JP2014189854A - Steel material for bearing excellent in rolling fatigue characteristic and machinability, and bearing parts - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a steel material for a bearing excellent in rolling fatigue characteristic and machinability.SOLUTION: The steel material for a bearing contains, C:0.8 to 1.1%, Si:0.15 to 0.8%, Mn:0.10 to 1%, P:0.05% or less (excluding 0%), S:0.005% to 0.015%, Cr:1.3 to 1.8%, Al:0.0002 to 0.005%, Ti:0.0005 to 0.010%, N:0.010% or less (excluding 0%), Ca:0.0002 to 0.002%, O:0.0030% or less (excluding 0%) and the balance iron with inevitable impurities. In the steel material for a bearing, an average composition of oxide-based inclusion contains, by mass%, CaO:20 to 50%, AlO:15 to 50%, SiO:20 to 62%, TiO:3 to 10%, and an estimated value of square root of a projected area of the maximum sulfide-based inclusion (√area max) is 50 to 150 μm.

Description

  The present invention exhibits excellent machinability when bearing steel is processed into rolling elements (rollers, needles, balls, races, etc.) for bearings used in various industrial machines and automobiles. The present invention relates to a bearing steel material that exhibits excellent rolling fatigue characteristics when used as a rolling element. The present invention also relates to a bearing component obtained from such a bearing steel material.

  High rolling stress is applied from the radial direction (perpendicular to the axis of the rotating body) to the rolling elements for bearings used in various industrial machines and automobiles. For this reason, rolling elements for bearings are required to have excellent rolling fatigue characteristics. The requirements for rolling fatigue characteristics are becoming stricter year by year in response to the higher performance and lighter weight of industrial machinery. To further improve the durability of bearing parts, the steel materials for bearings are even more demanding. Good rolling fatigue characteristics are required.

Conventionally, the rolling fatigue characteristics are hard oxide inclusions such as Al ₂ O ₃ produced mainly when using Al deoxidized steel among oxide inclusions produced in steel. It was thought to be deeply correlated with the number density of. Therefore, a method for improving rolling fatigue characteristics by reducing the number density of the hard oxide inclusions has been studied. For example, attempts have been made to improve rolling fatigue properties by reducing the oxygen content in the steel in the steel making process.

  However, in recent years, research on the relationship between rolling fatigue characteristics and nonmetallic inclusions typified by oxide inclusions has progressed, and the number density of oxide inclusions and the rolling fatigue characteristics are not necessarily correlated. It turns out not. That is, the rolling fatigue characteristics are closely correlated with the size of the nonmetallic inclusions, for example, the square root of the area of the nonmetallic inclusions. It has become clear that reducing the size of non-metallic inclusions is more effective than reducing the number density.

Therefore, instead of using the conventional Al deoxidized steel, while suppressing the Al content in the steel as much as possible, and making it a Si deoxidized steel, the composition of the oxide produced is mainly Al ₂ O ₃ Control to a composition mainly composed of SiO ₂ , CaO, etc., thereby reducing the size of the nonmetallic inclusions by extending and dividing the nonmetallic inclusions in the rolling process and improving the rolling fatigue characteristics. A method has been proposed.

For example, Patent Document 1 discloses a technique for improving cold workability and rolling fatigue characteristics by controlling the chemical component composition of steel, the average composition of oxide inclusions, and the like. In particular an average composition of the oxide _{inclusions, CaO: 10~60%, Al 2} O 3: 35% or less, MnO: 35% or less, and MgO: 15% or less, by controlling the balance SiO ₂ and impurities A technique for improving rolling fatigue characteristics is disclosed.

  Further, Patent Document 2 discloses a technique for improving rolling fatigue characteristics by adding Te to crystallize a sulfide-based inclusion into a crystal.

JP 2010-07092 A JP 2012-36434 A

  In recent years, from the viewpoint of reducing manufacturing costs, improvement in machinability when manufacturing various bearing parts from bearing steel has been demanded. Since steel for bearings is difficult to cut, it is subjected to spheroidizing annealing (softening treatment), but there is still a problem that tool wear is severe and tool life is short. Therefore, it is desired that the steel for bearings not only has excellent rolling fatigue characteristics but also has excellent machinability, but a steel for bearings having both characteristics has not been developed yet.

  The present invention has been made paying attention to the above-described circumstances, and an object thereof is to provide a steel material for bearings and bearing parts having excellent rolling fatigue characteristics and excellent machinability. .

Steel materials for bearings having excellent rolling fatigue characteristics and cutting workability according to the present invention that can solve the above problems are: C: 0.8 to 1.1%, Si: 0.15 to 0.8%, Mn : 0.10 to 1%, P: 0.05% or less (not including 0%), S: 0.005 to 0.015%, Cr: 1.3 to 1.8%, Al: 0.0002 -0.005%, Ti: 0.0005-0.010%, N: 0.010% or less (excluding 0%), Ca: 0.0002-0.002%, O: 0.0030% or less (The content is 0%), the balance is iron and inevitable impurities, the average composition of oxide inclusions contained in the steel is mass%, CaO: 20 to 50%, Al ₂ O ₃ : _{15~50%, SiO 2: 20~62%} , TiO 2: containing 3-10%, and, the projected area of the largest sulfide inclusions square ( Predictive value of area max) has the gist that a 50 to 150 [mu] m.

