CN110423955A - The heat-resisting gear-bearing steel of the super constrictive type superhigh intensity in surface layer and preparation method - Google Patents
The heat-resisting gear-bearing steel of the super constrictive type superhigh intensity in surface layer and preparation method Download PDFInfo
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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Abstract
The invention belongs to field of material technology, it is related to a kind of heat-resisting gear-bearing steel of the super constrictive type superhigh intensity in surface layer and preparation method, the chemical composition and mass fraction of steel are as follows: 0.08~0.18%C, 10.0~16.0%Co, 3.0~8.0%Ni, 3.0~7.0%Cr, 3.0~6.0%Mo, 0.5~2.0%W, 0.2~1.0%V, 0~0.1%Nb, remaining is Fe and impurity element.It is smelted using the methods of vacuum induction melting, " vacuum induction melting+vacuum arc remelting " or " vacuum induction melting+electroslag remelting ", steel ingot is by diffusion annealing and forging rolling is at steel, steel sample passes through conditioning treatment, carburizing and final heat treatment, the tensile strength of steel is not less than 1900MPa, yield strength is not less than 1600MPa, and carburized surface hardness is not less than 850HV (suitable 66HRC).The advantage is that having higher tensile strength, yield strength and preferable plasticity, toughness and heat resistance compared with prior art, there is the excellent super hardening capacity of surface layer carburizing and fatigue behaviour, reached the good fit of the superpower toughening of center portion and surface layer superhardization.
Description
Technical field
The invention belongs to field of material technology, it is related to a kind of heat-resisting gear-bearing steel of the super constrictive type superhigh intensity in surface layer and system
Preparation Method.
Background technique
Gear, bearing and transmission shaft are the machines such as aero-engine, helicopter, bullet train, heavy-duty car and wind generator
The key member of tool transmission system is on active service under the operating conditions such as heavy duty, high speed, violent state change and complex stress condition, it is desirable that
It has high bearing capacity and good heat-resistant antifriction performance, to guarantee that driving member has high reliability and durable
Property.In order to meet heavy duty, high gear, bearing and the requirement of transmission shaft, gear-bearing steel should have excellent surface layer super
Hardening capacity, high obdurability and heat resistance.
Gear-bearing steel of the invention not only has ultrahigh-intensity high-toughness, but also has the excellent super hardening capacity in surface layer
It with high thermal stability, can be applied to the components such as the gear, bearing, transmission shaft of high power density machine driven system, meet dress
For to performance requirements such as driving member high-mechanic, long-life, lightweights.
Alloying is the core of the heat-resisting gear-bearing steel of the super constrictive type superhigh intensity in surface layer, it determines that can steel pass through infiltration
Carbon and heat treatment are to obtain surface layer superhardization and the superpower toughening of center portion and other effects.Design of alloy and alloying element Optimized Matching
It is the critical issue of the heat-resisting gear-bearing steel of superhigh intensity.
Carburizing is the key that the heat-resisting gear-bearing steel application technology of the super constrictive type superhigh intensity in surface layer, by carburizing and finally
Heat treatment makes steel surface layer obtain high carbon martensite and the thereon microscopic structure of equally distributed suitable granular carbide, to reach
To ultrahigh hardness and enough hardening depths, and there is high residual compressive stress, while center portion obtains superhigh intensity and preferable
Plasticity and toughness meet the requirement of heavy-duty gear and bearing to significantly improve the anti-fatigue performance and wearability of steel.
Nineteen eighty-two U.S. GE, company had developed high-intensitive carburizing steel M50NiL.The steel is reduced on the basis of M50 bearing steel
Carbon content, and nickel element is increased, to significantly improve the plasticity and toughness of steel, and there is good carburizing performance.Steel
Exemplary chemical ingredient (mass fraction) is as follows: 0.13%C, 4.13%Cr, 3.40%Ni, 4.25%Mo, 1.23%V.By seeping
After carbon and final heat treatment, the surface hardness of steel reaches 60HRC~64HRC, infiltration layer carbide small and dispersed, center portion tensile strength
About 1400MPa, yield strength about 1200MPa, fracture toughness 50~60MPa √ m, can reach 316 DEG C using temperature.But
The intensity and surface hardness of M50NiL is lower, it is difficult to meet the use demand of heavy-duty gear and bearing.
