiment of the present invention 1 round steel bar As rolled.As can be seen from Figure 3, the metallographic structure of this As rolled is ferrite and pearlite.
Measure the critical phase temperature of embodiment 1 steel with the automatic phase transformation instrument of Formaster-F, when cooling after when starting when being respectively steel heating to form austenitic temperature Ac1, hypoeutectoid steel heating, all ferrites all change austenitic temperature Ac3, steel influence of high austenizing temp into, austenite decomposition is the temperature Ar1 of ferrite and pearlite, ferrite starts the temperature Ar3 separated out when cooling after hypoeutectoid steel influence of high austenizing temp.Ac1=724 DEG C of embodiment 1, Ac3=863 DEG C, Ar1=605 DEG C and Ar3=750 DEG C.
Heat-treated by the round steel bar of Φ 18, detailed process is as follows:
By the round steel bar prequenching of Φ 18.The temperature of prequenching is 900 DEG C and is incubated 60min, then shrends at 900 DEG C.By polishing after the polishing of round steel bar sample, with the nital corrosion of 4%, observe under an optical microscope.As shown in Figure 4, be the metallographic structure figure of round steel bar after the embodiment of the present invention 1 prequenching.As can be seen from Figure 4, this is organized as martensite.Again by round steel bar sample intercritical hardening.The temperature of intercritical hardening is 780 DEG C and is incubated 50min, then shrends at 780 DEG C.By polishing after the polishing of round steel bar sample, with the nital corrosion of 4%, observe under an optical microscope.As shown in Figure 5, be the metallographic structure figure of round steel bar after the embodiment of the present invention 1 intercritical hardening.As can be seen from Figure 5, this metallographic structure is martensite, bainite and ferrite.Then by round steel bar sample low-temperaturetempering.The temperature of low-temperaturetempering is 200 DEG C and is incubated 120min, then furnace cooling at 200 DEG C.By polishing after the polishing of round steel bar sample, with the nital corrosion of 4%, observe under an optical microscope.As shown in Figure 6, be the metallographic structure figure of round steel bar after the embodiment of the present invention 1 low-temperaturetempering.As can be seen from Figure 6, this metallographic structure is bainite, ferrite and tempered martensite.
The chemical composition mass percentage obtaining the boron micro-alloyed high-strength steel material of vanadium of embodiment 1 through above-mentioned steps is: C 0.21%, Mn 1.35%, Si 0.45%, S 0.02%, P 0.015%, V0.07%, B 0.0018%, and surplus is Fe and inevitable impurity.
Measure the relative quantity of the boron micro-alloyed high-strength steel ferrite of embodiment 1 vanadium and martensite two-phase with image analyzer, measuring result is in table 1.Tension testing machine carries out tensile test to the boron micro-alloyed high-strength steel of the vanadium of embodiment 1.Its mechanics properties testing value is in table 2.
Embodiment 2
Embodiment 2 is the round steel bar of Φ 25.The chemical composition mass percentage of this round steel bar is: C0.25%, Mn 1.50%, Si 0.45%, S 0.02%, P 0.015%, V0.09%, B 0.0025%, and surplus is Fe and inevitable impurity.The specification of this round steel bar is large than the specification of embodiment 1, and improve the mentality of designing that hardening capacity constituent content (C, V, Mn, B) is this steel chemical composition, the metallographic structure of this As rolled is ferrite and pearlite.
Measure the critical phase temperature of embodiment 2 steel with the automatic phase transformation instrument of Formaster-F, when cooling after when starting when being respectively steel heating to form austenitic temperature Ac1, hypoeutectoid steel heating, all ferrites all change austenitic temperature Ac3, steel influence of high austenizing temp into, austenite decomposition is the temperature Ar1 of ferrite and pearlite, ferrite starts the temperature Ar3 separated out when cooling after hypoeutectoid steel influence of high austenizing temp.Ac1=725 DEG C of embodiment 2, Ac3=860 DEG C, Ar1=606 DEG C and Ar3=745 DEG C.
Heat-treated by the round steel bar of Φ 25, detailed process is as follows:
By the round steel bar prequenching of Φ 25.The temperature of prequenching is 920 DEG C and is incubated 60min, then shrends at 920 DEG C.By polishing after the polishing of round steel bar sample, with the nital corrosion of 4%, observe under an optical microscope, after prequenching, the metallographic structure of round steel bar is martensite.Again by round steel bar sample intercritical hardening, the temperature of intercritical hardening is 800 DEG C and is incubated 60min, then shrends at 800 DEG C.By polishing after the polishing of round steel bar sample, with the nital corrosion of 4%, observe under an optical microscope, this metallographic structure is martensite, bainite and ferrite.Then by round steel bar sample low-temperaturetempering.The temperature of low-temperaturetempering is 230 DEG C and is incubated 120min, then furnace cooling at 230 DEG C.By polishing after the polishing of round steel bar sample, with the nital corrosion of 4%, observe under an optical microscope, this metallographic structure is bainite, ferrite and tempered martensite.
