JP5512231B2 - ERW steel pipe for drive shaft with excellent static torsional strength and method for manufacturing the same - Google Patents

Description

  The present invention relates to an electric resistance welded steel pipe for a hollow drive shaft that is excellent in static torsional strength characteristics and is used as an automobile part, and a method for producing the same.

  In general, in parts used for automobiles, particularly drive shafts, one of the required characteristics is static torsional strength. Conventionally, many solid parts have been used for drive shafts, but with the recent reduction in weight of automobiles, the demand for hollow drive shafts has increased. For this reason, a hollow drive shaft component excellent in static torsional strength has been required. In order to improve the static torsional strength characteristics, it is generally known that it is effective to increase the hardness and strength.

Patent Document 1 discloses that the inner peripheral surface is subjected to thermal effect treatment (heat treatment) over substantially the entire surface in the axial direction. For example, it is described that heat treatment is performed on the entire depth region from the outer peripheral surface to the inner peripheral surface by induction hardening and tempering from the outer peripheral surface of the hollow drive shaft to almost the entire surface.
Patent Document 2 also describes that heat treatment is performed on the entire depth region from the outer peripheral surface to the inner peripheral surface by induction hardening and tempering from the outer peripheral surface of the hollow drive shaft to almost the entire surface. Has been.

Patent Document 3 discloses that the hollow drive shaft is subjected to surface quenching at a quenching rate of 0.7 to 0.9 in order to make the static strength and fatigue strength higher than the solid strength. Here, the quenching rate is defined by a quenching depth H and a thickness of 400 Hv or more.
Patent Documents 4 and 5 describe manufacturing methods for leaving an uncured layer on the inner surface while ensuring a predetermined quenching depth from the outer surface.
Patent Document 6 discloses that the hardness ratio between the welded portion and the base material portion and the ratio between the ferrite band structure and the wall thickness are specified in order to satisfy the torsional strength of the hollow drive shaft.

As described above, as a means for improving the static torsional strength of the hollow drive shaft, generally, a method of defining the hardness in the thickness direction over the entire axial direction has been adopted. However, even in the parts manufactured by such a method, the high static torsional strength characteristics required in accordance with the recent performance improvement of automobiles and the like cannot be secured stably and sufficiently.
Moreover, it is requested | required that it may become a fracture | rupture form perpendicular | vertical with respect to an axial direction also as a fracture | rupture form at the time of a static torsion test.
In this way, in order to obtain a high static torsional strength and an optimal fracture mode, in addition to the method of ensuring the minimum hardness, other metallurgical factors are also considered as a steel structure factor. There was a need to manufacture.

JP 2002-349538 A JP 2002-356742 A JP 2003-90325 A JP 2006-2809 A JP 2006-2185 A JP 2004-162125 A

  The present invention has been made in view of the above-mentioned problems. In particular, automotive parts, in particular, electric shafts for drive shafts, which are cold-worked into a predetermined shape by hot working and subjected to induction hardening to form hollow parts. An object of the present invention is to provide an electric-sealed steel pipe for a drive shaft that is excellent in static torsional strength and a manufacturing method thereof.

  The gist of the present invention is as follows.

[1] Steel component is mass%, C: 0.25 to 0.55%, Si: 0.35% or less, Mn: 0.600 to 1.50%, Al: 0.001 to 0.060 %, O: 0.0001 to 0.0025 %, S: 0.0025% or less, P: 0.010% or less, N: 0.005% or less, B: less than 0.0003%, and the balance Fe And the relationship between the minimum hardness (Hv) of the cross section perpendicular to the pipe axis direction of the ERW steel pipe and the prior austenite grain size number (GS) of the cross section (1) ERW steel pipe for drive shafts with excellent static torsional strength, characterized by satisfying
0.25Hv-65GS + 500> 0 (1)
[2] The steel component is further in mass%, Cr: 0.05 to 1.00%, Mo: 0.05 to 1.00%, Ni: 0.10 to 2.00%, Cu: 0.00. 10 to 2.00%, Nb: 0.001 to 0.20%, V: 0.001 to 0.20%, Ti: 0.001 to 0.20%, Mg: 0.0001 to 0.0050% Ca: 0.0001 to 0.0100% of one or more of them are contained, [1] The electric-welded steel pipe for drive shafts having excellent static torsional strength according to the above [1].
[3] A method for producing an electric resistance welded steel pipe for a drive shaft according to [1] or [2], wherein the electric resistance welded steel pipe having the steel component according to [1] or [2] is formed. The drive shaft excellent in static torsional strength, wherein the electric resistance welded steel pipe is quenched at a temperature of 900 ° C. or higher and 1000 ° C. or lower and then tempered at a temperature of 100 ° C. or higher and 300 ° C. or lower . A method for manufacturing ERW steel pipes .

