CN109790614A

CN109790614A - Nitrogen treatment component and its manufacturing method

Info

Publication number: CN109790614A
Application number: CN201780058329.5A
Authority: CN
Inventors: 梅原崇秀; 祐谷将人
Original assignee: Nippon Steel Corp
Current assignee: Nippon Steel Corp
Priority date: 2016-10-05
Filing date: 2017-10-05
Publication date: 2019-05-21
Also published as: WO2018066667A1; BR112019005781A2; JP6766876B2; JPWO2018066667A1; US20200024720A1; EP3524709A4; EP3524709A1; KR20190022801A

Abstract

A kind of not only detorsion is excellent but also rotary bending fatigue intensity also excellent nitrogen treatment component and its manufacturing method, the nitrogen treatment component is characterized in that, using the steel with defined chemical composition as raw material, wherein, the component has be formed in steel surface to contain iron, nitrogen and carbon with a thickness of 3 μm of compound layers more than or lower than 15 μm, phase structure in the compound layer of range until from surface to 5 μm of depth in terms of the area ratio containing 50% or more γ ' phase, void area rate is lower than 1% in the range of until from surface to 3 μm of depth, the compressive residual stress on compound layer surface is 500MPa or more.

Description

Nitrogen treatment component and its manufacturing method

Technical field

The present invention relates to the steel parts for implementing gas nitriding processing, in particular to detorsion and bending fatigue strength Nitrogen treatment component and its manufacturing methods such as excellent gear, CVT pulley.

Background technique

For the steel part used in automobile and various industrial machines etc., in order to make fatigue strength, wearability and resistance to burning The engineering properties such as knot property improve, and implement the heat treatment of the Surface hardened layers such as carburizing and quenching, high-frequency quenching, nitridation and tufftride.

Nitrogen treatment and tufftride processing are due to being in A₁Point carries out in ferrite area below, in processes without phase Become, so heat treatment strain can be reduced.Therefore, nitrogen treatment and tufftride processing are mostly used for the dimensional accuracy for having high Component and large-scale component, such as gear used in transmission parts suitable for automobile, crankshaft used in engine.

Nitrogen treatment is the processing method for making nitrogen intrusion steel surface.For medium used in nitrogen treatment, have gas, Salt bath, plasma etc..For the transmission parts of automobile, the main gas nitriding processing excellent using productivity.Pass through gas Nitrogen treatment forms the compound layer (Fe with a thickness of 10 μm or more in steel surface₃The layer that the nitride such as N are precipitated), in turn, The steel surface layer of the downside of compound layer forms nitrogen diffusion layer, that is, hardened layer.Compound layer is mainly by Fe_2~3N (ε) and Fe₄N (γ ') is constituted, and the hardness of compound layer is high compared with the steel for becoming base material.Therefore, compound layer can make at the initial stage used The wearability of steel part improves.

Patent Document 1 discloses a kind of nitrogen treatment components, wherein by by the γ ' phase ratio in compound layer It is set as 30mol% or more, so that bending fatigue strength be made to improve.

Patent Document 2 discloses a kind of low strain dynamic and with excellent surface fatigue intensity and bending fatigue strength Steel member generates the iron nitride compound layer with defined structure in steel member.

Patent Document 3 discloses a kind of manufacturing methods for nitrogenizing component, by the way that the content of element is optimized, from And it improves the fatigue strength after nitrogen treatment, inhibit the deformation after nitrogen treatment.

Existing technical literature

Patent document

Patent document 1: Japanese Unexamined Patent Publication 2015-117412 bulletin

Patent document 2: Japanese Unexamined Patent Publication 2013-221203 bulletin

Patent document 3: International Publication No. 2016/098143

Summary of the invention

Problems to be solved by the invention

It is believed that the nitrogen treatment component of patent document 1 is due to being to have used CO in atmosphere gas₂The soft nitrogen of gas Change, so the surface side of compound layer easily becomes ε phase, therefore bending fatigue strength is also insufficient.In addition, patent document 2 No matter nitrogen treatment component is due to the ingredient of steel, according to NH₃Gas becomes 0.08~0.34, H₂Gas become 0.54~ 0.82、N₂Gas is controlled as 0.09~0.18 mode, so being possible to the knot of compound layer according to the ingredient of steel Structure and thickness do not reach target.

For the nitrogen treatment of patent document 3, the control of gas condition when processing is inappropriate, in compound layer The ratio of γ ' phase is lower, voidage is got higher, and easily becomes the starting point of spot corrosion and crooked fatigue fracture.In addition, with regard to patent document 3 For disclosed gas soft nitriding processing, voidage is easy to get higher.