The chemical composition mass percentage obtaining the boron micro-alloyed high-strength steel material of vanadium of embodiment 2 through above-mentioned steps is: C 0.25%, Mn 1.50%, Si 0.45%, S 0.02%, P 0.015%, V0.09%, B 0.0025%, and surplus is Fe and inevitable impurity.
Measure the relative quantity of the boron micro-alloyed high-strength steel ferrite of embodiment 2 vanadium and martensite two-phase with image analyzer, measuring result is in table 1.Tension testing machine carries out tensile test to the boron micro-alloyed high-strength steel of the vanadium of embodiment 2.Its mechanics properties testing value is in table 2.
Embodiment 3
Embodiment 3 is the round steel bar of Φ 25.The chemical composition mass percentage of this round steel bar is: C0.24%, Mn 1.7%, Si 0.8%, S 0.03%, P 0.03%, V0.1%, B 0.003%, and surplus is Fe and inevitable impurity.The specification of this round steel bar is large than the specification of embodiment 1, and improve the mentality of designing that hardening capacity constituent content (C, V, Mn, B) is this steel chemical composition, the metallographic structure of this As rolled is ferrite and pearlite.
Measure the critical phase temperature of embodiment 3 steel with the automatic phase transformation instrument of Formaster-F, when cooling after when starting when being respectively steel heating to form austenitic temperature Ac1, hypoeutectoid steel heating, all ferrites all change austenitic temperature Ac3, steel influence of high austenizing temp into, austenite decomposition is the temperature Ar1 of ferrite and pearlite, ferrite starts the temperature Ar3 separated out when cooling after hypoeutectoid steel influence of high austenizing temp.Ac1=725 DEG C of embodiment 2, Ac3=862 DEG C, Ar1=604 DEG C and Ar3=748 DEG C.
Heat-treated by the round steel bar of Φ 25, detailed process is as follows:
By the round steel bar prequenching of Φ 25.The temperature of prequenching is 940 DEG C and is incubated 120min, then shrends at 940 DEG C.By polishing after the polishing of round steel bar sample, with the nital corrosion of 4%, observe under an optical microscope, after prequenching, the metallographic structure of round steel bar is martensite.Again by round steel bar sample intercritical hardening, the temperature of intercritical hardening is 810 DEG C and is incubated 30min, then shrends at 810 DEG C.By polishing after the polishing of round steel bar sample, with the nital corrosion of 4%, observe under an optical microscope, this metallographic structure is martensite, bainite and ferrite.Then by round steel bar sample low-temperaturetempering.The temperature of low-temperaturetempering is 220 DEG C and is incubated 300min, then furnace cooling at 220 DEG C.By polishing after the polishing of round steel bar sample, with the nital corrosion of 4%, observe under an optical microscope, this metallographic structure is bainite, ferrite and tempered martensite.
The chemical composition mass percentage obtaining the boron micro-alloyed high-strength steel material of vanadium of embodiment 3 through above-mentioned steps is: C 0.24%, Mn 1.7%, Si 0.8%, S 0.03%, P 0.03%, V0.1%, B 0.003%, and surplus is Fe and inevitable impurity.
Measure the relative quantity of the boron micro-alloyed high-strength steel ferrite of embodiment 3 vanadium and martensite two-phase with image analyzer, measuring result is in table 1.Tension testing machine carries out tensile test to the boron micro-alloyed high-strength steel of the vanadium of embodiment 3.Its mechanics properties testing value is in table 2.
Embodiment 4
Embodiment 4 is the round steel bar of Φ 18.The chemical composition mass percentage of this round steel bar is: C0.22%, Mn 1.40%, Si 0.40%, S 0.01%, P 0.015%, V0.08%, B 0.001%, and surplus is Fe and inevitable impurity.The metallographic structure of this As rolled is ferrite and pearlite.
Measure the critical phase temperature of embodiment 4 steel with the automatic phase transformation instrument of Formaster-F, when cooling after when starting when being respectively steel heating to form austenitic temperature Ac1, hypoeutectoid steel heating, all ferrites all change austenitic temperature Ac3, steel influence of high austenizing temp into, austenite decomposition is the temperature Ar1 of ferrite and pearlite, ferrite starts the temperature Ar3 separated out when cooling after hypoeutectoid steel influence of high austenizing temp.Ac1=723 DEG C of embodiment 1, Ac3=861 DEG C, Ar1=607 DEG C and Ar3=751 DEG C.
Heat-treated by the round steel bar of Φ 18, detailed process is as follows:
By the round steel bar prequenching of Φ 18.The temperature of prequenching is 910 DEG C and is incubated 180min, then shrends at 910 DEG C.By polishing after the polishing of round steel bar sample, with the nital corrosion of 4%, observe under an optical microscope, after prequenching, the metallographic structure of round steel bar is martensite.Again by round steel bar sample intercritical hardening.The temperature of intercritical hardening is 820 DEG C and is incubated 120min, then shrends at 820 DEG C.By polishing after the polishing of round steel bar sample, with the nital corrosion of 4%, observe under an optical microscope, this metallographic structure is martensite, bainite and ferrite.Then by round steel bar sample low-temperaturetempering.The temperature of low-temperaturetempering is 240 DEG C and is incubated 60min, then furnace cooling at 240 DEG C.By polishing after the polishing of round steel bar sample, with the nital corrosion of 4%, observe under an optical microscope, this metallographic structure is bainite, ferrite and tempered martensite.
