Patent Application
20060065328
The present invention relates to machine structural steel products. In more particular, the present invention relates to a machine structural steel product having superior formability of rotary-forming, quenching-crack resistance, and torsional properties. A steel product is provided which is a machine structural steel product manufactured using an electric furnace instead of a blast furnace and which retains various properties even when a tramp element such as Cu or Ni is incorporated.
Machine structural members such as drive shafts for automobile use and constant velocity joints have been requested to have a torsional strength at a required level. In order to ensure the torsional strength, heretofore, a hot-rolled steel bar has been generally processed by the steps of hot-forging, normalizing whenever necessary, cutting, cold-forging, and the like so as to have a predetermined shape, followed by induction hardening and tempering.
In recent years, for the environment conservation, attempts have been made to reduce the weight of automobile bodies in order to improve the automobile gasoline mileage. For the reduction in weight of automobile components, it has been desired that the torsional strength of automobile members be improved. In addition, in a manufacturing process for automobile components, machinability and quenching-crack resistance of steel products have also been required.
For improving the torsional strength, it has been considered that quenched hardness and hardness penetration depth are increased by induction hardening. However, in order to increase the quenched hardness and the hardness penetration depth, either the change in high-frequency hardening conditions or the increase of the amount of alloy elements in a steel product must be carried out. In both cases described above, the manufacturing cost is inevitably increased. In order to simultaneously satisfy the torsional strength, machinability, and quenching-crack resistance of automobile components, for example, as disclosed in Patent Document 1, a technique specifying the amount of alloy elements has been proposed.
However, only by specifying chemical components according to the technique mentioned above, a problem may arise in that the composition range is very small which simultaneously satisfies the machinability, quenching-crack resistance, and torsional properties. In addition, a problem of unstable quality has not been still solved.
Accordingly, in order to solve the problems described above, the inventors of the present invention proposed a machine structural steel product having superior machinability, quenching-crack resistance, and torsional properties as disclosed, for example, in Patent Document 2 in which the steel texture is controlled at the same time when the components of the steel product are appropriately adjusted.
Patent Document 1: Japanese Unexamined Patent Application Publication No. 4-218641 (Claims)
Patent Document 2: U.S. Pat. No. 3,288,563 (Claims)
However, it was found that when the machine structural steel product disclosed in Patent Document 2 is manufactured using an electric furnace, desired properties cannot be obtained, and in particular, degradation in formability of rotary-forming is significant. Compared to a steel product manufactured using a blast furnace, a tramp element such as Cu or Ni is inevitably incorporated into the steel product manufactured using an electric furnace. It is believed that the tramp elements deteriorate the formability of rotary-forming.
A primary object of the present invention is to solve the problems described above. That is, an object of the present invention is to provide a machine structural steel product which has superior quenching-crack resistance and torsional properties and which effectively prevents the degradation in formability of rotary-forming even when manufactured using an electric furnace instead of a blast furnace. In addition, a drive shaft formed from this steel product is also proposed.
Through long and intensive research carried out by the inventors of the present invention in order to achieve the above objects, the following findings were obtained.
The present invention was made on the above findings, and the particular aspects of the present invention are as follows.
C: 0.35% to 0.50%;
Si: 0.15% or less;
Mn: 0.20% to 1.1%;
P: 0.02% or less;
S: 0.005% to 0.035%;
Cr: more than 0.1% to 0.2%;
Mo: 0.05% to 0.5%;
Ti: 0.01% to 0.05%;
Al: 0.01% to 0.05%;
N: 0.01% or less;
B: 0.0005% to 0.0050%;
Cu: 0.06% to 0.25%; and
Ni: 0.05% to 0.2%,
wherein an LD value represented by the following equation (1) of 120 or less is satisfied, and the balance of the composition includes Fe and inevitable impurities.
In the above equation, C, Mn, P, S, Si, Cr, Ni, Mo, and Cu in the equation each indicate the content (mass percent) of the respective elements.
V: 0.01% to 0.30%, and
Nb; 0.005% to 0.05%.
