WO2015104760A1 - アルミニウム合金クラッド材及びその製造方法、ならびに、当該アルミニウム合金クラッド材を用いた熱交換器及びその製造方法 - Google Patents
アルミニウム合金クラッド材及びその製造方法、ならびに、当該アルミニウム合金クラッド材を用いた熱交換器及びその製造方法 Download PDFInfo
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- WO2015104760A1 WO2015104760A1 PCT/JP2014/006306 JP2014006306W WO2015104760A1 WO 2015104760 A1 WO2015104760 A1 WO 2015104760A1 JP 2014006306 W JP2014006306 W JP 2014006306W WO 2015104760 A1 WO2015104760 A1 WO 2015104760A1
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- WIPO (PCT)
- Prior art keywords
- clad
- mass
- brazing
- aluminum alloy
- intermediate layer
- Prior art date
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- 239000000463 material Substances 0.000 title claims abstract description 467
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 107
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 31
- 238000005219 brazing Methods 0.000 claims abstract description 247
- 239000011162 core material Substances 0.000 claims abstract description 158
- 238000005096 rolling process Methods 0.000 claims abstract description 131
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- 239000000956 alloy Substances 0.000 claims abstract description 23
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- 238000000034 method Methods 0.000 claims description 42
- 238000005097 cold rolling Methods 0.000 claims description 32
- 238000005253 cladding Methods 0.000 claims description 21
- 229910052748 manganese Inorganic materials 0.000 claims description 21
- 229910052719 titanium Inorganic materials 0.000 claims description 21
- 229910052720 vanadium Inorganic materials 0.000 claims description 21
- 229910052726 zirconium Inorganic materials 0.000 claims description 21
- 238000005266 casting Methods 0.000 claims description 19
- 229910052804 chromium Inorganic materials 0.000 claims description 19
- 238000005098 hot rolling Methods 0.000 claims description 17
- 239000012535 impurity Substances 0.000 claims description 16
- 229910052742 iron Inorganic materials 0.000 claims description 16
- 229910052802 copper Inorganic materials 0.000 claims description 12
- 229910052751 metal Inorganic materials 0.000 claims description 11
- 239000002184 metal Substances 0.000 claims description 11
- 229910052712 strontium Inorganic materials 0.000 claims description 9
- 239000000945 filler Substances 0.000 claims description 8
- 230000004907 flux Effects 0.000 claims description 3
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- 238000005260 corrosion Methods 0.000 abstract description 77
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- 238000011156 evaluation Methods 0.000 description 10
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- 230000008018 melting Effects 0.000 description 5
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- 229910052708 sodium Inorganic materials 0.000 description 4
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- 229910018191 Al—Fe—Si Inorganic materials 0.000 description 3
- 229910018580 Al—Zr Inorganic materials 0.000 description 3
- QQHSIRTYSFLSRM-UHFFFAOYSA-N alumanylidynechromium Chemical compound [Al].[Cr] QQHSIRTYSFLSRM-UHFFFAOYSA-N 0.000 description 3
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- 229910018131 Al-Mn Inorganic materials 0.000 description 2
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- 238000007796 conventional method Methods 0.000 description 2
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- 229910018084 Al-Fe Inorganic materials 0.000 description 1
- 229910018125 Al-Si Inorganic materials 0.000 description 1
- 229910018192 Al—Fe Inorganic materials 0.000 description 1
- 229910018473 Al—Mn—Si Inorganic materials 0.000 description 1
- 229910018507 Al—Ni Inorganic materials 0.000 description 1
- 229910018520 Al—Si Inorganic materials 0.000 description 1
- KRHYYFGTRYWZRS-UHFFFAOYSA-M Fluoride anion Chemical compound [F-] KRHYYFGTRYWZRS-UHFFFAOYSA-M 0.000 description 1
- 229910001030 Iron–nickel alloy Inorganic materials 0.000 description 1
- 239000003570 air Substances 0.000 description 1
- 238000007743 anodising Methods 0.000 description 1
- 239000007864 aqueous solution Substances 0.000 description 1
- FFBHFFJDDLITSX-UHFFFAOYSA-N benzyl N-[2-hydroxy-4-(3-oxomorpholin-4-yl)phenyl]carbamate Chemical compound OC1=C(NC(=O)OCC2=CC=CC=C2)C=CC(=C1)N1CCOCC1=O FFBHFFJDDLITSX-UHFFFAOYSA-N 0.000 description 1
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Images
Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21D53/00—Making other particular articles
- B21D53/02—Making other particular articles heat exchangers or parts thereof, e.g. radiators, condensers fins, headers
- B21D53/04—Making other particular articles heat exchangers or parts thereof, e.g. radiators, condensers fins, headers of sheet metal
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D7/00—Casting ingots, e.g. from ferrous metals
- B22D7/005—Casting ingots, e.g. from ferrous metals from non-ferrous metals
-
- 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
- B23K1/00—Soldering, e.g. brazing, or unsoldering
-
- 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
- B23K1/00—Soldering, e.g. brazing, or unsoldering
- B23K1/0008—Soldering, e.g. brazing, or unsoldering specially adapted for particular articles or work
- B23K1/0012—Brazing heat exchangers
-
- 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
- B23K1/00—Soldering, e.g. brazing, or unsoldering
- B23K1/19—Soldering, e.g. brazing, or unsoldering taking account of the properties of the materials to be soldered
-
- 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
- B23K20/04—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating by means of a rolling mill
-
- 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
- B23K31/00—Processes relevant to this subclass, specially adapted for particular articles or purposes, but not covered by only one of the preceding main groups
- B23K31/02—Processes relevant to this subclass, specially adapted for particular articles or purposes, but not covered by only one of the preceding main groups relating to soldering or 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
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/001—Interlayers, transition pieces for metallurgical bonding of workpieces
- B23K35/002—Interlayers, transition pieces for metallurgical bonding of workpieces at least one of the workpieces being of light metal
-
- 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
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/02—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape
- B23K35/0222—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape for use in soldering, brazing
- B23K35/0233—Sheets, foils
- B23K35/0238—Sheets, foils layered
-
- 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
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
-
- 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
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/28—Selection of soldering or welding materials proper with the principal constituent melting at less than 950 degrees C
-
- 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
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/28—Selection of soldering or welding materials proper with the principal constituent melting at less than 950 degrees C
- B23K35/286—Al as the principal constituent
-
- 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
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/28—Selection of soldering or welding materials proper with the principal constituent melting at less than 950 degrees C
- B23K35/286—Al as the principal constituent
- B23K35/288—Al as the principal constituent with Sn or Zn
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
- B32B15/016—Layered products comprising a layer of metal all layers being exclusively metallic all layers being formed of aluminium or aluminium alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/10—Alloys based on aluminium with zinc as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/14—Alloys based on aluminium with copper as the next major constituent with silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/053—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with zinc as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/057—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with copper as the next major constituent
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F28—HEAT EXCHANGE IN GENERAL
- F28F—DETAILS OF HEAT-EXCHANGE AND HEAT-TRANSFER APPARATUS, OF GENERAL APPLICATION
- F28F21/00—Constructions of heat-exchange apparatus characterised by the selection of particular materials
- F28F21/08—Constructions of heat-exchange apparatus characterised by the selection of particular materials of metal
- F28F21/081—Heat exchange elements made from metals or metal alloys
- F28F21/084—Heat exchange elements made from metals or metal alloys from aluminium or aluminium alloys
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F28—HEAT EXCHANGE IN GENERAL
- F28F—DETAILS OF HEAT-EXCHANGE AND HEAT-TRANSFER APPARATUS, OF GENERAL APPLICATION
- F28F21/00—Constructions of heat-exchange apparatus characterised by the selection of particular materials
- F28F21/08—Constructions of heat-exchange apparatus characterised by the selection of particular materials of metal
- F28F21/089—Coatings, claddings or bonding layers made from metals or metal alloys
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
-
- 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
- B23K2101/00—Articles made by soldering, welding or cutting
- B23K2101/04—Tubular or hollow articles
- B23K2101/14—Heat exchangers
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2251/00—Treating composite or clad material
Definitions
- the present invention relates to a highly corrosion-resistant and highly formable aluminum alloy clad material and a method for producing the same, and more particularly, to a highly corrosion-resistant material suitably used as a refrigerant or high-temperature compressed air passage component in a heat exchanger such as a radiator.
- the present invention relates to a highly formable aluminum alloy clad material and a method for producing the same.
- the present invention relates to a heat exchanger using the highly corrosion-resistant and highly formable aluminum alloy clad material, and more particularly to a flow path forming component such as a heat exchanger for automobiles and a manufacturing method thereof.
- Aluminum alloys are lightweight and have high thermal conductivity, and can be realized with high corrosion resistance by appropriate processing. Therefore, they are used in automotive heat exchangers such as radiators, condensers, evaporators, heaters, and intercoolers.
- As a tube material for automotive heat exchangers an Al—Mn-based aluminum alloy such as 3003 alloy is used as a core material.
- a two-layer clad material obtained by cladding a material, or a three-layer clad material obtained by further cladding an Al—Si based aluminum alloy brazing material on the other surface of the core material is used.
- the heat exchanger is usually manufactured by combining such a clad tube material and a corrugated fin material and brazing at a high temperature of about 600 ° C.
- the tube shape is becoming more complex in order to achieve higher performance. Therefore, the material is required to have higher formability.
- the formability of the tube material has been adjusted by performing H14 tempering in which intermediate annealing is performed in the middle of cold rolling, or H24 tempering in which finishing annealing is performed after cold rolling.
- H14 tempering in which intermediate annealing is performed in the middle of cold rolling
- H24 tempering in which finishing annealing is performed after cold rolling.
- Patent Documents 1 and 2 disclose techniques for improving the formability of a clad material or electroweld weldability. However, these patent documents do not describe means for improving the corrosion resistance of the sacrificial anode material.
- Patent Document 3 discloses a technique for improving the corrosion resistance of the clad material. However, these patent documents do not describe means for improving the moldability of the clad material.
- the clad material described in Patent Document 1 improves the electroweldability of the material by setting the average crystal grain size in a cross section perpendicular to the longitudinal direction of the core material to 30 ⁇ m or less.
- the area ratio of Mg 2 Si having a particle size of 0.2 ⁇ m or more is specified to be 0.5% or less, which is also a means for improving the electro-weldability.
- the corrosion resistance of the sacrificial anode material only the addition amount of Zn or Mg is defined, and there is no description or suggestion about a technique for improving the corrosion resistance more than the conventional technique.
- the clad material described in Patent Document 2 improves the electroweldability of the material by making the core material into a fibrous structure.
- the hardness of the core material and the sacrificial anode material is specified to be 50 Hv or more, and the hardness ratio (sacrificial anode material / core material) is less than 1.0. It is a means for ensuring the fatigue strength.
