CN107988563B - A kind of fine grain ultra-high strength and toughness high speed axle steel and its heat treatment method - Google Patents
A kind of fine grain ultra-high strength and toughness high speed axle steel and its heat treatment method Download PDFInfo
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- CN107988563B CN107988563B CN201711214400.2A CN201711214400A CN107988563B CN 107988563 B CN107988563 B CN 107988563B CN 201711214400 A CN201711214400 A CN 201711214400A CN 107988563 B CN107988563 B CN 107988563B
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- 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
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- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- 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
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
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- 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
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- 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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- 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
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- 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
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- 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
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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Abstract
A kind of high speed axle steel of fine grain ultra-high strength and toughness, the chemical component of the steel is by weight percentage, C:0.24~0.32%, Si:0.20~0.40%, Cr:0.60~1.00%, Mn:0.40~0.70%, V:0.08~0.13%, Nb:0.02~0.10%, Ni:2.70~3.30%, Mo:0.40~0.60%, Alt:0.010~0.040%, P: < 0.010%, S: < 0.010%, O: < 0.0015%, N: < 0.008%, remaining is Fe and inevitable impurity；The present invention also provides the Heat-Treatment of Steel methods simultaneously.The present invention gives full play to effect of each element in axle steel, and is heat-treated using quenching+high tempering twice, and high speed axle is finally made to have the military services such as good shock resistance, antifatigue performance, excellent obdurability matching and good harden ability.The average grain size of austenite grain is 10-13 μm in the tissue of institute's axle steel of the present invention, yield strength Rp0.2>=900MPa, tensile strength Rm >=950MPa, elongation percentage A >=15%, 5mm notch room temperature impact of collision absorb function KU2>=100J, ductile-brittle transition temperature are lower than -80 DEG C.
Description
Technical field
The present invention relates to railcar axle-steel technical field more particularly to a kind of high speed axles of fine grain ultra-high strength and toughness
Steel and its heat treatment method.
Background technique
Axle is most harsh one of the component of rail transit train service condition, bears the self weight of train almost all and bears
Lotus.The highest running speed of High Speed Train in China has broken through 350 kilometers of speed per hour at present, and to 400 kilometers of speed per hour or more
Target development.Further speed-raising will propose higher performance requirement to axle material to 400 kilometers of speed per hour or more, it is ensured that tool
There are enough safeties, reliability and long life.Fatigue fracture is the principal mode for causing axle to fail, therefore, axle
Material need to have high-intensitive, high tenacity and the two excellent matching, can effectively hinder the germinating and extension of fatigue crack,
To guarantee the higher fatigue strength of axle and sufficiently long service life.Due to various countries' national conditions and technical thought difference, the world is each
The axle material of railway developed country high-speed railway is broadly divided into two major classes: high-quality medium carbon steel and high strength alloy steel.Such as Japan
The Shinkansen high-speed railway axle generallys use carbon steel (S38C), using surface mid frequency induction hardening heat treatment process, work
Skill is complicated, high to the technology controlling and process level requirement of equipment and personnel；European high-speed railway axle material then mostly uses greatly low-alloy
Structural steel (such as EA4T) can be obtained respective organization and performance by traditional Tempering and Quenching mode, but since this steel closes
Gold content is lower, and big section axle has harden ability deficiency, and axle section structure and performance are uneven, influence its entirety
Performance；European high-speed rail axle material small part selects 30NiCrMoV12 medium alloy constructional steel, in steel containing Cr0.60~
2.70~3.30wt.% of 1.00wt.%, Ni, 0.40~0.60wt.% of Mo, 0.08~0.13wt.% of V, such steel grade are quenched
Permeability is good, can oil quenching, hardness is high, corrosion resistance and good.It is real that horizontal and axle manufacturing enterprise is smelted according to the current steel billet in China
Border heat treatment process equips situation, and alloying Tempering and Quenching has preferentially been selected in the development for the high-speed train axle that domesticizes
Technology path.
