Soft nitrided induction hardened steel part

Abstract

A soft nitrided induction hardened steel part which is excellent in bearing fatigue strength comprised of a predetermined chemical composition wherein a dissolved N concentration from the surface to 0.2 mm depth is 0.05 to 1.50%, a Vicker's hardness from the surface to 0.2 mm depth after tempering at 300 C. is HV 600 or more, and t/r0.35 when an effective hardened layer depth t is 0.5 mm or more and a radius of a breakage risk site or half of the thickness is r (mm).

Claims

1. A soft nitrided induction hardened steel part comprising: a base material with a chemical composition consisting of, by mass %, C: 0.30 to 0.80%, Si: 0.02 to 2.5%, Mn: 0.35 to 2.0%, Al: 0.001 to 2.0%, Cr: 0.01 to 3.0%, S: 0.040% or less, N: 0.0030 to 0.02%, O: 0.005% or less P: 0.025% or less, Nb: 0.3% or less, Ti: 0.3% or less, V: 1.0% or less, Ni: 3.0% or less, Cu: 3.0% or less, Co: 3.0% or less, Mo: 1.0% or less, W: 0.5% or less, B: 0.005% or less, Ca: 0.01% or less, Mg: 0.01% or less, Zr: 0.05% or less, Te: 0.1% or less, Pb: 0.5% or less, REM: 0.005% or less, and a balance of Fe and impurities, wherein a concentration of dissolved N from the surface of the steel part to 0.2 mm depth is 0.05 to 1.50%, a Vicker's hardness from the surface to 0.2 mm depth after tempering at 300 C. is HV 600 or more, and an effective hardened layer depth t is 0.5 mm or more, a radius of a breakage risk site or half of a thickness is r in mm, and t/r0.35.

2. The soft nitrided induction hardened steel part according to claim 1, wherein the base material consists of one or more of, by mass %, Nb: 0.005 to 0.3%, Ti: 0.005 to 0.3%, V: 0.01 to 1.0%, Ni: 0.01 to 3.0%, Cu: 0.01 to 3.0%, Co: 0.01 to 3.0%, Mo: 0.01 to 1.0%, W: 0.03 to 0.5%, B: 0.0006 to 0.005%, Ca: 0.0005 to 0.01%, Mg: 0.0005 to 0.01%, Zr: 0.0005 to 0.05%, Te: 0.0005 to 0.1%, Pb: 0.0005 to 0.5% and REM: 0.0005 to 0.005%.

Description

BRIEF DESCRIPTION OF DRAWINGS

(1) FIG. 1 is a schematic view which explains a breakage risk site.

DESCRIPTION OF EMBODIMENTS

(2) The inventors etc. investigated the effects on the temper softening resistance of the surface layer and the compressive residual stress in the vicinity of the surface and as a result learned that by raising the dissolved N concentration of the surface layer and controlling the effective hardened layer depth to become shallower, the bearing fatigue strength becomes excellent.

(3) First, the reasons for definition of the chemical composition of the base material of the present invention will be explained. Here, the % in the chemical composition expresses mass %.

(4) C: 0.30 to 0.80%

(5) C is an element which is important for obtaining the strength of the steel. In particular, it is necessary for reducing the ferrite fraction of the structure before induction hardening and for quickly making the surface layer of the steel an austenite single phase in the case of high frequency heating so as to improve the hardenability at the time of induction hardening. If the content of C is less than 0.30%, the ferrite fraction will be high and induction hardening will not be enough for causing sufficient hardening. If the content of C is over 0.80%, the machineability and forgeability at the time of fabrication of the steel part will be remarkably impaired and, furthermore, the possibility of occurrence of quenching cracks at the time of induction hardening will become greater. Therefore, the content of C was made 0.30 to 0.80%. The content of C is preferably 0.40 to 0.60%.

(6) Si: 0.02 to 2.5%

(7) Si has the effect of improving the temper softening resistance of the surface layer and thereby improving the bearing fatigue strength. To obtain this effect, the content of Si has to be made 0.02% or more. If the content of Si is over 2.5%, the decarburization at the time of forging becomes remarkable. Therefore, the content of Si was made 0.02 to 2.5%. The content of Si is preferably 0.20 to 0.80%.

(8) Mn: 0.35 to 2.0%

(9) Mn is an element which improves the hardenability and raises the temper softening resistance of the surface layer so as to improve the bearing fatigue strength. Further, it is effective for reducing the ferrite fraction of the structure before induction hardening and improving the hardenability at the time of induction hardening. To obtain this effect, the content of Mn has to be made 0.35% or more. If the content of Mn is over 2.0%, the steel material becomes too hard at the time of manufacture which obstructs cutting of the steel bars. Furthermore, Mn easily segregates between the dendrites at the solidification stage at the time of steelmaking causing local hardening and sometimes making the steel material brittle. Therefore, the content of Mn was made 0.35 to 2.0%. The content of Mn is preferably 0.50 to 1.5%.

