CASE HARDENING STEEL

Description

TECHNICAL FIELD

[0001] 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.

BACKGROUND

[0002] For example, since an automobile component or the like is 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.

[0003] EP2530178 discloses a case hardening steel excellent in cold forgeability, has high fatigue strength after carburization, and suitably serves as a material for mechanical structures in the fields of construction machinery and automobiles.

[0004] JP2006152330 discloses a case hardening steel with high fatigue strength after carburization, good cold forgeability used for machine structural member parts.

[0005] PTL 1 (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.

[0006] Further, PTL 2 (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.

CITATION LIST

Patent Literature

[0007] 

PTL 1: JP3623313B

PTL 2: JP3764586B

[0008] The techniques disclosed in PTLs 1 and 2 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 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.

[0009] It could thus be helpful to provide a case hardening steel exhibiting good cold forgeability and having excellent fatigue strength after carburizing treatment.

SUMMARY

[0010] As a result of intensive studies regarding the chemical compositions of case hardening steels, 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.

[0011] This disclosure is based on these findings. We thus provide:

(1) A case hardening steel having a chemical composition containing

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:



where [%M] represents the content of element M (mass%).

(2) The case hardening steel according to aspect (1) wherein the chemical composition further contains one or more of

Cu: 0.5 mass% or less,

Ni: 0.5 mass% or less, and

V: 0.1 mass% or less.

[0012] With this disclosure, a case hardening steel with both excellent cold forgeability and high fatigue strength can be provided.

BRIEF DESCRIPTION OF THE DRAWINGS

[0013] In the accompanying drawings:

FIG. 1 is a graph showing the mean hardness of a material after carburizing made from a steel material containing 0.048 mass% of Al, in positions from the surface to a position 4 mm inside the material, and the hardness range measured.

FIG. 2 is a graph showing the mean hardness of a material after carburizing made from a steel material containing 0.043 mass% of Al, in positions from the surface to a position 4 mm inside the material, and the hardness range measured.

FIG. 3 is a graph showing the relationship between Al content and the maximum value of hardness variation.

FIG. 4 is a graph showing the relationship between the balance of addition amounts of Si and Mn, and the increase in deformation resistance.

FIG. 5 shows the shape of the V-grooved cold forgeability test piece for evaluation of critical upset ratio.

DETAILED DESCRIPTION

[0014] In the following, reasons for the limiting the steel composition of the case hardening steel of the disclosure to the aforementioned range will be explained in detail.

C: 0.10 mass% to 0.35 mass%

[0015] In order 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 a range of 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: 0.01 mass% to 0.13 mass%

[0016] 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 which is 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: 0.30 mass% to 0.80 mass%

[0017] Mn is an effective element for improving quench hardenability, and needs to be added in an amount of at least 0.30 mass%. However, since excessive addition of Mn would result 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.

P: 0.02 mass% or less

[0018] 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% would be 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 would lengthen refining time and increase refining costs, P content should be 0.012 % or more.

S: 0.03 mass% or less

[0019] S is an element which exists as a sulfide inclusion which is 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.

Al: 0.01 mass% to 0.045 mass%

[0020] If Al is excessively added, it fixes with N within steel as AIN, and develops a quench hardenability improving effect provided by B. In order to stabilize component strength after carburizing treatment, it is important to prevent the development of the quench hardenability improving effect provided by B, and in order to do so, the upper limit of Al needs to be 0.045 mass%.

[0021] 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% (FIG. 1) and 0.043 mass% (FIG. 2), respectively, in positions from the surface to a position 4 mm inside the material, and the hardness range measured are shown in FIG. 1 and FIG. 2.

[0022] As it is clear from FIG. 1 and FIG. 2, when the Al content is 0.048 mass% (FIG. 1), the hardness range measured (the range between the upper and lower broken lines in the figure) in each depth position from the surface (the horizontal axis in the figure) is larger than that of when the Al content is 0,043 mass% (FIG. 2), and there is a large variation in hardness in each depth position.

[0023] FIG. 3 shows the changes in the maximum value of hardness variation (the maximum value in the vertical axis direction between the upper and lower broken lines in FIG. 1 or FIG. 2) when 10 ppm of B and 45 ppm of N are contained with varying Al addition amounts.

[0024] As it is clear from FIG. 3, by setting the Al addition amount to 0,045 mass% or less, the variation of hardness from the surface of the material after carburizing to the inside thereof is reduced. Based on the above results, the upper limit value of Al content is set to 0.045 mass%.

