WO2012172895A1 - 被覆回転ツール - Google Patents

被覆回転ツール Download PDF

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Publication number
WO2012172895A1
WO2012172895A1 PCT/JP2012/062132 JP2012062132W WO2012172895A1 WO 2012172895 A1 WO2012172895 A1 WO 2012172895A1 JP 2012062132 W JP2012062132 W JP 2012062132W WO 2012172895 A1 WO2012172895 A1 WO 2012172895A1
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WO
WIPO (PCT)
Prior art keywords
coating layer
friction stir
stir welding
welding tool
joined
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Ceased
Application number
PCT/JP2012/062132
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English (en)
French (fr)
Japanese (ja)
Inventor
森口　秀樹
慶春 内海
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Sumitomo Electric Industries Ltd
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Sumitomo Electric Industries Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Sumitomo Electric Industries Ltd filed Critical Sumitomo Electric Industries Ltd
Priority to US14/126,218 priority Critical patent/US20140124564A1/en
Priority to EP12800868.7A priority patent/EP2722126B1/en
Publication of WO2012172895A1 publication Critical patent/WO2012172895A1/ja
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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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
    • B23K20/1255—Tools therefor, e.g. characterised by the shape of the probe
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
    • C23C14/06—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the coating material
    • C23C14/0641—Nitrides
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
    • C23C14/22—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the process of coating
    • C23C14/24—Vacuum evaporation
    • C23C14/32—Vacuum evaporation by explosion; by evaporation and subsequent ionisation of the vapours, e.g. ion-plating
    • C23C14/325—Electric arc evaporation
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
    • C23C28/04—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings of inorganic non-metallic material
    • C23C28/042—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings of inorganic non-metallic material including a refractory ceramic layer, e.g. refractory metal oxides, ZrO2, rare earth oxides
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
    • C23C28/04—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings of inorganic non-metallic material
    • C23C28/044—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings of inorganic non-metallic material coatings specially adapted for cutting tools or wear applications
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
    • C23C28/40—Coatings including alternating layers following a pattern, a periodic or defined repetition
    • C23C28/42—Coatings including alternating layers following a pattern, a periodic or defined repetition characterized by the composition of the alternating layers
    • 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
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02T—CLIMATE CHANGE MITIGATION TECHNOLOGIES RELATED TO TRANSPORTATION
    • Y02T50/00—Aeronautics or air transport
    • Y02T50/60—Efficient propulsion technologies, e.g. for aircraft

Definitions

  • the present invention relates to a friction stir welding tool.
  • friction stir welding technology for joining metal materials such as aluminum alloys was established.
  • frictional heat is generated by rotating while pressing a cylindrical friction stir welding tool having a small-diameter protrusion formed at the tip of a joining surface between metal materials for joining. Then, the metal materials are joined together by softening the metal material at the joining portion with this frictional heat to cause plastic flow.
  • the “joining portion” refers to a joining interface portion where joining of metal materials is desired by abutting metal materials or placing metal materials in an overlapping manner.
  • the metal material In the vicinity of the bonding interface, the metal material is softened to cause plastic flow.
  • the bonding interface disappears and bonding is performed.
  • dynamic recrystallization occurs at the same time in the metal material, the metal material near the bonding interface is atomized by the dynamic recrystallization, and the metal materials can be bonded with high strength (Japanese Patent Laid-Open No. 2003). -326372 (Patent Document 1)).
  • the friction stir welding technique is mainly applied to non-ferrous metals that cause plastic flow at a relatively low temperature, such as aluminum alloys and magnesium alloys.
  • a friction stir welding technique is superior to the resistance welding method in terms of the cost and time required for joining, the strength of the joined portion, and the like. For this reason, there is a need to apply not only to joining materials that cause plastic flow at low temperatures, but also to joining copper alloys and steel materials that cause plastic flow at high temperatures of 1000 ° C. or higher.
  • Patent Document 1 a portion of the surface of a friction stir welding tool that is in contact with a material to be joined is coated with a diamond film. Friction stir that increases the surface hardness and suppresses welding of low-melting light alloy components such as Al alloy and Mg alloy, which are to be joined, to the friction stir welding tool, thereby extending the tool life A joining tool is disclosed.
  • a friction stir welding tool such as that disclosed in Japanese Patent Application Laid-Open No. 2003-326372 (Patent Document 1), the wear resistance of the surface can be improved, and the tool life can be extended.
