WO2022249664A1 - Aluminum alloy, aluminum alloy wire, and method for manufacturing aluminum alloy wire - Google Patents
Aluminum alloy, aluminum alloy wire, and method for manufacturing aluminum alloy wire Download PDFInfo
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- WO2022249664A1 WO2022249664A1 PCT/JP2022/011698 JP2022011698W WO2022249664A1 WO 2022249664 A1 WO2022249664 A1 WO 2022249664A1 JP 2022011698 W JP2022011698 W JP 2022011698W WO 2022249664 A1 WO2022249664 A1 WO 2022249664A1
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- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 249
- 238000004519 manufacturing process Methods 0.000 title claims description 50
- 238000000034 method Methods 0.000 title claims description 29
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- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims abstract description 22
- 239000010949 copper Substances 0.000 claims abstract description 22
- 229910052749 magnesium Inorganic materials 0.000 claims abstract description 22
- 239000010703 silicon Substances 0.000 claims abstract description 22
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 22
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims abstract description 21
- 229910052802 copper Inorganic materials 0.000 claims abstract description 21
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 20
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 20
- 239000006185 dispersion Substances 0.000 claims abstract description 19
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- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 claims abstract description 12
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- 239000010936 titanium Substances 0.000 claims description 28
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 27
- 229910052719 titanium Inorganic materials 0.000 claims description 27
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- 229910052726 zirconium Inorganic materials 0.000 claims description 26
- 239000011651 chromium Substances 0.000 claims description 24
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- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 9
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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
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C1/00—Manufacture of metal sheets, metal wire, metal rods, metal tubes by drawing
- B21C1/003—Drawing materials of special alloys so far as the composition of the alloy requires or permits special drawing methods or sequences
-
- 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
- B21B1/16—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 wire rods, bars, merchant bars, rounds wire or material of like small cross-section
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C1/00—Manufacture of metal sheets, metal wire, metal rods, metal tubes by drawing
- B21C1/02—Drawing metal wire or like flexible metallic material by drawing machines or apparatus in which the drawing action is effected by drums
-
- 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
- C22C21/06—Alloys based on aluminium with magnesium 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
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
- C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
-
- 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
-
- 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
-
- 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
- C22F1/02—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working in inert or controlled atmosphere or vacuum
-
- 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
- C22F1/047—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 magnesium 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
- C22F1/05—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 of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions
-
- 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
Definitions
- the present disclosure relates to aluminum alloys, aluminum alloy wires, and methods of manufacturing aluminum alloy wires.
- This application claims priority based on Japanese Patent Application No. 2021-089504 filed in Japan on May 27, 2021, and incorporates all the content described in the Japanese application.
- Patent Document 1 discloses an aluminum alloy wire made of an aluminum alloy containing silicon and magnesium and having high tensile strength after solution treatment and aging treatment.
- the above aluminum alloy wire can be used as a raw material for aluminum alloy members.
- the aluminum alloy member is manufactured by subjecting the aluminum alloy wire to predetermined plastic working, followed by solution treatment and aging treatment.
- the aluminum alloy of the present disclosure contains 0.6% by mass or more and 1.5% by mass or less of silicon, 0.5% by mass or more and 1.3% by mass or less of magnesium, and 0.1% by mass or more and 1.2% by mass of copper.
- the composition includes 0.2% by mass or more and 1.15% by mass or less of manganese, and the balance is aluminum and unavoidable impurities.
- the average value of the degree of orientation of the 111 plane obtained by X-ray diffraction of the entire cross section in the state of being subjected to solution treatment and aging treatment is 50% or more, and the dispersion of the degree of orientation of the 111 plane is 45%. It is below.
- the aluminum alloy wire of the present disclosure is made of the aluminum alloy of the present disclosure.
- the method for producing an aluminum alloy wire of the present disclosure includes silicon of 0.6% by mass or more and 1.5% by mass or less, magnesium of 0.5% by mass or more and 1.3% by mass or less, and copper of 0.1% by mass or more and 1 .2% by mass or less, containing 0.2% by mass or more and 1.15% by mass or less of manganese, the balance being aluminum and unavoidable impurities.
- the degree of working in the second wire drawing is 20% or more and is greater than the degree of working in the first wire drawing.
- FIG. 1 is a perspective view showing an example of an aluminum alloy wire of an embodiment.
- FIG. 2 shows sample No. 1 of Test Example 1.
- 3 is a diagram showing an example of the distribution of the degree of orientation of the 111 plane in the cross section of the aluminum alloy wire of No. 3.
- FIG. 3 shows sample No. 1 of Test Example 1.
- 3 is a diagram showing, by contour lines, an example of the distribution of the degree of orientation of the 111 plane of the aluminum alloy wire of No. 3.
- FIG. FIG. 4 shows sample No. 1 of Test Example 1.
- 1 is a diagram showing an example of the distribution of the degree of orientation of the 111 plane in the cross section of the aluminum alloy wire of No. 1.
- FIG. FIG. 5 shows sample No. 1 of Test Example 1.
- FIG. 1 is a diagram showing, by contour lines, an example of the distribution of the degree of orientation of the 111 plane of the aluminum alloy wire No. 1.
- FIG. FIG. 6 is a diagram for explaining a method of measuring the orientation distribution of the 111 plane over the entire cross section of the sample.
- the aluminum alloy of the present disclosure and the aluminum alloy wire of the present disclosure have high strength in the solution treated and aged condition.
- the aluminum alloy wire manufacturing method of the present disclosure can manufacture the aluminum alloy wire of the present disclosure.
