WO2017154658A1 - 金属材の低温接合方法及び接合構造物 - Google Patents
金属材の低温接合方法及び接合構造物 Download PDFInfo
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- WO2017154658A1 WO2017154658A1 PCT/JP2017/007677 JP2017007677W WO2017154658A1 WO 2017154658 A1 WO2017154658 A1 WO 2017154658A1 JP 2017007677 W JP2017007677 W JP 2017007677W WO 2017154658 A1 WO2017154658 A1 WO 2017154658A1
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- 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
- B23K20/122—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
- B23K20/1205—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 translation movement
-
- 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
- B23K20/121—Control circuits therefor
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- 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
- B23K20/1225—Particular aspects of welding with a non-consumable tool
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- 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
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- 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
- B23K20/1245—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 characterised by the apparatus
- B23K20/125—Rotary tool drive mechanism
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- 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
-
- 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
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- 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
- B23K20/233—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 without ferrous layer
- B23K20/2336—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 without ferrous layer both layers being aluminium
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- 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
- B23K2103/00—Materials to be soldered, welded or cut
- B23K2103/02—Iron or ferrous alloys
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- 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
- B23K2103/00—Materials to be soldered, welded or cut
- B23K2103/02—Iron or ferrous alloys
- B23K2103/04—Steel or steel alloys
-
- 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
- B23K2103/00—Materials to be soldered, welded or cut
- B23K2103/08—Non-ferrous metals or alloys
- B23K2103/10—Aluminium or alloys thereof
Definitions
- the present invention relates to a low-temperature bonding method for directly bonding metal materials to each other and a bonded structure obtained by the low-temperature bonding method. More specifically, the present invention effectively suppresses deterioration of mechanical properties in a bonded portion and a heat-affected zone.
- the present invention relates to a low-temperature bonding method that can be used and a bonded structure obtained by the low-temperature bonding method.
- Patent Document 1 Japanese Patent Application Laid-Open No. 2005-131679
- a heat-treatable aluminum alloy material friction stir welding method is disclosed, characterized in that the heat-treatable aluminum alloy material in a restored state that has undergone the restoration process is subjected to friction stir welding.
- the joint can be configured so that the hardness of the base material becomes the smallest among the stir welded portion, the heat affected zone, and the base material. It is said that it is possible to advantageously obtain a bonding material excellent in ductility and by extension, press formability by preventing breakage at the affected part.
- Patent Document 2 Japanese Patent Application Laid-Open No. 2015-057292
- the materials to be joined has a face-centered cubic lattice structure, and the materials to be joined that are metal materials having a recrystallization temperature of 300 ° C. or lower are joined together.
- a friction stir welding step of joining the materials to be joined together by inserting a rotating rod-shaped tool into the joint, supplying a cooled coolant to the joint, and moving the tool.
- the friction stir welding method since a stirring portion composed of fine equiaxed grains sufficiently including dislocations can be formed by forced cooling with a refrigerant, the friction stir welding method has a face-centered cubic lattice structure. It is said that even a metal material having a recrystallization temperature of 300 ° C. or lower can obtain joint strength equal to or higher than that of the base material.
- JP 2005-131679 A Japanese Patent Laying-Open No. 2015-057292
- Patent Document 1 relatively increases the hardness of the joint by lowering the hardness of the base material serving as a reference by heat treatment.
- the mechanical properties possessed cannot be utilized.
- the object of the present invention is to provide a simple low-temperature bonding capable of effectively suppressing the deterioration of mechanical properties in various high-tensile steel and aluminum joints and heat-affected zones. It is providing the joining structure obtained by the method and the said low-temperature joining method.
- the present inventor has conducted extensive research on a method for achieving recrystallization by forming recrystallized grains at the bonding interface, and as a result, suppressing the temperature rise while introducing strong strain at the bonding interface, etc. Has been found to be extremely effective, and the present invention has been achieved.
- the present invention In this method, two metal materials are made to face each other at a bonded portion to form a bonded interface, and the two metal materials are bonded by press-fitting a rotating tool rotated at a predetermined rotation speed into the bonded portion. And By setting the peripheral speed of the outermost periphery of the rotating tool to be 51 mm / s or less, a strong strain is introduced into the bonded portion to reduce the recrystallization temperature that the metal material originally has, Generating recrystallized grains at the bonded interface with a bonding temperature lower than the recrystallization temperature that the metal material originally has, A low-temperature bonding method for metal materials characterized by the above.
- the joining temperature rises to about 70% of the melting point (K) of the materials to be joined.
- the rotary tool is used in the conventional friction stir welding. By rotating at an unbelievably low rotational speed, suppressing an increase in the bonding temperature and introducing strong strain, the bonding temperature is made lower than the recrystallization temperature originally possessed by the metal material to be bonded. The strength reduction of the part can be suppressed.
- the peripheral speed of the outermost periphery of the rotary tool by setting the peripheral speed of the outermost periphery of the rotary tool to 51 mm / s or less, it is possible to suppress an increase in bonding temperature due to an increase in the press-fit load of the rotary tool.
- the “recrystallization temperature inherent to the metal material” varies depending on the metal material, but is generally about 40% of the melting point (K) of the metal material.
- the joining temperature to be lower than the recrystallization temperature originally possessed by the metal material to be joined, the recrystallized grain size of the stirring portion formed by the press-fitting of the rotary tool can be reduced, and the fine graining can be performed. Can improve the mechanical properties of the stirring section.
- the bonding temperature is lowered by decreasing the rotation speed and increasing the press-fitting load, and the grain size of the recrystallized grains is 1 ⁇ m or less.
- the joining temperature in general friction stir welding is closely related to the rotational speed, press-fit load and moving speed of the press-fitting rotary tool. It rises as it falls.
- the rotational speed is set to be extremely small, the present inventor does not increase the joining temperature greatly even if the press-fitting load is increased. It has been found that the increase increases significantly.
- the moving speed of the rotary tool may be set as appropriate from the viewpoint of defect formation and bonding speed in the stirrer, etc., in the case of spot welding, the pushing and pulling speed of the rotary tool, in the case of line welding, What is necessary is just to adjust a moving speed.