Summary of the invention
In view of the above analysis, the present invention is intended to provide a kind of bullet train axle of vanadium containing niobium of fine grain superhigh tenacity is used
Steel.In chemical component, use in low C, the Alloying Design based on Cr, Ni, using Nb, V, Mo cooperate with multiple elements design it is micro-
Alloying thinking, it is preferred that emphasis is the Proper Match of C, Nb, V, Mo, Ni element gives full play to its effect in axle steel, obtains
Crystal grain is tiny and microscopic structure based on martensite, and axle steel is made to have the resultant forces such as superhigh intensity and toughness, high-hardenability
Performance, to have good shock resistance and antifatigue equal military services performance.
The purpose of the present invention is mainly achieved through the following technical solutions:
A kind of fine grain ultra-high strength and toughness high speed axle steel, the chemical component of the steel is C by weight percentage:
0.24~0.32%, Si:0.20~0.40%, Cr:0.60~1.00%, Mn:0.40~0.70%, V:0.08~0.13%,
Nb:0.02~0.10%, Ni:2.70~3.30%, Mo:0.40~0.60%, Alt:0.010~0.040%, P: <
0.010%, S: < 0.010%, O: < 0.0015%, N: < 0.008%, remaining is Fe and inevitable impurity.
Further, the average grain size of austenite grain is 10-13 μm in the tissue of the axle steel of acquisition.
Further, the yield strength R of the axle steelp0.2>=900MPa, tensile strength Rm >=950MPa, elongation percentage A
>=15%, 5mm notch room temperature impact of collision absorb function KU2>=100J, ductile-brittle transition temperature are lower than -80 DEG C.
The present invention also provides a kind of fine grain ultra-high strength and toughness high speed axle Heat-Treatment of Steel method, the steel after forging rolling is being quenched
After carrying out quenching heat treatment twice in fiery medium, then tempering is carried out, obtains the axle steel.
Further, carry out first time quenching heat treatment temperature be 920~950 DEG C, the heating and thermal insulation time be 60~
180min。
First time hardening heat selects 920~950 DEG C of progress austenitizings of higher temperature, it is therefore an objective to eliminate forging or rolling
Heterogeneous structure, while making V, Nb etc. parts back dissolving and homogenization, the heat preservation of 60~180min of short period be to inhibit
Austenite grain and the roughening that MX (M:V, Nb, X:C, N) particle has been precipitated, rapid cooling are martensite/bainites in order to obtain
Tissue, while MX being inhibited to be precipitated in cooling high temperature section.
Further, carry out second of quenching heat treatment temperature be 850~900 DEG C, the heating and thermal insulation time be 30~
120min。
In first time, quenching is obtained on more uniform tiny martensite organization foundation, and second of hardening heat selection is compared with low temperature
850-900 DEG C of degree carries out secondary austenitizing, mainly obtains more nanometer MX particles, and reduce AUSTENITE GRAIN COARSENING and incline
To thus soaking time can also extend to 120min, final to obtain uniformly tiny austenite grain and its phase-change organization.
Further, the temperature of tempering is 620~680 DEG C, soaking time 3~8 hours, air-cooled after tempering to arrive room
Temperature.
Further, the hardening media is water, water mist or oil.
The present invention provides a kind of method for preparing fine grain ultra-high strength and toughness high speed axle steel using the heat treatment method,
Using converter, electric furnace or vacuum induction furnace smelting, continuous casting or molding after external refining, slab through the laggard driving axis forging rolling of cogging,
It is air-cooled after forging rolling, the heat treatment is carried out, fine grain ultra-high strength and toughness high speed axle steel is obtained.
Further, the heating temperature of forging rolling is 1150~1250 DEG C, and finish-forging and finishing temperature are not less than 850 DEG C.
Austenite is decomposed phase transformation when to avoid forging rolling, and finish-forging and finishing temperature are not less than 850 DEG C, air-cooled after forging rolling,
Tiny austenite grain and excellent obdurability matching can be obtained using the heat treatment of quenching+high tempering twice.
