CN1831303B - Rolling bearing - Google Patents
Rolling bearing Download PDFInfo
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- CN1831303B CN1831303B CN2006100547555A CN200610054755A CN1831303B CN 1831303 B CN1831303 B CN 1831303B CN 2006100547555 A CN2006100547555 A CN 2006100547555A CN 200610054755 A CN200610054755 A CN 200610054755A CN 1831303 B CN1831303 B CN 1831303B
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
- F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
- F01L2305/00—Valve arrangements comprising rollers
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
- F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
- F01L2305/00—Valve arrangements comprising rollers
- F01L2305/02—Mounting of rollers
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
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- Heat Treatment Of Articles (AREA)
- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
Abstract
A rolling bearing comprises a roller ( 4 ), a roller shaft ( 2 ) provided inwardly of the roller ( 4 ), and rolling elements ( 3 ) provided between the roller ( 4 ) and the roller shaft ( 2 ), the roller shaft ( 2 ) having a nitrogen-rich layer and is arranged at its race surface, on which the rolling elements ( 3 ) run, not smaller than 11 in the JIS austenite grain size number and not smaller than HV653 in the Vickers hardness number, at both ends not greater than HV300, and at its core beneath a widthwise midpoint of the race surface not smaller than HV550.
Description
Technical field
The present invention relates to rolling bearing; Specifically; It is high to relate to crack fatigue strength; And the rolling bearing that rolling fatigue life is long for example goes for, and uses at the rolling bearing for rocker arm of the switching manipulation of the suction valve of the motor of automobile or outlet valve or is used for the planetary rolling bearing of planetary gear bearing mechanism.
Background technique
In nearest rolling bearing; For example use bearing as above-mentioned rolling bearing for rocker arm or planetary gears; For being not only the bearing that rolls (
) type entirely that does not use supporter, and can also as at a high speed, the requirement of high capacity purposes increases gradually.In the present invention, do not distinguish full roller bearing especially and hold and other rolling bearing, and all be recited as rolling bearing.In not having the rolling bearing of supporter,, not to bearing inside supply of lubricant well, then begin to peel off in addition from roller or seat ring if do not avoid the interference between the roller.
In addition, if the rotational speed of roller reaches at a high speed, then on roller surface, wear and tear, or can not smoothly control the roller position and take place crooked easily owing to the influence of assembly error or load deflection.Thereby, the peeling off or cause peeling off of the beginning of causing of also take place sliding from the type of inner beginning because of the surface pressure of part rises from the surface.Its result, cause sliding heating or local surface pressure rise, thereby, peel off easily, abrade, the type of beginning from the surface surface abrasion or peeling off such as peel off based on the type that begins from inside of load types.
In order to address the above problem, advised the scheme of the following stated.
(1) the valve mechanism of motor with cam follower device with bearing in, will be made as in the mathematic(al) expectation of the bearing under the rated speed of motor more than 1000 hours and (open the 2000-38907 communique) with reference to the spy.
(2) ratio with carbide is made as 1O%～25%; To be made as 10/l～3/10ths to the resolution ratio of the initial value of retained austenite; In addition, end hardness is made as HV830～960, and then; The mean wavelength of surface roughness is made as below the 25 μ m, and a kind of valve mechanism of motor is used bearing shaft with cam follower device.In order to realize above-mentioned characteristic, Bearing Steel is implemented carbonitriding processing and shot peening (opening flat 10-47334 communique with reference to the spy).
(3), on axle, be formed with the cam follower axle (opening flat 10-103339 communique) of solid lubricant film such as polymeric compound with reference to the spy in order to improve the anti-abrasiveness of axle.
(4), under the temperature lower, carry out plasma nitriding or ion plating and make the cam follower axle (spy open flat 10-110720 communique) of high hardness than tempering temperature by manufacturings such as tool steel.
(5) will be adjusted in valve mechanism in the motor below the 150MPa to the flexural stress of axle with cam follower device bearing (opening the 2000-38906 communique) with reference to the spy.
(6) valve mechanism of motor of coating the superior phosphate coating of lubricant oil retentivity at the rolling surface of bearing component parts is with cam follower (open the 2000-205284 communique with reference to the spy, the spy opens the 2002-31212 communique).
(7) valve mechanism of motor that has carried out convex surface processing (crowning) in the roller scroll zones of axle is with cam follower (open in fact clear 63-185917 communique).
(8) be made as 1.2%～1.7% and carried out high-concentration carburized processing or carbonitriding is handled and the hardness of inside is made as the axle (opening the 2002-194438 communique with reference to the spy) about HV300 for the concentration of carbon on top layer of the rolling surface that will constitute axle.
But the cam follower that has roller (roller) of motor exists to facial enforcement the in the two ends of axle and rivets shaping, and shaft supporting part is riveted the situation of processing when being fixed in rocking arm.In this case, the rolling surface of roller needs high hardness, but the end need be shaped with riveted joint for soft.That the exploitation of considering this point also becomes gradually is many (with reference to the spy open flat 5-321616 communique, with clear 62-7908 communique, special fair 6-15811 communique, with putting down the 6-80287 communique).
In addition, the interior quadrate part spare of planetary gears, the rolling surface of its roller need have high tenacity, but it is desirable for the end is made as soft can rivet shaping.That the exploitation of considering this point also becomes gradually is many (with reference to the spy open the 2003-301933 communique, the spy opens the 2004-003627 communique).
Yet; From now on; The service condition of rolling bearing of planetary gears such as rocking arm or A/T speed changer of switch that is used in suction valve or the outlet valve of motor car engine has promoted the lowering viscousity of speed up and heavy loadization, lubricant oil, thereby these conditions become and more badly can hardly be avoided.For the above-mentioned rolling bearing under such service condition, the life-span that requires to roll has long lifetime, high tenacity or high crack fatigue strength.