  According to the ERW steel pipe for a drive shaft having excellent static torsional strength and the manufacturing method thereof according to the present invention, an ERW steel pipe for driveshaft, which is a hollow part having excellent static torsional strength, can be obtained by the above configuration. Since it becomes possible to provide an electric resistance welded steel pipe for a drive shaft that can be satisfied as a component for automobiles and mechanical structures, the industrial effect is extremely large.

  DESCRIPTION OF THE PREFERRED EMBODIMENTS Embodiments of an electric resistance welded steel pipe for a drive shaft and a manufacturing method thereof according to the present invention will be described below. In addition, since this embodiment is described in detail for better understanding of the gist of the invention, the present invention is not limited unless otherwise specified.

The electric resistance welded steel pipe for drive shafts (hereinafter sometimes abbreviated as electric resistance welded steel pipe) having excellent static torsional strength according to the present invention has a steel component of mass%, C: 0.25 to 0.55%, Si: 0.35% or less, Mn: 0.600 to 1.50%, Al: 0.001 to 0.060%, O: 0.0001 to 0.0050%, S: 0.0025% or less, P : 0.010% or less, N: 0.005% or less, B: Less than 0.0003%, consisting of the balance Fe and inevitable impurities, the minimum hardness of the cross section perpendicular to the tube axis direction of the ERW steel pipe ( The relationship between Hv) and the prior austenite grain size number (GS) of the cross section satisfies the following formula (1).
0.25Hv-65GS + 500> 0 (1)

  In the ERW steel pipe of the present invention, the chemical composition, hardness, and austenite crystal grain size are defined in combination under specific conditions, and will be described in detail below for each requirement.

<Steel component>
Below, the reason for limitation about the steel component in this invention is demonstrated. In the present invention, an ERW steel pipe containing the following elements and having a steel component composed of the remaining Fe and inevitable impurities is used.
In addition, unless otherwise specified, the unit of content of each element in the following description shall be represented by mass%.

“C: Carbon” 0.25 to 0.55%
C is an element necessary for securing strength and high-frequency hardenability for automobiles and machine structural parts. However, if it is less than 0.25%, the strength of the final product is insufficient, and high-frequency hardenability is also achieved. It cannot be secured. On the other hand, if the C content exceeds 0.55%, it becomes rather hard and causes deterioration of cold workability.
Therefore, the C content is in the range of 0.25 to 0.55%.

“Si: silicon” 0.35% or less Si increases hardness by solid solution strengthening, and cold workability deteriorates.
Therefore, the Si content is set to 0.35% or less.

“Mn: Manganese” 0.600 to 1.50%
Mn is an element effective for ensuring induction hardenability, but if it is less than 0.600%, this effect is insufficient. On the other hand, when the content of Mn exceeds 1.50%, it becomes rather hard and causes deterioration of cold workability.
Therefore, the Mn content is in the range of 0.60 to 1.50%.

"Al: Aluminum" 0.001-0.060%
Al is a deoxidizing element and generates an oxide. When the Al content is less than 0.001%, there is no deoxidation effect, and when it exceeds 0.060%, the deoxidation effect is saturated.
Therefore, the Al content is in the range of 0.001 to 0.06%.

“O: oxygen” O: 0.0001 to 0.0050%,
O is a component inevitably contained in the steel and generates an oxide. It is difficult to control the O content to be less than 0.0001%, and when it exceeds 0.0050%, inclusions increase, and the torsional strength and fatigue strength are deteriorated.
Therefore, the content of O is set to a range of 0.0001 to 0.0050%.

“S: sulfur” 0.0025% or less S combines with Mn to form MnS. Since MnS may become a starting point of cracking in cold working, it is desirable that the content of S is as small as possible.
Therefore, the content of S is set to 0.0025% or less.

“P: Phosphorus” 0.010% or less P is a component inevitably contained in steel, but P causes grain boundary segregation and center segregation in steel and causes ductility deterioration. The content is limited to 0.010% or less.

