JP2001073082A - Steel excellent in rolling fatigue life and its production - Google Patents

Abstract

PROBLEM TO BE SOLVED: To produce steel in which the generation of the change of the structure in which the size of crystal grains different from a mother phase whitely shown by an optical microscope is refined to several tens nm is suppressed in case hardening steel and having an excellent life, particularly, an excellent rolling life even under high vibration and high loads and to provide a method for producing it. SOLUTION: This medium-high carbon steel excellent in a rolling fatigue life has a compsn. contg., by weight, >0.45 to 1.2% C, 0.05 to 1.5% Si, 0.20 to 2.0% Mn and <=0.015% N, moreover contg. one or >=two kinds selected from the three kinds of 0.01 to 0.20% Ti, 0.02 to 0.40% Nb and 0.01 to 0.20% V, also satisfying 0.05%<=Ti(%)+0.52×Nb(%)+0.94 ×V(%), and the balance Fe with inevitable impurities.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a steel having excellent rolling fatigue life, which is used as a steel for machine structural use or a steel for bearings, and in which fine precipitates are dispersed in the steel to generate during rolling fatigue. The present invention relates to a medium to high carbon steel which suppresses a special structural change that leads to early peeling and has an improved rolling fatigue life.

[0002]

2. Description of the Related Art Conventionally, general rolling members are made of various materials in accordance with diversified uses such as conditions of use. For small parts and general-purpose parts, high carbon chromium bearing steel such as SUJ2 is used. Or induction hardened steel such as S53C is used. By the way, industrial machines and automotive parts are becoming increasingly harsh in their use environments such as drive system parts and bearings due to their higher performance, higher output, and smaller size and lighter weight. For example, when rolling members such as toroidal type continuously variable transmissions, constant velocity joints, and bearings are used under high vibration and high load, conventional steel is less susceptible to corrosion than the parent phase under the rolling surface, and optical microscopes However, there is a problem that crystal grains different from the mother phase which looks white in the above-mentioned microstructure are refined down to a size of several tens of nanometers, thereby causing early breakage. As a countermeasure against this structural change, in the conventional method, the occurrence of this structural change is regarded as the reduction of C diffusion, and the carbon content in steel is increased to carry out medium carbonization or Cr is added. further,
For example, there is a technology disclosed in Japanese Patent Publication No. 2883460, which prevents the crystal grains from becoming coarse even when the quenching temperature is increased. However, this technology does not suppress the occurrence of the above structural change. No, life is not improved.

[0003]

SUMMARY OF THE INVENTION In view of the above-mentioned problems, an object of the present invention is to suppress the occurrence of the above-mentioned structural change, to provide an excellent life even under high vibration and high load.
In particular, it is an object of the present invention to provide a medium to high carbon steel having a rolling life and a method for producing the same.

[0004]

Means for Solving the Problems In order to solve the above problems, the present inventors have conducted intensive studies and observed changes in the structure of rolling members made of various steel materials under high vibration and high load. The change is the traditional organizational change (D
EC, WEC), that is, different from the conventional structure change in which tempering of the structure is considered to have progressed. In other words, the structure change portion of the rolling member made of steel under high vibration and high load, fatigue progresses locally,
The crystal grain size is reduced to the nm size. This is because local stress concentration occurs due to high vibration and high load, cracks occur, further stress concentration and stress complication occur at the crack portion, plastic deformation is repeated at the crack portion, and crystal grains are several tens nm. It is considered that a microstructural change that has been refined to the maximum has occurred.

[0005] Therefore, a component element for suppressing the generation of the fine cracks is added to the steel component, and after quenching and tempering, 10% is added to the steel.
Fine precipitates of 0 nm or less are uniformly dispersed to strengthen dispersion. The number of the fine precipitates of 100 nm or less is 1 /
10 μm ² , desirably 50 pieces / 10 μm ² . By the dispersion strengthening by the fine precipitates, the generation and propagation of cracks are suppressed, thereby suppressing the occurrence of structural change. Further, even when a crack starts from a non-metallic inclusion or the like existing in steel, the finely dispersed precipitate suppresses the movement of the transition, prevents plastic deformation, and suppresses structural change.