  In a preferred embodiment of the present invention, the bearing steel further includes Cu: 0.5% or less (excluding 0%), Ni: 0.5% or less (excluding 0%), and Mo: 0.5. % Containing at least one selected from the group consisting of% or less (not including 0%).

  The present invention also includes a bearing component obtained using the bearing steel material.

  According to the present invention, the chemical composition of the steel material, the average composition of the oxide inclusions contained in the steel material, and the predicted value of the sulfide inclusion (√area max) are appropriately controlled. It is possible to provide a steel material for bearings that is extremely excellent in dynamic fatigue characteristics and machinability. Such a steel material for bearings is excellent in machinability, so that the tool life can be improved and the manufacturing cost can be reduced.

  Moreover, the steel material for bearings of the present invention is useful as a material for bearing parts, such as rollers, needles, balls, etc., which are repeatedly subjected to a load mainly in the radial direction. Furthermore, the steel material for bearings of the present invention is useful as a material for bearing parts, such as races, which are repeatedly subjected to a load in the strus direction, and stably improves the rolling fatigue characteristics regardless of the direction in which the load is applied. be able to.

  The present inventors can stably improve the rolling fatigue characteristics regardless of the direction in which the load is applied without performing deoxidation treatment with Al, and can suppress early peeling, and steel (bearing In order to provide Si deoxidized steel for bearings with good cutting workability (for example, turning tool life, etc.) when finishing to the final shape by performing cutting etc. I have been studying it.

First, oxide inclusions obtained by Si deoxidation are crystallized in a high temperature region such as hot working to become a polycrystal. Polycrystalline oxide inclusions have higher deformation resistance than the parent phase steel, so there are voids at the interface between the steel (matrix) and oxide inclusions during hot working or cold working. , Which causes cracks and deteriorates the rolling fatigue characteristics. Therefore, the present inventors have intensively studied a method for suppressing crystallization by controlling the composition of the oxide inclusions obtained by Si deoxidation and suppressing the generation of voids by using an amorphous body. did. As a result, it became clear that crystallization can be suppressed by including TiO ₂ that has not been conventionally contained in the oxide inclusions obtained by Si deoxidation. Specifically, it has been found that rolling fatigue characteristics can be improved by using a Si deoxidized steel material containing Ti as a component in steel within a predetermined range and TiO ₂ as an oxide inclusion within a predetermined range. It was.

In the present invention, the reason why the rolling fatigue characteristics are improved by setting the oxide inclusions to a composition containing TiO ₂ is unknown in detail, but is considered as follows.

That is, when SiO ₂ -containing oxide inclusions obtained by Si deoxidation contain TiO _{2, they} are separated into two phases of TiO ₂ concentrated phase (A phase) and SiO ₂ concentrated phase (B phase). To do. The reason for separating into two phases is considered to be due to the property of separating into two liquid phases of TiO ₂ and SiO ₂ at the molten steel stage. As a result, SiO ₂ is SiO ₂ concentration in the concentrated phase (B phase) increases, gehlenite was easy to occur in the Si-deoxidized steel (Gehlenite), spinel _{(Spinel, MgO · Al 2 O} 3) crystalline, such as Is suppressed. On the other hand, in the TiO ₂ concentrated phase (A phase), when TiO ₂ is contained in the oxide inclusions, the liquidus temperature also decreases, and the above-described crystallization of gehlenite, spinel, etc. is suppressed. . Therefore, it is possible to suppress crystallization during hot working of the SiO ₂ -containing oxide inclusions, which was unavoidable in the conventional method. Further, cavities generated at the interface between the parent phase steel and the oxide inclusions can be suppressed. Furthermore, it is possible to suppress cavities generated inside the oxide inclusions that are polycrystalline. As a result, the rolling fatigue characteristics can be significantly improved.

Furthermore, since the SiO ₂ concentrated phase (B phase) has a high SiO ₂ concentration, it is amorphous but has high deformation resistance during hot working. Therefore, the extension of inclusions during hot working can be suppressed while maintaining an amorphous state. As a result, the aspect ratio (major axis / minor axis) can be kept low, so that the rolling fatigue characteristics can be stably improved regardless of the direction in which the load is applied, and early peeling can be suppressed. it can.

On the other hand, when a predetermined TiO ₂ concentration is not ensured in the oxide inclusions, cavities generated at the interface between the mother phase steel and the oxide inclusions, and the crystals inside the oxide inclusions And a cavity generated at the interface between the crystal and the crystal and the amorphous cannot be suppressed. As a result, it was found that desired rolling fatigue characteristics could not be ensured.

  Furthermore, in order to improve the machinability, it was considered important to appropriately control non-metallic inclusions. If only the improvement of the machinability is considered, it has been conventionally proposed to optimize the chemical composition of the steel material. However, from the viewpoint of controlling the composition of the oxide inclusions, it is difficult to greatly change the chemical composition of the steel material. Therefore, the present inventors have studied to improve the machinability by controlling the nonmetallic inclusions generated in the steel material.