1993, Latrobe company, U.S. Maloney et al. invented a kind of high-intensitive carburizing stainless steel CSS-42L, specially
Benefit US5424028.Chemical component (mass fraction) range of patent steel is as follows: 0.10%~0.25%C, 13.0%~
19.0%Cr, 5.0%~14.0%Co, 1.75%~5.25%Ni, 3.0%~5.0%Mo, 0.25%~1.25%V,
0.01%~0.10%Nb.The Exemplary chemical ingredient of CSS-42L steel are as follows: 0.13%C, 14.5%Cr, 12.5%Co, 2.25%
Ni, 4.0%Mo, 0.6%V, 0.03%Nb.After vacuum carburization and final heat treatment, room temperature surface hardness reach 65HRC with
On, 60HRC is still up at 427 DEG C.The steel is after 1038 DEG C of quenchings and 496 DEG C of tempering, tensile strength 1760MPa, yield strength
1336MPa, fracture toughness 50.4MPa √ m；After 1121 DEG C of quenchings and 496 DEG C of tempering, tensile strength 1764MPa, surrender is by force
Spend 1200MPa, fracture toughness 113MPa √ m.The carburizing performance of CSS-42L steel is poor, and infiltration layer carbide is coarse intensive, effectively hard
Change depth as shallow, and there are retained austenite soft zones when hardening heat is higher.
1999, Northwestern Univ USA Kuehmann et al. invented a kind of surface layer carburizing secondary hardened steel, the patent No.
US6176946.Chemical component (mass fraction) range of patent steel is as follows: 0.05%~0.24%C, and 15.0%~28.0%
Co, 1.5%~9.5%Ni, 3.5%~9.0%Cr ,≤2.5%Mo ,≤0.2%V.The patent produces C61 and two kinds of C69
Pinion steel.The wherein Exemplary chemical ingredient (mass fraction) of C61 steel are as follows: 0.15%C, 18.0%Co, 9.5%Ni, 3.5%Cr,
1.1%Mo, 0.08%V.It is hard by 1000 DEG C of vacuum carburizations and quenching ,≤- 73 DEG C of cold treatments and 482 DEG C of tempering, the surface of steel
Degree reaches 60~62HRC, infiltration layer carbide small and dispersed, and center portion tensile strength 1655MPa, yield strength 1551MPa are broken tough
143MPa √ m is spent, can reach 410 DEG C using temperature.The toughness and yield strength of C61 steel are high, but nitrided layer hardness is lower, it is difficult to hold
By high contact stress.The Exemplary chemical ingredient (mass fraction) of C69 steel are as follows: 0.10%C, 28.0%Co, 3.0%Ni, 5.1%
Cr, 2.5%Mo, 0.02%V.Pass through 1000 DEG C of vacuum carburizations and quenching ,≤- 73 DEG C of cold treatments and 496 DEG C of tempering, the surface of steel
Hardness reaches 65~67HRC, infiltration layer carbide small and dispersed, center portion tensile strength 1622MPa, yield strength 1346MPa, fracture
Toughness 44MPa √ m, can reach 450 DEG C using temperature.The toughness of C69 steel is lower, is unfavorable for fatigue property, and Co in steel
Content is up to 28%, higher cost.
2008, QuesTek company, U.S. Wright et al. invented a kind of secondary-hardening gear steel C64, the patent No.
US8801872.The chemical component (mass fraction) of steel is as follows: 0.11%C, 16.3%Co, 7.5%Ni, 3.5%Cr, 1.75%
Mo, 0.2%W, 0.02%V.Using 1000 DEG C of vacuum carburizations and quench ,≤- 73 DEG C of cold treatments and 496 DEG C tempering, the carburizing of steel
Surface hardness reaches 62~64HRC, infiltration layer carbide small and dispersed, center portion tensile strength 1679MPa, yield strength 1372MPa,
Fracture toughness 94MPa √ m, can reach 410 DEG C using temperature.The center portion intensity and carburized layer hardness of C64 steel are lower, have not yet been reached
Center portion superhigh intensity and surface layer ultrahigh hardness are horizontal.