- the aluminum alloy according to one aspect of the present disclosure contains 0.6% by mass or more and 1.5% by mass or less of silicon, 0.5% by mass or more and 1.3% by mass or less of magnesium, and 0.1% by mass of copper. % or more and 1.2 mass % or less, manganese of 0.2 mass % or more and 1.15 mass % or less, and the balance being aluminum and unavoidable impurities.
- the average value of the degree of orientation of the 111 plane obtained by X-ray diffraction of the entire cross section in a state of being subjected to solution treatment and aging treatment is 50% or more, and the degree of orientation of the 111 plane is 50% or more. Dispersion is 45% or less.
- the 111 plane in this disclosure means the crystal plane denoted as (111) in crystallography.
- the degree of orientation of the 111 plane in the present disclosure is determined using values obtained by normalizing the following three diffraction intensities obtained by X-ray diffraction over the entire cross section.
- the degree of orientation of the 111 plane in the present disclosure is the ratio of the normalized value of the diffraction intensity of the 111 plane to the total value of the three normalized values.
- the three diffraction intensities are the diffraction intensity on the 111th plane, the diffraction intensity on the 200th plane, and the diffraction intensity on the 220th plane.
- the 200 plane and 220 plane mean crystal planes denoted as (200) and (220) in crystallography.
- the average value of the degree of orientation of the 111 planes in the present disclosure is the average value of the above ratios at each measurement point over the entire cross section.
- the dispersion of the degree of orientation of the 111 plane in the present disclosure is a value obtained from the above average value.
- a method for measuring the average value and dispersion of the orientation degree of the 111 planes in the present disclosure will be described later.
- the entire cross section is subjected to X-ray diffraction measurement, and the orientation state of the 111 plane is specified using the value obtained by normalizing the diffraction intensity. can appropriately evaluate the degree of orientation of
- the cross section of the aluminum alloy is, for example, the following cross sections.
- the heating temperature is a temperature selected from the range of 530°C or higher and 580°C or lower.
- the heating time is selected from the range of 15 minutes or more and 120 minutes or less.
- the heating temperature is a temperature selected from the range of 150°C or higher and 180°C or lower.
- the heating time is selected from the range of 4 hours or more and 100 hours or less.
- the aluminum alloy of the present disclosure has a high tensile strength due to precipitation hardening in the state of solution heat treatment and aging treatment due to the specific composition described above.
- the state in which the 111 planes of the crystal grains are oriented occurs over the entire cross section rather than a part of the cross section.
- the aluminum alloy of the present disclosure having such a cross section is less likely to break when pulled in a direction perpendicular to the cross section, for example. From this point as well, the aluminum alloy of the present disclosure has high tensile strength.
- the aluminum alloys of the present disclosure have higher tensile strength than the aluminum alloys described in US Pat.
- the aluminum alloy of the present disclosure has high strength in the state of solution heat treatment and aging treatment.
- the aluminum alloy of the present disclosure has well-balanced heat resistance, corrosion resistance, and strength in the state of solution heat treatment and aging treatment, similar to alloys called 6000 series alloys in the international alloy symbol.
- Such an aluminum alloy of the present disclosure can be suitably used as an aluminum alloy member that requires higher strength in addition to heat resistance and corrosion resistance, and as a raw material for this aluminum alloy member.
- Examples of aluminum alloy members include automobile parts and various structural members. Automobile parts and various structural members can take the form of wires, bars, pipes, and the like. The raw material is, for example, an aluminum alloy wire, an aluminum alloy plate, or the like.
- the aluminum alloy of the present disclosure may further contain one or more elements selected from the group consisting of iron, chromium, zinc, titanium, and zirconium.
- the iron content is more than 0% by mass and 0.8% by mass or less.
- the content of chromium is more than 0% by mass and 0.35% by mass or less.
- the zinc content is more than 0% by mass and 0.5% by mass or less.
- the content of titanium is more than 0% by mass and 0.2% by mass or less.
- the content of zirconium is more than 0% by mass and 0.2% by mass or less.
- the above aluminum alloys tend to have higher tensile strength.
- the aluminum alloy of (2) above contains 1.0% by mass or more and 1.3% by mass or less of silicon, 0.5% by mass or more and 1.2% by mass or less of magnesium, and 0.3% by mass or more of iron. 0.8% by mass or less, 0.1% by mass or more and 0.4% by mass or less of copper, 0.2% by mass or more and 0.5% by mass or less of manganese, 0% by mass or more and 0.3% by mass or less of chromium, It may have a composition containing 0.001% by mass or more and 0.1% by mass or less of titanium, with the balance being aluminum and unavoidable impurities.
- This aluminum alloy may further contain 0.001% by mass or more and 0.2% by mass or less of zirconium.
- the above aluminum alloys tend to have higher tensile strength.
- the aluminum alloy of (2) above contains 0.6% by mass or more and 1.5% by mass or less of silicon, 0.7% by mass or more and 1.3% by mass or less of magnesium, and 0.02% by mass or more of iron. 0.4% by mass or less, 0.5% by mass or more and 1.2% by mass or less of copper, 0.5% by mass or more and 1.1% by mass or less of manganese, 0% by mass or more and 0.3% by mass or less of chromium, 0.005 mass% or more and 0.5 mass% or less of zinc, 0.01 mass% or more and 0.2 mass% or less of titanium, 0.05 mass% or more and 0.2 mass% or less of zirconium, and the balance being aluminum and It may have a composition consisting of unavoidable impurities.
- the above aluminum alloys tend to have higher tensile strength.
