Steel for surface hardening for machine structural use and part for machine structural use

Abstract

The present invention is steel for surface hardening for machine structural use which contains, by mass %, C: 0.3 to 0.6%, Si: 0.02 to 2.0%, Mn: 0.35 to less than 1.5%, and Al: 0.01 to 0.5%, is restricted to B: less than 0.0003%, S: 0.0001 to 0.021%, N: 0.003 to 0.0055%, P: 0.0001 to 0.03%, and O: 0.0001 to 0.0050%, has a ratio Mn/S of Mn and S satisfying 70 to 30,000, has a balance of Fe and unavoidable impurities, and, when nitrided, then induction hardened, has a surface hardenability of a Vicker's hardness when tempered at 300° C. of 650 or more.

Claims

1. A steel part for machine structural use, said steel part being nitrided, then induction hardened at less than 900° C. and tempered at 300° C., wherein the steel part has a steel composition that comprises, in mass %, C: 0.3 to 0.6%, Si: 0.02 to 2.0%, Mn: 0.35 to less than 1.5%, and Al: 0.01 to 0.5%, is restricted to B: less than 0.0002%, S: 0.0001 to 0.021%, N: 0.003 to 0.0055%, P: 0.0001 to 0.03%, and O: 0.0001 to 0.0050%, and one or more of W: 0.0025 to 0.5%, Cr: 0.2 to 2.0%, Mo: 0.05 to 1.0%, V: 0.05 to 1.0%, Nb: 0.005 to 0.3%, Ti: 0.005 to 0.2%, Ni: 0.05 to 2.0%, Cu: 0.01 to 2.0%, Ca: 0.0005 to 0.01%, Mg: 0.0005 to 0.01%, Zr: 0.0005 to 0.05%, Te: 0.0005 to 0.1%, and a balance of Fe and unavoidable impurities, wherein a ratio Mn/S is 70 to 30,000, and said steel part has a core of non-nitrided steel and a hardened nitrided layer on a surface of the steel part, wherein said steel part has holes having an equivalent circle diameter of 0.1 to 1 μm down to a depth of at least 5 μm from a surface of said hardened nitrided layer present on a scale of 5,133 to 47,635/mm.sup.2; and wherein the hardened nitrided layer has a Vicker's hardness of 650 or more and a thickness of 0.2 mm or more at its surface.

Description

BRIEF DESCRIPTION OF DRAWINGS

(1) FIG. 1 is a view showing an example of comparison of the cross-sectional hardness distributions of steel materials from the surfaces to the core directions for a steel material as soft nitrided and a steel material which is soft nitrided, then induction hardened.

(2) FIG. 2 gives views showing the structure of a hardened nitrided layer observed by an optical microscope and scan type electron microscope. FIG. 2A shows the structure which is observed by an optical microscope, while FIG. 2B shows the structure which is observed by a scan type electron microscope.

(3) FIG. 3 is a view showing the relationship between the Mn/S at the time of soft nitriding and the compound thickness.

(4) FIG. 4 is a view showing the relationship between the concentration of N at a depth of 0.2 mm from the surface of the steel after induction hardening and the Vicker's hardness (Hv) at the time of tempering at 300° C.

DESCRIPTION OF EMBODIMENTS

(5) The present invention treats a steel material, to which suitable amounts of Si, Mn, and Al have been added, by soft nitriding, then induction hardening to form a deep hardened nitrided layer with a high concentration of N, and improve the surface hardness and softening resistance to thereby obtain a high surface fatigue strength not only at ordinary temperature of course, but also at a 300° C. or so high temperature.

(6) First, the reasons for limitation of the necessary added elements in present invention will be explained. Note that, the % of the chemical composition show the mass %.

(7) C: 0.3 to 0.6%

(8) C is an important element for obtaining the strength of the steel. In particular, it is an element which is necessary for reducing the ferrite fraction of the micro structure before induction hardening, improving the hardenability at the time of induction hardening, and increasing the hardened layer depth. If the amount of addition of C is less than 0.3%, the ferrite fraction is high and the hardening at the time of induction hardening becomes insufficient, so the lower limit of the amount of addition of C was made 0.3%. On the other hand, if the amount of addition of C is excessive, the machineability and forgeability at the time of part fabrication are remarkably impaired and, furthermore, the possibility of cracks occurring at the time of induction hardening becomes greater, so the upper limit of the amount of addition of C was made 0.6%.

(9) Si: 0.02 to 2.0%

(10) Si has the effect of increasing the softening resistance of the hardened layer so as to improve the surface fatigue strength. To obtain that effect, the amount of addition of Si has to be at least 0.02%. On the other hand, if the amount of addition of Si is over 2.0%, the decarburization at the time of forging becomes remarkable, so 2.0% was made the upper limit.

(11) Mn: 0.35 to less than 1.5%

(12) Mn is an element effective for improving the hardenability and increasing the softening resistance to improve the surface fatigue strength. Furthermore, it has the effects of immobilizing the S in the steel as MnS so as to prevent S from concentrating at the steel material surface and N from invading the steel and of promoting the formation of a thick compound layer by soft nitriding. To immobilize the S in the steel as MnS to render it harmless, it is necessary to make Mn/S≧70. Further, it lowers the ferrite fraction of the structure before induction hardening and improves the hardenability at the time of induction hardening. To obtain that effect, Mn has to be added in 0.35% or more. If adding a suitable amount of Mn, the hardenability at the time of induction hardening is improved, so the hardness of the steel material after hardening rises and the surface fatigue strength is improved. However, if adding Mn in 1.5% or more, the hardness of the material rises more than necessary, the machineability of the material before soft nitriding is remarkably degraded, and the productivity is degraded. For this reason, the amount of addition of Mn is made less than 1.5%.

(13) Mn/S: 70 to 30000

(14) As explained above, to prevent the concentration of S at the steel material surface, it is necessary to add Mn to S by a certain ratio or more and render the S harmless by MnS. If the ratio Mn/S of the amounts of addition of Mn and S is 70 or more, the effect of rendering the S harmless is remarkably improved. However, if Mn/S is less than 70, S concentrates at the steel material surface and formation of a compound layer at the time of soft nitriding is inhibited, so Mn/S was made 70 or more.

(15) FIG. 3 is a view showing the relationship between the Mn/S at the time of soft nitriding under the conditions explained later and the compound thickness. As clear from FIG. 3, by making Mn/S 70 or more, after the soft nitriding, a 10 μm or more thickness compound layer is obtained. On the other hand, even if Mn/S exceeds 30000, the effect of rendering the S harmless becomes saturated, so the upper limit of Mn/S was made 30000.

(16) Al: 0.01 to 0.5%

(17) Al is an element which precipitates and diffuses in the steel as Al nitrides and thereby effectively acts to increase the grain fineness of the austenite structure at the time of induction hardening and, furthermore, improves the hardenability and increases the hardened layer depth. Further, it is an element which is effective for improvement of the machineability. Therefore, the amount of addition of Al has to be 0.01% or more. Further, it is an element which has the effect of bonding with N at the time of soft nitriding and raising the concentration of N near the surface layer of the steel material and is also effective for improving the surface fatigue strength. Therefore, the amount of addition of Al has to be made 0.01% or more. On the other hand, if the amount of addition of Al exceeds 0.5%, the precipitates (Al nitrides) will coarsen and cause the steel to become brittle, so the upper limit was made 0.5%.

