WO2015045299A1 - 構造用鋼の摩擦撹拌接合方法および構造用鋼の接合継手の製造方法 - Google Patents
構造用鋼の摩擦撹拌接合方法および構造用鋼の接合継手の製造方法 Download PDFInfo
- Publication number
- WO2015045299A1 WO2015045299A1 PCT/JP2014/004657 JP2014004657W WO2015045299A1 WO 2015045299 A1 WO2015045299 A1 WO 2015045299A1 JP 2014004657 W JP2014004657 W JP 2014004657W WO 2015045299 A1 WO2015045299 A1 WO 2015045299A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- heating
- steel
- joining
- rotating tool
- stir welding
- Prior art date
Links
Images
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
- B23K20/12—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding
- B23K20/122—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding using a non-consumable tool, e.g. friction stir welding
- B23K20/123—Controlling or monitoring the welding process
- B23K20/1235—Controlling or monitoring the welding process with temperature control during joining
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
- B23K20/12—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding
- B23K20/122—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding using a non-consumable tool, e.g. friction stir welding
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
- B23K20/12—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding
- B23K20/129—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding specially adapted for particular articles or workpieces
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
- B23K20/22—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating taking account of the properties of the materials to be welded
- B23K20/227—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating taking account of the properties of the materials to be welded with ferrous layer
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
- B23K20/24—Preliminary treatment
Definitions
- the present invention is caused by inserting a rotating tool into an unjoined part of a workpiece and rotating it, moving it, softening the workpiece by frictional heat with the rotating tool, and stirring the softened part by the rotating tool.
- the present invention relates to a friction stir welding method that uses plastic flow to perform joining without adding a filler material.
- the present invention advantageously eliminates the plastic flow failure due to insufficient heating of the workpiece, which is a concern particularly when this friction stir welding method is applied to the joining of structural steel, It is intended to improve workability.
- a butt portion that is in a state where the steel plates are just butt but not yet joined is referred to as an “unjoined portion”, while a portion joined and integrated by plastic flow is referred to as a “joined portion”. Shall be called.
- Patent Document 1 As a friction welding method, in Patent Document 1, by rotating both or one of a pair of metal materials, the metal material generates frictional heat and softens, while the softened portion is stirred to cause plastic flow. Thus, a technique for joining metal materials is disclosed. However, since this technique rotates the metal material to be joined, there is a limit to the shape and size of the metal material to be joined.
- Patent Document 2 a tool made of a material that is substantially harder than a workpiece is inserted into an unjoined portion of the workpiece, and the tool and workpiece are moved by rotating the tool while rotating the tool.
- a method has been proposed in which workpieces are continuously joined in the longitudinal direction by heat and plastic flow generated between the two.
- the friction welding method described in Patent Document 1 is a method of rotating workpieces and welding them by frictional heat between workpieces.
- the friction stir welding method disclosed in Patent Document 2 can be joined by moving the tool while rotating the joining member. For this reason, there is an advantage that even a member that is substantially infinitely long in the welding direction can be continuously solid-phase bonded in the longitudinal direction.
- it since it is a solid phase joining using the plastic flow of the metal by the frictional heat of a rotary tool and a joining member, it can join, without melt
- the heating temperature is low, deformation after joining is small, and since the joint is not melted, there are few defects, and in addition, there is no need for a filler material.
- the friction stir welding method is a method of joining low melting point metal materials represented by aluminum alloys and magnesium alloys, and its use is expanding in the fields of aircraft, ships, railway vehicles, automobiles, and the like.
- the reason for this is that these low-melting-point metal materials are difficult to obtain satisfactory characteristics of joints by conventional arc welding methods, and improve the productivity and high quality by applying the friction stir welding method. This is because a joint can be obtained.
- the application of friction stir welding to structural steel which is mainly applied as a structural material such as buildings, ships, heavy machinery, pipelines, and automobiles, is subject to solidification cracking and hydrogen cracking, which are problems in conventional fusion welding. Since the structural change of the steel material is suppressed, it can be expected that the joint performance is excellent. In addition, since the clean surfaces can be brought into contact with each other by stirring the bonding interface with a rotating tool, a merit that a preparatory step such as diffusion bonding is unnecessary can be expected. Thus, the application of the friction stir welding method to structural steel is expected to have many advantages. However, since the problem remains in joining workability, such as suppression of defect generation at the time of joining and an increase in joining speed, it has not been widely used as compared with low melting point metal materials.
- Patent Documents 5 and 6 disclose a joining method in which a heating means other than frictional heat generated between the rotary tool and the material to be joined is added for the purpose of improving the joining workability.
- Patent Document 5 includes a heating unit using an induction heating device, and by heating the workpieces before and after joining, friction that increases the joining speed and eliminates cracks in the joined part.
- a heating device of the stir welding method is disclosed.
- Patent Document 6 has a heating means using a laser device, and by partially heating the workpieces immediately before bonding, the bonding speed is suppressed while suppressing the microstructure change around the heating region due to preheating.
- a friction stir welding apparatus that achieves a higher speed is disclosed.
- the present invention has been developed in view of the above situation, and advantageously eliminates plastic flow defects due to insufficient heating of workpieces during friction stir welding of structural steel, and has sufficient strength and bonding workability.
- the purpose is to improve.
- a friction stir welding method in which the pre-heat treatment process conditions are scrutinized is provided.
- the inventors examined various preheat treatment process conditions before friction stir welding. as a result, c) By using a heat source with a high energy density such as a laser, the surface temperature, area, and position of the heating area in the pre-heat treatment process are strictly controlled, and the temperature in the thickness direction of the heating area is also adjusted as necessary. Control appropriately. As a result, it has been found that the joining workability can be improved without causing deterioration of the jointed joint properties such as the jointed joint strength.
- the gist configuration of the present invention is as follows. 1.
- T S (° C.) of the surface of the steel sheet by the heating
- T S ⁇ 0.8 ⁇ T A1 T A1 is shown in the following formula (1)
- the heating region is a heating region
- the minimum distance between the heating region and the rotating tool on the surface of the steel sheet is equal to or less than the diameter of the shoulder of the rotating tool
- the area of the heating region on the surface of the steel sheet is not more than the area of the maximum diameter portion of the pin portion of the rotating tool
- 50% or more of the area of the heating region is a joining center line that is a straight line that passes through the rotation axis of the rotary tool and is parallel to the joining direction on the surface of the steel plate, and is parallel to the joining center line and is advanced.
- T A1 (°C) 723-10.7 [% Mn] -16.9 [% Ni] +29.1 [% Si] +16.9 [% Cr] +290 [% As] +6.38 [% W] (1)
- [% M] is the content (mass%) of the M element in the steel plate which is a workpiece.
- T D (° C.)
- T A1 T A1 are shown in the following equation (1)
- T A1 723-10.7 [% Mn] -16.9 [% Ni] +29.1 [% Si] +16.9 [% Cr] +290 [% As] +6.38 [% W] (1)
- [% M] is the content (mass%) of the M element in the steel plate which is a workpiece.
- the present invention in the friction stir welding of structural steel, it is possible to advantageously eliminate the plastic flow failure due to insufficient heating of workpieces, which has been a concern in the past, and to improve the joining workability. It is also possible to obtain a high joint strength at the joint by suppressing the change of the structure.
- the present invention is a friction stir welding method for structural steel, and as shown in FIG. 1, a rotating tool is inserted in an unjoined portion of a steel plate and moved in the joining direction while being rotated.
- the steel sheet is joined by softening the steel sheet by frictional heat between the rotating tool and the steel sheet, and agitating the softened portion with the rotating tool to cause plastic flow.
- the rotating tool includes a shoulder portion and a pin portion that is disposed on the shoulder portion and shares the rotation axis with the shoulder portion, and at least the shoulder portion and the pin portion are made of a material harder than a steel plate that is a workpiece. It is formed.
- reference numeral 1 is a rotating tool
- 2 is a rotating shaft
- 3 is a steel plate
- 4 is a joint
- 5 is a heating means
- 6 is a cooling means
- 7 is a rear heating means
- 8 is a shoulder of the rotating tool
- 9 is rotating. It is a pin part of the tool
- ⁇ indicates the rotation tool inclination angle.
- AS” and “RS” represent an advancing side and a retreating side, respectively.
- the advanced side is defined as the side where the tool rotation direction and the joining direction coincide with each other
- the retreating side is defined as the side where the tool rotation direction and the joining direction are opposite to each other.
- reference numeral 10 denotes a joining center line
- this joining center line indicates a straight line passing through the rotation axis of the rotary tool on the surface of the steel plate and parallel to the joining direction.
- 11 is a straight line (hereinafter referred to as an AS line) parallel to the joining center line and separated from the advanced side by the same distance as the maximum radius of the pin portion of the rotary tool
- 12 is a heating region
- 13 is Cooling region
- 14 is a reheating region
- a is the shoulder diameter of the rotating tool
- b is the maximum diameter of the pin portion of the rotating tool
- X is the minimum distance between the heating region and the rotating tool
- D is the heating region.
- the thickness of the steel sheet is indicated by t.
- the steel plates to be joined by the friction stir welding method of the present invention usually have a strength of about 30% of the strength at normal temperature at a temperature of about 80% of TA1 , which is the transformation temperature of the steel. . Moreover, when it becomes higher than this temperature, intensity
- the surface temperature T S (° C.) of the steel sheet in the heating region is set to 0.8 ⁇ T A1 ° C. or higher.