The object of the present invention is to provide not only detorsion is excellent but also rotary bending fatigue intensity also excellent component And its manufacturing method.

Means for solving the problems

The inventors of the present invention are conceived to the form that the compound layer on surface of steel is formed in by nitrogen treatment, Relationship with fatigue strength is investigated.

Itself as a result, it has been found that: carried out under the nitridation gesture control for the C amount for considering blank by the way that the steel of ingredient will be had adjusted Nitridation inhibits porous generation, the compression on surface layer is remained so that surface to be nearby made to the phase structure based on γ ' phase Stress is set to be constant value or more, and thus, it is possible to make the nitridation with excellent detorsion and rotary bending fatigue intensity Component.

The present invention is further to be studied and completed repeatedly based on above-mentioned understanding, and purport is as described below.

A kind of nitrogen treatment component, which is characterized in that it is using following steel as raw material, and the steel are with quality % Meter containing C:0.20~0.60%, Si:0.05~1.5%, Mn:0.2~2.5%, P:0.025% or less, S:0.003~ 0.05%, Cr:0.05~0.50%, Al:0.01~0.05%, N:0.003~0.025%, Nb:0~0.1%, B:0~ 0.01%, Mo:0% more than or lower than 0.50%, V:0% more than or lower than 0.50%, Cu:0% more than or lower than 0.50%, Ni:0% is more than or lower than 0.50% and Ti:0% is more than or lower than 0.05%, and remainder is Fe and impurity, wherein the component Be formed in steel surface containing iron, nitrogen and carbon with a thickness of 3 μm of compound layers more than or lower than 15 μm, surface~5 μm Depth compound layer in phase structure in terms of the area ratio containing 50% or more γ ' phase, it is empty in the depth of surface~3 μm Gap the area ratio is lower than 10%, and the compressive residual stress on compound layer surface is 500MPa or more.

Invention effect

In accordance with the invention it is possible to obtain that not only detorsion is excellent but also the also excellent nitridation of rotary bending fatigue intensity Processing component.

Detailed description of the invention

Fig. 1 is the figure for illustrating the measuring method of depth of compound layer.

Fig. 2 is an example of the macrograph of compound layer and diffusion layer.

Fig. 3 is the figure for indicating to be formed with the appearance in gap in compound layer.

Fig. 4 is the example that the macrograph in gap is formed in compound layer.

Fig. 5 is the figure for indicating the relationship of phase structure and rotary bending fatigue intensity of nitridation gesture and compound layer.

Fig. 6 is the shape of the 4 bend test pieces used to evaluate detorsion.

Fig. 7 is the shape for evaluating the cylinder test film of rotary bending fatigue intensity.

Specific embodiment

Hereinafter, each necessary condition of the invention is described in detail.Firstly, the chemical group to the steel for becoming raw material At being illustrated.Hereinafter, indicating that the content of each component element and " % " of the concentration of element in parts surface refer to " quality % ".

[C:0.20%~0.60%]

C is the core hardness in order to ensure component and the element needed.When the content of C is lower than 0.20%, since core is strong Degree becomes too low, so detorsion and bending fatigue strength are greatly reduced.In addition, if the content of C is more than 0.60%, Compound layer thickness becomes larger, and detorsion and resistance to bend(ing) are greatly reduced.The preferred scope of C content is 0.30~0.50%.

[Si:0.05%~1.5%]

Si is to improve core hardness by solution strengthening.In order to play the effect, Si contains 0.05% or more.Another party Face, if the content of Si is more than 1.5%, since the intensity after bar steel, wire rod and warm and hot forging becomes excessively high, so machining Property is greatly reduced.The preferred scope of Si content is 0.08~1.3%.

[Mn:0.2%~2.5%]

Mn is to improve core hardness by solution strengthening.In addition, Mn in nitrogen treatment, is formed fine in hardened layer Nitride (Mn₃N₂), wearability and bending fatigue strength are improved by precipitation strength.These effects in order to obtain, Mn are needed It to be 0.2% or more.On the other hand, if the content of Mn is more than 2.5%, due to not only improving the effect of bending fatigue strength Saturation, and the hardness become after the bar steels of raw material, wire rod and warm and hot forging becomes excessively high, thus machinability significantly under Drop.The preferred scope of Mn content is 0.4~2.3%.

[P:0.025% or less]

P is impurity, keeps component brittle since cyrystal boundary segregation occurs, so content is preferably less.If the content of P is more than 0.025%, it is likely that detorsion and bending fatigue strength decline.For preventing the P of the decline of bending fatigue strength from containing The preferred upper limit of amount is 0.018%.It is difficult to for content to be set as 0 completely, real lower limit is 0.001%.