  • the diamond film has a very high thermal conductivity, a part of the frictional heat generated by the rotation of the friction stir welding tool escapes to the friction stir welding tool side, and the frictional heat is sufficiently generated on the workpiece side. It becomes difficult to conduct. As a result, it takes a long time until the plastic flow occurs after the small diameter protrusion of the friction stir welding tool is pressed against the material to be joined.
  • Patent Document 2 discloses a heat flow barrier in order not to conduct heat to the shaft portion of the friction stir welding tool. The providing technique is disclosed. By providing the heat flow barrier in this manner, frictional heat can be concentrated on the material to be joined.
  • Patent Document 3 provides a base layer on a base material, and TiN is formed on the base layer.
  • a friction stir welding tool provided with an adhesion prevention film made of TiAlN or the like is disclosed. Since such a tool for friction stir welding can prevent the metal component (aluminum) of the material to be bonded from adhering even when used for a long time, it can continue stable processing.
  • Patent Document 3 Japanese Patent Laid-Open No. 2005-152909
  • Patent Document 3 Japanese Patent Laid-Open No. 2005-152909
  • the friction stir welding tool The surface temperature of the tool is exposed to a high temperature of 1000 ° C. or higher, and the generated frictional heat conducts to the base material, and the base material is easily plastically deformed. Therefore, it can be said that the tool life of the tool is sufficiently long. There wasn't.
  • the adhesion prevention film of Japanese Patent Application Laid-Open No. 2005-152909 has a high thermal permeability, so that frictional heat generated by rotation with the material to be joined is thermally conducted to the base material, Frictional heat could not be sufficiently transmitted to the material to be joined, and it took time until the material to be joined became hot and plastic flow occurred.
  • an object of the present invention is to provide a friction stir welding tool that efficiently performs friction stir welding, bonds well at a low rotational speed, and is excellent in oxidation resistance and wear resistance.
  • the friction stir welding tool of the present invention includes a base material and a coating layer formed on the base material.
  • the coating layer is composed of two or more layers, and the entire coating layer is 8000 J. / S 0.5 ⁇ m 2 ⁇ K or less, at least one of the coating layers contains a hexagonal crystal system and / or amorphous, and at least one of the coating layers is cubic It includes a crystal-type crystal system, and the covering layer has a compressive stress.
  • the covering layer is preferably composed of 10 or more layers, more preferably 100 or more layers.
  • the coating layer preferably has a thickness of 10 ⁇ m or more.
  • the friction stir welding tool has a chuck portion that is chucked by the holder, and the coating layer is formed at least on the chuck portion on the base material.
  • the coating layer is preferably formed at least on a portion of the base material that is in contact with the material to be joined during the joining process. At least one of the coating layers is preferably formed by physical vapor deposition.
  • the present invention is a method for joining materials to be joined using a friction stir welding tool, wherein the joining is performed on materials to be joined having a melting point of 1000 ° C. or higher.
  • the friction stir welding tool of the present invention as described above can be suitably used for joining materials to be joined made of high melting point materials.
  • the friction stir welding tool of the present invention has the above-described configuration, thereby promoting the temperature rise of the materials to be joined at the time of joining, enabling friction stir welding in a short time, and the coating layer having excellent heat insulation properties. In addition, it exhibits the effect of excellent oxidation resistance and wear resistance.
  • the friction stir welding tool having such a configuration has a simple and inexpensive structure as compared with the structure of Patent Document 2 including a heat flow barrier made of a different kind of material, and makes it difficult to raise the temperature of the base material. In addition to being able to be joined in a short time, excellent wear resistance can be realized.
  • FIG. 1 is a schematic cross-sectional view of the friction stir welding tool of the present invention.
  • the friction stir welding tool 1 of the present invention includes a base material 2 and a coating layer 3 formed on the base material 2.
  • the friction stir welding tool 1 of the present invention having such a configuration can be used extremely usefully for, for example, wire joining (FSW) applications, spot joining (spot FSW) applications, and the like.
  • the friction stir welding tool 1 of the present invention has a shape including a probe portion 4 having a small diameter (diameter 2 mm or more and 8 mm or less) and a cylindrical portion 5 having a large diameter (diameter 4 mm or more and 20 mm or less).
  • the member to be joined is joined by rotating the probe portion 4 in a state where it is inserted or pressed into the joining portion of the joined material.
  • the probe portion 4 is pressed or inserted into two materials to be bonded in a laminated or line contact state, and the rotating probe portion 4 is linear with respect to the laminated or abutted portion.
  • the probe part 4 that rotates to a desired joining location of two joined materials that are stacked or abutted on each other is pressed, and the probe part 4 is continuously rotated at that location. Join materials together.
