Patent Application
20160060737
The disclosure relates to a case hardening steel applied for machine structure components used in the field of construction machinery and automobiles, in particular, to a case hardening steel having excellent cold forgeability and excellent fatigue strength after carburizing treatment.
Since automobile components or the like are often produced by cold forming a steel bar, the material therefor is required to have good cold forgeability. Therefore, the material is normally subjected to softening annealing to spheroidize carbide and improve cold forgeability. Further, in terms of the chemical composition of steel, proposals have been made to reduce the content of Si which greatly affects deformation resistance.
JP3623313B discloses that, by reducing Si content and, further by reducing the amount of other alloying elements to such an extent as to compensate for the quench hardenability improving effect provided by dissolved B, hardness is decreased and cold forgeability is improved.
Further, JP3764586B proposes a case hardening steel ensuring cold workability obtained by combining a chemical composition where Si and Mn which are solid-solution-strengthening elements are reduced and quench hardenability is ensured by dissolved B, with certain production conditions.
The techniques disclosed in JP '313 and JP '586 utilize the quench hardenability improving effect provided by B. However, the quench hardenability improving effect of B is greatly influenced by the cooling rate. On the other hand, since most cold-forged products have complicated shapes, the cooling rate inside components at the time of carburizing and quenching tends to become non-uniform and, as a result, dimensional accuracy after carburizing treatment decreases or component strength becomes insufficient.
Further, although Ti is added to prevent a reduction in the quench hardenability improving effect of B, since nitrides of Ti are generated in the solidification stage of casting, they tend to become coarse, and become the origin of fatigue fracture to shorten the lifetime of components.
It could thus be helpful to provide a case hardening steel exhibiting good cold forgeability and having excellent fatigue strength after carburizing treatment.
We discovered that by applying an appropriate chemical composition and appropriately managing the addition amount of Si, Cr, and Mn, a case hardening steel with excellent cold forgeability and fatigue strength can be obtained.
We thus provide:
C: 0.10 mass % to 0.35 mass %,
Si: 0.01 mass % to 0.13 mass %,
Mn: 0.30 mass % to 0.80 mass %,
P: 0.02 mass % or less,
S: 0.03 mass % or less,
Al: 0.01 mass % to 0.045 mass %,
Cr: 0.5 mass % to 3.0 mass %,
B: 0.0005 mass % to 0.0040 mass %,
Nb: 0.003 mass % to 0.080 mass %, and
N: 0.0080 mass % or less
in a range satisfying following formulas (1) and (2),
Ti as an impurity: 0.005 mass % or less, and
the balance being Fe and incidental impurities:
3.0[% Si]+9.2[% Cr]+10.3[% Mn]≧10.0 (1)
3.0[% Si]+1.0[% Mn]<1.0 (2)
where [% M] represents the content of element M (mass %).
Cu: 0.5 mass % or less,
Ni: 0.5 mass % or less, and
V: 0.1 mass % or less.
A case hardening steel with both excellent cold forgeability and high fatigue strength can be provided.
In the following, reasons for the limiting the steel composition of the case hardening steel to the aforementioned range will be explained in detail.
To perform quenching after carburizing heat treatment on the cold-forged product to increase the hardness of the central part of the forged product, 0.10 mass % or more of C is required. On the other hand, if C content exceeds 0.35 mass %, toughness of the core decreases, and therefore C content is limited to 0.10 mass % to 0.35 mass %. The C content is preferably 0.25 mass % or less, and more preferably 0.20 mass % or less.
Si is required as a deoxidizing agent, and needs to be added in an amount of at least 0.01 mass %. However, Si is an element preferentially oxidized in the carburized surface layer and facilitates grain boundary oxidization. Further, it causes solid solution strengthening of ferrite and increases deformation resistance to deteriorate cold forgeability. Therefore, the upper limit of Si content is 0.13 mass %. The Si content is preferably 0.02 mass % to 0.10 mass %, and more preferably 0.02 mass % to 0.09 mass %.
Mn is an effective element to improve quench hardenability, and needs to be added in an amount of at least 0.30 mass %. However, since excessive addition of Mn results in an increase in deformation resistance caused by solid solution strengthening, the upper limit of Mn content is 0.80 mass %. The Mn content is preferably 0.60 mass % or less, and more preferably 0.55 mass % or less.
Since P segregates in crystal grain boundaries and reduces toughness, it is desirable for the content thereof to be as low as possible. However, a content thereof of up to 0.02 mass % is tolerable. The P content is preferably 0.018 mass % or less. Further, although a lower limit thereof does not need to be limited to a particular value, considering that unnecessary reduction of P lengthens refining time and increases refining costs, P content should be 0.012% or more.