- the aluminum alloy of the present disclosure may have a tensile strength greater than 425 MPa in the solution treated and aged condition.
- the above aluminum alloy has high strength due to its high tensile strength.
- An aluminum alloy wire according to an aspect of the present disclosure is made of the aluminum alloy according to any one of (1) to (5) above.
- the aluminum alloy wire of the present disclosure is made of the aluminum alloy of the present disclosure, it has high strength in a state where solution treatment and aging treatment have been performed.
- Such an aluminum alloy wire of the present disclosure can be used as a raw material for high-strength aluminum alloy members.
- a method for manufacturing an aluminum alloy wire according to an aspect of the present disclosure includes silicon of 0.6% by mass or more and 1.5% by mass or less, magnesium of 0.5% by mass or more and 1.3% by mass or less, and copper.
- An aluminum alloy cast material having a composition containing 0.1% by mass or more and 1.2% by mass or less, 0.2% by mass or more and 1.15% by mass or less of manganese, and the balance being aluminum and inevitable impurities is subjected to plastic working.
- the degree of working in the second wire drawing is 20% or more and is greater than the degree of working in the first wire drawing.
- the method of manufacturing an aluminum alloy wire of the present disclosure can manufacture a high-strength aluminum alloy wire in a state in which solution treatment and aging treatment have been performed. The reason for this will be described later.
- the aluminum alloy may further contain one or more elements selected from the group consisting of iron, chromium, zinc, titanium, and zirconium.
- the iron content is more than 0% by mass and 0.8% by mass or less.
- the content of chromium is more than 0% by mass and 0.35% by mass or less.
- the zinc content is more than 0% by mass and 0.5% by mass or less.
- the content of titanium is more than 0% by mass and 0.2% by mass or less.
- the content of zirconium is more than 0% by mass and 0.2% by mass or less.
- the aluminum alloy wire manufacturing method described above can manufacture an aluminum alloy wire having a higher tensile strength.
- the aluminum alloy of the embodiment has the following composition and cross-sectional structure.
- the composition of the aluminum alloy of the embodiment contains silicon, magnesium, copper, and manganese within the ranges described later, with the balance being aluminum and unavoidable impurities.
- the aluminum alloy of the embodiment may further contain one or more elements selected from the group consisting of iron, chromium, zinc, titanium, and zirconium within the range described below.
- the 111 planes of the crystal grains are oriented in the normal direction of the cross section in a state in which solution treatment and aging treatment have been performed. In particular, the 111 plane is oriented in the normal direction of the cross section in many crystal grains among the crystal grains forming the cross section of the aluminum alloy.
- the composition and structure will be described in order below.
- Silicon, magnesium, copper, and manganese are collectively referred to as primary elements. Iron, chromium, zinc, titanium, and zirconium are collectively referred to as secondary elements. Each element is indicated by an element symbol.
- Si means silicon.
- Mg means magnesium.
- Cu means copper.
- Mn means manganese.
- Al means aluminum.
- Fe means iron.
- Cr means chromium.
- Zn means zinc.
- Ti means titanium.
- Zr means zirconium.
- a state in which the aluminum alloy is subjected to solution treatment and aging treatment is referred to as a state after heat treatment.
- the first element is an essential element and the second element is an optional element.
- the aluminum alloy of the embodiment contains 0.6 mass % to 1.5 mass % of silicon, 0.5 mass % to 1.3 mass % of magnesium, and 0.1 mass % to 1.3 mass % of copper.
- the content of iron in the aluminum alloy of the embodiment containing one or more secondary elements is more than 0% by mass and 0.8% by mass or less.
- the content of chromium is more than 0% by mass and 0.35% by mass or less.
- the zinc content is more than 0% by mass and 0.5% by mass or less.
- the content of titanium is more than 0% by mass and 0.2% by mass or less.
- the content of zirconium is more than 0% by mass and 0.2% by mass or less.
- the content of the first element is equal to or higher than the above-mentioned lower limit, compounds containing the first element are precipitated in the state after heat treatment. Since precipitates such as the above compounds are present in a dispersed state, an effect of improving strength by precipitation hardening can be obtained. When part of the first element is dissolved in aluminum, which is the main constituent of the matrix phase, the effect of improving strength by solid solution strengthening is also obtained.
- the content of the first element is equal to or less than the above-described upper limit, grain boundary embrittlement due to segregation of the first element is suppressed, and compounds containing the first element are less likely to coarsen. Particles such as coarse compounds can be starting points of cracks.
- the aluminum alloy of the embodiment has a high tensile strength after heat treatment. In the manufacturing process, cracks due to the coarse particles are less likely to occur, so cold plastic working such as cold wire drawing can be performed satisfactorily. From this point, the aluminum alloy of the embodiment is also excellent in manufacturability.
- the aluminum alloy of the embodiment containing the second element in addition to the first element tends to have higher tensile strength after heat treatment.
- the content ratio of the second element satisfies the upper limit range described above, the compound or the like containing the second element is less likely to become coarse.
- the cast material can have a fine structure. From these points, the aluminum alloy of the embodiment containing the second element in addition to the first element is excellent in workability when plastic working is included in the manufacturing process. The casting temperature can be lowered depending on the type of the second element. From these points, the aluminum alloy of the embodiment containing the second element in addition to the first element is superior in manufacturability.
- the first composition contains 1.0% by mass to 1.3% by mass of silicon, 0.5% by mass to 1.2% by mass of magnesium, 0.3% by mass to 0.8% by mass of iron, 0.1% by mass or more and 0.4% by mass or less of copper, 0.2% by mass or more and 0.5% by mass or less of manganese, 0.3% by mass or more of chromium, and 0.001% by mass of titanium 0.1% by mass or less, 0% by mass or more and 0.2% by mass or less of zirconium, and the balance being aluminum and unavoidable impurities.