(18) B: less than 0.0003%

(19) B is unavoidably included in steel. Even so, by restricting the content of B to less than 0.0003%, it does not detract from the advantageous effect of the present invention.

(20) B: 0.0003 to 0.005%

(21) If B is added into the steel, the N and B in the steel bond to form BN in the steel, but at the time of induction heating, the BN is decomposed and releases the B. This greatly improves the hardenability and improves the surface fatigue strength. To obtain that effect, the amount of addition of B has to be made 0.0003% or more. On the other hand, even if the amount of addition of B is over 0.005%, that effect becomes saturated. Furthermore, it becomes a cause of cracking at the time of rolling and forging, so 0.005% was made the upper limit. Note that, BN is formed during heat treatment with a slow cooling speed and during cooling in cold working with a normally slow cooling speed. Therefore, at the time of machining performed after cold working and before soft nitriding and induction hardening, BN improves the machineability. After machining, induction hardening causes the BN to break up resulting in a hardened nitrided layer. That hardened nitrided layer improves the surface fatigue strength. Therefore, this is perfect for production of a part for machine structural use where high surface fatigue strength is demanded.

(22) S: 0.0001 to 0.021%

(23) S has the effect of improving the machineability. However, S is a soft nitriding inhibiting element which concentrates at the steel material surface to thereby obstruct the entry of N to the steel material at the time of soft nitriding. If the amount of addition of S exceeds 0.021%, the entry of N into the steel material is remarkably inhibited and, furthermore, the forgeability is remarkably degraded. Therefore, to improve the machineability, when including S, it is necessary to make the content 0.021% or less. On the other hand, the industrial lower limit of the amount of addition of S was made 0.0001%. Note that, as explained above, to immobilize the S in the steel as MnS and eliminate its inhibitory effect on soft nitriding, the lower limit of Mn/S is made 70. On the other hand, even if Mn/S exceeds 30,000, the effect of eliminating the inhibitory effect on soft nitriding becomes saturated, so the upper limit of Mn/S has to be made 30,000.

(24) N: 0.003 to 0.0055%

(25) N forms various types of nitrides and is effective for increasing the grain fineness of the austenite structure at the time of induction hardening. To obtain that effect, it is necessary to make the amount of addition of N 0.003% or more. On the other hand, if excessive N is added, the hardness rises. Furthermore, the N and Al bond to form AlN, whereby the amount of solid solution Al effective for improvement of the machineability is reduced, so the machineability is degraded. Further, the excessively added N causes the ductility in the high temperature region to drop. Furthermore, it forms coarse AlN or coarse BN, so makes the material remarkably brittle resulting in cracks at the time of rolling and forging. Therefore, the amount of addition of N has to be limited to 0.0055% or less.

(26) P: 0.0001 to 0.03%

(27) P segregates at the grain boundaries and causes the toughness to drop, so is preferably reduced as much as possible. It has to be limited to 0.03% or less. The lower limit of the amount of addition of P is made the industrial limit of 0.0001%.

(28) O: 0.0001 to 0.0050%

(29) O is present in the steel as Al.sub.2O.sub.3, SiO.sub.2, and other oxide-based inclusions, but if the amount of O is great, such oxides become large in size. Such enlarged oxides form starting points for breakage of power transmission parts, so the content of O has to be limited to 0.0050% or less. The smaller the content of O, the better, so 0.0020% or less is more preferable. In the case of power transmission parts aiming at long service lifetime, 0.0015% or less is further preferable. Note that the lower limit of the content of 0 is made the industrial limit of 0.0001%.

(30) Next, the reasons for restriction of the optionally added elements will be explained.

(31) Elements for Strengthening Steel Material

(32) W: 0.0025 to 0.5%

(33) W is an element which improves the hardenability and thereby improves the surface fatigue strength. However, due to the addition of W, the hardness of the steel material rises and the machineability deteriorates, so there is a limit to the addition of W. To improve the hardenability so as to achieve a great improvement in the surface fatigue strength, the amount of addition of W is preferably made 0.0025% or more. More preferably, it is made 0.03% or more. On the other hand, if the amount of addition of W exceeds 0.5%, that effect becomes saturated and the economy is impaired, so 0.5% was made the upper limit.

(34) Cr: 0.2 to 2.0%

(35) Cr has the effect, by addition, of improving the nitriding characteristics and the softening resistance of the hardened layer and of improving the surface pressure fatigue strength. To obtain that effect, the amount of addition of Cr is preferably made 0.2% or more. On the other hand, if the amount of addition of Cr exceeds 2.0%, the machineability deteriorates, so the upper limit of the amount of addition of Cr is preferably made 2.0%.

(36) Mo: 0.05 to 1.0%

(37) Mo, by addition, has the effect of improving the softening resistance of the hardened layer and improving the surface fatigue strength plus the effect of strengthening and toughening the hardened layer to improve the bending fatigue strength. To obtain these effects, the amount of addition of Mo is preferably made 0.05% or more. On the other hand, even if the amount of addition of Mo exceeds 1.0%, these effects are saturated and economy is impaired, so the upper limit of the amount of addition of Mo is preferably made 1.0%.

(38) V: 0.05 to 1.0%

(39) V, by addition, precipitates and diffuses as nitrides in the steel and is effective for increasing the grain fineness of the austenite structure at the time of induction hardening. To obtain that effect, the amount of addition of V has to be made 0.05% or more. On the other hand, even if the amount of addition of V exceeds 1.0%, that effect becomes saturated and economy is impaired, so the upper limit of the amount of addition of V is preferably made 1.0%.

(40) Nb: 0.005 to 0.3%

(41) Nb, by addition, precipitates and diffuses as nitrides in the steel and is effective for increasing the grain fineness of the austenite structure at the time of induction hardening. To obtain that effect, the amount of addition of Nb is preferably 0.005% or more. On the other hand, even if the amount of addition of Nb exceeds 0.3%, that effect becomes saturated and economy is impaired, so the upper limit of the amount of addition of Nb is preferably made 0.3%.

(42) Ti: 0.005 to 0.2%

(43) Ti, by addition, precipitates and diffuses as nitrides in the steel and is effective for increasing the grain fineness of the austenite structure at the time of induction hardening. To obtain that effect, the amount of addition of Ti is preferably 0.0005% or more. On the other hand, if the amount of addition of Ti exceeds 0.2%, the precipitates (Ti nitrides) coarsen and cause the steel to become brittle, so the upper limit of the amount of addition of Ti is preferably made 0.2%.

(44) Ni: 0.05 to 2.0%

(45) Ni, by addition, has the effect of further improving the toughness. To obtain that effect, it is preferable to make the amount of addition of Ni 0.05% or more. On the other hand, if the amount of addition of Ni exceeds 2.0%, the machineability deteriorates, so the upper limit of the amount of addition of Ni is preferably made 2.0%.

