JP2009263767A - Method for manufacturing high-strength case hardened steel part - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a method for manufacturing high-strength case hardened steel parts which, when worked to gears, are higher in bending fatigue strength of dedendum than the conventional gears, are further excellent in face pressure fatigue strength as well, and even more, enable mass production. <P>SOLUTION: The steel raw material consists of texture containing, by mass%, 0.1 to 0.35% C, 0.05 to 1.1% Si, 0.5 to 2.0% Mn, 0.5 to 2.5% Cr, ≤0.015% P, ≤0.02% S, 0.02 to 0.05% Al, 0.008 to 0.02% N, and ≤0.0015% O within a range satisfying the following formulas (1), (2), consisting of the balance Fe and inevitable impurities. In addition, the maximum diameter of oxide-based non-metallic inclusions is ≤19 μm. The steel raw material is subjected to forging or machining, then to carburizing treatment or carbonitriding treatment to make the C content of the surface layer 0.7 to 0.9%, and further to perform shot peening of an arc height: 0.1 to 0.5 mmN such that the face roughness of a surface layer is made 0.5 to 1.5 μm in arithmetic average roughness.(1): 3.0≥ä([%Si]/2)+[%Mn]+[%Cr]}≥2.4.(2): 2.5≥[%Al]/[%N]≥1.8. <P>COPYRIGHT: (C)2010,JPO&INPIT

Description

  The present invention relates to a method for producing a high-strength case-hardened steel part suitable for use in high-strength gears having high bending fatigue strength and surface pressure fatigue strength, which are used in automobiles and various industrial equipment.

  In recent years, gears used in automobiles and the like have been required to be smaller in size as the weight of the vehicle body has been reduced due to energy saving, and the load on the gears has increased as the output of the engine has increased. Yes. The durability of the gear is mainly determined by the bending fatigue failure of the tooth root and the surface pressure fatigue failure of the tooth surface.

  Conventionally, gears have been manufactured by preparing gear materials using case-hardened steel defined by JIS SCM420H, SCM822H, etc., and subjecting the gear materials to surface treatment such as carburization. However, since such gears cannot withstand use under high stress, the tooth root bending fatigue strength and pitting resistance can be reduced by changing steel materials, heat treatment methods, surface work hardening, etc. I tried to improve the sex.

For example, in Patent Document 1, while reducing Si in steel and controlling Mn, Cr, Mo and Ni, the grain boundary oxide layer on the surface after carburizing heat treatment is reduced, and the occurrence of cracks is reduced. Moreover, by suppressing the generation of an incompletely hardened layer, the reduction of surface hardness is suppressed to increase the fatigue strength, and further Ca is added to control the elongation of MnS that promotes the generation and propagation of cracks. Is disclosed.
Patent Document 2 discloses a method for increasing the temper softening resistance using a steel material to which Si is added in an amount of 0.25 to 1.50%.

Japanese Patent Publication No. 07-122118 Japanese Patent No. 2945714

However, both of Patent Documents 1 and 2 described above have the following problems.
According to Patent Document 1, since the grain boundary oxide layer and the incompletely hardened layer are reduced by reducing Si, it is possible to suppress the occurrence of bending fatigue cracks at the tooth root. However, the resistance to temper softening decreases and the occurrence of fracture shifts from the tooth base to the tooth surface. As a result, temper softening due to frictional heat on the tooth surface cannot be suppressed, and the surface softens. There has been a problem that it is likely to occur.

  In Patent Document 2, Si or the like is added to increase the temper softening resistance, while the carburizing method is limited to vacuum carburizing or plasma carburizing to suppress the progress of grain boundary oxidation. The method is disadvantageous in that the production cost increases, and is not suitable for mass production.

  The present invention has been developed in view of the above circumstances, and is suitable for use in high-strength gears and the like that have higher bending fatigue strength at the root than conventional gears and also have excellent surface fatigue properties. It is an object of the present invention to propose an advantageous method for producing a high-strength case-hardened steel part that can be made into a steel.