S is an element existing as a sulfide inclusion and effective in improving machinability by cutting. However, since excessively adding S would lead to a reduction of cold forgeability, the upper limit thereof is 0.03 mass %. Further, although there is no particular lower limit, it may be set to 0.012% or more for the purpose of guaranteeing machinability by cutting.
If Al is excessively added, it fixes with N within steel as AlN, and develops a quench hardenability improving effect provided by B. To stabilize component strength after carburizing treatment, it is important to prevent the development of the quench hardenability improving effect provided by B, and to do so, the upper limit of Al needs to be 0.045 mass %.
The mean hardness of materials after carburizing, each containing 10 ppm of B and 45 ppm of N, and with an Al addition amount of 0.048 mass % (
As is clear from
As is clear from
Experiments for which results are shown in
On the other hand, since Al is an effective element for deoxidization, the lower limit thereof is 0.01 mass %. The content thereof is preferably 0.01 mass % to 0.040 mass %, and more preferably 0.015 mass % to 0.035 mass %.
Cr contributes to improving not only quench hardenability, but also resistance to temper softening, and is also an effective element to facilitate spheroidization of carbide. However, if Cr content is less than 0.5 mass %, the addition effect is limited. On the other hand, if it exceeds 3.0 mass %, it facilitates excessive carburizing or generation of retained austenite and adversely effects fatigue strength. Therefore, Cr content is limited to 0.5 mass % to 3.0 mass %. It is preferably 0.7 mass % to 2.5 mass %.
B bonds inside the steel with N and has an effect of reducing dissolved N. Therefore, it is possible to reduce dynamic strain aging at the time of cold forging caused by dissolved N, and contributes to reducing the deformation resistance during forging. 0.0005% or more of B needs to be added to obtain this effect. On the other hand, if B content exceeds 0.0040%, the effect of reducing deformation resistance reaches a plateau, and causes a reduction of toughness. Therefore, B content is limited to 0.0005 mass % to 0.0040 mass %. More preferably, B content is 0.0005 mass % to 0.0030 mass %.
Nb forms NbC inside the steel, and inhibits grain coarsening of austenite grains during carburizing heat treatment by a pinning effect. It needs to be added in an amount of at least 0.003 mass % to obtain this effect. On the other hand, if Nb is added in an amount exceeding 0.080 mass %, it may result in deterioration of grain coarsening inhibiting ability caused by precipitation of coarse NbC or deterioration of fatigue strength. Therefore, Nb content is 0.080 mass % or less. It is preferably 0.010 mass % to 0.060 mass %, and more preferably 0.015 mass % to 0.045 mass %.
It is important to minimize the Ti content mixed into steel. Ti tends to bond with N to form coarse TiN and, adding Ti simultaneously with Nb, makes it even more likely to generate coarse precipitates and causes a reduction in fatigue strength. Therefore, the upper limit of Ti contained as an impurity is 0.005 mass %. More preferably, Ti content is 0.003 mass % or less.
Since N dissolves in steel to cause dynamic strain aging during cold forging to increase deformation resistance, it needs to be minimized. Therefore, the amount of N mixed in is limited to 0.0080 mass % or less. The N content is preferably 0.0070 mass % or less, and more preferably 0.0065 mass % or less.
The proper composition ranges of the basic components are as explained above. However, it does not suffice for each element to only satisfy the aforementioned ranges, and it is also important for Si, Mn, and Cr, in particular, to satisfy the relationships of Formulae (1) and (2):
3.0[% Si]+9.2[% Cr]+10.3[% Mn]≧10.0 (1)
3.0[% Si]+1.0[% Mn]<1.0 (2)
where [% M] represents the content of element M (mass %).
Formula (1) relates to factors that influence quench hardenability and temper softening resistancy, and if Formula (1) is not satisfied, fatigue strength after carburizing treatment becomes insufficient. Further, Formula (2) relates to factors that influence cold forgeability, and if Formula (2) is satisfied, solid solution strengthening caused by Si and Mn can be inhibited, and thereby deformation resistance during cold forging can be reduced and die life can be enhanced.
The increase in deformation resistance was calculated for when only the addition amounts of Si and Mn were changed, compared to when Si and Mn are not added. As can be seen from the results shown in
Using a steel containing C: 0.18 mass %, Si: not added, Mn: not added, P: 0.012 mass %, S: 0.012 mass %, Al: 0.034 mass %, Cr: 1.7 mass %, B: 0.0013 mass %, Nb: 0.030 mass %, and N: 0.0052 mass %, and the balance including Fe and incidental impurities as the base material, 12 different steels with varying Si contents in a range of 0.03 mass % to 0.20 mass %, and varying Mn contents in a range of 0.34 mass % to 1.2 mass %, were prepared and hot rolled to a diameter of 40 mm. Then, the deformation resistance thereof was measured with a cold forgeability evaluation method described later, and the increase in deformation resistance was obtained by comparing with the deformation resistance of when Si and Mn are not added.