(46) Cu: 0.01 to 2.0%

(47) Cu is effective for strengthening the ferrite and improving the hardenability and corrosion resistance. If the amount of addition of Cu is less than 0.01%, that effect cannot be observed, so the amount of addition of Cu is preferably made 0.01% or more. On the other hand, even if the amount of addition of Cu exceeds 2.0%, the effect of improvement of the mechanical properties due to improvement of the hardenability becomes saturated, so the upper limit of the amount of addition of Cu is preferably made 2.0%. Note that, if adding Cu, the hot rollability is lowered and defects are easily caused at the time of rolling, so Cu is preferably added simultaneously with Ni.

(48) Elements for Improving Bending Strength

(49) When improvement of the bending fatigue strength of the part for machine structural use is sought, one or more of the following contents of Ca, Mg, Zr, and Te may be added in the following ranges.

(50) Ca: 0.0005 to 0.01%, Mg: 0.0005 to 0.01%, Zr: 0.0005 to 0.05%, Te: 0.0005 to 0.1%

(51) Ca, Mg, Zr, and Te are all elements which suppress the flattening of MnS present in the steel, improve the bending fatigue strength more, and make bending fatigue fracture of the gears and fatigue fracture of the spline bottoms of shaft parts more difficult. The effect of suppression of flattening of MnS is obtained by adding Ca in 0.0005% or more, Mg in 0.0005% or more, Zr in 0.0005% or more, and Te in 0.0005% or more. Therefore, it is preferable to make Ca: 0.0005%, Mg: 0.0005%, Zr: 0.0005%, and Te: 0.0005% the lower limits of the amounts of addition. On the other hand, even if adding Ca in more than 0.01%, Mg in more than 0.01%, Zr in more than 0.05%, and Te in more than 0.1%, the effect of suppression of flattening of MnS becomes saturated and the economy is impaired. Therefore, it is preferable to make Ca: 0.01%, Mg: 0.01%, Zr: 0.05%, and Te: 0.1% the upper limits of the amounts of addition.

(52) Further, in addition to the elements prescribed above, it is possible to include Pb, Bi, Sn, Zn, Rem, and Sb in ranges not impairing the advantageous effects of the present invention.

(53) Next, the thickness and hardness of the hardened nitrided layer at the surface layer of the steel part will be explained.

(54) The steel part of the present invention is a steel part which is treated by soft nitriding, then induction hardening to form a hardened nitrided layer. The surface hardenability of steel after forming the hardened nitrided layer has to be a Vicker's hardness of 650 or more when tempered at 300° C. If the Vicker's hardness is less than 650 when tempered at 300° C., the softening resistance is not sufficiently increased and, as a result, cracks occur and surface fatigue fracture occurs at the operating surfaces (steel part surfaces) which become high in temperature (around 300° C.).

(55) Further, the range of a Vicker's hardness of 650 or more when tempered at 300° C. is preferably down to a depth of 0.2 mm from the surface of the steel. If the range of a Vicker's hardness of 650 or more when tempered at 300° C. is shallower than 0.2 mm from the surface of the steel, the steel part cannot withstand the surface pressure which is applied. In particular, it cannot withstand the surface pressure which is applied at a 300° C. or so high temperature. The steel part therefore fractures by fatigue.

(56) Further, the thickness of the hardened nitrided layer is preferably 0.4 mm or more. If the thickness of the hardened nitrided layer is less than 0.4 mm, when the steel part is subjected to a high surface pressure, surface cracks are formed. Before these surface cracks form starting points for fracture, internal fracture occurs due to spalling and therefore the fatigue life of the steel part becomes shorter.

(57) In the actual steel part, whether the steel part is one which is soft nitrided, then induction hardened can be judged from the distribution of microstructures which are observed by an optical microscope after Nital corrosion of a sample taken from the steel part and the distribution of hardness from the surface to the core.

(58) To form a hardened nitrided layer and obtain a high surface fatigue strength, it is necessary to perform soft nitriding to form a compound layer (a layer mainly comprised of Fe.sub.3N, Fe.sub.4N, and other Fe nitrides) at the surfacemost layer of the steel. The Fe nitrides in the compound layer are decomposed by the induction heating performed after the soft nitriding whereby a sufficient amount of N is made to diffuse into the steel and a hardened nitrided layer is formed. That is, it is necessary to perform soft nitriding to form a compound layer serving as the source of supply of N for forming a hardened nitrided layer. Further, the hardened nitrided layer which is obtained by soft nitriding, then induction hardening exhibits a high N concentration.

(59) To make a sufficient amount of N diffuse in the steel and thickly form a hardened nitrided layer which is hard and can improve the softening resistance, in particular the hardened softening resistance, it is preferable to make the thickness of the compound layer after soft nitriding 10 μm or more.

(60) Further, the soft nitriding temperature is preferably made 500 to 600° C. in range. If the soft nitriding temperature is over 600° C., it is not possible to make the compound layer 10 μm or more. Furthermore, the concentration of N in the compound layer also becomes lower. Further, if the soft nitriding temperature exceeds 600° C., heat deformation, grain boundary oxidation, etc. of the steel material occur. On the other hand, if the soft nitriding temperature is less than 500° C., the penetration of N into the steel material remarkably falls, so the lower limit of the soft nitriding temperature is preferably made 500° C.

(61) If lengthening the soft nitriding time, the compound layer and nitrided layer depth become larger, but that effect becomes saturated in about 3 hours, so the soft nitriding time is preferably 1 to 3 hours.

(62) The cooling after the soft nitriding may be performed by any of the methods of air cooling, N.sub.2 gas cooling, oil cooling, etc.

(63) Further, as the soft nitriding, either of gas soft nitriding or salt bath soft nitriding may be applied.

(64) Note that, so long as a method by which the steel material surface is supplied with nitrogen and the surfacemost layer of the steel material is formed with a 10 μm or more compound layer, not only soft nitriding, but also nitriding (meaning a surface hardening method treating the surface by only NH.sub.3 for a long period of time and industrially differentiated from soft nitriding which uses a mixed atmosphere of NH.sub.3 and CO.sub.2 (in some cases, a mixed atmosphere further having N.sub.2 mixed in) to enable treatment in a short period of 1 to 3 hours) may be applied.

(65) In the present invention, soft nitriding is more preferable than nitriding in the point that the surfacemost layer of the steel can be formed with a 10 μm or more compound layer in a short time, but the invention is not limited to soft nitriding.

(66) Further, to break up the compound layer which is formed by soft nitriding on the surfacemost layer of the steel material and cause N to diffuse from that surfacemost layer to the inside of the steel material and thereby obtain a high surface hardenability of a Vicker's hardness of 650 or more when tempered at 300° C., it is necessary, after the soft nitriding, to treat the steel material by induction hardening which heats the material by induction heating to convert it to austenite for hardening and form a hardened nitrided layer.

(67) The heating method which performing the induction hardening has to consider the breakup of the compound layer which is formed by the soft nitriding. The induction heated temperature is made the austenite transformation point to less than 900° C. Further, the holding time is made 0.05 to 5 seconds. Note that, the “holding time” means the time for holding the temperature of the steel material in the range of the austenite transformation point to less than 900° C. from the point of time where the temperature of the induction heated steel material reaches the austenite transformation point.