As a result of intensive studies to solve the above problems, the inventors have obtained the following knowledge.
a) By increasing the amount of Si, Mn, and Cr in the steel material, the temper softening resistance is increased, and if the softening due to heat generation on the gear contact surface is suppressed, the generation of cracks in the tooth surface that occurs when the gear is driven can be suppressed. it can.
b) For grain boundary oxide layers that can be the starting point of bending fatigue and fatigue cracks, by adding more than a certain amount of Si, Mn, Cr, the growth direction of the grain boundary oxide layer is changed from the depth direction to the surface density increasing direction. change. Therefore, since there is no oxide layer grown in the depth direction to be a starting point, it becomes difficult to be a starting point for bending fatigue and fatigue cracks. Furthermore, this oxide layer is easy to peel off, and is almost unpeeled by shot peening, so there is no influence.
c) As described in the above a and b, Si, Mn, and Cr are effective for improving the temper softening resistance and controlling the grain boundary oxide layer. In order to achieve both of these effects, Si, Mn, It is necessary to strictly control the content of Cr.
d) In order to obtain high fatigue strength by increasing the surface compressive residual stress by shot peening, it is necessary to reduce not only the amount of oxygen in the steel but also the maximum value of oxide inclusions.
e) In order to improve the rolling fatigue life by shot peening, there is an appropriate arc height value and an appropriate value of surface roughness caused by shot peening.
The present invention is based on the above findings.

That is, the present invention is, in mass%, C: 0.1 to 0.35%, Si: 0.05 to 1.1%, Mn: 0.5 to 2.0%, Cr: 0.5 to 2.5%, P: 0.015% or less, S: 0.02% or less, Al: 0.02 to 0.05%, N: 0.008 to 0.02% and O: 0.0015% or less are contained within a range satisfying the following formulas (1) and (2), and the balance is Fe and inevitable impurities composition. In addition, after forging or machining a steel material having a maximum diameter of oxide-based nonmetallic inclusions of 19 μm or less, carburization or carbonitriding with a C content of 0.7 to 0.9% by mass is performed. Further, arc height: 0.1 to 0.5 mmN shot peening is performed, and the surface roughness of the surface layer is 0.5 to 1.5 μm in terms of arithmetic average roughness Ra. .
Record
3.0 ≧ {([% Si] / 2) + [% Mn] + [% Cr]} ≧ 2.4 --- (1)
2.5 ≧ [% Al] / [% N] ≧ 1.8 --- (2)
However, [% M] is the content of element M (% by mass)

  According to the present invention, for example, when processed into a gear, not only the bending fatigue characteristics of the tooth root but also the high-strength case-hardened steel parts excellent in the tooth surface fatigue characteristics can be obtained under mass production. it can.

The present invention will be specifically described below.
First, the reason why the component composition of the steel slab is limited to the above range in the present invention will be described. Unless otherwise specified, “%” in relation to ingredients means mass%.
C: 0.1-0.35%
In order to increase the hardness of the central part by quenching after carburizing treatment, 0.1% or more of C is required, but if the content exceeds 0.35%, the toughness of the core part decreases, so the C content is 0.1 to 0.35% It was limited to the range. Preferably it is 0.1 to 0.3% of range.

Si: 0.05-1.1%
Si is the most important element in the present invention. Si is an element that increases the softening resistance in the temperature range of 200 to 300 ° C. that is considered to be reached during the rolling of gears and the like, and at least 0.05% addition is indispensable for exerting the effect. Preferably 0.3% or more is added. However, Si, on the other hand, is a ferrite stabilizing element, and excessive addition raises the Ac ₃ transformation point, and ferrite tends to appear in the core with a low carbon content in the normal quenching temperature range, resulting in a decrease in strength. Invite. Excessive addition also has the disadvantage of hardening the steel before carburizing and degrading the machinability. In this respect, if the Si content is 1.1% or less, the above-described adverse effects do not occur, so the Si content is limited to a range of 0.05 to 1.1%. Preferably it is 0.3 to 1.1% of range.

Mn: 0.5-2.0%
Mn is an element effective for hardenability, and requires addition of at least 0.5%. However, Mn tends to form an abnormal carburizing layer, and excessive addition causes an excessive amount of retained austenite and leads to a decrease in hardness, so the upper limit was made 2.0%. Preferably it is 0.5 to 1.5% of range.

Cr: 0.5-2.5%
Cr is an element effective for improving not only hardenability but also temper softening resistance. However, if the content is less than 0.5%, the effect of addition is poor. On the other hand, if it exceeds 2.5%, the effect of increasing softening resistance is The Cr content is limited to the range of 0.5 to 2.5% because it becomes saturated and rather easily forms a carburized abnormal layer. Preferably it is 0.5 to 2.0% of range.

P: 0.015% or less P is segregated at the grain boundary and lowers the toughness of the carburized layer and the core. Therefore, the lower the content, the better, but 0.015% is acceptable.