Summary of the invention
The object of the invention is to provide the rolling bearing of the following stated; That is: in the service condition of cope with bad and on by the basis of high strength; Begin to peel off to the surface abrasion that begins to peel off from the surface etc. or from inside and show the long lifetime, and be easy to rivet processing in the end.
Rolling bearing of the present invention is to use the rocking arm of using at the switch of the valve of motor car engine.This rolling bearing has: foreign side's parts, the interior side's of said foreign side parts interior quadrate part spare and be present in said foreign side parts and interior quadrate part spare between solid of rotation; Wherein at least one parts of said foreign side parts and interior quadrate part spare have the nitrogen enriched layer; The austinite grain size of the skin section in the zone of the rolling surface of the said solid of rotation rotation of confession is more than No. 11 in said wherein at least one parts; And hardness is that HV (Vickers hardness) is more than 653; The hardness of the end of these parts is below the HV300; The hardness of the axle central part that rolling surface is central is made as more than HV710～HV730, and the zone of said rolling surface is carried out carbonitriding to said at least one parts and handled the back slow cool down extremely less than the A1 point by high frequency hardening more than the A point; Then high frequency hardening is implemented in the zone of said rolling surface and handled, said rolling bearing uses the SUJ2 Bearing Steel.
Constitute according to this, in the rolling bearing of threshold switch with rocking arm of motor car engine, can be in the skin section in the zone of its rolling surface, suppress peeling off of from surface beginning wait surface abrasion and begin from inside peeling off and realizing the long lifetime.In addition, limit the hardness of the end of said parts as described above, therefore, can be easy to rivet shaping.And then, for example, also can realize the high strength of parts, improve crack fatigue strength.Can not prolong the rolling fatigue life under the abominable service condition at the austinite grain size of the skin section of rolling surface under less than No. 11 situation, therefore, the austinite grain size of skin section is made as more than No. 11.In addition, configuration nitrogen enriched layer is for through to nitrogen enriched layer high frequency hardening and imperceptibility and Strengthening and Toughening microstructure.Wherein, so-called austenite crystal is meant in quenching and adds the austenite crystal of pining for phase transformation that also conduct resume in the past are remaining it becomes martensite mutually through cooling after.Above-mentioned austenite crystal is so long as manifest the processing of grain boundary to implement etching etc. as the metallographic specimen of the parts of object, and the grain boundary that makes it possible to observe gets final product.From the meaning of the grain boundary in the moment of heating before of quenching, can be called the original austenite particle.Measurement be can be as described above from the mean value conversion Mean particle diameter of the size indicator of JIS specification and obtain; Also can get the mean value of the length at the straight line of the random direction that overlaps metallographic structure and the interval of joining in the grain boundary through intercept method etc.; And be multiplied by augmenting factor, and draw three-dimensional gap length by two dimension.
Also have, above-mentioned nitrogen enriched layer is like the explanation of back, handles forming through carbonitriding, but can be in above-mentioned nitrogen enriched layer enriched with carbon, also can not enrichment.
Also can be made as as follows: the part except the skin section in the zone of above-mentioned rolling surface comprises that its microstructure has the zone of ferrite and carbide.
At this, ferrite (ferrite) is the α phase of iron, refers to not comprise as martensite etc. the ferrite of highdensity dislocation.Slowly the ferrite of the ferrite of heating generation and abundant tempering after quenching is corresponding therewith mutually by austenite (γ).The ferrite corresponding carbide such as cementite low with such dislocation density disperses under the state of thickization of cohesion.Thereby, the state that above-mentioned microstructure correspondence with ferrite and carbide typically is softened.The zone that the above-mentioned microstructure that is softened is present in beyond the skin section on the zone of rolling surface gets final product.Especially the hardness of the end of parts is to be precondition below the HV300, therefore, the end of above-mentioned parts is disposed above-mentioned softening tissue.
Also have, carbide mainly refers to cementite Fe
3C, but at the nitrogen enriched layer, it is few to compare carbon, but contain a lot of nitrogen, and therefore, as Fe
3(C, N) is the same, should be called carboritride.But for the ease of explanation, so-called carbide also comprises above-mentioned carboritride.In addition, steel comprise Mn etc. usually, therefore, are solid-solubilized in the carbide and show as (Fe, Mn)
3The mode of (C, N) and so on, and naturally comprise such mode.And then, when at high temperature carrying out tempering, not only comprise M
3The carbide of C type, but also comprise M
23C
6The carbide of type and other carbide, but above-mentioned carbide also comprises such carbide.
Can carry out high frequency hardening and form the zone of above-mentioned rolling surface.Constitute according to this, can obtain the sclerotic tissue of fine particle through the treating process of short time.Its result can realize the high strength or the high crack fatigue strength of bearing with cheap price under the prerequisite that does not make variation such as anti-surface abrasion property, anti-rolling fatigue life property.
Can the hardness of the skin section of above-mentioned rolling surface be made as more than the HV653, in addition, the hardness of the axle central part in the zone of this rolling surface be made as more than the HV550.Constitute according to this, reliably suppress rolling surface skin section surface abrasion or from the peeling off of inner beginning, thus, realize the long lifetime, in addition, can realize the high strength of the axle central part of its rolling surface or the high crack fatigue strength of above-mentioned parts.Under the prerequisite of hardness less than HV653 of the skin section of rolling surface, be difficult to realize the long lifetime under the above-mentioned condition, in addition, can not obtain tackling the high crack fatigue strength of the requirement of heavy loadization under less than the prerequisite of HV550 in the hardness of the axle central part of rolling surface.