In summary, High-performance gear bearing steel is the carburizing steel with precipitation-hardening effect at present.With a new generation
The development of mechanized equipment proposes requirements at the higher level, existing gear to the bearing capacity, service life and structural weight reduction of driving member
Bearing steel is lower due to center portion obdurability and case-hardening performance, it is difficult to meet the requirements.In order to adapt to driving member high-mechanic and
Light-weighted development, gear-bearing steel of new generation need to have the matched well of center portion superhigh intensity and surface layer ultrahigh hardness.Cause
This urgently studies the superpower heat-resisting gear-bearing steel with the super hardening capacity in surface layer, after over carburizing and final heat treatment, steel
Surface reaches ultrahigh hardness (hardness >=65HRC), center portion reach superhigh intensity (tensile strength >=1800MPa, yield strength >=
1400MPa), it is not less than 450 DEG C (it is required that steel belt roof bolt temperature is at 480 DEG C or more) using temperature.
Summary of the invention
The object of the present invention is to provide a kind of heat-resisting gear-bearing steel of the super constrictive type superhigh intensity in surface layer and preparation method,
After over carburizing and final heat treatment, there is the excellent super hardening capacity of carburizing and fatigue behaviour, meet high power density machinery
The requirement of transmission system.With super hardening capacity and superhigh intensity heat resistance, the tensile strength of steel is not less than
1900MPa, yield strength are not less than 1600MPa, and carburized surface hardness is not less than 850HV (suitable 66HRC).
To solve this technical problem, the technical scheme is that
A kind of heat-resisting gear-bearing steel of super constrictive type superhigh intensity in surface layer, the chemical composition and quality of the gear-bearing steel
Score are as follows: 0.08~0.18%C, 10.0~16.0%Co, 3.0~8.0%Ni, 3.0~7.0%Cr, 3.0~6.0%Mo,
0.5~2.0%W, 0.2~1.0%V, 0~0.1%Nb, remaining is Fe and impurity element.
A kind of preparation method of the heat-resisting gear-bearing steel of super constrictive type superhigh intensity in surface layer, comprises the following steps that and skill
Art parameter:
Step 1: high-purity smelting: it is as follows that impurity element mass content is controlled in smelting process: S≤0.0030%, P≤
0.0050%, O≤0.0010%, N≤0.0020%, H≤0.0001%；Guarantee the purity of final steel；
Step 2: steel ingot diffusion annealing: 1200~1240 DEG C of heating temperature, soaking time is no less than 10h, is furnace-cooled to 600
It DEG C comes out of the stove air-cooled；
Step 3: steel ingot is thermally processed into steel；
Step 4: steel conditioning treatment, using annealing and tempering combined processing；First by annealing to eliminate steel
Present in non-equilibrium microstructure, reduce hardness, and refine crystal grain.Since the harden ability of invention steel is very high, cooling procedure after annealing
In still can generate a small amount of non-equilibrium microstructure (such as bainite), then so that non-equilibrium microstructure is converted into iron by high tempering
Ferritic matrix and carbide tissue, further decrease hardness, most prepare for subsequent mechanical processing and carburizing.
Step 5: vacuum carburization: 900 DEG C~1000 DEG C of carburizing temperature, atmosphere pressure 100Pa~1000Pa, according to infiltration layer
Depth and hardness requirement selection, which are seeped, expands ratio and umber of pulse；
Step 6: final heat treatment, comprises the following processes:
1, vacuum hardening: 1050 DEG C~1120 DEG C of heating temperature, soaking time 0.5h~2h；
2, cold treatment: -60 DEG C~-100 DEG C of cooling temperature；
3, it is tempered: 480 DEG C~560 DEG C of heating temperature, soaking time 2h~3h, air-cooled；Tempering 2~4 times.By repeatedly returning
Fire reduces Residual Austenite Content in Carbonized Layes, precipitation-hardening effect is given full play to, to improve infiltration layer and center portion intensity.