[S:0.003%~0.05%]

S forms MnS in conjunction with Mn, improves machinability.The effect in order to obtain, S need for 0.003% with On.However, becoming easy if the content of S is more than 0.05% and generating coarse MnS, detorsion and flexural fatigue are strong Degree is greatly reduced.The preferred scope of S content is 0.005~0.03%.

[Cr:0.05%~0.50%]

Cr forms fine nitride (CrN) in nitrogen treatment in hardened layer, makes to be bent by precipitation strength tired Labor intensity improves.The effect in order to obtain, Cr need to be 0.05% or more.On the other hand, if the content of Cr is more than 0.5%, Then the hardness after the bar steel, wire rod and warm and hot forging due to becoming raw material becomes excessively high, so detorsion declines.Cr content Preferred scope be 0.10~0.30%.

[Al:0.01%~0.05%]

Al is deoxidant element, needs 0.01% or more for sufficient deoxidation.On the other hand, Al hard easy to form Oxide system field trash, if the content of Al is more than 0.05%, the decline of bending fatigue strength becomes significantly, even if meeting it Its necessary condition also cannot get desired bending fatigue strength.The preferred scope of Al content is 0.02~0.04%.

[N:0.003%~0.025%]

N forms AlN, VN in conjunction with Al, V.AlN, VN have following effects: passing through the pinning effect of austenite grain The tissue of steel before nitrogen treatment is miniaturize, the unevenness of the mechanical property of nitrogen treatment component is reduced.It is lower than in the content of N When 0.003%, it is difficult to obtain the effect.On the other hand, it if the content of N is more than 0.025%, to be formed slightly due to becoming easy Big AlN, so becoming difficult to obtain above-mentioned effect.The preferred scope of N content is 0.005~0.020%.

The chemical component of the steel of raw material as nitrogen treatment component of the invention contains above-mentioned element, remainder For Fe and inevitable impurity.So-called inevitable impurity refers to the process of ingredient contained in raw material or in manufacture In mixed ingredient, be not the ingredient it is intended that containing in steel.

But the steel for becoming the raw material of nitrogen treatment component of the invention can also be containing member as shown below usually generation For a part of Fe.

[Nb:0%~0.1%]

Nb forms NbC, NbN in conjunction with C, N.By the pinning effect of NbC, NbN, to show following effects: difficult to understand The coarsening of family name's body crystal grain is inhibited, and the tissue of the steel before nitrogen treatment is miniaturize, and reduces the machine of nitrogen treatment component The unevenness of tool characteristic.The effect can be obtained as long as micro addition Nb, but in order to more reliably obtain effect, Nb is preferably set to 0.01% or more.If the content of Nb is more than 0.1%, coarse NbC, NbN are formed due to becoming easy, so becoming difficult to Obtain above-mentioned effect.

[B:0%~0.01%]

B has the effect of inhibiting the cyrystal boundary segregation of P and improving toughness.In addition, forming BN in conjunction with N and proposing machinability It is high.These effects can be obtained as long as micro addition B, but in order to more reliably obtain effect, B be preferably set to 0.0005% with On.If the content of B is more than 0.01%, it is likely that not only said effect is saturated, but also can be caused because a large amount of BN is segregated Cracking is generated in steel.

[Mo:0% is more than or lower than 0.50%]

Mo forms fine nitride (Mo in nitridation in hardened layer₂N), keep flexural fatigue strong by precipitation strength Degree improves.In addition, Mo plays age-hardening effect in nitridation and improves core hardness.Mo for obtaining these effects contains Amount is preferably set to 0.01% or more.On the other hand, the content of Mo be 0.50% or more when, due to become raw material bar steel, Hardness after wire rod and warm and hot forging becomes excessively high, so machinability is remarkably decreased, cost of alloy also increases in addition to this.With In the Mo content for ensuring machinability the preferred upper limit be lower than 0.40%.

[V:0% is more than or lower than 0.50%]

V forms fine nitride (VN) in nitridation and tufftride, mentions bending fatigue strength by precipitation strength Height also improves the core hardness of component in addition to this.In addition, also having the effect of tissue miniaturization.These are acted in order to obtain, V is preferably set to 0.01% or more.On the other hand, when the content of V is 0.50% or more, due to becoming bar steel, the line of raw material Hardness after material and warm and hot forging becomes excessively high, so machinability is remarkably decreased, cost of alloy also increases in addition to this.For Ensure the preferred scope of the V content of machinability lower than 0.40%.