- T A1 (° C.) can be obtained by the following equation (1).
- T A1 (°C) 723-10.7 [% Mn] -16.9 [% Ni] +29.1 [% Si] +16.9 [% Cr] +290 [% As] +6.38 [% W] (1)
- [% M] is the content (mass%) of the M element in the steel sheet as the workpiece.
- the surface temperature of the steel plate in the heating region may be 1.5 ⁇ TM ° C. or less. preferable.
- the surface temperature of the steel sheet in the heating region is set to T M before contacting the rotating tool passing through the heating region. It is preferable to make it less than ° C. Note that T M (° C.) is the melting point of the steel sheet as the workpiece.
- Minimum distance between the heating area on the surface of the steel sheet and the rotating tool less than the shoulder diameter of the rotating tool If the distance between the heating area on the surface of the steel sheet and the rotating tool becomes too large, the temperature in the heating area will decrease before joining. Therefore, the effect of preheating cannot be obtained sufficiently. For this reason, the minimum distance between the heating region on the surface of the steel plate and the rotating tool moving in the joining direction is set to be equal to or smaller than the diameter of the shoulder of the rotating tool.
- the diameter is preferably 0.1 times or more the shoulder diameter of the rotary tool.
- the diameter of the shoulder of the rotary tool is about 8 to 60 mm.
- the area of the heating region on the surface of the steel plate not more than the area of the maximum diameter portion of the pin portion of the rotating tool.
- the heating region becomes too large, the microstructure of the region and its peripheral region changes.
- region in the surface of a steel plate shall be below the area of the largest diameter part of the pin part of a rotary tool.
- the area of the heating region on the surface of the steel plate is preferably 0.1 times or more the area of the maximum diameter portion in the pin portion of the rotary tool.
- the maximum diameter of the pin part of the rotating tool is about 2 to 50 mm.
- the starting point of plastic flow is the advanced side Along the rotation direction of the rotary tool, it passes the front in the joining direction, the retreating side, and the rear in the joining direction, and the advanced side is the end point.
- the advanced side is the starting point of plastic flow
- the steel sheet, which is the workpiece is likely to be insufficiently heated, and when the plastic flow is insufficient and defects occur, most of them are on the advanced side. appear.
- the area of the heating region is positioned between the joining center line and the AS line parallel to the joining center line, and the advancing side is preferentially heated. It is possible to promote plastic flow, suppress generation of defects, and increase the bonding speed. Preferably it is 60% or more of the area of a heating area, More preferably, it is 80% or more of range. It may be 100%. Further, from the viewpoint of preferentially heating the advanced side, the center of the heating region is positioned between the AS line and a straight line passing through the midpoint between the junction center line and the AS line.
- the center of the heating area is positioned on the advanced side with respect to the joining center line, and the distance from the heating area center to the joining center line is 0.5 times or more and 1 time or less of the maximum radius at the pin part of the rotating tool. It is preferable that
- the steel plates to be joined by the friction stir welding method of the present invention usually have a strength of about 30% of the strength at normal temperature at a temperature of about 80% of TA1 , which is the transformation temperature of the steel. Moreover, when it becomes higher than this temperature, intensity
- T D in the thickness direction of the heating area that defines the depth D of the heating zone to be described later shall be defined as 0.8 ⁇ T A1 ° C. or higher.
- T A1 (° C.) can be obtained by the following equation (1).
- T A1 (°C) 723-10.7 [% Mn] -16.9 [% Ni] +29.1 [% Si] +16.9 [% Cr] +290 [% As] +6.38 [% W] (1)
- [% M] is the content (mass%) of the M element in the steel sheet as the workpiece.
- a temperature gradient may exist in the thickness direction of the heating region, and in this case, the temperature in the thickness direction of the steel plate in the heating region is 1.5 ⁇ T M ° C.
- the temperature in the thickness direction of the steel sheet in the heating area is in contact with the rotating tool passing through the heating area in order to avoid damage to the rotating tool and alteration of the microstructure due to excessive rise in the temperature of the joint. It is preferable that the temperature is lower than T M ° C. Note that T M (° C.) is the melting point of the steel sheet as the workpiece.
- the depth D of the heating zone depth D of 30% or more heating areas in total thickness of the steel sheet, in a region where the temperature T D in the thickness direction of the heating region as described above is 0.8 ⁇ T A1 ° C. or higher, to be processed It is defined by the maximum depth from the surface of the steel plate.
- the depth D of the heating region is preferably 30% or more of the total thickness of the steel plates. This is because the plastic flow is further promoted by setting the depth D of the heating region to 30% or more of the total thickness of the steel sheet. This is because it is more advantageous in reducing the load on the rotary tool and increasing the joining speed. More preferably, it is 50% or more of the total thickness of the steel plates.
- the depth D of the heating region exceeds 90% of the total thickness of the steel plate, the heating is excessive and there is a concern about the change of the microstructure. Therefore, the depth D of the heating region is 90% of the total thickness of the steel plate. % Or less is preferable.
- the heating means used in the pre-heat treatment process is not particularly limited, but it is preferable to use a laser heating device. This is because the use of a laser with a high energy density as the heat source makes it possible to more accurately control the preheat treatment process conditions and improve the joint workability without damaging the joint characteristics. is there.
- the moving speed of the heating means used in the preheat treatment process may be approximately the same as the joining speed.
- the laser output and beam diameter may be set as appropriate according to the bonding conditions.
- a cooling means is provided behind the rotary tool that moves in the joining direction, and the joint is joined by the cooling means.
- Strength can be improved. This is because, usually after the completion of joining, the joined portion is naturally cooled, and there is a problem that the strength of the joined joint cannot be sufficiently obtained when the hardenability of the steel material being processed is low.
- the cooling means provided at the rear of the rotating tool that moves in the joining direction cools the joined portion of the steel sheet, and the strength can be improved by quenching by appropriately controlling the cooling rate.
- cooling by injecting an inert gas is suitable.
- a cooling rate in this case for example, a range from 800 ° C. to 500 ° C. is preferably set to 30 to 300 ° C./s.
- a rear heating means may be provided behind the rotary tool moving in the joining direction and after the cooling means described above, and the joined portion of the steel sheet may be reheated by the rear heating means.
- the cooling rate is preferably 30 to 300 ° C./s in the range of 800 ° C. to 500 ° C.
- the reheating temperature is preferably 550 to 650 ° C., for example.
- a cooling means may be provided behind the rotating tool that moves in the joining direction and after the above-described rear heating means, and the joining portion of the steel plates may be cooled by the cooling means.
- the structure immediately after joining, the structure can be compounded by reducing the cooling rate with the rear heating means and then increasing the cooling rate with the cooling means, thereby achieving joint characteristics having both strength and ductility. be able to.
- a cooling rate in this case, for example, it is preferable that the range from 800 ° C. to 600 ° C. is about 10 to 30 ° C./s, and then the range from 600 ° C. to 400 ° C. is about 30 to 300 ° C./s. is there.
- the rotational speed of the rotary tool is set in the range of 100 to 1000 rpm, and the target is to suppress the torque of the rotary tool and increase the joining speed to 1000 mm / min or more.
- general structural steel and carbon steel for example, rolled steel for welded structure according to JIS G 3106, carbon steel for mechanical structure according to JIS G 4051, and the like can be suitably used. It can also be advantageously applied to high-strength structural steels with a tensile strength of 800 MPa or more. Even in this case, the strength at the joint is 85% or more of the tensile strength of the steel plate (base material), and even 90%. The above strength can be obtained.
- Example 1 Friction stir welding was performed using a steel plate having a chemical composition and tensile strength shown in Table 1 with a plate thickness of 1.6 mm. The joint butt surfaces were joined in one pass on one side with a so-called I-shaped groove with no angle and a surface condition of the degree of milling. Table 2 shows the welding conditions of the friction stir welding.
- a rotating tool (shoulder diameter a: 12 mm, maximum pin diameter b: 4 mm, probe length c: 1.4 mm) made of tungsten carbide (WC) whose cross-sectional dimensions are shown in FIG. 4 is used.
- the bonded portion was shielded with argon gas to prevent surface oxidation.
- the steel plate 1 shown in Table 1 Prior to joining, in order to confirm a heating region by preheating using a laser as a heat source, the steel plate 1 shown in Table 1 is subjected to laser irradiation under the irradiation conditions (laser moving speed, laser output, and beam diameter) shown in Table 3. Light was irradiated and the surface temperature was measured by thermography. Furthermore, the cross section of the laser irradiation part was observed, and the microstructure was observed with a nital etchant.
- the region having the transformation point (T A1 ° C) or higher is the darkest, and is less than the transformation point (T A1 ° C) existing outside, but a high hardness structure such as martensite in the base material is tempered.
- the region of 0.8 ⁇ T A1 ° C or more was a circular shape having a diameter of 3.5 mm. Since the maximum diameter of the pin part of the rotary tool used here is 4.0 mm, the area of the heating region on the steel plate surface is equal to or less than the area of the maximum diameter part of the pin part of the rotary tool. Further, in the irradiation condition B, the region of 0.8 ⁇ TA1 ° C. or higher was a circular shape having a diameter of 2.0 mm.
- the area of the heating region on the surface of the steel sheet is equal to or less than the area of the maximum diameter portion of the pin portion of the rotary tool.