  As described above, fatigue peeling (rolling fatigue damage) starting from non-metallic inclusions in steel is known as one of the factors affecting the rolling fatigue characteristics. For such fatigue peeling, the predicted value of the square root (√area max) of the projected area of the maximum sulfide inclusion in the evaluation area (area) based on the extreme value statistical method (hereinafter referred to as “sulfide inclusion”). It is also known that it is effective to reduce (sometimes referred to as a predicted value of √area max) (that is, to reduce the size of sulfide inclusions (√area max)).

  However, as a result of repeated studies by the present inventors, it has been found that sulfide inclusions are effective in improving machinability, although they adversely affect rolling fatigue characteristics. That is, from the viewpoint of improving rolling fatigue characteristics, it was effective to reduce the predicted value of sulfide inclusions (√area max), but it was found that the machinability deteriorated (the test in Table 2 below). No. 15, 16). On the other hand, from the viewpoint of improving machinability, it was effective to increase the predicted value of sulfide inclusions (√area max), but it was found that the rolling fatigue characteristics deteriorated (the test shown in Table 2 below). No. 17, 19).

  As a result of further research, the present inventors have optimized the predicted value of sulfide inclusions (√area max) while controlling the oxide inclusions to a predetermined composition, so that rolling fatigue characteristics are improved. The present invention has been completed by finding that a steel material for bearings having both the characteristics of cutting and machinability can be provided.

  The present invention has been made on the basis of such knowledge, and its specific configuration is as follows.

  First, the chemical component composition of the steel material of the present invention will be described.

C: 0.8 to 1.1%
C is an essential element for increasing the quenching hardness and maintaining the strength at room temperature and high temperature to impart wear resistance. In order to exert such effects, it is necessary to contain C at least 0.8% or more. However, if the C content exceeds 1.1% and becomes excessive, giant carbides are easily generated in the core of the bearing, which adversely affects rolling fatigue characteristics. The preferable lower limit of the C content is 0.85% or more, more preferably 0.90% or more, and the preferable upper limit is 1.05% or less, more preferably 1.0% or less.

Si: 0.15-0.8%
In addition to effectively acting as a deoxidizing element, Si has an effect of increasing hardness by increasing resistance to quenching and tempering. In order to effectively exhibit these effects, the Si content needs to be 0.15% or more. However, if the Si content is excessive and exceeds 0.8%, not only the die life is reduced during forging, but also the cost is increased. The preferable lower limit of the Si content is 0.20% or more, more preferably 0.25% or more, and the preferable upper limit is 0.7% or less, more preferably 0.6% or less.

Mn: 0.10 to 1%
Mn is an element that improves the solid solution strengthening and hardenability of the steel matrix. When the Mn content is less than 0.10%, the effect is not exhibited. When the Mn content is more than 1%, the content of MnO, which is a lower oxide, is increased, the rolling fatigue characteristics are deteriorated, and the machinability is remarkably lowered. To do. The minimum with preferable Mn content is 0.2% or more, More preferably, it is 0.3% or more, and a preferable upper limit is 0.8% or less, More preferably, it is 0.6% or less.

P: 0.05% or less (excluding 0%)
P is an impurity element that segregates at the grain boundaries and adversely affects the rolling fatigue characteristics. In particular, when the P content exceeds 0.05%, the rolling fatigue characteristics are significantly deteriorated. Therefore, it is necessary to suppress the P content to 0.05% or less. Preferably it is 0.03% or less, more preferably 0.02% or less. In addition, P is an impurity inevitably contained in the steel material, and it is difficult to make the amount 0% in industrial production.

S: 0.005 to 0.015%
S is an element that forms sulfide inclusions (MnS), and is an effective element for improving the machinability. In order to acquire such an effect, it is necessary to contain S 0.005% or more. However, when the S content becomes excessive and exceeds 0.015%, coarse sulfides remain in the steel material, and the rolling fatigue characteristics deteriorate. Therefore, the S content must be suppressed to 0.015% or less. The preferable lower limit of the S content is 0.006% or more, more preferably 0.007% or more, and the preferable upper limit is 0.013% or less, more preferably 0.011% or less.

Cr: 1.3-1.8%
Cr is an element that improves the hardenability of the steel material and increases the hardness of the carbide, and is effective in improving the wear resistance of the part. In order to acquire such an effect, it is necessary to contain 1.3% or more of Cr. However, when the Cr content is excessive, coarse carbides are generated, which deteriorates rolling fatigue characteristics and machinability. Therefore, the Cr content needs to be suppressed to 1.8% or less. The minimum with preferable Cr content is 1.35% or more, More preferably, it is 1.4% or more, A preferable upper limit is 1.7% or less, More preferably, it is 1.6% or less.

Al: 0.0002 to 0.005%
Al is an undesirable element, and in the steel material of the present invention, it is necessary to reduce Al as much as possible. Therefore, deoxidation treatment by addition of Al after oxidative refining is not performed. When the Al content increases, especially when it exceeds 0.005%, the amount of hard oxides mainly composed of Al ₂ O ₃ increases, and even after the rolling down, the oxides become coarse oxides in the steel. Since it remains, the rolling fatigue characteristics deteriorate. Therefore, the Al content is 0.005% or less, preferably 0.002% or less, more preferably 0.0015% or less. However, if the Al content is less than 0.0002%, the Al ₂ O ₃ content in the oxide becomes too small, and a crystal phase containing a large amount of SiO ₂ is generated. Moreover, in order to control the Al content to less than 0.0002%, it is necessary to reduce not only the components in steel but also the Al content in the flux in order to suppress the mixing of Al. In bearing steel, which is a steel, a flux with a low Al content is very expensive and not economical. Therefore, the lower limit of the Al content is 0.0002% or more, preferably 0.0005% or more.