Can be made as as follows, that is: in the skin section in the zone of above-mentioned rolling surface, retained austenite occupies 10～50 volume %, and the axle central part at this rolling surface leaves retained austenite.According to this formation, in skin section, can suppress peeling off or the be full of cracks expansion in inner peeling off of beginning of surface beginning certainly, at the axle central part, can further improve strength level through the result of high frequency hardening.If the retained austenite of skin section less than 10 volume %, then can not obtain the long lifetime under abominable service condition, in addition,, then can not become trickle retained austenite if surpass 50% volume, on the contrary, cause the lifetime under above-mentioned service condition.In addition, the axle central part is hardened through high frequency hardening, therefore, produces retained austenite, but not as skin section not as many.That is, because the connecting shaft central part is also hardened, therefore, retained austenite exists.
The measurement of above-mentioned retained austenite can be passed through X-ray diffraction method, transmission electron microscopy known methods such as (TEM:Transmission Electron Microscopy).Austenite, different with ferrite or cementite, owing to be non-strong magnetism body, can also use magnetic balance equimagnetic measuring device to measure.
Above-mentioned wherein at least one parts can carry out carbonitriding and handle the back slow cool down A1 point of arriving more than the A1 point, secondly, high frequency hardening is carried out in the zone of rolling surface handle.Above-mentioned A1 point for example, is 723 ℃ corresponding to eutectoid temperature in the Fe-C type.In addition, near the common temperature of using the steel A1 of rolling bearing point also is it.
Through above-mentioned processing, can access skin section because of being difficult to the frayed influence long lifetime, and other part is riveted the parts of processing easily.By the part of high frequency hardening; Austinite grain size (JIS specification) is more than No. 1, and retained austenite is 10～50 volume %, and hardness is more than the HV653; Why be, and implemented high frequency hardening in the zone that comprises rolling surface because implemented the carbonitriding processing.In addition, the position that not influenced by high frequency hardening in the end etc., hardness is below the HV300, why be because after carbonitriding is handled no matter slow cool down or quick cooling, all carry out modified (tempering) and handle.
One of them side of foreign side's parts of the rolling bearing of the invention described above and interior quadrate part spare has the nitrogen enriched layer, and the end of its parts is softened, and therefore, can access superior wearability and riveted joint processability.And then, can guarantee high crack fatigue strength and the rolling contact fatigue intensity and the anti-surface abrasion property of above-mentioned parts with short time and simple treating process through high frequency hardening.Especially, through in the predetermined range of skin section, having retained austenite, effectively suppress the be full of cracks that produces and expand because of the load repetition.
With reference to accompanying drawing, to the object of the invention of they and other and characteristic from following beginning further explain.
Description of drawings
Fig. 1 representes the rolling bearing for rocker arm of mode of execution of the present invention.
Fig. 2 A is the sectional view along the II-II line of Fig. 1.
Fig. 2 B is the F portion enlarged view of Fig. 2 A, expression riveted joint fixed processing portion.
Fig. 3 representes other the rolling bearing of rolling bearing for rocker arm of mode of execution of the present invention.
Fig. 4 representes of the present invention and then other the rolling bearing of rolling bearing for rocker arm of mode of execution.
Fig. 5 is the rolling bearing enlarged view partly that the cam with the cam follower that has roller of the motor of Fig. 4 contacts.
Fig. 6 A is the front view of planetary gears.
Fig. 6 B is the longitudinal sectional view of planetary gears.
Fig. 6 C is the stereogram of planetary gears.
Fig. 7 is the longitudinal sectional view of automatic transmission.
Fig. 8 is the stereogram that blocks the part of needle roller bearing.
Fig. 9 is the line chart of the heat treatment cycle curve of explanation mode of execution of the present invention.
Figure 10 is other the line chart of heat treatment cycle curve of explanation mode of execution of the present invention.
Figure 11 is the line chart of expression embodiment's heat treatment cycle curve H1.
Figure 12 is the line chart of expression embodiment's heat treatment cycle curve H2.
Figure 13 A is the front view of sample, and expression hardness measurement position.
Figure 13 B is the transverse sectional view of sample, and expression hardness measurement position.
Figure 14 is the sketch of crack fatigue testing machine.
Figure 15 is the longitudinal sectional view of the rolling contact fatigue testing machine of foreign steamer rotation.
Embodiment
At first, the mode of execution that is useful in rolling bearing for rocker arm is recorded and narrated.Can know that with reference to Fig. 1 and Fig. 2 A swing part is a rocking arm 1 at central part via axle bush etc. with rotation mode freely by pitman arm shaft 5 supportings.
At a side's of this rocking arm 1 end 1b, be inserted with and regulate with screw rod 7.This regulates with screw rod 7 fixing through locking nut 8, the last end in contact of the steam supply valve of its lower end and internal combustion office or the valve 9 of outlet valve.This valve 9 is by the elastic force ejection of spring 10.
1a is provided with cam driven member main body 50 to rocking arm 1 in the opposing party's end, and cam driven member main body 50 has integratedly and forms forked roller support 14.At the outer circumferential face central part of roll shaft 2, be that roller 3 is supporting the roller 4 that constitutes foreign side's parts with rotation mode freely by rolling element.The axial direction of roller 3 is configured to the parallel axes with roll shaft.The outer circumferential face of this roller 4 utilizes the ejection force of spring 10 to contact with the camming surface of the cam that is arranged on camshaft 6.
F portion enlarged view like Fig. 2 A is shown in Fig. 2 B, at this forked roller support 14, is provided with chamfered section 14a, the two ends 2a of the roll shaft 2 of quadrate part spare in being equivalent to is riveted processing and forms riveted joint processing portion 25 be fixed.The 2a at the two ends of roll shaft is formed with the riveted joint processing portion 2b that utilizes plastic working, fills vacant space through forming chamfered section 14a.That is, the 2a at the two ends at least of roll shaft is suppressed at hardness below the HV300, makes to be easy to rivet processing, implements riveted joint processing, in the chamfered section formation riveted joint fixed processing portion 25 of roller support.