- the shape of the rotary tool is not particularly limited as long as the effects of the present invention are not impaired, and various types of conventionally known friction stir welding tools can be used. Generally, a rod-shaped rotating tool is used, but for example, a disk-shaped rotating tool may be used.
- the low-temperature bonding method of the present invention is different from conventional friction stir welding in terms of bonding conditions, bonding mechanism, etc., and a large strain is introduced near the interface to be bonded at low temperatures, so The temperature at which crystallization occurs is lower than the “recrystallization temperature inherent to the metal material”, and recrystallized grains are generated at the welded interface below the “recrystallization temperature inherent to the metal material”, which suppresses the formation of the heat affected zone. By doing so, good bonding is achieved.
- the end portions of the metal plates are brought into contact with each other to form a bonded portion, and the rotating tool is rotated along the longitudinal direction of the processed portion to move the metal plates together.
- the rotating tool is rotated along the longitudinal direction of the processed portion to move the metal plates together.
- Spot joining where the ends of the metal plates are butted together to make a joint, and the rotary tool is rotated without moving at the joint, and (3) the metal plates are overlapped at the joint Spot welding that inserts a rotating tool into the joint and rotates the rotating tool without moving at that location to join the metal plates together.
- (4) Superimposes the metal plates on the joint and rotates the rotating tool at the joint.
- the peripheral speed of the outermost periphery of the rotary tool is preferably 32 mm / s or less, and more preferably 19 mm / s or less.
- the press-fitting load is set to a value that can be press-fitted into the metal material without rotating the rotary tool.
- a rotary tool is press-fitted using softening of a material to be joined by frictional heat.
- an increase in joining temperature is suppressed, so It is necessary to press-fit the rotary tool in such a manner that it is plastically deformed. Further, a large strain can be introduced into the bonded interface by pressing the rotary tool into the bonded material with a large load.
- the press-fit load is applied to the metal material within a range in which a stress applied from the rotary tool to the metal material is equal to or higher than a yield stress of the metal material at the temperature of the bonded portion. It is preferable that the temperature is lowered as the temperature of the joint increases. Since the yield stress of the metal material decreases as the temperature increases, the minimum load required to press-fit the rotary tool into the metal material also decreases as the temperature increases. That is, as long as the rotary tool can be press-fitted into the metal material, it is possible to perform energy-saving and low-temperature joining by using as small a load as possible.
- the metal material is preferably aluminum or an aluminum alloy, and the metal material is more preferably a heat treatment type aluminum alloy, a work strengthened aluminum, or a work strengthened aluminum alloy. .
- aluminum or an aluminum alloy as a material to be bonded, it is possible to suppress a decrease in strength of the bonded portion due to an increase in crystal grain size or recovery.
- a heat treated aluminum alloy as a material to be bonded, precipitates It is also possible to suppress the strength reduction of the joint due to the coarsening and solid solution of the steel. Furthermore, the strength reduction accompanying recovery or recrystallization can be more effectively suppressed by using the work strengthened aluminum or the work strengthened aluminum alloy as the material to be joined.
- the low-temperature bonding method of the present invention can also be suitably used for dissimilar material bonding, and in the case of dissimilar material bonding, it is only necessary to have the characteristics of the present invention with respect to at least one material to be bonded.
- the metal material is preferably an iron-based metal, and more preferably high-tensile steel.
- high-tensile steel as the material to be joined, it is possible to suppress the formation of the heat-affected zone, which has been a problem with conventional joining techniques, especially for high-tensile steel with a base metal hardness of less than 350 HV.
- the low-temperature bonding method of the invention it is possible to obtain a bonded portion having a hardness substantially equal to the base material hardness (which hardly causes a decrease in hardness).
- the above metal material is a material to be bonded using the low temperature bonding method of the present invention, but normal friction stir welding (the bonding temperature is about 70 to 80% of the melting point of the material to be bonded).
- the friction stir welding it is preferable to use a metal in which the strength of the joints (stirring part, heat-processing affected part, and heat affected part) is less than the base material strength.
- the low temperature bonding method of the present invention can achieve bonding at an extremely low temperature as compared with conventional bonding methods, it can be suitably used for dissimilar material bonding where formation of intermetallic compounds at the bonding interface is a problem.
- it can be suitably used for the dissimilar material joining of an aluminum material and a magnesium material and the dissimilar material joining of an aluminum material and a steel material.
- the rotating tool is made of an iron-based metal.
- the life of the rotary tool is a big problem.
- various rotary tools made of refractory metals and ceramics have been studied, but in addition to not having a sufficient life, the tool becomes expensive.
- the present inventor paid attention to the bonding temperature of the low-temperature bonding method of the present invention, and produced a rotary tool using an iron-based metal having a strength higher than that of the steel to be bonded at the bonding temperature.
- steel can be joined with a rotating tool.
- the rotary tool made of iron-based metal it is possible to achieve joining with a very inexpensive rotary tool as compared with a rotary tool conventionally used for friction stir welding of steel.
- the present invention also provides: Having a high-strength steel joint having a base metal hardness of less than 350 HV, The joint includes fine equiaxed recrystallized grains having an average grain size of 1 ⁇ m or less, The hardness of the joint and the heat-affected zone is approximately equal to or greater than the base material hardness; Also provided is a joint structure characterized by:
- the joint in the joint structure of the present invention is not mechanically joined but is metallurgically joined.
- the joint is basically composed of fine equiaxed recrystallized grains having the same composition as the high-tensile steel material to be joined, and the mean grain size of the fine equiaxed recrystallized grains is 1 ⁇ m or less. Therefore, it has mechanical characteristics that are not inferior to the base material.
- a heat-affected zone is formed at the joint of high-tensile steel, and the hardness of the heat-affected zone is lower than that of the base material.
- the hardness of the heat-affected zone is the base. It is above the material hardness.