- the second composition contains 0.6% to 1.5% by mass of silicon, 0.7% to 1.3% by mass of magnesium, 0.02% to 0.4% by mass of iron, 0.5 to 1.2% by mass of copper, 0.5 to 1.1% by mass of manganese, more than 0 to 0.3% by mass of chromium, and 0.005% by mass of zinc 0.5% by mass or less, 0.01% by mass or more and 0.2% by mass or less of titanium, 0.05% by mass or more and 0.2% by mass or less of zirconium, and the balance being aluminum and unavoidable impurities.
- the second composition may further contain 0.005 mass % or more and 0.05 mass % or less of strontium.
- the third composition contains 0.9% by mass to 1.3% by mass of silicon, 0.8% by mass to 1.2% by mass of magnesium, more than 0% by mass and 0.4% by mass or less of iron, and copper 0.65% by mass or more and 1.1% by mass or less, manganese of 0.55% by mass or more and 1.15% by mass or less, chromium of 0% by mass or more and 0.35% by mass or less, zinc of 0.12% by mass or more and 0 0.075% by mass or less of titanium, 0.05% by mass or more and 0.17% by mass or less of zirconium, and the balance being aluminum and inevitable impurities.
- the third composition roughly corresponds to the composition of the alloy indicated by the international alloy symbol A6056.
- the silicon content may be more than 1.0% by mass and 1.3% by mass or less, or 1.1% by mass or more and 1.3% by mass or less.
- the content of magnesium may be 0.6% by mass or more and 1.1% by mass or less, or 0.7% by mass or more and 1.0% by mass or less.
- the content of iron may be 0.3% by mass or more and 0.7% by mass or less, or 0.3% by mass or more and 0.6% by mass or less.
- the content of copper may be 0.2% by mass or more and 0.4% by mass or less.
- the content of manganese may be 0.2% by mass or more and 0.4% by mass or less, or 0.2% by mass or more and 0.3% by mass or less.
- the content of chromium may be 0.005% by mass or more and 0.20% by mass or less, or 0.01% by mass or more and 0.10% by mass or less.
- the content of titanium may be 0.005% by mass or more and 0.05% by mass or less, or 0.01% by mass or more and 0.05% by mass or less.
- zirconium is included, the content of zirconium may be 0.001% by mass or more and 0.20% by mass or less, or 0.005% by mass or more and 0.10% by mass or less.
- the total content of titanium and zirconium may be 0.01% by mass or more and 0.10% by mass or less.
- the content of silicon may be 0.8% by mass or more and 1.4% by mass or less, or 1.1% by mass or more and 1.3% by mass or less.
- the content of magnesium may be 0.8% by mass or more and 1.3% by mass or less, or 0.8% by mass or more and 1.0% by mass or less.
- the iron content may be 0.05% by mass or more and 0.40% by mass or less.
- the content of copper may be 0.8% by mass or more and 1.2% by mass or less.
- the manganese content may be 0.7% by mass or more and 1.1% by mass or less.
- the content of chromium may be 0.01% by mass or more and 0.30% by mass or less, or 0.05% by mass or more and 0.30% by mass or less.
- the content of zinc may be 0.05% by mass or more and 0.25% by mass or less.
- the content of titanium may be 0.01% by mass or more and 0.15% by mass or less.
- the content of zirconium may be 0.08% by mass or more and 0.2% by mass or less.
- the total content of titanium and zirconium may be 0.10% by mass or more and 0.20% by mass or less.
- strontium When strontium is included, the content of strontium may be 0.005% by mass or more and 0.04% by mass or less.
- the silicon content may be 0.9% by mass or more and 1.2% by mass or less.
- the content of magnesium may be 0.8% by mass or more and 1.0% by mass or less.
- the content of iron may be 0.10% by mass or more and 0.25% by mass or less.
- the content of copper may be 0.65% by mass or more and 0.85% by mass or less.
- the content of manganese may be 0.55% by mass or more and 0.80% by mass or less, or 0.55% by mass or more and 0.65% by mass or less.
- the content of chromium may be 0.01% by mass or more and 0.10% by mass or less, or 0.02% by mass or more and 0.05% by mass or less.
- the content of zinc may be 0.13% by mass or more and 0.25% by mass or less.
- the content of titanium may be 0.001% by mass or more and 0.075% by mass or less, or 0.01% by mass or more and 0.075% by mass or less.
- the content of zirconium may be 0.10% by mass or more and 0.17% by mass or less.
- the total content of titanium and zirconium may be 0.11% by mass or more and 0.20% by mass or less.
- the aluminum alloy of the embodiment may further include boron in the range of 50 ppm by mass or less.
- an aluminum alloy having high tensile strength after heat treatment preferably has the following structure. It is preferable that the 111 planes of the crystal grains are more oriented than the other crystal planes of the crystal grains over the entire cross section of the aluminum alloy. In other words, it is preferable that most of the crystal grains forming the cross section of the aluminum alloy have the 111 plane orientation.
- the average value of the degree of orientation of the 111 plane obtained by X-ray diffraction of the entire cross section after heat treatment is 50% or more. Further, the dispersion of the degree of orientation of the 111 plane is 45% or less.
- the 111 plane is oriented in the normal direction of the cross section in more than half of the crystal grains forming the cross section of the aluminum alloy. If the distribution of the degree of orientation of the 111 plane is 45% or less, the distribution of the oriented crystal planes among the crystal grains forming the cross section of the aluminum alloy is concentrated on the 111 plane.