At this, will use as rolling bearing for rocker arm by the rolling bearing that roll shaft 2, roller 3, roller 4 constitute.Generally, do not using under the situation of supporter, be called full roller bearing and hold, but in the present invention, describing unlike above-mentioned equally special differentiation.Above-mentioned rolling bearing for rocker arm is because rotation contact cam 6 time, therefore, and to the pushing force and the impact force of roller 4 operating cams 6.
In the rolling bearing in this mode of execution, roll shaft 2 has the nitrogen enriched layer, and high frequency hardening is implemented in the zone of the rolling surface that solid of rotation is rolled, and austinite grain size is more than No. 11 of superfine (according to the JIS specifications), and hardness is more than HV653.Except the zone of said rolling surface (skin section and axle central part), if ferrite granularity or austinite grain size are below No. 10, then belong to thicker, in addition, the hardness of the end of said roll shaft 2 is low, is in the scope below the HV300.In addition, owing to high frequency hardening has been implemented in the zone of the rolling surface that solid of rotation is rotated, therefore, in skin section, retained austenite occupies 10～50 volume %.In addition, therefore the axle central part of rolling surface central authorities radio frequency heating and quenching when above-mentioned skin section is carried out high frequency hardening, is hardened, and generates retained austenite in addition.Its result in skin section, is difficult to take place simultaneously surface abrasion and reaches the peeling off from inner beginning type based on load types; In addition, in the scope from the axle central part to skin section of rolling surface, has high strength or high crack fatigue strength at least, on the other hand; At other positions such as ends; Because hardness is low, therefore, is easy to rivet processing.
Fig. 3 representes other the rolling bearing for rocker arm of mode of execution of the present invention.In this cam follower; Cam follower main body 50 is fixed on roller hole (not shown) with roll shaft 2; The switch of motor contacts with a side end 1a with the end of valve 9; Pivot contacts with the other end 1a, and said roller hole is opening between a side's of rocking arm 1 end 1b and the opposing party's end 1a, and is crossed between the sidewall.The cam follower main body 50 that is provided with pivotal bearing part 15 by the regulation of spring 10 around valve towards ejection, will pass on the driving force of coming to support from cam 6, and overcome the ejection force movement of valve 90 of said spring with roller 4.Do not having under the prerequisite of supporter, solid of rotation 3 is configured between roll shaft 2 and the roller 4.
In addition, Fig. 4 representes of the present invention and then other the rolling bearing for rocker arm of mode of execution.Fig. 5 is the figure that the part of the rocking arm rolling bearing that comprises Fig. 4 is amplified.In Fig. 4, running shaft 5 is configured in the central part of rocking arm 1, and rocking arm 1 is around its rotation.The end 1b of one side's of rocking arm 1 arm contacts with the end of engine valve 9, and the end 1a of the opposing party's arm contacts with the end of continuous motion stem 16.Regulate the function of contact position that has end 1a and the continuous motion stem 16 of adjusting rocking arm with screw rod 8.
The 16a of Bearing Installation portion at the sky of the lower end that is positioned at continuous motion stem 16 is provided with cam driven member main body 50, through assembly 17 rolling bearing for rocker arm is installed.Cam 6 contacts with the roller 4 of this rolling bearing driving force is transferred to continuous motion stem 16.Identical with above-mentioned mode of execution, under the prerequisite that does not have supporter, solid of rotation 3 is configured between roll shaft 2 and the roller 4.
In the parts of the rolling bearing for rocker arm that constitutes above-mentioned motor, the roll shaft 2 of interior quadrate part spare has been implemented the heat treatment that begins to explain at this, and its skin section is made into superfine austenite grain.
The interior quadrate part spare of above-mentioned Fig. 3 and Fig. 5 is that roll shaft 2 has the nitrogenize enriched layer, and implementing that in the skin section in the rolling surface zone that solid of rotation rolls high frequency hardening, austinite grain size are arranged is more than No. 1 of superfine (according to the JIS specification), and hardness is more than the HV653.Except the zone of said rolling surface (skin section and axle central part), having austinite grain size is more than No. 10 and thicker, and in addition, especially the hardness of end is low, is in the part of the following scope of HV300.In addition, the zone of the rolling surface that rolls at solid of rotation, implementing has high frequency hardening, and therefore, in skin section, retained austenite occupies 10～50 volume %.In addition, therefore the axle central part of rolling surface central authorities radio frequency heating and quenching when above-mentioned skin section is implemented high frequency hardening, is hardened, and in addition, generates retained austenite.Its result in skin section, is difficult to take place surface abrasion and from the peeling off of inner beginning type, in addition, at least in the scope from the axle central part to skin section of rolling surface by high strength, thereby, improve crack fatigue strength.On the other hand, at other positions such as ends,, therefore, be easy to riveted joint processing because hardness is low.Thereby processing is riveted at the two ends of roll shaft, in the chamfered section formation riveted joint fixed processing portion of roll shaft support.
Secondly, the mode of execution of the rolling bearing of the planet pin that is useful in planetary gear bearing mechanism is recorded and narrated.Shown in Fig. 6 A～6C and 7, between the sun gear axle 62 and inner gear shaft 72 of planetary gears 60 in automatic speed variator, comprise sun gear 64, internal gear 70, a plurality of planetary pinion 66.Sun gear 64 is formed with tooth at outer circumferential face, has with sun gear 62 all-in-one-pieces to concern.Internal gear 70 is formed with tooth at inner peripheral surface, has with internal gear 72 all-in-one-pieces to concern.Each planetary pinion 66 between sun gear 64 and internal gear 70, and can with 70 both engagements of sun gear 64 and internal gear, the periphery around sun gear 64 when carrying out rotation dallies.The gear of planetary gears 60 is in engagement often; Can be through applying driving force to one of them of sun gear 64 or planet frame 68 or internal gear 70; Or lock one of them, change rotating speed, sense of rotation, moment of torsion of the inner gear shaft 72 of corresponding sun gear axle 62 etc.