Preferably, smelting process uses vacuum induction melting, " vacuum induction melting+vacuum arc weight in the step 1
Any one of it is molten " or " vacuum induction melting+electroslag remelting ".
By forging or being rolled into steel after steel ingot cogging described in the step 3；The forging or rolling temperature range are
1160 DEG C~900 DEG C, slow cooling to room temperature simultaneously carries out 600 DEG C~700 DEG C tempering, and tempering insulation time is no less than 6h.
Annealing process technological parameter in the step 4 are as follows: 850 DEG C~900 DEG C of heating temperature, soaking time is no less than 2h,
Be furnace-cooled to 600 DEG C come out of the stove it is air-cooled.
Drawing process technological parameter in the step 4 are as follows: 600 DEG C~700 DEG C of heating temperature, soaking time is no less than 6h,
It is air-cooled.
Preferably, penetration enhancer is acetylene or propane in the step 5.
Preferably, cold using air cooling or oil in vacuum hardening in step 1 described in step 6.
1h~3h cooling time in step 2 described in step 6 is returned in air and is warmed to room temperature.
A cold treatment can be carried out in step 3 described in step 6 between every double tempering, it can also be without cold treatment.Root
Cold treatment number is determined according to carburized layer concentration of carbon and residual austenite content difference.If infiltration layer concentration of carbon is high, retained austenite contains
Amount is high, then increases cold treatment number, vice versa.
The beneficial effects of the present invention are:
By vacuum carburization and final heat treatment, the tensile strength of steel is not less than 1900MPa, and yield strength is not less than
1600MPa, yield strength are not less than 1600MPa, and carburized surface hardness is not less than 850HV (suitable 66HRC).With prior art phase
Than steel of the present invention has higher tensile strength, yield strength and preferable plasticity, toughness and heat resistance, has excellent table
The super hardening capacity of layer carburizing and fatigue behaviour have reached the good fit of center portion super-strengthening and surface layer superhardization.Steel of the present invention can
Mitigate construction weight for heavily loaded high gear and bearing to improve component load-bearing ability.
Alloys producing is as follows in steel of the present invention:
C is one of the main alloy element of steel of the present invention.C is austenite former, in steel of the present invention C mainly with
Gap is dissolved atom and the form of carbide exists.The C being solid-solution in austenite reduces Ms temperature strongly, increases retained austenite and contains
Amount and stability, increase the harden ability of steel, inhibit the formation of free ferrite.The C being solid-solution in ferrite has strong consolidate
Molten invigoration effect significantly improves the intensity of infiltration layer and center portion martensite.During high tempering after quenching, supersaturated C is former
Son is precipitated from martensitic matrix forms M2C type carbide, plays precipitation enhancement, further increases nitrided layer hardness and center portion is strong
Degree.In Casting Ingot Solidification Process, C and carbide Nb, V, Mo, W etc. form the primary carbides such as MC, M6C, with
It cannot be dissolved completely in austenitization afterwards, form a Residual Carbides.One time Residual Carbides can refine austenite
Crystal grain, but more coarse carbide will lead to the toughness of steel and fatigue behaviour and reduce.The excessively high toughness that will lead to steel of C content and
Plasticity is insufficient, and can inhibit the diffusion rate of C atom in carburizing process, reduces depth of penetration.And C amount is too low will lead to center portion
Intensity is insufficient.Therefore, the C content of steel of the present invention is 0.08%~0.18%.