  • the present invention also relates to a method for joining materials to be joined using a friction stir welding tool, wherein the joining can be performed on materials to be joined having a melting point of 1000 ° C. or higher.
  • the friction stir welding tool of the present invention can be joined to a material to be joined having a melting point of 1000 ° C. or higher, which has been considered difficult to join with a conventional friction stir welding tool. It has the usability of.
  • the friction stir welding tool 1 of the present invention can be used for various applications, it can be suitably used particularly for joining high-strength steels that have been mainly used in the resistance welding method in the past. . That is, the friction stir welding tool 1 of the present invention provides a means to replace the conventional resistance welding method in such high-strength steel joining applications. In addition to joining the joining material, dynamic recrystallization occurs at the joint, so the structure becomes finer, and the joining material is joined compared to the conventional resistance welding method in which the joined material becomes a liquid phase during joining. The strength of the portion is improved. Therefore, the friction stir welding tool of the present invention can be very effectively used for joining high-strength steels having high specific strength, particularly ultra-high-strength steels of 980 MPa or more.
  • FIG. 2 is a schematic cross-sectional view of a preferred embodiment of the friction stir welding tool of the present invention.
  • the friction stir welding tool 1 of the present invention preferably has a chuck portion 7 so that the cylindrical portion 5 is chucked by the holder.
  • a chuck portion 7 can be formed, for example, by cutting a part of the side surface of the cylindrical portion 5.
  • a shoulder portion 6 a portion that comes into contact with the material to be joined at the time of joining processing.
  • the covering layer 3 is more preferably formed at least in a portion on the base material 2 and in contact with the material to be joined at the time of joining processing.
  • the friction stir welding tool 1 of the present invention preferably includes a base material 2 and a coating layer 3 on the whole surface or part of the chuck portion 7 on the base material 2.
  • a coating layer 3 on the surface of the chuck portion 7 on the base material 2 in this way, the heat of the friction stir welding tool 1 that has become high temperature due to the conduction of frictional heat does not escape to the holder in contact with it. Can be conducted to the material to be joined.
  • the materials to be joined can be friction stir welded in a short time or at a low rotational speed.
  • the life of the friction stir welding tool 1 can be improved.
  • a conventionally known material known as such a base material 2 for joining processing can be used without particular limitation.
  • cemented carbide for example, WC base cemented carbide, including WC, including Co, or further including carbonitride such as Ti, Ta, Nb, etc.
  • cermet TiC, TiN, TiCN, etc.
  • High-speed steel, tool steel, ceramics such as titanium carbide, silicon carbide, silicon nitride, aluminum nitride, aluminum oxide, sialon, and mixtures thereof), cubic boron nitride sintered body
  • the substrate 2 include diamond sintered bodies, hard materials in which cBN particles are dispersed, and the like. Among these, when a Ti nitride or carbonitride is included in the base material, excellent oxidation resistance can be expected, so that it is very preferable as a tool for friction stir welding exposed to a high-temperature oxidizing
  • the base material 2 used in the present invention may have a modified surface.
  • a de- ⁇ layer may be formed on the surface, or in the case of cermet, a surface hardened layer may be formed, and even if the surface is modified in this way, The effect is shown.
  • the coating layer 3 formed on the base material 2 is composed of two or more layers, and the entire coating layer has a heat permeability of 8000 J / s 0.5 ⁇ m 2 ⁇ K or less. It is characterized by having.
  • the frictional heat generated by the rotation of the friction stir welding tool is less likely to be conducted to the base material side and more easily conducted to the material to be joined.
  • the temperature rise of the material can be promoted, and the plastic flow of the material to be joined can be accelerated.
  • Thermal effusivity of such a coating layer 3 is more preferably less 6000J / s 0.5 ⁇ m 2 ⁇ K, more preferably not more than 5500J / s 0.5 ⁇ m 2 ⁇ K.
  • the thermal permeability of the coating layer 3 adopts a value calculated using a thermophysical microscope (product name: Thermal Microscope TM3 (BETHEL)) using a thermoreflectance method. To do.
  • the effect of the present invention is shown by the fact that the coating layer 3 of the present invention has a heat shielding property as a whole, so that the frictional heat hardly penetrates into the base material.
  • a coating layer as a whole 8000J / s 0.5 ⁇ m 2 ⁇ K or less in the thermal effusivity of the present invention, not necessarily one layer constituting the coating layer is 8000J / s 0.5 ⁇ m 2 ⁇ K or less of heat penetration It does not have to be a rate.