The effect of each element of the present invention and proportion are according to as follows:
Carbon: most important intensified element and one of the element for improving harden ability, to guarantee enough intensity and harden ability, C
Content must be in 0.24wt.% or more；But when C content is higher than 0.32wt.%, the plasticity and toughness of steel can be significantly reduced, therefore
It is 0.24~0.32wt.% that the present invention, which controls C content,.
Silicon: solution strengthening effect is significant but damages toughness also significant alloying element, while being also main deoxidation in steel
Element.Therefore, the present invention mainly utilizes its deoxidation, and it is 0.20~0.40wt.% that control Si content, which is reduced levels,.
Manganese: the effective element of deoxidization desulfuration, while being also the element for guaranteeing harden ability.But, Mn too high levels similar with Si
The toughness of steel can be significantly reduced, Mn content is too low then effectively deoxidization desulfuration and cannot to guarantee the harden ability of steel.Therefore, control of the present invention
Mn content processed is 0.40~0.70%.
Chromium: moderate Cr is added in steel of the present invention can not only significantly improve the harden ability of steel, moreover it is possible to improve material structure
Uniformity.(Fe, Cr) is formed when Cr is dissolved in cementite3When C alloy cementite, the work of refinement crystal grain and cementite can be played
With being improved the obdurability of material to obtain uniformly tiny quenching crystal grain and tempered structure.But excessive Cr and C
Cr easy to form7C3Equal carbide, damage toughness, the plasticity of steel.Therefore, the present invention control Cr content be 0.60~
1.00wt.%.
Nickel: improve the most effective alloying element of steel toughness, cda alloy cost and its with other alloying elements tough
Property, the collaboration in terms of harden ability, the content of Ni is controlled in 2.70~3.30wt.% in steel of the present invention.
Molybdenum: the present invention obtains tiny austenite grain, significant nano-second-phase by Mo, Nb, V combined microalloying
Precipitation strengthening effect and high resistance to tempering, it is hereby achieved that fine grain, high tenacity high tempering tissue.In addition, Mo with
The rational proportion of the alloying elements such as Cr, Ni and C, V can obtain good harden ability under fine austenite crystalline form.Mo
Content is lower than 0.40wt.%, and above-mentioned effect is limited, too high levels, then above-mentioned effect saturation, which even results in, improves resistance to tempering
Effect is superfluous, will improve the alloy and tempering heat treatment process cost of steel.Therefore, the present invention control Mo content 0.40~
0.60wt.%.
Vanadium: steel of the present invention is middle low-carbon alloy steel, using higher V microalloying, can be precipitated first in forging rolling (V,
Mo secondly a large amount of (V, Mo) (CN) nano-second-phase refinements are precipitated again in) (C, N) fining austenite grains when being heat-treated and reheating
Heat the crystallite dimension of austenite.Again, the V that heat treatment reheats considerable part solid solution in austenite improves harden ability, simultaneously
It is largely precipitated during high tempering, occupies a part of C in steel, form a large amount of, nanometer second based on V, C and Mo
Phase, rather than the cementite of larger particles, to obtain uniformly tiny austenite grain and its phase-change organization.Steel V of the present invention
Content is controlled in 0.08~0.13wt.%, and excessively high V content will lead to that VC Precipitation Temperature is excessively high, amount of precipitation is excessive, particle size
It is easy coarse, is unfavorable for fining austenite grains, it is unfavorable to the intensity, toughness of axle steel etc..Too low V, the above comprehensive function
It is unobvious.
Niobium: for middle low-carbon alloy steel Nb can be precipitated in high temperature forging rolling first using Nb microalloying in steel of the present invention
(C, N), fining austenite grains；Secondly heat treatment reheats the Nb being partially dissolved in austenite easily in crystal boundary segregation, postpones difficult to understand
Family name's body phase transformation, improves the harden ability of steel.Unobvious, effect increase when being higher than 0.10wt.% is acted on more than when lower than 0.02wt.%
It is unobvious, reach saturation.Therefore, steel Nb content control of the present invention is in 0.02~0.10wt.%.
