Patent Application
20140321789
The present invention relates to a machine part, a rolling bearing, a tapered roller bearing, and a method for manufacturing the machine part, and more particularly to a machine part, a rolling bearing, a tapered roller bearing, and a method for manufacturing the machine part that can simultaneously achieve improvement in durability and improvement in dimensional stability.
As measures to improve durability of a machine part made of steel, such as a rolling bearing, a carbonitriding process is known in which carbon and nitrogen are introduced into a surface layer portion of a part prior to a quenching treatment (e.g., see Japanese Patent Laying-Open No. 5-118336 (PTD 1). It is known that this carbonitriding process improves the rolling fatigue life of a rolling bearing, for example, and in particular, the life in an environment in which hard foreign substances intrude into the rolling bearing (a foreign-substance intruding environment).
However, considering recent demands for improved durability of machine parts, the conventional carbonitriding process may not ensure sufficient durability depending on the application. Specifically, in a transmission or a differential of a vehicle, for example, space allowed for a bearing is becoming smaller for increasing the number of stages of the transmission and enlarging driving space. Therefore, size reduction of a bearing that supports a transmission shaft in a transmission or a differential is being developed, and the need to support a load equivalent to that in conventional cases with a smaller bearing has arisen. When the bearing is made smaller, and in a tapered roller bearing on which a larger end face of a tapered roller is guided in contact with a larger flange surface of an inner ring, for example, contact pressure between the tapered roller and the larger flange surface becomes inevitably higher. As a result, a problem arises in that seizure occurs between the tapered roller and the larger flange surface.
Another problem may also arise in that the rate of secure dimensional changes increases with the employment of carbonitriding, resulting in reduced dimensional stability of a machine part.
The present invention was made to solve the above-described problems, and has an object to provide a machine part, a rolling bearing, a tapered roller bearing, and a method for manufacturing the machine part that can simultaneously achieve improvement in durability and improvement in dimensional stability.
A machine part according to one aspect of the present invention is constituted of steel containing at least 0.60 mass % and not more than 1.50 mass % of carbon, at least 0.15 mass % and not more than 2.50 mass % of silicon, at least 0.30 mass % and not more than 1.50 mass % of manganese, and at least 0.20 mass % and not more than 2.00 mass % of chromium with the rest consisting of an impurity. A nitrogen concentration in a surface layer portion under a contact surface to be in contact with another part is at least 0.3 mass %. An average quantity of residual austenite as a whole is not more than 20 volume %.
A machine part according to another aspect of the present invention is constituted of steel containing at least 0.60 mass % and not more than 1.50 mass % of carbon, at least 0.15 mass % and not more than 2.50 mass % of silicon, at least 0.30 mass % and not more than 1.50 mass % of manganese, and at least 0.20 mass % and not more than 2.00 mass % of chromium, and further containing at least either one of not more than 0.5 mass % of nickel and not more than 0.2 mass % of molybdenum with the rest consisting of an impurity. A nitrogen concentration in a surface layer portion under a contact surface to be in contact with another part is at least 0.3 mass %. An average quantity of residual austenite as a whole is not more than 20 volume %.
The inventors of the present application have studied measures to simultaneously achieve improvement in durability and improvement in dimensional stability in a machine part used in contact with another part. As a result, they arrived at the following recognition and yielded the present invention.
In a machine part, damage such as cracks is likely to occur in a surface (contact surface) in contact with another part, such as a rolling contact surface of a rolling bearing and immediately below that surface. Therefore, by carbonitriding this contact surface, durability can be improved. At this time, according to the studies conducted by the inventors of the present application, the contact surface is improved in durability by setting the average nitrogen concentration in a region from a surface which is a contact surface to a depth of 20 μm (in the specification, claims and abstract of the present application, a “surface layer portion” indicates a region from a surface to a depth of 20 μm, and a “nitrogen concentration in the surface layer portion” indicates the average nitrogen concentration in the surface layer portion) to at least 0.3 mass %. On the other hand, when the nitrogen concentration in quench-hardened steel is increased, the quantity of residual austenite increases. With this being decomposed during use of the machine part, the rate of secular changes increases.
Here, in terms of durability of the contact surface, the nitrogen concentration in the surface layer portion, that is, a very thin layer having a depth within 20 μm from the surface is dominant. On the other hand, the rate of secular changes is affected by the quantity of residual austenite in the whole machine part. Therefore, a study on simultaneous achievement of improved durability and improved dimensional stability by reducing the quantity of residual austenite in the whole machine part while increasing the nitrogen concentration in the surface layer portion has revealed that improvement in durability and improvement in dimensional stability can be simultaneously achieved by setting the nitrogen concentration in the surface layer portion under the contact surface to at least 0.3 mass % and setting the whole average quantity of residual austenite to not more than 20 volume %. Such a combination of the nitrogen concentration in the surface layer portion and the whole quantity of residual austenite can be achieved by, for example, introducing nitrogen of higher concentration than in usual carbonitriding to the surface of a part, and then conducting a tempering treatment at a temperature higher than usual.
In the machine part of the present invention, the nitrogen concentration in the surface layer portion under the contact surface is set to at least 0.3 mass %, and the whole average quantity of residual austenite is set to not more than 20 volume %. As a result, according to the machine part of the present invention, the machine part that can simultaneously achieve improvement in durability and improvement in dimensional stability can be provided.
The reason why the component range of the steel constituting the machine part of the present invention has been limited to the aforementioned range is now described.
Carbon: at least 0.60 mass % and not more than 1.50 mass %
The carbon content exerts a remarkable influence on the hardness of the contact surface of the machine part after the quench hardening. If the carbon content in the steel is less than 0.60 mass %, it becomes difficult to supply sufficient hardness to the contact surface after the quench hardening. Alternatively, the need to compensate for the carbon content in the surface by a carburizing treatment or the like arises, resulting in reduced production efficiency and increased manufacturing cost. If the carbon content exceeds 1.50 mass %, on the other hand, occurrence of cracking (quench cracking) at the time of the quench hardening is apprehended. Therefore, the carbon content has been set to at least 0.60 mass % and not more than 1.50 mass %.
Silicon: at least 0.15 mass % and not more than 2.50 mass %
Silicon contributes to improvement in temper softening resistance of the steel. If the silicon content in the steel is less than 0.15 mass %, the temper softening resistance becomes insufficient, and there is a possibility that the hardness of the contact surface remarkably lowers due to tempering after the quench hardening or temperature rise during use of the machine part. If the silicon content exceeds 2.50 mass %, on the other hand, the hardness of the material before the quenching increases, and workability in cold working at the time of forming the material into the machine part lowers. Therefore, the silicon content has been set to at least 0.15 mass % and not more than 2.50 mass %.
Manganese: at least 0.30 mass % and not more than 1.50 mass %
Manganese contributes to improvement in quenchability of the steel. If the manganese content is less than 0.30 mass %, this effect is not sufficiently attained. If the manganese content exceeds 1.50 mass %, on the other hand, the hardness of the material before the quenching increases, and the workability in the cold working lowers. Therefore, the manganese content has been set to at least 0.30 mass % and not more than 1.50 mass %.