(68) FIG. 4 is a view showing the relationship between the concentration of N at a depth of 0.2 mm from the surface of the steel after induction hardening and the Vicker's hardness (Hv) at the time of tempering at 300° C.

(69) As clear from FIG. 4, when the Vicker's hardness after 300° C. tempering at a depth of 0.2 mm from the surface of the steel is 650 or more, the concentration of N at a depth of 0.2 mm from the surface of the steel was 0.5% or more.

(70) Further, if the temperature of the induction heating is 900° C. or more, N will unnecessarily diffuse to the inside, the concentration of N at a depth of 0.2 mm from the surface will not become 0.5% or more, the Vicker's hardness when tempered at 300° C. will become less than 650, and, as a result, the surface fatigue strength will not be able to be improved. Further, if the temperature of the induction heating is 900° C. or more, the increase in the oxide layer at the steel material surface will cause degradation of the mechanical properties.

(71) On the other hand, if the temperature of the induction heating is less than the austenite transformation point, the steel material will not transform to martensite, so it is not possible to obtain a high surface hardness.

(72) If the holding time is less than 0.05 second, the breakup of the compound layer and the diffusion of the N produced by the decomposition of the compound layer will become insufficient. On the other hand, if the holding time is over 5 seconds, N will unnecessarily diffuse to the inside, the concentration of N at a depth of 0.2 mm from the surface will not become 0.5% or more, the Vicker's hardness when tempered at 300° C. will become less than 650, and, as a result, the surface fatigue strength will not be able to be improved.

(73) The frequency when performing induction heating is preferably, for a small part, around 400 kHz and, for a large part, around 5 kHz.

(74) The coolant which is used for the hardening may be water, a polymer quenchant, or other water-based coolant with a large cooling ability.

(75) After induction hardening, it is preferable to perform low temperature tempering of around 150° C. in accordance with general carburized quenched parts so as to secure the toughness of the part.

(76) Next, the surface layer structure of the steel material and steel part of the present invention will be explained.

(77) The steel material and steel part of the present invention are soft nitrided, then induction hardened, so have 10,000 holes/mm.sup.2 or more holes of 0.1 to 1 μm in an equivalent circle diameter down to a depth of 5 μm or more from the surface.

(78) For example, in a member like a gear in which the surface fatigue due to rolling becomes a cause of fracture, the lubrication of the operating surface is important. If not sufficiently lubricated, the parts will contact each other resulting in seizing or sticking and surface fatigue fracture will occur. To form a sufficient lubricating film, it is effective to provide an oil reservoir at the operating surface so that a film of lubricant is continuously formed.

(79) The steel material and steel part of the present invention have, at the surfacemost layer of the steel material, a hardened nitrided layer which is obtained by using soft nitriding to form a compound layer mainly comprised of Fe.sub.3N, Fe.sub.4N, and other Fe nitrides, breaking up these Fe nitrides by induction heating, and transforming the steel to austenite for hardening. This hardened nitrided layer is formed by the Fe nitrides in the compound layer being decomposed and the N which is released diffusing to the inside of the steel material. In this process of formation, the locations where the Fe nitrides were present in the compound layer form a large number of dispersed holes. The hardened nitrided layer therefore becomes a hard porous layer. Further, these large number of dispersed holes function as an oil reservoir whereby the lubrication effect is improved and the steel material is further improved in wear resistance and durability.

(80) The holes are of a size of 0.1 to 1 μm in an equivalent circle diameter and a density of 10,000 holes/mm.sup.2 or more. Further, these holes function as an oil reservoir if present down to a depth of 5 μm or more from the surface. Such holes are obtained by controlling the conditions of the soft nitriding and induction heating.

(81) Even a compound layer as soft nitrided has a small number of holes, so these have the function as an oil reservoir, but the compound layer as soft nitrided is extremely brittle and cannot withstand a large surface pressure, so the steel material as soft nitrided invites surface fatigue fracture.

(82) If the size of the holes is a circle equivalent diameter of over 1 μm, the surface smoothness of the steel part will deteriorate and form the starting points for pitching and other surface fatigue fracture and the surface fatigue strength will be lowered. On the other hand, if the main dimension of the holes is an equivalent circle diameter of less than 0.1 μm, a sufficient function as an oil reservoir cannot be obtained.

(83) If the density of the holes is less than 10,000 holes/mm.sup.2, the holes will not effectively function as an oil reservoir.

(84) Further, gears and other sliding members are generally used until being worn down about 5 μm from the surface of the members, so the holes are preferably present down to a depth of 5 μm or more from the surface of the steel part.

(85) The size and density of the holes depend on the soft nitriding and induction heating conditions. To obtain the size and density of holes which effectively function as an oil reservoir, preferably the soft nitriding temperature is made 580° C. to less than 600° C., the induction heating temperature is made 880° C. to less than 900° C., and the holding time is made 1 to 4 seconds. Note that, these conditions of course satisfy the conditions for obtaining a hardened nitride layer provided at a steel material and steel part having a high surface fatigue strength.

(86) Further, the surface layer after hardening was made a martensite structure, while the core was left as a ferrite-pearlite structure. This is because by making only the surface layer transform to martensite, the surface layer is given compressive residual stress and the surface fatigue strength is improved. If transforming even the core part to martensite, the compressive residual stress of the surface layer ends up being reduced and the surface fatigue strength falls.

(87) Note that, what was explained above was just an illustration of an embodiment of the present invention. Various changes may be made within the scope of description of the claims.

EXAMPLES

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

(89) Each of the steel materials having the chemical compositions shown in Tables 1 to 2 and Tables 4 to 5 was forged and annealed, then fabricated into roller pitching test pieces for evaluation of the surface fatigue strength, that is, a small roller test piece having 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.

(90) The small roller test piece and large roller test piece were soft nitrided (nitrided for 2 hours at temperatures shown in Table 3 and Table 6, then cooled by N.sub.2 gas, nitriding gas composition: 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)), then induction hardened (frequency 100 kHz). The coolant used at the time of induction hardening was tapwater or a polymer quenchant. After that, the test pieces were tempered at 150° C. for 60 minutes and used for fatigue tests.

(91) The fabricated small roller test piece and large roller test piece were used for a standard surface fatigue test, that is, a roller pitching fatigue test.

(92) The roller pitching fatigue test was performed by having the small roller test piece pushed against by various hertz, stresses (surface pressures) by the large roller test piece and setting the slip rate at −40% (peripheral speed of large roller test piece being 40% larger than small roller test piece at contacting parts of the small roller test piece and the large roller test piece). Note that, the rotational direction and the contacting parts of the small roller test piece and the large roller test piece are made the same. Further, the temperature of the gear oil which was fed to the contacting parts of the small roller test piece and large roller test piece was made 90° C.

(93) The cutoff number of the test was made the 10 million cycles (10.sup.7 cycles) showing the fatigue limit of general steel, while the maximum hertz stress at which 10 million cycles was reached at the small roller test piece without the occurrence of pitching was made the fatigue limit of the small roller test piece. The occurrence of pitching was detected by a vibration meter attached to the tester. After detection of vibration, the rotations of both the small roller test piece and the large roller test piece were made to stop and the occurrence of pitching and rotational speed were confirmed.