- the region of 0.8 ⁇ TA1 ° C. or higher was a circular shape having a diameter of 4.5 mm. Since the maximum diameter of the pin part of the rotary tool used here is 4.0 mm, the area of the heating region on the steel plate surface exceeds the area of the maximum diameter part of the pin part of the rotary tool.
- the depth D 0 of the region where T A1 ° C or higher and the depth of 0.8 ⁇ T A1 ° C or higher were 0.47 and 0.50 mm, respectively. Since the thickness t of the steel plate, which is a workpiece, is 1.6 mm, the depth D of the heating region is about 31.3% of the thickness t of the steel plate. On the other hand, under irradiation condition C, the depth D 0 of the region where T A1 ° C or higher and the depth of 0.8 ⁇ T A1 ° C or higher (depth D of the heating region) were 0.09 and 0.10 mm, respectively. It was. Since the thickness t of the steel plate as the workpiece is 1.6 mm, the depth D of the heating region is about 6.3% of the thickness t of the steel plate.
- Table 5 shows preheating process conditions by laser irradiation performed before joining of workpieces and process conditions performed after joining.
- cooling by gas ejection was performed, and in the heating (and reheating), induction heating was performed.
- ⁇ in the preheating process condition and the process condition performed after bonding indicates a case where the preheating process and the post-bonding process such as cooling and heating were not performed, respectively.
- the center of the heating area is located on the advancing side and the retreating side from the junction center line, respectively. Indicates.
- Table 6 also shows the measured values of the torque of the rotating tool when joining, and a tensile test piece with the size of No. 1 test piece specified in JIS Z 3121 from the obtained joint. The tensile strength when performed is shown. In addition, it can be said that the greater the torque of the rotary tool, the lower the plastic fluidity and the more likely to cause defects.
- Example 2 As in Example 1, a steel plate with a chemical composition and tensile strength shown in Table 1 with a thickness of 1.6 mm is used, and the surface of the joint butt surface is angled so that it is milled with a so-called I-shaped groove. Friction stir welding was performed with a pass. Table 7 shows the joining conditions of the friction stir welding. Similarly to Example 1, a rotary tool (tungsten diameter a: 12 mm, maximum pin diameter b: 4 mm, probe length c: 1.4, made of tungsten carbide (WC) whose cross-sectional dimensions are shown in FIG. 4 is used. mm), and at the time of bonding, the bonded portion was shielded with argon gas to prevent surface oxidation.
- a rotary tool tungsten diameter a: 12 mm, maximum pin diameter b: 4 mm, probe length c: 1.4, made of tungsten carbide (WC) whose cross-sectional dimensions are shown in FIG. 4 is used. mm
- the steel plate 1 shown in Table 1 Prior to joining, in order to confirm the heating region by preheating using a laser as a heat source, the steel plate 1 shown in Table 1 is subjected to laser irradiation under the irradiation conditions (laser moving speed, laser output, and beam diameter) shown in Table 8. Light was irradiated and the surface temperature was measured by thermography. Further, the cross section of the laser irradiated portion was observed, and the microstructure was observed with a nital corrosion liquid in the same manner as in Example 1. The depth D 0 of the region where the transformation point (T A1 ° C) or higher was reached, and 0.8 ⁇ T The depth of the region where the temperature was A1 ° C. or higher (the depth D of the heating region) was measured. Table 9 shows the measurement results.
- the region where the irradiation condition D is 0.8 ⁇ T A1 ° C or higher is an elliptical diameter in which the laser moving direction is the major axis, and the perpendicular direction to the laser moving direction is the minor axis.
- the major axis was 3.8 mm and the minor axis was 3.2 mm. Since the maximum diameter of the pin part of the rotary tool used here is 4.0 mm, the area of the heating region on the steel plate surface is equal to or less than the area of the maximum diameter part of the pin part of the rotary tool.
- irradiation condition E the region where the temperature is 0.8 ⁇ TA1 ° C.
- the area of the heating region on the surface of the steel sheet is equal to or less than the area of the maximum diameter portion of the pin portion of the rotary tool.
- the region where the temperature is 0.8 ⁇ T A1 ° C or more has an elliptical diameter in which the laser moving direction is the major axis and the direction perpendicular to the laser moving direction is the minor axis, the major axis is 4.9 mm and the minor axis is 4.1 mm. It was. Since the maximum diameter of the pin part of the rotary tool used here is 4.0 mm, the area of the heating region on the steel plate surface exceeds the area of the maximum diameter part of the pin part of the rotary tool.
- the cross-section observation of the laser irradiation unit the irradiation conditions D, T depth of A1 ° C. became more regions D 0 and 0.8 ⁇ T A1 ° C. or higher and became area depth ( The depth D) of the heating area was 0.30 and 0.32 mm, respectively. Since the thickness t of the steel plate, which is the workpiece, is 1.6 mm, the depth D of the heating region, which is the depth of the region over 0.8 ⁇ TA1 ° C., is about 20.0% of the thickness t of the steel plate. Become.
- the depth D 0 of the region where T A1 ° C or higher and the depth of 0.8 ⁇ T A1 ° C or higher were 0.51 and 0.54 mm, respectively. Since the thickness t of the steel plate as the workpiece is 1.6 mm, the depth D of the heating region is about 33.8% of the thickness t of the steel plate.