(10) Al: 0.001 to 2.0%

(11) Al is an element which forms nitrides at the time of soft nitridation, makes the total N concentration of the surface layer increase, and makes the dissolved N concentration of the surface layer increase due to part or all of the nitrides dissolving at the time of induction hardening. Further, even if undissolved nitrides are present at the time of induction hardening, they disperse in the steel, so have the effect of effectively working to refine the austenite structure at the time of induction hardening treatment. Further, it is an element which is also effective for improving the machineability. For this reason, the content of Al has to be made 0.001% or more. If the content of Al is over 2.0%, the precipitates coarsen and make the steel brittle. Therefore, the content of Al was made 0.001 to 2.0%. The content of Al is preferably 0.020 to 0.10%.

(12) Cr: 0.01 to 3.0%

(13) Cr is an element which has an effect similar to Al. That is, Cr is an element which forms nitrides at the time of soft nitridation, makes the total N concentration of the surface layer increase, and makes the dissolved N concentration of the surface layer increase by part or all of the nitrides dissolving at the time of induction hardening. Further, even if nitrides are present which do not dissolve at the time of induction hardening, they disperse in the steel, so have the effect of effectively acting to refine the austenite structure at the time of induction hardening treatment. To obtain this effect, the content of Cr has to be made 0.01% or more. If the content of Cr exceeds 3.0%, the machineability deteriorates. Therefore, the Cr content was made 0.01 to 3.0%. The Cr content is preferably 0.05% to less than 1.0%.

(14) S: 0.040% or less

(15) S is an impurity element. Further, if deliberately included, it is an element which is effective for improvement of the machineability. If the content of S is over 0.040%, the forgeability remarkably declines. Therefore, the content of S was made 0.040% or less. The content of S is preferably 0.001 to 0.015%.

(16) N: 0.003 to 0.02%

(17) N forms various nitrides and works effectively to prevent coarsening of the austenite structure of the core part. To obtain this effect, the content of N has to be made 0.003% or more. If the content of N is over 0.02%, the Al, Cr, and other alloy elements which originally have the actions of making the total N concentration increase at the time of soft nitridation form coarse nitrides at the time of solidification. The coarse nitrides do not dissolve at the time of induction hardening, so the actual dissolved N concentration after induction hardening becomes lower. Therefore, the content of N was made 0.003 to 0.02%. The content of N is preferably 0.004 to less than 0.012%.

(18) O (oxygen) and P are impurities, but have to be particularly restricted in the present invention.

(19) O: 0.005% or less

(20) O is present in the steel as Al.sub.2O.sub.3, SiO.sub.2, and other oxide-based inclusions, but if O is large in amount, the oxides become large in size. These become starting points for fracture of the power transmission parts. For this reason, the content of O has to be restricted to 0.005% or less. The smaller the content of O, the better, so 0.002% or less is preferable. Furthermore, if aiming at longer lifetime, 0.0015% or less is preferable.

(21) P: 0.025% or less

(22) P segregates at the grain boundaries to cause the toughness to fall, so has to be reduced as much as possible. It is restricted to 0.025% or less.

(23) The balance of the base material is Fe and impurities. The impurities mean elements which enter from the raw materials of the steel and the manufacturing environment.

(24) Next, the reasons for definition of the chemical ingredients which can be optionally included will be explained.

(25) Steel Material-Reinforcing Elements

(26) Nb: 0.3% or less

(27) Nb is an element which has an effect similar to Al. That is, Nb is an element which forms nitrides at the time of soft nitridation, makes the total N concentration of the surface layer increase, and makes the dissolved N concentration of the surface layer increase by part or all of the nitrides dissolving at the time of induction hardening. Further, even if nitrides are present which do not dissolve at the time of induction hardening, they disperse in the steel, so have the effect of effectively acting to refine the austenite structure at the time of induction hardening treatment. Further, this is an element which is effective for improving the machineability. However, even if over 0.3% is included, the effect becomes saturated and the economicalness is impaired. Therefore, the content of Nb when including it was made 3.0% or less. To stably obtain the above effect, the content of Nb is preferably made 0.005% or more.

(28) Ti: 0.3% or less

(29) Ti is an element which has an effect similar to Al. That is, Ti is an element which forms nitrides at the time of soft nitridation, makes the total N concentration of the surface layer increase, and makes the dissolved N concentration of the surface layer increase by part or all of the nitrides dissolving at the time of induction hardening. Further, even if nitrides are present which do not dissolve at the time of induction hardening, they disperse in the steel, so have the effect of effectively acting to refine the austenite structure at the time of induction hardening treatment. However, if the content of Ti is over 0.3%, the precipitate coarsens and the steel is made brittle. Therefore, the content of Ti when including it was made 3.0% or less. To stably obtain the above effect, the content of Ti is preferably made 0.005% or more.