Ti: 0.0005 to 0.010%
Ti is an element that plays a particularly important role in the present invention. By adding a predetermined amount of Ti and appropriately controlling the TiO ₂ content in the oxide, problems that have been difficult to solve can be solved, and rolling fatigue characteristics are further improved. That is, crystallization during hot working of SiO ₂ -containing oxide inclusions obtained in Si deoxidized steel, which was a difficult problem to solve, cavities generated at the interface between the parent phase steel and oxide inclusions, It is possible to suppress cavities generated in the oxide inclusions that are polycrystalline. Furthermore, the predetermined amount of Ti effectively works to reduce the aspect ratio, and thereby rolling fatigue characteristics are further improved. In order to obtain such an effect, the Ti content needs to be 0.0005% or more. However, if the Ti content increases and exceeds 0.010%, a TiO ₂ -based oxide is generated alone as a crystal phase. Therefore, the Ti content is set to 0.010% or less. The preferable lower limit of the Ti content is 0.0008% or more, more preferably 0.0011% or more, and the preferable upper limit is 0.0050% or less, more preferably 0.0030% or less.

N: 0.010% or less (excluding 0%)
It is recommended that N be reduced as much as possible in order to generate TiN and deteriorate rolling fatigue characteristics. Therefore, the upper limit of the N content is 0.010% or less, preferably 0.008% or less, more preferably 0.006% or less.

Ca: 0.0002 to 0.002%
Ca is effective in controlling the CaO content in the oxide, softening oxide inclusions, and improving rolling fatigue characteristics. In order to exert such effects, the Ca content is set to 0.0002% or more. However, if the Ca content becomes excessive and exceeds 0.002%, the proportion of CaO in the oxide composition becomes too high, the oxide becomes hard, and adversely affects the rolling fatigue characteristics. Therefore, the Ca content is set to 0.002% or less. The lower limit of the preferable Ca content is 0.0003% or more, more preferably 0.0005% or more, and the preferable upper limit is 0.001% or less, more preferably 0.0008% or less.

O: 0.0030% or less (excluding 0%)
O is an undesirable impurity element. When the content of O increases, particularly exceeding 0.0030%, a coarse oxide is likely to be formed, and remains as a coarse oxide even after rolling, which adversely affects rolling fatigue characteristics. Therefore, the upper limit of the O content is 0.0030% or less. A preferable upper limit is 0.0025% or less, more preferably 0.0020% or less.

  The contained elements specified in the present invention are as described above, and the balance is iron and inevitable impurities. As the inevitable impurities, mixing of elements (for example, As, H, and N) that are brought in depending on the situation of raw materials, materials, manufacturing facilities, and the like can be allowed. In the present invention, inevitable impurities other than those described above may be included in a range that does not affect the above-described characteristics of the present invention. Inevitable impurities are allowed to be, for example, up to 0.10%.

  In the present invention, the following selective elements (Cu, Ni, Mo) can be positively contained within a specified range in order to improve rolling fatigue characteristics.

Selected from the group consisting of Cu: 0.5% or less (not including 0%), Ni: 0.5% or less (not including 0%), and Mo: 0.5% or less (not including 0%) These elements may be used alone or in combination of two or more.

Cu: 0.5% or less (excluding 0%)
Cu is an element that effectively acts to improve corrosion resistance. In order to obtain such an effect, the amount of Cu is preferably 0.15% or more, more preferably 0.2% or more. On the other hand, when Cu is excessive, the hot rollability is lowered, and cracks are likely to occur during production. Therefore, the amount of Cu is preferably 0.5% or less, more preferably 0.4% or less, and more preferably 0.3% or less.

Ni: 0.5% or less (excluding 0%)
Ni is an element having the same effect as Cu in terms of corrosion resistance, and is an element effective for improving impact properties by increasing toughness. In order to obtain such an effect, the amount of Ni is preferably 0.15% or more, more preferably 0.2% or more. On the other hand, Ni is expensive, and it is desirable to reduce it from the viewpoint of cost. Moreover, when Ni becomes excess, cutting workability will fall. Therefore, the amount of Ni is preferably 0.5% or less, more preferably 0.4% or less, and more preferably 0.3% or less.

Mo: 0.5% or less (excluding 0%)
Mo is an effective element in terms of toughness with Ni, and is an effective element for improving toughness. In order to obtain such an effect, the Mo amount is preferably 0.15% or more, more preferably 0.2% or more. On the other hand, Mo is expensive and it is desirable to reduce it from a cost viewpoint. Therefore, the Mo amount is preferably 0.5% or less, more preferably 0.45% or less.

Next, oxide inclusions present in the steel material will be described. As described above, in the present invention, with respect to the oxide contained in the steel, the average composition of the oxide is a ratio (mass%) to the total oxide (100%), CaO: 20 to 50%, Al ₂ O _3. 15 to 50%, SiO ₂ : 20 to 62%, TiO ₂ : 3 to 10%, and the remainder is characterized by being made of other oxides.