- the corrosion resistance of the sacrificial anode material only the addition amount of Zn or Mn is defined here, and there is no description or suggestion about a technique for improving the corrosion resistance more than the conventional technique.
- the corrosion resistance in an alkaline environment is improved by setting the crystal grain size of the sacrificial anode material to 100 to 700 ⁇ m.
- the components are defined for the core material, and its structure and mechanical properties are not described, and there is no description or suggestion about improvement of moldability.
- the present invention has been completed to solve the above problems, and has an excellent formability when an aluminum alloy clad material is used as, for example, a tube material of a heat exchanger.
- An object of the present invention is to provide an aluminum alloy clad material having excellent corrosion resistance and a method for producing the same, a heat exchanger using the same, and a method for producing the same.
- Such an aluminum alloy clad material having high corrosion resistance and high formability can be suitably used as a flow path forming component of an automotive heat exchanger.
- an aluminum alloy core material, an intermediate layer material clad on one surface of the core material, and a surface of the intermediate material material that is not on the core material side would be clad.
- the core material contains Si: 0.05-1.50 mass%, Fe: 0.05-2.00 mass%, Mn: 0.5-2.0 mass%, It consists of an aluminum alloy composed of the balance Al and inevitable impurities, and the intermediate layer material is Zn: 0.5 to 8.0 mass%, Si: 0.05 to 1.50 mass%, Fe: 0.05 to 2.00 mass.
- the brazing filler metal is made of an aluminum alloy composed of the remaining Al and inevitable impurities, and the brazing filler metal is Si: 2.5 to 13.0 mass%, Fe: 0.05 to 1.20 m. It consists of an aluminum alloy containing ss%, the balance Al and inevitable impurities, the crystal grain size of the intermediate layer material before brazing addition heat is 60 ⁇ m or more, and along the rolling direction of the core material before brazing addition heat An aluminum alloy cladding characterized in that R1 / R2 is 0.30 or less when the crystal grain size in the plate thickness direction is R1 ( ⁇ m) and the crystal grain size in the rolling direction is R2 ( ⁇ m) A material was used.
- the core material comprises Mg: 0.05 to 0.50 mass%, Cu: 0.05 to 1.50 mass%, Ti: 0.05 to 0.30 mass%, Zr. : Aluminum alloy further containing one or more selected from 0.05 to 0.30 mass%, Cr: 0.05 to 0.30 mass%, and V: 0.05 to 0.30 mass% It was.
- the intermediate layer material comprises Ni: 0.05 to 2.00 mass%, Mn: 0.05 to 2.00 mass%, Ti: 0.05 to 0.00.
- the brazing material according to any one of the first to third aspects of the present invention includes: Zn: 0.5-8.0 mass%, Cu: 0.05-1.50 mass%, Mn: 0.00. 05 to 2.00 mass%, Ti: 0.05 to 0.30 mass%, Zr: 0.05 to 0.30 mass%, Cr: 0.05 to 0.30 mass%, and V: 0.05 to 0.30 mass% It was made of an aluminum alloy further containing one or more selected from
- the brazing material is selected from Na: 0.001 to 0.050 mass% and Sr: 0.001 to 0.050 mass% in any one of the first to fourth aspects. It was made of an aluminum alloy further containing seeds or two kinds.
- the present invention provides the method for producing an aluminum alloy clad material according to any one of claims 1 to 5, wherein the aluminum alloys for the core material, the intermediate layer material, and the brazing material are respectively casted.
- a hot rolling process in which the cast intermediate layer material ingot and the brazing material ingot are each hot-rolled to a predetermined thickness, and an intermediate layer material having a predetermined thickness is clad on one surface of the core material ingot.
- a rolling start temperature is 400 to 520 ° C.
- a rolling pass in which the rolling reduction in one pass is 30% or more while the temperature of the clad material is 200 to 400 ° C. is limited to 5 times or less.
- the clad material is maintained at 200 to 560 ° C. for 1 to 10 hours.
- an aluminum alloy core material in claim 7, an aluminum alloy core material, an intermediate layer material clad on one surface of the core material, and a brazing material clad on a surface of the intermediate material that is not on the core material side;
- the core material contains Si: 0.05 to 1.50 mass%, Fe: 0.05 to 2.00 mass%, Mn: 0 .5 to 2.0 mass%, and is made of an aluminum alloy composed of the balance Al and inevitable impurities.
- the intermediate layer material is made of Zn: 0.5 to 8.0 mass%, Si: 0.05 to 1.50 mass.
- the brazing material and the brazing material clad on the other surface of the core material contain Si: 2.5 to 13.0 mass%, Fe: 0.05 to 1.20 mass%, and the balance is Al and inevitable impurities. It is made of an aluminum alloy, and the intermediate layer material has a crystal grain size of 60 ⁇ m or more before the brazing addition heat.
- the crystal grain size in the plate thickness direction is R1 ( ⁇ m), when the crystal grain size in the rolling direction is R2 ( ⁇ m), R1 / R2 is 0.30 or less.
- the present invention provides an eighth aspect according to the seventh aspect, wherein the core material comprises Mg: 0.05 to 0.50 mass%, Cu: 0.05 to 1.50 mass%, Ti: 0.05 to 0.30 mass%, Zr. : Aluminum alloy further containing one or more selected from 0.05 to 0.30 mass%, Cr: 0.05 to 0.30 mass%, and V: 0.05 to 0.30 mass% It was.
- the intermediate layer material comprises Ni: 0.05-2.00 mass%, Mn: 0.05-2.00 mass%, Ti: 0.05-0.
- the brazing material clad on the surface of the intermediate layer material not on the core material side and the brazing material clad on the other surface of the core material are Zn: 0.5-8.0 mass%, Cu: 0.05-1.50 mass%, Mn: 0.05-2.00 mass%, Ti: 0.05-0.30 mass%, Zr: 0.05-0.
- the brazing material clad on a surface of the intermediate layer material that is not on the core material side and the brazing material clad on the other surface of the core material are Na: It was made of an aluminum alloy further containing one or two selected from 0.001 to 0.050 mass% and Sr: 0.001 to 0.050 mass%.
- the present invention provides the method for producing an aluminum alloy clad material according to any one of claims 7 to 11 according to claim 12, wherein the core material, the intermediate layer material, and the intermediate layer material are not on the core material side.
- the step of casting an aluminum alloy of the brazing material for the brazing material and the brazing material clad on the other side of the core material, and the clad on the surface of the cast intermediate layer material ingot and the intermediate layer material not on the core material side A hot rolling step of hot rolling the brazing material ingot clad on the other surface of the brazing material ingot and the core material to a predetermined thickness, and an intermediate layer material having a predetermined thickness on one surface of the core material ingot
- the hot pressure A hot-clad rolling process,
- the present invention is the heat exchanger using the aluminum alloy clad material according to any one of claims 1 to 5 and 7 to 11 according to claim 13, wherein the crystal of the intermediate layer material after brazing heat is applied.
- a heat exchanger having a particle size of 100 ⁇ m or more was obtained.
- the present invention is the method of manufacturing a heat exchanger according to claim 14, wherein the aluminum alloy material is brazed using a flux in an inert gas atmosphere. It was set as the manufacturing method.
- the aluminum alloy clad material according to the present invention when used, for example, as a tube material for a heat exchanger, it can be molded well even if the tube shape is complicated, and after the additional heat is added, it is superior to the intermediate layer material. Corrosion resistance.
- a heat exchanger for automobiles or the like By using such an aluminum alloy clad material for a flow path forming component or the like, a heat exchanger for automobiles or the like is provided.
- This clad material is excellent in brazing properties such as erosion resistance, and is suitably used as a heat exchanger tube material for automobiles from the viewpoint of light weight and good thermal conductivity.
- the aluminum alloy clad material according to the present invention has excellent formability by appropriately controlling the components and metal structure of the core material, and is clad on one surface of the core material. It has excellent corrosion resistance by appropriately controlling the components and metal structure of the intermediate layer material.
- the clad on the other surface of the core material is not particularly limited.
- the brazing material is also clad on the other surface of the core material as the aluminum alloy clad material according to the second embodiment of the present invention.
- first brazing material the brazing material clad on the surface of the intermediate layer material that is not on the core material side
- second brazing material The components of the brazing material clad on the surface
- Core material The core materials of the first and second forms include: Si: 0.05 to 1.50 mass% (hereinafter simply referred to as “%”), Fe: 0.05 to 2.00%, Mn: 0.5 An aluminum alloy containing ⁇ 2.0% as an essential element and the balance Al and inevitable impurities is used.
- the core material of both forms includes Mg: 0.05 to 0.50%, Cu: 0.05 to 1.50%, Ti: 0.05 to 0.30%, Zr : 0.05 to 0.30%, Cr: 0.05 to 0.30%, and V: 0.05 to 0.30%, further containing one or more selected elements as a selective additive element May be.
- Both forms of core material may further contain inevitable impurities in addition to the essential elements and selective additive elements, each 0.05% or less and 0.15% or less in total.
- a JIS 3000 series alloy for example, an Al—Mn series alloy such as JIS 3003 alloy is preferably used.
- JIS 3000 series alloy for example, an Al—Mn series alloy such as JIS 3003 alloy is preferably used.
- each component will be described in detail. These components are common to the first and second embodiments.
- Si forms an Al-Fe-Mn-Si intermetallic compound together with Fe and Mn, and improves the strength of the core material by dispersion strengthening, or dissolves in the aluminum matrix and dissolves the core material by solid solution strengthening. Improve strength.
- the Si content is 0.05 to 1.50%. If it is less than 0.05%, high-purity aluminum ingots must be used, resulting in high costs. On the other hand, if it exceeds 1.50%, the melting point of the core material is lowered, and the risk of melting the core material during brazing increases.
- the Si content is preferably 0.10 to 1.20%.
- Fe forms an Al—Fe—Mn—Si intermetallic compound together with Si and Mn, and improves the strength of the core material by dispersion strengthening.
- the amount of Fe added is 0.05 to 2.00%. If the content is less than 0.05%, high-purity aluminum ingots must be used, resulting in high costs. On the other hand, if it exceeds 2.00%, a giant intermetallic compound is easily formed during casting, and the plastic workability is lowered.
- the Fe content is preferably 0.10 to 1.50%.
- Mn forms an Al-Mn-Si-based or Al-Fe-Mn-Si-based intermetallic compound together with Si, improves the strength of the core material by dispersion strengthening, or forms a solid solution by dissolving in the aluminum matrix.
- the strength of the heartwood is improved by melt strengthening.
- the Mn content is 0.5 to 2.0%. If the content is less than 0.5%, the above effect is insufficient. If the content exceeds 2.0%, a giant intermetallic compound is easily formed during casting, and the plastic workability is lowered.
- the Mn content is preferably 0.8 to 1.8%.
- Mg may be contained because it improves the strength of the core material by precipitation of Mg 2 Si.