(94) Further, for evaluation of the temper softening resistance, a cylindrical hardness measurement test piece of a diameter of 26 mm and a length of 100 mm was fabricated. The hardness measurement test piece was soft nitrided and induction hardened under the same conditions for the small roller test piece and large roller test piece. After that, this was tempered at 300° C. for 60 minutes, was cut cross-sectionally, then was measured for the hardness distribution from the surface to the core of the hardness measurement test piece by a Vicker's hardness meter. Note that, the surface layer of the hardness measurement test piece after induction hardening was a martensite structure, while the core part was left as a ferrite-pearlite structure. Further, together with this, the concentration of N at a depth of 0.2 mm from the surface of the hardness measurement test piece was measured by EPMA.

(95) Further, the density of the holes which have an equivalent circle diameter of 0.1 to 1 μm was found by cutting a hardness measurement test piece, which was soft nitrided and induction hardened under the same conditions as the small roller test piece and large roller test piece, at a cross-section perpendicular to rolling, burying this in resin, polishing it to a mirror finish, then image processing the surfacemost layer part. The image processing was performed at 3000× for 40 fields of 50 μm.sup.2 each. The number of holes found by image processing was converted to the number of holes per mm.sup.2.

(96) Furthermore, for evaluation of the machineability, a cylindrical test piece of a diameter of 45 mm and a length of 100 mm was fabricated. The machineability is evaluated in the state of the material before soft nitriding and induction hardening, so the test piece for evaluation of the machineability was used as is for forging and annealing. The machineability was evaluated by a deep hole drilling test using MQL (minimum quantity lubrication) by an NC machining center used for production of gears, crankshafts, and other auto parts. The number of holes drilled until drill breakage when drilling under the conditions shown in Table 7 was measured. However, when reaching 1000 or more holes, the machineability was judged to be good and the test was cut off.

(97) Table 3 and Table 6 show the results. As shown in Table 3, in each of the invention examples of Examples 1 to 40, the surface fatigue strength (maximum hertz stress) at 10 million cycles (10.sup.7 cycles) in a roller pitching fatigue test is a high value of 3700 MPa or more. It is clear that each has a superior surface fatigue strength. It was confirmed that it is possible to obtain good results compared with the comparative examples of Examples 41 to 62 shown in Table 6. Due to such superior surface fatigue strength, the steel material and steel part of the present invention and steel can be used for members upon which a high surface pressure is applied both at ordinary temperature of course and also at a high temperature of around 300° C.

(98) For example, each of the invention examples of Examples 1 to 8 is a steel to which Si, Mn, and Al are added in suitable amounts. Due to the formation of a compound layer of a thickness of 10 μm or more by soft nitriding of less than 600° C. and the 0.08 to 4.9 seconds of induction hardening after that at the austenite transformation point to 900° C., it could be confirmed that a Vicker's hardness of 650 or more after 300° C. tempering is obtained and, as a result, a superior surface fatigue strength is obtained. Further, in each of the invention examples of Examples 1 to 8, the thickness of the hardened nitrided layer is 0.4 mm or more. It could be confirmed that the concentration of N down to a position 0.2 mm from the surface is high. Further, from the number of holes drilled being 1000 or more, it could be confirmed that the machineability after forging (before soft nitriding and induction hardening) was also superior.

(99) Further, even in Examples 9 to 24 where optional elements were added, the surface fatigue strength (maximum hertz stress) at the 10,000 million cycle (10.sup.7 cycle) in a roller pitching fatigue strength is a high value of 0.3700 MPa or more. It could be confirmed that a good surface fatigue strength is obtained.

(100) Further, in each of the invention examples of Examples 25 to 40, there are 10,000 holes/mm.sup.2 or more holes of an equivalent circle diameter of 0.1 to 1 μm present down to a depth of 5 μm from the surface of the hardened nitrided layer, but the surface fatigue strength (maximum hertz stress) at the 10,000 million cycle (10.sup.7 cycle) in a roller pitching fatigue strength is a high value of 3700 MPa or more. It could be confirmed that a good surface fatigue strength is obtained.

(101) As opposed to this, in each of the comparative examples of Examples 41 to 62, where steels with chemical compositions outside the range of the present invention are soft nitrided, then induction hardened, the fatigue test lifetime was the value of the surface fatigue strength (maximum hertz stress) at a 10 million cycle (10.sup.7 cycle) lifetime of less than 3700 MPa. Compared with the invention examples, it could be confirmed that the surface fatigue strength was inferior.

(102) In the comparative example of Example 42, the amount of addition of B was over the upper limit of the present invention, while in the comparative example of Example 43, the amount of addition of N was over the upper limit, so each steel was remarkably brittle, cracks occurred during forging, and the steel could not be evaluated.

(103) In each of the comparative examples of Examples 44 and 48, the Mn/S is low, concentration of S at the steel material surface cannot be prevented, and, for this reason, the thickness of the compound layer after soft nitriding is thin, the Vicker's hardness after 300° C. tempering is less than 650, and, as a result, the surface fatigue strength (maximum hertz stress) is low. Further, the thickness of the hardened nitrided layer of the steel part after induction hardening is a thin one of less than 0.4 mm, while the concentration of N down to a depth of 0.2 mm from the surface is also low.

(104) The comparative example of Example 49 has a low Mn/S, so has a low thickness of the compound layer, and has a Vicker's hardness after 300° C. tempering of less than 650, so, as a result, it was confirmed, the surface fatigue strength (maximum hertz stress) is low.

(105) Each of the comparative examples of Examples 51 to 54 has a chemical composition within the range of the present invention, but has a Vicker's hardness of less than 650 after 300° C. tempering and, as a result, it was confirmed, has a maximum hertz stress of less than 3000 MPa. This is because, in each of Examples 51 to 54, while the compound layer after soft nitriding has a sufficient thickness, in Example 51, the induction heating temperature is too high, so the N unnecessarily diffuses to the inside of the steel material, while the thickness of the hardened nitrided layer is a sufficient 0.65 mm, the Vicker's hardness after 300° C. tempering is 506, or less than 650, and, furthermore, an oxide layer is formed at the steel material surface, so the surface fatigue strength (maximum hertz stress) is lowered. Further, the concentration of N at a depth of 0.2 mm from the surface of the steel material is also a low 0.09%. In Example 53, the holding time (induction heating time) is too long, so the N unnecessarily diffuses to the inside of the steel material, while the thickness of the hardened nitrided layer is a sufficient 0.70 mm, the Vicker's hardness after 300° C. tempering is 540, or less than 650, and, as a result, the surface fatigue strength (maximum hertz stress) is low. Further, the concentration of N at a depth of 0.2 mm from the surface of the steel material is also a low 0.20%.