Aluminium: Al is strong deoxidant element, and AlN can be also formed in conjunction with N, can play Grain refinement, and content is lower than
0.020wt.%, the above effect are unobvious.Al content in steel of the present invention is controlled in 0.020~0.040wt.%.
Nitrogen: in the presence of having Nb, V, Al etc. in steel, N can form carbonitride with them, can effectively inhibit austenite
Crystal grain is grown up.Nb, V, Al equal size design of steel of the present invention allow the control range of N content to be < 0.008wt.%.
Oxygen: O easily forms oxide and is mingled with, and is the impurity element of high speed axle steel, unfavorable to toughness, plasticity, serious to reduce
Fatigue behaviour.Steel control O content of the present invention is lower than 0.0015%.
Phosphorus: steel of the present invention is controlled P as impurity element, content < 0.010wt.%.
Sulphur: steel of the present invention is controlled S as impurity element, content < 0.010wt.%.
The present invention has the beneficial effect that:
The present invention provides a kind of novel Cr-Ni-Mo-Nb-V high speed axles steel, multiple using low C, Nb, V, Mo in novel
Microalloying, the design of higher Ni alloy are closed, the combined microalloying refinement heating austenite grain of Nb, V, Mo collaboration, warp are utilized
After crossing appropriate heat treatment, the martensite group of uniform fine grain austenite grain and the enhancing of Nb microalloy nano-second-phase can be obtained
It knits, realizes high-intensitive, high tenacity excellent matching, finally make high speed axle with good shock resistance and antifatigue equal military services
Can, meet the service demand of 400 kilometers of speed per hour or more bullet train axles.Of the invention focuses on C, Nb, V, Mo, Ni element
Proper Match, give full play to its effect in axle steel, obtain that crystal grain is tiny and microscopic structure based on martensite, make
Axle steel has the comprehensive mechanical properties such as high intensity, high tenacity, high-hardenability, to have good shock resistance and antifatigue etc.
Military service performance.
Other features and advantages of the present invention will illustrate in the following description, also, part can become from specification
It obtains it is clear that understand through the implementation of the invention.The objectives and other advantages of the invention can be by written explanation
Specifically noted method is achieved and obtained in book, claims and specific embodiment.
Specific embodiment
Below with reference to embodiment, the invention will be further described, and the embodiment of the present invention can be used for illustrating original of the invention
Reason.
A kind of ultra-fine grain ultra-high strength and toughness high speed axle steel, the chemical component of the axle steel include C, Si, Cr, Mn,
V, Nb, Ni, Mo, Al, P, S, O and N, Yu Wei Fe and inevitable impurity.
Preferably, the content of C is 0.24~0.32%, this is because the excessively high plasticity that can cause steel of carbon content and toughness
It significantly reduces, for the plasticity and toughness for guaranteeing steel, C content should be reduced suitably, and the intensity of loss is then mainly by Nb, V, Mo microalloy
Nano-second-phase makes up.
Preferably, the content of Si is 0.20~0.40%, and element silicon has significant solution strengthening effect, but silicon also has
Damage toughness effect, the present invention mainly utilizes its deoxidation, in order not to damage the wilfulness of steel, need by Si content control compared with
Low-level.
Preferably, Cr:0.60~1.00%, the through hardening of steel can not only be significantly improved by adding moderate Cr in steel of the present invention
Property, moreover it is possible to improve the uniformity of material structure.(Fe, Cr) is formed when Cr is dissolved in cementite3When C alloy cementite, it can play thin
Change the effect of crystal grain and cementite, to obtain uniformly tiny quenching crystal grain and tempered structure, obtains the obdurability of material
It improves.But excessive Cr and C Cr easy to form7C3Equal carbide, damage toughness, the plasticity of steel.
Preferably, Mn:0.40~0.70%, manganese are the effective elements of deoxidization desulfuration, while being also the member for guaranteeing harden ability
Element.But similar with Si, Mn too high levels can significantly reduce the toughness of steel, and Mn content is too low then cannot effectively deoxidization desulfuration and guarantee
The harden ability of steel.