- the aluminum alloy of such an embodiment has a high orientation of the 111 plane of crystal grains. In general, the higher the orientation of the 111 planes of the crystal grains of an aluminum alloy, the higher the tensile strength. Accordingly, the aluminum alloys of the embodiments have high tensile strength in the post-heat treatment state.
- the average value of the degree of orientation of the 111 plane may be 55% or more, further 60% or more.
- the distribution of the degree of orientation of the 111 plane may be 40% or less, and may be 38% or less.
- the average value of the degree of orientation of the 111 plane is 50% or more and 100% or less.
- the distribution of the degree of orientation of the 111 plane is more than 0% and 45% or less. Considering manufacturability, the average value of the degree of orientation of the 111 plane may be 99% or less, and the dispersion of the degree of orientation of the 111 plane may be 1% or more.
- the orientation of the 111 plane of the crystal grains is evaluated not only in part of the cross section but in the entire cross section.
- the aluminum alloys of the embodiments certainly have a higher strength structure in the post-heat treatment state than if only a portion of the cross-section was evaluated.
- the cross section to be measured for the degree of orientation of the 111 plane is a cross section cut along a plane perpendicular to the longitudinal direction at an arbitrary position in the longitudinal direction of the wire rod.
- a cross section cut along a plane perpendicular to the longitudinal direction of the wire made of the aluminum alloy of the embodiment, that is, the aluminum alloy wire 1 of the embodiment may be referred to as a cross section.
- the 111 plane of the crystal grains is more oriented than the other crystal planes in the entire cross section as described above.
- the orientation direction of the 111 plane in each cross section is the normal direction of the cross section, that is, the direction along the longitudinal direction of the wire. Such a wire is difficult to break even when pulled in the longitudinal direction of the wire.
- the average value of the orientation degree of the 111 plane is 50% or more even in the state where the aging treatment is not performed.
- the dispersion of the degree of orientation is 45% or less. That is, it is considered that the orientation of the 111 plane of the crystal grains does not substantially change before and after the aging treatment.
- the aluminum alloy of the embodiment has, for example, a tensile strength of more than 425 MPa at room temperature after heat treatment.
- the normal temperature here is 5° C. or higher and 35° C. or lower.
- the aluminum alloy of the embodiment having a tensile strength of more than 425 MPa is excellent in strength.
- the aluminum alloy of the embodiment having a tensile strength of more than 427 MPa, 430 MPa or more, or even 440 MPa or more is superior in strength.
- the aluminum alloy of the embodiment has a high tensile strength of 450 MPa or more, 460 MPa or more, and further 470 MPa or more.
- the tensile strength at room temperature may be, for example, more than 425 MPa and 550 MPa or less.
- the aluminum alloys of embodiments can have various shapes.
- the aluminum alloys of the embodiments have somewhat long shapes.
- the aluminum alloy of such an embodiment has an end surface which is a plane perpendicular to its longitudinal direction and an extension extending in the longitudinal direction.
- the length of the extension along the longitudinal direction is greater than the diameter of a circle having an area equal to the area of the outer contour of the end face.
- the cross section to be measured for the degree of orientation of the 111 plane is obtained by cutting the stretched portion along a plane perpendicular to the longitudinal direction.
- the aluminum alloy of the embodiment having an extended portion is, for example, a wire rod, a pipe, a plate material, or the like. That is, the extending portion may be a solid body such as a wire rod or a plate material, or a hollow body such as a pipe.
- An aluminum alloy wire 1 of the embodiment is made of the aluminum alloy of the embodiment.
- the aluminum alloy wire 1 of the embodiment has an end surface 10 and an extension portion 11 as shown in FIG.
- the end surface 10 here is a surface perpendicular to the longitudinal direction of the aluminum alloy wire 1 .
- the extending portion 11 extends in the longitudinal direction.
- the aluminum alloy wire 1 of the embodiment typically has the same outer contour and the same wire diameter over the entire length of the extended portion 11 as shown in FIG.
- the wire diameter here is the diameter of a circle having the same area as the area of the end face 10 or the area of a cross section cut along a plane perpendicular to the longitudinal direction.
- the wire diameter of the aluminum alloy wire 1 of the embodiment is not particularly limited.
- the wire diameter is, for example, about 3 mm or more and 15 mm or less.
- the cross section to be measured for the degree of orientation of the 111 plane is the cross section.
- the average value of the degree of orientation of the 111 plane obtained by X-ray diffraction of the entire cross section is 50% or more. Further, the dispersion of the degree of orientation of the 111 plane is 45% or less.
- such cross sections are arranged in the longitudinal direction.
- the aluminum alloy wire 1 of such an embodiment has a high tensile strength of over 425 MPa in the state after heat treatment.
- the aluminum alloy of the embodiment can constitute an aluminum alloy member.
- the aluminum alloy member is made of the aluminum alloy of the embodiment and subjected to solution treatment and aging treatment.
- a specific example is an aluminum alloy member obtained by subjecting the aluminum alloy wire 1 of the embodiment to plastic working, followed by solution treatment and aging treatment.
- Another example is an aluminum alloy member obtained by subjecting a plate material made of the aluminum alloy of the embodiment to plastic working, followed by solution treatment and aging treatment. The plastic working here is performed so that the cross section of the aluminum alloy member has the specific orientation described above after the solution treatment and the aging treatment.