(106) Each of the comparative examples of Examples 55 to 5 has a Vicker's hardness of less than 650 after 300° C. tempering and, as a result, it was confirmed the surface fatigue strength (maximum hertz stress) is less than 3000 MPa. This is because the compound layer after soft nitriding is thin, so the thickness of the hardened nitrided layer is also thin. For example, in Example 56, the chemical composition is within the range of the present invention, but the soft nitriding temperature is too low, so the compound layer is thin, the Vicker's hardness after 300° C. tempering is less than 650, and, as a result, the surface fatigue strength (maximum hertz stress) is low. Further, the thickness of the hardened nitrided layer is a thin 0.16 mm.

(107) The comparative example of Example 57 has an amount of addition of Mn smaller than the range of the present invention, has an amount of addition of S greater than the range of the present invention, has an Mn/S smaller than the range of the present invention, and has too high a soft nitriding temperature, so the compound layer is thin, the Vicker's hardness after 300° C. tempering is 387, or less than 650, and, as a result, it was confirmed, the surface fatigue strength (maximum hertz stress) is low. Further, the thickness of the hardened nitrided layer is a thin 0.15 mm, while the concentration of N at a depth of 0.2 mm from the surface of the steel material is a low 0.08%.

(108) Each of the comparative examples of Example 58 to 60 has a Vicker's hardness of less than 650 after 300° C. tempering and, as a result, has a low surface fatigue strength (maximum hertz stress). This is because each of Examples 58 to 60 has a thin compound layer and unsuitable induction heating conditions, so has a thin hardened nitrided layer. For example, Example 58 has an amount of addition of Mn lower than the range of the present invention and has an Mn/S smaller than the range of the present invention, so the compound layer is thin. Further, the induction heating temperature is high, so the Vicker's hardness after 300° C. tempering becomes 507, or less than 650, and, as a result, the surface fatigue strength (maximum hertz stress) is low. Further, the thickness of the hardened nitrided layer is a thin 0.14 mm, while the concentration of N at a depth of 0.2 mm from the surface of the steel material is a low 0.07%.

(109) The comparative example of Example 62 has an Mn/S of 15 or lower than the range of the present invention and has a high soft nitriding temperature, so the compound layer is thin, and has a high induction heating temperature, so has a Vicker's hardness of less than 650 after 300° C. tempering, as a result of which the surface fatigue strength (maximum hertz stress) is an extremely low 2600 MPa. Further, the thickness of the hardened nitrided layer is a thin 0.23 mm, while the concentration of N at a depth of 0.2 mm from the surface of the steel material is a low 0.16%.

(110) From the above, it could be confirmed that the invention examples, which are comprised of steel to which Si, Mn, and Al are added in suitable amounts and where Mn/S is made a suitable, range, which are soft nitriding, then are induction hardened, and which have surface hardenability of a Vicker's hardness of 650 or more when tempered at 300° C., exhibit a superior surface fatigue strength of a maximum hertz stress of 3700 MPa or more.

(111) TABLE-US-00001 TABLE 1 Chemical composition (mass %) Example Class C Si Mn P S Al O N B  1 Inv. ex. 0.32 0.61 0.66 0.014 0.006 0.120 0.002 0.0034 0.0004  1a Inv. ex. 0.55 0.19 0.81 0.020 0.008 0.030 0.001 0.0039 0.0001  1b Inv. ex. 0.53 0.19 0.79 0.025 0.010 0.022 0.002 0.0044 0.0002  2 Inv. ex. 0.37 0.59 1.15 0.022 0.008 0.035 0.001 0.0034 0.0005  3 Inv. ex. 0.49 0.45 1.16 0.009 0.009 0.069 0.004 0.0042 0.0010  4 Inv. ex. 0.51 1.20 1.40 0.025 0.016 0.153 0.002 0.0040 0.0006  5 Inv. ex. 0.54 0.25 0.80 0.019 0.007 0.126 0.003 0.0031 0.0015  6 Inv. ex. 0.55 0.85 0.96 0.012 0.010 0.159 0.001 0.0038 0.0023  7 Inv. ex. 0.55 1.32 1.23 0.021 0.014 0.080 0.002 0.0041 0.0004  8 Inv. ex. 0.59 0.85 0.72 0.021 0.006 0.099 0.004 0.0049 0.0038  9 Inv. ex. 0.54 1.30 0.85 0.017 0.009 0.025 0.002 0.0030 0.0004 10 Inv. ex. 0.46 0.85 0.79 0.023 0.009 0.021 0.003 0.0043 0.0009 11 Inv. ex. 0.44 0.69 1.07 0.015 0.010 0.192 0.001 0.0044 0.0008 12 Inv. ex. 0.41 1.41 1.44 0.014 0.011 0.102 0.001 0.0040 0.0017 13 Inv. ex. 0.51 0.79 0.85 0.022 0.012 0.110 0.001 0.0036 0.0005 14 Inv. ex. 0.55 0.34 1.12 0.015 0.008 0.099 0.001 0.0044 0.0009 15 Inv. ex. 0.45 0.91 0.67 0.020 0.009 0.089 0.001 0.0042 0.0006 16 Inv. ex. 0.45 0.75 1.29 0.021 0.018 0.021 0.003 0.0037 0.0005 17 Inv. ex. 0.35 0.40 0.50 0.020 0.005 0.089 0.004 0.0049 0.0005 18 Inv. ex. 0.46 0.54 0.71 0.020 0.007 0.021 0.002 0.0041 0.0005 19 Inv. ex. 0.45 1.41 0.53 0.010 0.007 0.087 0.005 0.0050 0.0021 20 Inv. ex. 0.51 0.29 0.85 0.023 0.007 0.045 0.004 0.0050 0.0005 21 Inv. ex. 0.50 1.67 0.56 0.021 0.004 0.089 0.004 0.0042 0.0004 22 Inv. ex. 0.49 0.55 0.83 0.013 0.010 0.310 0.004 0.0050 0.0029 23 Inv. ex. 0.48 1.00 1.20 0.024 0.010 0.110 0.004 0.0040 0.0008 24 Inv. ex. 0.45 0.89 1.32 0.011 0.011 0.109 0.002 0.0038 0.0010 25 Inv. ex. 0.40 0.25 0.55 0.010 0.005 0.082 0.001 0.0041 0.0006 26 Inv. ex. 0.45 1.43 0.69 0.011 0.009 0.096 0.001 0.0042 0.0015 27 Inv. ex. 0.48 0.59 1.00 0.020 0.009 0.085 0.002 0.0038 0.0029 28 Inv. ex. 0.51 1.00 0.85 0.018 0.007 0.101 0.003 0.0031 0.0006 29 Inv. ex. 0.55 1.56 0.75 0.013 0.008 0.123 0.002 0.0042 0.0005 30 Inv. ex. 0.56 1.90 0.84 0.020 0.006 0.030 0.003 0.0040 0.0005 31 Inv. ex. 0.43 0.25 0.43 0.017 0.003 0.193 0.003 0.0051 0.0033 32 Inv. ex. 0.50 0.95 0.75 0.020 0.005 0.102 0.003 0.0043 0.0006 33 Inv. ex. 0.48 0.72 1.02 0.013 0.007 0.110 0.003 0.0035 0.0010 34 Inv. ex. 0.41 0.81 0.75 0.013 0.009 0.099 0.002 0.0040 0.0004 35 Inv. ex. 0.45 0.31 0.83 0.020 0.011 0.123 0.001 0.0033 0.0004 36 Inv. ex. 0.53 0.51 1.01 0.011 0.013 0.025 0.002 0.0041 0.0009 37 Inv. ex. 0.57 0.46 1.07 0.015 0.015 0.243 0.002 0.0051 0.0022 38 Inv. ex. 0.50 0.66 1.13 0.010 0.011 0.034 0.002 0.0046 0.0007 39 Inv. ex. 0.45 1.01 0.83 0.018 0.010 0.025 0.003 0.0046 0.0010 40 Inv. ex. 0.42 0.26 0.58 0.016 0.006 0.027 0.002 0.0036 0.0004