- the irradiation condition F (the depth D of the heating zone) T depth of A1 ° C. became more regions D 0 and 0.8 ⁇ T A1 ° C. or higher and became region of depth respectively 0.10,0.11mm met It was. Since the thickness t of the steel plate as the workpiece is 1.6 mm, the depth D of the heating region is about 6.9% of the thickness t of the steel plate.
- Table 10 shows preheating process conditions by laser irradiation performed before joining of workpieces and process conditions performed after joining.
- cooling by gas ejection was performed, and in the heating (and reheating), induction heating was performed.
- ⁇ in the preheating process condition and the process condition performed after bonding indicates a case where the preheating process and the post-bonding process such as cooling and heating were not performed, respectively.
- the center of the heating area is located on the advancing side and the retreating side from the junction center line, respectively. Indicates.
- Table 11 also shows the measured values of the torque of the rotating tool when performing the joining and a tensile test piece with the size of No. 1 test piece specified in JIS Z 3121 from the obtained joint. The tensile strength when performed is shown. In addition, it can be said that the greater the torque of the rotary tool, the lower the plastic fluidity and the more likely to cause defects.
Landscapes
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Pressure Welding/Diffusion-Bonding (AREA)
- Heat Treatment Of Articles (AREA)
Abstract
Description
なお、本明細書では、例えば鋼板を突き合わせただけで未だ接合されていない状態にある突き合わせ部分を「未接合部」、一方、塑性流動により接合されて一体化された部分を「接合部」と呼ぶものとする。
しかしながら、この技術は、接合対象とする金属材料を回転させるものであるから、接合する金属材料の形状や寸法に限界がある。
a)通常の摩擦撹拌接合では、接合のために必要な熱源が、回転ツールと被加工材との間で発生する摩擦熱のみである。そのため、構造用鋼を摩擦撹拌接合法により接合する場合には、被加工材である構造用鋼を軟化させるために必要な熱量を十分に確保することができない。その結果、接合部において十分な塑性流動が得られず、接合速度の低下や接合欠陥の発生などといった接合施工性の劣化が懸念される。
上記した本技術を工業化する上で非常に重要となる接合施工性の劣化を回避するためには、摩擦撹拌接合前の予熱処理プロセスが有効であると考えられる。
その結果、
c)レーザなどのエネルギー密度の高い熱源を用いることで、予熱処理プロセスでの加熱領域の表面温度、面積、位置を厳密に制御し、また必要に応じて加熱領域の厚さ方向における温度についても適正に制御する。それにより、接合継手強度等の接合継手特性の劣化を招くことなく、接合施工性を向上できるとの知見を得た。
本発明は、上記の知見に立脚するものである。
1.肩部および該肩部に配され該肩部と回転軸を共有するピン部を含み、少なくとも該肩部と該ピン部は被加工材である鋼板よりも硬い材質からなる回転ツールを、該鋼板の未接合部に挿入して回転させながら接合方向に移動させ、該回転ツールと該鋼板との摩擦熱により該鋼板を軟化させつつ、その軟化した部位を該回転ツールで撹拌することにより塑性流動を生じさせて、該鋼板を接合する構造用鋼の摩擦撹拌接合方法において、
接合方向へ移動する該回転ツールの前方に設けた加熱手段により該鋼板を加熱し、該加熱により該鋼板の表面の温度TS(℃)が、
TS ≧ 0.8×TA1 (TA1は下記の式(1)に示す)
となる領域を加熱領域としたとき、該鋼板の表面における、該加熱領域と該回転ツールとの最小距離を、該回転ツールの肩部の直径以下とし、
また該鋼板の表面における該加熱領域の面積を、該回転ツールのピン部の最大径部の面積以下とし、
さらに該加熱領域の面積の50%以上が、該鋼板の表面において、該回転ツールの回転軸を通り接合方向に平行な直線である接合中央線と、該接合中央線に平行で、かつアドバンシングサイドへ該回転ツールのピン部の最大半径と同じ距離だけ隔てた直線、との間に位置する構造用鋼の摩擦撹拌接合方法。
記
TA1(℃)=723-10.7[%Mn]-16.9[%Ni]+29.1[%Si]
+16.9[%Cr]+290[%As]+6.38[%W] ・・・(1)
ただし、[%M]は、被加工材である鋼板におけるM元素の含有量(質量%)である。
TD ≧ 0.8×TA1 (TA1は下記の式(1)に示す)
を満足する領域における前記鋼板の表面からの最大深さを加熱領域の深さDとしたとき、該加熱領域の深さDが、前記鋼板の合計厚さtの30%以上となる前記1に記載の構造用鋼の摩擦撹拌接合方法。
記
TA1(℃)=723-10.7[%Mn]-16.9[%Ni]+29.1[%Si]
+16.9[%Cr]+290[%As]+6.38[%W] ・・・(1)
ただし、[%M]は、被加工材である鋼板におけるM元素の含有量(質量%)である。
本発明は、構造用鋼の摩擦撹拌接合方法であり、図1に示すように、回転ツールを、鋼板の未接合部に挿入して回転させながら接合方向に移動させる。それにより回転ツールと鋼板との摩擦熱により該鋼板を軟化させつつ、その軟化した部位を回転ツールで撹拌することにより塑性流動を生じさせて、鋼板を接合する。ここで、回転ツールは、肩部、およびこの肩部に配置され、この肩部と回転軸を共有するピン部を含み、少なくとも肩部とピン部は被加工材である鋼板よりも硬い材質により形成される。
図中、符号1が回転ツール、2は回転軸、3は鋼板、4は接合部、5は加熱手段、6が冷却手段、7が後方加熱手段、8が回転ツールの肩部、9は回転ツールのピン部であり、αで回転ツール傾斜角度を示す。なお、「AS」および「RS」は、それぞれアドバンシングサイドおよびリトリーティングサイドを表す。
ここで、アドバンシングサイドとは、ツール回転方向と接合方向が一致する側と、リトリーティングサイドとは、ツール回転方向と接合方向が反対となる側とそれぞれ定義する。
なお、図中、符号10は接合中央線であり、この接合中央線は、鋼板の表面において回転ツールの回転軸を通り接合方向に平行な直線を示す。また、11は接合中央線に平行で、かつアドバンシングサイドへ回転ツールのピン部の最大半径と同じ距離だけ隔てた直線(以下、AS線と呼ぶものとする)、12は加熱領域、13は冷却領域、14は再加熱領域であり、aで回転ツールの肩部直径を、bで回転ツールのピン部の最大径を、Xで加熱領域と回転ツールとの最小距離を、Dで加熱領域の深さを、tで鋼板の厚さをそれぞれ示す。
本発明の摩擦撹拌接合方法で接合する鋼板は、図3に示すように、通常、鋼の変態温度であるTA1の80%程度の温度では、常温時の強度の30%程度の強度となる。また、この温度より高くなると、さらに強度が低下する。よって、鋼板の表面温度を0.8×TA1℃以上として鋼板を予め軟化させ、当該鋼板を撹拌し、塑性流動を促進することで、回転ツールにかかる負荷を低減し、また接合速度も高速度化することができる。このため、本発明では、加熱領域における鋼板の表面温度TS(℃)を、0.8×TA1℃以上とする。なお、TA1(℃)は次式(1)により求めることができる。
TA1(℃)=723-10.7[%Mn]-16.9[%Ni]+29.1[%Si]
+16.9[%Cr]+290[%As]+6.38[%W] ・・・(1)
ここで、[%M]は、被加工材である鋼板におけるM元素の含有量(質量%)である。
ただし、厚さ方向へ加熱領域を確保するためには加熱領域の表面には温度勾配が存在しても良く、その場合、加熱領域における鋼板の表面温度は1.5×TM℃以下とすることが好ましい。さらに、接合部の温度が過度に上昇することによる回転ツールの損傷やミクロ組織の変質を避けるため、加熱領域における鋼板の表面温度は、該加熱領域を通過する回転ツールと接触するまでにTM℃未満とすることが好ましい。
なお、TM(℃)は被加工材である鋼板の融点である。
鋼板の表面における加熱領域と回転ツールとの間隔が大きくなり過ぎると、接合前に加熱領域における温度が低下してしまい、予熱による効果が十分に得られない。このため、鋼板の表面における加熱領域と接合方向へ移動する回転ツールとの最小距離は、回転ツールの肩部の直径以下とする。
ただし、加熱領域と回転ツールの間隔が小さくなり過ぎると、回転ツールが加熱手段による熱で損傷する恐れがあるので、鋼板の表面における加熱領域と接合方向へ移動する回転ツールとの最小距離は、回転ツールの肩部の直径の0.1倍以上とすることが好ましい。
なお、回転ツールの肩部の直径は、8~60mm程度である。
加熱領域が大きくなり過ぎると当該領域およびその周辺領域のミクロ組織が変化する。特に、マルテンサイト組織により強化された高張力鋼板の場合は、フェライト-オーステナイト変態温度以下での加熱であっても、マルテンサイトが焼き戻されることで軟化を生じ、接合継手強度を大幅に低下させてしまう。このため、鋼板の表面における加熱領域の面積は、回転ツールのピン部の最大径部の面積以下とする。
一方、加熱領域の面積が小さくなりすぎると、予熱による効果が十分に得られなくなる。よって、鋼板の表面における加熱領域の面積は、回転ツールのピン部における最大径部の面積の0.1倍以上とすることが好ましい。
なお、回転ツールのピン部の最大径は、2~50mm程度である。
鋼材の摩擦撹拌接合においては、塑性流動の始点はアドバンシングサイドであり、回転ツールの回転方向に沿って、接合方向前方、リトリーティングサイド、接合方向後方を通り、アドバンシングサイドが終点となる。このように、アドバンシングサイドは塑性流動の始点となるため、被加工材である鋼板の加熱不足が生じ易く、塑性流動が不十分で欠陥が発生する場合には、その殆どがアドバンシングサイドで発生する。
従って、鋼板の表面において、加熱領域の面積の50%以上を、接合中央線と、該接合中央線に平行なAS線との間に位置させ、アドバンシングサイドを優先的に加熱することで、塑性流動を促進し、欠陥の発生を抑え、接合速度の高速化を図ることができる。好ましくは加熱領域の面積の60%以上、より好ましくは80%以上の範囲である。なお、100%であってもよい。
また、アドバンシングサイドを優先的に加熱するという観点からは、加熱領域の中心を、接合中央線とAS線の中間点を通る直線と、AS線との間に位置させる。換言すれば、加熱領域の中心を接合中央線よりもアドバンシングサイド側に位置させ、さらに加熱領域中心から接合中央線までの距離を、回転ツールのピン部における最大半径の0.5倍以上1倍以下とすることが好ましい。
前述したように、本発明の摩擦撹拌接合方法で接合する鋼板は、通常、鋼の変態温度であるTA1の80%程度の温度では、常温時の強度の30%程度の強度となる。また、この温度より高くなると、さらに強度が低下する。よって、加熱領域の厚さ方向の領域においても、温度を0.8×TA1℃以上として鋼板を予め軟化させる。そして当該鋼板を撹拌し、塑性流動を促進することで、回転ツールにかかる負荷をさらに低減し、また接合速度も一層高速度化させることが好ましい。従って、後述する加熱領域の深さDを規定する加熱領域の厚さ方向の温度TDは、0.8×TA1℃以上として定義するものとした。なお、TA1(℃)は次式(1)により求めることができる。