- Still another example is an aluminum alloy member obtained by subjecting the aluminum alloy wire 1 of the embodiment to solution treatment and aging treatment. That is, the aluminum alloy member may be linear or bar-shaped. Alternatively, the aluminum alloy member may be tubular.
- the aluminum alloy member is made of an extruded material obtained by extruding the aluminum alloy wire 1 with the longitudinal direction of the aluminum alloy wire 1 of the embodiment as the extrusion direction.
- This aluminum alloy member extends along the extrusion direction.
- the cross section to be measured for the degree of orientation of the 111 plane is obtained by cutting the aluminum alloy member along a plane perpendicular to the extrusion direction.
- the average value of the degree of orientation of the 111 plane obtained by X-ray diffraction of the entire cross section is 50% or more. Further, the dispersion of the degree of orientation of the 111 plane is 45% or less.
- the aluminum alloy member described above has high strength because it is made of an aluminum alloy having the above-described specific composition and the above-described specific structure. Moreover, this aluminum alloy member is lighter than a metal member made of an iron-based alloy such as steel. Such aluminum alloy members can be used in applications where light weight and high strength are desired, such as automobile parts and various structural members.
- the inventors of the present invention have investigated a method for producing an aluminum alloy having the specific composition described above and having excellent strength when subjected to solution treatment and aging treatment. As a result, the inventors of the present invention have found that it is preferable that the plastic working performed immediately after the solution treatment be cold working and have a large degree of working. Based on this knowledge, when manufacturing the aluminum alloy of the embodiment, for example, the following method for manufacturing an aluminum alloy can be used.
- a method for producing an aluminum alloy includes a step of cold working a raw material made of an aluminum alloy to produce a cold-worked material.
- the above-mentioned aluminum alloy has a composition containing the above-mentioned first element within the above-mentioned range, with the balance being aluminum and unavoidable impurities.
- the above material is a worked material that has undergone the first plastic working.
- the cold working is the second plastic working with a degree of working of 20% or more.
- the aluminum alloy may have a composition containing the second element within the above range in addition to the above first element.
- Dislocations are released more easily in hot working and warm working than in cold working.
- strains, ie, dislocations, associated with the second plastic working tend to accumulate in the aluminum alloy as compared with warm working or hot working.
- the more dislocations are accumulated the easier it is for the 111 planes of the crystal grains to be oriented during the subsequent solution treatment.
- a structure in which many 111 planes of crystal grains are oriented in the entire cross section of the aluminum alloy is obtained in a state where solution treatment and aging treatment are performed as described above.
- the raw material made of the aluminum alloy described above is a cast material subjected to the first plastic working.
- the first plastic working is, for example, rolling.
- the first plastic working is, for example, hot working.
- the materials described above can be subjected to a softening treatment under the following conditions.
- the softening treatment applied to the material may be referred to as initial softening treatment.
- the heating temperature is a temperature selected from the range of 250°C or higher and lower than 500°C.
- the retention time is a time selected from the range of 1 hour or more and 100 hours or less.
- the softening atmosphere is, for example, an air atmosphere or a non-oxidizing atmosphere.
- the non-oxidizing atmosphere is, for example, a reduced pressure atmosphere, an inert gas atmosphere, a reducing gas atmosphere, or the like.
- the heating temperature may be 300° C. or higher and 480° C. or lower, and further 300° C. or higher and 460° C. or lower.
- the plastic workability of the aluminum alloy after the initial softening treatment is enhanced. Therefore, the workability of the second plastic working can be increased. If the initial softening treatment is not applied to the material, dislocations introduced by the first plastic working are accumulated in the aluminum alloy. As a result, it is easy to obtain an aluminum alloy in which many dislocations are accumulated.
- the second plastic working applied to the material is cold working as described above.
- the second plastic working is, for example, wire drawing, rolling, extrusion, or the like. If the second plastic working is wire drawing, a wire is obtained. If the second plastic working is rolling, a plate material is typically obtained. If the second plastic working is extrusion, wire rods, plate materials, pipes and the like can be obtained depending on the shape of the extrusion die.
- ⁇ Processing degree The higher the working degree of the second plastic working, the higher the orientation of the 111 plane. From the viewpoint of improving the strength, the workability of the second plastic working may be 30% or more, 40% or more, or 60% or more.
- the workability here is a ratio obtained by dividing the difference between the cross-sectional area before the second plastic working and the cross-sectional area after the second plastic working by the cross-sectional area before the second plastic working.
- a softening treatment can be applied during the second plastic working.
- the softening treatment performed during the second plastic working may be referred to as an intermediate softening treatment.
- the conditions of the intermediate softening treatment it is preferable to refer to the conditions of the initial softening treatment described above.
- the working degree in the cold working after the intermediate softening treatment is preferably larger than the working degree in the cold working before the intermediate softening treatment.
- the degree of cold working after the intermediate softening treatment may be 30% or more, 40% or more, or even 60% or more.
- the method for manufacturing an aluminum alloy wire of the embodiment includes the following first step, second step, third step, and fourth step.
- ⁇ conditions> Cold drawing is performed.
- a softening treatment is performed during wire drawing.
- the workability of the wire drawing after the softening treatment is 20% or more and is greater than the workability of the wire drawing before the softening treatment.
- the first step is a step of manufacturing a processed material by subjecting a cast material of an aluminum alloy containing the first element in the above range and the balance being aluminum and inevitable impurities to plastic working.
- the aluminum alloy forming the cast material may further contain the second element within the range described above.
- the second step is a step of manufacturing the first drawn wire material by subjecting the worked material to the first cold wire drawing process.
- the third step is a step of manufacturing a softened material by subjecting the first drawn wire material to a softening treatment.