CaO: 20-50%
CaO is a basic oxide, and when it is contained together with SiO ₂ that is an acidic oxide, the liquidus temperature of the oxide is lowered, and there is an effect of suppressing crystallization of the oxide. Such an effect is obtained by controlling the CaO content in the average composition of the oxide to 20% or more. However, if the CaO content is too high, the oxide will crystallize, so it is necessary to make it 50% or less. The minimum with preferable CaO content in an oxide is 22% or more, More preferably, it is 25% or more, A preferable upper limit is 43% or less, More preferably, it is 41% or less.

Al ₂ O ₃ : 15-50%
When the content of the oxide in the average composition exceeds 50%, the Al ₂ O ₃ (corundum) phase is crystallized in the rolling temperature range, or the MgO · Al ₂ O ₃ (spinel) phase is crystallized together with MgO. These solid phases are hard and difficult to break during rolling and cold working, and are present as coarse inclusions, and therefore deteriorate the rolling fatigue characteristics. From such a viewpoint, the Al ₂ O ₃ content in the average composition of the oxide is set to 50% or less. Preferably it is 43% or less, More preferably, it is 41% or less. On the other hand, if the Al ₂ O ₃ content in the oxide inclusions is too low, CaO and SiO ₂ become hard inclusions mainly, and the rolling fatigue characteristics are deteriorated. Therefore, the content of Al ₂ O ₃ is set to 15% or more. A preferable lower limit is 17% or more, and more preferably 20% or more.

SiO ₂ : 20 to 62%
SiO ₂ is an acidic oxide and is an essential component for softening oxide inclusions and improving the rolling fatigue life. In order to exhibit such an effect effectively, it is necessary to contain 20% or more of SiO _{2 in the} oxide. However, if the SiO ₂ content exceeds 62%, a crystal phase containing a large amount of SiO ₂ is generated and cavities are formed, so that the rolling fatigue characteristics are deteriorated. The preferable lower limit of the SiO ₂ content in the oxide is 25% or more, more preferably 30% or more, and the preferable upper limit is 50% or less, more preferably 45% or less.

TiO ₂ : 3 to 10%
TiO ₂ is an oxide component that characterizes the present invention. When it is contained together with SiO ₂ that is an acidic oxide, TiO ₂ is separated into two phases of TiO ₂ concentrated phase (A phase) and SiO ₂ concentrated phase (B phase). Both phases have the effect of suppressing hardening. As a result, suppression of crystallization during hot working of SiO ₂ -containing oxide inclusions obtained from Si deoxidized steel, suppression of cavities generated at the interface between the parent phase steel and oxide inclusions, It is possible to suppress the cavities generated in the oxide inclusions that are the crystalline bodies, and the rolling fatigue characteristics are further improved. In addition, the softening of the inclusions reduces the wear of the cutting tool and improves the cutting workability. Such an effect can be obtained by controlling the TiO ₂ content in the average composition of the oxide to 3% or more. However, if the TiO ₂ content is too high, a TiO ₂ -based oxide is generated alone as a crystal phase, a cavity is formed, and the rolling fatigue characteristics deteriorate, so the content is made 10% or less. The preferable lower limit of the TiO ₂ content in the oxide is 4% or more, more preferably 5% or more, and the preferable upper limit is 8% or less, more preferably 7% or less.

As described above, the oxide contained in the steel material of the present invention is basically composed of CaO, Al ₂ O ₃ , SiO ₂ , and TiO ₂ , but it is intended that other oxides may be contained. Other oxides may be included as long as desired characteristics are obtained without adversely affecting the effect of the oxide inclusions. The total amount (mass%) of the other oxides is preferably controlled to 20% or less, more preferably 15% or less, still more preferably 10% or less, and most preferably 5% or less as a ratio to the total oxides. It is preferable.

Predicted value of square root (√area max) of projected area of maximum sulfide inclusion (predicted value of √area max of sulfide inclusion): 50 to 150 μm
Sulfide inclusions are non-metallic inclusions that affect both rolling fatigue characteristics and machinability. In order to obtain the effect of improving the machinability by sulfide inclusions, the predicted value of sulfide inclusions (√area max) needs to be 50 μm or more. Even if the predicted value of sulfide inclusions (√area max) is 50 μm or more, sulfide inclusions are softer than oxide inclusions, and the composition of oxide inclusions is as described above. If properly controlled, rolling fatigue failure can be suppressed. However, if the predicted value of sulfide inclusions (√area max) becomes larger than 150 μm, it is stretched in the manufacturing process (rolling) and stress concentrates around the sulfide inclusions to cause rolling fatigue characteristics. Decreases. Therefore, the predicted value of sulfide inclusions (√area max) needs to be 150 μm or less. The predicted value of sulfide inclusions (√area max) is preferably 60 μm or more, more preferably 70 μm or more, preferably 130 μm or less, more preferably 100 μm or less.

  Next, a method for producing the bearing steel material according to the present invention will be described.