TA1(℃)=723-10.7[%Mn]-16.9[%Ni]+29.1[%Si]
+16.9[%Cr]+290[%As]+6.38[%W] ・・・(1)
ここで、[%M]は、被加工材である鋼板におけるM元素の含有量(質量%)である。
ただし、厚さ方向へ加熱領域を確保するためには加熱領域の厚さ方向には温度勾配が存在しても良く、その場合、加熱領域における鋼板の厚さ方向の温度は1.5×TM℃以下とすることが好ましい。さらに、接合部の温度が過度に上昇することによる回転ツールの損傷やミクロ組織の変質を避けるために、加熱領域における鋼板の厚さ方向の温度は、該加熱領域を通過する回転ツールと接触するまでにTM℃未満とすることが好ましい。
なお、TM(℃)は被加工材である鋼板の融点である。
加熱領域の深さDは、上記した加熱領域の厚さ方向の温度TDが0.8×TA1℃以上となる領域における、被加工材である鋼板の表面からの最大深さで規定される。ここで、この加熱領域の深さDは、鋼板の合計厚さの30%以上とすることが好ましい。というのは、加熱領域の深さDを鋼板の合計厚さの30%以上とすることで、塑性流動がさらに促進される。それにより、回転ツールにかかる負荷低減および接合速度の高速度化において、一層有利となるからである。より好ましくは鋼板の合計厚さの50%以上である。
しかしながら、加熱領域の深さDが、鋼板の合計厚さの90%を超えると、加熱が過多となりミクロ組織の変化が懸念されるので、加熱領域の深さDは鋼板の合計厚さの90%以下とすることが好ましい。
というのは、エネルギー密度の高いレーザを熱源に用いることで、予熱処理プロセス条件の制御をより正確に行うことができ、接合継手特性を損なうことなく接合施工性の向上を図ることができるからである。
というのは、通常、接合完了後、接合部は自然放冷状態となるため、被加工材である鋼材の焼入れ性が低い場合は、接合継手の強度が十分に得られないという問題があった。この点、接合方向へ移動する前記回転ツールの後方に設けた冷却手段により、前記鋼板の接合部を冷却し、その際冷却速度を適切に制御することで、焼入れによる強度向上を図ることができる。具体的な冷却手段としては、不活性ガスの噴出による冷却が好適である。この場合の冷却速度としては、例えば800℃から500℃の範囲を30~300℃/sとすることが好適である。
これにより、接合部が冷却手段による冷却で焼入れされ、過度に硬化した場合に、該後方加熱手段で焼き戻しすることにより硬度を抑え、強度と靭性を併せ持つ継手特性を達成することができる。この場合の冷却速度としては、例えば800℃から500℃の範囲を30~300℃/s、再加熱温度としては、例えば550~650℃とすることが好適である。
この場合には、接合直後において、後方加熱手段で冷却速度を小さく、その後、冷却手段で冷却速度を大きくすることで、組織を複合化することができ、強度と延性を併せ持つ継手特性を達成することができる。この場合の冷却速度としては、例えば、800℃から600℃の範囲を10~30℃/s程度とし、その後、600℃から400℃の範囲を30~300℃/s程度とすることが好適である。
従って、本発明では、回転ツールの回転数を100~1000rpmの範囲とし、回転ツールのトルクを抑え、接合速度を1000mm/min以上に高速化することを目標とする。
また、本発明の対象鋼種としては、一般的な構造用鋼や炭素鋼、例えばJIS G 3106の溶接構造用圧延鋼材、JIS G 4051の機械構造用炭素鋼などを好適に用いることができる。また、引張強度が800MPa以上の高強度構造用鋼にも有利に適用でき、この場合であっても、接合部において、鋼板(母材)の引張強度の85%以上の強度、さらには90%以上の強度が得られる。
板厚1.6mmの表1に示す化学組成、引張強さの鋼板を用いて、摩擦撹拌接合を実施した。継手突合せ面は、角度をつけないいわゆるI型開先でフライス加工程度の表面状態により片面1パスで接合を行った。摩擦撹拌接合の接合条件を表2に示す。また、ここでは、図4に断面寸法を示す炭化タングステン(WC)を素材とした回転ツール(肩部直径a:12mm、ピン部の最大径b:4mm、プローブ長さc:1.4mm)を用い、接合時にはアルゴンガスにより接合部をシールドし、表面の酸化を防止した。
ここで、変態点(TA1℃)以上となった領域は最も濃く、その外側に存在する変態点(TA1℃)未満であるが母材中のマルテンサイトなどの高硬度組織が焼き戻される領域は比較的薄くエッチングされるため、変態点(TA1℃)以上となった領域、変態点(TA1℃)未満での焼き戻し領域、母材の領域はそれぞれ識別可能である。さらに、鉄鋼の熱処理の知見より、変態点(TA1℃)未満での焼き戻し領域は、0.8×TA1℃以上かつTA1℃未満の領域と一致することが知られている。このようなナイタール腐食液によるミクロ組織観察より、変態点(TA1℃)以上となった領域の深さD0、および0.8×TA1℃以上となった領域の深さ(加熱領域の深さD)を測定した。
これらの測定結果を表4に示す。
また、照射条件Bにおいて、0.8×TA1℃以上となる領域は直径2.0mmの円形状であった。従って、上記と同様に、鋼板表面における加熱領域の面積は、回転ツールのピン部の最大径部の面積以下となる。
一方、照射条件Cにおいて、0.8×TA1℃以上となる領域は直径4.5mmの円形状であった。ここで用いた回転ツールのピン部の最大直径は4.0mmであるため、鋼板表面における加熱領域の面積は、回転ツールのピン部の最大径部の面積を超えることとなる。
照射条件Bにおいて、TA1℃以上となった領域の深さD0および0.8×TA1℃以上となった領域の深さ(加熱領域の深さD)はそれぞれ0.47、0.50mmであった。被加工材である鋼板の厚さtは1.6mmであるので、加熱領域の深さDは、鋼板の厚さtの約31.3%となる。
一方、照射条件Cにおいて、TA1℃以上となった領域の深さD0および0.8×TA1℃以上となった領域の深さ(加熱領域の深さD)はそれぞれ0.09、0.10mmであった。被加工材である鋼板の厚さtは1.6mmであるので、加熱領域の深さDは、鋼板の厚さtの約6.3%となる。
なお、表5中、予熱プロセス条件および接合後に行ったプロセス条件における「-」は、それぞれ予熱プロセスおよび冷却や加熱といった接合後のプロセスを行わなかった場合を示す。また、接合中央線から加熱領域中心までの距離における「(AS)」、「(RS)」との記載は、加熱領域の中心が、接合中央線からそれぞれアドバンシングサイド、リトリーティングサイドにあることを示す。
なお、回転ツールのトルクが大きいほど塑性流動性が低く、欠陥などが生じ易いと言える。
一方、比較例1~5では、回転ツールのトルクが80N・m以上となり、塑性流動性に劣っていた。
実施例1と同様に板厚1.6mmの表1に示す化学組成、引張強さの鋼板を用いて、継手突合せ面に角度をつけないいわゆるI型開先でフライス加工程度の表面状態により片面1パスで摩擦撹拌接合を実施した。摩擦撹拌接合の接合条件を表7に示す。また、実施例1と同様に、図4に断面寸法を示す炭化タングステン(WC)を素材とした回転ツール(肩部直径a:12mm、ピン部の最大径b:4mm、プローブ長さc:1.4mm)を用い、接合時にはアルゴンガスにより接合部をシールドし、表面の酸化を防止した。
これらの測定結果を表9に示す。
また、照射条件Eにおいて、0.8×TA1℃以上となる領域はレーザ移動方向が長径、レーザ移動方向と直角方向が短径となる楕円径となり、長径は2.2mm、短径は1.8mmであった。従って、上記と同様に、鋼板表面における加熱領域の面積は、回転ツールのピン部の最大径部の面積以下となる。
一方、照射条件Fにおいて、0.8×TA1℃以上となる領域はレーザ移動方向が長径、レーザ移動方向と直角方向が短径となる楕円径となり、長径は4.9mm、短径は4.1mmであった。ここで用いた回転ツールのピン部の最大直径は4.0mmであるため、鋼板表面における加熱領域の面積は、回転ツールのピン部の最大径部の面積を超えることとなる。
照射条件Eにおいて、TA1℃以上となった領域の深さD0および0.8×TA1℃以上となった領域の深さ(加熱領域の深さD)はそれぞれ0.51、0.54mmであった。被加工材である鋼板の厚さtは1.6mmであるので、加熱領域の深さDは、鋼板の厚さtの約33.8%となる。
一方、照射条件Fにおいて、TA1℃以上となった領域の深さD0および0.8×TA1℃以上となった領域の深さ(加熱領域の深さD)はそれぞれ0.10、0.11mmであった。被加工材である鋼板の厚さtは1.6mmであるので、加熱領域の深さDは、鋼板の厚さtの約6.9%となる。
なお、表10中、予熱プロセス条件および接合後に行ったプロセス条件における「-」は、それぞれ予熱プロセスおよび冷却や加熱といった接合後のプロセスを行わなかった場合を示す。また、接合中央線から加熱領域中心までの距離における「(AS)」、「(RS)」との記載は、加熱領域の中心が、接合中央線からそれぞれアドバンシングサイド、リトリーティングサイドにあることを示す。
なお、回転ツールのトルクが大きいほど塑性流動性が低く、欠陥などが生じ易いと言える。
一方、比較例6では回転ツールが接合中に破損し、接合ができなかった。また、比較例7~10は、未接合部分が残る状態となって接合ができず、従って、健全な継手は得られなかった。このため、比較例6~10では、回転ツールトルク等の測定は行っていない。
2 回転軸
3 鋼板
4 接合部
5 加熱手段
6 冷却手段
7 後方加熱手段
8 回転ツールの肩部
9 回転ツールのピン部
10 接合中央線
11 AS線
12 加熱領域
13 冷却領域
14 再加熱領域
a 回転ツールの肩部直径
b 回転ツールのピン部の最大径
c 回転ツールのプローブ長さ
X 加熱領域と回転ツールとの最小距離
D 加熱領域の深さ
t 鋼板の厚さ
α 回転ツール傾斜角度
Claims (8)
- 肩部および該肩部に配され該肩部と回転軸を共有するピン部を含み、少なくとも該肩部と該ピン部は被加工材である鋼板よりも硬い材質からなる回転ツールを、該鋼板の未接合部に挿入して回転させながら接合方向に移動させ、該回転ツールと該鋼板との摩擦熱により該鋼板を軟化させつつ、その軟化した部位を該回転ツールで撹拌することにより塑性流動を生じさせて、該鋼板を接合する構造用鋼の摩擦撹拌接合方法において、
接合方向へ移動する該回転ツールの前方に設けた加熱手段により該鋼板を加熱し、該加熱により該鋼板の表面の温度TS(℃)が、
TS ≧ 0.8×TA1 (TA1は下記の式(1)に示す)
となる領域を加熱領域としたとき、該鋼板の表面における、該加熱領域と該回転ツールとの最小距離を、該回転ツールの肩部の直径以下とし、
また該鋼板の表面における該加熱領域の面積を、該回転ツールのピン部の最大径部の面積以下とし、
さらに該加熱領域の面積の50%以上が、該鋼板の表面において、該回転ツールの回転軸を通り接合方向に平行な直線である接合中央線と、該接合中央線に平行で、かつアドバンシングサイドへ該回転ツールのピン部の最大半径と同じ距離だけ隔てた直線、との間に位置する構造用鋼の摩擦撹拌接合方法。
記
TA1(℃)=723-10.7[%Mn]-16.9[%Ni]+29.1[%Si]
+16.9[%Cr]+290[%As]+6.38[%W] ・・・(1)
ただし、[%M]は、被加工材である鋼板におけるM元素の含有量(質量%)である。 - 前記加熱領域の厚さ方向の領域に関し、温度TD(℃)が、
TD ≧ 0.8×TA1 (TA1は下記の式(1)に示す)
を満足する領域における前記鋼板の表面からの最大深さを加熱領域の深さDとしたとき、該加熱領域の深さDが、前記鋼板の合計厚さtの30%以上となる請求項1に記載の構造用鋼の摩擦撹拌接合方法。
記
TA1(℃)=723-10.7[%Mn]-16.9[%Ni]+29.1[%Si]
+16.9[%Cr]+290[%As]+6.38[%W] ・・・(1)
ただし、[%M]は、被加工材である鋼板におけるM元素の含有量(質量%)である。 - 前記加熱手段が、レーザ加熱装置である請求項1または2に記載の構造用鋼の摩擦撹拌接合方法。
- 接合方向へ移動する前記回転ツールの後方に、後方加熱手段を設け、該後方加熱手段により、前記鋼板の接合部を加熱する請求項1~3のいずれかに記載の構造用鋼の摩擦撹拌接合方法。
- 前記回転ツールの後方で、かつ前記後方加熱手段の後に、冷却手段を設け、該冷却手段により前記鋼板の接合部を冷却する請求項4に記載の構造用鋼の摩擦撹拌接合方法。
- 接合方向へ移動する前記回転ツールの後方に、冷却手段を設け、該冷却手段により、前記鋼板の接合部を冷却する請求項1~3のいずれかに記載の構造用鋼の摩擦撹拌接合方法。
- 接合方向へ移動する前記回転ツールの後方で、かつ前記冷却手段の後に、後方加熱手段を設け、該後方加熱手段により、前記鋼板の接合部を再加熱する請求項6に記載の構造用鋼の摩擦撹拌接合方法。
- 請求項1~7のいずれかに記載の摩擦撹拌接合方法を用いる構造用鋼の接合継手の製造方法。