- the present invention also provides: At least one substrate portion; And having a joint part joining the base parts together,
- the base portion is a high-tensile steel material or a heat-treatable aluminum alloy material,
- the joining portion has substantially the same composition as the base material portion,
- the joint includes fine equiaxed recrystallized grains having an average grain size of 1 ⁇ m or less,
- the hardness of the joint and heat-affected zone is approximately 80% or more of the base material,
- a joint structure characterized by:
- the bonded portion is not mechanically formed, and metallurgical bonding is achieved.
- a significant decrease in mechanical properties at the joint becomes a serious problem.
- fine equiaxed recrystallization with an average grain size of 1 ⁇ m or less. The interface to be bonded has disappeared due to the grains, and the hardness of the bonded portion and the heat-affected zone is approximately 80% or more of the base material portion.
- the recrystallized grain size varies depending on the temperature and strain history, it varies depending on the location to be observed, but it is sufficient if there is a region having an average grain size of 1 ⁇ m or less at and near the bonding interface.
- the average particle diameter is just to calculate the said average particle diameter by the intercept method with respect to the observation image by an optical microscope or a scanning electron microscope, for example.
- the base material portion is preferably a high-tensile steel material having a base metal hardness of 350 HV or higher.
- a significant decrease in hardness is inevitable in the joint portion and the heat-affected zone of the high-strength steel material having a base metal hardness of 350 HV or more, but in the joint structure of the present invention, the high hardness Even if the high-tensile steel material having the above is used for the base part, the hardness reduction of the joint part and the heat-affected part is effectively suppressed.
- the base material portion is a high-tensile steel material having a base material hardness of less than 350 HV, and the hardness of the joint portion and the heat affected zone is substantially equal to or greater than the base material hardness.
- a high-tensile steel material having a hardness of less than 350 HV for the base material By using a high-tensile steel material having a hardness of less than 350 HV for the base material, a decrease in the hardness of the joint and the heat-affected zone is almost completely suppressed.
- the base material portion is a heat-treatable aluminum alloy material
- the joint and the heat treatment part have a hardness of approximately 90% or more of the base material hardness.
- Heat treatment type aluminum easily decreases in hardness due to temperature rise during welding, but even when heat treatment type aluminum alloy material is used for the base part, the hardness of the joint and heat treatment part is approximately 9 of the base material hardness. Maintains over 10%.
- the joining structure of this invention can be suitably manufactured with the low-temperature joining method of the metal material of the above-mentioned this invention.
- the simple low-temperature joining method which can suppress effectively the fall of the mechanical characteristic in the junction part and heat-affected zone of various high-tensile steel and aluminum, and the joining structure obtained by the said low-temperature joining method Can be provided.
- Example 4 is a cross-sectional photograph of a joint obtained in Example 3.
- 6 is a cross-sectional photograph of a joint obtained in Example 4.
- 6 is a cross-sectional photograph of a joint obtained in Example 5.
- 6 is a surface photograph of a joint obtained in Examples 6 to 8.
- 7 is a cross-sectional photograph of a joint obtained in Example 6.
- 2 is a cross-sectional photograph of a joint obtained in Comparative Example 1. It is the hardness distribution (joint part horizontal direction) of a junction part in case base material hardness is 350HV. It is the hardness distribution (joint part horizontal direction) of a junction part in case base material hardness is 450HV. It is a graph which shows the relationship between the minimum hardness of a junction part, and a rotational speed.
- FIG. 1 is a graph which shows the relationship between the minimum hardness of a junction part, and base material hardness. It is the hardness distribution (joint part horizontal direction) of the junction part obtained in Example 3.
- FIG. 2 is the hardness distribution (joint part horizontal direction) of the junction part obtained in Example 4.
- FIG. It is the hardness distribution (joint part horizontal direction) of the junction part obtained in Example 6.
- FIG. It is the shear tensile strength of the joint obtained in Example 2 and Comparative Example 2.
- 2 is an orientation map image in the vicinity of a bonding interface obtained in Example 1.
- FIG. 6 is an orientation map image in the vicinity of a bonding interface obtained in Example 2.
- FIG. 6 is an orientation map image in the vicinity of a bonding interface obtained in Comparative Example 3.
- It is a graph which shows the relationship between joining maximum temperature and tool rotation speed. 10 is a graph showing temperature changes during bonding in Example 3.
- the low-temperature joining method for metal materials according to the present invention differs in the joining mechanism, but the joining process is similar to friction stir welding.
- Friction stir welding is referred to as FSW (Friction Stir Welding), where the ends of the materials to be joined made of two metal materials to be joined are brought into contact with each other, and a protrusion (probe) provided at the tip of the rotary tool is used. It is a method of joining two metal members by inserting between both ends and moving the rotating tool along the longitudinal direction of these ends while rotating.
- the metal material low-temperature bonding method according to the present invention is as follows: (1) The end portions of the metal plates are brought into contact with each other to form a bonded portion, and the rotary tool is moved while rotating along the longitudinal direction of the processed portion.
- FIG. 1 is a schematic view showing an embodiment of the low-temperature bonding method for metal materials of the present invention.
- the joined portion 6 is formed by superimposing the joined material 2 and the joined material 2 ′ and press-fitting the rotating tool 4 rotated at a low speed from one of the joined materials with a large load.
- FIG. 1 shows a case where a rotary tool 4 having a cylindrical projection (probe) 10 on the bottom surface of a cylindrical main body (shoulder) 8 is used.
- the joint portion 6 is formed below the main body portion (shoulder portion) 8 and around the projection portion (probe portion) 10. .
- FIG. 2 shows a case where the rotary tool 4 having no projection (probe part) 10 on the bottom surface of the cylindrical main body part (shoulder part) 8 is used. By pressing into 2, the joint 6 is formed.
- the protrusion (probe part) 10 is not provided, it is preferable that the rolling tool 4 is press-fitted only into the material to be joined 2 arranged on the upper side and the joining part 6 is formed below the bottom surface of the rotating tool 4.