  • the coating layer 3 formed on the base material 2 of the friction stir welding tool 1 of the present invention includes two or more layers. That is, the coating layer 3 is composed of two or more layers having different compositions.
  • At least one of the coating layers 3 includes a hexagonal crystal system and / or an amorphous material.
  • a hexagonal crystal system or an amorphous material By including a hexagonal crystal system or an amorphous material in this way, frictional heat generated by rotation becomes difficult to be conducted to the base material 2 side and easily conducted to the material to be joined, and the temperature of the material to be joined is increased. Can be promoted. Thereby, the plastic flow of a to-be-joined material can be sped up, and a joining speed can be sped up more.
  • the welding resistance to steel can be improved, and the wear resistance can be improved.
  • At least one of the coating layers 3 includes a cubic crystal system. Since a layer containing a cubic crystal system has a property of high hardness, the wear resistance can be improved by including one or more layers containing a cubic crystal system.
  • the layer containing the cubic crystal system includes a case of containing a hexagonal crystal system and / or an amorphous material. That is, the layer containing a cubic crystal system may be composed of a mixed crystal of a cubic crystal system and a hexagonal crystal system and / or amorphous. In this case, the layer containing a cubic crystal system also serves as a layer containing a hexagonal crystal system and / or an amorphous material.
  • the crystal structure of said coating layer can be confirmed by the diffraction peak of XRD (X-ray diffraction).
  • Such a coating layer 3 is provided for imparting the above-mentioned characteristics.
  • the wear resistance, oxidation resistance, toughness, and used probe of the friction stir welding tool 1 are used. It is possible to impart an action of improving various characteristics such as coloring property for identification.
  • the coating layer is a compound comprising a nitride or an oxide of Al and at least one element selected from the group consisting of Ti, Si, Zr, Hf, Nb, Ta, Mo, Cr and W, Alternatively, it is preferably composed of a solid solution of the compound.
  • the atomic ratio of Al is preferably 50 to 65%. If the Al ratio exceeds 65%, hexagonal crystals are precipitated. It was thought that the hardness of the layer was reduced and the wear resistance was reduced.
  • the present inventors have discovered a new fact that overturns conventional technical common sense. That is, according to the conventional knowledge, when forming AlTiN, the atomic ratio of Al was adjusted to 65% or less in order to avoid the formation of hexagonal crystals in the coating layer. It has been found that even if hexagonal crystals are formed in a part of the coating layer, the effect of improving the wear resistance can be obtained by reducing the thermal permeability of the entire coating layer. In other words, in order to improve the wear resistance, it is clear that it is preferable to form a hexagonal crystal structure at least partially in the coating layer, contrary to the prior art.
  • the inventors have examined the atomic ratio of Al to the metal to be combined.
  • the atomic ratio of Al when combined with V, the atomic ratio of Al is 70% or more, and when combined with Cr, the atomic ratio of Al is 75% or more, W
  • the atomic ratio of Al when combined with Nb, the atomic ratio of Al is 55% or more, and when combined with Hf, the atomic ratio of Al is 20% or more, so that hexagonal crystals can be easily precipitated in the coating layer and wear resistance is improved. It became clear that it improved remarkably.
  • a suitable atomic ratio of Al when a metal other than Ti, V, Cr, W, Nb, Hf, etc. is not shown, the coating layer may contain hexagonal crystals even with other metals.
  • the atomic ratio of Al is adjusted, the effect of the present invention is presumed to be obtained.
  • the atomic ratio of Si with respect to the metal element contained in the coating layer is 10% or less.
  • the coating layer is preferably composed of 10 or more layers, more preferably 100 or more layers.
  • the coating layer is preferably composed of 10 or more layers, more preferably 100 or more layers.
  • the coating layer includes at least a part of the super multi-layer structure.
  • a super multi-layer structure is a laminate in which two or more layers having different properties and compositions are laminated with a thickness of several nanometers to several hundreds of nanometers (usually alternately laminated one above the other).
  • the coating is performed using a plurality of different targets at the same time, so the film formation speed is excellent, and film characteristics such as hardness, heat insulation, and oxidation resistance of the coating layer are combined by combining layers with different properties and compositions. Is preferable.
  • the coating layers 3 since at least one of the coating layers 3 needs to be coated so as to have high adhesion to the base material 2, it is formed by a film forming process having high adhesion to the base material 2. It is preferable that As such a film forming process, any conventionally known film forming process can be used. For example, a PVD (physical vapor deposition) method, a CVD (chemical vapor deposition) method, or the like can be used. These film forming processes may be combined.