Chromium: at least 0.20 mass % and not more than 2.00 mass %
Chromium contributes to improvement in quenchability of the steel. If the chromium content is less than 0.20 mass 0%, this effect is not sufficiently attained. If the chromium content exceeds 2.00 mass %, on the other hand, there arises such a problem that the material cost rises. Therefore, the chromium content has been set to at least 0.20 mass % and not more than 2.00 mass %.
Nickel: at least 0.5 mass %
Nickel also contributes to improvement in quenchability of the steel. While nickel is not an essential component in the steel constituting the machine part according to the present invention, the same can be added in a case where particularly high quenchability is required to the steel constituting the machine part such as a large machine part. If the nickel content exceeds 0.5 mass %, however, there is a possibility that the quantity of residual austenite after the quenching increases to cause reduction of dimensional stability. Therefore, nickel is preferably added to the steel constituting the machine part in the range of not more than 0.5 mass %.
Molybdenum: not more than 0.2 mass %
Molybdenum also contributes to improvement in quenchability of the steel. If the molybdenum content exceeds 0.2 mass %, however, there arises such a problem that the material cost rises. Therefore, molybdenum is preferably added to the steel constituting the machine part in the range of not more than 0.2 mass %.
In the above-described machine part, in the above-described surface layer portion under the contact surface, five or more carbonitrides having a diameter of not more than 0.5 μm may present per 100 μm2 in a section perpendicular to the contact surface.
Because the surface layer portion is strengthened by the presence of fine carbonitrides having a diameter of not more than 0.5 μm at a ratio of five or more per 100 μm2 in the surface layer portion, the surface layer portion is improved more in durability, so that a machine part having excellent durability is obtained. Here, a carbonitride is an iron carbide or is obtained by substituting part of carbon in that carbide with nitrogen, and includes a Fe—C-based compound and a Fe—C—N-based compound. This carbonitride may also contain an alloying element contained in steel, such as chromium.
In the above-described machine part, the quantity of residual austenite in a region having a depth of 50 μm from the contact surface may be at least 20 volume %. Then, the durability of the contact surface, and in particular, the durability of the contact surface in a foreign-substance intruding environment can be improved.
The above-described machine part may be a part constituting a bearing. The machine part of the present invention having improved durability of the contact surface and excellent dimensional stability is suitable for a part constituting a bearing such as a rolling bearing.
The above-described machine part may be an inner ring of a rolling bearing and may have a nitrogen concentration of not more than 0.05 mass % in a radially inner surface. Dimensional changes due to decomposition of residual austenite often appear as expansion in part dimensions. On the other hand, an inner ring of a rolling bearing is often used with its radially inner surface fitted over the outer circumferential surface of a shaft or the like. Therefore, when the inner diameter expands, the fitted state of the inner ring over the shaft may become unstable. Addressing this, the nitrogen concentration in the radially inner surface can be reduced to not more than 0.05 mass % to restrain the above-described problems from arising.
A rolling bearing according to the present invention includes a raceway member and a plurality of rolling elements arranged in contact with the raceway member the present invention. At least either one of the raceway member and the rolling elements is the above-described machine part of the present invention. According to the rolling bearing of the present invention, by including the above-described machine part of the present invention as a component, a rolling bearing that can simultaneously achieve improvement in durability and improvement in dimensional stability can be provided.
A tapered roller bearing according to one aspect of the present invention includes an outer ring having a conical outer ring raceway surface, an inner ring having a conical inner ring raceway surface and being provided with a larger flange surface on a larger diameter side of the inner ring raceway surface and a smaller flange surface on a smaller diameter side, a plurality of tapered rollers arranged rollably between the outer ring raceway surface and the inner ring raceway surface, and a cage holding the tapered rollers at a predetermined spacing in a circumferential direction. During use of the bearing, a larger end face of each of the tapered rollers is guided in contact with the larger flange surface of the inner ring. R/RBASE has a value ranging from 0.75 to 0.87 where R indicates a radius of curvature of the larger end face of each of the tapered rollers and RBASE indicates a distance from a vertex of a conical surface including an outer circumferential surface of each of the tapered rollers to the larger flange surface of the inner ring. At least any one of the outer ring, the inner ring and the tapered rollers is the above-described machine part according to the one aspect of the present invention.
A tapered roller bearing according to another aspect of the present invention includes an outer ring having a conical outer ring raceway surface, an inner ring having a conical inner ring raceway surface and being provided with a larger flange surface on a larger diameter side of the inner ring raceway surface and a smaller flange surface on a smaller diameter side, a plurality of tapered rollers arranged rollably between the outer ring raceway surface and the inner ring raceway surface, and a cage holding the tapered rollers at a predetermined spacing in a circumferential direction. During use of the bearing, a larger end face of each of the tapered rollers is guided in contact with the larger flange surface of the inner ring. R/RBASE has a value ranging from 0.75 to 0.87 where R indicates a radius of curvature of the larger end face of each of the tapered rollers and RBASE indicates a distance from a vertex of a conical surface including an outer circumferential surface of each of the tapered rollers to the larger flange surface of the inner ring. At least any one of the outer ring, the inner ring and the tapered rollers is the above-described machine part according to the other aspect of the present invention.
The inventors of the present application have studied measures to achieve improvement in dimensional stability while securing high durability in a tapered roller bearing. As a result, they have arrived at the following recognition and yielded the present invention.
In the above-described tapered roller bearing including the inner ring, the outer ring and the tapered roller, when calculating the thickness of an oil film formed between the larger flange surface of the inner ring and the larger end face of the tapered roller utilizing the Karna's formula, the thickness of the oil film is at maximum when R/RBASE is 0.76. When R/RBASE exceeds 0.9, the thickness of the oil film rapidly decreases.
On the other hand, when calculating a maximum Hertzian stress between the larger flange surface of the inner ring and the larger end face of the tapered roller, the maximum Hertzian stress monotonously decreases with increase of R/RBASE.
Here, to suppress heat generation due to sliding friction between the larger flange surface of the inner ring and the larger end face of the tapered roller to restrain seizure of the inner ring and the tapered roller, it is desirable to increase the thickness of the oil film and decrease the maximum Hertzian stress. Further, according to the studies conducted by the inventors of the present application, seizure can effectively be restrailed from occurring by adjusting the value of R/RBASE at 0.75 to 0.87. It is noted that the value of R/RBASE of a general tapered roller bearing is approximately 0.90 to 0.97.