Also have,, also can use the interior wheel of the periphery that is fixed on planet pin 74 that is independent of planet pin 74 as the interior quadrate part spare of rolling bearing 80.Equally, as foreign side's parts of rolling bearing 80, also can use the foreign steamer in the interior week that is fixed on sun gear 66 that is independent of sun gear 66.
Among the parts that constitute rolling bearing 80 were bearing part, to the heat treatment of having implemented as the planet pin 74 of interior quadrate part spare to begin to explain at this, its top layer was made into superfine austenite grain.
In the rolling bearing in this embodiment; Interior quadrate part spare is that planet gear shaft 74 has the nitrogen enriched layer; Skin section in the zone of the rolling surface of solid of rotation rotation has been implemented high frequency hardening, and austinite grain size is more than No. 11 of superfine (according to the JIS specifications), and hardness is more than the HV653.Except the zone of said rolling surface (skin section and axle central part), exist like the bottom, that is: below No. 10, in addition, especially the hardness of end is in the following scope of low HV300 to austinite grain size for thicker.In the zone of the rolling surface that solid of rotation rotates, owing to implemented high frequency hardening, therefore, in skin section, retained austenite is more than the 10 volume %, below the 50 volume %.Therefore the axle center of rolling surface central authorities radio frequency heating and quenching when above-mentioned skin section is implemented high frequency hardening, is hardened, and in addition, generates retained austenite.Its result in skin section, is difficult to take place surface abrasion and from the peeling off of inner beginning type, in addition, at least in the scope from the axle central part to skin section of rolling surface by high strength, thereby, improve crack fatigue strength.On the other hand, at other positions such as ends,, therefore, be easy to riveted joint processing because hardness is low.Thereby processing is riveted at the two ends of roll shaft, in the chamfered section formation riveted joint fixed processing portion of roll shaft support.
Secondly, the interior quadrate part spare (roller bearing 2 or planet pin 74) to above-mentioned rolling bearing comprises that the heat treatment that carbonitriding is handled describes.Fig. 9 is the figure of the heat treatment method of explanation mode of execution of the present invention.In addition, Figure 10 is other the figure of heat treatment method of explanation mode of execution of the present invention.Fig. 9 is after carrying out the carbonitriding processing, and the heat treatment cycle curve of direct slow cool down, Figure 10 are that quick cooling is carried out the heat treatment cycle curve that quenching with Subsequent tempering is a temper then under the state of ordering less than A1 after carrying out the carbonitriding processing.The slow cool down of the heat treatment cycle curve among Fig. 9 and the quenching with Subsequent tempering among Figure 10 to the end for example of the part beyond the zone that reduces rolling surface, are played the effect that reduces hardness in correspondence with each other.Any one in the heat treatment cycle curve of Fig. 9 and Figure 10 no matter, all after, high frequency hardening is implemented in the zone (skin section～axle central part) of the rolling surface of above-mentioned parts, afterwards, implement low-temperature tempering.
In addition, can above-mentioned arbitrary heat treatment be implemented in the interior quadrate part spare and the cam of bearing part.
No matter handle through any one carbonitriding in the above-mentioned heat treatment, all forming " carbonitriding processing layer " is the nitrogen enriched layer.Because the concentration of carbon as raw-material steel in carbonitriding is handled is high, therefore, exist carbon under the atmosphere that common carbonitriding handles to be difficult to infiltrate the situation on the surface of steel.For example, under the high situation of the concentration of carbon of steel, there is the carburized case that generates than its high concentration of carbon, also exists to be difficult to generate situation than its high concentration of carbon.
But nitrogen concentration also relies on Cr concentration etc., however in common raw-material steel be to greatest extent about 0.25 weight % below, promptly very low, therefore, do not receive the influence of the concentration of carbon of raw material steel, and generate significant nitrogen enriched layer.
Secondly, how to generate microstructure by each processing spec like Fig. 9 and Figure 10.At first, for example the state more than the A1 point carries out the carbonitriding processing.In carbonitriding is handled, on the above-mentioned parts of rolling bearing, form the nitrogen enriched layer.In this nitrogen enriched layer, be that C, N hypereutectoid are infiltrated to iron atom Fe infitration type element, for example, and in austenite, carbide precipitate (2 coexistence mutually).That is, in the nitrogen enriched layer, constitute hypereutectoid steel.In addition, do not carrying out the inside that carbonitriding is handled, utilizing raw material is the composition of original steel, becomes the austenite phase.In addition, raw material are that steel also can be at ferrite and austenite 2 mutually or carry out carbonitriding under austenite and the temperature that cementite 2 coexists mutually and handle.
Secondly, when cooling, in the curve (being made as heating curve H1) of Fig. 9, begin to carry out slow cool down from the carbonitriding treatment temperature.The purpose of this slow cool down is softening tissue and improves processability.In this slow cool down, generate the pearlite that constitutes by ferrite and cementite in inside by above-mentioned austenite, but, promote softening through thickization of cohesion under the prerequisite that the cementite in the pearlite is not made as laminarization.Thereby, the temperature range of slow cool down be about (A1 point-100 ℃)～get final product till the carbonitriding treatment temperature.Even slow cool down is to low temperature thus, can not expect thickization of cohesion of cementite, spended time lowers efficiency on the contrary.Roughly, get final product about 620 ℃.Afterwards, can use ventilation type, also can carry out water-cooled or oil injection type for the shortening time.