  • the PVD method can form the coating layer 3 at a lower temperature than the CVD method, and can form the film while distorting the coating layer 3, so that the crystal grains tend to be finely divided.
  • a coating layer having a low heat permeability can be formed.
  • compressive stress can be introduced into the coating layer 3, and chipping of the coating layer that is likely to occur during use of the tool can be easily suppressed.
  • PVD method suitably used in the present invention
  • a conventionally known PVD method can be used without any particular limitation.
  • PVD methods include sputtering, arc ion plating, and vapor deposition.
  • the coating layer of the present invention preferably has a thickness of 5 ⁇ m or more and 50 ⁇ m or less.
  • the thickness of the coating layer of the present invention is more preferably 10 ⁇ m or more and 30 ⁇ m or less, and further preferably 10 ⁇ m or more and 20 ⁇ m or less. Thereby, the tool life can be further extended and the chipping resistance can be improved.
  • the thickness of the coating layer refers to the thickness of the coating layer on any part of the surface of the friction stir welding tool.
  • the thickness of the coating layer formed on the base material of the friction stir welding tool Of the thickness it means the thickness of the coating layer at the tip of the probe portion.
  • the coating layer of the present invention is preferably formed so as to cover the entire surface of the base material, but a part of the base material is not covered by the coating layer, or any part on the base material However, even if the coating layer has a different structure, it does not depart from the scope of the present invention.
  • the coating layer in this invention is at least on a base material, Comprising: It is preferable to form in the whole surface or part of a chuck
  • the coating layer of the present invention has a compressive stress.
  • the chipping resistance of a coating layer can be improved because a coating layer has a compressive stress.
  • the presence or absence of compressive stress in the coating layer can be determined by the sin 2 ⁇ method using an X-ray stress measurement apparatus.
  • At least one of the coating layers of the present invention is preferably formed by a physical vapor deposition (PVD) method, and can be formed by any PVD method as long as the PVD method is used.
  • PVD physical vapor deposition
  • the type of formation method is not particularly limited.
  • the elements constituting the coating layer 3 are supplied to the base material in a low energy in an ionic state, so that the impact when these both collide is small. As a result, the crystallinity of the coating layer formed becomes low, and the thermal permeability of the coating layer 3 formed as a result can be reduced.
  • the crystal structure of the coating layer 3 is hexagonal or amorphous,
  • the thermal permeability of at least one of the coating layers can be reduced.
  • the bombardment process before forming the coating layer 3 is performed by adjusting the consistency between the crystal grains contained in the coating layer 3 and the WC crystal grains contained in the substrate in the interface region between the base material 2 and the coating layer 3. It is an important process to enhance. Specifically, after introducing the argon gas, the substrate bias voltage is maintained at ⁇ 1500 V, and the surface of the cemented carbide substrate is bombarded while emitting thermoelectrons by the W filament, and then the coating layer 3 is formed. In the interface region between the base material 2 and the coating layer 3, the crystal grains contained in the coating layer 3 and the WC crystal grains contained in the base material can have consistency.
  • the surface of the WC crystal grains in the interface region and the oxide layer can be removed by the bombarding treatment, and the surface activity of the WC crystal grains is increased, so that the crystal grains of the coating layer are separated from the WC crystal grains. It is thought that it is because it grows with consistency. As described above, the consistency between the crystal grains contained in the coating layer and the WC crystal grains contained in the base material is enhanced, and the bonding force between the coating layer and the WC crystal grains (that is, the base material) is strong. Thus, excellent peel resistance can be realized. When nitride or carbonitride is present in the substrate, particularly excellent peel resistance is exhibited.
  • the thickness of the coating layer in an Example is measured by directly observing the cross section using a scanning electron microscope (SEM: Scanning Electron Microscope) or a transmission electron microscope (TEM: Transmission Electron Microscope).
  • the coating layer is formed by the cathode arc ion plating method, but the coating layer may be formed by, for example, a balanced or unbalanced sputtering method.
  • the friction stir welding tool shown in FIG. 1 is produced.
  • the friction stir welding tool of the present embodiment includes a substantially cylindrical column portion 5 having a diameter of 10 mm and a height of 20 mm, and a probe portion 4 projecting concentrically with the column portion 5 at the center of the tip of the column portion 5. And have.
  • the probe portion 4 has a substantially cylindrical shape with a diameter of 4 mm and a height of 0.7 mm.