[0025] Experiments for which results are shown in FIG. 1 to FIG. 3 were conducted under the following conditions. The steel used in the experiments contained C: 0.16 mass%, Si: 0.09 mass%, Mn: 0.53 mass%, P: 0.012 mass%, S: 0.012 mass%, Cr: 1.9 mass%, B: 0.0015 mass%, Nb: 0.025 mass%, and N: 0.0065 mass%, the Al addition amount being as described above, and the balance including Fe and incidental impurities. After the steel was processed into a round bar having a diameter of 25 mm, it was 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. The hardness from the surface of the cross section of the tempered round bar to the position 4 mm inside was measured in the same cross section in 10 areas per depth position to obtain the mean value, maximum value and the minimum value of Vickers hardness in each depth position from the surface.

[0026] 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: 0.5 mass% to 3.0 mass%

[0027] Cr contributes to improving not only quench hardenability but also resistance to temper softening, and is also an effective element for facilitating 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 a range of 0.5 mass% to 3.0 mass%. It is preferably in the range of 0.7 mass% to 2.5 mass%.

B: 0.0005 mass% to 0.0040 mass%

[0028] 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. In order to obtain this effect, 0.0005 % or more of B needs to be added. 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 a range of 0.0005 mass% to 0.0040 mass%. More preferably, B content is in the range of 0.0005 mass% to 0.0030 mass%.

Nb: 0.003 mass% to 0.080 mass%

[0029] Nb forms NbC inside the steel, and inhibits grain coarsening of austenite grains during carburizing heat treatment by a pinning effect. To obtain this effect, it needs to be added in an amount of at least 0.003 mass%. 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%.

Ti: 0.005 mass% or less

[0030] 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.

N: 0.0080 mass% or less

[0031] 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.

[0032] The proper composition ranges of the basic components of the disclosure are as explained above. However, in this disclosure, 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 the following formulas (1) and (2).



where [%M] represents the content of element M (mass%).

[0033] The above 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, the above 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.

[0034] 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 FIG. 4, when 3.0[%Si] + 1.0[%Mn] is less than 1, the increase in deformation resistance is surely inhibited. Here, Experiments for which results are shown in FIG. 4 were conducted under the following conditions.

[0035] 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.

[0036] 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.

[0037] Since Cu is an effective element for improving quench hardenability, it is preferably added in an amount of 0.05 mass% or more. However, excessively adding Cu would cause deterioration of surface characteristics of the steel sheet and increase alloy costs. Therefore, the upper limit thereof is 0.5 mass%.

[0038] Since Ni and V are effective elements for improving 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%.

EXAMPLES

[0039] In the following, the constitution and effect of the case hardening steel of the disclosure 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 the disclosure.

[0040] A steel having a chemical composition shown in Table 1 was obtained by steelmaking, and a bloom produced from the molten steel thereof was subjected to hot rolling and formed into a steel bar of 40mmϕ. Evaluation on cold forgeability was performed for the obtained steel bar.

[0041] Here, the cold forgeability was evaluated based on two criteria, namely, deformation resistance and critical upset ratio.

[0042] 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 1/4 of the diameter D of the steel bar (hereinafter, this position is referred to as "1/4D 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. Here, Fig. 5(a) is a top view illustrating the shape of the notched columnar test piece used for evaluating the cold forgeability, Fig. 5(b) is a side view thereof, and Fig. 5(c) is a view illustrating the detailed dimensions of the V-shaped groove of Fig. 5(b). In the drawings, reference numeral 1 denotes the V-shaped groove, 2 denotes the surfaces to be compressed (top and bottom surfaces), and 3 denotes the conical recesses (restraint recesses).

[0043] 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 the deformability and the deformation resistance. The 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 the 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.

[0044] Next, fatigue properties were evaluated based on two points namely, bending fatigue and surface fatigue.

[0045] From the 1/4 D position of the above steel bar, a rotary bending test piece for evaluating bending fatigue strength and a roller pitting test piece for evaluating 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.

[0046] As shown in Table 2, all of the examples according to the disclosure are excellent in both cold forgeability and fatigue strength.