Hereinafter, the present invention will be described in detail. The reasons the composition of a steel product of the present invention is specified in the above range will be described. In the present invention, “%” used for components indicates “mass percent”, unless otherwise stated.
C: 0.35% or More, 0.50% or Less
C is an element having the largest influence on the high-frequency hardenability and is an effective element for increasing the hardness and the depth of a hardened layer by quenching and for ensuring a torsional strength of 1,400 MPa or more after induction hardening and tempering. However, when the content is less than 0.35%, the effect of the carbon component is not sufficient, and when the content is more than 0.50%, the machinability and quenching-crack resistance are degraded. Accordingly, the C content is set in the range of from 0.35% to 0.50%.
Si: 0.15% or Less
In addition to a function as a deoxidizing element, Si is an element having a function of reinforcing steel when being dissolved in ferrite, thereby improving the torsional strength. The content is preferably more than 0.05%. However, when the Si content is more than 0.15%, the machinability is remarkably deteriorated, and hence the content is set to 0.15% or less.
Mn: 0.2% or More, 1.1% or Less
Mn is an effective element for improving the hardenability and increasing the hardness penetration depth in induction hardening, thereby contributing the improvement of the torsional strength. However, when the content is less than 0.2%, the effect of the Mn component is not sufficient. On the other hand, when the content is more than 1.1%, in addition to the formability of rotary-forming, the machinability and the torsional strength are also degraded. Accordingly, the content of Mn is set in the range of from 0.2% to 1.1%. Preferable content is in the range of from 0.2% to 0.8%.
P: 0.020% or Less
Since P is liable to segregate in austenite grain boundaries in quenching and to facilitate quenching-cracking, the content of P is preferably decreased as small as possible. From this point of view, the content is decreased to 0.020% or less.
S: 0.005% or More, 0.035% or Less
S forms MnS in steel and has a function of improving the machinability, and hence the content is set to 0.005% or more. However, since MnS tends to initiate cracking and causes the decrease in strength and toughness, the maximum content of S is set to 0.035%. Preferable content is in the range of from 0.010% to 0.035%.
Cr: More than 0.1%, 0.2% or Less
Cr is a particularly important element in the present invention, and when Cr is contained, the adverse influence of tramp elements such as Cu and Ni can be advantageously removed, the adverse influence being degradation in formability of rotary-forming, torsion properties, machinability, and the like. However, when the content of Cr is 0.1% or less, the effect of Cr component is not sufficient. On the other hand, when the content is more than 0.2%, since the formability of rotary-forming, machinability, and torsional strength are degraded, the content of Cr is set to more than 0.1% to 0.2%.
Mo: 0.05% or More, 0.5% or Less
Mo is not only effective for improving the hardenability but also has a function of facilitating the growth of bainite so as to improve the machinability. Hence, the content must be 0.05% or more; however, when the content is more than 0.5%, the machinability is adversely degraded. Accordingly, the content of Mo is set in the range of from 0.05% to 0.5%. Preferable content is in the range of from 0.1% to 0.5%.
Ti: 0.01% or More, 0.05% or Less
Ti forms a nitride with N and reduces the grain size of austenite in high-temperature heating. This element is essential for ensuring dissolved B that is effective for improving the hardenability. Hence, the content must be 0.01% or more; however, when the content is more than 0.05%, the toughness is degraded. Accordingly, the content of Ti is set in the range of from 0.01% to 0.05%.
Al: 0.01% or More, 0.05% or Less
Al is an effective element as a deoxidizing agent, and to obtain this effect, the content thereof must be at least 0.01%. However, when the content is more than 0.05%, giant alumina grains are grown and initiates fatigue damage, thereby decreasing the fatigue strength. Hence, the content of Ai is set in the range of from 0.01% to 0.05%.
N: 0.01% or Less
N is an effective element for forming a nitride with Al or Ti and for reducing the grain size of austenite in high-frequency heating, and hence the fatigue strength can be improved. However, when the content thereof is more than 0.01%, the nitride is coarsely grown, and the fatigue strength is adversely degraded. In addition, when an excessive amount of N is contained, BN is formed, and as a result, the amount of dissolved B component effective for improving the hardenability is disadvantageously decreased. Hence, the content of N is set to 0.01% or less.