Priority Applications (6)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP14847434.9A EP3053696B1 (en) | 2013-09-30 | 2014-09-10 | Friction stir welding method for structural steel and method of manufacturing joint for structural steel |
JP2015501976A JP5943142B2 (ja) | 2013-09-30 | 2014-09-10 | 構造用鋼の摩擦撹拌接合方法および構造用鋼の接合継手の製造方法 |
US15/025,585 US9821407B2 (en) | 2013-09-30 | 2014-09-10 | Friction stir welding method for structural steel and method of manufacturing joint for structural steel |
KR1020167009119A KR101809388B1 (ko) | 2013-09-30 | 2014-09-10 | 구조용 강의 마찰 교반 접합 방법 및 구조용 강의 접합 조인트의 제조 방법 |
CN201480053753.7A CN105592969B (zh) | 2013-09-30 | 2014-09-10 | 结构用钢的摩擦搅拌接合方法及结构用钢的接合接头的制造方法 |
MX2016003815A MX2016003815A (es) | 2013-09-30 | 2014-09-10 | Metodo de soldadura por friccion-agitacion para acero estructural y metodo de fabricacion de junta para acero estructural. |
Applications Claiming Priority (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2013205235 | 2013-09-30 | ||
JP2013-205235 | 2013-09-30 | ||
JP2013224540 | 2013-10-29 | ||
JP2013-224540 | 2013-10-29 |
Publications (2)
Publication Number | Publication Date |
---|---|
WO2015045299A1 true WO2015045299A1 (ja) | 2015-04-02 |
WO2015045299A8 WO2015045299A8 (ja) | 2016-03-24 |
Family
ID=52742473
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2014/004657 WO2015045299A1 (ja) | 2013-09-30 | 2014-09-10 | 構造用鋼の摩擦撹拌接合方法および構造用鋼の接合継手の製造方法 |
Country Status (7)
Country | Link |
---|---|
US (1) | US9821407B2 (ja) |
EP (1) | EP3053696B1 (ja) |
JP (1) | JP5943142B2 (ja) |
KR (1) | KR101809388B1 (ja) |
CN (1) | CN105592969B (ja) |
MX (1) | MX2016003815A (ja) |
WO (1) | WO2015045299A1 (ja) |
Cited By (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US20160214203A1 (en) * | 2013-09-30 | 2016-07-28 | Jfe Steel Corporation | Friction stir welding method for steel sheets and method of manufacturing joint |
US20160221117A1 (en) * | 2013-09-30 | 2016-08-04 | Jfe Steel Corporation | Friction stir welding method for steel sheets and method of manufacturing joint |
US20160228981A1 (en) * | 2013-09-30 | 2016-08-11 | Jfe Steel Corporation | Friction stir welding method for structural steel and method of manufacturing joint for structural steel |
WO2016147668A1 (ja) * | 2015-03-19 | 2016-09-22 | Jfeスチール株式会社 | 構造用鋼の摩擦撹拌接合装置 |
WO2017169991A1 (ja) | 2016-03-31 | 2017-10-05 | Jfeスチール株式会社 | 構造用鋼の摩擦撹拌接合方法及び装置 |
WO2017169992A1 (ja) | 2016-03-31 | 2017-10-05 | Jfeスチール株式会社 | 構造用鋼の摩擦撹拌接合方法及び装置 |
WO2018003740A1 (ja) * | 2016-06-27 | 2018-01-04 | 川崎重工業株式会社 | 摩擦攪拌点接合方法および摩擦攪拌点接合装置 |
WO2018070316A1 (ja) * | 2016-10-11 | 2018-04-19 | Jfeスチール株式会社 | 摩擦撹拌接合方法および装置 |
WO2018070317A1 (ja) * | 2016-10-11 | 2018-04-19 | Jfeスチール株式会社 | 摩擦撹拌接合方法および装置 |
Families Citing this family (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP6231236B1 (ja) * | 2017-03-30 | 2017-11-15 | 株式会社日立製作所 | 摩擦攪拌接合装置及び摩擦攪拌接合制御装置並びに摩擦攪拌接合方法 |
CA3081330A1 (en) * | 2017-10-31 | 2019-05-09 | MELD Manufacturing Corporation | Solid-state additive manufacturing system and material compositions and structures |
US11065713B1 (en) * | 2018-05-31 | 2021-07-20 | Seagate Technology Llc | Disk drive apparatus including pre-treated, welded housing that provides sealed cavity for holding hard disk drive components |
JP2020075255A (ja) * | 2018-11-05 | 2020-05-21 | 日本軽金属株式会社 | 液冷ジャケットの製造方法及び摩擦攪拌接合方法 |
CN109570734B (zh) * | 2019-01-10 | 2021-12-21 | 广东和胜新能源科技有限公司 | 搅拌摩擦焊接工艺 |
US11794272B2 (en) * | 2019-08-08 | 2023-10-24 | Nippon Light Metal Company, Ltd. | Automatic joining system |
JP7347235B2 (ja) * | 2020-01-24 | 2023-09-20 | 日本軽金属株式会社 | 液冷ジャケットの製造方法及び摩擦攪拌接合方法 |
JP7347234B2 (ja) * | 2020-01-24 | 2023-09-20 | 日本軽金属株式会社 | 液冷ジャケットの製造方法及び摩擦攪拌接合方法 |
CN112917000A (zh) * | 2021-03-31 | 2021-06-08 | 西南交通大学 | 一种基于相变控温的搅拌摩擦焊接系统及方法 |
US11872649B2 (en) * | 2021-04-07 | 2024-01-16 | Frank's International, Llc | Offshore pipelaying system using friction stir welding |
Citations (13)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS62183979A (ja) | 1986-01-17 | 1987-08-12 | ザ ウエルデイング インステイテユ−ト | 摩擦溶接方法及びその装置 |
JPH07505090A (ja) | 1991-12-06 | 1995-06-08 | ザ ウェルディング インスティテュート | 摩擦溶接方法 |
JP2003094175A (ja) | 2001-09-20 | 2003-04-02 | Yaskawa Electric Corp | 摩擦撹拌接合法の加熱装置 |
JP2003532542A (ja) | 2000-05-08 | 2003-11-05 | ブリガム ヤング ユニバーシティ | 高耐摩耗性工具を使用する金属基複合材料、鉄合金、非鉄合金及び超合金の摩擦撹拌接合 |
JP2004504158A (ja) * | 2000-07-20 | 2004-02-12 | エーアーデーエス・ドイッチェランド・ゲゼルシャフト ミット ベシュレンクテル ハフツング | 摩擦攪拌溶接の方法 |
JP2004154790A (ja) * | 2002-11-05 | 2004-06-03 | Mitsubishi Heavy Ind Ltd | 摩擦攪拌接合装置とその接合方法 |
JP2004174575A (ja) * | 2002-11-28 | 2004-06-24 | Mitsubishi Heavy Ind Ltd | 攪拌接合方法及び攪拌接合装置 |
JP2004195480A (ja) * | 2002-12-16 | 2004-07-15 | Furuya Kinzoku:Kk | 薄板の接合方法 |
JP2005088080A (ja) * | 2003-09-11 | 2005-04-07 | Boeing Co:The | 可変速度のピンによる摩擦攪拌溶接のための方法及び装置 |
JP2005288474A (ja) | 2004-03-31 | 2005-10-20 | Nippon Sharyo Seizo Kaisha Ltd | 摩擦撹拌接合装置及び摩擦撹拌接合方法 |
JP2006021217A (ja) * | 2004-07-07 | 2006-01-26 | Kawasaki Heavy Ind Ltd | スポット接合用摩擦撹拌接合装置 |
JP2006192452A (ja) * | 2005-01-12 | 2006-07-27 | Mitsubishi Heavy Ind Ltd | 金属の処理方法、回転工具、金属処理装置及び金属の表面改質方法 |
JP2007185683A (ja) * | 2006-01-12 | 2007-07-26 | Mitsubishi Heavy Ind Ltd | 亀裂補修方法 |
Family Cites Families (35)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US5829664A (en) * | 1996-11-15 | 1998-11-03 | Aluminum Company Of America | Resistance heated stir welding |
SE9701265D0 (sv) * | 1997-04-04 | 1997-04-04 | Esab Ab | Förfarande och anordning för friktionsomrörningssvetsning |
US5942314A (en) * | 1997-04-17 | 1999-08-24 | Mitsui Mining & Smelting Co., Ltd. | Ultrasonic welding of copper foil |
DE10036170C1 (de) * | 2000-07-25 | 2001-12-06 | Eads Deutschland Gmbh | Laserunterstütztes Reibrührschweißverfahren |
WO2003045615A2 (en) * | 2001-11-27 | 2003-06-05 | THE UNITED STATES OF AMERICA as represented by the ADMINISTRATOR OF THE NATIONAL AERONAUTICS AND SPACE | Thermal stir welding process and apparatus |