(30) V: 1.0% or less

(31) V is an element which has an effect similar to Al. That is, V is an element which forms nitrides at the time of soft nitridation, makes the total N concentration of the surface layer increase, and makes the dissolved N concentration of the surface layer increase by part or all of the nitrides dissolving at the time of induction hardening. Further, even if nitrides are present which do not dissolve at the time of induction hardening, they disperse in the steel, so have the effect of effectively acting to refine the austenite structure at the time of induction hardening treatment. However, even if over 1.0% is included, the effect becomes saturated and the economicalness is impaired. Therefore, the content of V when including it was made 1.0% or less. To stably obtain the above effect, the content of V is preferably made 0.01% or more.

(32) W: 0.5% or less

(33) W is an element which has an effect similar to Al. That is, W is an element which forms nitrides at the time of soft nitridation, makes the total N concentration of the surface layer increase, and makes the dissolved N concentration of the surface layer increase by part or all of the nitrides dissolving at the time of induction hardening. Further, even if nitrides are present which do not dissolve at the time of induction hardening, they disperse in the steel, so have the effect of effectively acting to refine the austenite structure at the time of induction hardening treatment. Further, W lowers the ferrite fraction of the structure before induction hardening and improves the hardenability at the time of induction hardening. If the content of W is over 0.5%, the machineability deteriorates. Furthermore, the effect becomes saturated and the economicalness is impaired. Therefore, the content of W when including it was made 0.5% or less. To stably obtain the above effect, the content of W is preferably made 0.03% or more.

(34) Hardenability-Improving Elements

(35) Ni: 3.0% or less

(36) Ni raises the hardenability and further improves the toughness. If the content of Ni exceeds 3.0%, the machineability deteriorates. Therefore, the content of Ni when including it was made 3.0% or less. To stably obtain the above effect, the content of Ni is preferably made 0.01% or more.

(37) Cu: 3.0% or less

(38) Cu reinforces the ferrite and is also effective for improving the hardenability and improving the corrosion resistance. Even if over 3.0% is included, the effect becomes saturated in terms of the mechanical properties. Therefore, the content of Cu when including it was made 3.0% or less. To stably obtain the above effect, the content of Cu is preferably made 0.01% or more. Cu causes a drop in the hot ductility and easily becomes a cause of defects at the time of rolling, so inclusion simultaneously with Ni is preferable.

(39) Co: 3.0% or less

(40) Co contributes to improvement of the hardenability. Even if over 3.0%, the effect becomes saturated. Therefore, the content of Co when including it was made 3.0% or less. To stably obtain the above effect, the content of Co is preferably made 0.01% or more.

(41) Mo: 1.0% or less

(42) Mo improves the temper softening resistance of the surface layer, so in addition to the effect of improving the bearing fatigue strength, also has the effect of making the hardened layer stronger and tougher and improving the bending fatigue strength. Even if over 1.0% is included, the effect becomes saturated and the economicalness is impaired. Therefore, the content of Mb when including it was made 1.0% or less. To stably obtain the above effect, the content of Mo is preferably made 0.01% or more.

(43) B: 0.005% or less

(44) B contributes to improvement of the hardenability. Even if over 0.005%, its effect becomes saturated. Therefore, the content of B when including it was made 0.005% or less. To stably obtain the above effect, the content of B is preferably made 0.0006% or more.

(45) Machineability-Improving Elements

(46) When machineability is also sought when fabricating the parts, one or more elements which are selected from Ca, Mg, Zr, Te, Pb, and a REM are included.

(47) Ca: 0.01% or less, Mg: 0.01% or less, Zr: 0.05% or less, Te: 0.1% or less, Pb: 0.5% or less, and REM: 0.005% or less

(48) These elements suppress the flattening of MnS and are present in the form of brittle phases so improve the machineability. To give these effects, at least one element which is selected from Ca: 0.01% or less, Mg: 0.01% or less, Zr: 0.05% or less, Te: 0.1% or less, Pb: 0.5% or less, and REM: 0.005% or less is included. A REM is a rare earth metal. Even if an element is included in over the upper limit value, its effect becomes saturated and the economicalness is impaired. Therefore, the contents of Ca, Mg, Zr, Te, Pb, and REM when including them were made respectively 0.01% or less, 0.01% or less, 0.05% or less, 0.1% or less, 0.5% or less, and 0.005% or less. To stably obtain the above effect, the contents of Ca, Mg, Zr, Te, Pb, and REM when including them are preferably made 0.0005% or more.