- the Mg content is 0.05 to 0.50%. If it is less than 0.05%, the above effect is insufficient, and if it exceeds 0.50%, brazing becomes difficult.
- the Mg content is preferably 0.10 to 0.40%.
- Cu may be contained because it improves the strength of the core material by solid solution strengthening.
- the Cu content is 0.05 to 1.50%. If it is less than 0.05%, the above effect is insufficient, and if it exceeds 1.50%, there is a high risk of cracking of the aluminum alloy during casting.
- the Cu content is preferably 0.30 to 1.00%.
- Ti may be contained because it improves the strength of the core material by solid solution strengthening.
- the Ti content is 0.05 to 0.30%. If it is less than 0.05%, the above effect is insufficient. If it exceeds 0.30%, it becomes easy to form a giant intermetallic compound, and the plastic workability is lowered.
- the Ti content is preferably 0.10 to 0.20%.
- Zr may be contained because it improves the strength of the core material by solid solution strengthening and precipitates an Al—Zr-based intermetallic compound to coarsen the crystal grains after the brazing heat.
- the Zr content is 0.05 to 0.30%. If it is less than 0.05%, the above effect cannot be obtained. On the other hand, when it exceeds 0.30%, it becomes easy to form a huge intermetallic compound, and plastic workability is lowered.
- the Zr content is preferably 0.10 to 0.20%.
- Cr Cr may be contained because it has the effect of improving the strength of the core material by solid solution strengthening and precipitating Al—Cr-based intermetallic compounds to coarsen the crystal grains after brazing addition heat.
- the Cr content is 0.05 to 0.30%. If it is less than 0.05%, the above effect cannot be obtained. On the other hand, when it exceeds 0.30%, it becomes easy to form a huge intermetallic compound, and plastic workability is lowered.
- the Cr content is preferably 0.10 to 0.20%.
- V improves the strength of the core material by solid solution strengthening and also improves the corrosion resistance.
- the V content is 0.05 to 0.30%. If it is less than 0.05%, the above effect cannot be obtained. On the other hand, when it exceeds 0.30%, it becomes easy to form a huge intermetallic compound, and plastic workability is lowered.
- the V content is preferably 0.10 to 0.20%.
- Mg, Cu, Ti, Zr, Cr, and V may be contained in the core material as required, if necessary.
- the intermediate layer materials of the first and second embodiments include Zn: 0.5 to 8.0%, Si: 0.05 to 1.50%, Fe: 0.05 to 2.00%.
- An aluminum alloy which is contained as an essential element and which consists of the balance Al and inevitable impurities is used.
- the intermediate layer material in both forms is Ni: 0.05 to 2.00%, Mn: 0.05 to 2.00%, Ti: 0.05 to 0.30%, Zr : 0.05 to 0.30%, Cr: 0.05 to 0.30%, and V: 0.05 to 0.30%, further containing one or more selected elements as a selective additive element May be.
- unavoidable impurities may be further contained in amounts of 0.05% or less, respectively, and 0.15% or less in total.
- Zn can lower the pitting corrosion potential, and can improve the corrosion resistance due to the sacrificial anticorrosion effect by forming a potential difference with the core material.
- the Zn content is 0.5 to 8.0%. If it is less than 0.5%, the effect of improving the corrosion resistance due to the sacrificial anticorrosive effect cannot be sufficiently obtained. On the other hand, if it exceeds 8.0%, the corrosion rate increases, the intermediate layer material disappears early, and the corrosion resistance decreases.
- the Zn content is preferably 1.0 to 6.0%.
- Si forms an Al—Fe—Si based intermetallic compound with Fe, and when it contains Mn at the same time, forms an Al—Fe—Mn—Si based intermetallic compound with Fe and Mn,
- the strength of the intermediate layer material is improved by dispersion strengthening, or the strength of the intermediate layer material is improved by solid solution strengthening in the aluminum matrix.
- Si makes the potential of the intermediate layer material noble, the sacrificial anticorrosive effect is hindered and the corrosion resistance is lowered.
- the Si content is 0.05 to 1.50%. If the content is less than 0.05%, high-purity aluminum ingots must be used, resulting in high costs. On the other hand, if it exceeds 1.50%, the pitting corrosion potential of the intermediate layer material becomes noble and the sacrificial anticorrosive effect is lost, and the corrosion resistance is lowered.
- the Si content is preferably 0.10 to 1.20%.
- Fe forms an Al—Fe—Si intermetallic compound together with Si, and if it contains Mn simultaneously, forms an Al—Fe—Mn—Si intermetallic compound together with Si and Mn,
- the strength of the intermediate layer material is improved by dispersion strengthening.
- the amount of Fe added is 0.05 to 2.00%. If the content is less than 0.05%, high-purity aluminum ingots must be used, resulting in high costs. On the other hand, if it exceeds 2.00%, a giant intermetallic compound is easily formed during casting, and the plastic workability is lowered.
- the Fe content is preferably 0.10 to 1.50%.
- Ni forms an Al-Ni-based or Al-Fe-Ni-based intermetallic compound together with Fe. Since these intermetallic compounds have a higher corrosion potential than aluminum matrix and are noble, they act as corrosion cathode sites. Therefore, if these intermetallic compounds are dispersed in the intermediate layer material, the starting point of corrosion is dispersed. As a result, corrosion in the depth direction is difficult to proceed, and the corrosion resistance is improved. Further, Ni has an effect of improving the strength of the intermediate layer material. Therefore, in order to improve corrosion resistance and strength, the Ni content is set to 0.05 to 2.00%. If it is less than 0.05%, the effect of improving the corrosion resistance and strength cannot be sufficiently obtained. On the other hand, if it exceeds 2.00%, a giant intermetallic compound is easily formed during casting, and the plastic workability is lowered. The Ni content is preferably 0.10 to 1.50%.
- Mn may be contained because it improves the strength and corrosion resistance of the intermediate layer material.
- the Mn content is 0.05 to 2.00%. If it exceeds 2.00%, a huge intermetallic compound is likely to be formed during casting, and the plastic workability is lowered. On the other hand, if it is less than 0.05%, the effect cannot be sufficiently obtained.
- the Mn content is preferably 0.05 to 1.80%.
- Ti improves the strength of the intermediate layer material by solid solution strengthening and also improves the corrosion resistance.
- the Ti content is 0.05 to 0.30%. If it is less than 0.05%, the above effect cannot be obtained. If it exceeds 0.30%, it becomes easy to form a giant intermetallic compound, and the plastic workability is lowered.
- the Ti content is preferably 0.05 to 0.20%.
- Zr may be contained because it has the effect of improving the strength of the intermediate layer material by solid solution strengthening and precipitating Al—Zr-based intermetallic compounds to coarsen the crystal grains after brazing addition heat.
- the Zr content is 0.05 to 0.30%. If it is less than 0.05%, the above effect cannot be obtained. On the other hand, when it exceeds 0.30%, it becomes easy to form a huge intermetallic compound, and plastic workability is lowered.
- the Zr content is preferably 0.10 to 0.20%.
- Cr Cr may be contained because it has the effect of improving the strength of the intermediate layer material by solid solution strengthening and precipitating Al—Cr-based intermetallic compounds to coarsen the crystal grains after brazing addition heat.
- the Cr content is 0.05 to 0.30%. If it is less than 0.05%, the above effect cannot be obtained. If it exceeds 0.30%, it becomes easy to form a giant intermetallic compound, and the plastic workability is lowered.
- the Cr content is preferably 0.10 to 0.20%.
- V may be contained because it improves the strength of the intermediate layer material by solid solution strengthening and also improves the corrosion resistance.
- the V content is 0.05 to 0.30%. If it is less than 0.05%, the above effect cannot be obtained. If it exceeds 0.30%, it becomes easy to form a giant intermetallic compound, and the plastic workability is lowered.
- the V content is preferably 0.05 to 0.20%.
- Ni, Mn, Ti, Zr, Cr, and V only need to be contained in the intermediate layer material if necessary.
- the first and second brazing materials in the first and second embodiments contain Si: 2.5 to 13.0%, Fe: 0.05 to 1.20% as essential elements, and the balance An aluminum alloy composed of Al and inevitable impurities is used.
- both types of brazing filler metals are Zn: 0.5 to 8.0%, Cu: 0.05 to 1.50%, Mn: 0.05 to 2.00%, Ti: One or two selected from 0.05 to 0.30%, Zr: 0.05 to 0.30%, Cr: 0.05 to 0.30% and V: 0.05 to 0.30% You may further contain the above as a 1st selective addition element.
- Na is selected from 0.001 to 0.050% and Sr: 0.001 to 0.050%. One or two of these may be further contained as a second selective additive element.
- Si By adding Si, the melting point of the brazing material is lowered to form a liquid phase, thereby enabling brazing.
- the Si content is 2.5 to 13.0%. If it is less than 2.5%, the resulting liquid phase is small and brazing becomes difficult to function. On the other hand, if it exceeds 13.0%, for example, when this brazing material is used as a tube material, the amount of Si diffusing into the mating material such as fins becomes excessive, and the mating material will melt.
- the Si content is preferably 3.5 to 12.0%.
- Fe Fe easily forms an Al—Fe-based or Al—Fe—Si-based intermetallic compound. Therefore, the amount of Si that is effective for brazing is reduced and brazing properties are lowered.
- the Fe content is 0.05 to 1.20%. If it is less than 0.05%, high-purity aluminum ingots must be used, resulting in high costs. On the other hand, if it exceeds 1.20%, the amount of Si effective for brazing is reduced and brazing becomes insufficient.
- the Fe content is preferably 0.10 to 0.50%.
- Zn can make the pitting corrosion potential base, and since it can improve the corrosion resistance due to the sacrificial anticorrosion effect by forming a potential difference with the core material, Zn may be contained.
- the Zn content is 0.5 to 8.0%. If it is less than 0.5%, the effect of improving the corrosion resistance due to the sacrificial anticorrosive effect cannot be sufficiently obtained. On the other hand, if it exceeds 8.0%, the corrosion rate increases, the sacrificial anticorrosion layer disappears early, and the corrosion resistance decreases.
- the Zn content is preferably 1.0 to 6.0%.
- Cu Since Cu improves the strength of the brazing material by solid solution strengthening, Cu may be contained.
- the Cu content is 0.05 to 1.50%. If it is less than 0.05%, the above effect is insufficient, and if it exceeds 1.50%, there is a high risk of cracking of the aluminum alloy during casting.
- the Cu content is preferably 0.30 to 1.00%.
- the preferable content of Cu is 0.05 to 0.60%. Since Cu makes the pitting corrosion potential noble, if it exceeds 0.6%, the sacrificial anticorrosive effect by Zn may be lost.
- Mn may be contained because it improves the strength and corrosion resistance of the brazing material.
- the Mn content is 0.05 to 2.00%. If it exceeds 2.00%, a huge intermetallic compound is likely to be formed during casting, and the plastic workability is lowered. On the other hand, if it is less than 0.05%, the effect cannot be sufficiently obtained.