“N: Nitrogen” N: 0.005% or less N is a component inevitably contained in steel, but if N is contained in a large amount, it causes toughness or ductility deterioration. Limited to 0.005% or less.

"B: Boron (boron)" B: less than 0.0003% B is an element effective for ensuring high-frequency hardenability, but if it is 0.0003% or more, the strength may vary.
Therefore, the B content is less than 0.0003%.

In this invention, after making each said element essential, 1 type or 2 types or more of each element demonstrated below can be added selectively.
Hereinafter, the reason for limiting the content of each selectively added element will be described.

"Cr: Chromium" 0.05-1.00%
Cr is an element effective for ensuring induction hardenability, but if it is less than 0.05%, this effect is insufficient. On the other hand, when the content of Cr exceeds 1.00%, it is rather hard and causes deterioration of cold workability.
Therefore, the Cr content is in the range of 0.05 to 1.00%.

"Mo: Molybdenum" 0.05-1.00%
Mo is an element effective for ensuring high-frequency hardenability, but if it is less than 0.05%, this effect is insufficient. On the other hand, if the Mo content exceeds 1.00%, it becomes rather hard and causes deterioration of cold workability.
Therefore, the Mo content is in the range of 0.05 to 1.00%.

“Ni: nickel” 0.10 to 2.00%,
Ni is an element effective for ensuring high-frequency hardenability, but if it is less than 0.10%, this effect is insufficient. On the other hand, if the Ni content exceeds 2.00%, it becomes rather hard and causes deterioration of cold workability.
Therefore, the Ni content is in the range of 0.10 to 2.00%.

"Cu: Copper" 0.10 to 2.00%
Cu is an element effective for ensuring induction hardenability, but if less than 0.10%, this effect is insufficient. On the other hand, if the Cu content exceeds 2.00%, it becomes rather hard and causes deterioration of cold workability.
Therefore, the Cu content is in the range of 0.10 to 2.00%.

“Nb: Niobium” 0.001 to 0.20%
Nb precipitates as NbCN because of its strong affinity with C and N. When quenching a hollow drive shaft, NbCN acts as pinning particles, and suppresses the growth of austenite crystal grains and suppresses coarsening of the grain size. However, if the Nb content is less than 0.001%, the above effect is insufficient. On the other hand, when the content of Nb exceeds 0.20%, precipitation hardening of NbCN becomes remarkable, resulting in deterioration of cold workability.
Therefore, the Nb content is in the range of 0.001 to 0.20%.

“V: vanadium” 0.001 to 0.20%,
V precipitates as VC because of its strong affinity with C. When quenching a hollow drive shaft, VC acts as pinning particles, and suppresses the growth of austenite crystal grains and suppresses coarsening of the grain size. However, when the V content is less than 0.001%, the above effect is insufficient. On the other hand, when the content of V exceeds 0.20%, precipitation hardening of VC becomes remarkable, which causes deterioration of cold workability.
Therefore, the V content is in the range of 0.001 to 0.20%.

“Ti: Titanium” 0.001 to 0.20%,
Ti precipitates as TiN because of its strong affinity with N. When quenching a hollow drive shaft, TiN acts as pinning particles, and has the function of suppressing the growth of austenite crystal grains and suppressing the coarsening of the grain size. However, when the Ti content is less than 0.001%, the above effects are insufficient. On the other hand, when the Ti content exceeds 0.20%, precipitation hardening of TiN becomes remarkable, which causes deterioration of cold workability.
Therefore, the Ti content is in the range of 0.001 to 0.20%.

“Mg: Magnesium” 0.0001 to 0.0050%
Mg is a deoxidizing element and generates an oxide. This oxide becomes a precipitation nucleus of MnS and is effective in fine and uniform dispersion of MnS. However, if the Mg content is less than 0.0001%, there is no effect, and if it exceeds 0.0050%, the yield is drastically lowered and the effect is saturated.
Therefore, the Mg content is in the range of 0.0001 to 0.0050%.

“Ca: calcium” 0.0001 to 0.0100%
Ca is effective for adjusting the form of inclusions in the base metal and the ERW weld and improving the cold workability. However, when there is too much content of Ca, the inclusion in steel will increase and conversely cold workability will deteriorate.
Therefore, the Ca content is in the range of 0.0001 to 0.0100%.