(112) TABLE-US-00002 TABLE 2 (Continuation of Table 1) Chemical composition (mass %) Ex. Class Cr Mo W V Nb Ti Ni Cu Ca Mg Zr Te Mn/S  1 Inv. ex. 116  1a Inv. ex. 101  1b Inv. ex. 79  2 Inv. ex. 142  3 Inv. ex. 126  4 Inv. ex. 90  5 Inv. ex. 108  6 Inv. ex. 94  7 Inv. ex. 91  8 Inv. ex. 126  9 Inv. ex. 0.75 93 10 Inv. ex. 0.28 90 11 Inv. ex. 0.19 0.23 112 12 Inv. ex. 0.13 135 13 Inv. ex. 0.51 0.12 74 14 Inv. ex. 1.13 0.09 145 15 Inv. ex. 1.30 0.10 71 16 Inv. ex. 0.79 0.31 72 17 Inv. ex. 0.43 0.14 0.22 0.09 99 18 Inv. ex. 1.84 0.12 0.14 0.44 0.10 105 19 Inv. ex. 0.02 0.11 77 20 Inv. ex. 0.30 0.10 0.0011 0.0011 121 21 Inv. ex. 0.38 0.05 0.48 0.11 0.0044 148 22 Inv. ex. 1.63 0.69 0.25 0.12 0.14 0.009 82 23 Inv. ex. 0.79 0.35 0.11 0.13 0.0009 0.0008 122 24 Inv. ex. 0.78 0.09 0.11 0.15 0.06 0.07 0.24 0.08 0.0006 0.0006 0.0027 0.009 123 25 Inv. ex. 120 26 Inv. ex. 76 27 Inv. ex. 108 28 Inv. ex. 128 29 Inv. ex. 95 30 Inv. ex. 142 31 Inv. ex. 1.13 132 32 Inv. ex. 0.10 140 33 Inv. ex. 0.79 0.12 142 34 Inv. ex. 1.01 0.07 0.11 80 35 Inv. ex. 0.52 0.01 0.10 73 36 Inv. ex. 1.10 0.07 0.06 0.10 0.02 76 37 Inv. ex. 0.61 0.26 0.11 71 38 Inv. ex. 0.95 0.09 0.06 0.11 0.62 0.14 101 39 Inv. ex. 0.85 0.11 0.12 0.02 0.25 0.11 82 40 Inv. ex. 0.94 0.05 0.12 0.13 0.06 0.04 0.36 0.09 0.0005 0.0006 0.0026 0.010 91

(113) TABLE-US-00003 TABLE 3 After induction hardening Tempering at 300° C. Surface at depth fatigue Soft nitriding Induction Hardened of 0.2 mm strength Compound heating nitrided from Hole (maximum Machineability, layer conditions layer surface, density hertz no. of Temp. thickness Temp. Time thickness Vicker's (holes/ stress) Ex. Class holes (° C.) (μm) (° C.) (s) (mm) hardness mm.sup.2) (MPa)  1 Inv. ex. >1000 552 28 897 1.6 0.40 691 7435 3700  1a Inv. ex. >1000 575 24 899 4.9 0.40 720 8352 3700  1b Inv. ex. >1000 575 26 898 4.9 0.41 709 7257 3700  2 Inv. ex. >1000 582 30 877 2.5 0.42 705 7432 3700  3 Inv. ex. >1000 566 23 837 4.2 0.42 718 6614 3700  4 Inv. ex. >1000 575 21 894 2.9 0.41 691 5457 3700  5 Inv. ex. >1000 583 24 881 4.9 0.40 764 6684 3700  6 Inv. ex. >1000 577 23 832 4.4 0.41 819 6357 3700  7 Inv. ex. >1000 590 19 854 4.9 0.40 675 8532 3700  8 Inv. ex. >1000 553 21 893 2.4 0.42 894 8533 3700  9 Inv. ex. >1000 598 27 898 0.9 0.41 689 7607 3750 10 Inv. ex. >1000 552 20 861 0.08 0.42 709 8381 3750 11 Inv. ex. >1000 587 25 859 3.2 0.42 757 7006 3800 12 Inv. ex. >1000 588 22 801 2.4 0.40 759 8725 3750 13 Inv. ex. >1000 575 20 890 1.8 0.42 679 5469 3750 14 Inv. ex. >1000 582 26 882 0.9 0.41 728 5453 3750 15 Inv. ex. >1000 591 28 892 0.5 0.40 704 5737 3750 16 Inv. ex. >1000 595 29 855 3.4 0.42 698 5133 3750 17 Inv. ex. >1000 570 22 885 2.2 0.42 746 8739 3800 18 Inv. ex. >1000 569 25 893 4.5 0.40 765 8153 3800 19 Inv. ex. >1000 590 24 882 4.4 0.41 805 7211 3750 20 Inv. ex. >1000 571 22 881 2.5 0.41 801 7724 3800 21 Inv. ex. >1000 580 31 872 4.5 0.42 693 7031 3750 22 Inv. ex. >1000 574 27 898 0.5 0.40 909 7759 3750 23 Inv. ex. >1000 571 24 895 0.8 0.41 715 7058 3750 24 Inv. ex. >1000 588 28 822 3.2 0.41 840 8906 3800 25 Inv. ex. >1000 589 25 882 1.2 0.40 831 20880 3800 26 Inv. ex. >1000 582 28 890 2.9 0.42 791 26862 3800 27 Inv. ex. >1000 593 27 899 2.4 0.41 909 19154 3800 28 Inv. ex. >1000 591 26 896 1.9 0.42 701 42901 3800 29 Inv. ex. >1000 581 25 894 2.4 0.42 690 21158 3800 30 Inv. ex. >1000 598 28 882 2.8 0.42 696 43255 3800 31 Inv. ex. >1000 583 33 893 1.2 0.41 994 11438 3800 32 Inv. ex. >1001 599 30 888 3.4 0.41 707 20960 3800 33 Inv. ex. >1002 587 29 884 1.2 0.42 744 17667 3800 34 Inv. ex. >1000 585 24 889 3.4 0.42 798 37155 3850 35 Inv. ex. >1000 596 26 893 1.3 0.41 678 29928 3850 36 Inv. ex. >1000 596 29 888 1.3 0.41 841 47635 3850 37 Inv. ex. >1000 581 23 882 3.1 0.42 809 34410 3800 38 Inv. ex. >1000 588 28 893 2.8 0.42 778 30449 3850 39 Inv. ex. >1000 581 26 898 1.2 0.41 739 10752 3850 40 Inv. ex. >1000 596 27 895 2.1 0.41 790 47202 3850