- the Mn content is preferably 0.05 to 1.80%.
- Ti may be contained because it improves the strength of the brazing filler metal by solid solution strengthening and also improves the corrosion resistance.
- the Ti content is 0.05 to 0.30%. If it is less than 0.05%, the above effect cannot be obtained. If it exceeds 0.30%, it becomes easy to form a giant intermetallic compound, and the plastic workability is lowered.
- the Ti content is preferably 0.10 to 0.20%.
- Zr may be contained because it has the effect of improving the strength of the brazing filler metal by solid solution strengthening and precipitating Al—Zr-based intermetallic compounds to coarsen the crystal grains after brazing addition heat.
- the Zr content is 0.05 to 0.30%. If it is less than 0.05%, the above effect cannot be obtained. If it exceeds 0.30%, it becomes easy to form a giant intermetallic compound, and the plastic workability is lowered.
- the Zr content is preferably 0.10 to 0.20%.
- Cr Cr may be contained because it has the effect of improving the strength of the brazing material by solid solution strengthening and precipitating Al—Cr-based intermetallic compounds to coarsen the crystal grains after the brazing heat.
- the Cr content is 0.05 to 0.30%. If it is less than 0.05%, the above effect cannot be obtained. If it exceeds 0.30%, it becomes easy to form a giant intermetallic compound, and the plastic workability is lowered.
- the Cr content is preferably 0.10 to 0.20%.
- V may be contained because it improves the strength of the brazing filler metal by solid solution strengthening and also improves the corrosion resistance.
- the V content is 0.05 to 0.30%. If it is less than 0.05%, the above effect cannot be obtained. If it exceeds 0.30%, it becomes easy to form a giant intermetallic compound, and the plastic workability is lowered.
- the V content is preferably 0.10 to 0.20%.
- Na, Sr Na and Sr exhibit the effect of refining the Si particles in the brazing material.
- the contents of Na and Sr are 0.001 to 0.050%, respectively. If the respective contents are less than 0.001%, the above effects cannot be obtained sufficiently. On the other hand, when each content exceeds 0.050%, an oxide film becomes thick and brazeability is reduced. Each preferable content is 0.003 to 0.020%.
- These Zn, Cu, Mn, Ti, Zr, Cr, V, Na, and Sr may be contained in the brazing material if necessary.
- Crystal grain size of the intermediate layer material In the aluminum alloy clad material of the present invention, the crystal grain size of the intermediate layer material before brazing heat is regulated to 60 ⁇ m or more, and the crystal grain size of the intermediate layer material after brazing heat is regulated to 100 ⁇ m or more. . This is intended to improve the corrosion resistance of the intermediate layer material after the brazing heat.
- the crystal grain size here refers to an arithmetic average value of diameters corresponding to circle diameters of the intermediate layer material observed from the rolling surface and a region surrounded by grain boundaries as crystal grains. Shall.
- the grain boundary refers to a boundary where the adjacent crystal orientation difference is 20 degrees or more.
- the method for measuring the crystal grain size is not particularly limited, but is generally based on electron beam backscatter diffraction (EBSD). The reason for this limitation will be described below.
- the intermediate layer material is clad for the purpose of sacrificial corrosion prevention by preferentially corroding the intermediate layer material so that the corrosion progresses in a planar shape and prevents perforation corrosion of the tube.
- the corrosion rate of the intermediate layer material is high, the intermediate layer material disappears early and loses the effect of sacrificial protection, and the tube is corroded.
- the inventors have found that the corrosion rate of the crystal grain boundary in the intermediate layer material is faster than that in the crystal grain, and the corrosion rate can be suppressed by reducing the area of the crystal grain boundary. Reducing the area of the crystal grain boundary is synonymous with increasing the crystal grain size. Further detailed examination revealed that, after brazing heat, if the crystal grain size of the intermediate layer material is 100 ⁇ m or more, the corrosion rate of the intermediate layer material is suppressed, and the aluminum alloy clad material has excellent corrosion resistance. .
- the crystal grain size of the intermediate layer material after the brazing heat is preferably 120 ⁇ m or more.
- the upper limit of the crystal grain size of the intermediate layer material after the brazing heat is not particularly limited, but it is difficult to set it to 1000 ⁇ m or more.
- the inventors have found that there is a positive correlation between the crystal grain size of the intermediate layer material before the brazing heat and the crystal grain size of the intermediate layer material after the brazing heat. It was. That is, in order to obtain a large crystal grain size of the intermediate layer material after the brazing heat, it is necessary that the crystal grain size of the intermediate layer material before the brazing heat is large. As a result of examining this point in detail, it has been found that when the crystal grain size of the intermediate layer material before the brazing heat is 60 ⁇ m or more, the crystal grain size of the intermediate layer material after the brazing heat is 100 ⁇ m or more. .
- the crystal grain size of the intermediate layer material before brazing heat is less than 60 ⁇ m
- the crystal grain size of the intermediate layer material after brazing heat is less than 100 ⁇ m.
- the crystal grain size of the intermediate layer material before brazing addition heat is preferably 80 ⁇ m or more.
- the upper limit value of the crystal grain size of the intermediate layer material before the brazing heat is not particularly limited, but it is difficult to set it to 1000 ⁇ m or more.
- Crystal grain size of core material in the aluminum alloy clad material of the present invention is R1 ( ⁇ m) in the cross section along the rolling direction of the core material before brazing addition heat, and the crystal grain size in the rolling direction is When R2 ( ⁇ m) is set, R1 / R2 is defined to be 0.30 or less. This is an index for improving the moldability of the clad material before brazing heat.
- the crystal grain sizes R1 and R2 ( ⁇ m) here are obtained by observing a cross section along the rolling direction of the cladding material and using the region surrounded by the grain boundaries as crystal grains.
- the maximum diameter in the plate thickness direction was defined as R1, and the maximum diameter in the rolling direction was defined as R2.
- the grain boundary refers to a boundary where the adjacent crystal orientation difference is 20 degrees or more.
- the method for measuring the crystal grain size is not particularly limited, but is generally based on electron beam backscatter diffraction (EBSD).
- EBSD electron beam backscatter diffraction
- the formability of the aluminum alloy has been improved by adjusting the mechanical properties according to the tempering determined by the conditions of the intermediate annealing and the subsequent rolling rate.
- the material is cracked.
- the present inventors have found that the more excellent the formability is obtained when the crystal grains of the core material before brazing heat are flat in the rolling direction in the cross section along the rolling direction.
- it was set as the parameter
- index which shows the flatness of a crystal grain by said R1 / R2.
- index which shows the flatness of a crystal grain by said R1 / R2.
- Detailed investigations by the present inventors have revealed that when R1 / R2 is 0.30 or less, the crystal grains of the core material are sufficiently flat and have excellent formability.
- R1 / R2 exceeds 0.30, the flatness of crystal grains of the core material is insufficient, and excellent workability cannot be obtained.
- R1 / R2 is preferably 0.20 or less.
- the manufacturing method of the aluminum alloy clad material according to the first aspect of the present invention includes a step of casting aluminum alloys for the core material, the intermediate layer material, and the first brazing material, and the cast intermediate layer material.
- a clad step of clad the first brazing material with the thickness of the clad material, a hot clad rolling step of hot rolling the clad material, and a cold rolling step of cold rolling the hot clad rolled clad material And one or more annealing steps of annealing the clad material in one or both of the middle of the cold rolling process and after the cold rolling process.
- the manufacturing method of the aluminum alloy clad material according to the second aspect of the present invention includes a step of casting aluminum alloys for the core material, the intermediate layer material, the first brazing material and the second brazing material, respectively, A hot rolling step of hot rolling each of the layer material ingot, the first brazing material ingot and the second brazing material ingot to a predetermined thickness, and an intermediate layer material having a predetermined thickness on one surface of the core material ingot And clad a first brazing material having a predetermined thickness on a surface of the intermediate layer material that is not on the core material side, and a second brazing material having a predetermined thickness on the other surface of the core material ingot.
- a clad process for forming a clad material a hot clad roll process for hot rolling the clad material, a cold roll process for cold rolling the clad material that has been hot clad rolled, and during the cold rolling process and cold rolling One or both of the steps after the process And a one or more annealing step of annealing the wood.
- the heating condition in the casting process of the core material, the first and second brazing materials, and the intermediate layer material are not particularly limited, but are usually performed by water-cooled semi-continuous casting. Further, in the step of hot rolling the core material, the intermediate layer material, and the first and second brazing materials to a predetermined thickness, the heating condition is to be performed at a temperature of 400 to 560 ° C. for 1 to 10 hours. preferable. If it is less than 400 ° C., cracking or the like may occur during rolling because of poor plastic workability. When the temperature is higher than 560 ° C., the ingot may be melted during heating. If the heating time is less than 1 hour, the temperature of the ingot is non-uniform and the plastic workability is poor, and cracking or the like may occur during rolling. If it exceeds 10 hours, the productivity is significantly impaired.
- the rolling start temperature is 400 to 520 ° C.
- the temperature of the clad material is 200 to 400.
- the rolling pass in which the reduction rate in one pass is 30% or more while the temperature is C is limited to 5 times or less.
- the hot clad rolling process may be divided into a rough rolling process and a finish rolling process.
- a reverse type or tandem type rolling mill is used in the finish rolling process. In a reverse rolling mill, one-way rolling is defined as one pass, and in a tandem rolling mill, rolling with one set of rolling rolls is defined as one pass.
- the aluminum alloy clad material of the present invention needs to increase the crystal grain size of the intermediate layer material before the brazing heat is applied.
- the crystal grains of the intermediate layer material are formed in the annealing process during manufacturing. The greater the strain accumulated in the intermediate layer material before annealing, the greater the driving force of grain growth that occurs during annealing, resulting in larger crystals. Grains can be obtained.
- the aluminum alloy clad material of the present invention needs to make the crystal grains of the core material flat before the brazing heat is applied.
- the core crystal grains are also formed in the annealing process during manufacturing. The smaller the strain accumulated in the core before annealing, the smaller the driving force for grain growth in the thickness direction that occurs during annealing. As a result, flat crystal grains can be obtained.
- the core material in the hot clad rolling process dynamic recovery occurs during hot clad rolling, so even if a rolling pass with a rolling reduction of 30% or more is applied, the core material Since the shear strain that enters does not increase, the flatness of the core crystal grains is not affected.
- the temperature of the clad material in the hot clad rolling process is less than 200 ° C., cracks occur during hot rolling, and the clad material cannot be manufactured.
- the rolling reduction rate in one pass is less than 30%, the shear strain entering the core material does not increase, so the flatness of the core material crystal grains is not affected.
- the rolling pass where the rolling reduction is 30% or more when the temperature of the clad material is 200 to 400 ° C. is preferably 4 passes or less. Note that the rolling reduction is preferably 35% or more. Further, if a rolling pass exceeding 50% is applied, the material may be cracked.