The chemical composition mass percentage obtaining the boron micro-alloyed high-strength steel material of vanadium of embodiment 4 through above-mentioned steps is: C 0.22%, Mn 1.40%, Si 0.40%, S 0.01%, P 0.015%, V0.08%, B 0.001%, and surplus is Fe and inevitable impurity.
Measure the relative quantity of the boron micro-alloyed high-strength steel ferrite of embodiment 4 vanadium and martensite two-phase with image analyzer, measuring result is in table 1.Tension testing machine carries out tensile test to the boron micro-alloyed high-strength steel of the vanadium of embodiment 4.Its mechanics properties testing value is in table 2.
The ferrite of table 1 various embodiments of the present invention and the relative quantity (%) of martensite two-phase
| Embodiment | Martensite (tempering) | Ferrite |
| 1 | 59.15 | 40.85 |
| 2 | 65.12 | 34.88 |
| 3 | 64.01 | 35.99 |
| 4 | 60.27 | 39.73 |
The mechanics properties testing value of table 2 various embodiments of the present invention
The present invention is after quenching in advance, non-equilibrium microstructure martensite is obtained in steel, there is high density dislocation, when heating in (α+γ) two-phase region, martensite dislocation partly remains, these dislocations constitute austenite crystal core nucleating center, increase austenite nucleation rate, and thus austenite primary grain is thinner.Austenite Grain Growth main manifestations is crystal boundary migration, owing to there is second-phase ferrite in tissue, hinders its crystal boundary migration, inhibits Austenite Grain Growth.The migration of crystal boundary is the diffusion of atom near crystal boundary simultaneously, and intercritical hardening Heating temperature is lower, is unfavorable for atomic diffusion, and therefore crystal boundary migration speed is less.The comprehensive action of above factor makes the obvious refinement of the austenite crystal of steel, improves the toughness of steel.Intercritical hardening can significantly improve the obdurability of steel, suppresses steel belt roof bolt fragility.Particularly be organized as the steel of lath martensite before intercritical hardening, after intercritical hardening, its highly malleablized effect is better.
In sum, the invention has the advantages that and propose a kind of new thermal treatment process, namely containing the Asia temperature treatment process of vanadium boron steel, the steel of thermal treatment process process have excellent mechanical property thus, the intensity of steel significantly improves, and have good ductility, tensile strength reaches 1200-1320MPa simultaneously, yield strength 950-1050MPa, unit elongation 19-24%.Threadiness (α+M) duplex structure can be obtained through intercritical hardening, i.e. martensite and ferritic structure, or polyphase structure (martensite+bainite+ferrite), obtain tempered martensite and ferritic structure (or tempered martensite+bainite+ferrite) after tempered.Under this technique, the intensity of steel obviously increases, and plasticity is better, has excellent comprehensive mechanical property.This steel can be applied on plate product, building material product and property product made from steel.
Claims (2)
1. a thermal treatment process for the boron micro-alloyed high-strength steel of vanadium, is characterized in that, comprising: prequenching, intercritical hardening and low-temperaturetempering, and the Heating temperature of described prequenching is 900-940 DEG C, 900-940 DEG C of insulation 60-180 minute, then shrend; The Heating temperature of described intercritical hardening is 780 DEG C-820 DEG C, is 30-120 minute 780 DEG C of-820 DEG C of soaking times, then shrend; The tempering temperature of described low-temperaturetempering is 200-240 DEG C, is 60-300 minute, then furnace cooling 200-240 DEG C of soaking time; The mass percentage of the chemical composition of the boron micro-alloyed high-strength steel of described vanadium obtained comprises: C≤0.25%, Mn≤1.7%, Si≤0.8%, S≤0.03%, P≤0.03%, V≤0.1%, B 0.001%-0.003%, and surplus is Fe and impurity.
2. the thermal treatment process of the boron micro-alloyed high-strength steel of vanadium as claimed in claim 1, it is characterized in that, the mass percentage of the chemical composition of the boron micro-alloyed high-strength steel of described vanadium obtained comprises: C0.21%, Mn 1.35%, Si 0.45%, S 0.02%, P 0.015%, V0.07%, B 0.0018%; Or, C 0.25%, Mn 1.50%, Si 0.45%, S 0.02%, P 0.015%, V0.09%, B 0.0025%; Or, C 0.24%, Mn 1.7%, Si 0.8%, S 0.03%, P 0.03%, V0.1%, B 0.003%; Or, C 0.22%, Mn 1.40%, Si 0.40%, S 0.01%, P 0.015%, V0.08%, B 0.001%.
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| CN102747274A (en) * | 2012-07-13 | 2012-10-24 | 江苏永钢集团有限公司 | Vanadium-boron microalloyed waste heat treatment reinforced bar steel and production technique thereof |
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| CN102747274A (en) * | 2012-07-13 | 2012-10-24 | 江苏永钢集团有限公司 | Vanadium-boron microalloyed waste heat treatment reinforced bar steel and production technique thereof |
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