[Cu:0% is more than or lower than 0.50%]

Cu improves the core hardness of component and the hardness of nitrogen diffusion layer as solution strengthening element.In order to play Cu Solution strengthening effect, preferably comprise 0.01% or more.On the other hand, when the content of Cu is 0.50% or more, due to becoming Hardness after the bar steels of raw material, wire rod and warm and hot forging becomes excessively high, so machinability is remarkably decreased, heat is prolonged in addition to this Malleability also declines, thus in hot rolling, when warm and hot forging become injurious surface mark Producing reason.For maintaining the Cu of high-temperature ductility to contain The preferred scope of amount is lower than 0.40%.

[Ni:0% is more than or lower than 0.50%]

Ni improves core hardness and surface hardness by solution strengthening.In order to play Ni solution strengthening effect, Preferably comprise 0.01% or more Ni.On the other hand, when the content of Ni is 0.50% or more, after bar steel, wire rod and warm and hot forging Hardness become excessively high, so machinability is remarkably decreased, cost of alloy also increases in addition to this.For adequately being cut The preferred scope for cutting the Ni content of processability is lower than 0.40%.

[Ti:0% is more than or lower than 0.05%]

Ti forms TiN in conjunction with N, improves core hardness and surface hardness.The effect in order to obtain, Ti are preferably set It is 0.005% or more.On the other hand, when the content of Ti is 0.05% or more, make the effect of core hardness and surface hardness raising Saturation, cost of alloy also increases in addition to this.The preferred scope of Ti content is 0.007% more than or lower than 0.04%.

Next, being illustrated to the compound layer of nitrogen treatment component of the invention.

[thickness of compound layer: 3 μm more than or lower than 15 μm]

So-called compound layer refers to that the layer of the iron-nitride formed by nitrogen treatment, thickness will affect nitrogen treatment The detorsion and bending strength of component.If compound layer is blocked up, the starting point of crooked fatigue fracture is easily become.If Compound layer is excessively thin, then is unable to fully obtain the residual stress on surface, detorsion and bending fatigue strength decline.In this hair In bright nitrogen treatment component, from the viewpoint of detorsion and bending strength, the thickness of compound layer be set as 3 μm with Above and it is lower than 15 μm.

The thickness of compound layer will be ground, is etched simultaneously for the vertical cross-section of test material after gas nitriding processing Optical microscopy is observed to measure.Etching is with 3% nital progress 20~30 seconds.Compound layer exists In the surface layer of low-alloy steel, it is observed as the uncorroded layer of white.By optical microscopy to the tissue shot with 500 times Photo observes 5 visual field (visual field areas: 2.2 × 10⁴μm²).In each visual field, measure at 4 points for every 30 μm in the horizontal direction.It will The average value of 20 points of the value measured is defined as compound thickness (μm).The outline of measuring method is shown in Fig. 1, is shown in Fig. 2 An example of the macrograph of compound layer and diffusion layer out.

[γ ' the phase ratio of the compound layer of surface~5 μm: 50% or more]

If the ratio of γ ' phase is low in the compound layer of surface~5 μm, ε phase ratio is high, compound layer is rectified in bending The starting point of fracture is easily become when timing and flexural fatigue.This is because: the Fracture Toughness of ε phase is mutually lower than γ '.In addition, such as Near fruit surface mutually be γ ' phase, then near surface mutually be ε phase the case where compared with, become easy by it is aftermentioned compression it is residual It stays stress to import surface, fatigue strength can be made to improve.

γ ' phase ratio in compound layer passes through electron backscatter diffraction method (Electron BackScatter Diffraction:EBSD it) finds out.Specifically, to 150 μ of area until slave most surface to 5 μm of depth of compound layer m²EBSD measurement is carried out, production differentiates the analysis diagram of γ ' phase, ε phase.Then, image is parsed for obtained EBSD, uses figure The area ratio that γ ' phase is found out as handling application program, is defined as γ ' phase ratio (%).In EBSD measurement, with 4000 times It is appropriate that the multiplying power of front and back, which measures 10 visual fields or so,.

Above-mentioned γ ' phase ratio refers to the ratio of the γ ' phase of " compound layer " of the depth of surface~5 μm.I.e. in chemical combination In the case that the thickness of nitride layer is started from surface less than 5 μm, the γ ' calculated in the region of this part of compound layer thickness is compared Rate.As an example, if it is 3 μm that the thickness of compound, which is from surface start of calculation, the compound layer of the depth of surface~3 μm γ ' phase ratio become γ ' phase ratio.