- the intermediate layer in the vicinity of the surface layer of the clad material even if the rolling pass in which the reduction rate is 30% or more is limited to 5 times or less while the temperature of the clad material is 200 to 400 ° C. in the hot clad rolling process
- a large shear strain enters the material. Therefore, sufficient grain growth occurs in the intermediate layer material in the intermediate annealing, and large crystal grains can be obtained in the intermediate layer material. That is, the above control in hot clad rolling makes it possible to make the crystal grain size of the intermediate layer material coarse and make the crystal grains of the core material flat.
- the crystal grain size of the intermediate layer material before brazing heat is controlled by adjusting the rolling start temperature in the hot clad rolling process. If the starting temperature of hot clad rolling is 520 ° C. or less, a large shear strain enters the intermediate layer material during hot clad rolling, and the crystal grain size of the intermediate layer material before brazing heat can be increased. When the starting temperature of hot clad rolling exceeds 520 ° C., dynamic recovery occurs in the intermediate layer material during hot clad rolling to reduce shear strain, and the crystal grain size of the intermediate layer material before the brazing heat is increased. Can not do it.
- the starting temperature of hot clad rolling is 400 to 520 ° C.
- the starting temperature of hot clad rolling is preferably 420 to 500 ° C.
- the hot clad rolling process there is no particular lower limit for the number of passes with a rolling reduction of 30% or more while the temperature of the clad material is 200 to 400 ° C.
- productivity is impaired because many passes with a rolling reduction of less than 30% are required to obtain a desired effect. Therefore, it is preferable to include one or more passes with a rolling reduction of 30% or more.
- the plate thickness after hot clad rolling is not particularly limited, but is usually preferably about 2.0 to 5.0 mm.
- an annealing step of annealing the clad material one or more times in one or both of the cold rolling step and after the cold rolling step Is provided. Specifically, (1) one or more intermediate annealings are performed during the cold rolling process, (2) the final annealing process is performed once after the cold rolling process, or (3) (1 ) And (2) are implemented. In this annealing step, the clad material is held at 200 to 560 ° C. for 1 to 10 hours.
- the annealing step is performed for the purpose of adjusting the strain in the material.
- the intermediate layer material can be recrystallized to obtain large crystal grains as described above.
- the cladding material temperature in the annealing process is less than 200 ° C. or when the holding time is less than 1 hour, recrystallization of the intermediate layer material is not completed.
- the annealing temperature exceeds 560 ° C, the brazing material may be melted. Even if the holding time exceeds 10 hours, there is no problem in the performance of the clad material, but the productivity is significantly impaired.
- the upper limit of the number of annealing steps is not particularly limited, but is preferably 3 times or less in order to avoid an increase in cost due to an increase in the number of steps.
- the ingot obtained by casting the aluminum alloy core material may be subjected to a homogenization treatment step before the cladding step.
- a homogenization treatment step it is usually preferable to hold the ingot at 450 to 620 ° C. for 1 to 20 hours. If the temperature is less than 450 ° C. or if the holding time is less than 1 hour, the homogenizing effect may not be sufficient, and if it exceeds 620 ° C., the core material ingot may be melted. Moreover, even if holding time exceeds 20 hours, the homogenization effect is saturated and it is not economical.
- the clad rate (one side) of the intermediate layer material is preferably 3 to 25%. As described above, a large shear strain needs to be applied only to the intermediate layer material in the hot clad rolling process during the manufacturing process. However, if the cladding ratio of the intermediate layer material exceeds 25%, sufficient shear strain is not applied to the entire intermediate layer material, and the entire intermediate layer material may not be able to have a recrystallized structure. On the other hand, if the cladding rate of the intermediate layer material is less than 3%, the intermediate layer material may be too thin to cover the entire core material during hot cladding rolling.
- the clad rate of the intermediate layer material is more preferably 5 to 20%.
- the clad rate of the first and second brazing materials is not particularly limited, but is usually clad at about 3 to 30%.
- the aluminum alloy clad material is suitably used as a heat exchanger member such as a tube material or a header plate, particularly as a tube material.
- a heat exchanger member such as a tube material or a header plate, particularly as a tube material.
- the aluminum alloy clad material is bent, and the overlapping portions at both ends thereof are brazed and joined to produce a tube material for flowing a medium such as cooling water.
- the header plate provided with the hole joined to the both ends of a tube material is produced by processing the said aluminum alloy clad material.
- the heat exchanger according to the present invention has a structure in which, for example, the above-described tube material, fin material, and header plate are combined, and these are brazed at once.
- the crystal grain size of the intermediate layer material of the aluminum alloy clad material after the brazing heat is 100 ⁇ m or more. It is characterized by being. With this feature, as described above, it is possible to improve the corrosion resistance of the intermediate layer material after the brazing heat.
- the heat exchanger is assembled by arranging fin materials on the outer surface of the tube material with both end portions attached to the header plate. Subsequently, the both ends overlapping part of the tube material, the fin material and the tube material outer surface, the both ends of the tube material and the header plate are simultaneously joined by one brazing heating.
- a brazing method a nocolock brazing method, a vacuum brazing method, and a flux-free brazing method are used, but a nocolock brazing method is preferable.
- the brazing is usually performed by heating at a temperature of 590 to 610 ° C. for 2 to 10 minutes, preferably at a temperature of 590 to 610 ° C. for 2 to 6 minutes.
- the brazed one is usually cooled at a cooling rate of 20 to 500 ° C./min.
- a core alloy having the alloy composition shown in Table 1, an intermediate layer alloy having the alloy composition shown in Table 2, and a brazing alloy having the alloy composition shown in Table 3 were cast by DC casting, respectively, and both sides were faced. Finished.
- the thickness of the ingot after chamfering was 400 mm in all cases.
- the clad rate to be the target thickness is calculated by the final thickness, and after being subjected to a heating process at 520 ° C. for 3 hours so as to obtain the required thickness, a predetermined thickness is obtained. Hot rolled to thickness.
- Table 4 shows the conditions for homogenizing the core material.
- the intermediate layer material of Table 2 was combined with one side of the core material alloy, and the brazing material of Table 3 was combined with the surface of the intermediate layer material that was not on the core material side.
- the other side of the core was combined with the brazing material shown in Table 3.
- the brazing material clad on the surface of the intermediate layer other than the core material side is defined as the first brazing material
- the brazing material clad on the other surface of the core material is defined as the second brazing material.
- the cladding rates of the first and second brazing materials and the intermediate layer material were both 10%.
- Table 4 shows the temperature and time in the heating process, and the start temperature and end temperature in the hot clad rolling process. Further, in the hot clad rolling process, while the temperature of the clad material is 200 ° C. to 400 ° C., the rolling pass in which the reduction rate in one pass is 30% or more is applied once or more. Is shown in Table 4. In all of the examples of the present invention, since the start temperature is 400 ° C. or higher and the end temperature is 200 ° C.
- the temperature of the clad material is 200 ° C. to 400 ° C. It is.
- the clad material was cold rolled.
- batch-type intermediate annealing once or twice was performed in the middle of cold rolling, and then final cold rolling was performed to prepare a clad material sample having a final sheet thickness of 0.3 mm.
- batch annealing was performed once after the final cold rolling without intermediate annealing, and a clad material sample having a final thickness of 0.3 mm was produced.
- a fin material having a thickness of 0.07 mm, a tempered H14, and an alloy component of 3003 alloy with 1.0% Zn added thereto was corrugated to obtain a heat exchanger fin material.
- This fin material is placed on the first brazing material surface or the second brazing material surface of the above clad material sample, immersed in a 5% fluoride flux aqueous solution, and subjected to brazing addition heat at 600 ° C. for 3 minutes. Then, a mini-core sample was prepared by Noclock brazing.
- the fins were peeled off, and the fin joint ratio was determined from the number of contacts (number of peaks) between the fins and the brazing material and the ratio of the locations where the fillets were formed.
- the case where the fin joint ratio of this mini-core sample was 95% or more and the clad material sample and the fin were not melted was judged as acceptable (O).
- the crystal grain was arbitrarily measured at 10 locations in the same visual field, and the arithmetic average value thereof was defined as R1 / R2.
- the mirror-polished sample was anodized and observed with a polarizing microscope.
- R1 0 was set. .
- the other surface which is not one surface of the core material where the first brazing material is clad is not considered as an evaluation target. It was. Also, those with a brazing evaluation of “x” were excluded from the evaluation because an appropriate minicore sample could not be produced.
- Comparative Example 48 the starting temperature of the hot clad rolling process exceeded 520 ° C. Therefore, the crystal grain size of the intermediate layer material before brazing was less than 60 ⁇ m, the crystal grain size of the intermediate layer material after brazing was less than 100 ⁇ m, and the corrosion resistance of the first brazing material was rejected.
- the intermediate annealing temperature was less than 200 ° C. Therefore, the intermediate layer material before brazing had a fibrous structure, the crystal grain size of the intermediate layer material after brazing was less than 100 ⁇ m, and the corrosion resistance of the first brazing material was rejected.
- the time for intermediate annealing was less than 1 hour. Therefore, the intermediate layer material before brazing had a fibrous structure, the crystal grain size of the intermediate layer material after brazing was less than 100 ⁇ m, and the corrosion resistance of the first brazing material was rejected.
- the aluminum alloy clad material according to the present invention has high strength after brazing and is excellent in brazing and corrosion resistance such as fin joint ratio and erosion resistance, and is therefore particularly suitable as a flow path forming part of an automotive heat exchanger. Used for.