In the nitrogen enriched layer, by the austenite generation ferrite of (carbide+austenite) tissue, carbide wherein condenses thickization.
In addition, in the curve (being made as heating curve H2) of Figure 10, for example carry out oil cooling etc. by the carbonitriding treatment temperature and quench.In this case, in inside, utilize the composition of original steel to generate martensite etc. by austenite.This martensitic structure is hard.Under the state that directly uses, therefore the riveted joint processing difficulties, carries out above-mentioned temper (quenching with Subsequent tempering).Tempering under the A1 point as far as possible near the temperature of A1 under carry out rapidly.That is, carry out high-temperature tempering.Thereby, it is desirable for tempering and in the scope of A1 point～650 ℃, carry out, in addition more preferably, in the scope of A1 point～680 ℃, carry out.Through this tempering, the high dislocation density of martensitic structure disappears, and obtains the tissue of the low ferrite of dislocation density and the cementite of thickization of cohesion.
In addition, in the nitrogen enriched layer, through quenchings such as oil coolings, by the austenite generation martensite of the tissue that when heating, generates (carbide+austenite).Martensite is softened owing to above-mentioned tempering equally.The former carbide cohesion that pre-exists.Also have, in the explanation of above-mentioned microstructure, as stated, with nitrogen or more the secondary cause of the microstructure of complicated reality ignore.
Secondly, according to heating curve H1 and H2, carry out high frequency hardening.In the last stage of this high frequency hardening, the nitrogen enriched layer is the carbide (ratio is big) and the ferritic tissue of fusion cohesion.In high frequency hardening, heating rapidly at this moment, in the time of the carbide solid solution, makes austenite give birth to nuclear.Because the density of the carbide that disperses is very high, therefore, it is very high that austenite is given birth to cuclear density, and the austenite of giving birth to nuclear associates each other and the crystal grain of the austenite structure that forms is superfine.In addition, because the nitrogen enriched layer is a hypereutectoid steel, therefore, and the carbide coexistence, the harsh achievement of this carbide stops the growth of the austenite grain of superfine.Thereby, in the nitrogen enriched layer, can obtain the austenite grain of superfine.Follow the temperature of heating rapidly to uprise, the carbide solid solution, solid solution has a lot of carbon on the austenite of superfine.In addition,, can receive the influence that is not the nitrogen enriched layer, but change basic identically with the variation of above-mentioned skin section at the axle central part.
Secondly, if at high frequency hardening, promptly quench after the heating rapidly, then austenite becomes morphology of martensite.At this moment, because solid solution has a lot of carbon, therefore, austenite is stablized, and trickle regional residual between the martensite has the unchanged austenite of form.These are exactly retained austenite.This retained austenite is owing to being formed between the martensite, and is therefore, very trickle.As percent by volume, retained austenite is 10～50 volume %.
Under the prerequisite that about 180 ℃ down greatly do not reduce hardness carry out tempering thereafter.In the tempering under about these 180 ℃, keep highdensity dislocation to disappear hardly.This tempering is that stabilizing tissue carries out.In this tempering, cementite does not condense, and takes place softening hardly yet.The high frequency hardening that comprises above-mentioned retained austenite is organized tough, and can under abominable service condition, realize the long life-span.
Through carrying out above-mentioned heat treatment, can the austenitic grain size in the zone (skin section and axle central part) of rolling surface be made as the ultrafine dust more than No. 11.In addition, can the hardness of skin section be made as more than the HV653, retained austenite is made as 10～50 volume %, preferred scope is the scope of 15～35 volume %.In addition, can the hardness of axle central part be made as more than the HV550, retained austenite is existed.On the other hand, with the part beyond the zone of rolling surface, for example, the hardness of end is made as below the HV300.Thereby, through above-mentioned heat treated bearing part by high strength or make and have high crack fatigue strength, thereby the rolling contact fatigue characteristic is the long lifetime, in addition, is easy to riveted joint processing.
Use Bearing Steel SUJ2, implemented the heat treatment of heating curve H1 shown in Figure 11 (corresponding diagram 9) and heating curve H2 (corresponding diagram 7) shown in Figure 12.Promptly; At first the steel to steel pipe or Cold Forging carry out the above carbonitriding processing of A1 point, afterwards, and according to heating curve H1 or H2; Slow cool down is to below (heating curve H1) A1 point, or quick cooling austenite (heating curve H2) carries out tempering (modified) after below the A1 point.Then, the zone corresponding with rolling surface (skin section～axle central part) implemented high frequency hardening.Above-mentioned heating curve H1, the temperature of H2 such as Figure 11 and shown in Figure 12.
In the sample that roll shaft 2 or planet pin 74 are made through above-mentioned heat treatment as sample, be 10～50 volume % at the skin section retained austenite, more preferably, and 15～35 volume %, the austinite grain size superfine turns to more than No. 11.In addition, the axle central part in the zone of rolling surface is together also quenched by radio frequency heating with above-mentioned skin section, and retained austenite is residual.This sample has been carried out hardness measurement.In addition, for relatively, also the sample body J in the example in the past of only carrying out high frequency hardening in skin section has been carried out hardness measurement.The shape of each sample and hardness measurement position are shown in Figure 13 A and 13B.Figure 13 A is the front view of sample body, and Figure 13 B is the transverse sectional view of sample body central authorities (through an A) in addition.In addition, measurement result is as shown in table 1.In Figure 13 A and Figure 13 B, the zone of the rolling surface 32 of sample body has the part 31 of also being hardened by high frequency hardening across between skin section～axle central part.