- the joining temperature is adjusted by using the rotational speed, press-fitting load and moving speed of the rotary tool 4 as control parameters, and the joining temperature is inherently maintained by the material to be joined (2, 2 ′).
- the “recrystallization temperature inherently possessed by the material to be joined (2, 2 ′)” varies depending on its composition, processing state (degree of processing), etc.
- the recrystallization temperature of each metal is W: 1200 ° C., Mo: 900 ° C., Fe: 500 ° C., Cu: 200-230 ° C., Al: 150-240 ° C., Mg: 150 ° C.
- the “recrystallization temperature inherently possessed by the material to be joined (2, 2 ′)” in the present invention may be a value conventionally known for a metal material corresponding to the material to be joined (2, 2 ′). If there is no appropriate report value, the structure of the material to be bonded (2, 2 ′) heat-treated at each temperature may be observed to confirm the presence or absence of recrystallization.
- the bonding temperature when bonding is achieved by generating recrystallized grains at the bonded interface, the bonding temperature does not normally cause recrystallization “the bonded material (2, 2 ′) The recrystallization temperature is lower than “originally possessed”.
- a temperature at which recrystallization occurs by introducing strong strain into the bonded portion by press-fitting the rotary tool 4 with the temperature rise suppressed as much as possible (actual recrystallization temperature). Is reduced.
- the peripheral speed of the outermost periphery of the rotary tool 4 by setting the peripheral speed of the outermost periphery of the rotary tool 4 to 51 mm / s or less, strong strain is introduced into the bonded portion while suppressing an increase in bonding temperature, and the metal material originally has.
- the recrystallization temperature is lowered.
- the shoulder diameter of the rotary tool 4 is 12 mm
- the outermost peripheral speed can be set to 51 mm / s by setting the rotation speed to 80 rpm.
- the bonding temperature lower than the “recrystallization temperature inherent to the material to be bonded (2, 2 ′)”, the coarsening of the recrystallized grains formed in the bonded portion and the hardness reduction in the heat affected zone are suppressed. be able to.
- the shape of the rotary tool 4 is not particularly limited as long as the effects of the present invention are not impaired, and various types of conventionally known friction stir welding tools can be used, but the cylindrical body portion (shoulder portion) can be used. It is preferable to use what has a cylindrical projection part (probe part) in the bottom face. By making the bottom surface of the protruding portion (probe portion) substantially flat, strong strain can be efficiently introduced in the vicinity of the bonded interface.
- the bonding temperature can be lowered by lowering the rotational speed of the rotary tool 4 and increasing the press-fitting load, and by setting an appropriate rotational speed and press-fitting load, the grain size of the bonded portion can be reduced to 1 ⁇ m. It can be as follows.
- the rotational speed of the rotary tool 4 may be adjusted as appropriate so that the joining temperature is lower than the “recrystallization temperature inherent to the material to be joined (2, 2 ′)”, but the peripheral speed of the outermost periphery is 32 mm / s or less. It is preferable to set it to 19 mm / s or less.
- the peripheral speed of the outermost periphery of the rotary tool By setting the peripheral speed of the outermost periphery of the rotary tool to 32 mm / s or less, a temperature increase in the vicinity of the bonded interface can be suppressed. Moreover, the raise of joining temperature can be suppressed more reliably by the peripheral speed of the outermost periphery of a rotary tool being 19 mm / s or less.
- the shoulder diameter of the rotary tool 4 is 12 mm
- the peripheral speed of the outermost circumference is 32 mm / s when the rotation speed is 50 rpm, and 19 mm / s when the rotation speed is 30
- the press-fit load of the rotary tool 4 may be adjusted as appropriate so that the joining temperature is lower than the “recrystallization temperature inherent to the material to be joined (2, 2 ′)”, but the material to be joined without rotating the rotary tool 4. It is preferable to set it to a value that can be press-fitted into (2, 2 ′).
- the rotary tool 4 is press-fitted using softening of the material to be joined (2, 2 ′) due to frictional heat.
- an increase in the joining temperature is suppressed. Therefore, it is necessary to press-fit the rotary tool 4 in a mode in which the material to be joined (2, 2 ′) is plastically deformed.
- a large strain can be introduced into the bonded interface by pressing the rotary tool 4 into the bonded material (2, 2 ') with a large load.
- the material to be joined (2, 2 ′) is preferably aluminum or an aluminum alloy, and the material to be joined (2, 2 ′) is more preferably a heat treated aluminum alloy, a work strengthened aluminum or a work strengthened aluminum alloy. preferable.
- aluminum or an aluminum alloy as the material to be joined (2, 2 ′)
- By using a heat-treatable aluminum alloy it is possible to suppress a decrease in strength of the joint due to coarsening and solid solution of precipitates.
- the work strengthened aluminum or the work strengthened aluminum alloy as the material to be joined (2, 2 '), it is possible to more effectively suppress the strength reduction accompanying recovery and recrystallization.
- the material to be joined (2, 2 ') is preferably an iron-based metal, and more preferably high-tensile steel.
- high-tensile steel as the material to be joined (2, 2 ′), it is possible to suppress the formation of the heat affected zone, which has been a problem with conventional joining techniques, and in particular, the base material hardness is less than 350 HV.
- the low-temperature bonding method of the present invention to a tensile steel material, it is possible to obtain a bonded portion having a hardness substantially equal to the base material hardness (almost no decrease in hardness).
- the joining portion (stirring portion, thermal processing) It is preferable to use a metal having a strength of the affected zone and the heat affected zone that is less than the strength of the base material.
- the low-temperature bonding method of the present invention it is possible to effectively suppress the strength reduction for the metal material.
- the low-temperature bonding method of the present invention achieves bonding at an extremely low temperature compared to conventional bonding methods, it can be suitably used for dissimilar material bonding where formation of intermetallic compounds at the bonding interface is a problem. For example, it can be suitably used for dissimilar material joining between an aluminum material and a magnesium material and dissimilar material joining between an aluminum material and a steel material.
- Rotating tool 4 is preferably made of iron metal.
- the life of the rotary tool 4 is a serious problem.