S: 0.02% or less S is an element that exists as sulfide inclusions and is effective in improving machinability. However, excessive addition causes a decrease in fatigue strength, so the upper limit was made 0.02%.

Al: 0.02 to 0.05%
Al is an element that combines with N to form AlN and contributes to the refinement of austenite crystal grains. To obtain this effect, 0.02% or more of addition is required, but the content is 0.05%. In order to promote the formation of Al ₂ O ₃ inclusions that are harmful to fatigue strength, the Al content is limited to a range of 0.02 to 0.05%.

N: 0.008 to 0.02%
N is an element that combines with Al to form AlN and contributes to the refinement of austenite crystal grains. Therefore, the appropriate addition amount is determined by the quantitative balance with Al, but 0.008% or more of addition is necessary to exert the effect. However, if added in excess, bubbles are generated in the steel ingot during solidification and deterioration of forgeability is caused, so the upper limit is made 0.02%. Preferably it is 0.01 to 0.015% of range.

O: 0.0015% or less O is an element that exists as an oxide inclusion in steel and impairs fatigue strength. A lower value is preferable, but 0.0015% is acceptable.

Although the proper composition range of the basic component of the present invention has been described above, in the present invention, it is not sufficient that each element simply satisfies the above range. For Si, Mn, Cr, Al, and N, It is important to satisfy the relationship of equations (1) and (2).
3.0 ≧ {([% Si] / 2) + [% Mn] + [% Cr]} ≧ 2.4 --- (1)
2.5 ≧ [% Al] / [% N] ≧ 1.8 --- (2)
However, [% M] is the content of element M (% by mass)

The above formula (1) is a factor affecting the hardenability and temper softening resistance.If the formula (1) is less than 2.4, the improvement effect of the hardenability and temper softening resistance is not sufficient, while 3.0 If it exceeds, not only the above improvement effect is saturated, but also the workability is deteriorated.
The above formula (2) is a factor that affects the refinement of austenite crystal grains, and if the value of formula (2) is less than 1.8, the effect of miniaturization is poor, while if it exceeds 2.5, the grain becomes easy In addition to coarsening, the workability is lowered due to the solid solution Al and N.

In the present invention, it is also important to control the size of oxide inclusions present in the material.
In other words, even if the amount of oxygen in the steel is reduced, if the maximum diameter of the oxide in the steel is large, improvement in surface pressure fatigue strength cannot be expected, so the maximum diameter of oxide inclusions present in the material is 19 μm or less. Limit to.
In order to adjust the size of the oxide inclusions within the above range, the RH degassing step is important, and the treatment time at this time is preferably 50 minutes or more.

Surface C concentration: 0.7-0.9%
Carburization increases the C content of the surface layer. As a result, the surface hardness is increased, and bending fatigue and surface fatigue strength are improved. However, if the C concentration of the steel sheet surface layer is less than 0.7%, the effect is not sufficient. On the other hand, if it exceeds 0.9%, cementite precipitates at the grain boundaries near the surface layer and becomes the starting point of fatigue. Reduces fatigue strength. Therefore, the surface layer C amount after carburizing is limited to a range of 0.7 to 0.9%.
The surface layer means from the steel plate surface to a depth of 50 μm.

Shot peening arc height: 0.1 to 0.5 mmN
Shot peening has the effect of further increasing bending fatigue strength and surface fatigue strength by applying compressive residual stress in the vicinity of the surface layer. When this treatment is performed, if the arc height is less than 0.1 mmN, compressive residual stress is applied too little, and sufficient improvement of bending fatigue strength and surface fatigue strength cannot be obtained. Since the bending fatigue strength and the contact pressure fatigue strength may be deteriorated, the arc height of shot peening is limited to the range of 0.1 to 0.5 mmN.

Surface roughness after shot peening: 0.5 to 1.5 μm in arithmetic average roughness Ra
If the surface condition is too rough, it will act as a stress concentration source and the bending fatigue strength and surface fatigue strength will decrease, so the upper limit of Ra is set to 1.5 μm. On the other hand, if the surface condition is too good, lubrication with oil becomes insufficient during a fatigue test under high surface pressure, and the surface pressure fatigue strength decreases, so 0.5 μm is the lower limit.