Table 1
The hardness measurement result
| The hardness measurement position | Routine in the past | The present invention's example | ? |
| Sample body J | Sample body J heating curve H 1 | Sample body J heating curve H 2 | ? |
| A | 780 | 790 | 790 |
| B | 735 | 800 | 800 |
| C | 220 | 250 | 260 |
| D | 210 | 260 | 270 |
| E | 215 | 730 | 710 |
| Retained austenite amount (volume %) | 7.5 | 24.7 | 25.5 |
| Austinite grain size number | 10.5 | 12 | 12 |
Can know according to table 1, in the sample body 1 and sample body 2 of the present invention's example, in the zone of rolling surface 32 (skin section～axle central part); The hardness of skin section A, B is HV790～800; In addition, axle central part E (with reference to Figure 13 B) is high for very, and is HV710～730; In addition, be HV250～270 among C beyond the zone of rolling surface and the D.The C of this position and the hardness of D are for being fit to the hardness of riveted joint processing.On the other hand, in routine in the past sample body J, be HV735～780 at the regional mesexine A of portion of rolling surface and the hardness of B, very low at axle central part E in addition, and be HV215.In addition, not receiving measuring position C and the hardness of D of the influence of high frequency hardening is HV210～220.
Table 2
Sample body
| ? | Sample body | Handle | The austinite grain size that A is ordered number | Retained austenite (volume %) |
| Routine in the past | Sample body J | Only rolling surface is carried out high frequency hardening | 10.5 | 7.5 |
| The present invention's example | Sample body 1 | Heating curve H 1 | 12 | 24.7 |
| Test body 2 | Heating curve H 2 | 12 | 25.5 | ? |
In addition, as shown in table 2, the above-mentioned size indicator of sample body 1,2 of the present invention is No. 12, and very trickle, and the nitrogen enriched layer is 10.5 in routine in the past sample body J, and thick slightly.In addition, the retained austenite that A is ordered is 24.7 volume % in the sample body 1 of product of the present invention, is 25.5 volume % in sample body 2 in addition, and is in suitable scope.On the other hand, be 7.5 volume % among the test body J of example in the past, and depart from and be in a little side from the scope that can prevent surface abrasion etc.
To the sample body 1,2 of product of the present invention and in the past the sample body J of example carry out the crack fatigue testing specimen and verified whether by high strength.Test method, shown in figure 14, be to utilize under the state of fulcrum 27 supporting at two ends with sample body 30, apply load portion 28 to the central part utilization of sample body 30 and repeat to apply load, method.Test conditions is as shown in table 3.The number of repetition of load till breakage to change applies drawn, and obtained to apply load one damaged number of times line.Test result is as shown in table 4.
Table 3
Crack fatigue test condition
| Apply load | 2000～10000N (arbitrarily) |
| Apply frequency | 10～120Hz (changing) according to applying load |
| Apply waveform | The Sin ripple |
| Apply number of times | Until breakage |
Table 4
The crack fatigue test results
| Sample body | Apply number of times 10 6Inferior damaged load (ratio) | ? |
| Routine in the past | Sample body J | 1 |
| The present invention's example | Sample body 1 | 1.32 |
| Sample body 2 | 1.28 | ? |
In table 4, be made as under 1 the prerequisite in the value of sample body J of example in the past, will be 10 applying number of times
6The interior damaged load that applies is represented with ratio.In the sample body of product of the present invention, be 1.32, compare example in the past, increased 32%.In addition, in sample body 1 of the present invention, be 1.28, comparing in the past, example has increased 28%.Its result can confirm to have realized high crack fatigue strength.
Secondly, said sample body 1 and 2 has carried out the rotary-type fatigue life test of foreign steamer.The austinite grain size of the A point (skin section) of sample body number and retained austenite are illustrated in table 2, in addition test conditions are illustrated in table 5.The testing apparatus of the rotary-type fatigue life test of above-mentioned foreign steamer is illustrated in Figure 15.In this fatigue experimental device, configuration roller 35 makes the outside of clamping sample body 30 from above-below direction, and the rotation when outside is close to and apply external pressure of the skin section of 35 pairs of sample body 30 of roller is to sample body 30 stress applications.
Table 5
The fatigue life test condition
| Project | Content |
| Testing machine | The rotary-type life test machine of foreign steamer |
| Test film | Rocker bearing tissue article |
| Load (N) | 2200N |
| The foreign steamer rotational speed | 7000rpm |
| Lubricated | Engine oil 10w-30 |
| The oil temperature | 100℃ |
| Life-span | Peel off the life-span |
Can know according to above-mentioned test conditions, in process of the test, surface abrasion and peeling off from inner beginning type taken place.Thereby,, can confirm to wear and tear and the inner certainly life-span of peeling off both that begins type through implementing this test.The result of this fatigue test is as shown in table 6.
Table 6
Test result of fatigue life
| ? | Sample body | Life-span is than (L10) |
| Routine in the past | Sample body J | 1.0 |
| The present invention's example | Sample body 1 | 3.8 |
| Sample body 2 | 3.8 | ? |
Can know that according to table 6 sample body 1 and 2 of the present invention's example has 3.3～3.8 times the long lifetime of the sample body J of example in the past.In routine in the past sample body J; Have reason to think owing to do not carry out the carbonitriding processing; Also have, do not carry out that high frequency hardening is handled and the metal structure (austinite grain size, retained austenite amount) that causes and cause lack fatigue life at whole skin section～axle central part.
Should think that this disclosed mode of execution and embodiment are example in all respects, not provide constraints.Scope of the present invention is not limited to above-mentioned explanation, all changes of carrying out in the meaning that the protection domain that is included in and requires is impartial and the scope.
In rolling bearing of the present invention; In the parts of the roll shaft of the rocking arm of motor car engine and planet pin of planetary gears etc.; The zone of its rolling surface all has superiority on anti-surface abrasion, rolling fatigue life and crack fatigue strength; In addition, the end that is softened has good riveted joint processability, therefore effectively.