- the fourth step is a step of manufacturing a second drawn wire material by subjecting the softened material to a second cold wire drawing process.
- the workability in the second wire drawing is 20% or more.
- the degree of working in the second wire drawing is greater than the degree of working in the first wire drawing.
- the plastic working of the first step corresponds to the first plastic working described above.
- the softening treatment in the third step corresponds to the intermediate softening treatment described above.
- the first wire drawing and the second wire drawing correspond to the second plastic working described above.
- the method for manufacturing an aluminum alloy wire according to the embodiment in the method for manufacturing an aluminum alloy wire according to the embodiment, as described above, cold wire drawing is performed before and after the softening treatment, so that dislocations are accumulated in the aluminum alloy as compared with the case where warm working or hot working is performed. easy. Further, by performing the softening treatment, it is possible to increase the workability of the second wire drawing after the softening treatment as described above. Therefore, dislocations can be accumulated in the aluminum alloy by the second wire drawing after the softening treatment.
- the aluminum alloy wire manufacturing method of such an embodiment can manufacture the aluminum alloy wire 1 of the embodiment.
- a material made of an aluminum alloy having a specific composition is excellent in cold wire drawability.
- the aluminum alloy wire manufacturing method of the embodiment using such a material can mass-produce the aluminum alloy wire 1 of the embodiment.
- the cast material is manufactured using, for example, a die casting method, a continuous casting method, or the like.
- the plastic working is, for example, hot rolling, and the material to be worked is, for example, continuously cast and rolled material. If the processed material is a continuously cast rolled material, a continuous long aluminum alloy wire can be produced.
- the aluminum alloy wire 1 of the embodiment can be mass-produced when the processed material is a continuously cast and rolled material.
- the above-mentioned initial softening treatment can be applied to the processed material.
- the initial softening treatment it is possible to increase the degree of working in the subsequent first wire drawing as described above.
- the initial softening treatment is not performed, an aluminum alloy wire in which a large amount of dislocations are finally accumulated tends to be obtained as described above.
- the workability of the first wire drawing is preferably 30% or more. If the workability of the first wire drawing is 30% or more, the dislocations introduced by the first wire drawing tend to remain to some extent after the softening treatment. As a result, it is easy to finally obtain an aluminum alloy wire in which many dislocations are accumulated.
- the working ratio of the first wire drawing may be 35% or more, or 40% or more.
- the working ratio of the first wire drawing is selected from a range of, for example, 30% or more and 80% or less, although it depends on the final wire diameter.
- the working degree of the first wire drawing is a ratio obtained by dividing the difference between the cross-sectional area before the first wire drawing and the cross-sectional area after the first wire drawing by the cross-sectional area before the first wire drawing.
- the conditions of the softening treatment in the third step the conditions of the initial softening treatment described above may be referred to.
- the working degree of the second wire drawing in the fourth step can be increased.
- the working degree of the second wire drawing in the fourth step can be made larger than the working degree of the first wire drawing in the second step. As a result, dislocations can be accumulated in the aluminum alloy by the second wire drawing.
- ⁇ Fourth step> The higher the workability of the second wire drawing in the fourth step, the higher the orientation of the 111 plane. If the workability of the second wire drawing is 20% or more, it is easy to finally obtain an aluminum alloy wire in which many dislocations are accumulated. Since the working degree of the second wire drawing is higher than the working degree of the first wire drawing, it is easy to finally obtain an aluminum alloy wire in which many dislocations are accumulated. As described above, the working ratio of the first wire drawing is preferably 30% or more, so the working ratio of the second wire drawing may be more than 30%, 40% or more, or even 60% or more.
- the working ratio of the second wire drawing is selected from the range of 20% or more and 99.9% or less so that a second wire drawing having a predetermined final wire diameter can be obtained.
- the working degree of the second wire drawing is a ratio obtained by dividing the difference between the cross-sectional area before the second wire drawing and the cross-sectional area after the second wire drawing by the cross-sectional area before the second wire drawing.
- a method for manufacturing the aluminum alloy member described above includes, for example, the following processing steps and heat treatment steps.
- the working step is a step of manufacturing the third worked material by applying the third plastic working to the second plastic working material subjected to the second plastic working or the second drawn wire material.
- the heat treatment step is a step of sequentially subjecting the third processed material to solution treatment and aging treatment to produce an aged material.
- the third plastic processing includes, for example, extrusion processing, forging processing, wire drawing processing, and the like.
- the conditions for solution treatment and aging treatment are as described above.
- the aluminum alloy of the embodiment and the aluminum alloy wire 1 of the embodiment have high tensile strength in the state of being subjected to solution treatment and aging treatment.
- Test Example 1 the above effect will be specifically described by taking the aluminum alloy wire 1 of the embodiment as an example.
- the manufacturing method of the aluminum alloy wire of the embodiment can manufacture the aluminum alloy wire 1 of the embodiment having a high tensile strength in a state of solution treatment and aging treatment.
- Test Example 1 The structures of the aluminum alloy wires having the compositions shown in Table 1 were subjected to solution treatment and aging treatment, and the tensile strength was examined. Tables 2 to 4 show the conditions for manufacturing the aluminum alloy wires and the results of the investigation.
- the aluminum alloy wire of each sample is basically produced by cold drawing a continuously cast and rolled material.
- a continuously cast rolled material can be produced by, for example, a known Propertit type continuous casting and rolling mill. Except for some of the samples, softening treatment is performed during the wire drawing process.
- the first composition, second composition, and third composition in the item of composition correspond to the first composition, second composition, and third composition shown in Table 1, respectively.