<Hardness and austenite grain size number>
In the present invention, the relationship between the minimum hardness (Hv) of the cross section perpendicular to the pipe axis direction of the ERW steel pipe and the prior austenite grain size number (GS) of the cross section is expressed by the following expression {0.25Hv−65GS + 500> 0}. It is considered to be a satisfactory configuration.
Hereinafter, the reasons for limiting the hardness and the austenite grain size will be described in detail.

  The torsional fatigue strength of the ERW steel pipe for drive shafts of the present invention, which is a hollow part made of a steel material induction-hardened after cold working according to the manufacturing conditions described later, has a correlation with the hardness of the part, improving the torsional fatigue strength. Therefore, it is necessary to increase the hardness. As a result of intensive studies by the present inventors, the steel material having the chemical components defined in the present invention has a relationship between the minimum hardness (HV) of hollow parts after normal induction hardening and the austenite grain size (GS). By satisfying the following formula {0.25Hv-65GS + 500> 0}, it was confirmed that the static torsional strength could be secured and the fracture occurred perpendicular to the axial direction of the drive shaft.

  On the other hand, the relationship between the minimum hardness (HV) and the austenite grain size (GS) of the electric resistance welded steel pipe for drive shafts of the present invention, which is a hollow part after induction hardening, is represented by the following formula {0.25Hv−65GS + 500 <0}. With such a relationship, it has been clarified that stable static torsional strength cannot be obtained and breakage occurs in the shear direction. Therefore, in the present invention, the ERW steel pipe is cold-worked and formed into a predetermined shape, and is minimum in the entire thickness direction and circumferential direction of the ERW steel pipe for drive shafts, which is a hollow part after induction hardening. The relationship between the hardness (Hv) and the austenite grain size number (GS) was represented by the following formula {0.25Hv−65GS + 500> 0}.

Note that the hardness of the cross section is measured at a load of 10 kg at a pitch of 1 mm from the inner surface to the outer surface in a cross section perpendicular to the tube axis direction. It can be measured by measuring the hardness in the thickness direction at the positions of 180 ° and 270 ° and determining the minimum hardness (Hv).
The austenite particle size number can be measured by corroding the cross section in the tube axis direction with a 3% nitric acid + 97% ethanol solution and observing the austenite particle size. At this time, in the field of view of 50 to 200 times, regions in the thickness direction and the circumferential direction can be taken with an optical micrograph, and the particle size number of austenite can be measured according to ASTM.

<Static torsional strength>
The static torsional strength described in the present invention is expressed by torsional shear stress. As a method of measuring the static torsional strength of ERW steel pipe, for example, using a torsional fatigue tester, gradually increasing the torsional angle, measuring the torque until it breaks, and using the test sample It can be measured by calculating the shear stress from the cross-sectional dimensions of a certain ERW steel pipe.

<Manufacturing method (manufacturing conditions)>
The method for producing an electric resistance welded steel pipe for a drive shaft having excellent static torsional strength according to the present invention, in producing the above-described electric resistance welded steel pipe of the present invention, after first forming an electric resistance welded steel pipe having the above steel components, The electric resistance welded steel pipe is quenched at a temperature of 900 ° C. or higher and 1000 ° C. or lower, and then tempered.

According to the manufacturing method of the present invention, a steel pipe is cold-worked and formed into a predetermined shape, subjected to induction hardening, and parts for automobiles and machine structures having desired characteristics. Finish in steel pipe. The method of induction hardening at this time is not particularly limited, and may be performed by a normal method in this field. Further, the steel pipe to which the present invention can be applied is not particularly limited as long as it satisfies the configuration of the present application by hollowing out not only an electric resistance steel pipe but also, for example, a steel bar.
Below, the manufacturing conditions prescribed | regulated by this invention are demonstrated in detail.

"Quenching temperature"
In the present invention, after forming the ERW steel pipe, the quenching temperature when quenching the ERW steel pipe is defined as a temperature of 900 ° C. or higher and 1000 ° C. or lower. When the quenching temperature is less than 900 ° C., the hardenability is lowered, and the static torsional strength does not satisfy the predetermined strength. On the other hand, if the quenching temperature exceeds 1000 ° C., the austenite grain size becomes coarse and the toughness is lowered, and no fracture perpendicular to the axial direction occurs. Accordingly, the quenching temperature range is set to 900 ° C. or higher and 1000 ° C. or lower.