(114) TABLE-US-00004 TABLE 4 Chemical composition (mass %) Ex. Class C Si Mn P S Al O N B 41 Comp. ex. 0.15 0.83 1.45 0.022 0.016 0.015 0.002 0.0090 42 Comp. ex. 0.55 0.10 0.89 0.009 0.011 0.025 0.001 0.0052 0.0152 43 Comp. ex. 0.45 0.25 0.50 0.010 0.006 0.450 0.001 0.0160 0.0030 44 Comp. ex. 0.44 1.33 0.51 0.015 0.051 0.074 0.002 0.0090 48 Comp. ex. 0.55 0.28 0.31 0.010 0.025 0.020 0.005 0.0047 49 Comp. ex. 0.56 0.26 0.85 0.005 0.013 0.030 0.001 0.0056 50 Comp. ex. 0.11 0.80 2.59 0.013 0.012 0.029 0.001 0.0110 0.0005 51 Comp. ex. 0.35 0.32 1.44 0.016 0.010 0.025 0.002 0.0053 0.0008 52 Comp. ex. 0.40 0.25 1.35 0.018 0.011 0.017 0.002 0.0052 0.0009 53 Comp. ex. 0.44 0.68 1.23 0.012 0.013 0.013 0.003 0.0047 0.0008 54 Comp. ex. 0.45 0.10 1.11 0.014 0.012 0.025 0.003 0.0051 0.0006 55 Comp. ex. 0.47 0.45 1.45 0.013 0.011 0.026 0.004 0.0047 0.0006 56 Comp. ex. 0.55 0.45 1.34 0.021 0.018 0.052 0.003 0.0050 0.0005 57 Comp. ex. 0.44 0.86 0.30 0.022 0.024 0.027 0.002 0.0047 0.0006 58 Comp. ex. 0.45 0.25 0.25 0.005 0.015 0.030 0.001 0.0050 0.0010 59 Comp. ex. 0.55 0.25 0.33 0.005 0.013 0.029 0.001 0.0047 0.0006 60 Comp. ex. 0.55 0.25 0.28 0.003 0.010 0.033 0.001 0.0053 61 Comp. ex. 0.11 0.12 0.79 0.009 0.010 0.020 0.001 0.0090 62 Comp. ex. 0.20 0.25 0.25 0.010 0.017 0.015 0.001 0.0047

(115) TABLE-US-00005 TABLE 5 (Continuation of Table 4) Chemical composition (mass %) Ex. Class Cr Mo W V Nb Ti Ni Cu Ca Mg Zr Te Mn/S 41 Comp. ex. 91 42 Comp. ex. 81 43 Comp. ex. 83 44 Comp. ex. 0.51 1.43 10 48 Comp. ex. 0.60 0.11 0.37 12 49 Comp. ex. 0.49 0.59 0.51 0.0018 65 50 Comp. ex. 0.050 216 51 Comp. ex. 144 52 Comp. ex. 1.89 0.41 123 53 Comp. ex. 0.91 95 54 Comp. ex. 0.48 0.07 0.31 93 55 Comp. ex. 1.34 0.22 0.0020 132 56 Comp. ex. 0.15 105 57 Comp. ex. 0.54 0.09 0.30 0.10 13 58 Comp. ex. 0.50 0.0016 17 59 Comp. ex. 0.49 0.0017 25 60 Comp. ex. 28 61 Comp. ex. 0.30 79 62 Comp. ex. 0.90 0.50 0.50 15

(116) TABLE-US-00006 TABLE 6 After induction hardening Tempering at 300° C. Surface Soft at depth fatigue nitriding Induction Hardened of 0.2 mm strength Compound heating nitrided from Hole (maximum Machineability, layer conditions layer surface, density hertz no. of Temp. thickness Temp. Time thickness Vicker's (holes/ stress) Ex. Class holes (° C.) (μm) (° C.) (s) (mm) hardness mm.sup.2) (MPa) 41 Comp. ex. 81 593 15 876 1.4 0.33 595 3312 2900 42 Comp. ex. — — — — — — — — — 43 Comp. ex. — — — — — — — — — 44 Comp. ex. 189 590 2 850 3.2 0.13 465 4934 2600 48 Comp. ex. 65 559 4 884 5.0 0.29 570 2754 2800 49 Comp. ex. 66 585 1 879 3.2 0.09 467 2038 2300 50 Comp. ex. 45 587 12 880 4.7 0.65 575 4271 2900 51 Comp. ex. >1000 590 24 980 4.0 0.65 506 2394 2700 52 Comp. ex. >1000 595 25 700 3.5 0.20 398 2816 2150 53 Comp. ex. >1000 577 20 890 8.0 0.70 540 1865 2900 54 Comp. ex. >1000 580 21 845 0.03 0.07 425 880 2600 55 Comp. ex. >1000 680 5 837 4.9 0.10 401 3082 2600 56 Comp. ex. >1000 490 4 880 3.0 0.16 551 1155 2700 57 Comp. ex. >1000 700 3 886 2.1 0.15 387 4670 2500 58 Comp. ex. >1000 570 2 910 2.5 0.14 507 575 2600 59 Comp. ex. >1000 570 3 690 1.2 0.10 401 4366 2200 60 Comp. ex. 33 570 3 920 4.2 0.12 565 2865 2700 61 Comp. ex. 89 590 10 1000 4.0 0.32 572 3482 2800 62 Comp. ex. 45 650 4 1000 2.0 0.23 518 1293 2600

(117) TABLE-US-00007 TABLE 7 Machining conditions Drill Others Machining speed: Size: φ5 mm × Opening depth: 90 mm 65 m/min length 168 mm Judgment of life: Total Feed: 0.17 mm/rev Material: Ceramic coating number of holes until Lubrication: Mist Cemented carbide drill breaks (cut off lubrication (MQL) Projecting amount: 105 mm at 1000)

(118) Note that, what is explained above only illustrates embodiments of the present invention. The present invention can be changed in various ways within the scope of the language of the claims.

INDUSTRIAL APPLICABILITY

(119) As explained above, by soft nitriding, then induction hardening, the steel for surface hardening for machine structural use of the present invention is remarkably increased in hardness at the surface of the steel material and is increased in softening resistance to thereby give a high surface fatigue strength. The present invention is high in value of use in industry.

(120) Further, the parts for machine structural use of the present invention can be used for power transmission parts of automobiles etc. for which a high surface fatigue strength is demanded not only at ordinary temperature of course, but also under usage conditions of resulting in a high temperature of around 300° C., for example, gears, continuously variable transmissions, bearings, constant velocity joints, hubs, etc. They greatly contribute to the higher output and lower cost of automobiles etc. and have remarkable advantageous effects in industry.

REFERENCE SIGNS LIST

(121) 1: cross-sectional hardness distribution of steel material as soft nitrided 2: cross-sectional hardness distribution of steel material which is soft nitrided, then induction hardened 10: hardened nitrided layer 20: hole 30: porous layer 40: surfacemost layer