  • a base material for the friction stir welding tool a base material having the above-described tool shape and having the material shown in Table 1 below is prepared.
  • the base material is made of cemented carbide and contains WC crystal grains.
  • the average grain size of the crystal grains (the surface of the base material (interface portion with the coating layer)) is shown in Table 1. As described.
  • the inside of the chamber of the apparatus is depressurized by a vacuum pump, and the temperature of the base material is heated to 450 ° C. by a heater installed in the apparatus, so that the pressure in the chamber is 1.0 ⁇ 10 ⁇ 4 Pa. Evacuate until
  • argon gas is introduced to maintain the pressure in the chamber at 3.0 Pa, the substrate bias power supply voltage of the base material is gradually increased to ⁇ 1500 V, and the W filament is heated to emit thermoelectrons. Then, the surface of the substrate is cleaned for 15 minutes. Thereafter, the argon gas is exhausted.
  • the friction stir welding tool of this embodiment has a probe portion 4 and a shoulder portion 6 as shown in FIG. 2, but has a chuck portion 7 so that the cylindrical portion 5 is chucked by the holder.
  • the chuck portion 7 is scraped from two opposite directions on the side surface of the cylindrical portion 5 at a portion 10 mm from the upper surface of the cylindrical portion 5, and has a substantially cylindrical cross section. When the chuck portion 7 is viewed from the holder side, the length of the chord formed by cutting is 7 mm.
  • the friction stir welding tool of Example 1 is manufactured by forming a coating layer on the probe portion and the shoulder portion 6 so as to be in direct contact with the base material. Specifically, using an alloy target (Ti 0.5 Al 0.5 and Al 0.75 Ti 0.25 ) which is a metal evaporation source set in advance, while introducing nitrogen gas as a reaction gas, the reaction gas pressure is 4.0 Pa.
  • an alloy target Ti 0.5 Al 0.5 and Al 0.75 Ti 0.25
  • an arc current of 100 A is supplied to the cathode electrode, metal ions are generated from an arc evaporation source, and a Ti 0.5 Al 0.5 N layer having a thickness of 6 ⁇ m; A covering layer composed of an Al 0.75 Ti 0.25 N layer having a thickness of 6 ⁇ m is formed on the probe portion and the shoulder portion 6.
  • Example 2 to 7 the friction stir welding tool was prepared by the same method as in Example 1 except that the composition and composition of the coating layer were different from those in Example 1 as shown in Table 2 below. Make it.
  • Example 3 a Ti 0.5 Al 0.5 N layer having a thickness of 0.05 ⁇ m and an Al 0.75 Ti 0.25 N layer having a thickness of 0.05 ⁇ m are alternately stacked on each substrate in a total of 240 layers.
  • a coating layer composed of layers is formed.
  • two types of compositions are listed, but after forming the composition described on the left side first, the composition described on the right side immediately above it. It means to form.
  • Example 8 a friction stir welding tool is produced in the same manner as in Example 3 except that the coating layer is formed on the chuck portion in addition to the probe portion and the shoulder portion as compared with Example 3.
  • the friction stir welding tools of Comparative Examples 1 and 3 to 5 are manufactured by the same method as in Example 1 except that the composition of the coating layer is different from that of Example 1 as shown in Table 2.
  • the friction stir welding tool of Comparative Example 2 is produced by forming a coating layer having the composition shown in Table 2 on the base material shown in Table 1 using a known CVD method.
  • thermophysical microscope using a thermoreflectance method product name: thermal microscope TM3 (stock), for the coating layers of the friction stir welding tools of Examples 1 to 9 and Comparative Examples 1 to 5 manufactured as described above.
  • the heat penetration rate of the entire coating layer was measured by the company BETHEL)), and the result is shown in the column of “Heat penetration rate” in Table 2.
  • the compressive residual stress of the coating layer is measured by the sin 2 ⁇ method using an X-ray stress measuring apparatus and it is determined that there is a compressive stress, “Yes” is displayed in the “Compressive stress” column of Table 2. In the case where it is determined that there is no compressive stress, “None” is indicated in the “compressive stress” column of Table 2.
  • the crystal structure of the coating layer of the friction stir welding tool of each example and each comparative example is confirmed by electron beam diffraction using XRD (X-ray diffraction) or TEM.
  • XRD X-ray diffraction
  • TEM TEM-ray diffraction
  • the approach speed is evaluated according to the following evaluation criteria.
  • the number of spots means the number of junction points.