[0006] That is, the means of the present invention for solving the above-mentioned problem is that, in the invention of claim 1, C: 0.
More than 45 to 1.2%, Si: 0.05 to 1.5%, Mn:
0.20 to 2.0%, N: ≤ 0.015%, Ti: 0.01 to 0.20%, Nb: 0.02 to
0.40%, V: One or more selected from three kinds of 0.01 to 0.20%, and 0.05% ≦
Ti (%) + 0.52 × Nb (%) + 0.94 × V
(%), And is excellent in rolling fatigue life, characterized by the balance of Fe and unavoidable impurities.

[0007] According to the second aspect of the present invention, C: 0.
More than 45 to 1.2%, Si: 0.05 to 1.5%, Mn:
0.20 to 2.0%, B: 0.0005 to 0.0050
%, N: ≤ 0.015%, and further, Ti: 0.
01 to 0.20%, Nb: 0.02 to 0.40%, V:
One or two selected from three types of 0.01 to 0.20%
At least 0.05% ≦ Ti (%) + 0.
A steel excellent in rolling fatigue life, satisfying 52 × Nb (%) + 0.94 × V (%) and characterized by the balance of Fe and unavoidable impurities.

According to the third aspect of the present invention, C: 0.
More than 45 to 1.2%, Si: 0.05 to 1.5%, Mn:
0.20 to 2.0%, N: ≤ 0.015%, Ti: 0.01 to 0.20%, Nb: 0.02 to
0.40%, V: One or more selected from three kinds of 0.01 to 0.20%, and 0.05% ≦
Ti (%) + 0.52 × Nb (%) + 0.94 × V
(%), Cr: 0.15 to 3.0%, M
o: 0.05 to 2.0%, Ni: 0.05 to 3.0%, containing one or more selected from three types, with the balance being F
e and unavoidable impurities, and is excellent in rolling fatigue life.

According to the fourth aspect of the present invention, C: 0.
More than 45 to 1.2%, Si: 0.05 to 1.5%, Mn:
0.20 to 2.0%, B: 0.0005 to 0.0050
%, N: ≤ 0.015%, and further, Ti: 0.0
1 to 0.20%, Nb: 0.02 to 0.40%, V:
One or two selected from three types of 0.01 to 0.20%
At least 0.05% ≦ Ti (%) + 0.
52 × Nb (%) + 0.94 × V (%), Cr: 0.15 to 3.0%, Mo: 0.05 to 2.0
%, Ni: 0.05 to 3.0%, one or more selected from the three types, and is a steel excellent in rolling fatigue life characterized by being composed of the balance of Fe and inevitable impurities. .

According to a fifth aspect of the present invention, the steel according to any one of the first to fourth aspects is hot-rolled at 1250 to 1400 ° C. to form a billet, and further rolled at a temperature of Ac ₃ to 1050 ° C. This is a method for producing a steel material having an excellent rolling fatigue life, which is characterized by using a wire.

The reasons for adding the constituent elements of the steel of the present invention and the reasons for limiting the amount of addition are described below.

C is added to secure hardness after quenching and tempering. If it is less than 0.45%, it is not sufficient to secure the hardness, and if it exceeds 1.2%, giant carbide is generated, and the life and impact value are reduced. Therefore, C: more than 0.45 to 1.2
%.

[0013] Si is added for a deoxidizing effect in steel making and for ensuring hardenability. If it is less than 0.05%, the deoxidizing effect is insufficient, and if it exceeds 1.5%, the cold workability decreases. Therefore, Si is set to 0.05 to 1.5%.

Mn is added for hardenability. To achieve this effect, 0.20% or more is required.
If it exceeds 2.0%, the workability is reduced. So Mn:
0.20 to 2.0%.

[0015] Ti precipitates fine Ti carbides in the steel. The dispersion strengthening of the precipitates suppresses the occurrence of cracks in repeated fatigue under high vibration and high load, and suppresses the occurrence of structural change accompanying the cracks.
However, this effect is ineffective at less than 0.01% Ti. If Ti: more than 0.20%, more than ten μm of Ti carbonitride generated at the time of solidification increases, and the cold workability decreases. Therefore, Ti: 0.01% to 0.20% is set.

Nb, like Ti, contains fine Nb in steel.
Precipitates carbide. The reason for the limitation is the same as that of Ti, and the dispersion strengthening of the above precipitates suppresses the occurrence of cracks and the occurrence of the structural change accompanying the repeated fatigue under high vibration and high load under high vibration. . But,
This effect is ineffective when Nb is less than 0.02%. N
b: If it exceeds 0.40%, more than 10 μm of Nb carbonitride generated during solidification increases, and the cold workability decreases. Therefore, Nb is set to 0.02 to 0.40%.