In bearing parts such as the outer ring, the inner ring and the rolling element, in a surface in contact with another part (contact surface) and immediately under that surface, damage such as cracks or seizure is likely to occur. Addressing this, this contact surface can be carbonitrided to improve durability. At this time, according to the studies conducted by the inventors of the present application, the contact surface is improved in durability by setting the average nitrogen concentration in a region from a surface which is the contact surface to a depth of 20 μm (in the specification, claims and abstract of the present application, a “surface layer portion” indicates a region from the surface to a depth of 20 μm, and a “nitrogen concentration in the surface layer portion” indicates the average nitrogen concentration in the surface layer portion) to at least 0.3 mass %. Particularly by increasing the nitrogen concentration in the surface layer portion, the quantity of residual austenite in the vicinity of the rolling contact surface increases, so that durability to withstand rolling fatigue in a foreign-substance intruding environment is improved. Further, by increasing the nitrogen concentration in the surface layer portion, temper softening resistance in that surface layer portion is improved. Therefore, even when the temperature of the contact portion is raised by, for example, the sliding contact between the inner ring and the tapered roller (e.g., the sliding contact between the larger end face and the larger flange surface), hardness of that contact portion is restrained from decreasing, and seizure is restrained from occurring.
On the other hand, the nitrogen concentration in the quench-hardened steel is increased, the quantity of residual austenite increases. With this being decomposed during use of the bearing part, the rate of secular changes increases.
Here, in terms of durability of the contact surface, the nitrogen concentration in the surface layer portion, that is, a very thin layer having a depth within 20 μm from the surface is dominant. On the other hand, the rate of secular changes is affected by the quantity of residual austenite in the whole machine part. Therefore, a study on simultaneous achievement of improved durability and improved dimensional stability by reducing the quantity of residual austenite in the whole machine part while increasing the nitrogen concentration in the surface layer portion has revealed that improvement in durability and improvement in dimensional stability can be simultaneously achieved by setting the nitrogen concentration in the surface layer portion under the contact surface to at least 0.3 mass % and setting the whole average quantity of residual austenite to not more than 20 volume %. Such a combination of the nitrogen concentration in the surface layer portion and the whole quantity of residual austenite can be achieved by, for example, introducing nitrogen of higher concentration than in usual carbonitriding to the surface of a part, and then conducting a tempering treatment at a temperature higher than usual.
In the tapered roller bearing of the present invention, seizure between the larger end face of the tapered roller and the larger flange surface of the inner ring is restrained by adjusting the value of R/RBASE to range from 0.75 to 0.87. Further, because at least any one of the outer ring, the inner ring and the tapered roller is a high-strength bearing part (the machine part according to the present invention described above) in which the nitrogen concentration in the surface layer portion under the contact surface is set to at least 0.3 mass % and the whole average quantity of residual austenite is set to not more than 20 volume %, dimensional stability can be improved while achieving improvement in durability to withstand rolling fatigue in a severe environment including a foreign-substance intruding environment and further restraint of seizure by improvement in temper softening resistance. As a result, according to the tapered roller bearing of the present invention, a tapered roller bearing that can achieve improvement in dimensional stability while securing high durability can be provided.
In the above-described tapered roller bearing, the smaller flange surface of the above-described inner ring may be formed by a surface in parallel to the smaller end face of the tapered roller.
Accordingly, even if there are fluctuations in the dimensions of a chamfer on the smaller end face and in the shape of the smaller end face, smaller end face 49 and smaller flange surface 44 lying in parallel to each other come into surface contact in the initial assembled state. Therefore, the gap between the larger end face and the larger flange surface at this time is not affected by fluctuations in the dimensions of the chamfer on the smaller end face and in the shape of the smaller end face, and the time until each tapered roller settles into a regular position after the start of operation less fluctuates. As a result, the running-in time of the tapered roller bearing can be shortened.
In the above-described tapered roller bearing, the larger flange surface of the above-described inner ring may have a surface roughness Ra ranging from 0.05 to 0.20 μm.
By setting above-described surface roughness Ra to at least 0.05 μm, at the running-in performed at low speeds, the lubrication condition between the larger flange surface of the inner ring and the larger end face of the tapered roller can be boundary lubrication, rather than mixed lubrication between fluid lubrication and boundary lubrication. Therefore, the coefficient of friction is stabilized, and preload force can be managed accurately. It is noted that since a sufficient oil film is formed between the larger flange surface and the larger end face under the general bearing use condition in which the rotating speed exceeds 100 rpm, the lubrication condition is brought into fluid lubrication, so that the coefficient of friction becomes sufficiently small. On the other hand, even when the temperature of the bearing increases at high-speed rotation and the viscosity of the lubricant decreases by setting surface roughness Ra to not more than 0.20 μm, the thickness of the oil film can be secured sufficiently, and seizure can be restrained from occurring more reliably.
In the above-described tapered roller bearing, the gap between the smaller flange surface of the inner ring and the smaller end face of the tapered roller, left when the larger end face of the above-described tapered roller comes into contact with the larger flange surface of the inner ring, may be controlled to be not more than 0.4 mm. Accordingly, the number of rotations until the tapered roller settles into the regular position at the running-in can be reduced to shorten the running-in time.
In the above-described tapered roller bearing, the smaller flange surface of the above-described inner ring may be a ground surface or a turned surface. Accordingly, the gap between the smaller flange surface of the inner ring and the smaller end face of the tapered roller can be managed accurately.
In the above-described tapered roller bearing, the larger flange surface of the inner ring may include a base surface to be in contact with the larger end face of each of the tapered rollers, and a flank smoothly connecting with an outer side of the base surface and being curved in a direction spaced away from the larger end face of each of the tapered rollers.
Accordingly, a gap is left in proximity to the outer edge of a contact region between the larger flange surface of the inner ring and the larger end face of the tapered roller. As a result, the function of drawing the lubricant toward the contact region is enhanced, so that a sufficient oil film is formed. Moreover, formation of this smooth flank can restrain a scratch that would be caused by contact between the tapered roller and the larger flange surface of the inner ring when skew of the tapered roller occurs.
In the above-described tapered roller bearing, the flank may have a sectional shape including an arcuate region. Accordingly, a flank having an excellent function of drawing the lubricant can easily be formed.
In the above-described tapered roller bearing, a recess having a circular planar shape may be provided at a central portion of the larger end face of each of the tapered rollers, and an outer circumferential end of the recess may be positioned in a boundary region between the base surface and the flank of the inner ring.
Accordingly, the lubricant can be guided to the vicinity of the above-described gap left in proximity to the outer edge of the contact region between the larger flange surface of the inner ring and the larger end face of the tapered roller to supply the lubricant sufficiently to that gap. Moreover, an allowable skew angle of the tapered roller can be increased further.
In the above-described tapered roller bearing, the boundary between the base surface and the flank may be positioned at an outer edge of a maximum contact ellipse produced by contact between the larger end face of each of the tapered rollers and the larger flange surface under an allowable maximum axial load of the bearing.
Accordingly, the above-described gap to which the lubricant is drawn can be left appropriately over the entire used load range of the tapered roller bearing.
In the above-described tapered roller bearing, in the surface layer portion under the contact surface, five or more carbonitrides having a diameter of not more than 0.5 μm may be present per 100 μm2 in a section perpendicular to the contact surface
Because the surface layer portion is strengthened by the presence of fine carbonitrides having a diameter of not more than 0.5 μm at a ratio of five or more per 100 μm2 in the surface layer portion, the surface layer portion is improved more in durability, so that a machine part having excellent durability is obtained. Here, a carbonitride is an iron carbide or is obtained by substituting part of carbon in that carbide with nitrogen, and includes a Fe—C-based compound and a Fe—C—N-based compound. This carbonitride may also contain an alloying element contained in steel, such as chromium.