  • Abrasion resistance After spot bonding (spot FSW) of 1000 spots, the diameter of the probe portion is measured, and the wear resistance is evaluated according to the following evaluation criteria based on the diameter reduction amount (mm).
  • Abrasion reduction is less than 0.05 mm
  • the friction stir welding tools of Examples 1 to 9 are superior in balance of joining speed, wear resistance, and welding resistance to those of Comparative Examples 1 to 5.
  • the reason why the joining speed is increased is that the frictional heat generated by using a coating layer having a thermal permeability of 8000 J / s 0.5 ⁇ m 2 ⁇ K or less. This is thought to be due to effective use.
  • the reason why the wear resistance is improved is considered to be due to the fact that the coating layer has a layer containing a cubic crystal system, and the reason why the weld resistance is improved is that the hexagonal crystal system and This is considered to be due to containing amorphous. Further, it is considered that the chipping resistance is improved when the coating layer has a compressive stress.
  • the friction stir welding tool according to the present invention of Examples 1 to 9 can be expected to have a longer life and the joining efficiency can be improved as compared with the friction stir welding tool of Comparative Examples 1 to 5. Can be confirmed.
  • the friction stir welding tool of Example 8 has a higher tool entry speed than the friction stir welding tool of Example 3. This is because the friction stir welding tool of Example 8 has a coating layer also formed on the chuck portion, so the heat of the friction stir welding tool, which has become high due to the conduction of frictional heat, is applied to the holder in contact with it. It is considered that heat is accumulated in the base material without escaping, and the generated frictional heat is effectively conducted to the material to be joined and softening of the material to be joined is advanced.
  • Friction stir welding tool 2 base material, 3 coating layer, 4 probe part, 5 cylinder part, 6 shoulder part, 7 chuck part.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Inorganic Chemistry (AREA)
  • Ceramic Engineering (AREA)
  • Pressure Welding/Diffusion-Bonding (AREA)
PCT/JP2012/062132 2011-06-16 2012-05-11 被覆回転ツール Ceased WO2012172895A1 (ja)

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US14/126,218 US20140124564A1 (en) 2011-06-16 2012-05-11 Coated rotary tool
EP12800868.7A EP2722126B1 (en) 2011-06-16 2012-05-11 Coated rotating tool

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Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2014034730A1 (ja) * 2012-08-28 2014-03-06 三菱マテリアル株式会社 表面被覆切削工具
JP2015124407A (ja) * 2013-12-26 2015-07-06 住友電工ハードメタル株式会社 被膜、切削工具および被膜の製造方法
US20150345012A1 (en) * 2012-12-28 2015-12-03 Sumitomo Electric Hardmetal Corp. Surface coated member and method for manufacturing same
CN115181951A (zh) * 2022-07-13 2022-10-14 南昌航空大学 一种高速钢搅拌摩擦焊搅拌头用多层涂层及其制备方法

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN106392300A (zh) * 2016-11-23 2017-02-15 北京世佳博科技发展有限公司 一种提高搅拌摩擦焊搅拌头寿命的方法
JP7082356B2 (ja) * 2018-06-06 2022-06-08 国立大学法人大阪大学 摩擦攪拌接合用ツール及び摩擦攪拌接合方法
WO2020185680A1 (en) * 2019-03-08 2020-09-17 Brigham Young University Refill friction stir spot welding using superabrasive tool
CN116240485A (zh) * 2023-03-18 2023-06-09 营口理工学院 一种提高搅拌摩擦焊搅拌头耐高温摩擦磨损性能的方法

Citations (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