Preferably, V:0.08~0.13%, steel of the present invention are middle low-carbon alloy steel, using higher V microalloying, first
(V, Mo) (C, N) fining austenite grains can be precipitated in forging rolling, a large amount of (V, Mo) secondly is precipitated when being heat-treated and reheating
(CN) nano-second-phase refinement reheats the crystallite dimension of austenite.Again, it is solid to reheat considerable part in austenite for heat treatment
Molten V improves harden ability, while being largely precipitated during high tempering, occupies a part of C in steel, is formed largely, with V, C
With the nano-second-phase based on Mo, rather than the cementite of larger particles, thus obtain uniformly tiny austenite grain and its
Phase-change organization.Excessively high V content will lead to that VC Precipitation Temperature is excessively high, amount of precipitation is excessive, particle size is easy coarse, be unfavorable for thin
Change austenite grain, it is unfavorable to the intensity, toughness of axle steel etc..Too low V, the above comprehensive function are unobvious.
Preferably, Nb:0.02~0.10%, steel of the present invention is middle low-carbon alloy steel, first can be with using Nb microalloying
Nb (C, N) is precipitated in high temperature forging rolling, fining austenite grains；Secondly it is easy to reheat the Nb being partially dissolved in austenite for heat treatment
In crystal boundary segregation, austenite phase transformation is postponed, the harden ability of steel is improved.It acts on unobvious more than when lower than 0.02wt.%, is higher than
Effect increases unobvious when 0.10wt.%, reaches saturation.
Preferably, Ni:2.70~3.30%, the present invention in nickel be improve steel toughness alloying element, cda alloy at
This and its cooperateing in terms of obdurability, harden ability with other alloying elements, in steel of the present invention the content control of Ni 2.70~
3.30wt.%.
Preferably, Mo:0.40~0.60%, the present invention obtain tiny austenite by Mo, Nb, V combined microalloying
Crystal grain, significant nano-second-phase precipitation strengthening effect and high resistance to tempering, it is hereby achieved that fine grain, high tenacity height
Warm tempered structure.It, can be under fine austenite crystalline form in addition, the rational proportion of the alloying elements such as Mo and Cr, Ni and C, V
Obtain good harden ability.Mo content is lower than 0.40wt.%, and above-mentioned effect is limited, too high levels, then above-mentioned effect is saturated even
Cause the effect for improving resistance to tempering superfluous, the alloy and tempering heat treatment process cost of steel will be improved.
Preferably, Alt:0.010~0.040%, Al are strong deoxidant elements, and AlN can be also formed in conjunction with N, can be played
Grain refinement, content are lower than 0.020wt.%, and the above effect is unobvious.Al content in steel of the present invention is controlled 0.020
~0.040wt.%.
Preferably, N: < 0.008%, in the presence of having Nb, V, Al etc. in steel, N can form carbonitride with them, can be with
It is effective to inhibit Austenite Grain Growth.Steel of the present invention Nb, V, Al equal size design allow N content control range be <
0.008wt.%.
Preferably, the content of impurity element is respectively P in the present invention: < 0.010%, S: < 0.010%, O: <
0.0015%, remaining is Fe and inevitable impurity.
High tenacity high speed axles steel according to the present invention uses converter, electric furnace or vacuum induction furnace smelting, the outer essence of furnace
Continuous casting or molding after refining, for slab through the laggard driving axis forging rolling of cogging, heating temperature is 1150~1250 DEG C, difficult to understand when to avoid forging rolling
Family name's body is decomposed phase transformation, and finish-forging and finishing temperature are not less than 850 DEG C, air-cooled after forging rolling, using the heat of quenching+high tempering twice
Processing can obtain tiny austenite grain and excellent obdurability matching.