“Tempering treatment temperature”
In the production method of the present invention, the tempering temperature in the tempering treatment is preferably in the range of 100 ° C. or more and 300 ° C. or less. When the tempering temperature is 100 ° C. or lower, hydrogen diffusion becomes insufficient and there is a concern that cracking may occur. On the other hand, if the quenching temperature exceeds 300 ° C., the structure is recovered due to tempering, and static torsional strength cannot be ensured. Therefore, the range of the tempering temperature is set to 100 ° C. or more and 300 ° C. or less.

  As described above, according to the ERW steel pipe for a drive shaft having excellent static torsional strength and a method for manufacturing the same according to the present invention, the drive shaft that is a hollow part having excellent static torsional strength is provided by the above configuration. Since the electric resistance welded steel pipe can be obtained, it is possible to provide an electric resistance welded steel pipe for a drive shaft that is satisfactory as a part for automobiles and machine structures. Therefore, the industrial effect is extremely large.

  Hereinafter, the present invention will be described in more detail by giving examples of the drive shaft electric resistance welded steel pipe excellent in static torsional strength of the present invention and its manufacturing method, but the present invention is originally limited to the following examples. However, the present invention can be carried out with appropriate modifications within a range that can meet the gist of the preceding and following descriptions, and these are all included in the technical scope of the present invention.

[Manufacture of ERW steel pipe]
In the steel making process, the deoxidation / desulfurization and chemical components of the molten steel are controlled, and by continuous casting, the chemical components composition shown in Table 1 below is used, and the steel thicknesses 1 to 16 are set to the plate thicknesses shown in Table 2 below. A steel strip was produced. Next, these steel strips were continuously formed into a tubular shape with the outer diameters shown in Table 2 below, and then the edge portions of the tubular steel strips were welded by high frequency welding. Next, the obtained tubular steel strip was tempered at 900 ° C. or higher and 1000 ° C. or lower under the conditions shown in Table 2 below, and then tempered at a temperature of 100 ° C. or higher and 300 ° C. or lower. ˜16 ERW steel pipes were produced.

[Evaluation test]
The electric resistance welded steel pipe manufactured by the above method was subjected to the following evaluation test, and the results are shown in Table 3 below.
First, as the minimum hardness (Hv), the minimum hardness was determined from the hardness distribution in the thickness direction by a Vickers hardness meter. The load at this time was 10 kg.
As for the austenite particle size number, the section in the tube axis direction was corroded with 3% nitric acid + 97% ethanol solution, and the austenite particle size was observed. At this time, the region in the thickness direction and the circumferential direction is photographed with an optical micrograph in a field of view of 50 to 200 times, and the austenite grain size number is derived by measuring the austenite grain size in accordance with ASTM. It was.

The static torsional strength is calculated from the cross-sectional dimensions of the ERW steel pipe using a commercially available torsional fatigue tester, measuring the torque until the torsion angle is gradually increased while gradually increasing the torsion angle. Measured by determining the shear stress.
Moreover, about the fracture | rupture form, it confirmed by observing the fracture surface of the ERW steel pipe fractured | ruptured by the test using the said torsional fatigue testing machine by scanning electron microscope.

  A list of chemical composition of the ERW steel pipe of this example is shown in Table 1, and a list of conditions of the outer diameter and thickness (sheet thickness), quenching temperature, and tempering temperature of the ERW steel pipe is shown in Table 2 below. Table 3 below shows a list of evaluation results of minimum hardness (Hv), austenite grain size number, static torsional strength, and fracture mode.

[Evaluation results]
Steel numbers 1 to 12 shown in Tables 1 to 3 are examples of the present invention that satisfy the respective specifications of the present invention, and steel numbers 13 to 16 are comparative examples in which any requirement is outside the specified range of the present invention. It is.
As shown in the evaluation result list of Table 3, steel strips having steel components specified in the present invention were formed and welded, and the steel Nos. 1 to 12 were subjected to quenching treatment and tempering treatment specified in the present invention. It was confirmed that the relationship between the minimum hardness (Hv) and the austenite grain size number (GS) of the sewn steel pipe is a steel characteristic satisfying the following formula {0.25Hv−65GS + 500> 0}. These ERW steel pipes having steel numbers 1 to 12 have a static torsional strength exceeding 3500 Nm, achieving predetermined characteristics, and the fracture form is perpendicular to the axial direction, which is a good fracture form. I was able to confirm.