γ ' phase ratio is preferably 60% or more, and more preferably 65% or more, further preferably 70% or more.

It is also possible to consider use X-ray diffraction the method that finds out for γ ' phase ratio.However, with regard to being carried out using X-ray diffraction Measurement for, measurement region thicken, correct γ ' phase ratio can not be found out.Therefore, in the compound layer in the present invention γ ' phase ratio be set as the value found out by EBSD.

[the void area rate of the compound layer of surface~3 μm: being lower than 10%]

The gap of the compound layer of surface~3 μm can generate stress concentration, become the starting point of crooked fatigue fracture.Therefore, Void area rate needs to be set to be lower than 10%.

Gap is formed in the following way: in the steel surface small by base material bring binding force, from energy such as crystal boundaries Stable position, N in amount₂Gas is detached from along crystal boundary from steel surface, and gap is consequently formed.With regard to N₂Generation for, it is aftermentioned Nitrogenize gesture K_NIt is more high, become more is easy to produce.This is because: due to K_NIt gets higher and causes bcc → γ ' → ε phase transformation, with γ ' compares the N of ε phase₂Solid solution capacity it is larger, so ε, which is compared, is easy to produce N₂Gas.It shows in Fig. 3 and is formed in compound layer The outline in gap shows the macrograph for being formed with gap in Fig. 4.

Void area rate can be measured by optical microphotograph sem observation.Specifically, to the table in the section for test material The depth of face~3 μm measures 5 visual field (visual field areas: 5.6 × 10 with 1000 times of multiplying power³μm²), for each visual field, by gap It is set as void area rate in the ratio shared into the range of 3 μm of depth from most surface.

Void area rate is preferably shorter than 5%, more preferably less than 2%, even more preferably below 1%, most preferably 0.

[compressive residual stress on compound layer surface: 500MPa or more]

Nitrogen treatment component of the invention is by nitrogen treatment to make the Surface hardened layer of steel, while to the surface section of steel Compressive residual stress is imported, the fatigue strength of component, wearability improve.Nitrogen treatment component of the invention passes through to compound layer Above-mentioned raising is carried out, the compressive residual stress of 500MPa or more is further imported in surface, to become with excellent The component of bending fatigue strength.Manufacturing method for importing from such compressive residual stress to the surface of component will be chatted later It states.

Next, being illustrated to an example of the manufacturing method of nitrogen treatment component of the invention.

In the manufacturing method of nitrogen treatment component of the invention, gas nitriding is implemented to the steel with above-mentioned ingredient Processing.The treatment temperature of gas nitriding processing is 550~620 DEG C, and the gas nitriding processing whole processing time is 1.5~10 small When.

[treatment temperature: 550~620 DEG C]

The temperature (nitrogen treatment temperature) of gas nitriding processing is mainly related with the diffusion velocity of nitrogen, to surface hardness and firmly Change layer depth to impact.If nitrogen treatment temperature is too low, the diffusion velocity of nitrogen is slow, and surface hardness is lower, hardened-depth Degree shoals.On the other hand, if nitrogen treatment temperature is more than A_C1Point can then generate the nitrogen compared with ferritic phase (α phase) in steel The small austenite phase (γ phase) of diffusion velocity, surface hardness is lower, and case depth shoals.Therefore, in the present embodiment, Nitrogen treatment temperature is 550~620 DEG C around ferrite temperature region.In this case, surface hardness is able to suppress to be lower, And it is able to suppress case depth to shoal.

[gas nitriding processing whole processing time: 1.5~10 hours]

Gas nitriding processing is comprising NH₃、H₂、N₂Atmosphere under implement.The time of nitrogen treatment entirety, i.e. from nitridation Time (processing time) until the start and ending of processing is related with the scattering and permeating of the formation of compound layer and decomposition and nitrogen, Surface hardness and case depth are impacted.If handled, the time is too short, and surface hardness is lower, and case depth becomes Shallowly.On the other hand, if processing overlong time, denitrogenation, decarburization, the surface hardness decline of steel can be generated.If handling the time Too long, then further manufacturing cost is got higher.Therefore, the processing time of nitrogen treatment entirety is 1.5~10 hours.

In addition, the atmosphere that the gas nitriding of present embodiment is handled is in addition to NH₃、H₂And N₂In addition, also inevitably include The impurity such as oxygen, carbon dioxide.Preferred atmosphere is NH₃、H₂And N₂Add up to 99.5% (volume %) or more.