US6780525B2 (en) * | 2001-12-26 | 2004-08-24 | The Boeing Company | High strength friction stir welding |
US20050224562A1 (en) * | 2002-03-26 | 2005-10-13 | Prevey Paul S | Apparatus and method for forming a weld joint having improved physical properties |
US7360676B2 (en) * | 2002-09-21 | 2008-04-22 | Universal Alloy Corporation | Welded aluminum alloy structure |
US6802444B1 (en) * | 2003-03-17 | 2004-10-12 | The United States Of America As Represented By The National Aeronautics And Space Administration | Heat treatment of friction stir welded 7X50 aluminum |
US20070138239A1 (en) * | 2005-12-15 | 2007-06-21 | Sumitomo Light Metal Industries, Ltd. | Method of joining heat-treatable aluminum alloy members by friction stir welding and joined product obtained by the method and used for press forming |
JP4468125B2 (ja) * | 2004-09-27 | 2010-05-26 | 三菱重工業株式会社 | 摩擦撹拌接合方法及び装置 |
US7078647B2 (en) * | 2004-10-21 | 2006-07-18 | Wisconsin Alumni Research Foundation | Arc-enhanced friction stir welding |
JP2007111716A (ja) * | 2005-10-19 | 2007-05-10 | Showa Denko Kk | クランプ装置、接合装置および接合方法 |
DE102006048580C5 (de) * | 2006-10-13 | 2015-02-19 | Fraunhofer-Gesellschaft zur Förderung der angewandten Forschung e.V. | Verfahren und Vorrichtung zum rissfreien Schweißen, Reparaturschweißen oder Auftragsschweißen heißrissanfälliger Werkstoffe |
US20080099533A1 (en) * | 2006-10-31 | 2008-05-01 | General Electric | Method for controlling microstructure via thermally managed solid state joining |
US20080302539A1 (en) * | 2007-06-11 | 2008-12-11 | Frank's International, Inc. | Method and apparatus for lengthening a pipe string and installing a pipe string in a borehole |
CA2706955A1 (en) * | 2007-11-28 | 2009-06-04 | Frank's International, Inc. | Methods and apparatus for forming tubular strings |
US20090261146A1 (en) * | 2008-03-25 | 2009-10-22 | Hou Gene J | Donor material technology for friction stir welding |
US20100136369A1 (en) * | 2008-11-18 | 2010-06-03 | Raghavan Ayer | High strength and toughness steel structures by friction stir welding |
KR101382912B1 (ko) * | 2009-03-16 | 2014-04-08 | 신닛테츠스미킨 카부시키카이샤 | 켄칭성이 우수한 붕소 첨가 강판 및 제조 방법 |
CN101899630A (zh) | 2009-05-25 | 2010-12-01 | 宝山钢铁股份有限公司 | 900MPa级屈服强度的工程机械用调质钢板及其生产方法 |
DE102010054453A1 (de) * | 2010-12-14 | 2012-06-14 | Hochschule Für Angewandte Wissenschaften - Fachhochschule Kempten | Verfahren zum Fügen von Werkstücken |
US9259774B2 (en) * | 2011-05-03 | 2016-02-16 | GM Global Technology Operations LLC | Clinching method and tool for performing the same |
JP5461476B2 (ja) * | 2011-05-27 | 2014-04-02 | 三菱重工業株式会社 | 摩擦攪拌接合装置 |
DE102011078144A1 (de) * | 2011-06-27 | 2012-12-27 | Airbus Operations Gmbh | Verfahren und vorrichtung zum verbinden von fügeteilen, sowie bauteil |
US8579180B2 (en) * | 2011-09-23 | 2013-11-12 | Dwight A. Burford | Mandrel tool probe for friction stir welding having physically-separate spiraled surfaces |
FI126176B (sv) * | 2011-10-17 | 2016-07-29 | Uponor Infra Oy | Förfarande för framställning av skivformiga strukturer |
WO2013081731A1 (en) * | 2011-12-01 | 2013-06-06 | Lawrence Livermore National Security, Llc | System and method for light assisted friction stir processing and welding of metallic and non-metallic materials |
CN103305750A (zh) * | 2012-03-09 | 2013-09-18 | 株式会社神户制钢所 | 极低温韧性优异的厚钢板 |
US9033205B2 (en) * | 2012-07-27 | 2015-05-19 | Alfredo CASTILLO | Friction stir welding with temperature control |
WO2015045420A1 (ja) * | 2013-09-30 | 2015-04-02 | Jfeスチール株式会社 | 鋼板の摩擦撹拌接合方法及び接合継手の製造方法 |
KR102194358B1 (ko) * | 2013-09-30 | 2020-12-23 | 제이에프이 스틸 가부시키가이샤 | 강판의 마찰 교반 접합 방법 및 접합 이음매의 제조 방법 |
US9821407B2 (en) * | 2013-09-30 | 2017-11-21 | Jfe Steel Corporation | Friction stir welding method for structural steel and method of manufacturing joint for structural steel |
US10440784B2 (en) * | 2014-10-14 | 2019-10-08 | Illinois Tool Works Inc. | Reduced-distortion hybrid induction heating/welding assembly |
KR101954561B1 (ko) * | 2015-03-19 | 2019-03-05 | 제이에프이 스틸 가부시키가이샤 | 구조용 강의 마찰 교반 접합 장치 |
-
2014
- 2014-09-10 US US15/025,585 patent/US9821407B2/en active Active
- 2014-09-10 MX MX2016003815A patent/MX2016003815A/es active IP Right Grant
- 2014-09-10 CN CN201480053753.7A patent/CN105592969B/zh active Active
- 2014-09-10 KR KR1020167009119A patent/KR101809388B1/ko active IP Right Grant
- 2014-09-10 JP JP2015501976A patent/JP5943142B2/ja active Active
- 2014-09-10 EP EP14847434.9A patent/EP3053696B1/en active Active
- 2014-09-10 WO PCT/JP2014/004657 patent/WO2015045299A1/ja active Application Filing
Patent Citations (14)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS62183979A (ja) | 1986-01-17 | 1987-08-12 | ザ ウエルデイング インステイテユ−ト | 摩擦溶接方法及びその装置 |
JPH07505090A (ja) | 1991-12-06 | 1995-06-08 | ザ ウェルディング インスティテュート | 摩擦溶接方法 |
JP2003532542A (ja) | 2000-05-08 | 2003-11-05 | ブリガム ヤング ユニバーシティ | 高耐摩耗性工具を使用する金属基複合材料、鉄合金、非鉄合金及び超合金の摩擦撹拌接合 |
JP2003532543A (ja) | 2000-05-08 | 2003-11-05 | ブリガム ヤング ユニバーシティ | 高耐摩耗性工具を使用する摩擦撹拌接合 |
JP2004504158A (ja) * | 2000-07-20 | 2004-02-12 | エーアーデーエス・ドイッチェランド・ゲゼルシャフト ミット ベシュレンクテル ハフツング | 摩擦攪拌溶接の方法 |
JP2003094175A (ja) | 2001-09-20 | 2003-04-02 | Yaskawa Electric Corp | 摩擦撹拌接合法の加熱装置 |
JP2004154790A (ja) * | 2002-11-05 | 2004-06-03 | Mitsubishi Heavy Ind Ltd | 摩擦攪拌接合装置とその接合方法 |
JP2004174575A (ja) * | 2002-11-28 | 2004-06-24 | Mitsubishi Heavy Ind Ltd | 攪拌接合方法及び攪拌接合装置 |
JP2004195480A (ja) * | 2002-12-16 | 2004-07-15 | Furuya Kinzoku:Kk | 薄板の接合方法 |
JP2005088080A (ja) * | 2003-09-11 | 2005-04-07 | Boeing Co:The | 可変速度のピンによる摩擦攪拌溶接のための方法及び装置 |
JP2005288474A (ja) | 2004-03-31 | 2005-10-20 | Nippon Sharyo Seizo Kaisha Ltd | 摩擦撹拌接合装置及び摩擦撹拌接合方法 |
JP2006021217A (ja) * | 2004-07-07 | 2006-01-26 | Kawasaki Heavy Ind Ltd | スポット接合用摩擦撹拌接合装置 |
