JP2007296563A - Friction welding method for steel and aluminum alloy - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a friction welding method for steel and an aluminum alloy by which an improved high strength can be obtained in the friction welding for a hollow member of steel and another hollow member of an age-hardening aluminum alloy. <P>SOLUTION: In the method where the edge faces of the hollow members are butted, and the edge faces are welded by friction welding, the aluminum alloy is the age-hardening alloy of Al-Cu-Mg base, Al-Si-Mg base or Al-Zn-Mg base subjected to artificial aging treatment, and the artificial aging treatment heating within the temperature range of 100 to 200°C is performed again after performing the friction welding. <P>COPYRIGHT: (C)2008,JPO&INPIT

Description

  The present invention relates to a friction welding method for a steel hollow member and an aluminum alloy hollow member.

  Conventionally, in the case of an automobile propeller shaft, axle housing, torsion bar, etc., when it is intended to realize a structure in which members made of steel hollow members are partially replaced with aluminum alloy hollow members, steel and aluminum It is necessary to join the alloy, but when steel and aluminum alloy are joined by fusion welding such as MIG welding, TIG welding or electron beam welding, iron and aluminum form a brittle intermetallic compound. It becomes impossible.

  On the other hand, since friction welding does not generate a liquid phase during joining, it is one of the few methods that enables joining of steel and aluminum alloy, but in reality, friction welding of steel and aluminum alloy is not easy, and aluminum alloy The current situation is that a bonding strength close to the base metal strength is not obtained. The reason for this is that, when joining similar materials such as steel or aluminum alloys, the oxide layer and contaminants present on the surface of the material are discharged into the burrs generated during pressure welding, whereas the strength difference between steel and aluminum alloys is different. In high pressure dissimilar materials, high strength materials such as steel are not deformed, so oxide layers and contaminants are likely to remain at the bonding interface, and a small amount of intermetallic compounds are formed at the bonding interface. This is because the metal flow of a hollow member such as a tube tends to be non-uniform inside and outside the tube of the hollow member.

In order to improve the joint strength in friction welding between steel and aluminum alloy, for example, an improvement of the pressure welding method by mechanical control of a pressure welding machine (for example, see Patent Document 1) is proposed, and an aluminum alloy excellent in pressure welding property is also proposed. (For example, refer to Patent Document 2) However, even in the proposed friction welding, the vicinity of the joint surface is heated to about 500 ° C. in a short time, but in the case of an age-hardened alloy of an aluminum alloy. In this case, a softened layer is formed due to thermal effects within a certain area from the joint surface, and the part affected by heat is discharged to some extent as burrs during upsetting, so it is not possible to make the softened layer thinner by increasing the upset pressure. However, it cannot be completely eliminated, and the strength of the softened layer and the strength of the interface itself govern the strength of the bonding material. It becomes inferior than that of the base material of chloride alloy.
Japanese Patent Laid-Open No. 5-138371 JP 2001-234268 A

  In friction welding of steel and aluminum alloy, a softened layer with low strength is formed on the side of the aluminum alloy near the interface due to the heat effect of frictional heat. The thickness of the softened layer is usually 2 mm to 8 mm depending on the joining conditions. In the friction welding of steel and aluminum alloy, the formation of a softened layer is inevitable, and the strength of the interface between the steel and the aluminum alloy itself and the strength of the softened layer determine the strength of the bonding material.

  In the process of examining friction welding of steel pipes and age-hardened Al-Cu-Mg alloy pipes, Al-Si-Mg alloy pipes, and Al-Zn-Mg alloy pipes that have been artificially aged. It was found that the strength of the softened layer can be increased while maintaining the strength of the interface itself by heat treatment in a specific temperature range after the friction pressure bonding.

  The present invention has been made on the basis of the above findings, and the object thereof is improved high strength in friction welding of a hollow member of steel such as a steel pipe and a hollow member of the aluminum alloy such as an age-hardening type aluminum alloy pipe. It is an object of the present invention to provide a method for friction welding of steel and aluminum alloy that makes it possible to obtain the above.