In addition, although there is no restriction | limiting in particular about the manufacturing conditions of the steel raw material of this invention, It is as follows about suitable manufacturing conditions.
After heating the steel material having the above-mentioned preferred component composition to 1100 ° C. or higher, rolling it at a temperature of 800 to 950 ° C. and rolling at a reduction ratio of about 30 to 80%, and then setting the temperature range of 800 to 500 ° C. to 1.0 Cool at a rate of ℃ / s or less.
As described above, in order to suppress the maximum diameter of the oxide inclusions in the material to 19 μm or less, it is desirable that the treatment time is set to 50 minutes or longer in the RH degassing step.

Steels having various component compositions shown in Table 1 were melted in a 100 kg vacuum melting furnace. At that time, in order to change the amount of O and the size of the oxide, the degree of vacuum was changed as shown in Table 1. Next, after forging to 150 mm square, it was welded to a dummy billet, hot rolled at a heating temperature of 1100 ° C., and rolled into a steel bar having a diameter of 30 to 50 mm. A rotating bending fatigue test piece and a roller pitching test piece for evaluating the surface pressure fatigue strength were processed from the rolled steel bar. These test pieces were carburized at 930 ° C. for 7 hours. The surface layer C content was controlled by changing the carbon potential of the atmosphere during carburizing. After carburizing, it was put in an oil temperature of 60 ° C. and then tempered at 180 ° C. for 1 hour in an oil bath.
The results of examining the maximum diameter of the oxide are also shown in Table 1.
Table 2 shows the results of examining the surface layer C content, shot peening arc height value, surface roughness rotational bending fatigue strength, surface pressure fatigue strength, prior austenite grain size, and machinability of the obtained case hardening steel. Shown in

The evaluation method is as follows.
For the maximum oxide diameter, 30 samples were prepared by cutting the L section of the rolled material into 10 × 10 mm ^2, and the maximum oxide diameter of each sample was measured after polishing. Then, the predicted oxide diameter in the case of 30000 mm ² by the extreme value statistical method from these 30 data was taken as the maximum oxide diameter.
The grain boundary oxidation depth was measured by observing the surface of the test specimen after carburizing treatment with an optical microscope with a magnification of 400 times, measuring the maximum grain boundary oxidation depth in each field, and taking the average of the 10 fields. It was.
The prior austenite grain size was obtained by cutting an optical microscope photograph of 1000 magnifications from a grip portion of a quenched and tempered test piece and cutting it.
The rotating bending fatigue test was performed using an Ono type rotating bending fatigue tester at a rotation speed of 1800 rpm and evaluated with a limit strength of 10 ⁷ times.
Further, the surface fatigue strength was obtained by a roller pitching test. The roller pitching test was evaluated with a limit strength of 10 ⁶ times under the conditions of slip ratio: 40% and oil temperature: 80 ° C.
Shot peening is achieved by setting the shot grain size to the arc height value (specified by the amount of warpage of the shot when hitting a shot with a hardness HRC46 width: 19 mm and length: 75 mm). The test piece surface roughness at each arc height value was adjusted by changing the size.
As for the machinability test, a peripheral cutting test was performed using a round bar obtained by forging the obtained material to 50 mm. The tool uses P20 type, cutting: 2mm, cutting speed: 200mm / min, feed: 0.25mm / rev, cutting without lubrication, cutting time: width of tool flank wear at 900 seconds Observed and measured with a stereomicroscope.

  As shown in Table 2, all of the inventive examples obtained according to the present invention have a shallow grain boundary oxidation depth, and are superior in rotational bending fatigue strength and surface pressure fatigue strength compared to the comparative examples.

Claims (1)

In mass%, C: 0.1 to 0.35%, Si: 0.05 to 1.1%, Mn: 0.5 to 2.0%, Cr: 0.5 to 2.5%, P: 0.015% or less, S: 0.02% or less, Al: 0.02 to 0.05% , N: 0.008 to 0.02% and O: 0.0015% or less in a range satisfying the following formulas (1) and (2), the balance being the composition of Fe and inevitable impurities, and an oxide-based nonmetal A steel material having a structure with a maximum diameter of 19 μm or less is forged or machined, and then subjected to carburizing or carbonitriding to make the C content of the surface layer 0.7 to 0.9 mass%, and arc height: 0.1 A method for producing a high-strength case-hardened steel part, characterized by performing shot peening of .about.0.5 mmN and adjusting the surface roughness of the surface layer to an arithmetic average roughness Ra of 0.5 to 1.5 .mu.m.
Record
3.0 ≧ {([% Si] / 2) + [% Mn] + [% Cr]} ≧ 2.4 --- (1)
2.5 ≧ [% Al] / [% N] ≧ 1.8 --- (2)
However, [% M] is the content of element M (% by mass)