- various rotary tools 4 made of refractory metals and ceramics have been studied, but in addition to not being able to obtain a sufficient life, they become expensive tools.
- the bonding temperature is as low as less than the “recrystallization temperature inherent to the material to be bonded (2, 2 ′)”, so that the steel material is removed with the rotating tool 4 made of iron metal. Can be joined.
- the rotary tool 4 made of an iron-based metal it is possible to achieve joining with the rotary tool 4 that is extremely inexpensive as compared with the rotary tool 4 conventionally used for friction stir welding of steel.
- the protrusion (probe portion) is cut by a shearing stress applied to the rotation tool 4 during joining, and the workpiece (2 , 2 ′).
- the protrusion (probe part) is filled in the recess formed in the joint by the press-fitting of the protrusion (probe part), a more preferable joint is formed from the viewpoint of joint strength.
- the rotary tool 4 and the material to be joined (2, 2 ') are the same type of material, there is no serious problem with respect to environmental resistance such as corrosion.
- the low-temperature bonding method of the present invention can be applied to general butt bonding, and in this case, the region in which the materials to be bonded (2, 2 ′) are butted in the mode shown in FIG.
- a good line joint can be obtained by press-fitting the rotary tool 4 and moving it along the butt line.
- FIG. 4 is a schematic cross-sectional view of the vicinity of the junction in the junction structure of the present invention.
- the spot junction part is shown as a typical aspect of the junction part in the junction structure of this invention.
- the joining structure 20 of the present invention has at least one or more base material portions 22 and a joining portion 24 obtained by joining the base material portions 22 to each other.
- the base material part 22 is a high-strength steel material or a heat-treatable aluminum alloy material, and the joint part 24 has substantially the same composition as the base material part 22. That is, other elements are not positively added with respect to the formation of the junction 24.
- the joint 24 includes fine equiaxed recrystallized grains having an average grain size of 1 ⁇ m or less, and in particular, the joint interface is formed by the formation of the fine equiaxed recrystallized grains. Further, due to the formation of fine equiaxed recrystallized grains in the joint, the hardness of the joint 24 and the heat affected zone 26 is approximately 80% or more of the base material 22.
- the joint 24 is not mechanically formed, and metallurgical joining is achieved. Further, with regard to high-tensile steel materials and heat-treatable aluminum alloy materials, a significant decrease in mechanical properties at the joint 24 is a serious problem. However, in the joined structure 20, fine equiaxed recrystallized grains having an average grain size of 1 ⁇ m or less. As a result, the bonded interface disappears, and the hardness of the bonded portion 24 and the heat-affected zone 26 is approximately 80% or more of the base material portion.
- the base material portion 22 is a high-tensile steel material having a base material hardness of 350 HV or higher.
- a significant decrease in hardness is inevitable in the joint portion 24 and the heat-affected zone 26 of the high-strength steel material having a base metal hardness of 350 HV or higher. Even if the high-tensile steel material having the above is used for the base material portion 22, the hardness reduction of the joint portion 24 and the heat affected zone 26 is effectively suppressed.
- the base material part 22 is a high-tensile steel material having a base material hardness of less than 350 HV, and the hardness of the joining part 24 and the heat affected zone 26 is approximately equal to or more than the base material hardness. .
- the base material portion 22 By using a high-tensile steel material having a hardness of less than 350 HV for the base material portion 22, the hardness reduction of the joint portion 24 and the heat-affected zone 26 is suppressed almost completely.
- the base material portion 22 is a heat treatment type aluminum alloy material
- the hardness of the joint portion 24 and the heat treatment portion 26 is approximately 90% or more of the base material hardness.
- Heat treatment type aluminum easily decreases in hardness due to temperature rise during welding, but even when heat treatment type aluminum alloy material is used for the base material part 22, the hardness of the joint 24 and heat treatment part 26 is the base material hardness. Of over 90%.
- Example 1 Carbon steel plates (JIS-S45C) were superposed in the arrangement shown in FIG. 5, and a rotary tool was press-fitted from the upper carbon steel plate to perform point bonding.
- a cylindrical tool ⁇ 12 mm, no probe
- the thickness of the carbon steel plate was 1.0 mm or 1.5 mm.
- the rotational speed of the rotary tool was 30 rpm or 50 rpm
- the load was 12 ton or 15 ton
- the joining time was 10 seconds or 30 seconds.
- the recrystallization temperature of Fe is ⁇ 500 ° C.
- the recrystallization temperature of S45C, which is carbon steel, is about 600 ° C.
- the carbon steel sheet used as the test material is changed in hardness (strength) by tempering treatment at temperatures of 400 ° C., 500 ° C., and 600 ° C.
- FIG. 5 shows an SEM photograph and an EBSD grain boundary image of the carbon steel sheet that had been tempered at each temperature.
- FE-SEM JSM-7001FA manufactured by JEOL Ltd.
- OSL data Collection ver 5.31 manufactured by TSL were used.
- Example 2 A cylindrical tool ( ⁇ 12 mm, probe: ⁇ 4 mm, length 1.8 mm) made of tool steel (Hitachi Metals, YXR33) is used as the rotary tool, the rotary tool rotation speed is 50 rpm, the load is 15 ton, and the joining time is 10 seconds. Except that, point bonding was performed in the same manner as in Example 1.
- Example 3 A cylindrical tool ( ⁇ 12mm, probe: ⁇ 4mm, length 1.8mm) made of tool steel (JIS-SKD61) is used as the rotating tool, and a low carbon steel plate (JIS-SPCC) is used as the material to be joined. Spot joining was performed in the same manner as in Example 1 except that 50 rpm, the load was 6 ton, and the joining time was 60 seconds.
- JIS-SKD61 tool steel
- JIS-SPCC low carbon steel plate
- Example 4 In the arrangement shown in FIG. 5, aluminum alloy plates (JIS-A6061-T6) were superposed on each other, and a rotary tool was press-fitted from the upper aluminum alloy plate to perform point joining.