In the above-described tapered roller bearing, the quantity of residual austenite in a region having a depth of 50 μm from the contact surface may be at least 20 volume %. Then, the durability of the contact surface, and in particular, the durability of the contact surface in a foreign-substance intruding environment can be improved.
In the above-described tapered roller bearing, the inner ring may be the above-described high-strength bearing part, and the nitrogen concentration in the radially inner surface of the inner ring may be not more than 0.05 mass %.
Dimensional changes due to decomposition of residual austenite often appear as expansion in part dimensions. On the other hand, an inner ring of a rolling bearing is often used with its radially inner surface fitted over the outer circumferential surface of a shaft or the like. Therefore, when the inner diameter expands, the fitted state of the inner ring over the shaft may become unstable. Addressing this, the nitrogen concentration in the radially inner surface can be reduced to not more than 0.05 mass % to restrain the above-described problems from arising.
The above-described tapered roller bearing may be used for supporting a transmission shaft of a vehicle. The above-described vehicle may be a two-wheel vehicle. In a gear shaft support device for a vehicle in which a gear shaft is rotatably supported by a bearing in a housing filled with a gear oil, the above-described tapered roller bearing may be used as that bearing. The tapered roller bearing of the present invention is suitable for the above-described application in which size reduction is required while securing sufficient durability.
A method for manufacturing a machine part according to one aspect of the present invention includes the steps of producing a formed member by forming steel containing at least 0.60 mass % and not more than 1.50 mass % of carbon, at least 0.15 mass % and not more than 2.50 mass % of silicon, at least 0.30 mass % and not more than 1.50 mass % of manganese, and at least 0.20 mass % and not more than 2.00 mass % of chromium with the rest consisting of an impurity, carbonitriding the formed member, quench hardening the formed member having been carbonitrided, tempering the formed member having been quench hardened, and machining the formed member having been tempered, thereby forming a contact surface being a surface to be in contact with another part. In the step of carbonitriding the formed member, the formed member is carbonitrided such that a nitrogen concentration in a surface layer portion under the contact surface is at least 0.3 mass % in the step of forming the contact surface. In the step of tempering the formed member, the formed member is tempered such that an average quantity of residual austenite of the formed member as a whole is not more than 20 volume %. The steps of carbonitriding the formed member, quench hardening the formed member, tempering the formed member, and forming the contact surface are carried out such that, in the surface layer portion under the contact surface, five or more carbonitrides having a diameter of not more than 0.5 μm are present per 100 μm2 in a section perpendicular to the contact surface.
A method for manufacturing a machine part according to another aspect of the present invention includes the steps of producing a formed member by forming steel containing at least 0.60 mass % and not more than 1.50 mass % of carbon, at least 0.15 mass % and not more than 2.50 mass % of silicon, at least 0.30 mass % and not more than 1.50 mass % of manganese, and at least 0.20 mass % and not more than 2.00 mass % of chromium, and further containing at least either one of not more than 0.5 mass % of nickel and not more than 0.2 mass % of molybdenum with the rest consisting of an impurity, carbonitriding the formed member, quench hardening the formed member having been carbonitrided, tempering the formed member having been quench hardened, and machining the formed member having been tempered, thereby forming a contact surface being a surface to be in contact with another part. In the step of carbonitriding the formed member, the formed member is carbonitrided such that a nitrogen concentration in a surface layer portion under the contact surface is at least 0.3 mass % in the step of forming the contact surface. In the step of tempering the formed member, the formed member is tempered such that an average quantity of residual austenite of the formed member as a whole is not more than 20 volume %. The steps of carbonitriding the formed member, quench hardening the formed member, tempering the formed member, and forming the contact surface are carried out such that, in the surface layer portion under the contact surface, five or more carbonitrides having a diameter of not more than 0.5 μm are present per 100 μm2 in a section perpendicular to the contact surface.
According to the methods for manufacturing a machine part of the one and the other aspects of the present invention, the machine parts of the one and the other aspects, in each of which, in the surface layer portion under the contact surface, five or more carbonitrides having a diameter of not more than 0.5 μm are present per 100 μm2 in a section perpendicular to the contact surface, can be manufactured.
In the above-described methods for manufacturing a machine part, in the step of quench hardening the formed member, the formed member may be quench hardened by cooling a region to be the surface layer portion under the contact surface at a cooling rate of at least 20° C./sec on average in a temperature range from a quenching temperature to 600° C. and at least 30° C./sec on average in a temperature range from the quenching temperature to 400° C. Accordingly, a region to be a surface layer portion decreased in quenchability by carbonitriding is quench hardened reliably.
As is clear from the above description, according to the machine part, rolling bearing, tapered roller bearing, and method for manufacturing the machine part of the present invention, a machine part, a rolling bearing, a tapered roller bearing, and a method for manufacturing the machine part that can simultaneously achieve improvement in durability and improvement in dimensional stability can be provided.
Embodiments of the present invention are now described with reference to the drawings. In the following drawings, the same reference numerals are assigned to identical or corresponding portions, and redundant description is not repeated.
First, referring to
Referring to
Outer ring 11, inner ring 12 and ball 13, each serving as the bearing part according to the present embodiment, have a nitrogen concentration of at least 0.3 mass % in surface layer portions 11B, 12B and 13B under the contact surfaces, and the average quantity of residual austenite in each of whole outer ring 11, whole inner ring 12 and whole ball 13 is not more than 20 volume %. As a result, outer ring 11, inner ring 12 and ball 13 are machine parts that can simultaneously achieve improvement in durability and improvement in dimensional stability.
It is noted that the steel constituting outer ring 11, inner ring 12 and ball 13 may further contain at least either one of not more than 0.5 mass % of nickel and not more than 0.2 mass % of molybdenum. Accordingly, the steel is improved in quenchability, and bearing parts of a large-sized rolling bearing can be obtained.
In outer ring 11, inner ring 12 and ball 13, in surface layer portions 11B, 12B and 13B under the contact surfaces (outer ring rolling contact surface 11A, inner ring rolling contact surface 12A and ball rolling surface 13A), five or more carbonitrides having a diameter of not more than 0.5 μm are preferably present per 100 μm2 in a section perpendicular to the contact surface. By the presence of a large number of such fine carbonitrides in surface layer portions 11B, 12B and 13B, surface layer portions 11B, 12B and 13B are improved more in durability, so that outer ring 11, inner ring 12 and ball 13 having excellent durability are obtained. More preferably, ten or more of the above-described carbides are present in the above-described regions. It is noted that the presence (numbers) of the above-described carbides can be checked by, for example, observing the above-described regions with a scanning electron microscope (SEM) and subjecting the observation result to image analysis processing.