  On the other hand, the electric resistance welded steel pipes of steel numbers 13 to 16, which are comparative examples, cannot achieve a strength (3500 Nm) of static torsional strength or higher because any requirement is outside the specified range of the present invention. Or the fracture form did not become a form perpendicular to the axial direction.

In Steel No. 13, N in the steel component exceeds the upper limit defined in the present invention, and the quenching temperature is less than the lower limit defined in the present invention. For this reason, the relationship between the minimum hardness (Hv) and the austenite grain size number (GS) does not satisfy the following formula {0.25Hv-65GS + 500> 0}, and the static torsional strength is less than 3500 Nm and is insufficient. The fracture form of shear cracks was not obtained, and a form perpendicular to the axial direction could not be obtained.
In Steel No. 14, the quenching temperature exceeds the upper limit defined in the present invention. For this reason, the austenite grains are coarsened to form a fracture form of shear cracks, a form perpendicular to the axial direction cannot be obtained, and the static torsional strength cannot achieve a predetermined strength.

Moreover, in the steel number 15, the tempering temperature exceeds the upper limit prescribed | regulated by this invention. For this reason, the relationship between the minimum hardness and the austenite grain size number does not satisfy the following formula {0.25Hv-65GS + 500> 0}, and a desired static torsional strength of 3500 Nm or more cannot be obtained.
In Steel No. 16, since the tempering temperature is less than the lower limit specified in the present invention, hydrogen cracking occurs, and the desired static torsional strength of 3500 Nm or more cannot be obtained. The fracture form perpendicular to the direction was not obtained.

In Steel Nos. 17 and 19, the amount of C or Mn is less than the lower limit specified in the present invention, so the relationship between the minimum hardness and the austenite grain number is represented by the following formula {0.25Hv-65GS + 500> 0}. The desired static torsional strength of 3500 Nm or higher was not obtained.
Steel No. 18 has an amount of C exceeding the upper limit defined in the present invention, so that hydrogen cracking occurs, the static torsional strength is insufficient at less than 3500 Nm, and the hydrogen cracking form is broken. A shape perpendicular to the axial direction could not be obtained.
In Steel No. 20, the amount of Mn exceeded the upper limit defined in the present invention, so that the static torsional strength was insufficient at less than 3500 Nm, and a form perpendicular to the axial direction could not be obtained.

  From the results of the embodiments described above, the drive shaft ERW steel pipe excellent in static torsional strength and the manufacturing method thereof according to the present invention are excellent in static torsional strength and have a good fracture shape. It is clear that an ERW steel pipe is obtained.

Claims (3)

Steel component is mass%,
C: 0.25 to 0.55%,
Si: 0.35% or less,
Mn: 0.600 to 1.50%,
Al: 0.001 to 0.060%,
O: 0.0001 to 0.0025 %,
S: 0.0025% or less,
P: 0.010% or less,
N: 0.005% or less,
B: ERW steel pipe containing less than 0.0003% and comprising the balance Fe and inevitable impurities,
The static relationship characterized in that the relationship between the minimum hardness (Hv) of the cross section perpendicular to the pipe axis direction of the ERW steel pipe and the prior austenite grain size number (GS) of the cross section satisfies the following formula (1): ERW steel pipe for drive shafts with excellent torsional strength.
0.25Hv-65GS + 500> 0 (1) Steel component is further mass%,
Cr: 0.05-1.00%,
Mo: 0.05-1.00%,
Ni: 0.10 to 2.00%,
Cu: 0.10 to 2.00%,
Nb: 0.001 to 0.20%,
V: 0.001 to 0.20%,
Ti: 0.001 to 0.20%,
Mg: 0.0001 to 0.0050%,
Ca: 0.0001 to 0.0100%
1 or 2 or more types are contained among these, The electric-resistance-welded steel pipe for drive shafts excellent in the static torsional strength of Claim 1 characterized by the above-mentioned. A method for producing an electric resistance welded steel pipe for a drive shaft according to claim 1 or 2,
After the electric resistance welded steel pipe having the steel component according to claim 1 or 2 is formed, the electric resistance welded steel pipe is quenched at a temperature of 900 ° C or higher and 1000 ° C or lower, and then tempered at a temperature of 100 ° C or higher and 300 ° C or lower. A method for producing an electric resistance welded steel pipe for a drive shaft excellent in static torsional strength, characterized by performing tempering treatment at a temperature .