  In order to achieve the above object, the friction welding method of steel and aluminum alloy according to claim 1 is a method in which the end faces of a hollow steel member and an aluminum alloy hollow member are butted and joined together by friction welding. The alloy is an Al-Cu-Mg, Al-Si-Mg, Al-Zn-Mg, age-hardened alloy that has been artificially aged, and after friction welding, again in the temperature range of 100-200 ° C. It is characterized by performing an artificial aging treatment for heating.

The method of friction welding of steel and aluminum alloy according to claim 2 is a method in which the end surfaces of a steel hollow member and an aluminum alloy hollow member are butted together and the end surfaces are joined to each other by friction welding. , Al-Si-Mg, Al-Zn-Mg based age-hardening type alloys that have been subjected to artificial aging treatment. After friction welding, the artificial aging treatment is performed again in the temperature range of 100 to 200 ° C for t seconds. It is characterized by giving.
However, t (second) is 2 × 10 ⁻¹⁶ · (T + 273) · exp [Q / {8.314 (T + 273)}] ≦ t ≦ 18 × 10 ⁻¹⁶ · (T + 273) · exp [Q / {8 .314 (T + 273)}] (T: temperature (° C.), Q: 145000 in the case of Al—Cu—Mg alloy and Al—Si—Mg alloy, Al—Zn—Mg alloy 130,000 in case)

  The friction welding method for steel and aluminum alloy according to claim 3 is characterized in that, in claim 1 or 2, the hollow member is a tube.

  According to the present invention, the friction welding of a steel hollow member and an age-hardening aluminum alloy, Al-Cu-Mg, Al-Si-Mg, and Al-Zn-Mg aluminum alloy hollow member is improved. A method of friction welding of steel and aluminum alloy that makes it possible to obtain high strength is provided.

  INDUSTRIAL APPLICABILITY The present invention is particularly effective when applied to friction welding between a steel pipe and the above-described aluminum alloy pipe. In an automobile member such as a propeller shaft, an axle housing, and a torsion bar, a member made of steel is partially made of an aluminum alloy. This is applied when the structure is replaced with, and is effective for weight reduction.

  The present invention friction-welds a steel hollow member and an age-hardened aluminum alloy hollow member that has been aged in any of Al—Cu—Mg, Al—Si—Mg, and Al—Zn—Mg. In this case, the end surfaces of both hollow members are brought into contact with each other and the end surfaces are joined to each other by friction welding, and then an artificial aging treatment is performed again in a temperature range of 100 to 200 ° C.

The artificial aging treatment is preferably performed in the temperature range of 100 to 200 ° C. for t seconds. t (seconds) is short because the precipitation proceeds fast at high temperatures, and needs to be long because precipitation proceeds slowly at low temperatures. Therefore, t (seconds) is a kinetic parameter including temperature T (K). It is prescribed as follows.
2 × 10 ⁻¹⁶ · T · exp (Q / {RT}) ≦ t ≦ 18 × 10 ⁻¹⁶ · T · exp (Q / {RT}) Here, T is the absolute temperature (K), R is the gas constant of 8.314 (J / mol / K), Q is the activation energy of precipitation, and the Al—Cu—Mg and Al—Si—Mg alloys In this case, 145000 (J / mol), and in the case of an Al—Zn—Mg based alloy, 130,000 (J / mol).

If the temperature is Celsius (℃),
2 × 10 ⁻¹⁶ · (T + 273) · exp [Q / {8.314 (T + 273)}] ≦ t ≦ 18 × 10 ⁻¹⁶ · (T + 273) · exp [Q / {8.314 (T + 273)}] expressed. However, T is temperature (° C.), and Q is 145000 in the case of Al—Cu—Mg alloy and Al—Si—Mg alloy, and 130,000 in the case of Al—Zn—Mg alloy.