B: 0.0005% or More, 0.0050% or Less
B has an effect of improving the torsional strength by improving the hardenability and by increasing the hardness penetration depth in high-frequency hardening. In order to obtain the above effect, the content thereof must be 0.0005% or more; however, when the content is more than 0.0050%, the toughness is decreased. Hence, the content of B is set in the range of from 0.0005% to 0.0050%.
Cu: 0.06% or More, 0.25% or Less
Cu is an element which is inevitably incorporated as a tramp element. When the content is more than 0.25%, degradation in formability of rotary-forming and the like may occur in some cases, and hence the content is set to 0.25% or less. On the other hand, when the content is decreased to less than 0.06%, the manufacturing cost is increased, and as a result, the content is set to 0.06% or more.
Ni: 0.05% or More, 0.2% or Less
Ni is an element which is inevitably incorporated as a tramp element. When the content is more than 0.2%, degradation in formability of rotary-forming and the like may occur in some cases, and hence the content is set to 0.2% or less. On the other hand, when the content is decreased to less than 0.05%, the manufacturing cost is increased, and as a result, the content is set to 0.05% or more.
The primary components are described above, and according to the present invention, in addition to those components, the following elements may also be optionally used.
V: 0.01% Mr more, 0.30% or Less, and Nb: 0.005% or More, 0.050% or Less
Both V and Nb form carbonitrides and reduce the grain size of austenite, thereby effectively contributing the improvement of strength. However, when the contents of V and Nb are less than 0.01% and less than 0.005%, respectively, the effects thereof are not sufficient. On the other hand, when the contents of V and Nb are more than 0.30% and more than 0.050%, respectively, a large and coarse material is precipitated, and the toughness is decreased thereby. Hence, the content of V is set in the range of from 0.01% to 0.30%, and the content of Nb is set in the range of from 0.005% to 0.050%.
Although the appropriate ranges of the components are described above, according to the present invention, it is not enough that the individual components simply satisfy the above ranges, and the individual components must be controlled so that the LD value represented by the following equation (1) is 120 or less.
In the above equation, C, Mn, P, S, Si, Cr, Ni, Mo, and Cu each indicate the content (mass percent) of the respective elements.
This LD value is the index of the texture and the hardness through the hardenability.
In this embodiment, the formability of rotary-forming are evaluated by a die life obtained in a form-rolling test.
As shown in the figure, in both cases, when the LD value is more than 120, the die life is rapidly decreased; however, when the LD value is 120 or less, the die life, that is, the formability of rotary-forming, of the high Cr and high Si steel of the present invention is much superior.
Accordingly, in the present invention, the components are controlled to obtain an LD value of 120 or less.
In the present invention, the steel texture is not particularly specified; however, a texture composed of ferrite as a primary component and approximately 5 to 30% of a bainite phase on an area percent basis is preferably used.
The steel product described above is most preferably used for power transmission devices, particularly for automobile drive shafts and constant velocity joints. In addition to the superior machinability, since the load carrying capacity is increased, a significant advantage, that is, weight reduction, can be obtained.
Next, preferable manufacturing conditions according to the present invention will be described.
A steel melting method for the steel product of the present invention may be performed by a known method and is not particularly limited. The machine structural steel of the present invention has superior formability of rotary-forming even when Cu or Ni is incorporated, which is difficult to be removed in steel melting performed by using an electric furnace, and hence the steel melting is preferably performed using an electric furnace. Vacuum degassing such as RH degassing, refining using ladles, and the like may be additionally performed. Molten steel is solidified by a continuous casting method or an ingot-making method and is then formed into materials having predetermined shapes through hot rolling or hot/warm forging. After processed by intermediate heat treatment, whenever necessary, such as normalizing, spheroidized annealing, or softening annealing, the materials thus obtained are finished into a desired shape by cold working such as cutting, forging, or form rolling.
In the present invention, the product having a predetermined shape is formed by hot rolling or hot forging, or is then further processed by normalizing. Cooling after the formation of austenite by this hot rolling or hot forging followed by normalizing or the like is preferably performed at a rate of approximately 0.2 to 2.0° C./sec in order to produce an appropriate amount of bainite. In particular, for a steel bar having a large diameter, accelerated cooling in which cooling is controlled is preferably performed.