- a cylindrical tool ⁇ 12 mm, no probe
- the rotational speed of the rotary tool was 30 to 50 rpm
- the load was 3.5 to 8 ton
- the joining time was 20 seconds or 30 seconds.
- the recrystallization temperature of Al is 150 to 240 ° C.
- the recrystallization temperature of A6061, which is an aluminum alloy is 250 to 350 ° C.
- Example 5 Point bonding was performed in the same manner as in Example 4 except that the shape of the rotating tool was ⁇ 12 mm, the probe was ⁇ 4 mm, and the length was 1 mm.
- Example 6 A linear processing region was formed by press-fitting a rotary tool into a pure aluminum plate (A1050 H24) having a thickness of 3 mm and moving it.
- a cylindrical tool ( ⁇ 12 mm, probe: ⁇ 4 mm, length 0.9 mm) made of WC—Ni cemented carbide was used as the rotating tool. Further, the rotational speed of the rotary tool was 50 rpm, the moving speed was 10 mm / min, and the friction stirring process was performed by controlling the position of the rotary tool.
- Example 7 Friction stirring was performed in the same manner as in Example 6 except that the rotation speed was 10 rpm.
- Example 8 Friction stirring was performed in the same manner as in Example 6 except that the rotation speed was 5 rpm.
- FIG. 7 shows a cross-sectional photograph of the joint (30 rpm, 15 ton, 30 s) obtained in Example 1.
- a concave portion is formed in the upper carbon steel plate by press-fitting the rotary tool, and the upper carbon steel plate and the lower carbon steel plate are joined below the concave portion.
- no defect or the like is observed in the bonding region, and that a good bonding is achieved.
- FIG. 1 A cross-sectional photograph of the joint obtained in Example 2 is shown in FIG.
- a concave portion corresponding to the bottom shape of the rotary tool is formed in the upper carbon steel plate, and the upper carbon steel plate and the lower carbon steel plate are joined below the concave portion. Yes.
- no defect or the like is observed in the bonding region, and that a good bonding is achieved.
- FIG. 9 shows a cross-sectional photograph of the joint obtained in Example 3.
- a rotary tool having a probe By press-fitting a rotary tool having a probe, a concave portion corresponding to the bottom shape of the rotary tool is formed in the upper carbon steel plate, and the probe portion of the broken rotary tool is buried in the concave portion. It can be seen that the upper carbon steel plate and the lower carbon steel plate are bonded to each other below the recess, and no defects or the like are observed in the bonding region, thereby achieving good bonding.
- FIG. 10 shows a cross-sectional photograph of the joint (40 rpm, 7 ton, 30 s) obtained in Example 4. Similar to the joint obtained in Example 1, a recess is formed in the upper aluminum alloy plate, and the upper aluminum alloy plate and the lower aluminum alloy plate are joined below the recess. Here, no defect or the like is observed in the bonding region.
- FIG. 11 shows a cross-sectional photograph of the joint (40 rpm, 6 tons, 20 s) obtained in Example 5. Similar to the joint obtained in Example 2, by pressing the rotary tool having a probe, a concave portion corresponding to the shape of the bottom surface of the rotary tool is formed on the upper aluminum alloy plate, and below the concave portion, The upper aluminum alloy plate and the lower aluminum alloy plate are joined. Here, it can be seen that no defect or the like is observed in the bonding region, and that a good bonding is achieved.
- FIG. 12 shows a surface photograph of the stirring section obtained in Examples 6-8. It can be seen that a linear stirring region is formed under any conditions. Moreover, the friction stir is achieved satisfactorily and no groove-like defects are confirmed.
- Fig. 13 shows a cross-sectional photograph of the joint obtained in Example 6. Even in the cross-sectional photograph, no defect is confirmed, and it can be seen that a good stirring portion is formed even when the rotational speed of the rotary tool is set extremely low.
- FIG. 14 shows a cross-sectional photograph of the joint (400 rpm, 4.5 ton, 10 s) obtained in Comparative Example 1. Similar to the joint obtained in Example 1, a recess is formed in the upper carbon steel plate, and the upper carbon steel plate and the lower carbon steel plate are joined below the recess. Here, no defect or the like is observed in the bonding region.
- FIG. 17 shows the relationship between the minimum hardness of the joint obtained in Example 1 and Comparative Example 1 and the rotational speed of the rotary tool.
- the minimum hardness of the joint (200 to 1200 rpm) obtained in Comparative Example 1 is significantly lower than the hardness of the base material regardless of the joining conditions.
- the minimum hardness shows a high value.
- FIG. 17 when the rotational speed is set to 80 rpm, a decrease in the hardness of the joint is effectively suppressed. In particular, when the rotational speed is set to 50 rpm, the suppression effect is remarkable. When the rotational speed is set to 30 rpm, almost no decrease in hardness from the base material is observed.
- FIG. 18 shows the relationship between the minimum hardness of the joint obtained in Example 1 and Comparative Example 1 and the base material hardness.
- the hardness reduction from the base material hardness is remarkable, but for the joint obtained in Example 1, the hardness reduction is clearly reduced.
- the rotation speed is 30 rpm, the hardness does not decrease until the base material hardness is 350 HV.
- FIG. 19 and 20 show the hardness distribution (horizontal direction of the joint) of the joint obtained in Example 3 and Example 4.
- FIG. Even when friction stir welding, which is solid phase bonding, is used, in the conventional aluminum alloy plate (JIS-A6061-T6) joint, it was inevitable to form a softened region (heat affected zone). No softened region (heat affected zone) less than the base metal hardness is observed in the joints obtained in 3 and Example 4.
- FIG. 21 shows the hardness distribution (horizontal direction of the joint) of the joint obtained in Example 6. In addition, it measured in the upper part of the stirring part, the middle part, and the lower part, respectively.
- the pure aluminum used as the test material is not an O material but an H24 material, but the hardness of the stirring portion shows a significantly higher value than that of the base material.
- a softened region (heat affected zone) having a hardness lower than the base material hardness is not recognized at the joint.