V, like Ti, precipitates fine V carbides in the steel. The reason for the limitation is the same as Ti.
By the dispersion strengthening of the precipitates described above, cracks are suppressed from occurring during repeated fatigue under high vibration and high load, and the occurrence of a structural change accompanying the cracks is suppressed. However, this effect is ineffective when V: less than 0.01%.
If V: exceeds 0.20%, V-carbonitrides of tens of μm formed during solidification increase, and the cold workability decreases. Therefore, V is set to 0.01 to 0.20%.

In order for Ti, Nb and V to sufficiently exhibit the above-mentioned effects, 0.05% ≦ Ti (%) +
It is necessary to satisfy 0.52 × Nb (%) + 0.94 × V (%), and within this range, one or more of Ti, Nb, and V are added.

N precipitates Ti carbonitride, Nb carbonitride and V carbonitride of about 10 μm at the time of solidification of steel and lowers the cold workability, so the upper limit is made 0.015%.

B is added for hardenability. But,
Less than 0.0005% has no effect, 0.005%
If the content is too large, the hardenability will be reduced, and the toughness will be further reduced. Therefore, B: 0.0005 to 0.0050
%.

Cr, Mo and Ni are added for the hardenability of low alloy case hardened steel. However, if the amount is small, the effect is not obtained. If the amount is too large, the effect is saturated and the cost increases. In any case, in order to obtain the effect of addition, in consideration of economy, C
r: 0.15 to 3.0%, Mo: 0.05 to 2.0%,
Ni: 0.05 to 3.0%, and one or more of them are selectively used.

A steel satisfying the following expression (1) according to any one of claims 1 to 4 is obtained at 1250 to 1400 ° C.
Hot rolling to a billet in further Ac ₃ to 1050 by rolling to a bar wire at ° C., a 100nm following fine precipitates in steel 1/10 [mu] m ^2, preferably 50/10 [mu] m ² Is precipitated, and the dispersion strengthening by the fine precipitates suppresses the generation and propagation of cracks, thereby suppressing the occurrence of structural change.

[0023]

DESCRIPTION OF THE PREFERRED EMBODIMENTS Embodiments of the present invention will be described below with reference to steels of Examples shown in Table 1. Examples 1 to 9 in Table 1
A steel containing the chemical component (1) and the balance consisting of Fe and unavoidable impurities is melted at 100 kg VIM. The obtained steel material is billet-rolled at 1250 ° C. to 1400 ° C., and Ac ₃ to 10
Bar-rolling is performed at 50 ° C. to precipitate fine Ti carbide, Nb carbide, and V carbide of 100 nm or less. The number of the fine precipitates is 1/10 μm ² or more, preferably 50 /
It is 10 μm ² .

[0024]

EXAMPLES Table 1 shows chemical compositions of steels of Examples and Comparative Examples of invention steels. First, the steel of the present invention having the steel components shown in Table 1 and the test steel of the comparative example are melted. Comparative examples show nine kinds of 1 to 9,
Examples of the present invention show nine types of 1 to 9. In Table 1,
P, S, and O indicate impurity levels. In these, none of the test steels of Comparative Examples 1 to 9 satisfied the relational expression of the formula (1).

[0025]

[Equation 1] 0.05% ≦ Ti (%) + 0.52 × Nb (%) + 0.94 × v (%) (1)

On the other hand, the steels of the present invention, Examples 1 to 9, all satisfied the above-mentioned relational expression (1).

[0027]

[Table 1]

The test specimens of steel shown in each of the examples and comparative examples were prepared by rolling a billet at 1250 ° C. to 1400 ° C. in an actual manufacturing process and 100 kg VIM as an alternative to bar wire rolling at Ac _{3 to} 1050 ° C. The test material dissolved in
It is rolled by heating to 00 ° C., finish forged at 950 ° C., processed into the following driven roller test piece, and induction hardened or soot hardened. The test material was tested by the following test method to reproduce rolling fatigue under high vibration and high load. In this test method, when a conventional steel is tested, it breaks with a short life with a structural change. Table 2 shows the result of the durability life test, the life value and the presence / absence of the occurrence of structural change.

The test method was as follows: outer diameter φ130 mm × 18 wt
Using a driving roller made of SCM420 carburized material with an end surface shape of R = 150, a driven roller made of a test piece having an outer diameter of 26 mm and a flat end surface was rotated at 15,000 rpm by the above driving roller to apply surface pressure and repeatedly fatigued. Let it. Further, during the test, vibration is applied to the driven roller unit from a vibrator. The contact portion between the driving roller and the driven roller is processed to have Ra = 0.1 μm or less, a contact surface pressure of 350 kgf / mm ² is applied, and a fatigue test is performed during lubrication.