Co is one of the main alloy element of steel of the present invention.Co is austenite former, is dissolved in the form of displaced atom
In austenite or ferrite.The Co being solid-solution in austenite improves Ms temperature, promotes austenite to martensite transfor mation, reduces
Residual austenite content.Can make that more C, Ni elements and Cr, Mo element are added in steel using this key property of Co, thus
Improve the obdurability and carburizing performance of steel.On the one hand the Co being solid-solution in ferrite reduces solubility of Mo, W atom in steel,
Promote the precipitation of M2C carbide, enhances precipitation-hardening effect, so that carburized layer is reached ultrahigh hardness, center portion reaches superhigh intensity.Separately
On the one hand, Co makes Fe generate shortrange order, reduces the self-diffusion coefficient of Fe, and when tempering delays returning for martensite dislocation substructure
It is multiple, so that the precipitation for precipitated phase M2C provides more nucleation sites；Co improves activation energy of the C in ferrite simultaneously, reduces
Diffusion coefficient of the C in ferrite increases the nucleation rate of M2C carbide and inhibits its agglomeration, advantageously form tiny more
Dissipate the precipitated phase of distribution；The formation of Ni, Co collective effect promotion Fe3C back dissolving and M2C carbide.In addition, Co is by delaying geneva
The reply of body substructure and the agglomeration of precipitated phase, to improve steel belt roof bolt drag and thermal stability.When Co amount is excessively high, it will increase
The content for adding twin crystal martensite reduces toughness and plasticity, and keeps the cost of steel excessively high.When Co amount is too low, precipitation-hardening effect
Deficiency is unable to reach infiltration layer superhardization and center portion super-strengthening.Therefore Co content is 10.0%~16.0%C in steel of the present invention.
Cr is one of the main alloy element of steel of the present invention.Cr is ferrite former, closes austenite phase field, strongly
Ms temperature is reduced, the harden ability of steel is improved.The corrosion resistance and inoxidizability of Cr raising steel.It is blunt that the addition of Cr makes Fe generate anode
Change, improves corrosion resistance of the steel in oxidizing acid.Mo element is added in Li-adding Al alloy, can further improve its corrosion resistance.Cr is
Medium carbide former, Cr enters formation alloyed cementite (FeCr) 3C in cementite phase in drawing process, improves it
Stability.Since diffusion velocity of the Cr in ferritic phase is greater than the carbide formers such as Mo, W, therefore the increase of Cr amount promotes
M2C precipitation dynamic process keeps post-curing peak mobile to low-temperature short-time direction, and the aggregation for accelerating M2C carbide is long
Big speed.Cr is the important alloying element for guaranteeing carburizing performance.Cr and Mo cooperatively forms alloy carbide, improves infiltration layer carbon
Content is without reducing depth of penetration.The Cr and Mo being solid-solution in austenite inhibit the formation of infiltration layer bainite, improve infiltration layer and quench
Permeability.Cr content increase (about 5%) is conducive to infiltration layer carbide dispersion and is uniformly distributed, and reduces distribution along crystal boundary tendency.Quench heating
When, Cr promotes the dissolution of infiltration layer carbide, improves depth of penetration, and ensure that infiltration layer post-curing acts on；Meanwhile infiltration layer is not
Molten carbide quantity is reduced, and size refinement is conducive to improve toughness and fatigue behaviour.Cr amount will lead to carburized layer Ms when excessively high strong
There is retained austenite soft zone, and forms intensive, coarse carbide with elements such as Mo, W, V in strong reduction, reduces fatigability
Can, reduce depth of penetration；Cr amount will cause carburized layer and center portion harden ability insufficient when too low.Therefore the Cr content of steel of the present invention is
3.0%~7.0%.
Ni is the main toughening element of steel of the present invention.Ni is austenite former, mainly to be dissolved atom shape in steel
Formula exists.The Ni being solid-solution in austenite reduces the Ms temperature of martensite transfor mation, improves overcooling austenite stability.It is solid-solution in iron
Ni in ferritic can reduce the Interaction Energy of dislocation and foreign atom, make in martensite that there are more mobile dislocations, thus
Improve plasticity and toughness, reduces cleavage fracture tendency.Meanwhile Ni improve stacking fault energy, reduce dislocation width, make commutative Banach aglebra be easy into
Row.Ni reduces the As temperature of adverse transformation austenite, the formation of adverse transformation austenite when promoting to be tempered.In Cr-Mo-W post-curing
Ni is added in steel can promote the back dissolving of alloyed cementite (FeCr) 3C, provide enough carbon contents for the formation of M2C carbide.Ni
Carburized layer carbon content and depth of penetration are reduced, increases infiltration layer residual austenite content, keeps infiltration layer gentle to center portion transition.In addition,
Ni can also improve steel to atmospheric corrosion, seawater corrosion and the drag of caustic corrosion, consider Ni to the shadow of obdurability and carburizing performance etc.