(49) Next, the dissolved N concentration from the surface down to a 0.2 mm depth and the Vicker's hardness from the surface down to a 0.2 mm depth after tempering at 300 C. will be explained. Below, the dissolved N concentration from the surface down to a 0.2 mm depth will be referred to as the dissolved N concentration of the surface layer. Further, the Vicker's hardness from the surface down to a 0.2 mm depth after tempering at 300 C. will be referred to as the tempered hardness of the surface layer at 300 C..

(50) The dissolved N concentration of the surface layer is the value of the total amount of N in the steel minus the amounts of N which are contained in the AlN, NbN, TiN, VN, and other nitrides. The amount of dissolved N of the surface layer is obtained by using the inert gas melting-heat conductivity method to measure the total N amount, using the SPEED method of the constant potential electrolytic corrosion method using a nonaqueous solvent electrolyte and a 0.1 m filter to electrolytically extract the residue, and using the indophenol light absorption method to measure the amount of N in the nitride then using the following formula (2) for calculation:
(Amount of dissolved N)=(Total amount of N)(Amount of N in nitrides)(2)

(51) To measure the region from the surface down to 0.2 mm depth, as the measurement sample, a cutting scrap when cutting down to 0.2 mm is used. However, to keep down the effect of a temperature rise due to the heat generated at the time of cutting, it is necessary that the cutting scrap not exhibit a temper color.

(52) The inventors changed the soft nitridation conditions, induction hardening conditions, and chemical composition of the steel material, changed the dissolved N concentration of the surface layer after induction hardening, and investigated the tempered hardness of the surface layer at 300 C. after tempering at 300 C. for 60 minutes. As a result, it was confirmed that with a dissolved N concentration of the surface layer of 0.05% to 1.5% in range, the higher the dissolved N concentration of the surface layer, the more the tempered hardness of the surface layer at 300 C. is improved.

(53) The N which is dissolved in the martensite, in the same way as C, is present in the crystals as substituted type dissolved atoms, so contributes to solution strengthening and dislocation strengthening and improves the strength. If tempering at 300 C., the dissolved C precipitates as carbides and the dissolved C concentration in the martensite falls so the strength of the steel falls. On the other hand, N maintains a dissolved state, so even if the steel is tempered at 300 C., the steel will maintain a high strength. For this reason, compared with a part which is treated by only carburized quenching or only induction hardening, a part which is treated by soft nitridation and induction hardening has a higher 300 C. tempered hardness.

(54) If the dissolved N concentration of the surface layer is less than 0.05%, the improvement in the tempered hardness of the surface layer at 300 C. is small and the bearing fatigue strength is low. To obtain a sufficiently high tempered hardness of the surface layer at 300 C., 0.10% or more is preferable. If the dissolved N concentration of the surface layer is over 1.5%, the martensite transformation start temperature at the time of cooling falls and the residual austenite after induction hardening becomes higher. As a result, due to the increase in the dissolved N concentration of the surface layer, the hardness falls more than the hardness of the surface layer after quenching and the tempered hardness of the surface layer at 300 C. are improved. For this reason, conversely the bearing fatigue strength falls.

(55) The 300 C. tempered hardness of the surface layer is made 600 or more because if the depth at which the tempered hardness of the surface layer at 300 C. becomes 600 or more is shallower than 0.2 mm from the surface, the steel part cannot withstand the bearing pressure which is applied and cracks under fatigue.

(56) Next, the effective hardened layer depth will be explained.

(57) The effective hardened layer depth t is prescribed by the JIS G0559. In a steel part of the present invention, the effective hardened layer depth t is 0.5 mm or more and the following formula [1] is satisfied.
t/r0.35[1]
where t: effective hardened layer depth (mm), r: radius of breakage risk site or half of thickness (mm)

(58) The r of the radius of the breakage risk site or half of the thickness is an indicator which is used for comparing the effective hardened layer depth and size of a part. A breakage risk site is a risk cross-section in design. In a columnar like part such as a shaft, r is the radius of the minimum diameter part or the cross-sectional part where the stress concentration becomes the maximum (case where cross-section is circular) or half of the thickness (case where cross-section is rectangular). In a gear part, the part which is shown by the arrow in FIG. 1 is the breakage risk site (fatigue fracture site) 1, while 2r is the thickness 2.

(59) By making the ratio of the region which transforms to austenite at the time of high frequency heating, that is, the ratio of the effective hardened layer depth to the size of the part, smaller, it is possible to make the compressive residual stress in the vicinity of the surface increase and to reduce the quenching strain.