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
JP2003326372A (ja) 2002-05-10 2003-11-18 Nachi Fujikoshi Corp 摩擦攪拌接合用ツール
JP2004195525A (ja) * 2002-12-20 2004-07-15 Hitachi Ltd 摩擦攪拌接合方法
JP2005152909A (ja) 2003-11-21 2005-06-16 Mitsubishi Heavy Ind Ltd 回転ツール及び摩擦撹拌接合装置及び摩擦撹拌接合方法
JP2005199281A (ja) * 2004-01-13 2005-07-28 Dijet Ind Co Ltd 摩擦攪拌接合用ツール
JP2008155277A (ja) * 2006-12-26 2008-07-10 Osaka Univ 金属材の接合方法
JP2009241085A (ja) * 2008-03-28 2009-10-22 Nippon Steel Corp 接合強度特性に優れたラミネート鋼板の接合方法
JP2010520810A (ja) * 2006-08-21 2010-06-17 ハー．ツェー．スタルク リミテッド 摩擦撹拌接合用の高融点金属工具
WO2010074165A1 (ja) * 2008-12-24 2010-07-01 国立大学法人大阪大学 金属材の加工方法、金属材の加工方法によって加工された構造物及び回転ツール
JP2010264479A (ja) * 2009-05-14 2010-11-25 Osg Corp 摩擦攪拌接合用ツール
JP2011011235A (ja) * 2009-07-02 2011-01-20 Sumitomo Electric Ind Ltd 被覆回転ツール
JP2011504808A (ja) * 2007-11-16 2011-02-17 ベーレリト ゲーエムベーハー ウント コー． カーゲー． 摩擦攪拌溶接工具

Family Cites Families (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR100633286B1 (ko) * 1998-10-27 2006-10-11 미츠비시 마테리알 고베 툴스 가부시키가이샤 내마모성이 우수한 경질피막 피복부재
US7857188B2 (en) * 2005-03-15 2010-12-28 Worldwide Strategy Holding Limited High-performance friction stir welding tools
JP2009155721A (ja) * 2007-12-03 2009-07-16 Kobe Steel Ltd 摺動性に優れる硬質皮膜とその硬質皮膜の形成方法
JP5334561B2 (ja) * 2008-12-22 2013-11-06 住友電気工業株式会社 表面被覆切削工具
WO2011074530A1 (ja) * 2009-12-17 2011-06-23 住友電気工業株式会社 被覆回転ツール
JP2012130948A (ja) * 2010-12-22 2012-07-12 Sumitomo Electric Ind Ltd 回転ツール
EP2656959A4 (en) * 2010-12-22 2017-07-26 Sumitomo Electric Industries, Ltd. Rotating tool

Patent Citations (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
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
JP2003326372A (ja) 2002-05-10 2003-11-18 Nachi Fujikoshi Corp 摩擦攪拌接合用ツール
JP2004195525A (ja) * 2002-12-20 2004-07-15 Hitachi Ltd 摩擦攪拌接合方法
JP2005152909A (ja) 2003-11-21 2005-06-16 Mitsubishi Heavy Ind Ltd 回転ツール及び摩擦撹拌接合装置及び摩擦撹拌接合方法
JP2005199281A (ja) * 2004-01-13 2005-07-28 Dijet Ind Co Ltd 摩擦攪拌接合用ツール
JP2010520810A (ja) * 2006-08-21 2010-06-17 ハー．ツェー．スタルク リミテッド 摩擦撹拌接合用の高融点金属工具
JP2008155277A (ja) * 2006-12-26 2008-07-10 Osaka Univ 金属材の接合方法
JP2011504808A (ja) * 2007-11-16 2011-02-17 ベーレリト ゲーエムベーハー ウント コー． カーゲー． 摩擦攪拌溶接工具
JP2009241085A (ja) * 2008-03-28 2009-10-22 Nippon Steel Corp 接合強度特性に優れたラミネート鋼板の接合方法
WO2010074165A1 (ja) * 2008-12-24 2010-07-01 国立大学法人大阪大学 金属材の加工方法、金属材の加工方法によって加工された構造物及び回転ツール
JP2010264479A (ja) * 2009-05-14 2010-11-25 Osg Corp 摩擦攪拌接合用ツール
JP2011011235A (ja) * 2009-07-02 2011-01-20 Sumitomo Electric Ind Ltd 被覆回転ツール

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of EP2722126A4

Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2014034730A1 (ja) * 2012-08-28 2014-03-06 三菱マテリアル株式会社 表面被覆切削工具
US9415446B2 (en) 2012-08-28 2016-08-16 Mitsubishi Materials Corporation Surface coated cutting tool
US20150345012A1 (en) * 2012-12-28 2015-12-03 Sumitomo Electric Hardmetal Corp. Surface coated member and method for manufacturing same
US9777367B2 (en) * 2012-12-28 2017-10-03 Sumitomo Electric Hardmetal Corp. Surface coated member and method for manufacturing same
JP2015124407A (ja) * 2013-12-26 2015-07-06 住友電工ハードメタル株式会社 被膜、切削工具および被膜の製造方法
CN115181951A (zh) * 2022-07-13 2022-10-14 南昌航空大学 一种高速钢搅拌摩擦焊搅拌头用多层涂层及其制备方法
CN115181951B (zh) * 2022-07-13 2023-04-28 南昌航空大学 一种高速钢搅拌摩擦焊搅拌头用多层涂层及其制备方法

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EP2722126A4 (en) 2015-04-15
EP2722126A1 (en) 2014-04-23

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