Still more preferably, in outer ring 11, inner ring 12 and ball 13, the quantity of residual austenite in regions having a depth of 50 μm from the contact surfaces (outer ring rolling contact surface 11A, inner ring rolling contact surface 12A and ball rolling surface 13A) is at least 20 volume %. Accordingly, durability of outer ring rolling contact surface 11A, inner ring rolling contact surface 12A and ball rolling surface 13A serving as contact surfaces, and in particular, durability of the contact surfaces in a foreign-substance intruding environment can be improved.
Furthermore, referring to
Next, referring to
Raceway rings 21 of thrust needle roller bearing 2 correspond to outer ring 11 and inner ring 12 of the deep groove ball bearing and needle rollers 23 of thrust needle roller bearing 2 correspond to balls 13 of the deep groove ball bearing. They are made of a similar raw material, and have nitrogen enriched layers 21D, 23D, inner portions 21C, 23C, surface layer portions 21B, 23B, raceway ring rolling contact surface 21A, and rolling contact surface 23A having a similar nitrogen concentration and a similar quantity of residual austenite. Accordingly, raceway rings 21 and needle rollers 23 are machine parts that can simultaneously achieve improvement in durability and improvement in dimensional stability.
Next, a method for manufacturing the bearing parts and the rolling bearing according to the above-described embodiment will be described. Referring to
Next, a forming step is carried out as a step (S20). In this step (S20), machining, such as forging or turning, is carried out on the bar steel, steel wire or the like prepared in step (S10), for example, so that formed members formed into shapes of outer ring 11, inner ring 12, balls 13, raceway rings 21, needle rollers 23, and the like shown in
Next, a carbonitriding step is carried out as a step (S30). In this step (S30), the formed member produced in step (S20) is carbonitrided. This carbonitriding can be carried out as will be described below, for example. First, the above-described formed member is preheated for a time at least 30 minutes and not more than 90 minutes in the temperature range of at least 780° C. and not more than 820° C. Next, the preheated formed member is heated in an atmosphere in which an ammonia gas is further introduced into an endoergic gas, such as a RX gas, adjusted in carbon potential by the addition of a propane gas or a butane gas as an enriched gas to be carbonitrided. The temperature of carbonitriding can be set to at least 820° C. and not more than 880° C., for example. The time of carbonitriding can be set in accordance with the nitrogen concentration of a nitrogen enriched layer to be formed in the formed member, and can be set to, for example, at least four hours and not more than twelve hours, preferably to at least four hours and not more than seven hours. Accordingly, the nitrogen enriched layer can be formed while restraining decarburization of the formed member.
Next, a quenching step is carried out as a step (S40). In this step (S40), the formed member with the nitrogen enriched layer formed therein by carbonitriding in step (S30) is rapidly cooled down from a predetermined quenching temperature to be quenched. This quenching temperature can be set to, for example, at least 820° C. and not more than 880° C., and preferably to at least 850° C. and not more than 880° C. The quenching treatment can be carried out by, for example, dipping the formed member in a quenching oil as a coolant kept at a predetermined temperature. In this step (S40), a region in the formed member to be a surface layer portion under a contact surface is preferably cooled at a cooling rate of at least 20° C./sec on average in a temperature range from the quenching temperature to 600° C. and at least 30° C./sec on average in a temperature range from the quenching temperature to 400° C. Accordingly, regions decreased in quenchability by carbonitriding in step (S30), to be surface layer portions, can be quench hardened reliably.
Next, a tempering step is carried out as a step (S50). In this step (S50), the formed member subjected to the quenching treatment in step (S40) is subjected to a tempering treatment. Specifically, the tempering treatment is carried out by holding the formed member for a time period of at least half an hour and not more than three hours in an atmosphere heated to a temperature range of at least 180° C. and not more than 240° C., for example. Furthermore, the tempering temperature may be at least 180° C. and not more than 210° C.
Next, a finishing step is carried out as a step (S60). In this step (S60), by machining the formed member subjected to the tempering treatment in step (S50), a contact surface to be in contact with another part, namely, outer ring rolling contact surface 11A, inner ring rolling contact surface 12A and ball rolling surface 13A of deep groove ball bearing 1, as well as raceway ring rolling contact surface 21A and rolling contact surface 23A of thrust needle roller bearing 2 are formed. As the finishing, grinding can be carried out, for example. Through the above steps, outer ring 11, inner ring 12, balls 13, raceway rings 21, needle rollers 23, and the like, each serving as the bearing part according to the present embodiment, are completed.
Furthermore, an assembling step is carried out as a step (S70). In this step (S70), outer ring 11, inner ring 12, balls 13, raceway rings 21, and needle rollers 23 produced through steps (S10) to (S60) are combined with separately prepared cages 14, 24 and the like to assemble deep groove ball bearing 1 or thrust needle roller bearing 2 according to the above-described embodiment. Accordingly, the method for manufacturing the rolling bearing according to the above-described embodiment is completed.
Here, in the above-described step (S30), the formed member is carbonitrided such that the nitrogen concentration in surface layer portions 11B, 12B, 13B, 21B, and 23B under the contact surfaces becomes at least 0.3 mass % by the finishing in subsequent step (S60). That is, in consideration of a machining allowance in step (S60) and the like, nitrogen enriched layers 11D, 12D, 13D, 21D, and 23D having a nitrogen amount adjusted such that the nitrogen concentration in the surface layer portions after the completion of the contact surfaces can be at least 0.3 mass % are formed.
Furthermore, in above-described step (S50), the formed member is subjected to the tempering treatment such that the average quantity of residual austenite in the whole formed member is not more than 20 volume %.
In a finished product, to set the quantity of residual austenite in regions having a depth of 50 μm from outer ring rolling contact surface 11A, inner ring rolling contact surface 12A and ball rolling surface 13A of deep groove ball bearing 1 as well as raceway ring rolling contact surface 21A and rolling contact surface 23A of thrust needle roller bearing 2 serving as contact surfaces to at least 20 volume %, the distribution of nitrogen concentration formed in step (S30), the quenching temperature in step (S40), the tempering temperature in step (S50), the machining allowance in step (S60), or the like, for example, can be adjusted.
Furthermore, to set the nitrogen concentration in radially inner surface 12E of inner ring 12 to not more than 0.05 mass %, step (S30) may be carried out after covering radially inner surface 12E with a jig or a coading layer, for example.
To bring about a state where, in a cross section perpendicular to the contact surfaces, five or more carbonitrides having a diameter of not more than 0.5 μm are present per 100 μm2 in surface layer portions 11B, 12B, 13B, 21B, and 23B, the quenching temperature in step (S40), the tempering temperature in step (S50), or the like, for example, can be adjusted.
Next, a differential of a vehicle including a tapered roller bearing according to a second embodiment as another embodiment of the present invention will be described.
Next, tapered roller bearing 5 will be described as a representative example of the tapered roller bearing according to the above-described embodiment. Referring to
Referring to
As shown in
On the other hand,
From the viewpoint of reducing torque loss and heat generation caused by sliding friction between the larger flange surface of the inner ring and the larger end face of the tapered roller, it is desirable to increase oil film thickness t and decrease maximum Hertzian stress p. With reference to the calculation results of
It is noted that although not shown, above-described tapered roller bearings 3 and 4 also have a structure similar to that of above-described tapered roller bearing 5. In the present embodiment, smaller flange surface 44 of inner ring 45 is described as a ground surface, but can be a turned surface for cost reduction.