- R1 Crystal grain size in the plate thickness direction in the core cross section along the rolling direction
- R2 Crystal grain size in the rolling direction in the core cross section along the rolling direction
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Abstract
Description
本発明に係るアルミニウム合金クラッド材は、心材の成分及び金属組織を適切に制御することにより優れた成形性を有し、また、心材の一方の面にクラッドされた中間層材の成分及び金属組織を適切に制御することにより優れた耐食性を有する。本発明の第1の形態に係るアルミニウム合金クラッド材では、心材の他方の面へのクラッドについては、特に制限するものではない。例えば、チューブが溶接などの方法で製管され、なおかつフィンとのろう付を必要としないような場合は、本発明の第1の形態に係るアルミニウム合金クラッド材として、心材の他方の面には何もクラッドしなくても良い。これに対して、チューブ材同士や、チューブとフィンとのろう付を行う場合には、本発明の第2の形態に係るアルミニウム合金クラッド材として、心材の他方の面にもろう材がクラッドされる。
第1及び第2の形態の心材には、Si:0.05~1.50mass%(以下、単に「%」と記す)、Fe:0.05~2.00%、Mn:0.5~2.0%を必須元素として含有し、残部Al及び不可避的不純物からなるアルミニウム合金が用いられる。
Siは、Fe、Mnと共にAl-Fe―Mn-Si系の金属間化合物を形成し、分散強化により心材の強度を向上させ、或いは、アルミニウム母相中に固溶して固溶強化により心材の強度を向上させる。Si含有量は、0.05~1.50%である。0.05%未満では、高純度アルミニウム地金を使用しなければならずコスト高となる。一方、1.50%を超えると心材の融点が低下し、ろう付け時に心材が溶融する虞が高くなる。Si含有量は、好ましくは0.10~1.20%である。
Feは、Si、Mnと共にAl-Fe-Mn-Si系の金属間化合物を形成し、分散強化により心材の強度を向上させる。Feの添加量は、0.05~2.00%である。含有量が0.05%未満では、高純度アルミニウム地金を使用しなければならずコスト高となる。一方、2.00%を超えると鋳造時に巨大金属間化合物が形成され易くなり、塑性加工性を低下させる。Fe含有量は、好ましくは0.10~1.50%である。
Mnは、Siと共にAl-Mn-Si系またはAl-Fe-Mn-Si系の金属間化合物を形成し、分散強化により心材の強度を向上させ、或いは、アルミニウム母相中に固溶して固溶強化により心材の強度を向上させる。Mn含有量は、0.5~2.0%である。0.5%未満では上記効果が不十分となり、2.0%を超えると鋳造時に巨大金属間化合物が形成され易くなり、塑性加工性を低下させる。Mn含有量は、好ましくは0.8~1.8%である。
Mgは、Mg2Siの析出により心材の強度を向上させるので含有させてもよい。Mg含有量は、0.05~0.50%である。0.05%未満では上記効果が不十分となり、0.50%を超えるとろう付が困難となる。Mg含有量は、好ましくは0.10~0.40%である。
Cuは、固溶強化により心材の強度を向上させるので含有させてもよい。Cu含有量は、0.05~1.50%である。0.05%未満では上記効果が不十分となり、1.50%を超えると鋳造時におけるアルミニウム合金の割れ発生の虞が高くなる。Cu含有量は、好ましくは0.30~1.00%である。
Tiは、固溶強化により心材の強度を向上させるので含有させてもよい。Ti含有量は、0.05~0.30%である。0.05%未満では上記効果が不十分となる。0.30%を超えると巨大金属間化合物を形成し易くなり、塑性加工性を低下させる。Ti含有量は、好ましくは0.10~0.20%である。
Zrは、固溶強化により心材の強度を向上させると共に、Al-Zr系の金属間化合物を析出させてろう付加熱後の結晶粒を粗大化する作用を有するので含有させてもよい。Zr含有量は、0.05~0.30%である。0.05%未満では上記効果が得られない。一方、0.30%を超えると巨大金属間化合物を形成し易くなり、塑性加工性を低下させる。Zr含有量は、好ましくは0.10~0.20%である。
Crは、固溶強化により心材の強度を向上させると共に、Al-Cr系の金属間化合物を析出させてろう付加熱後の結晶粒を粗大化する作用を有するので含有させてもよい。Cr含有量は、0.05~0.30%である。0.05%未満では上記効果が得られない。一方、0.30%を超えると巨大金属間化合物を形成し易くなり、塑性加工性を低下させる。Cr含有量は、好ましくは0.10~0.20%である。
Vは、固溶強化により心材の強度を向上させると共に、耐食性も向上させるので含有させてもよい。V含有量は、0.05~0.30%である。0.05%未満では上記効果が得られない。一方、0.30%を超えると巨大金属間化合物を形成し易くなり、塑性加工性を低下させる。V含有量は、好ましくは0.10~0.20%である。
第1及び第2の形態の中間層材には、Zn:0.5~8.0%、Si:0.05~1.50%、Fe:0.05~2.00%を必須元素として含有し、残部Al及び不可避的不純物からなるアルミニウム合金が用いられる。
Znは孔食電位を卑にすることができ、心材との電位差を形成することで犠牲防食効果により耐食性を向上することができる。Znの含有量は0.5~8.0%である。0.5%未満では、犠牲防食効果による耐食性向上の効果が十分に得られない。一方、8.0%を超えると、腐食速度が速くなり早期に中間層材が消失して耐食性が低下する。Zn含有量は、好ましくは1.0~6.0%である。
Siは、Feと共にAl-Fe-Si系の金属間化合物を形成し、またMnを同時に含有している場合にはFe、Mnと共にAl-Fe-Mn-Si系の金属間化合物を形成し、分散強化により中間層材の強度を向上させ、或いは、アルミニウム母相中に固溶して固溶強化により中間層材の強度を向上させる。また、Siは中間層材の電位を貴にするため、犠牲防食効果を阻害して耐食性を低下させる。Siの含有量は、0.05~1.50%である。含有量が0.05%未満では、高純度アルミニウム地金を使用しなければならずコスト高となる。一方、1.50%を超えると中間層材の孔食電位が貴になって犠牲防食効果を失わせ、耐食性が低下する。Si含有量は、好ましくは0.10~1.20%である。
Feは、Siと共にAl-Fe-Si系の金属間化合物を形成し、またMnを同時に含有している場合にはSi、Mnと共にAl-Fe-Mn-Si系の金属間化合物を形成し、分散強化により中間層材の強度を向上させる。Feの添加量は、0.05~2.00%である。含有量が0.05%未満では、高純度アルミニウム地金を使用しなければならずコスト高となる。一方、2.00%を超えると鋳造時に巨大金属間化合物が形成され易くなり、塑性加工性を低下させる。Fe含有量は、好ましくは0.10~1.50%である。
Niは、Al-Ni系、或いは、Feと共にAl-Fe-Ni系の金属間化合物を形成する。これらの金属間化合物はアルミニウムのマトリックスより腐食電位が大きく貴であるため、腐食のカソードサイトとして作用する。そのため、これらの金属間化合物が中間層材に分散していると、腐食の起点が分散する。その結果、深さ方向への腐食が進行し難くなり、耐食性が向上するので含有させてもよい。更に、Niは中間層材の強度を向上させる効果も有する。そこで、耐食性や強度を向上させるために、Niの含有量は、0.05~2.00%とする。0.05%未満では上記耐食性や強度の向上効果が十分に得られない。一方、2.00%を超えると鋳造時に巨大金属間化合物が形成され易くなり、塑性加工性を低下させる。Ni含有量は、好ましくは0.10~1.50%である。
Mnは、中間層材の強度と耐食性を向上させるので含有させてもよい。Mnの含有量は、0.05~2.00%である。2.00%を超えると鋳造時に巨大金属間化合物が形成され易くなり、塑性加工性を低下させる。一方、0.05%未満では、その効果が十分得られない。Mn含有量は、好ましくは0.05~1.80%である。
Tiは、固溶強化により中間層材の強度を向上させると共に、耐食性も向上させるので含有させてもよい。Ti含有量は、0.05~0.30%である。0.05%未満では、上記効果が得られない。0.30%を超えると巨大金属間化合物を形成し易くなり、塑性加工性を低下させる。Ti含有量は、好ましくは0.05~0.20%である。
Zrは、固溶強化により中間層材の強度を向上させると共に、Al-Zr系の金属間化合物を析出させてろう付加熱後の結晶粒を粗大化する作用を有するので含有させてもよい。Zr含有量は、0.05~0.30%である。0.05%未満では上記効果が得られない。一方、0.30%を超えると巨大金属間化合物を形成し易くなり、塑性加工性を低下させる。Zr含有量は、好ましくは0.10~0.20%である。
Crは、固溶強化により中間層材の強度を向上させると共に、Al-Cr系の金属間化合物を析出させてろう付加熱後の結晶粒を粗大化する作用を有するので含有させてもよい。Cr含有量は、0.05~0.30%である。0.05%未満では上記効果が得られない。0.30%を超えると巨大金属間化合物を形成し易くなり、塑性加工性を低下させる。Cr含有量は、好ましくは0.10~0.20%である。
Vは、固溶強化により中間層材の強度を向上させると共に耐食性も向上させるので含有させてもよい。V含有量は、0.05~0.30%である。0.05%未満では上記効果が得られない。0.30%を超えると巨大金属間化合物を形成し易くなり、塑性加工性を低下させる。V含有量は、好ましくは0.05~0.20%である。
第1及び第2の形態における第1及び第2のろう材には、Si:2.5~13.0%、Fe:0.05~1.20%を必須元素として含有し、残部Al及び不可避的不純物からなるアルミニウム合金が用いられる。
Siを添加することによりろう材の融点が低下して液相を生じさせ、これによってろう付を可能にする。Si含有量は2.5~13.0%である。2.5%未満では、生じる液相が僅かでありろう付が機能し難くなる。一方、13.0%を超えると、例えばこのろう材をチューブ材に用いた場合に、フィンなどの相手材へ拡散するSi量が過剰となり、相手材の溶融が発生してしまう。Si含有量は、好ましくは3.5~12.0%である。
Feは、Al-Fe系やAl-Fe-Si系の金属間化合物を形成し易いために、ろう付に有効となるSi量を低下させてろう付性の低下を招く。Fe含有量は、0.05~1.20%である。0.05%未満では、高純度アルミニウム地金を使用しなければならずコスト高を招く。一方、1.20%を超えると、ろう付に有効となるSi量を低下させてろう付が不十分となる。Fe含有量は、好ましくは0.10~0.50%である。
Znは孔食電位を卑にすることができ、心材との電位差を形成することで犠牲防食効果により耐食性を向上することができるので含有させてもよい。Znの含有量は0.5~8.0%である。0.5%未満では、犠牲防食効果による耐食性向上の効果が十分に得られない。一方、8.0%を超えると、腐食速度が速くなり早期に犠牲防食層が消失して耐食性が低下する。Zn含有量は、好ましくは1.0~6.0%である。