Claims (5)
1. a rolling bearing is characterized in that,
Have: foreign side's parts, the interior side's of said foreign side parts interior quadrate part spare and be present in said foreign side parts and interior quadrate part spare between solid of rotation,
Wherein at least one parts of said foreign side parts and interior quadrate part spare have the nitrogen enriched layer; In said at least one parts; Supplying the austinite grain size of skin section in zone of the rolling surface of said solid of rotation rotation is more than No. 11, and hardness is HV (Vickers hardness) more than 653, and the hardness of the end of these parts is below the HV300; The hardness of the axle central part that rolling surface is central is made as HV710～HV730
The zone of said rolling surface is by high frequency hardening,
Said at least one parts are carried out carbonitriding handle the back slow cool down more than the A points, then high frequency hardening is implemented in the zone of said rolling surface and handled to less than the A1 point,
Said rolling bearing uses the SUJ2 Bearing Steel.
2. rolling bearing according to claim 1 is characterized in that,
Except the axle central part of the skin section in the zone of said rolling surface and rolling surface central authorities, comprise that its microstructure has the zone of ferrite and carbide.
3. rolling bearing according to claim 1 is characterized in that,
In the skin section in the zone of said rolling surface, retained austenite occupies 10～50 volume %, and there is retained austenite in the axle central part in these rolling surface central authorities.
4. the described rolling bearing of claim 1 that is used for rocking arm.
5. the said rolling bearing of claim 1 that is used for planetary gears.
Applications Claiming Priority (6)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2005069815A JP4566036B2 (en) | 2005-03-11 | 2005-03-11 | Rolling bearing |
| JP2005-069815 | 2005-03-11 | ||
| JP2005069815 | 2005-03-11 | ||
| JP2005151433A JP2006329268A (en) | 2005-05-24 | 2005-05-24 | Rolling bearing for planetary gear mechanism |
| JP2005-151433 | 2005-05-24 | ||
| JP2005151433 | 2005-05-24 |
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| CN1831303A CN1831303A (en) | 2006-09-13 |
| CN1831303B true CN1831303B (en) | 2012-03-21 |
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| JP2008020003A (en) * | 2006-07-13 | 2008-01-31 | Ntn Corp | Process for producing track member and valve gear, and track member |
| JP5388264B2 (en) * | 2007-12-14 | 2014-01-15 | Ｎｔｎ株式会社 | Manufacturing method of rolling shaft |
| JP5603889B2 (en) * | 2011-02-14 | 2014-10-08 | ヤマハ発動機株式会社 | Steel part, single-cylinder internal combustion engine, straddle-type vehicle, and method for manufacturing steel part |
| US10087989B2 (en) | 2013-06-06 | 2018-10-02 | Ntn Corporation | Bearing component and rolling bearing |
| WO2014196431A1 (en) | 2013-06-06 | 2014-12-11 | Ntn株式会社 | Bearing component and rolling bearing |
| US10156259B2 (en) | 2013-06-06 | 2018-12-18 | Ntn Corporation | Bearing component and rolling bearing |
| WO2014196428A1 (en) | 2013-06-06 | 2014-12-11 | Ntn株式会社 | Bearing component and rolling bearing |
| EP3181838B1 (en) * | 2015-12-16 | 2019-10-23 | Aktiebolaget SKF | Method for manufacturing a pin for cam follower roller device |
| JP7550510B2 (en) * | 2019-09-26 | 2024-09-13 | Ntn株式会社 | Rolling bearings |
| JP2021055167A (en) * | 2019-10-01 | 2021-04-08 | Ntn株式会社 | Bearing component |
| CN114737149A (en) * | 2022-04-27 | 2022-07-12 | 苏州特兴哲金属制品有限公司 | Carbon nitrogen co-cementation surface modification method for GCr15 bearing |
| WO2024075695A1 (en) * | 2022-10-05 | 2024-04-11 | Ｎｓｋステアリング＆コントロール株式会社 | Shaft unit, manufacturing method therefor, and electric assist device |
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|---|---|---|---|---|
| US4696581A (en) * | 1985-12-03 | 1987-09-29 | Ntn Toyo Bearing Co., Ltd. | Rolling bearing |
| US20040079310A1 (en) * | 2002-10-17 | 2004-04-29 | Ntn Corporation | Full-type rolling bearing and roller cam follower for engine |
| CN1573148A (en) * | 2003-06-05 | 2005-02-02 | Ntn株式会社 | Rolling bearing, cam-follower, and cam |
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| JPS61279620A (en) * | 1985-06-03 | 1986-12-10 | Daido Steel Co Ltd | Working heat treating method for steel |
| JPH05179350A (en) * | 1991-12-27 | 1993-07-20 | Ntn Corp | Production of roller shaft for cam follower with roller |
| JPH0557496U (en) * | 1991-12-27 | 1993-07-30 | エヌティエヌ株式会社 | Cam follower with roller |
| JP2004278528A (en) * | 2003-02-28 | 2004-10-07 | Ntn Corp | Cam follower with roller and steel member of engine |
| JP4380217B2 (en) * | 2003-05-14 | 2009-12-09 | 日本精工株式会社 | Manufacturing method of pinion shaft |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4696581A (en) * | 1985-12-03 | 1987-09-29 | Ntn Toyo Bearing Co., Ltd. | Rolling bearing |
| US20040079310A1 (en) * | 2002-10-17 | 2004-04-29 | Ntn Corporation | Full-type rolling bearing and roller cam follower for engine |
| CN1573148A (en) * | 2003-06-05 | 2005-02-02 | Ntn株式会社 | Rolling bearing, cam-follower, and cam |
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| Title |
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