Furthermore, outer ring 41, inner ring 45 and tapered roller 46 serving as bearing parts are made of quench-hardened steel containing at least 0.60 mass % and not more than 1.50 mass % of carbon, at least 0.15 mass % and not more than 2.50 mass % of silicon, at least 0.30 mass % and not more than 1.50 mass % of manganese, and at least 0.20 mass % and not more than 2.00 mass % of chromium with the rest consisting of an impurity, for example, SUJ2 which is a JIS high-carbon chromium bearing steel. In regions including outer ring raceway surface 40, inner ring raceway surface 42, larger flange surface 43, smaller flange surface 44, and the surface of the tapered roller (larger end face 48, smaller end face 49 and tapered roller rolling surface 46A serving as a rolling contact surface) serving as contact surfaces, nitrogen enriched layers 41D, 45D and 46D having a nitrogen concentration higher than in inner portions 41C, 45C and 46C are respectively formed as shown in
In tapered roller bearing 5 according to the above-described embodiment, seizure between larger end face 48 of tapered roller 46 and larger flange surface 43 of inner ring 45 is restrained by adjusting the value of R/RBASE to range from 0.75 to 0.87. Furthermore, outer ring 41, inner ring 45 and tapered roller 46 are high-strength bearing parts in which the nitrogen concentration in surface layer portions 41B, 45B and 46B under the contact surfaces is set to at least 0.3 mass % and the whole average quantity of residual austenite is set to not more than 20 volume %. Accordingly, a tapered roller bearing is obtained in which dimensional stability is improved while achieving improvement in durability to withstand rolling fatigue in a severe environment including a foreign-substance intruding environment and further restraint of seizure by improvement in temper softening resistance. As a result, tapered roller bearing 5 has high durability and excellent dimensional stability.
It is noted that steel constituting outer ring 41, inner ring 45 and tapered roller 46 may further contain at least either one of not more than 0.5 mass % of nickel and not more than 0.2 mass % of molybdenum. Accordingly, the steel is improved in quenchability, and bearing parts of a large-sized rolling bearing can be obtained.
In outer ring 41, inner ring 45 and tapered roller 46, five or more carbonitrides having a diameter of not more than 0.5 μm are preferably present per 100 μm2 in surface layer portions 41B, 45B and 46B under the contact surfaces (outer ring raceway surface 40, inner ring raceway surface 42, larger flange surface 43, smaller flange surface 44, and the surface of the tapered roller (larger end face 48, smaller end face 49 and tapered roller rolling surface 46A serving as the rolling contact surface)). By the presence of a large number of such fine carbonitrides in surface layer portions 41B, 45B and 46B, surface layer portions 41B, 45B and 46B are improved more in durability, so that outer ring 41, inner ring 45 and tapered roller 46 having excellent durability are obtained. More preferably, ten or more of the above-described carbides are present in the above-described regions. It is noted that the presence (numbers) of the above-described carbides can be checked by, for example, observing the above-described regions with a scanning electron microscope (SEM) and subjecting the observation result to image analysis processing.
Furthermore, in outer ring 41, inner ring 45 and tapered roller 46, the quantity of residual austenite in the regions having a depth of 50 μm from the contact surfaces is preferably at least 20 volume %. Accordingly, durability of outer ring raceway surface 40, inner ring raceway surface 42, larger flange surface 43, smaller flange surface 44, and the surface of the tapered roller (larger end face 48, smaller end face 49 and tapered roller rolling surface 46A serving as the rolling contact surface) serving as the contact surfaces, and in particular, durability of the rolling contact surface in a foreign-substance intruding environment can be improved.
Referring to
Next, a variation of the tapered roller bearing according to the above-described embodiment will be described. The tapered roller bearing according to the present variation basically has a structure and effects similar to those of the tapered roller bearing according to the above-described embodiment. As will be described below, however, the present variation differs from the case of the above-described embodiment in terms of the structure of larger end face 48 of tapered roller 46 and larger flange surface 43 of inner ring 45.
Referring to
Tapered roller 46 rolls with larger end face 48 being pressed against larger flange surface 43 during use of the bearing. Therefore, part of spherical surface 48a comes into contact with base surface 43a to produce a contact ellipse 50 as shown in
Contact ellipse 50 becomes larger as the axial load during use of the bearing is higher. Assuming a maximum contact ellipse under an allowable maximum axial load, tapered roller bearing 5 according to the present variation is designed such that the boundary between flank 43b and base surface 43a lies in proximity to the outer edge of this maximum contact ellipse. Accordingly, the wedge-shaped gap into which the lubricant is drawn can be formed appropriately over the entire used load range.
Next, a method for manufacturing the bearing parts and the rolling bearing according to the above-described embodiment will be described. Referring to
Next, a forming step is carried out as step (S20). In this step (S20), machining, such as forging or turning, is carried out on the bar steel, steel wire or the like prepared in step (S10), for example, so that formed members formed into the shape of outer ring 41, inner ring 45 and tapered roller 46 are produced.
Next, a carbonitriding step is carried out as step (S30). In this step (S30), the formed member produced in step (S20) is carbonitrided. This carbonitriding can be carried out as will be described below, for example. First, the above-described formed member is preheated for a time at least 30 minutes and not more than 90 minutes in the temperature range of at least 780° C. and not more than 820° C. Next, the preheated formed member is heated in an atmosphere in which an ammonia gas is further introduced into an endoergic gas, such as a RX gas, adjusted in carbon potential by the addition of a propane gas or a butane gas as an enriched gas to be carbonitrided. The temperature of carbonitriding can be set to at least 820° C. and not more than 880° C., for example. The time of carbonitriding can be set in accordance with the nitrogen concentration of a nitrogen enriched layer to be formed in the formed member, and can be set to, for example, at least four hours and not more than twelve hours, preferably to at least four hours and not more than seven hours. Accordingly, the nitrogen enriched layers can be formed while restraining decarburization of the formed member.
Next, a quenching step is carried out as step (S40). In this step (S40), the formed member with the nitrogen enriched layer formed therein by carbonitriding in step (S30) is rapidly cooled down from a predetermined quenching temperature to be quenched. This quenching temperature can be set to, for example, at least 820° C. and not more than 880° C., and preferably to at least 850° C. and not more than 880° C. The quenching treatment can be carried out by, for example, dipping the formed member in a quenching oil as a coolant kept at a predetermined temperature. In this step (S40), a region in the formed member to be a surface layer portion under a contact surface is preferably cooled at a cooling rate of at least 20° C./sec on average in a temperature range from the quenching temperature to 600° C. and at least 30° C./sec on average in a temperature range from the quenching temperature to 400° C. Accordingly, the region decreased in quenchability by carbonitriding in step (S30), to be a surface layer portion, can be quench hardened reliably.