Steel of the present invention is by vacuum induction furnace smelting, and wherein 1#~3# is embodiment steel, compared steel be according to
The test steel of 30NiCrMoV12 standard design, chemical component are as shown in table 1.Embodiment steel and compared steel are through smelting, casting, forging
After rolling, it is processed into normal room temperature tensile sample (L0=5d0,d0=5mm), Charpy notch impact specimen (10mm × 10mm ×
55mm) and metallographic specimen (10mm × 10mm × 20mm).Tensile sample, impact specimen and metallographic specimen add in a vacuum furnace
Heat keeps the temperature 2h to 930 DEG C, then air-cooled, is then heated to 880 DEG C in a vacuum furnace again, keeps the temperature 1h, oil quenching.When tempering
Tempering temperature be 675 DEG C, soaking time 4h is air-cooled to room temperature after tempering.Tensile sample and impact specimen are processed into final ruler
It is very little, and accordingly tested according to national standard, mechanical performance index is listed in table 2, and metallographic specimen is ground again, polishes, and
After being saturated picric acid aqueous corrosion, original austenite grain degree is measured using division lines method, the results are shown in Table 2.In table 1-2,
Rp0.2For yield strength, Rm is tensile strength, and A is elongation after fracture, KU2Function is absorbed for room temperature 5mm notch impact of collision.
1 chemical component of table (wt.%)
Mechanical property when table 2 is tempered
Tempered martensite is obtained after heat treatment, embodiment 1#~3# steel obtains tensile strength 980MPa or more, room
The favorable comprehensive mechanical property of warm ballistic work 100J or more, ductile-brittle transition temperature reach -85 DEG C hereinafter, and obtaining uniformly tiny
Austenite grain, average-size are 10-13 μm, are matched compared with compared steel with more excellent obdurability.
The foregoing is only a preferred embodiment of the present invention, but scope of protection of the present invention is not limited thereto,
In the technical scope disclosed by the present invention, any changes or substitutions that can be easily thought of by anyone skilled in the art,
It should be covered by the protection scope of the present invention.
Claims (5)
1. a kind of fine grain ultra-high strength and toughness high speed axle steel, which is characterized in that the chemical component of the steel is with weight percent
It is calculated as, C:0.24~0.32%, Si:0.20~0.40%, Cr:0.60~1.00%, Mn:0.40~0.70%, V:0.08~
0.13%, Nb:0.02~0.10%, Ni:2.70~3.30%, Mo:0.40~0.60%, Alt:0.010~0.040%, P: <
0.010%, S: < 0.010%, O: < 0.0015%, N: < 0.008%, remaining is Fe and inevitable impurity；
The average grain size of austenite grain is 10-13 μm in the tissue of the axle steel；
The yield strength R of the axle steelp0.2>=900MPa, tensile strength Rm >=950MPa, elongation percentage A >=15%, 5mm notch
Room temperature impact of collision absorbs function KU2>=100J, ductile-brittle transition temperature are lower than -80 DEG C.
2. a kind of fine grain ultra-high strength and toughness high speed axle Heat-Treatment of Steel method described in claim 1, which is characterized in that forging rolling
After steel afterwards carries out quenching heat treatment twice in hardening media, then tempering is carried out, obtains the axle steel；
The temperature for carrying out first time quenching heat treatment is 920~950 DEG C, and the heating and thermal insulation time is 60~180min；
The temperature for carrying out second of quenching heat treatment is 850~900 DEG C, and the heating and thermal insulation time is 10~120min；
The temperature of tempering is 620~680 DEG C, soaking time 3~8 hours, air-cooled after tempering to arrive room temperature.
3. heat treatment method according to claim 2, which is characterized in that the hardening media is water, water mist or oil.
4. a kind of method that fine grain ultra-high strength and toughness high speed axle steel is prepared using heat treatment method described in Claims 2 or 3,
It is characterized in that, continuous casting or molding, slab are laggard through cogging after external refining using converter, electric furnace or vacuum induction furnace smelting
It drives a vehicle axis forging rolling, it is air-cooled after forging rolling, the heat treatment is carried out, fine grain ultra-high strength and toughness high speed axle steel is obtained.
5. preparing the method for fine grain ultra-high strength and toughness high speed axle steel according to claim 4, which is characterized in that forging rolling
Heating temperature is 1150~1250 DEG C, and finish-forging and finishing temperature are not less than 850 DEG C.
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