Fine Ti carbide of 100 nm or less, Nb
The number of fine precipitates of carbides and V carbides was confirmed by performing induction hardening or quenching in the same process as the test specimen for the life test, preparing a thin film sample for a transmission electron microscope from the quenched material, The precipitate was counted by observing 200 μm ² with a microscope. As a result, in all the steels of the examples of the present invention, the number of fine precipitates was 1/10 μm ² or more, and was in the range of 50/10 μm ² .

All of the steels of Comparative Examples 1 to 9 that do not satisfy the formula (1) undergo structural changes. On the other hand, no structural change occurred in all of the steels of Examples 1 to 9 of the present invention that satisfied Expression (1). L ₁₀ of the rolling life is shown in Table 2 together show the life of Comparative Example 1 as 1. L ₁₀ life of the steel of the present invention are excellent with 5-fold to 3-fold compared to the comparative example.

[0032]

[Table 2]

[0033]

As described above, according to the present invention,
The high carbon steel is added with a specific amount of an element that suppresses the generation of cracks, and one or more, preferably 50, fine precipitates having a diameter of 100 nm or less per 10 μm ² are uniformly dispersed in the steel after quenching and tempering. Because of the strengthening, the occurrence of structural change is suppressed, and a medium to high carbon steel having excellent life even under high vibration and high load, particularly excellent rolling life can be obtained.

Claims (5)

[Claims] 1% by weight C: more than 0.45% to 1.2%,
Si: 0.05 to 1.5%, Mn: 0.20 to 2.0
%, N: ≤ 0.015%, and further, Ti: 0.0
1 to 0.20%, Nb: 0.02 to 0.40%, V:
One or two selected from three types of 0.01 to 0.20%
At least 0.05% ≦ Ti (%) + 0.
A steel excellent in rolling fatigue life, which satisfies 52 × Nb (%) + 0.94 × V (%) and is composed of a balance of Fe and unavoidable impurities. 2. In% by weight, C: more than 0.45% to 1.2%,
Si: 0.05 to 1.5%, Mn: 0.20 to 2.0
%, B: 0.0005 to 0.0050%, N: ≦ 0.0
15%, and further, Ti: 0.01 to 0.20
%, Nb: 0.02-0.40%, V: 0.01-0.
One or more selected from 20% of the three types, and 0.05% ≦ Ti (%) + 0.52 × Nb
(%) + 0.94 × V (%), and is excellent in rolling fatigue life, characterized by the balance of Fe and unavoidable impurities. 3.% by weight, C: more than 0.45 to 1.2%,
Si: 0.05 to 1.5%, Mn: 0.20 to 2.0
%, N: ≤ 0.015%, and further, Ti: 0.0
1 to 0.20%, Nb: 0.02 to 0.40%, V:
One or two selected from three types of 0.01 to 0.20%
At least 0.05% ≦ Ti (%) + 0.
52 × Nb (%) + 0.94 × V (%), Cr: 0.15 to 3.0%, Mo: 0.05 to 2.0
%, Ni: steel containing one or more selected from three types of 0.05 to 3.0%, the balance being Fe and unavoidable impurities, and excellent in rolling fatigue life. 4.% by weight, C: more than 0.45 to 1.2%,
Si: 0.05 to 1.5%, Mn: 0.20 to 2.0
%, B: 0.0005 to 0.0050%, N: ≦ 0.0
15%, and Ti: 0.01 to 0.20%,
Nb: 0.02 to 0.40%, V: 0.01 to 0.20
% Or one or more selected from three kinds, and 0.05% ≦ Ti (%) + 0.52 × Nb (%) +
0.94 x V (%), and Cr: 0.15
3.0%, Mo: 0.05 to 2.0%, Ni: 0.05
A steel having an excellent rolling fatigue life, characterized in that it contains one or more selected from three types of up to 3.0%, and the balance consists of Fe and unavoidable impurities. 5. The method according to claim 1, wherein the steel according to any one of claims 1 to 4 is hot-rolled at 1250 to 1400 ° C. to obtain a steel slab, and further rolled at Ac ₃ to 1050 ° C. to obtain a rod or wire. A method for producing a steel material that has excellent rolling fatigue life.