  The steel material for bearings of the present invention can be manufactured based on a conventionally known manufacturing process. That is, steel is melted (melting process), and a slab is cast according to a conventional method (casting process). The obtained slab is subjected to soaking (corresponding to a solution treatment), then hot forged, and cooled to room temperature (block rolling process). Then, the steel material for bearings is obtained by reheating and hot working (for example, hot rolling) (bar rolling process).

  In the above conventional manufacturing process, in the present invention, in particular, from the viewpoint of controlling the average composition of oxide inclusions and the predicted value of sulfide inclusions (√area max), pay attention to the melting and casting processes. In other steps, a method usually used for producing bearing steel can be appropriately selected and used.

Melting process:
First, when steel is melted, deoxidation by Si addition is performed without performing the deoxidation treatment by Al addition that is usually performed. At the time of melting, in order to control the respective contents of CaO and Al ₂ O ₃ , the Al content contained in the steel is 0.0002 to 0.005% as described above, and the Ca content is It controls to 0.0002 to 0.002% respectively.

Further, no particular limitation is imposed on the method of controlling the TiO _2, according to the method commonly used in the art, in the step of melting, as the Ti content contained in the steel described above, 0.0005 to 0.010% Ti may be added so as to be controlled within the range. The method of adding Ti is not particularly limited, and for example, it may be adjusted by adding an iron-based alloy containing Ti, or the Ti concentration in the molten steel may be controlled by controlling the slag composition.

SiO ₂ is obtained by controlling other oxides as described above.

  Furthermore, in the present invention, at the time of melting, in order to control the formation of sulfide inclusions, the S content contained in the steel is controlled to 0.005 to 0.015% as described above. Moreover, what is necessary is just to adjust an additive element etc. suitably at the time of melting so that it may become a chemical component composition of a desired steel material.

Casting process:
After smelting steel and adjusting a chemical component composition, a slab is produced. In the present invention, by appropriately controlling the average cooling rate from the solidification start temperature (liquidus temperature) to the solidification end temperature (solidus temperature) of the molten steel (hereinafter referred to as “average cooling rate during casting”), The predicted value of sulfide inclusions (√area max) can be controlled within the desired range. If the average cooling rate at the time of casting is too high, MnS becomes finer, and the predicted value of sulfide inclusions (√area max) in the steel for bearings obtained through the following steps tends to be less than 50 μm. On the other hand, if the average cooling rate is too slow, coarse sulfide inclusions are likely to crystallize between the branches of the solidified structure, and the sulfide inclusions are stretched in the rolling process described later. The predicted value of the object (√area max) exceeds 150 μm. Therefore, in order to keep the predicted value of sulfide inclusions (√area max) in the steel for bearings within the predetermined range, the average cooling rate during casting is preferably 200 ° C./hour or more, more preferably 250 ° C. / Hour or more, more preferably 300 ° C./hour or more, preferably 700 ° C./hour or less, more preferably 650 ° C./hour or less, further preferably 600 ° C./hour or less. The method for adjusting the cooling rate is not particularly limited, and may be a known method. For example, the amount of cooling water or the cooling time may be adjusted.

Split rolling process:
Subsequently, the slab is subjected to soaking treatment and then hot forging. The soaking temperature is not particularly limited. For example, the slab may be heated to about 1100 to 1300 ° C., held in the temperature range for about 30 to 10 hours, hot forged, and cooled to room temperature by air cooling or the like.

Bar rolling process:
The steel slab (billet) after hot forging is reheated and hot processed (for example, hot rolling such as bar rolling) to obtain the steel for bearing of the present invention. In the present invention, the temperature at the time of reheating is not particularly limited. For example, hot rolling may be performed by heating to about 900 ° C to 1100 ° C.

  The shape of the steel material for bearings after hot working is not particularly limited, and may be a desired shape (for example, wire rod or steel bar).

  The steel material for bearings is controlled in the requirements specified in the present invention, that is, the predicted values of chemical composition, oxide-based average composition, and sulfide-based inclusion (√area max). There is an effect excellent in workability.

  The steel material for bearings of the present invention thus obtained is subjected to spheroidizing annealing to soften the steel material, and then subjected to cold working (for example, cold forging), cutting work, polishing work, and the like. To the part shape. Thereafter, quenching and tempering are performed to obtain a desired hardness, and then finish polishing or the like is performed as necessary to obtain a bearing component.

  The shape of the steel material stage includes both a linear shape and a rod shape applicable to such production, and the size can be appropriately determined according to the final product.

  Moreover, the conditions at the time of manufacturing a bearing component are not specifically limited, What is necessary is just to carry out on well-known conditions. For example, the spheroidizing annealing may be performed by a general slow cooling method, that is, after holding in a temperature range of about 720 to 790 ° C. for 3 to 10 hours, and then cooling at an average cooling rate of 10 to 15 ° C./min. Moreover, what is necessary is just to cool an oil treatment, for example, after heating to 800-850 degreeC. The subsequent tempering process should just cool after heating to 140-200 degreeC, for example.

  Examples of the bearing parts include rollers, needles, balls, and races. The bearing parts thus obtained have rolling fatigue characteristics and cutting workability that are superior to those of the conventional bearing parts.

  Hereinafter, the present invention will be described more specifically with reference to examples. The present invention is not limited to the following examples, and can be implemented with appropriate modifications within a range that can be adapted to the purpose described above and below. They are all included in the technical scope of the present invention.