The heating can be held isothermally at a specific temperature within 100 to 200 ° C, but is not necessarily held isothermally, and is a two-stage aging that holds twice at different temperatures within 100 to 200 ° C, for example 150 ° C After holding at a temperature for a time, hold at a temperature of 180 ° C. for a time and set the total heating time to a time in the above range, or a method of aging with a temperature gradient with a temperature gradient, for example from 120 ° C. A method of increasing the temperature up to 160 ° C. over the time in the above range, a method of decreasing the temperature from 180 ° C. to 150 ° C. over the time in the above range, or the above range within a temperature range of 100 to 200 ° C. It is also possible to employ a method of increasing the temperature, raising and lowering the time. The heating time t in these methods is a time obtained by adding the holding time t _n at the aging temperature T _n (° C.) as shown below.
2 × 10 ⁻¹⁶ · exp [Q / {8.314 (T + 273)}] ≦ Σ {t _n / (T _n +273)} ≦ 18 × 10 ⁻¹⁶ · exp [Q / {8.314 (T + 273)} ]

After joining by friction welding, the aging treatment is performed under the above conditions, so that the softened layer softened by the heat effect is age-hardened again while maintaining the strength of the joining interface, and the strength of the joining material is increased. Can do. When the heating time t is shorter than 2 × 10 ⁻¹⁶ · (T + 273) · exp [Q / {8.314 (T + 273)}], it is difficult to improve the strength of the softened layer while maintaining the strength of the bonding interface. And the strength of the bonding material is not improved. When the heating time t exceeds 18 × 10 ⁻¹⁶ · (T + 273) · exp [Q / {8.314 (T + 273)}], the strength of the bonding interface itself is lowered. Although the exact reason is not clear, it is considered that preferential precipitation at the bonding interface proceeds and the interface strength is lowered. Furthermore, once the softened layer whose strength has been improved is softened again, the entire aluminum alloy is softened and the strength is lowered.

  Examples of the present invention will be described below in comparison with comparative examples to demonstrate the effects. These examples show one embodiment of the present invention, and the present invention is not limited thereto.

Example 1
Friction welding was performed using a combination of a steel pipe STKM13A having an outer diameter of 60.5 mm and a thickness of 3.1 mm and an aluminum alloy pipe 6061-T6 having the same diameter and the same thickness. The steel pipe was on the rotation side, and the rotation speed was 1200 rpm. Of the friction welding conditions, Table 1 shows the friction pressure P1, the friction margin U1, and the upset pressure P2. As for the brake timing, the rotary brake and the upset pressure load are applied immediately after the friction process is completed, that is, the timing is shifted, and the upset time T2 is set to 8 seconds. These conditions are within the range of conditions necessary for satisfactorily bonding STKM13A and 6061-T6.

  After the pressure welding, the bonded pipes were subjected to the heat treatment shown in Table 1, and after the heat treatment, the pipes were cut longitudinally to cut out strip-shaped test pieces and subjected to joint tensile tests. The test results are shown in Table 1. The joint efficiency is a ratio (%) of the tensile strength of the bonding material to the tensile strength 306 MPa of the base material 6061-T6.

  Invention material No. which was heat-treated according to the present invention. Nos. 1 to 9 are comparative materials No. 1 and No. 9 which are bonded under the same friction welding conditions and have no heat treatment. The tensile strength and joint efficiency are remarkably superior to those of 10, 15, and 17. On the other hand, the comparative material No. in which the heat treatment condition is out of the above range. Nos. 11 to 14, 16, 18, and 19 are comparative materials No. in which heat input in heat treatment is insufficient or heat input is excessive, and joined under the same pressure welding conditions and without heat treatment. The increase in tensile strength and joint efficiency is smaller or lower than that of 10, 15, and 17.

Example 2
Friction welding was performed using a combination of a steel tube STKM13A having an outer diameter of 50 mm and a thickness of 2 mm and an aluminum alloy tube 2024-T6 or 7N01-T6 having the same diameter and thickness. The steel pipe was on the rotation side and the rotation speed was 800 rpm. Of the friction welding conditions, Table 2 shows the friction pressure P1, the friction margin U1, and the upset pressure P2. As for the brake timing, the rotary brake and the upset pressure load are applied immediately after the friction process is completed, that is, the timing is shifted, and the upset time T2 is set to 8 seconds. These conditions are within the range of conditions necessary to satisfactorily join STKM13A and 2024-T6 or STKM13A and 7N01-T6.