Although the basic components of the case hardening steel of the disclosure are as explained above, one or more of Cu: 0.5 mass % or less, Ni: 0.5 mass % or less, and V: 0.1 mass % or less may also be contained as necessary.
Since Cu is an effective element to improve quench hardenability, it is preferably added in an amount of 0.05 mass % or more. However, excessively adding Cu causes deterioration of surface characteristics of the steel sheet and increases alloy costs. Therefore, the upper limit thereof is 0.5 mass %.
Since Ni and V are effective elements to improve quench hardenability and toughness, they are preferably contained respectively in amounts of 0.05 mass % or more and 0.01 mass % or more. However, since they are expensive, the upper limits of the content thereof are each limited to 0.5 mass % and 0.1 mass %.
In the following, the constitution and effect of the case hardening steel will be explained in more detail with reference to the examples. However, the case hardening steel is not restricted by any means to these examples, which may be changed appropriately within the range conforming to the purpose of the disclosure, all of such changes being included within the technical scope of this disclosure.
A steel having a chemical composition shown in Table 1 was obtained by steel-making, and a bloom produced from the molten steel thereof was subjected to hot rolling and formed into a steel bar of 40 mmφ. Evaluation on cold forgeability was performed for the obtained steel bar.
Cold forgeability was evaluated based on two criteria, namely, deformation resistance and critical upset ratio.
Test pieces each being in a columnar shape of 15 mm in diameter and 22.5 mm in height were collected from the steel bars as rolled, the test pieces each having the center axis positioned at a depth of ¼ of the diameter D of the steel bar (hereinafter, this position is referred to as “¼D position”) from the outer periphery thereof. The columnar test pieces thus obtained each had conical recesses formed at the center positions on the top and bottom surfaces thereof, the conical recesses each having a bottom surface of 2 mmφ in diameter and having a central angle of 120°. The recesses thus formed were configured to serve as restraint recesses. The columnar test pieces each further have a V-shaped groove in the side surface thereof, the groove extending in the height direction of the test piece so that the test piece was obtained as a notched columnar test piece.
The cold forgeability was evaluated as follows. That is, the test pieces were each subjected to compression test in which a compressive load was applied to each of the two surfaces 2 to be compressed in a state where the top and bottom surfaces of the test piece were restrained, to thereby measure deformability and deformation resistance. Deformability was evaluated based on the maximum compressibility to crack initiation from the floor of the V-groove 1 (referred to as critical upset ratio), while deformation resistance was evaluated based on a deformation stress at a compressibility of 60% (referred to as “60% deformation resistance”). The steel can be considered excellent in cold forgeability when the critical upset ratio is 50% or more and the deformation resistance value is 800 MPa or less.
Next, fatigue properties were evaluated based on two points namely, bending fatigue and surface fatigue.
From the ¼ D position of the above steel bar, a rotary bending test piece to evaluate bending fatigue strength and a roller pitting test piece to evaluate surface fatigue strength were collected. These test pieces were subjected to carburizing at 930° C. for 3 hours with a carbon potential of 1.0 mass %, then oil quenched at 60° C., and then tempered at 180° C. for 1 hour. For each carburized test piece, a rotating bending fatigue test and a roller pitting test was performed. The rotating bending fatigue test was performed at a speed of 3500 rpm and the fatigue limit strength after 107 cycles was evaluated. The roller pitting test was performed under the conditions of a slip rate of 40% and an oil temperature of 80° C., and strength after 107 cycles (critical strength at which pitting occurs in test piece surface) was evaluated. The obtained results are shown in Table 2. With a bending fatigue strength of 800 MPa or more and a surface fatigue strength of 3500 MPa or more, fatigue strength is considered excellent.
As shown in Table 2, all of our examples are excellent in both cold forgeability and fatigue strength.
0.09
0.36
0.14
1.06
0.9
1.02
0.048
0.0090
0.3
1.01
3.2
0.0003
0.0050
0.090
0.002
0.006
1.00
750
3420
821
47
790
830
45
819
49
3450
815
42
805
48
790
3400
812
54
740
48
720
3370
780
3300
3420
760
3460
790
3420
804
49
| Number | Date | Country | Kind |
|---|---|---|---|
| 2013-074347 | Mar 2013 | JP | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/JP2014/000191 | 1/16/2014 | WO | 00 |