Preparation of Test Pieces Using a small melting furnace, test materials having various chemical composition compositions shown in Table 1 below (the balance is iron and inevitable impurities) were melted to prepare cast pieces (size: 230 mm in diameter). In melting, Si deoxidation treatment was performed without performing the Al deoxidation treatment that is usually performed. At this time, the molten steel was cooled from the solidification start temperature (liquidus temperature) to the solidification end temperature (solidus temperature) at the average cooling rate shown in Table 2 (in the table, “average cooling rate during casting”).

  The obtained slab was heated to 1250 ° C. and held at that temperature for 1 hour, then hot forged at 1200 ° C. and cooled to room temperature. Subsequently, it was reheated to 1000 ° C. and hot-rolled (900 to 1000 ° C.) to produce a round steel bar (bearing steel: test piece). Using this test piece, the average composition of oxide inclusions and the predicted value of sulfide inclusions (√area max) were measured.

  Further, the above round bar steel was cut and spheroidized annealed (held at 770 ° C. for 6 hours, then cooled to 680 ° C. at an average cooling rate of −10 ° C./hr and then allowed to cool) to soften the steel material. Then, it processed into the test piece (diameter 60mm, thickness: 5mm) for a disk-shaped thrust type | mold rolling fatigue test. The test piece was heated at 840 ° C. for 30 minutes and then oil-quenched, and tempered at 160 ° C. for 120 minutes. Finally, finish polishing (surface roughness: Ra 0.1 μm) was performed to produce a thrust type rolling fatigue test piece, and the rolling fatigue life was evaluated.

  Further, after cutting the above round bar steel (65 mm diameter bearing steel: test piece) and softening the steel by spheroidizing annealing under the above conditions, the outer peripheral portion is cut by 1.5 mm on one side and a cutting test piece (Diameter 62 mm: Length 250 mm) was prepared and the cutting tool life was evaluated.

(Method for measuring the average composition of oxide inclusions)
In measuring the composition (average composition) of oxide inclusions, the following test pieces were used. First, test specimens (size: 20 × 20 × 10 mm) were prepared so that a cross section in the rolling direction could be observed at the D / 2 position (D is a diameter) from the surface of the round bar steel (bearing steel) obtained as described above. Cut out, one micro sample (structure observation sample) was cut out, and the cross section was polished. The average composition of oxide inclusions was observed using an electron probe microprobe X-ray analyzer (EPMA, trade name “JXA-8500F”) manufactured by JEOL Datum. The component composition was quantitatively analyzed for oxide inclusions having a thickness of 1 μm or more. At this time, the observation area was set to 100 mm ² (polished surface), and the component composition at the center of the inclusion was quantitatively analyzed by wavelength dispersion spectroscopy of characteristic X-rays. The analysis target elements are Ca, Al, Si, Ti, Mn, Mg, Na, Cr, Zr, and O (oxygen), and the relationship between the X-ray intensity and the element concentration of each element using a known substance as a calibration curve in advance. The average inclusion composition was determined by quantifying the amount of elements contained in each sample from the X-ray intensity obtained from the inclusions to be analyzed and the calibration curve, and arithmetically averaging the results. .

(Measurement method of predicted value of sulfide inclusion (√area max))
The maximum size of the sulfide inclusions was calculated using an extreme value statistical method using a micro sample cut out from the round bar steel test piece (size: 20 × 20 × 10 mm). The maximum size of the sulfide inclusions was assumed to follow an extreme value distribution (here, Weibull distribution), and was calculated using an extreme value statistics method (Extreme Value Statistics Method). First, the surface of the micro sample is observed using an optical microscope (magnification 100 × 20 fields: 15 mm ² per field, total field area 300 mm ² ). In each field of view, the square root (√area max) of the projected area of the largest sulfide inclusion is measured. Using the measured value of √area max of the maximum sulfide inclusions of 20 fields of view and using the extreme probability paper, the standardized variable is Y = 8.11 (predicted area: equivalent to 1 million mm ²⁾ ) As the predicted maximum size. In addition, the said measuring method is well-known, What is necessary is just to set in accordance with a conventional method about measuring conditions other than the above. Regarding the measurement method, for example, “Problem of JIS point calculation method and inclusion evaluation by extreme value statistical method and its application, Iron and Steel Vol. 79 (1993) No. 12” are also references. In this example, the predicted value of sulfide inclusions (√area max) was evaluated as 50 to 150 μm as acceptable.

(Rolling fatigue characteristics)
The rolling fatigue life of the thrust rolling fatigue specimen was measured to evaluate the rolling fatigue characteristics. Using a thrust type rolling fatigue tester, the rolling fatigue test was performed 16 times for each test piece under the conditions of repetition rate: 1500 rpm, surface pressure: 5.3 GPa, number of cancellations: 2 × 10 ⁸ times. The rolling fatigue life (L ₁₀ life: the number of stress repetitions until fatigue failure at a cumulative failure probability of 10% obtained by plotting on the wiper probability paper) was measured. When the rolling fatigue life (L ₁₀ life) exceeded 15 × million cycles (cycle), it was evaluated that the rolling fatigue characteristics were excellent (accepted). In addition, the case where the rolling fatigue life was 20 × 1 million times or more was evaluated as being superior in rolling fatigue characteristics.