Cuは、固溶強化によりろう材の強度を向上させるので含有させてもよい。Cu含有量は、0.05~1.50%である。0.05%未満では上記効果が不十分となり、1.50%を超えると鋳造時におけるアルミニウム合金の割れ発生の虞が高くなる。Cu含有量は、好ましくは0.30~1.00%である。なお、ろう材がZnを含有している場合、Cuの好ましい含有量は0.05~0.60%である。Cuは孔食電位を貴にするため、0.6%を超えるとZnによる犠牲防食効果を失わせる場合がある。
Mnは、ろう材の強度と耐食性を向上させるので含有させてもよい。Mnの含有量は、0.05~2.00%である。2.00%を超えると鋳造時に巨大金属間化合物が形成され易くなり、塑性加工性を低下させる。一方、0.05%未満では、その効果が十分得られない。Mn含有量は、好ましくは0.05~1.80%である。
Tiは、固溶強化によりろう材の強度を向上させると共に耐食性も向上させるので含有させてもよい。Ti含有量は、0.05~0.30%である。0.05%未満では、上記効果が得られない。0.30%を超えると巨大金属間化合物を形成し易くなり、塑性加工性を低下させる。Ti含有量は、好ましくは0.10~0.20%である。
Zrは、固溶強化によりろう材の強度を向上させると共に、Al-Zr系の金属間化合物を析出させてろう付加熱後の結晶粒を粗大化する作用を有するので含有させてもよい。Zr含有量は、0.05~0.30%である。0.05%未満では上記効果が得られない。0.30%を超えると巨大金属間化合物を形成し易くなり、塑性加工性を低下させる。Zr含有量は、好ましくは0.10~0.20%である。
Crは、固溶強化によりろう材の強度を向上させると共に、Al-Cr系の金属間化合物を析出させてろう付加熱後の結晶粒を粗大化する作用を有するので含有させてもよい。Cr含有量は、0.05~0.30%である。0.05%未満では上記効果が得られない。0.30%を超えると巨大金属間化合物を形成し易くなり、塑性加工性を低下させる。Cr含有量は、好ましくは0.10~0.20%である。
Vは、固溶強化によりろう材の強度を向上させると共に耐食性も向上させるので含有させてもよい。V含有量は、0.05~0.30%である。0.05%未満では上記効果が得られない。0.30%を超えると巨大金属間化合物を形成し易くなり、塑性加工性を低下させる。V含有量は、好ましくは0.10~0.20%である。
Na、Srは、ろう材中のSi粒子を微細化する効果を発揮する。Na、Srの含有量はそれぞれ、0.001~0.050%である。それぞれの含有量が0.001%未満では、上記効果が十分に得られない。一方、それぞれの含有量が0.050%を超える場合は、酸化被膜が厚くなり、ろう付性を低下させる。それぞれの好ましい含有量は、いずれも0.003~0.020%である。
本発明のアルミニウム合金クラッド材では、ろう付加熱前における中間層材の結晶粒径を60μm以上、ろう付加熱後における中間層材の結晶粒径を100μm以上に規定する。これは、ろう付加熱後における中間層材の耐食性の向上を目的としたものである。なお、図1に示すように、ここでの結晶粒径とは、中間層材を圧延面から観察し、粒界で囲まれた領域を結晶粒としてその円相当径直径の算術平均値をいうものとする。また粒界とは、隣接する結晶方位差が20度以上である境界を指すものとする。結晶粒径の測定方法は特に限定されるものではないが、電子線後方散乱回折法(EBSD)によるのが一般的である。以下にこの限定理由を説明する。
本発明のアルミニウム合金クラッド材は、ろう付加熱前における心材の圧延方向に沿った断面において、板厚方向の結晶粒径をR1(μm)とし、圧延方向の結晶粒径をR2(μm)としたとき、R1/R2を0.30以下に規定する。これは、ろう付加熱前における、クラッド材の成形性向上を図るための指標である。図2に示すように、ここでの結晶粒径R1及びR2(μm)とは、クラッド材の圧延方向に沿った断面を観察して粒界で囲まれた領域を結晶粒として、各結晶粒の板厚方向の最大径をR1とし圧延方向の最大径をR2として定義した。また、粒界とは、隣接する結晶方位差が20度以上である境界を指すものとする。結晶粒径の測定方法には特に限定されるものではないが、電子線後方散乱回折法(EBSD)によるのが一般的である。なお、心材の加工度が非常に大きい場合、鏡面研磨後に陽極酸化を行って陽極酸化面を偏光顕微鏡で観察すると、図3に示すような繊維状組織が観察される。このような場合は、板厚方向の結晶粒径が完全につぶされており、R1=0であると定義する。
本発明に係る上記第1形態のアルミニウム合金クラッド材の製造方法は、心材用、中間層材用及び第1ろう材用のアルミニウム合金をそれぞれ鋳造する工程と、鋳造した中間層材鋳塊及び第1ろう材鋳塊を所定の厚さまでそれぞれ熱間圧延する熱間圧延工程と、心材鋳塊の一方の面に所定の厚さとした中間層材をクラッドし、他方の面に所定の厚さとした第1ろう材をクラッドしてクラッド材とするクラッド工程と、クラッド材を熱間圧延する熱間クラッド圧延工程と、熱間クラッド圧延したクラッド材を冷間圧延する冷間圧延工程と、冷間圧延工程の途中及び冷間圧延工程の後の一方又は両方においてクラッド材を焼鈍する1回以上の焼鈍工程とを含む。
心材、第1及び第2のろう材及び中間層材の鋳造工程における条件に特に制限は無いが、通常は水冷式の半連続鋳造によって行われる。また、心材、中間層材、第1及び第2のろう材、をそれぞれ所定の厚さまで熱間圧延する工程において、その加熱条件は、400~560℃の温度で、1~10時間行うのが好ましい。400℃未満では塑性加工性が乏しいため圧延時にコバ割れなどを生じる場合がある。560℃を超える高温の場合には、加熱中に鋳塊が溶融してしまう虞がある。加熱時間が1時間未満では鋳塊の温度が不均一となって塑性加工性が乏しく、圧延時にコバ割れなどを生じる場合があり、10時間を超える場合は生産性を著しく損なってしまう。
上記第1及び第2の態様に係るアルミニウム合金クラッド材の製造方法では、熱間クラッド圧延工程において、圧延開始温度が400~520℃であり、クラッド材の温度が200~400℃である間に1パスでの圧下率が30%以上となる圧延パスを5回以下に制限する。なお、熱間クラッド圧延工程は、粗圧延工程と仕上圧延工程に分けてもよい。仕上圧延工程では、リバース式又はタンデム式の圧延機が用いられる。リバース式圧延機では、片道1回の圧延を1パスと定義し、タンデム式圧延機では、圧延ロール1組による圧延を1パスと定義する。
上記第1及び第2の態様に係るアルミニウム合金クラッド材の製造工程では、冷間圧延工程の途中及び冷間圧延工程の後の一方又は両方において、クラッド材を1回以上焼鈍する焼鈍工程が設けられる。具体的には、(1)冷間圧延工程の途中において1回以上の中間焼鈍が実施され、(2)冷間圧延工程の後に最終焼鈍工程が1回実施され、或いは、(3)(1)及び(2)が実施されるものである。この焼鈍工程では、クラッド材を200~560℃で1~10時間保持する。
アルミニウム合金心材を鋳造して得られる鋳塊を、クラッド工程の前に均質化処理工程に供しても良い。均質化処理工程は、通常、450~620℃で1~20時間鋳塊を保持するのが好ましい。温度が450℃未満の場合や保持時間が1時間未満では均質化効果が十分でない場合があり、620℃を超えると心材鋳塊の溶融を生じてしまう虞がある。また、保持時間が20時間を超えても、均質化効果が飽和し経済性に欠ける。
本発明のアルミニウム合金クラッド材では、中間層材のクラッド率(片面)を3~25%とするのが好ましい。上述のように、製造工程中の熱間クラッド圧延工程において、中間層材にのみ大きなせん断ひずみが加えられる必要がある。しかしながら、中間層材のクラッド率が25%を超えると、中間層材全体に十分なせん断ひずみが加わらず、中間層材全体を再結晶組織とすることができない場合がある。一方、中間層材のクラッド率が3%未満では、中間層材が薄過ぎるため、熱間クラッド圧延中において心材全体にわたって中間層材を被覆することができない場合がある。中間層材のクラッド率は、より好ましくは5~20%である。
なお、第1及び第2のろう材のクラッド率に特に制限は無いが、通常はいずれも3~30%程度でクラッドされる。
上記アルミニウム合金クラッド材は、チューブ材、ヘッダープレートなどの熱交換器用部材として、特にチューブ材として好適に用いられる。例えば、上記アルミニウム合金クラッド材に曲げ成形を施し、その両端部の重ね合せ部分をろう付け接合して、冷却水などの媒体を流すためのチューブ材が作製される。また、上記アルミニウム合金クラッド材を加工して、チューブ材の両端部と接合される孔を備えたヘッダープレートが作製される。本発明に係る熱交換器は、例えば、上記のチューブ材、フィン材及びヘッダープレートを組み合わせ、これらを一度にろう付加工した構造を有する。
各クラッド材試料から、圧延方向と平行な方向にJIS5号試験片を切り出し、圧延方向と平行な方向に5%ストレッチしてから、中間層材面を曲げの内側とし、曲げ半径R0.05mmの180°曲げを行なった。これの曲げR断面を観察できるよう樹脂埋めして、鏡面研磨を行い、光学顕微鏡により割れ発生の有無を評価した。その結果、心材に割れが発生していない場合を成形性合格(○)とし、心材に割れが発生した場合を成形性不合格(×)とした。なお、両ろう材、中間層材での割れ発生の有無は評価対象外とした。
厚さ0.07mm、調質H14、合金成分は3003合金に1.0%のZnを添加したフィン材を用意し、これをコルゲート成形して熱交換器フィン材とした。このフィン材を上記クラッド材試料の第1のろう材の面又は第2のろう材面に配置し、5%のフッ化物フラックス水溶液中に浸漬し、600℃で3分のろう付加熱に供して、ノコロックろう付によりミニコア試料を作製した。ろう付け後、フィンを剥離して、フィンとろう材の接触数(山数)とフィレットが形成されている箇所の比率からフィン接合率を求めた。このミニコア試料のフィン接合率が95%以上であり、かつ、クラッド材試料及びフィンに溶融が生じていない場合をろう付性が合格(○)とした。一方、(1)フィン接合率が95%未満の場合と、(2)クラッド材試料及びフィンの少なくともいずれかに溶融が生じた場合とにおいて、(1)及び(2)、或いは、(1)又は(2)をろう付性が不合格(×)とした。
600℃で3分の熱処理(ろう付加熱に相当)を施したクラッド材試料を、引張速度10mm/分、ゲージ長50mmの条件で、JIS Z2241に従って引張試験に供した。得られた応力-ひずみ曲線から引張強さを読み取った。その結果、引張強さが120MPa以上の場合を合格(○)とし、それ未満を不合格(×)とした。
ろう付加熱(600℃で3分の熱処理でありろう付加熱に相当)前のクラッド材試料、ならびに、ろう付加熱後のクラッド材試料の表面から研磨してろう材を除去した後、中間層材のL-LT面を鏡面研磨し、中間層材結晶粒径測定用試料とした。この試料における2mm×2mmの領域をSEM(走査型電子顕微鏡)においてEBSDにかけ、その結果から結晶方位差が20度以上である境界を粒界として検出し、結晶粒径(円相当直径)を算出した。なお、測定箇所は、任意に10箇所選定して、その算術平均値をもって結晶粒径とした。また、中間層材の再結晶化が完了していないため繊維状組織であり、結晶粒径を測定できなかったものについては、「繊維状」と記入した。