(60) If the effective hardened layer becomes deeper, not only does the compressive residual stress in the vicinity of the surface fall, but also quenching cracks are caused, so the upper limit of formula [1] is made 0.35. For example, in a large roller test piece which is used in a roller pitting fatigue test, when making the effective hardened layer depth 40 mm for a radius 65 mm, quenching cracks are caused at the surface at the time of induction hardening. To make the compressive residual stress in the vicinity of the surface higher, 0.3 or less is preferable.

(61) The reason for setting the lower limit of formula [1] is not dependent on the size of the part. Accordingly, the lower limit is not made the lower limit of formula [1], but is set by making the effective hardened layer depth 0.5 mm or more. If the effective hardened layer depth becomes shallower, a high shear stress is generated at the core part as well, a fissure is formed between the hardened layer and the core part, and the fissure grows causing spalling. The effective hardened layer depth, viewed from safety, is preferably made 0.75 mm or more.

(62) The soft nitridation treatment temperature is made 500 C. or more, since the lower the temperature, the longer the treatment time. On the other hand, if the soft nitridation treatment temperature exceeds the A.sub.1 point, the heat treatment strain will become greater, so the temperature is made less than the A.sub.1 point of the steel material.

(63) The cooling after the soft nitridation treatment may be performed by any method of natural cooling, air-cooling, gas cooling, oil cooling, etc.

(64) As the soft nitridation treatment, a method of N penetration in any surroundings of a gas atmosphere, salt bath, or electrical field may be applied. Note that not only soft nitridation treatment, but also nitridation treatment (treatment causing penetration of N without accompanying penetration of C), and oxynitridation treatment (nitridation treatment+oxidation treatment) may also be applied.

(65) The heating method when applying induction hardening has to be determined while considering the dissolved N concentration of the surface layer. The high frequency heating temperature where a dissolved N concentration of the surface layer of 0.05 to 1.5% can be realized is 950 C. or more. The higher the high frequency heating temperature, the more the dissolved N concentration of the surface layer increases, but if the temperature is made too high, the crystal grains will coarsen and strain will cause the parts precision to fall, so the high frequency heating temperature is made 1200 C. or less. The more preferable high frequency heating temperature is 950 to 1050 C., more preferably 960 to 980 C.

(66) If the frequency of the high frequency heating is too low, thee targeted heating temperature and the hardened layer depth and effective hardened layer depth cannot both be achieved. If the frequency is too high, realization industrially becomes difficult due to the hardware performance. The frequency of the high frequency heating is made 100 to 300 kHz.

(67) The effective hardened layer depth depends on the size of the part. If the effective hardened layer depth is 0.5 mm or more and is suitably adjusted to satisfy formula [1], mainly the heating time is adjusted. For example, in the case of a radius 13 mm of a small roller which is used for a roller pitting fatigue test, if the frequency is made 200 kHz and the high frequency heating temperature is made 950 C., when the heating time is 25 seconds, the effective hardened layer depth will exceed 4.55 mm. This is off from formula [1], so the time is made 20 seconds or less. On the other hand, under the same conditions, if the heating time falls under 0.7 second, the effective hardened layer depth becomes 0.5 mm or less, so the time is made 0.7 second or more.

(68) After the induction hardening, shot peening or other mechanical surface hardening treatment may be performed.

(69) The soft nitridation, high frequency heating, and quenching may be performed a plurality of times.

EXAMPLES

(70) Next, examples of the present invention will be explained. The conditions of the examples are illustrations which are employed for confirming the workability and advantageous effects of the present invention. The present invention is not limited to these illustrations. The present invention can employ various conditions so long as not departing from the gist of the present invention and so long as achieving the object of the present invention.

(71) A steel material having each chemical composition which is shown in Table 1 was heated to 1250 C., then hot forged and allowed to cool to room temperature, then was again heated and was annealed at 850 C. for 1 hour. After that, it was machined to fabricate pieces for a roller pitting fatigue test consisting of a small roller test piece which has a cylindrical part with a diameter of 26 mm and a width of 28 mm and a large roller test piece with a diameter of 130 mm and a width of 18 mm. Furthermore, a diameter 26 mm, length 100 mm hardness and residual stress measurement test piece was fabricated.