- FIG. 22 shows the shear tensile strength of the joints obtained in Example 2 and Comparative Example 2. Since the joint obtained in Comparative Example 2 breaks from the softened region (heat-affected zone), the shear tensile strength remains at about 8 kN. On the other hand, the joint obtained in Example 2 in which the softened region (heat affected zone) is not formed has a shear tensile strength of about 12 kN.
- the shear tensile strength is 5.5 kN when the joining condition is 6 tons, 50 rpm, and 30 seconds, and the shear tensile strength when the joining conditions are 7 tons, 40 rpm, and 30 seconds is 4. It was 8 kN.
- the joint obtained in Comparative Example 3 has a shear tensile strength of 2.7 kN. In Example 3, a joint having a significantly higher shear tensile strength than that of the conventional friction stir spot joining is obtained. I understand that.
- FIG. 23 and FIG. 24 show orientation map images in the vicinity of the joint interface for the joints obtained in Example 1 and Example 2, respectively. Near both joint interfaces, fine equiaxed grains are generated by recrystallization, and the average crystal grain system is significantly lower than 1 ⁇ m (Example 1: 0.25 ⁇ m, Example 2: 0.33 ⁇ m).
- FIG. 25 shows an orientation map image in the vicinity of the bonding interface with respect to the bonding portion obtained in Comparative Example 3. While the average crystal grain size of the base material is 20 ⁇ m, the average crystal grain size of the fine equiaxed grains generated in the vicinity of the bonding interface is 0.24 ⁇ m.
- FIG. 26 shows the relationship between the maximum joining temperature and the tool rotation speed in Example 1 and Comparative Example 1.
- the maximum joining temperature in Example 1 is dramatically lower than that in Comparative Example 1, and it can be seen that joining of carbon steel sheets is achieved at a low temperature around 300 ° C. Moreover, the said result has shown that joining temperature less than the recrystallization temperature (about 600 degreeC) which a carbon steel plate (S45C) originally has was implement
- FIG. 27 shows the temperature change during joining in Example 3. It can be seen that the bonding temperature rose from the start of bonding and reached the highest temperature at the end of the bonding time, but remained at an extremely low temperature of 92.1 ° C. at 40 rpm and 69.9 ° C. at 30 rpm. . The results also show that a bonding temperature lower than the recrystallization temperature (250 to 350 ° C.) inherent to the aluminum alloy plate (A6061) has been realized.
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Abstract
Description
2つの金属材を被接合部において対向させて被接合界面を形成し、前記被接合部に所定の回転速度で回転させた回転ツールを圧入することで前記2つの金属材を接合する方法であって、
前記回転ツールの最外周の周速を51mm/s以下とすることにより、前記被接合部に強ひずみを導入して前記金属材が本来有する再結晶温度を低下させ、
接合温度を前記金属材が本来有する再結晶温度未満として前記被接合界面に再結晶粒を生成させること、
を特徴とする金属材の低温接合方法、を提供する。
350HV未満の母材硬度を有する高張力鋼材の接合部を有し、
前記接合部には平均粒径が1μm以下の微細等軸再結晶粒を含み、
前記接合部及び熱影響部の硬度が略前記母材硬度以上であること、
を特徴とする接合構造物も提供する。
少なくとも1つ以上の基材部と、
前記基材部同士を接合した接合部と、を有し、
前記基材部は高張力鋼材又は熱処理型アルミニウム合金材であり、
前記接合部は前記基材部と略同一の組成を有し、
前記接合部は平均粒径が1μm以下の微細等軸再結晶粒を含み、
前記接合部及び熱影響部の硬度が前記基材部の略8割以上であること、
を特徴とする接合構造物も提供する。
前記接合部及び前記熱処理部の硬度が前記母材硬度の略9割以上であること、が好ましい。熱処理型アルミニウムは溶接時の温度上昇によって容易に硬度低下が生じるが、基材部に熱処理型アルミニウム合金材を用いた場合であっても、接合部及び熱処理部の硬度が母材硬度の略9割以上を維持している。