In addition, final induction hardening and tempering may be performed by heating for approximately 0.2 to 1.0 second at an output of approximately 120 kW using a induction hardening apparatus at a frequency of approximately 15 kHz, followed by tempering at a temperature of 170° C. for approximately 30 minutes.
Steel having the composition shown in Table 1 was melted in a steel converter, followed by continuous casting to form a bloom having a size of 400×540 mm, and subsequently, a billet of 150 mm square was formed therefrom by hot rolling. Next, this billet was formed into a straight bar 25 mm in diameter by heating to 1,030° C., followed by hot rolling, and was then air-cooled at a cooling rate of 0.7° C./sec.
The results of measurement of the texture, formability of rotary-forming, torsional properties, and quenching-crack resistance of the bar steel thus formed are shown in Table 2.
The measurement method of the steel texture and the various properties are as follows.
After a photograph of the mictrotexture of the straight bar after cooling was taken using an optical microscope, the texture of the steel was identified from this photograph, and in addition, the area percent of a bainite phase was measured by an image analyzer.
The formability of rotary-forming were evaluated by the die life in accordance with a form-rolling test. The die life was determined by the number of material which was form-rolled until the form-rolling could not be further continued due to tooth tipping, peeling of a fracture surface, tooth abrasion, and the like.
The material of the die was SKD 11, and the spline data were as follows.
Tooth form: involute form, module: 1.27, pressure angle: 30°, number of teeth: 21, pitch diameter: 26.27 mm, large diameter: 28.1 mm, small diameter: 24.88 mm, over-pin diameter (pin 2.5 mm in diameter): 30.49 mm
After a torsion test piece in the form of a smooth round bar having a parallel portion 20 mm in diameter was formed from a straight bar and was then quenched at a frequency of 15 kHz using a induction hardening apparatus, tempering treatment at 170° C. for 30 minutes was performed, and the torsion test was then performed. The hardness penetration depth after the induction hardening and tempering was set to approximately 4 mm. The torsion test was performed by using a torsion tester of 4,900 J (500 kgf·m), and the maximum torsional shear strength was measured as the torsional strength.
For the measurement of the quenching-crack resistance, a round bar (20 mm in diameter) having a V-shaped groove on the surface thereof along the shaft direction was formed from the above straight bar 25 mm in diameter and was then processed by induction hardening equivalent to that described above. After 10 locations on a C cross-section of the round bar were polished and observed, the evaluation was performed by the number of generated cracks.
For the test of the machinability, an opening having a length of 12 mm was formed using a drill made of SKH 4 having a diameter of 4 mm at a rotation speed of 1,500 rpm, and the operation described above was repeated until the formation of the opening could not be further continued, thereby obtaining the total length (mm) of the openings. This total length of the openings thus formed was evaluated as a tool life.
As can be apparently seen from Table 2, the steel products obtained according to the present invention have superior formability of rotary-forming, torsional properties, quenching-crack resistance, and machinability.
The static strength and the fatigue strength of a drive shaft, which was formed from the steel product of the present invention provided with a hardened layer by induction hardening and tempering, will be described with reference to
According to the present invention, adverse influences of tramp element can be removed even from a machine structural steel product manufactured by using an electric furnace, the tramp elements being inevitably incorporated in the steel product. A steel product can be obtained having superior formability of rotary-forming, torsional properties, quenching-crack resistance, and hardenability. In particular, when the steel product according to the present invention is used for forming power transmission devices, such as automobile drive shafts and velocity constant joints, in addition to superior machinability, significant advantage, that is, weight reduction, can be obtained due to the high strength.
*F: Ferrite, P: Perlite, B: Balnite
| Number | Date | Country | Kind |
|---|---|---|---|
| 2002-304190 | Oct 2002 | JP | national |
| Filing Document | Filing Date | Country | Kind | 371c Date |
|---|---|---|---|---|
| PCT/JP02/13564 | 12/26/2002 | WO | 3/7/2005 |