JP2006192452A (ja) * | 2005-01-12 | 2006-07-27 | Mitsubishi Heavy Ind Ltd | 金属の処理方法、回転工具、金属処理装置及び金属の表面改質方法 |
JP2007185683A (ja) * | 2006-01-12 | 2007-07-26 | Mitsubishi Heavy Ind Ltd | 亀裂補修方法 |
Cited By (34)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US20160221117A1 (en) * | 2013-09-30 | 2016-08-04 | Jfe Steel Corporation | Friction stir welding method for steel sheets and method of manufacturing joint |
US20160228981A1 (en) * | 2013-09-30 | 2016-08-11 | Jfe Steel Corporation | Friction stir welding method for structural steel and method of manufacturing joint for structural steel |
US20160214203A1 (en) * | 2013-09-30 | 2016-07-28 | Jfe Steel Corporation | Friction stir welding method for steel sheets and method of manufacturing joint |
US10005151B2 (en) * | 2013-09-30 | 2018-06-26 | Jfe Steel Corporation | Friction stir welding method for steel sheets and method of manufacturing joint |
US9821407B2 (en) * | 2013-09-30 | 2017-11-21 | Jfe Steel Corporation | Friction stir welding method for structural steel and method of manufacturing joint for structural steel |
US9833861B2 (en) * | 2013-09-30 | 2017-12-05 | Jfe Steel Corporation | Friction stir welding method for steel sheets and method of manufacturing joint |
US10766099B2 (en) | 2015-03-19 | 2020-09-08 | Jfe Steel Corporation | Friction stir welding apparatus for structural steel |
WO2016147668A1 (ja) * | 2015-03-19 | 2016-09-22 | Jfeスチール株式会社 | 構造用鋼の摩擦撹拌接合装置 |
JP6004147B1 (ja) * | 2015-03-19 | 2016-10-05 | Jfeスチール株式会社 | 構造用鋼の摩擦撹拌接合装置 |
KR20180119635A (ko) | 2016-03-31 | 2018-11-02 | 제이에프이 스틸 가부시키가이샤 | 구조용 강의 마찰 교반 접합 방법 및 장치 |
WO2017169991A1 (ja) | 2016-03-31 | 2017-10-05 | Jfeスチール株式会社 | 構造用鋼の摩擦撹拌接合方法及び装置 |
JPWO2017169991A1 (ja) * | 2016-03-31 | 2018-04-05 | Jfeスチール株式会社 | 構造用鋼の摩擦撹拌接合方法及び装置 |
EP3437782A4 (en) * | 2016-03-31 | 2019-07-24 | JFE Steel Corporation | METHOD AND DEVICE FOR FRICTION-AGITATION BONDING OF CONSTRUCTION STEEL |
US11241755B2 (en) | 2016-03-31 | 2022-02-08 | Jfe Steel Corporation | Friction stir welding method and apparatus for structural steel |
KR102096919B1 (ko) * | 2016-03-31 | 2020-04-03 | 제이에프이 스틸 가부시키가이샤 | 구조용 강의 마찰 교반 접합 방법 및 장치 |
WO2017169992A1 (ja) | 2016-03-31 | 2017-10-05 | Jfeスチール株式会社 | 構造用鋼の摩擦撹拌接合方法及び装置 |
JPWO2017169992A1 (ja) * | 2016-03-31 | 2018-04-05 | Jfeスチール株式会社 | 構造用鋼の摩擦撹拌接合方法及び装置 |
KR102098217B1 (ko) * | 2016-03-31 | 2020-04-07 | 제이에프이 스틸 가부시키가이샤 | 구조용 강의 마찰 교반 접합 방법 및 장치 |
EP3437781A4 (en) * | 2016-03-31 | 2019-06-12 | JFE Steel Corporation | METHOD AND DEVICE FOR FRICTION-AGITATION BONDING OF CONSTRUCTION STEEL |
KR20180119636A (ko) | 2016-03-31 | 2018-11-02 | 제이에프이 스틸 가부시키가이샤 | 구조용 강의 마찰 교반 접합 방법 및 장치 |
CN109070261A (zh) * | 2016-03-31 | 2018-12-21 | 杰富意钢铁株式会社 | 结构用钢的摩擦搅拌接合方法和装置 |
CN109070262A (zh) * | 2016-03-31 | 2018-12-21 | 杰富意钢铁株式会社 | 结构用钢的摩擦搅拌接合方法和装置 |
WO2018003740A1 (ja) * | 2016-06-27 | 2018-01-04 | 川崎重工業株式会社 | 摩擦攪拌点接合方法および摩擦攪拌点接合装置 |
JP6309183B1 (ja) * | 2016-06-27 | 2018-04-11 | 川崎重工業株式会社 | 摩擦攪拌点接合方法および摩擦攪拌点接合装置 |
JPWO2018070317A1 (ja) * | 2016-10-11 | 2018-10-11 | Jfeスチール株式会社 | 摩擦撹拌接合方法および装置 |
CN109803784A (zh) * | 2016-10-11 | 2019-05-24 | 杰富意钢铁株式会社 | 摩擦搅拌接合方法及装置 |
KR20190039985A (ko) * | 2016-10-11 | 2019-04-16 | 제이에프이 스틸 가부시키가이샤 | 마찰 교반 접합 방법 및 장치 |
KR20190039743A (ko) * | 2016-10-11 | 2019-04-15 | 제이에프이 스틸 가부시키가이샤 | 마찰 교반 접합 방법 및 장치 |
JPWO2018070316A1 (ja) * | 2016-10-11 | 2018-10-11 | Jfeスチール株式会社 | 摩擦撹拌接合方法および装置 |
WO2018070317A1 (ja) * | 2016-10-11 | 2018-04-19 | Jfeスチール株式会社 | 摩擦撹拌接合方法および装置 |
KR102173603B1 (ko) * | 2016-10-11 | 2020-11-03 | 제이에프이 스틸 가부시키가이샤 | 마찰 교반 접합 방법 및 장치 |
KR102181820B1 (ko) * | 2016-10-11 | 2020-11-24 | 제이에프이 스틸 가부시키가이샤 | 마찰 교반 접합 방법 및 장치 |
CN109803784B (zh) * | 2016-10-11 | 2021-09-28 | 杰富意钢铁株式会社 | 摩擦搅拌接合方法及装置 |
WO2018070316A1 (ja) * | 2016-10-11 | 2018-04-19 | Jfeスチール株式会社 | 摩擦撹拌接合方法および装置 |
Also Published As
Publication number | Publication date |
---|---|
EP3053696A1 (en) | 2016-08-10 |
EP3053696A4 (en) | 2016-08-31 |
MX2016003815A (es) | 2016-08-01 |
JPWO2015045299A1 (ja) | 2017-03-09 |
KR101809388B1 (ko) | 2017-12-14 |
US9821407B2 (en) | 2017-11-21 |
CN105592969A (zh) | 2016-05-18 |
WO2015045299A8 (ja) | 2016-03-24 |
US20160228981A1 (en) | 2016-08-11 |
JP5943142B2 (ja) | 2016-06-29 |
KR20160052705A (ko) | 2016-05-12 |
CN105592969B (zh) | 2018-01-16 |
EP3053696B1 (en) | 2017-08-16 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP5943142B2 (ja) | 構造用鋼の摩擦撹拌接合方法および構造用鋼の接合継手の製造方法 | |
JP6004147B1 (ja) | 構造用鋼の摩擦撹拌接合装置 | |
JP6497451B2 (ja) | 摩擦撹拌接合方法および装置 | |
JP6332561B2 (ja) | 構造用鋼の摩擦撹拌接合方法及び装置 | |
JP6992773B2 (ja) | 両面摩擦攪拌接合方法および両面摩擦攪拌接合装置 | |
WO2015045420A1 (ja) | 鋼板の摩擦撹拌接合方法及び接合継手の製造方法 | |
JP6332562B2 (ja) | 構造用鋼の摩擦撹拌接合方法及び装置 | |
JP6493564B2 (ja) | 摩擦撹拌接合方法および装置 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
ENP | Entry into the national phase |
Ref document number: 2015501976 Country of ref document: JP Kind code of ref document: A |
|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 14847434 Country of ref document: EP Kind code of ref document: A1 |
|
REEP | Request for entry into the european phase |
Ref document number: 2014847434 Country of ref document: EP |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2014847434 Country of ref document: EP |
|
WWE | Wipo information: entry into national phase |
Ref document number: IDP00201601914 Country of ref document: ID |
|
WWE | Wipo information: entry into national phase |
Ref document number: MX/A/2016/003815 Country of ref document: MX |
|
WWE | Wipo information: entry into national phase |
Ref document number: 15025585 Country of ref document: US |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
ENP | Entry into the national phase |
Ref document number: 20167009119 Country of ref document: KR Kind code of ref document: A |