本発明の金属材の低温接合方法は、その接合メカニズムは異なるが、接合プロセスは摩擦攪拌接合に類似している。摩擦攪拌接合とは、FSW(Friction Stir Welding)と称され、接合しようとする二つの金属材からなる被接合材それぞれの端部を突き合わせ、回転ツールの先端に設けられた突起部(プローブ)を両者の端部の間に挿入し、これら端部の長手方向に沿って回転ツールを回転させつつ移動させることによって、二つの金属部材を接合する方法である。
図4に、本発明の接合構造物における接合部近傍の概略断面図を示す。なお、本発明の接合構造物における接合部の代表的な態様として、図4ではスポット接合部を示している。
図5に示す配置で炭素鋼板(JIS-S45C)同士を重ね合わせ、上側の炭素鋼板から回転ツールを圧入して点接合を施した。ここで、回転ツールにはWC-Ni超硬合金製の円柱状ツール(φ12mm,プローブなし)を用い、炭素鋼板の板厚は1.0mm又は1.5mmとした。回転ツールの回転速度は30rpm又は50rpm、荷重は12ton又は15ton、接合時間は10秒又は30秒とした。なお、上述のとおりFeの再結晶温度は~500℃であり、炭素鋼であるS45Cの再結晶温度は約600℃である。
回転ツールに工具鋼製(日立金属,YXR33)の円柱状ツール(φ12mm,プローブ:φ4mm,長さ1.8mm)を使用し、回転ツールの回転速度を50rpm、荷重を15ton、接合時間を10秒としたこと以外は実施例1と同様にして、点接合を施した。
回転ツールに工具鋼製(JIS-SKD61)の円柱状ツール(φ12mm,プローブ:φ4mm,長さ1.8mm)、被接合材に低炭素鋼板(JIS-SPCC)を用い、回転ツールの回転速度を50rpm、荷重を6ton、接合時間を60秒としたこと以外は実施例1と同様にして、点接合を施した。
図5に示す配置で、アルミニウム合金板(JIS-A6061-T6)同士を重ね合わせ、上側のアルミニウム合金板から回転ツールを圧入して点接合を施した。ここで、回転ツールにはWC-Ni超硬合金製の円柱状ツール(φ12mm,プローブなし)を用い、アルミニウム合金板の板厚は1.0mmとした。回転ツールの回転速度は30~50rpm、荷重は3.5~8ton、接合時間は20秒又は30秒とした。なお、上述のとおりAlの再結晶温度は150~240℃であり、アルミニウム合金であるA6061の再結晶温度は250~350℃である。
回転ツールの形状をφ12mm,プローブ:φ4mm,長さ1mmとした以外は実施例4と同様にして、点接合を施した。
板厚3mmの純アルミニウム板(A1050 H24)に回転ツールを圧入して移動させることで、線状の処理領域を形成させた。回転ツールにはWC-Ni超硬合金製の円柱状ツール(φ12mm,プローブ:φ4mm,長さ0.9mm)を用いた。また、回転ツールの回転速度は50rpm、移動速度は10mm/minとし、回転ツールの位置制御にて摩擦攪拌処理を施した。
回転速度を10rpmとした以外は実施例6と同様にして、摩擦攪拌処理を施した。
回転速度を5rpmとした以外は実施例6と同様にして、摩擦攪拌処理を施した。
回転速度を200~1200rpm、荷重を4.5ton、接合時間を10秒とした以外は実施例1と同様にして、点接合を施した。
回転ツールにWC-Ni超硬合金製の円柱状ツール(φ12mm,プローブ:φ4mm,長さ1.8mm)を用いた以外は比較例1と同様にして、点接合を施した。
回転速度を2500rpm、荷重を0.4ton、接合時間を1.2秒とした以外は実施例4と同様にして、点接合を施した。
接合部における欠陥形成の有無及び接合界面の状況等を確認するため、接合部の断面を光学顕微鏡によって観察した。
上記実施例及び比較例で得られた接合部の断面について、ビッカース硬度試験を行った。なお、ビッカース硬度測定は荷重:0.1kgf、荷重負荷時間:15sの条件で行った。
上記実施例及び比較例で得られた継手に関して、せん断引張強度を測定した。測定には引張試験機(SHIMADZU Autograph AGS-X 10kN)を用い、クロスヘッド速度1mm/minで継手のせん断引張強度を測定した。
接合部における結晶粒の粒径及び形状を確認するため、接合部の断面のEBSD測定を行った。なお、EBSD測定にはFE-SEM(日本電子株式会社製JSM-7001FA)及びTSL社製のOIM data Collection ver5.31を用いた。
熱画像カメラ(CINO社製 CPA-T640)を用い、上記実施例及び比較例における接合温度の測定を行った。
4・・・回転ツール、
6・・・接合部、
8・・・本体部(ショルダ部)、
10・・・突起部(プローブ部)、
20・・・接合構造物、
22・・・基材部、
24・・・接合部、
26・・・熱影響部。
Claims (14)
- 2つの金属材を被接合部において対向させて被接合界面を形成し、前記被接合部に所定の回転速度で回転させた回転ツールを圧入することで前記2つの金属材を接合する方法であって、
前記回転ツールの最外周の周速を51mm/s以下とすることにより、前記被接合部に強ひずみを導入して前記金属材が本来有する再結晶温度を低下させ、
接合温度を前記金属材が本来有する再結晶温度未満として前記被接合界面に再結晶粒を生成させること、
を特徴とする金属材の低温接合方法。 - 前記再結晶粒の粒径を1μm以下とすること、
を特徴とする請求項1に記載の金属材の低温接合方法。 - 前記回転ツールの最外周の周速を32mm/s以下とすること、
を特徴とする請求項1及び2に記載の金属材の低温接合方法。 - 前記回転ツールの最外周の周速を19mm/s以下とすること、
を特徴とする請求項1~3のうちのいずれかに記載の金属材の低温接合方法。 - 前記回転ツールの圧入荷重を、前記回転ツールを回転させない状態で前記金属材に圧入できる値以上とすること、
を特徴とする請求項1~4のうちのいずれかに記載の金属材の低温接合方法。 - 前記回転ツールから前記金属材に印加される応力が、前記被接合部の温度における前記金属材の降伏応力以上となる範囲において、
前記圧入荷重を前記被接合部の温度上昇に伴って低下させること、
を特徴とする請求項1~5のうちのいずれかに記載の金属材の低温接合方法。 - 前記金属材がアルミニウム又はアルミニウム合金であること、
を特徴とする請求項1~6のうちのいずれかに記載の金属材の低温接合方法。 - 前記金属材が熱処理型アルミニウム合金、加工強化型アルミニウム又は加工強化型アルミニウム合金であること、
を特徴とする請求項1~7のうちのいずれかに記載の金属材の低温接合方法。 - 前記金属材が鉄系金属であること、
を特徴とする請求項1~6のうちのいずれかに記載の金属材の低温接合方法。 - 前記回転ツールが鉄系金属製であること、
を特徴とする請求項1~9のうちのいずれかに記載の金属材の低温接合方法。 - 少なくとも1つ以上の基材部と、
前記基材部同士を接合した接合部と、を有し、
前記基材部は高張力鋼材又は熱処理型アルミニウム合金材であり、
前記接合部は前記基材部と略同一の組成を有し、
前記接合部は平均粒径が1μm以下の微細等軸再結晶粒を含み、
前記接合部及び熱影響部の硬度が前記基材部の略8割以上であること、
を特徴とする接合構造物。 - 前記基材部が350HV以上の母材硬度を有する高張力鋼材であること、
を特徴とする請求項11に記載の接合構造物。 - 前記基材部が350HV未満の母材硬度を有する高張力鋼材であり、
前記接合部及び前記熱影響部の硬度が略前記母材硬度以上であること、
を特徴とする請求項11に記載の接合構造物。 - 前記基材部が熱処理型アルミニウム合金材であり、
前記接合部及び前記熱処理部の硬度が前記母材硬度の略9割以上であること、
を特徴とする請求項11に記載の接合構造物。
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