It rings, Ni is containing measurement 3.0%~8.0% in steel of the present invention.
Mo and W is the main intensified element of steel of the present invention.Mo is similar with the effect of W, is ferrite former, reduces
Ms temperature improves the harden ability of overcooling austenite stability and steel.In drawing process after quenching, Mo and W and C atom are formed
M2C phase generates precipitation-hardening effect, significantly improves the intensity and hardness of center portion and infiltration layer, reaches center portion super-strengthening and infiltration layer is super
Hardening.Increase with Mo and W content, from the precipitation for kinetically having postponed M2C carbide, improves the reply, again of ferritic phase
Crystallization and creep resistance, to make steel that there is high resistance to tempering and heat resistance.Mo is compared with W, the former acts on precipitation-hardening
Relatively strong, the latter's hardening effect is weaker, but has postponed overaging.Mo, W are added simultaneously, not only have stronger precipitation-hardening effect, but also
Overaging drag with higher.The Proper Match of Cr content and Mo, W content had both guaranteed normally be precipitated in martensitic matrix
The M2C carbide of small and dispersed, while again will not its roughening.Mo and W can also reduce the temper brittleness of steel.Mo makes steel surface
Passivation is generated, resistance to spot corrosion, slit and corrosion resistant, proof stress corruption of the steel in reductant (especially ionic medium containing Cl) are improved
Performances such as erosion and resistance to corrosion fatigue etc..In addition, Mo and W still form the important element of carburized layer carbide, effectively increase
Infiltration layer concentration of carbon improves infiltration layer wearability, has refined infiltration layer crystal grain.Mo, W and Cr collective effect improve carburized layer through hardening
Property, it is suppressed that the formation of bainite structure.When Mo, W content are excessively high, precipitation-hardening effect is strong, cause the intensity of steel excessively high and
Toughness is insufficient, and austenitizing temperature raising causes quenching distortion to increase.Cause the intensity and hardness decline of steel when too low.Therefore this
Mo, the W content of invention steel are respectively 3.0%~6.0% and 0.5%~2.0%.
V and Nb is a small amount of addition element of steel of the present invention.V and Nb is carbide, in steel mainly with
Carbide form exists, and carbide stability is high, especially NbC.For steel when heating austenitizing, MC type carbide is (especially
NbC it) is difficult to be dissolved completely, so that fining austenite grains, make steel that can carry out high-temperature carburizing and direct quenching, to simplify technique mistake
Journey.The V and Nb being solid-solution in austenite increase overcooling austenite stability, will be from martensite in drawing process after quenching
MC type carbide (such as VC, NbC) is precipitated and generates precipitation-hardening.MC type carbide is not easy agglomeration, effectively increases steel
Temper resistance and heat resistance.In carburizing process, Nb and V preferentially form carbide in conjunction with C, in austenitization
Not exclusively solid solution, to make in infiltration layer austenite containing the alloying elements such as more Cr, Mo, W, with improve infiltration layer harden ability and
Corrosion resistance.Since the solid solubility of VC is greater than NbC, V mainly plays precipitation enhancement in steel of the present invention, and Nb is mainly used for refining
Crystal grain.In steel when V, Nb too high levels, will lead to center portion and infiltration layer, there are coarse undissolved carbides, reduce toughness and fatigability
Energy.Therefore, V, Nb content are respectively 0.2%~1.0% and 0%~0.1% in steel of the present invention.