  After the pressure welding, the joined pipes were subjected to the heat treatment shown in Table 2, and after the heat treatment, the pipes were cut longitudinally to cut out strip-shaped test pieces and subjected to joint tensile tests. The test results are shown in Table 2. The joint efficiency is a ratio (%) of the tensile strength of the bonding material to the tensile strength 477 MPa of the base material 2024 -T6 or the tensile strength 366 MPa of 7N01-T6.

  Invention material No. which was heat-treated according to the present invention. Nos. 20 to 27 are comparative materials No. 20 bonded under the same friction welding conditions and without heat treatment. The tensile strength and joint efficiency are remarkably superior to those of 28 and 31. On the other hand, the comparative material No. in which the heat treatment condition is out of the above range. Nos. 29, 30, 32, and 33 are comparative materials No. No. 29, 30, 32, and 33, which have insufficient heat input or excessive heat input, and are joined under the same pressure welding conditions and have no heat treatment. The amount of increase in tensile strength and joint efficiency is smaller or lower than 28 and 31.

Example 3
A steel pipe STKM15A (outer diameter 50 mm, thickness 2.4 mm) was used as the rotation side, and this was joined by friction welding with a 6082-T6 forged material having a hollow portion having the same shape as that of the steel pipe. FIG. 1 shows a cross-section (showing a cross section after welding). The joining end face of the steel pipe was processed so that the surface roughness was Ra: 7.0 μm. The friction welding conditions were P1: 25 MPa, P2: 110 MPa, U1: 0. 4 mm, N: 800 rpm (circumferential speed 2.09 m / s), brake timing P2L0.1s (rotation brake is applied after the friction process is completed, but the friction pressure is maintained for 0.1 second thereafter to delay the start of upset pressure load. ), T2: 4 s After pressure welding, heat treatment was performed after heating at 180 ° C. for 4 hours and then allowed to cool, and strip-shaped tensile test pieces were cut out and a tensile test was performed. Was 260 MPa, but it showed a high value of 307 MPa when heat-treated.

In Example 3, it is a figure which shows the longitudinal cross-section after carrying out the friction welding of the steel pipe and the 6062-T6 forging material.

Claims (3)

In a method in which the end surfaces of a hollow steel member and an aluminum alloy hollow member are butted and joined to each other by friction welding, the aluminum alloy is Al-Cu-Mg-based, Al-Si-Mg-based, Al-Zn-Mg-based. A method of friction welding of steel and aluminum alloy, characterized in that the artificial aging treatment is an age-hardening type alloy that has been subjected to artificial aging treatment and is subjected to artificial aging treatment that is again heated in a temperature range of 100 to 200 ° C. after friction welding. In a method in which the end surfaces of a hollow steel member and an aluminum alloy hollow member are butted and joined to each other by friction welding, the aluminum alloy is Al-Cu-Mg-based, Al-Si-Mg-based, Al-Zn-Mg-based. A friction-welding method for steel and aluminum alloy, characterized in that it is an age-hardening type alloy that has been subjected to artificial aging treatment and is subjected to artificial aging treatment that is heated again in a temperature range of 100 to 200 ° C. for t seconds after friction welding. .
However, t (second) is 2 × 10 ⁻¹⁶ · (T + 273) · exp [Q / {8.314 (T + 273)}] ≦ t ≦ 18 × 10 ⁻¹⁶ · (T + 273) · exp [Q / {8 .314 (T + 273)}] (T: temperature (° C.), Q: 145000 in the case of Al—Cu—Mg alloy and Al—Si—Mg alloy, Al—Zn—Mg alloy 130,000 in case) 3. The method of friction welding of steel and aluminum alloy according to claim 1, wherein the hollow member is a pipe.

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