(72) TABLE-US-00001 TABLE 1 Chemical composition Example Class C Si Mn P S Cr Al N O Nb TI V 1 Inv. ex. 0.55 0.25 1.00 0.013 0.020 0.13 0.010 0.0051 0.004 2 Inv. ex. 0.57 2.21 0.38 0.010 0.015 0.05 0.031 0.0062 0.001 3 Inv. ex. 0.75 0.20 0.40 0.019 0.002 0.03 0.050 0.0055 0.001 4 Inv. ex. 0.33 0.26 0.51 0.012 0.005 2.51 0.033 0.0052 0.002 5 Inv. ex. 0.52 0.05 1.95 0.011 0.007 0.20 0.032 0.0032 0.001 6 Inv. ex. 0.50 0.51 0.75 0.009 0.021 0.15 0.035 0.0195 0.001 0.032 7 Inv. ex. 0.57 0.23 0.82 0.012 0.024 0.71 0.003 0.0047 0.001 0.035 8 Inv. ex. 0.53 0.24 0.81 0.020 0.004 0.23 1.490 0.0049 0.001 0.05 9 Inv. ex. 0.54 0.75 0.70 0.016 0.001 0.15 0.025 0.0046 0.002 10 Inv. ex. 0.56 0.26 0.75 0.013 0.002 0.56 0.030 0.0051 0.001 11 Inv. ex. 0.54 0.24 0.73 0.005 0.013 1.21 0.035 0.0045 0.001 12 Inv. ex. 0.55 0.25 0.76 0.023 0.014 0.11 0.034 0.0052 0.001 13 Inv. ex. 0.56 0.23 0.82 0.016 0.017 0.21 0.032 0.0058 0.001 14 Inv. ex. 0.53 0.26 0.76 0.015 0.015 0.15 0.033 0.0056 0.001 15 Inv. ex. 0.52 0.23 0.80 0.011 0.009 0.18 0.032 0.0055 0.001 16 Inv. ex. 0.55 0.22 0.86 0.022 0.001 0.20 0.035 0.0054 0.001 17 Inv. ex. 0.56 0.25 0.86 0.019 0.003 0.14 0.036 0.0051 0.001 18 Inv. ex. 0.57 0.26 0.78 0.013 0.015 0.16 0.032 0.0053 0.001 19 Inv. ex. 0.53 0.20 0.77 0.014 0.002 0.13 0.030 0.0050 0.001 20 Inv. ex. 0.54 0.24 0.81 0.012 0.012 0.15 0.035 0.0055 0.001 21 Inv. ex. 0.55 0.23 0.79 0.009 0.013 1.15 0.031 0.0057 0.001 0.121 22 Inv. ex. 0.55 0.26 0.80 0.024 0.016 0.13 0.033 0.0053 0.001 0.11 23 Inv. ex. 0.54 0.24 0.82 0.014 0.014 0.15 0.033 0.0046 0.001 0.103 24 Inv. ex. 0.53 0.25 0.83 0.013 0.018 0.16 0.035 0.0052 0.001 25 Inv. ex. 0.42 0.26 0.81 0.017 0.016 0.12 0.032 0.0047 0.001 0.51 26 Comp. ex. 0.55 0.25 1.00 0.013 0.020 0.13 0.010 0.0051 0.004 27 Comp. ex. 0.33 0.26 0.51 0.012 0.005 2.51 0.033 0.0052 0.002 28 Comp. ex. 0.55 0.25 1.00 0.013 0.020 0.13 0.010 0.0051 0.004 29 Comp. ex. 0.75 0.20 0.40 0.019 0.002 0.03 0.050 0.0055 0.001 30 Comp. ex. 0.52 0.05 1.95 0.011 0.007 0.20 0.032 0.0032 0.001 31 Comp. ex. 0.52 0.05 1.95 0.011 0.007 0.20 0.032 0.0032 0.001 32 Comp. ex. 0.21 0.23 0.72 0.011 0.012 0.85 0.027 0.0052 0.002 33 Comp. ex. 0.75 0.20 0.40 0.019 0.002 0.03 0.050 0.0055 0.001 Chemical composition Example Ni Cu Co Mo W B Ca Mg Zr Te Pb REM 1 2 3 4 5 6 7 8 9 1.01 10 0.30 11 0.05 12 0.16 13 0.10 14 0.0020 15 0.0025 16 0.0014 17 0.0016 18 0.0650 19 0.11 20 0.0010 21 0.0030 22 0.05 23 0.0007 24 0.75 0.0006 25 0.51 0.0006 26 27 28 29 30 31 32 33

(73) The small rollers and large rollers were, except for Examples 30 and 31, treated by soft nitridation treatment and induction hardening. The soft nitridation treatment consisted of holding the rollers in a soft nitridation atmosphere at 600 C. for a predetermined time, then cooling them by N.sub.2 gas. The composition of the gas which was used for the soft nitridation treatment was N.sub.2(0.45 Nm.sup.3/h)+NH.sub.3(0.5 Nm.sup.3/h)+CO.sub.2(0.05 Nm.sup.3/h), while the soft nitridation time was 2 hours in Examples 1 to 25, 28, 29, and 32 to 34, 0.5 hour in Example 26, and 5 hours in Example 27. After the soft nitridation treatment, induction hardening was performed under the conditions which are shown in Table 2. For the coolant at the time of induction hardening, tapwater or a polymer quenching agent was used. After that, the rollers were tempered at 150 C. for 60 minutes and used for fatigue tests.