[Table 2]

[0047] 

Table 2

No.	Steel No.	Cold Forgeability		Fatigue Strength after Carburizing		Remarks
		Deformation Resistance (Mpa)	Critical Upset Ratio (%)	Bending Fatigue Strength (MPa)	Surface Fatigue Strength (MPa)
1	A	701	61	830	3650	Example of Disclosure
2	B	721	62	840	3600	Example of Disclosure
3	C	725	56	870	3710	Example of Disclosure
4	D	741	58	870	3750	Example of Disclosure
5	E	753	54	910	3900	Example of Disclosure
6	F	750	60	810	3550	Example of Disclosure
7	G	755	53	830	3740	Example of Disclosure
8	H	779	55	920	3930	Example of Disclosure
10	J	708	68	750	3420	Comparative Example
11	K	821	47	790	3590	Comparative Example
12	L	830	45	840	3600	Comparative Example
13	M	819	49	890	3680	Comparative Example
14	N	750	55	810	3450	Comparative Example
15	O	815	42	840	3540	Comparative Example
16	P	805	48	790	3400	Comparative Example
17	Q	812	54	740	3560	Comparative Example
18	R	820	48	820	3600	Comparative Example
19	S	740	54	720	3370	Comparative Example
20	T	788	53	780	3300	Comparative Example
21	U	725	61	840	3420	Comparative Example
22	V	780	54	760	3460	Comparative Example
23	W	751	58	790	3420	Comparative Example
24	X	804	49	830	3550	Comparative Example

REFERENCE SIGNS LIST

[0048] 

1 V-shaped Groove

2 Surfaces to be Compressed (Top and Bottom Surfaces)

3 Conical Recesses (Restraint Recesses)

Claims

1. A case hardening steel having a chemical composition consisting of

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%,

N: 0.0080 mass% or less

in a range satisfying following formulas (1) and (2),

Ti as an impurity: 0.005 mass% or less,

optionally one or more of

Cu: 0.5 mass% or less,

Ni: 0.5 mass% or less,

V: 0.1 mass% or less,

and the balance being Fe and incidental impurities:



where [%M] represents the content of element M (mass%).

Ansprüche

1. Einsatzstahl mit einer chemischen Zusammensetzung bestehend aus

C: 0,10 Massenprozent bis 0,35 Massenprozent,

Si: 0,01 Massenprozent bis 0,13 Massenprozent,

Mn: 0,30 Massenprozent bis 0,80 Massenprozent,

P: 0,02 Massenprozent oder weniger,

S: 0,03 Massenprozent oder weniger,

Al: 0,01 Massenprozent bis 0,045 Massenprozent,

Cr: 0,5 Massenprozent bis 3,0 Massenprozent,

B: 0,0005 Massenprozent bis 0,0040 Massenprozent,

Nb: 0,003 Massenprozent bis 0,080 Massenprozent,

N: 0,0080 Massenprozent oder weniger,

in einem Bereich, der die folgenden Formeln (1) und (2) erfüllt,

Ti als eine Verunreinigung: 0,005 Massenprozent oder weniger,

gegebenenfalls eines oder mehrere von

Cu: 0,5 Massenprozent oder weniger,

Ni: 0,5 Massenprozent oder weniger,

V: 0,1 Massenprozent oder weniger,

und wobei der Rest Fe und zufällige Verunreinigungen sind:



wobei [%M] den Gehalt des Elements M (Massenprozent) bedeutet.

Revendications

1. Acier de cémentation ayant une composition chimique constituée de

C : de 0,10 % en masse à 0,35 % en masse,

Si : de 0,01 % en masse à 0,13 % en masse,

Mn : de 0,30 % en masse à 0,80 % en masse,

P : 0,02 % en masse ou moins,

S : 0,03 % en masse ou moins,

Al : de 0,01 % en masse à 0,045 % en masse,

Cr : de 0,5 % en masse à 3,0 % en masse,

B : de 0,0005 % en masse à 0,0040 % en masse,

Nb : de 0,003 % en masse à 0,080 % en masse,

N : 0,0080 % en masse ou moins

dans une plage satisfaisant les formules (1) et (2) suivantes,

Ti en tant qu'impureté : 0,005 % en masse ou moins,

éventuellement l'un ou plus parmi

Cu : 0,5 % en masse ou moins,

Ni : 0,5 % en masse ou moins,

V : 0,1 % en masse ou moins,

le reste étant du Fe et des impuretés inévitables :



où [%M] représente la teneur en élément M (% en masse).

Drawing