Next, a tempering step is carried out as step (S50). In this step (S50), the formed member subjected to the quenching treatment in step (S40) is subjected to a tempering treatment. Specifically, the tempering treatment is carried out by holding the formed member for a time period of at least half an hour and not more than three hours in an atmosphere heated to a temperature range of at least 180° C. and not more than 240° C. for example. Furthermore, the tempering temperature may be at least 180° C. and not more than 210° C.
Next, a finishing step is carried out as step (S60). In this step (S60), by machining the formed member subjected to the tempering treatment in step (S50), a contact surface to be in contact with another part, namely, outer ring raceway surface 40 of outer ring 41, inner ring raceway surface 42 of inner ring 45 and tapered roller rolling surface 46A of tapered roller 46 are formed. As the finishing, grinding can be carried out, for example. Through the above steps, outer ring 41, inner ring 45, tapered rollers 46, and the like, each serving as the bearing part according to the present embodiment, are completed.
Furthermore, an assembling step is carried out as step (S70). In this step (S70), outer ring 41, inner ring 45 and tapered rollers 46 produced through steps (S10) to (S60) are combined with separately prepared cage 47 and the like to assemble tapered roller bearing 5 according to the above-described embodiment. Accordingly, the method for manufacturing the rolling bearing according to the above-described embodiment is completed.
Here, in the above-described step (S30), the formed member is carbonitrided such that the nitrogen concentration in surface layer portions 41B, 45B and 46B under the contact surfaces becomes at least 0.3 mass % by the finishing in subsequent step (S60). That is, in consideration of a machining allowance in step (S60) and the like, nitrogen enriched layers 41D, 45D and 46D having a nitrogen amount adjusted such that the nitrogen concentration in the surface layer portions after the completion of the contact surfaces can be at least 0.3 mass % are formed.
Furthermore, in above-described step (S50), the formed member is subjected to the tempering treatment such that the whole average quantity of residual austenite in the formed member is not more than 20 volume %.
In a finished product, to set the quantity of residual austenite in regions having a depth of 50 μm from outer ring raceway surface 40, inner ring raceway surface 42 and tapered roller rolling surface 46A serving as contact surfaces to at least 20 volume %, the distribution of nitrogen concentration formed in step (S30), the quenching temperature in step (S40), the tempering temperature in step (S50), the machining allowance in step (S60), or the like, for example, can be adjusted.
Furthermore, to set the nitrogen concentration in radially inner surface 45E of inner ring 45 to not more than 0.05 mass %, step (530) may be carried out after covering radially inner surface 45E with a jig or a coading layer, for example.
To bring about a state where, in a cross section perpendicular to the contact surfaces, five or more carbonitrides having a diameter of not more than 0.5 μm are present per 100 μm2 in surface layer portions 41B, 45B and 46B, the quenching temperature in step (S40), the tempering temperature in step (50), or the like, for example, can be adjusted.
It is noted that tapered roller bearing 5 described in the above-described embodiment is an example of the tapered roller bearing of the present invention. The tapered roller bearing of the present invention is applicable to tapered roller bearings of various forms.
An experiment was carried out to study the influence of the nitrogen concentration in the surface layer portions exerted on durability of a raceway ring of a rolling bearing. Specifically, a rolling fatigue life test was carried out with an impression formed at the rolling contact surface of a raceway ring (inner ring). The procedure of the experiment will be described below.
The test was carried out with a JIS 6206 deep groove ball bearing (having an inner diameter of 30 mm, an outer diameter of 62 mm, a width of 16 mm, nine rolling elements, and made of SUJ2) and a JIS 30206 tapered roller bearing (bearing parts made of JIS SUJ2). First, an inner ring was produced through a procedure similar to that of the above-described embodiment. At this time, the distribution of concentration of nitrogen which intrudes to the vicinity of the inner ring surface was controlled by adjusting the undecomposed ammonia partial pressure, hydrogen partial pressure, carbon activity, heat treatment time, and quenching temperature in an atmosphere during carbonitriding. For comparison, inner rings not subjected to carbonitriding were also produced. As a result, inner rings having four types of distributions of nitrogen concentration as shown in
Next, an impression was formed at each obtained inner ring. Here, as an evaluation method of rolling bearing life simulating an actual use environment, a life test under foreign-substance mixed lubrication may be carried out. This test method is to evaluate the flexing life of a rolling bearing by operating it with particles having a particle diameter of 100 μm to 180 μm (having a hardness of approximately 800 HV) produced by gas atomization mixed into the lubricant of the rolling bearing. The reason for setting the particle diameter to 100 μm to 180 μm is because hard foreign substances having a particle diameter of approximately 100 μm at maximum may be mixed in an actual use environment.
The shape and microstructure of a protrusion of the impression is a major factor that determines the life. The shape of the protrusion of the impression is considered to be determined by a microstructure of a material down to the impression depth. The microstructure of steel varies depending on the nitrogen concentration. From these, the life in an environment where a hard foreign substance intrudes is considered to depend not only on the nitrogen concentration in the surface but also on the nitrogen concentration from the surface to the impression depth.
The impression depth becomes approximately 20 μm at maximum as described above. From this, the specification of the present application and the like define a region from the surface to a depth of 20 μm as a surface layer portion and an average nitrogen concentration in the surface layer portion as a “nitrogen concentration in the surface layer portion.” Specifically, the nitrogen concentration in this surface layer portion can be examined by performing a linear analysis on a cross section perpendicular to the surface in the depth direction by EPMA (Electron Probe Micro Analysis) to calculate the average value from the surface to a depth of 20 μm.
In light of the above result of study, an impression was formed at the inner ring by pressing a conical diamond Rockwell hardness measuring indenter (an indenter having a spherical surface of a curvature of 0.2 mm at the vertex of a cone having a vertex angle of 120°) against the center of the rolling contact surface (the center of groove bottom) at a load of 196N. By measuring the shape of the formed impression by a three-dimensional surface shape device, it was confirmed that the protrusion on the peripheral of the impression had a substantially symmetric shape in the axial direction and the circumferential direction with the center of the impression serving as the axis of symmetry.