ろう付加熱(600℃で3分の熱処理でありろう付加熱に相当)前のクラッド材試料、ならびに、ろう付加熱後のクラッド材試料を用い、圧延方向に沿った断面が測定面となるよう樹脂埋めして鏡面研磨し、心材結晶粒径測定用試料とした。この試料における長さ2mm×厚さ0.2mmの領域をSEMにおいてEBSDにかけ、その結果から結晶方位差が20度以上である境界を粒界として検出した。結晶粒の板厚方向の最大径R1及び圧延方向の最大径R2を測定し、R1/R2の値を算出した。なお、結晶粒は、同一視野で任意に10箇所測定し、その算術平均値をもってR1/R2とした。また、EBSDにおいて結晶粒界が検出されなかった場合は、鏡面研磨した試料を陽極酸化させて偏光顕微鏡で観察し、図3に示すような繊維状組織が見られた場合はR1=0とした。
ろう付性の評価にて用いたものと同じミニコア試料を用い、フィンと接合していない側の表面を絶縁樹脂でマスキングして、フィンと接合している面を試験面とし、JIS-H8502に基づいて500時間及び1000時間のCASS試験に供した。その結果、1000時間でクラッド材に腐食貫通の生じなかったものをCASSの耐食性優秀合格(◎)とし、500時間でクラッド材に腐食貫通の生じなかったものをCASSの耐食性合格(○)とし、500時間で腐食貫通が生じたものをCASSの耐食性不合格(×)とした。なお、本評価は第1のろう材については全てを評価対象とし、第2のろう材についてはZnが添加されているもののみを対象とした。また、第2のろう材がクラッドされていない試料では、心材の第1のろう材がクラッドされている一方の面ではない他方の面(心材が露出している面)については評価対象としなかった。また、ろう付性の評価「×」のものは適切なミニコア試料を作製できなかったため、評価対象外とした。
R2・・・圧延方向に沿った心材断面における圧延方向の結晶粒径
Claims (14)
- アルミニウム合金の心材と、当該心材の一方の面にクラッドされた中間層材と、当該中間層材の心材側ではない面にクラッドされたろう材とを備えるアルミニウム合金クラッド材において、前記心材が、Si:0.05~1.50mass%、Fe:0.05~2.00mass%、Mn:0.5~2.0mass%を含有し、残部Al及び不可避的不純物からなるアルミニウム合金からなり、前記中間層材が、Zn:0.5~8.0mass%、Si:0.05~1.50mass%、Fe:0.05~2.00mass%を含有し、残部Al及び不可避的不純物からなるアルミニウム合金からなり、前記ろう材が、Si:2.5~13.0mass%、Fe:0.05~1.20mass%を含有し、残部Al及び不可避的不純物からなるアルミニウム合金からなり、前記中間層材のろう付加熱前における結晶粒径が60μm以上であり、ろう付加熱前における前記心材の圧延方向に沿った断面において、板厚方向の結晶粒径をR1(μm)、圧延方向の結晶粒径をR2(μm)としたとき、R1/R2が0.30以下であることを特徴とするアルミニウム合金クラッド材。
- 前記心材が、Mg:0.05~0.50mass%、Cu:0.05~1.50mass%、Ti:0.05~0.30mass%、Zr:0.05~0.30mass%、Cr:0.05~0.30mass%及びV:0.05~0.30mass%から選択される1種又は2種以上を更に含有するアルミニウム合金からなる、請求項1に記載のアルミニウム合金クラッド材。
- 前記中間層材が、Ni:0.05~2.00mass%、Mn:0.05~2.00mass%、Ti:0.05~0.30mass%、Zr:0.05~0.30mass%、Cr:0.05~0.30mass%及びV:0.05~0.30mass%から選択される1種又は2種以上を更に含有するアルミニウム合金からなる、請求項1又は2に記載のアルミニウム合金クラッド材。
- 前記ろう材が、Zn:0.5~8.0mass%、Cu:0.05~1.50mass%、Mn:0.05~2.00mass%、Ti:0.05~0.30mass%、Zr:0.05~0.30mass%、Cr:0.05~0.30mass%及びV:0.05~0.30mass%から選択される1種又は2種以上を更に含有するアルミニウム合金からなる、請求項1~3のいずれか一項に記載のアルミニウム合金クラッド材。
- 前記ろう材が、Na:0.001~0.050mass%及びSr:0.001~0.050mass%から選択される1種又は2種を更に含有するアルミニウム合金からなる、請求項1~4のいずれか一項に記載のアルミニウム合金クラッド材。
- 請求項1~5のいずれか一項に記載のアルミニウム合金クラッド材の製造方法であって、前記心材用、中間層材用及びろう材用のアルミニウム合金をそれぞれ鋳造する工程と、鋳造した中間層材鋳塊及びろう材鋳塊を所定の厚さまでそれぞれ熱間圧延する熱間圧延工程と、心材鋳塊の一方の面に所定厚さとした中間層材をクラッドし、当該中間層材の心材側ではない面に所定厚さとしたろう材をクラッドしてクラッド材とするクラッド工程と、クラッド材を熱間圧延する熱間クラッド圧延工程と、熱間クラッド圧延したクラッド材を冷間圧延する冷間圧延工程と、冷間圧延工程の途中及び冷間圧延工程の後の一方又は両方においてクラッド材を焼鈍する1回以上の焼鈍工程とを含み、前記熱間クラッド圧延工程において、圧延開始温度が400~520℃であり、クラッド材の温度が200~400℃である間に1パスでの圧下率が30%以上となる圧延パスを5回以下に制限し、前記焼鈍工程において、クラッド材が200~560℃で1~10時間保持されることを特徴とするアルミニウム合金クラッド材の製造方法。
- アルミニウム合金の心材と、当該心材の一方の面にクラッドされた中間層材と、当該中間層材の心材側ではない面にクラッドされたろう材と、当該心材の他方の面にクラッドされたろう材とを備えるアルミニウム合金クラッド材において、前記心材が、Si:0.05~1.50mass%、Fe:0.05~2.00mass%、Mn:0.5~2.0mass%を含有し、残部Al及び不可避的不純物からなるアルミニウム合金からなり、前記中間層材が、Zn:0.5~8.0mass%、Si:0.05~1.50mass%、Fe:0.05~2.00mass%を含有し、残部Al及び不可避的不純物からなるアルミニウム合金からなり、前記中間層材の心材側ではない面にクラッドされたろう材及び前記心材の他方の面にクラッドされたろう材が、Si:2.5~13.0mass%、Fe:0.05~1.20mass%を含有し、残部Al及び不可避的不純物からなるアルミニウム合金からなり、前記中間層材のろう付加熱前における結晶粒径が60μm以上であり、ろう付加熱前における前記心材の圧延方向に沿った断面において、板厚方向の結晶粒径をR1(μm)、圧延方向の結晶粒径をR2(μm)としたとき、R1/R2が0.30以下であることを特徴とするアルミニウム合金クラッド材。
- 前記心材が、Mg:0.05~0.50mass%、Cu:0.05~1.50mass%、Ti:0.05~0.30mass%、Zr:0.05~0.30mass%、Cr:0.05~0.30mass%及びV:0.05~0.30mass%から選択される1種又は2種以上を更に含有するアルミニウム合金からなる、請求項7に記載のアルミニウム合金クラッド材。
- 前記中間層材が、Ni:0.05~2.00mass%、Mn:0.05~2.00mass%、Ti:0.05~0.30mass%、Zr:0.05~0.30mass%、Cr:0.05~0.30mass%及びV:0.05~0.30mass%から選択される1種又は2種以上を更に含有するアルミニウム合金からなる、請求項7又は8に記載のアルミニウム合金クラッド材。
- 前記中間層材の心材側ではない面にクラッドされたろう材及び前記心材の他方の面にクラッドされたろう材が、Zn:0.5~8.0mass%、Cu:0.05~1.50mass%、Mn:0.05~2.00mass%、Ti:0.05~0.30mass%、Zr:0.05~0.30mass%、Cr:0.05~0.30mass%及びV:0.05~0.30mass%から選択される1種又は2種以上を更に含有するアルミニウム合金からなる、請求項7~9のいずれか一項に記載のアルミニウム合金クラッド材。
- 前記中間層材の心材側ではない面にクラッドされたろう材及び前記心材の他方の面にクラッドされたろう材が、Na:0.001~0.050mass%及びSr:0.001~0.050mass%から選択される1種又は2種を更に含有するアルミニウム合金からなる、請求項7~10のいずれか一項に記載のアルミニウム合金クラッド材。
- 請求項7~11のいずれか一項に記載のアルミニウム合金クラッド材の製造方法であって、前記心材用、中間層材用、中間層材の心材側ではない面にクラッドされるろう材用及び心材の他方の面にクラッドされるろう材のアルミニウム合金をそれぞれ鋳造する工程と、鋳造した中間層材鋳塊、中間層材の心材側ではない面にクラッドされるろう材鋳塊及び心材の他方の面にクラッドされるろう材鋳塊を所定の厚さまでそれぞれ熱間圧延する熱間圧延工程と、心材鋳塊の一方の面に所定厚さとした中間層材をクラッドし、当該中間層材の心材側ではない面に所定厚さとしたろう材をクラッドし、心材鋳塊の他方の面に所定厚さとしたろう材をクラッドしてクラッド材とするクラッド工程と、クラッド材を熱間圧延する熱間クラッド圧延工程と、熱間クラッド圧延したクラッド材を冷間圧延する冷間圧延工程と、冷間圧延工程の途中及び冷間圧延工程の後の一方又は両方においてクラッド材を焼鈍する1回以上の焼鈍工程とを含み、前記熱間クラッド圧延工程において、圧延開始温度が400~520℃であり、クラッド材の温度が200~400℃である間に1パスでの圧下率が30%以上となる圧延パスを5回以下に制限し、前記焼鈍工程において、クラッド材が200~560℃で1~10時間保持されることを特徴とするアルミニウム合金クラッド材の製造方法。
- 請求項1~5及び7~11のいずれか一項に記載のアルミニウム合金クラッド材を用いた熱交換器であって、ろう付加熱後における前記中間層材の結晶粒径が100μm以上であることを特徴とする熱交換器。
- 請求項13に記載の熱交換器の製造方法であって、不活性ガス雰囲気中でフラックスを用いてアルミニウム合金材をろう付することを特徴とする熱交換器の製造方法。
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WO2017170204A1 (ja) * | 2016-03-29 | 2017-10-05 | 株式会社Uacj | 熱交換器用アルミニウム合金製ブレージングシート及びその製造方法 |
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Also Published As
Publication number | Publication date |
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PT2015104760B (pt) | 2019-12-12 |
CN105745343B (zh) | 2019-05-03 |
US20160319401A1 (en) | 2016-11-03 |
DE112014006121T5 (de) | 2016-09-22 |
CN105745343A (zh) | 2016-07-06 |
JP6452626B2 (ja) | 2019-01-16 |
JPWO2015104760A1 (ja) | 2017-03-23 |
US9976201B2 (en) | 2018-05-22 |
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