Specific embodiment
In order to make the object, technical scheme and advantages of the embodiment of the invention clearer, below by the present invention in conjunction with the embodiments
In technical solution be clearly and completely described.Obviously, described embodiment is a part of the embodiments of the present invention, and
It is not all of embodiment.Based on the embodiments of the present invention, those skilled in the art are not making creative work
Under the premise of, every other embodiment obtained shall fall within the protection scope of the present invention.
The feature of the various aspects of the embodiment of the present invention is described more fully below.In the following detailed description, it proposes
Many concrete details, so as to complete understanding of the present invention.But for those of ordinary skill in the art, very bright
Aobvious, the present invention can also be implemented in the case where not needing these details.Below to the description of embodiment
Just for the sake of being better understood by showing example of the invention to the present invention.The present invention is not limited to presented below any
Specific setting and method, but cover all product structures covered without departing from the spirit of the invention, method
Any improvement, replacement etc..
In an embodiment of the present invention, 12 furnace this hair have been smelted using vacuum induction melting+vacuum consumable remelting method
The steel of bright alloying component.After steel ingot high annealing bar is forged or is rolled within the scope of 1160 DEG C~900 DEG C.After forging
Slow cooling is to room temperature and carries out 680 DEG C, 10h tempering.
Conditioning treatment is carried out to steel.850 DEG C~900 DEG C are carried out first, then 3h annealing carries out 650 DEG C~700
DEG C, 10h tempering.
It is machined carburizing sample, and carries out vacuum carburization processing.Carburizing temperature is 950 DEG C~1000 DEG C carburizings, atmosphere
Pressure is 120Pa~180Pa, and penetration enhancer is acetylene, seeps and expands ratio 0.10~0.50, umber of pulse 30~60.
Final heat treatment is carried out to carburizing sample and mechanical property sample.Vacuum hardening temperature is 1060 DEG C~1100 DEG C,
Soaking time is 1.0h~1.5h, air-cooled or oily cold；Cold treatment temperature be -70 DEG C~-90 DEG C, cooling time 2h, in air
In return warm to room temperature；Tempering temperature is 500 DEG C~550 DEG C, and soaking time is 2~3h, is air-cooled to room temperature.According to infiltration layer concentration of carbon
Times of tempering and cold treatment number are determined with residual austenite content, to guarantee nitrided layer hardness and center portion intensity.In embodiment,
Embodiment 1,2,3,4,12 carries out a cold treatment after quenching and is tempered three times, and embodiment 5,6,7,8,9,10,11 is quenching
Cold treatment, tempering, cold treatment, tempering, cold treatment and tempering are successively carried out afterwards.
The chemical component of steel of the present invention is shown in Table 1, and conventional mechanical property is shown in Table 2, and rotary bending fatigue performance is shown in Table 3.In table
In be included in the chemical composition and mechanical property of compared steel (C69 and CSS-42L).
As shown in Table 1, compared with C69 steel, the Co content of steel of the present invention is lower to reduce cost, and Mo content is higher to improve
Center portion intensity and carburized layer hardness；Compared with CSS-42L steel, the Cr content of steel of the present invention is lower to improve carburizing performance, and Ni contains
It measures higher to improve toughness.
As shown in Table 2, steel ratio C69 and CSS-42L steel of the present invention have higher tensile strength, yield strength and good
Plasticity and toughness, while there is the super hardening capacity of excellent carburizing.
As shown in Table 3, there is excellent rotary bending fatigue performance, fatigue life is significantly higher than pair after steel carburizing of the present invention
Than steel CSS-42L and M50NiL.
The chemical component (mass fraction, %) of the steel of the present invention of table 1 and compared steel
The conventional mechanical property of table 2 steel of the present invention and compared steel
The rotary bending fatigue performance of the steel of the present invention of table 3 and compared steel
Finally it should be noted that: the above embodiments are merely illustrative of the technical solutions of the present invention, but protection of the invention
Range is not limited thereto, and anyone skilled in the art in the technical scope disclosed by the present invention, can be thought easily
It is modified or replaceed to various equivalent, these, which are modified or replaceed, should all be included within the scope of the present invention.