The inner ring thus produced was combined with a common outer ring not subjected to carbonitriding or not having any impression formed therein, a rolling element, a cage, and the like to assemble a bearing. The obtained bearing was then subjected to a life test. The test result is shown in
In
An experiment was carried out to study the influence of the quantity of residual austenite on secular dimensional changes. Using SUJ2 as a raw material, ring-shaped test pieces having an outer diameter of 60 mm, an inner diameter of 54 mm, and a width t of 15 mm were produced with the quenching temperature, tempering temperature and the nitrogen concentration in the surface layer portion varied. A heat treatment was carried out to heat each of these test pieces to 230° C. and keep it for two hours. The dimensional difference in outer diameter before and after the heat treatment was divided by the outer diameter before the heat treatment to calculate the rate of secure dimensional changes. The test result is shown in Table 1. On the other hand, the distribution of the quantity of residual austenite in each of the above-described test pieces is shown in
Referring to Table 1 and
An experiment was carried out to study the distributed state of carbonitrides in a surface layer portion under a contact surface. Under a procedure similar to that in the case of the above-described embodiment, a test piece of SUJ2 was produced on the condition that the carbon activity during carbonitriding was adjusted to restrain disappearance of carbide due to solution. This manufacturing condition corresponds to the manufacturing condition for the test piece whose long life was confirmed in the above-described Example 1. Specifically, the quenching temperature was 850° C. the tempering temperature was 180° C. and the nitrogen concentration in the surface layer portion was 0.3 mass % (Example A). On the other hand, for comparison, a test piece was produced similarly on the condition that decarburization occurred in the vicinity of the surface (Comparative Example). The distributions of carbon concentration and nitrogen concentration in the vicinity of the surface in the test pieces of Comparative Example and Example A are shown in
Referring to
Here, for Examples A and B corresponding to the manufacturing condition on which a long life was confirmed in above-described Example 1, the number of carbonitrides having a diameter of not more than 0.5 μm considered to contribute to precipitation strengthening was calculated based on SEM photographs of the surface layer portion (SEM photographs of a cross section perpendicular to the surface). The calculation result is shown in Table 2.
The number of carbonitrides present in a region within 100 μm2 was checked three times (at three positions) for each test piece to calculate the average value. As shown in Table 2, it was confirmed that in Examples A and B in which a long life was confirmed, five or more carbonitrides having a diameter of not more than 0.5 μm were present within 100 μm2.
An experiment was carried out to confirm the effect achieved by setting the values of R/RBASE and δ described above to appropriate ranges.
A tapered roller bearing was prepared in which radius of curvature R of the larger end face of a tapered roller was adjusted in such a range where above-described R/RBASE=0.75 to 0.87, the larger flange surface of an inner ring had a surface roughness Ra of 0.12 μm, the smaller flange surface was formed by a ground surface lying in parallel to the smaller end face of the tapered roller, and gap δ was adjusted to fall within the range of δ≦0.4 mm (Example). The dimensions of the bearing had an inner diameter of 40 mm and an outer diameter of 68 mm in any case. On the other hand, for comparison, a tapered roller bearing was also prepared in which the value of R/RBASE fell outside the above-described range, the smaller flange surface of the inner ring was inclined outwardly relative to the smaller end face of the tapered roller, and gap δ exceeded 0.4 mm (Comparative Example). The dimensions of each bearing are equal to those in the above-described Example. More specifically, four types of tapered roller bearings corresponding to the Example shown in Table 3 and three types of tapered roller bearings corresponding to the Comparative Example were prepared.
Then, for each of the tapered roller bearings of the above-described Example and Comparative Example, a seizure resistance test was carried out with a rotary testing machine. A running-in test was also carried out for the tapered roller bearings of Example D and Comparative Example B. The number of samples in the running-in test was 66 for Example D and 10 for Comparative Example B. The test conditions for the seizure resistance test are indicated below.
Applied load-19.61 kN
Rotating speed: 1000 to 3500 rpm
Lubricant: turbine VGS6 (a lubrication amount of 40 ml/min, a lubrication temperature of 40° C.±3° C.)
The test result is shown in Table 3. Seizure in the seizure resistance test occurred between the larger flange surface of the inner ring and the larger end face of the tapered roller.
In each of the tapered roller bearings of the Example, the limit rotating speed for the occurrence of seizure in the seizure resistance test is at least 2700 rpm, which means that the friction resistance between the larger flange surface of the inner ring and larger end face of the tapered roller is small. On the other hand, in the tapered roller bearings of the Comparative Example, the limit rotating speed for the occurrence of seizure is not more than 2500 rpm, which may be disadvantageous under the usual use condition of a differential or the like. Comparative Example C in which surface roughness Ra of the larger flange surface is high exhibits a limit rotating speed for the occurrence of seizure smaller than in Comparative Example B having an identical radius of curvature R.
According to the result of running-in test, the average value of the number of rotations until each tapered roller settled into the regular position is six in the Comparative Example, while it is 2.96 in the Example, which is about half. It is understood that the standard deviation of fluctuations in the number of rotations is small in the Example, so that the running-in time can be shortened stably.
An experiment was carried out to confirm improvement in temper softening resistance caused by forming nitrogen enriched layers. First, a test piece of JIS SUJ2 was prepared. Then, this was heated to 850° C. in an atmosphere where an ammonia gas was added to an RX gas and kept for 180 minutes, so that the nitrogen concentration in the surface layer portion became at least 0.3 mass %. Then, a quench-hardened sample was produced (Example, high-concentration nitrided product). On the other hand, for comparison, a similar test piece was prepared. This was heated to 850° C. in an RX gas atmosphere and kept for 80 minutes. Then, a quench-hardened sample was produced (Comparative Example; normally quenched product). A heat treatment was carried out to heat the thus obtained samples of the Example and the Comparative Example in an atmosphere kept at a predetermined temperature, and the surface hardness after the heat treatment was measured. The experimental result is shown in
Referring to
Although in the above-described first embodiment and Examples 1 to 3, components of the rolling bearing have been described as an exemplary machine part of the present invention, the machine part of the present invention is not limited to this, but is applicable to various machine parts having a contact surface to be in contact with another part, such as components of a universal joint or a gear.
It should be understood that the embodiments and examples disclosed herein are illustrative and non-restrictive in every respect. The scope of the present invention is defined by the claims not by the description above, and is intended to include any modification within the meaning and scope equivalent to the terms of the claims
A machine part, a rolling bearing, a tapered roller bearing, and a method for manufacturing the machine part of the present invention may be particularly advantageously applied to a machine part, a rolling bearing, a tapered roller bearing, and a method for manufacturing the machine part required to simultaneously achieve improvement in durability and improvement in dimensional stability.
1 deep groove ball bearing; 2 thrust needle roller bearing; 3, 4, 5 tapered roller bearing; 11, 41 outer ring; 11A outer ring rolling contact surface, 11B, 12B, 13B, 21B, 23B, 41B, 45B, 46B surface layer portion; 11C, 12C, 13C, 21C, 23C, 41C, 45C, 46C inner portion; 11D, 12D, 131D, 21D, 23D, 41D, 451, 46D nitrogen enriched layer; 12, 45 inner ring; 12A inner ring rolling contact surface; 12E, 45E radially inner surface; 13 ball; 13A ball rolling surface; 14, 24 cage; 21 raceway ring; 21A raceway ring rolling contact surface; 23A rolling contact surface: 31 housing; 32 drive pinion; 33 ring gear; 34 differential gear case; 35 pinion; 36 side gear; 40 outer ring raceway surface; 42 inner ring raceway surface; 43 larger flange surface; 43a base surface; 43b flank; 43c chamfer; 46A rolling surface; 48 larger end face; 48a spherical surface; 50 contact ellipse.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2011-268922 | Dec 2011 | JP | national |
| 2012-225137 | Oct 2012 | JP | national |
| Filing Document | Filing Date | Country | Kind | 371c Date |
|---|---|---|---|---|
| PCT/JP2012/081337 | 12/4/2012 | WO | 00 | 6/6/2014 |