If the carbon monoxide comprising several % or so, carbon dioxide atmosphere under implement gas soft nitriding processing, can It is preferentially produced the high ε phase of the solid solution limit of C.Since C can not be almost dissolved by γ ' layer, so implementing tufftride processing In the case of, it is single-phase that compound layer becomes ε.In turn, since the speed of growth ratio γ ' of ε phase is mutually fast, so stably generating ε phase Gas soft nitriding when compound layer can be formed thicklyer with the thickness than needs.Therefore, it does not need to implement gas in the present invention The processing of body tufftride, but need to implement to control nitridation gesture K as described later_NGas nitriding processing.

[gas condition of nitrogen treatment]

In nitridation treatment method of the invention, implement nitrogen under the nitridation gesture that is controlled considering the C amount of blank Change processing.Thereby, it is possible to by the phase structure in the compound layer of the depth of surface~5 μm be set as γ ' phase ratio be 50% with On, the void area rate in the depth of surface~3 μm is set to be lower than 1%, by the compressive residual stress on compound layer surface It is set as 500MPa or more.

The nitridation gesture K of gas nitriding processing_NIt is defined by following formula.

K_N(atm^-1/2)=((NH₃Divide (atm))/[(H₂It divides (atm))^3/2]

The NH of the atmosphere of gas nitriding processing₃And H₂Partial pressure can be controlled by adjusting the flow of gas.In order to pass through Nitrogen treatment forms compound layer, K when gas nitriding being needed to handle_NMore than certain value, but as described above, if K_NBecome Must be excessively high, then it is easy to produce N₂The ratio of the ε phase of gas becomes more, and gap becomes more.Therefore, K is set_NCondition, inhibit gap production Life is important.

The research of the inventors of the present invention as a result, it has been found that: gas nitriding processing nitrogen treatment gesture will affect chemical combination The phase structure of nitride layer and the rotary bending fatigue intensity of nitrogen treatment component, optimal nitridation gesture are determined by the C content of steel.

Specifically, it is understood that: when the C content (quality %) of steel is set as (quality %C), if gas nitriding is handled When nitrogen treatment gesture gas nitriding processing in always meet 0.15≤K_N≤ -0.17 × ln (quality %C)+0.20, then change It is 50% or more that the phase structure for closing nitride layer, which can reach γ ' phase ratio, in turn, nitrogen treatment component have high detorsion and Rotary bending fatigue intensity.

Even if the average nitrogen treatment gesture of gas nitriding processing meets above formula, taking even be unsatisfactory for the nitridation of above formula for the moment In the case where handling gesture value, the γ ' phase ratio in compound layer will not become 50% or more.

Shown in Fig. 5 the relationship of the γ ' ratio and rotary bending fatigue intensity to nitrogen treatment gesture and compound layer into Gone investigation result.Fig. 5 is the figure of the steel a (table 1) about aftermentioned embodiment.

Like this, in this nitridation treatment method, in nitridation gesture K corresponding with the C amount of steel of blank is become_NUnder implement Gas nitriding processing.Thus, it becomes able to steadily assign γ ' phase to the surface of steel, excellent resist bending correction can be obtained Property, rotary bending fatigue intensity, be preferably able to be bent it is mandatory be 1.2% or more, rotary bending fatigue intensity is The nitrogen treatment component of 520MPa or more.

Embodiment

Steel a~aa with chemical component shown in table 1 is melted with 50kg vacuum fusion furnace to manufacture molten steel, Molten steel is cast and has manufactured steel ingot.It should be noted that a~s in table 1 be with chemistry specified in the present invention at The steel divided.On the other hand, steel t~aa is comparative example of at least one kind of element or more departing from chemical component specified in the present invention Steel.

[table 1]

Warm and hot forging is carried out to the steel ingot and the pole that diameter is 25mm is made.Then, after by the annealing of each pole, implement to cut It cuts processing and has made shown in Fig. 2 for evaluating the square test film of detorsion.In turn, it has made shown in Fig. 3 For evaluating the cylinder test film of resist bending fatigue strength.

For test film collected, gas nitriding processing is implemented under the following conditions.Test film is packed into gas In nitriding furnace, NH is imported in furnace₃、H₂、N₂Each gas, implement nitrogen treatment under the conditions of shown in the table 2.Wherein, it tries Test number 32 be set as being added in atmosphere be calculated as with volume fraction 3% CO₂The gas soft nitriding of gas is handled.To the GN 2 Changing treated, test film implemented using 80 DEG C of oil that oil is cold.

H in atmosphere₂Partial pressure is using the thermal conductivity H being directly mounted on gas nitriding furnace body₂Sensor carries out Measurement.The thermal conductivity degree difference of calibrating gas and measurement gas is converted into gas concentration to be determined.H₂Partial pressure is in gas It is persistently determined during nitrogen treatment.