Claims (10)
1. a kind of heat-resisting gear-bearing steel of super constrictive type superhigh intensity in surface layer, it is characterised in that: the chemistry of the gear-bearing steel
Composition and mass fraction are as follows: 0.08~0.18%C, 10.0~16.0%Co, 3.0~8.0%Ni, 3.0~7.0%Cr, 3.0~
6.0%Mo, 0.5~2.0%W, 0.2~1.0%V, 0~0.1%Nb, remaining is Fe and impurity element.
2. a kind of preparation method of the heat-resisting gear-bearing steel of super constrictive type superhigh intensity in surface layer as described in claim 1, special
Sign is: the preparation method comprises the following steps that:
Step 1: high-purity smelting: it is as follows that impurity element mass content is controlled in smelting process: S≤0.0030%, P≤
0.0060%, O≤0.0010%, N≤0.0020%, H≤0.0001%；
Step 2: steel ingot diffusion annealing: 1200~1240 DEG C of heating temperature, soaking time is no less than 10h, is furnace-cooled to 600 DEG C and goes out
Furnace is air-cooled；
Step 3: steel ingot is thermally processed into steel；
Step 4: steel conditioning treatment, using annealing and tempering combined processing；
Step 5: vacuum carburization: 900 DEG C~1000 DEG C of carburizing temperature, atmosphere pressure 100Pa~1000Pa,
Step 6: final heat treatment, comprises the following processes:
6.1, vacuum hardening: 1050 DEG C~1120 DEG C of heating temperature, soaking time 0.5h~2h；
6.2, cold treatment: -60 DEG C~-100 DEG C of cooling temperature；
6.3, it is tempered: 480 DEG C~560 DEG C of heating temperature, soaking time 2h~3h, air-cooled；Tempering 2~4 times.
3. the preparation method of the heat-resisting gear-bearing steel of the super constrictive type superhigh intensity in surface layer according to claim 2, feature
Be: smelting process described in step 1 uses vacuum induction melting, " vacuum induction melting+vacuum arc remelting " or " vacuum
Any one of induction melting+electroslag remelting ".
4. the preparation method of the heat-resisting gear-bearing steel of the super constrictive type superhigh intensity in surface layer according to claim 2, feature
It is: by forging or being rolled into steel after steel ingot cogging described in step 3；The forging or rolling temperature range are 1160 DEG C
~900 DEG C, slow cooling to room temperature simultaneously carries out 600 DEG C~700 DEG C tempering, and tempering insulation time is no less than 6h.
5. the preparation method of the heat-resisting gear-bearing steel of the super constrictive type superhigh intensity in surface layer according to claim 2, feature
It is: annealing process technological parameter in the step 4 are as follows: 850 DEG C~900 DEG C of heating temperature, soaking time is no less than 2h, furnace
Be cooled to 600 DEG C come out of the stove it is air-cooled.
6. the preparation method of the heat-resisting gear-bearing steel of the super constrictive type superhigh intensity in surface layer according to claim 2, feature
It is: drawing process technological parameter in the step 4 are as follows: 600 DEG C~700 DEG C of heating temperature, soaking time is no less than 6h, empty
It is cold.
7. the preparation method of the heat-resisting gear-bearing steel of the super constrictive type superhigh intensity in surface layer according to claim 2, feature
Be: penetration enhancer is acetylene or propane in the step 5.
8. the preparation method of the heat-resisting gear-bearing steel of the super constrictive type superhigh intensity in surface layer according to claim 2, feature
It is: cold using air cooling or oil in vacuum hardening in the 6.1st step described in step 6.
9. the preparation method of the heat-resisting gear-bearing steel of the super constrictive type superhigh intensity in surface layer according to claim 2, feature
Be: 1h~3h cooling time in the 6.2nd step described in step 6 is returned in air and is warmed to room temperature.
10. the preparation method of the heat-resisting gear-bearing steel of the super constrictive type superhigh intensity in surface layer according to claim 2, feature
It is: a cold treatment can be carried out in the 6.2nd step described in step 6 between every double tempering.
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