(74) In Example 30, soft nitridation treatment was not performed. Only induction hardening was performed. Further, in Example 31, only soft nitridation treatment was performed under the above conditions (soft nitridation time: 2 hours). Induction hardening was not performed.

(75) The fabricated large rollers and small rollers were used for a standard bearing fatigue test of a roller pitting fatigue test. In the roller pitting fatigue test, a large roller was pushed against a small roller by a bearing pressure of a Hertzian stress of 3500 MPa, the peripheral speed directions at the contact parts were made the same directions, and the slip rate was made 40% (peripheral speed of contact parts 40% larger at large roller than small roller) for rotation. The temperature of the gear oil which was supplied to the contact part was made 80 C. The lifetime was made the number of rotations of the small roller until pitting occurred at the small roller. The occurrence of pitting was detected by making the two rollers stop rotation when a vibration meter attached to the tester detected vibration and visually confirming the existence of pitting. Further, the cutoff point in the test was made 10,000,000 cycles (10.sup.7 cycles).

(76) The residual stress measurement test pieces were subjected to soft nitridation treatment and induction hardening and tempering under the same conditions for the small rollers and large rollers. The N concentration was measured using the above method. The material was electrolytically polished down to 0.01 mm depth, then X-rays were used to measure the residual stress at the 0.01 mm depth. Further, the residual stress measurement test pieces were used for tempering treatment at 300 C. for 60 minutes, were cut to obtain cross-sections, then were measured for hardness profiles from the surfaces to the core parts by a wicker's hardness meter at 0.1 mm pitch.

(77) As shown in Table 2, Examples 1 to 25 all had lifetimes in the roller pitting fatigue test of 10,000,000 cycles (10.sup.7 cycles) or more and gave good results of having excellent bearing fatigue strength (high fatigue test lifetime).

(78) For example, Example 1 had a dissolved N concentration of the surface layer of 0.20% and a compressive residual stress in the vicinity of the surface of 433 MPa, so was excellent in the tempered hardness of the surface layer at 300 C. and exhibited a high compressive residual stress in the vicinity of the surface, therefore in a roller pitting fatigue test, the lifetime was 10,000,000 cycles or more and a good bearing fatigue strength was obtained.

(79) TABLE-US-00002 TABLE 2 Soft High frequency nitridation heating After induction hardening Total N conditions Surface to 0.2 mm position Effective concentration Tem- Dissolved N 300 C. hardened from surface Fre- pera- concen- Residual tempered layer Fatigue test to 0.2 mm quency ture Time tration stress hardness depth life Example Class position (%) (kHz) ( C.) (s) (%) (MPa) (Hv) (mm) t/r (cycles) 1 Inv. ex. 0.21 150 960 2.5 0.20 433 1.50 0.12 627 10,000,000 cycle durability 2 Inv. ex. 1.20 150 950 15.0 1.18 528 4.42 0.34 850 10,000,000 cycle durability 3 Inv. ex. 0.09 150 960 1.5 0.06 465 0.81 0.06 606 10,000,000 cycle durability 4 Inv. ex. 1.12 150 1050 5.1 0.68 452 3.82 0.29 722 10,000,000 cycle durability 5 Inv. ex. 0.31 100 970 2.5 0.29 436 1.79 0.14 645 10,000,000 cycle durability 6 Inv. ex. 0.24 150 970 2.4 0.22 434 1.42 0.11 626 10,000,000 cycle durability 7 Inv. ex. 0.23 150 970 2.5 0.21 435 1.51 0.12 630 10,000,000 cycle durability 8 Inv. ex. 0.92 150 970 2.1 0.14 430 1.29 0.10 640 10,000,000 cycle durability 9 Inv. ex. 0.22 150 970 2.3 0.21 431 1.56 0.12 627 10,000,000 cycle durability 10 Inv. ex. 0.18 100 970 1.9 0.16 435 1.31 0.10 618 10,000,000 cycle durability 11 Inv. ex. 0.25 150 970 0.5 0.22 510 0.55 0.04 630 10,000,000 cycle durability 12 Inv. ex. 0.15 150 970 2.7 0.13 427 1.41 0.11 610 10,000,000 cycle durability 13 Inv. ex. 0.29 150 970 2.4 0.27 444 1.45 0.11 643 10,000,000 cycle durability 14 Inv. ex. 0.14 150 970 2.6 0.12 419 1.60 0.12 607 10,000,000 cycle durability 15 Inv. ex. 0.11 150 970 1.8 0.09 417 1.52 0.12 600 10,000,000 cycle durability 16 Inv. ex. 0.19 150 970 2.3 0.17 433 1.38 0.11 619 10,000,000 cycle durability 17 Inv. ex. 0.17 150 970 2.4 0.15 430 1.42 0.11 615 10,000,000 cycle durability 18 Inv. ex. 0.15 150 970 2.5 0.13 425 1.53 0.12 611 10,000,000 cycle durability 19 Inv. ex. 0.11 150 970 2.3 0.09 420 1.45 0.11 600 10,000,000 cycle durability 20 Inv. ex. 0.13 150 970 2.3 0.11 421 1.52 0.12 605 10,000,000 cycle durability 21 Inv. ex. 0.30 150 970 2.3 0.20 436 1.40 0.11 626 10,000,000 cycle durability 22 Inv. ex. 0.18 150 970 2.4 0.13 426 1.45 0.11 610 10,000,000 cycle durability 23 Inv. ex. 0.21 150 970 2.1 0.18 435 1.32 0.10 620 10,000,000 cycle durability 24 Inv. ex. 0.15 150 970 2.5 0.13 421 1.56 0.12 609 10,000,000 cycle durability 25 Inv. ex. 0.28 150 970 2.0 0.12 420 1.32 0.10 614 10,000,000 cycle durability 26 Comp. ex. 0.03 150 970 2.5 0.01 356 1.60 0.12 552 5,100,000 cycle durability 27 Comp. ex. 2.11 150 970 3.0 1.55 50 1.81 0.14 369 300,000 cycle durability 28 Comp. ex. 0.19 40 970 17.0 0.18 +5 8.20 0.63 622 5,500,000 cycle durability 29 Comp. ex. 0.11 150 970 0.3 0.08 620 0.28 0.02 610 80,000 cycle durability 30 Comp. ex. 150 970 2.3 0.00 336 1.51 0.12 538 2,100,000 cycle durability 31 Comp. ex. 0.30 0.00 10 0.05 0.00 245 30,000 cycle durability 32 Comp. ex. 0.15 150 970 2.3 0.14 235 1.44 0.11 370 900,000 cycle durability 33 Comp. ex. 0.09 150 940 3.2 0.03 351 1.62 0.12 578 8,900,000 cycle durability