In addition, NH₃Partial pressure is that manual glass pipe type NH is installed outside furnace₃Analysis meter is determined.

Measurement in every 10 minutes remains NH₃Partial pressure, at the same time calculate nitridation gesture K_N, in the way of converging to target value, To NH₃Flow and N₂Flow is adjusted.Every measurement NH₃Calculatings in 10 minutes of partial pressure nitrogenize gesture K_N, according to converging to target value Mode, to NH₃Flow and N₂Flow is adjusted.

[table 2]

Underscore refers to outside for the scope of the present invention.

^*Target in the foot present invention with thumb down.

※ is the CO for being added to 3% with volume basis in atmosphere₂The gas soft nitriding of gas is handled.

[measurement of compound layer thickness and void area rate]

Mirror ultrafinish is carried out to the section in the direction vertical with length direction of gas nitriding treated small roller bearing to go forward side by side Etching is gone.Using scanning electron microscope (Scanning Electron Microscope:SEM) to the section of etching into Row observation, has carried out the confirmation of the presence or absence of the measurement of compound layer thickness and the gap of surface section.Etching is with 3% nitric acid ethyl alcohol Solution has carried out 20~30 seconds.

Compound layer, which can be used as, is present in the uncorroded layer of white on surface layer to confirm.From the tissue shot with 4000 times 10 visual field (visual field areas: 6.6 × 10 of photo²μm²) in compound layer is observed, determine at 3 points to every 10 μm respectively The thickness of compound layer.Also, measured 30 points of average value is defined as compound thickness (μm).

Similarly, 2 values are carried out by image processing application program and has found out gap from most surface to 3 μm of depth 90 μm of the area of range²In the ratio between the shared gross area (void area rate, unit are " % ").Then, by measured 10 The average value of visual field is defined as void area rate (%).Compound layer be lower than 3 μm in the case where, similarly will from surface to Measure object is used as until 3 μm of depth.

[measurement of γ ' phase ratio]

Chemical combination has been found out by electron backscatter diffraction method (Electron BackScatter Diffraction:EBSD) γ ' phase ratio in nitride layer.To 150 μm of area until slave most surface to 5 μm of depth of compound layer²EBSD measurement is carried out, Production differentiates the analysis diagram of γ ' phase, ε phase, parses image for obtained EBSD, is determined using image processing application program γ ' phase ratio (%).In EBSD measurement, 10 visual fields are determined with 4000 times of multiplying power.

Then, the γ ' of measured the 10 visual fields average value compared is defined as γ ' phase ratio (%).In compound In the case that layer is less than 5 μm, the γ ' phase ratio in the region of this part of compound layer thickness has been calculated.

[compound layer residual stress]

For the small roller bearing contact portion after nitridation, using small portion's X-ray residual stress measurement device, in the condition of table 3 Under determine the residual stress σ of γ ' phase, ε phase and mother layer (matrix)_γ’、σ_ε、σ_m.In turn, γ ' phase, ε phase are found out by EBSD And mother layer is in 90 μm of area from most surface to 3 μm of depth bounds²In shared area ratio V_γ’、V_ε、V_m, use the area ratio V_γ’、V_ε、V_mResidual stress σ is found out by following formula_c, by residual stress σ_cIt is set as the residual stress on surface.

σ_c=V_γ’σ_γ’+V_εσ_ε+V_mσ_m

[table 3]

[detorsion]

Static buckling test is implemented to the square test film handled for gas nitriding.Static buckling test is by interior Come what is carried out, rate of straining is set as 2mm/ points for 4 points of bendings that side distance between the fulcrum is 30mm, outside distance between the fulcrum is 80mm Clock.Deformeter is installed in the portion R of square test film length direction, having found out becomes nothing in the generation cracking of the portion R, the measurement of deformeter Maximum strain amount (%) when method carries out is used as detorsion.

It is 1.2% or more as target using detorsion in component of the present invention.

[rotary bending fatigue intensity]

Small wild formula rotary bending fatigue test is implemented to the cylinder test film handled for gas nitriding.Revolving speed is set as 3000rpm, test cut-off number are set as indicating the 1 × 10 of the fatigue limit of general steel⁷It is secondary, it will be tried in rotary bending fatigue It tests and is not produced fracture in piece and reached 1 × 10⁷Secondary maximum stress is set as the tired pole of rotary bending fatigue test piece Limit.

In component of the present invention, maximum stress when using fatigue limit is 520MPa or more as target.