(Machinability)
For the evaluation of cutting workability, a cutting tool was turned using a cemented carbide tool (P10 type: JIS B 4053 1998), and the amount of tool wear was measured. Cutting conditions were cutting speed: 100 m / min, feed: 0.3 mm / rev, cutting depth: 1.5 mm, and no cutting oil (dry type).

  The test piece was cut for a certain period of time, and the machinability was evaluated at the time (minutes) when the flank wear amount of the tool was 0.2 mm. When the cutting tool life exceeded 15 minutes, it was evaluated that the cutting workability was excellent (accepted). Moreover, it evaluated that the case where a cutting tool lifetime was 20 minutes or more was more excellent in cutting workability.

  These results can be considered as follows.

  First, test no. 1 to 14 all satisfy the chemical composition of the steel material defined in the present invention, and the average composition of oxide inclusions and the predicted value of sulfide inclusions (√area max) are also appropriately controlled. This is an example. It can be seen that these are all excellent in rolling fatigue characteristics and cutting workability.

  On the other hand, the following test No. Since Nos. 15 to 25 do not satisfy any of the requirements of the present invention, the rolling fatigue characteristics and / or the machinability deteriorated.

  Test No. 15 and 16 are examples in which both exceed the average cooling rate during forging recommended in the present invention. Therefore, the predicted value of sulfide inclusions (√area max) is too low, and the machinability is low.

  Test No. 17 is an example in which the average cooling rate during forging recommended in the present invention was lower. Therefore, the predicted value of sulfide inclusions (√area max) is too large, and the rolling fatigue characteristics are low.

  Test No. 18 is an example where S falls below the definition of the present invention. In this example, since the amount of S was too small, the predicted value of sulfide inclusions (√area max) was too small and the machinability was low.

  Test No. 19 is an example in which S exceeds the definition of the present invention. In this example, since the amount of S was too large, the predicted value of sulfide inclusions (√area max) was too large, and the rolling fatigue characteristics were low.

Test No. No. 20 is an example in which Al falls below the definition of the present invention. In this example, the amount of Al was too small to properly control the average composition of oxide inclusions. Therefore, the oxide inclusions have a composition mainly composed of hard SiO ₂ and have low rolling fatigue characteristics.

Test No. 21 is an example in which Al exceeds the definition of the present invention. In this example, the amount of Al was too large, and the average composition of oxide inclusions could not be controlled appropriately. Therefore, the oxide inclusions cannot be sufficiently softened due to a small amount of SiO _{2, and} are too hard because Al ₂ O ₃ is too large. As a result, the rolling fatigue characteristics were low.

Test No. 22 is an example in which Ti falls below the definition of the present invention. In this example, the amount of Ti was too small, and the average composition of oxide inclusions could not be controlled appropriately. For this reason, the oxide inclusions have too little TiO ₂ , cannot suppress the hardening, and have low rolling fatigue characteristics.

Test No. 23 is an example in which Ti exceeds the definition of the present invention. In this example, the amount of Ti was too large, and the average composition of oxide inclusions could not be controlled appropriately. Therefore, the oxide inclusions have too much TiO ₂ , and the generation of cavities at the interface between the mother phase and the oxide inclusions and inside the oxide inclusions cannot be sufficiently suppressed. Was low.

  Test No. 24 is an example in which Ca falls below the definition of the present invention. In this example, the amount of Ca was too small to properly control the average composition of oxide inclusions. Therefore, the oxide inclusions have too little CaO and cannot be controlled to be soft oxide inclusions, and the rolling fatigue characteristics are low.

  Test No. 25 is an example in which Ca exceeds the definition of the present invention. In this example, the amount of Ca was too large, and the average composition of oxide inclusions could not be controlled appropriately. Therefore, the oxide inclusions contained too little CaO, the oxides were hardened, and the rolling fatigue characteristics were low.

Claims (3)

C: 0.8 to 1.1% (% means “mass%”, the same applies to the chemical composition)
Si: 0.15 to 0.8%,
Mn: 0.10 to 1%,
P: 0.05% or less (excluding 0%),
S: 0.005 to 0.015%,
Cr: 1.3-1.8%,
Al: 0.0002 to 0.005%,
Ti: 0.0005 to 0.010%,
N: 0.010% or less (excluding 0%),
Ca: 0.0002 to 0.002%, and O: 0.0030% or less (excluding 0%)
The balance consists of iron and inevitable impurities,
The average composition of oxide inclusions contained in the steel is mass%,
CaO: 20 to 50%,
Al ₂ O ₃ : 15-50%,
SiO _2: 20~62%, and TiO _2: containing 3-10%, and,
A steel material for bearings having excellent rolling fatigue characteristics and excellent machinability, wherein the predicted value of the square root (√area max) of the projected area of the largest sulfide inclusion is 50 to 150 μm. Furthermore,
Cu: 0.5% or less (excluding 0%),
Ni: 0.5% or less (not including 0%), and Mo: 0.5% or less (not including 0%)
The bearing steel material according to claim 1, comprising at least one selected from the group consisting of:   A bearing component comprising the steel for bearing according to claim 1.