(80) Examples 26 and 27 are examples where the dissolved N concentration of the surface layer after induction hardening is off from the present invention. Example 26 has the same steel material as in Example 1, but the soft nitridation treatment is shorter in time. For this reason, the dissolved N concentration of the surface layer fails to reach 0.05%, the tempered hardness of the surface layer at 300 C. is a low value of less than HV 600, and the lifetime is short. Example 27 has the same steel material as in Example 4, but the soft nitridation treatment is longer in time. For this reason, the dissolved N concentration of the surface layer exceeded 1.5% and residual austenite was present in a large quantity, so the tempered hardness of the surface layer at 300 C. was low and, furthermore, the change in volume at the time of quenching was small, so the compressive residual stress in the vicinity of the surface fell, so the lifetime was short.

(81) Examples 28 and 29 respectively have a t/r after induction hardening and an effective hardened layer depth t outside the range of the present invention. In each case, the fatigue test life failed to reach 10 million cycles. Example 28 had a low frequency of high frequency heating and a long heating time. For this reason, while the steel material was the same as Example 1, for the shape of the test piece, the effective hardened layer depth was shallow, the compressive residual stress in the vicinity of the surface fell, and the lifetime was short. Example 29 had a short high frequency heating time. For this reason, while the steel material was the same as Example 1, the effective hardened layer depth was shallow, spalling occurred, and the lifetime was short.

(82) Example 30 is an example where a steel material of the same chemical composition as Example 5 is subjected to only induction hardening. There was almost no dissolved N of the surface layer, the tempered hardness of the surface layer at 300 C. and the compressive residual stress in the vicinity of the surface fell, and the lifetime was short.

(83) Example 31 is an example where a steel material of the same chemical composition as Example 5 is subjected to only soft nitridation treatment and is not subjected to induction hardening. The tempered hardness of the surface layer at 300 C. was low and the lifetime was short.

(84) Example 32 is an example where the concentration of C is lower than the range of the present invention and sufficient hardness could not be obtained after induction hardening. For this reason, the dissolved N concentration of the surface layer and the t/r were in the range of the present invention, but the lifetime was short.

(85) Example 33 is an example where a steel material of the same chemical composition as Example 3 is subjected to heat treatment changed in conditions of induction hardening. The high frequency heating temperature was low and the dissolved N concentration became low, so the tempered hardness of the surface layer at 300 C. was low and the lifetime was short.

REFERENCE SIGNS LIST

(86) 1. breakage risk site (fatigue fracture site) 2. thickness (2r)