[test result]

It shows the result in table 2.The ingredient of the steel of test number 1~23 and the condition of gas nitriding processing are of the invention In range, compound thickness is 3~15 μm, and γ ' the layer ratio of compound layer is 50% or more, and compound layer void area rate is low In 10%, the compressive residual stress of compound layer reaches 500MPa or more.As a result, having obtained detorsion is 1.2% Above, rotary bending fatigue intensity is 520MPa or more result good in this way.

The nitriding temperature of test number 26 is excessively high, as a result, the γ ' phase ratio of compound layer is low, void area rate is big, Residual stress becomes tensile stress, and rotary bending fatigue intensity is lower.

Test number 27 since nitriding temperature is too low, do not form compound layer, the residual stress on surface is also lower, so Rotary bending fatigue intensity is lower.

Test number 28 is since nitridation time is too long, void area rate becomes larger, the residual stress on surface is released along with this It puts and is lower, so rotary bending fatigue intensity is lower.

Test number 29 is since nitridation time is too short, cannot get sufficient compound layer thickness, the residual stress on surface becomes Low, case depth also shoals, so as starting point being broken using mother layer in early days.

Test number 30 is since the lower limit of nitridation gesture is low, cannot get sufficient compound layer thickness, the residual stress on surface It is lower, so rotary bending fatigue intensity is lower.

Test number 31 is since the lower limit of nitridation gesture is too low, is lower without generating the residual stress of compound layer, surface, institute It is lower with rotary bending fatigue intensity.

The upper limit for height of the nitridation gesture of test number 32, void area rate increase, detorsion, rotary bending fatigue intensity It is lower.

Test number 33 is since the upper limit of nitridation gesture is excessively high, compound layer thickness thickens, γ ' phase ratio is low, void area Rate increases, so detorsion, rotary bending fatigue intensity are lower.

Test number 34 is lower due to handling for tufftride, on surface almost without generation γ ' phase, residual stress, so Detorsion, rotary bending fatigue intensity are lower.

Test number 35 is since the C amount of steel is excessively high, compound layer thickness thickens, so detorsion, rotoflector are tired Labor intensity is lower.

Test number 36 is since the C amount of steel is too low, does not obtain sufficient core strength, so as starting point using mother layer It is broken in early days.

Test number 37 is since the Si amount of steel is excessively high, hardness of base material becomes excessively high, so detorsion is lower.

Test number 38 is since the Mn amount of steel is too low, does not obtain sufficient hardened layer hardness, core hardness, so with mother Layer is broken as starting point in early days.

Test number 39 is since P, S amount of steel are excessively high, the generation of P cyrystal boundary segregation and coarse MnS, so as to cause in morning Phase is broken.

Test number 40 is since the Cr amount of steel is too low, does not obtain sufficient diffusion layer hardness, core hardness, so with mother Layer is broken as starting point in early days.

The Al amount of the steel of test number 41 is excessively high, generates oxide system field trash, as starting point is sent out using mother layer in early stage Fracture is given birth to.

Test number 42 is since C amount, the Mn amount of steel are low, Cr amount is high, so the hardness of base material is got higher, detorsion, rotation Turn bending fatigue strength to be lower.

More than, embodiments of the present invention are illustrated.However, above-mentioned embodiment is merely used for implementing Illustration of the invention.It therefore, can within the scope of its spirit will be upper the present invention is not limited to above-mentioned embodiment The embodiment stated suitably changes and implements.

Claims

1. a kind of nitrogen treatment component, which is characterized in that it is the component using following steel as raw material, and the steel are with matter Amount % meter contains:

C:0.20%~0.60%,

Si:0.05%~1.5%,

Mn:0.2%~2.5%,

P:0.025% or less,

S:0.003%~0.05%,

Cr:0.05%~0.50%,

Al:0.01%~0.05%,

N:0.003%~0.025%,

Nb:0%~0.1%,

B:0%~0.01%,

Mo:0% more than or lower than 0.50%,

V:0% more than or lower than 0.50%,

Cu:0% more than or lower than 0.50%,

Ni:0% more than or lower than 0.50% and

Ti:0% more than or lower than 0.05%,

Remainder be Fe and impurity,

Wherein, the component have be formed in steel surface containing iron, nitrogen and carbon with a thickness of 3 μm more than or lower than 15 μm Compound layer,

Phase structure in the compound layer of range until from surface to 5 μm of depth contains 50% or more in terms of the area ratio γ ' phase,

Void area rate is lower than 10% in the range of until from surface to 3 μm of depth,

The compressive residual stress on compound layer surface is 500MPa or more.