- the item of softening treatment indicates heating temperature (° C.) and holding time (hour). For example, "380° C. ⁇ 10 h" means that the heating temperature is 380° C. and the holding time is 10 hours.
- Tables 2 to 4 the samples whose conditions are described in the three items of working degree (%) of the first wire drawing, softening treatment, and working degree (%) of the second wire drawing will be described.
- the aluminum alloy wires of these samples are manufactured by sequentially subjecting a continuously cast rolled material to a first cold drawing process, a softening treatment, and a second cold drawing process. The aluminum alloy wires of these samples were not subjected to initial softening treatment.
- a hyphen "-" is described in the working degree (%) of the first wire drawing, and the conditions are described in the two items of the softening treatment and the working degree (%) of the second wire drawing. I will explain the sample that was made.
- the aluminum alloy wires of these samples are manufactured by applying a softening treatment to the continuously cast and rolled material, and then applying a cold wire drawing process at the reduction ratio (%) of the second wire drawing process.
- the aluminum alloy wires of these samples were continuously subjected to cold wire drawing after being subjected to initial softening treatment of continuously cast and rolled material, and were not subjected to intermediate softening treatment.
- Tables 2 to 4 the conditions are described in two items, the working degree (%) of the first wire drawing and the working degree (%) of the second wire drawing, and the softening treatment is indicated by a hyphen "-". I will explain the sample that was made.
- the aluminum alloy wires of these samples were obtained by subjecting the continuously cast and rolled material to cold wire drawing at the degree of reduction (%) of the first wire drawing, and then to the second drawing without intermediate softening treatment. It is manufactured by applying cold wire drawing with a working degree (%) of wire working.
- the aluminum alloy wires of these samples were obtained by continuous cold drawing of continuously cast and rolled materials, and were not subjected to both initial softening and intermediate softening.
- the total working ratio in this cold wire drawing is larger than the working ratio described in the item of working ratio (%) in the second wire drawing in Tables 2 to 4.
- the wire diameter of the continuously cast rolled material is selected from the range of 5 mm or more and 30 mm or less.
- the wire diameter of the second drawn wire manufactured after the second wire drawing is a value selected from the range of approximately 1.0 mm or more and 21 mm or less depending on the degree of working.
- the obtained aluminum alloy wire of each sample is subjected to solution treatment and aging treatment under the conditions described above to produce a heat treated wire.
- a disc-shaped sample is obtained by cutting the obtained heat-treated wire along a plane perpendicular to the longitudinal direction of the heat-treated wire.
- the sample has two circular cross-sections. The entire area of one of the two cross-sections is smoothed by mechanical polishing.
- the surface roughness of the cross section after polishing is about 0.2 ⁇ m in terms of arithmetic mean roughness Ra.
- 2000 water resistant paper can be used for mechanical polishing.
- X-ray diffraction is performed across the polished cross section as follows.
- the sample 3 is placed on a flat surface 51f provided on the movable stage 51 .
- This arrangement is performed so that the mechanically polished cross section 30 of the sample 3 is parallel to the surface 51f, and the cross section 30 is irradiated with X-rays 6 from a predetermined direction D.
- a predetermined direction D is a direction corresponding to a predetermined plane index F.
- FIG. The given plane index F is the crystal plane identified by the Miller indices.
- the plane index F is any one of the 111 plane, 200 plane, and 220 plane.
- X-rays 6 from an X-ray source (not shown) and diffracted X-rays 60 are indicated by dashed lines.
- the X-rays 60 diffracted from the cross section 30 are detected by the detector 52 .
- the X-rays 60 are detected repeatedly while the sample 3 is two-dimensionally moved in a plane parallel to the cross section 30 by the movable stage 51 so that the entire cross section 30 is measured. In this way, the distribution of diffraction intensity over the entire cross section 30 is obtained. Note that the X-ray 6 does not move when the sample 3 is moved two-dimensionally. Further, the arithmetic unit 53, which will be described later, is set so as to exclude the diffraction intensity from a position where the cross section 30 does not exist.
- the diffraction intensity distribution of the 111th plane, the 200th plane, and the 220th plane are obtained.
- the angle ⁇ is the angle formed by the plane index F and the X-ray 6 .
- the angle 2 ⁇ is the angle between the given direction D and the diffracted X-ray 60 .
- a theoretical value based on a predetermined direction D is used to calculate a normalized value of each diffraction intensity.
- the normalized value is a value obtained by dividing each diffraction intensity by the theoretical value of the peak intensity of X-ray diffraction.
- a normalized distribution is calculated from the distribution of each diffraction intensity using the normalized values.
- the normalized distribution of the 111th plane, the normalized distribution of the 200th plane, and the normalized distribution of the 220th plane are calculated.
- the above theoretical values may be obtained from the PDF (Powder Diffraction File) database published by ICDD (International Center for Diffraction Data).
- the peak intensity may be obtained by fitting the X-ray profile data at each measurement point and using the maximum value or integrated value of this fitting curve instead of the peak intensity of the raw data. Fitting functions used in the above fitting are, for example, the Lorentz function and the Gauss function.
- the normalized value of the diffraction intensity on the 111th surface, the normalized value of the 200th surface diffraction intensity, and the normalized value of the 220th surface diffraction intensity are obtained. Furthermore, the sum of these three normalized values is obtained. Furthermore, the ratio of the value obtained by normalizing the diffraction intensity of the 111 plane to the total value is calculated. This ratio is the degree of orientation of the 111 plane.
- the average value of the degree of orientation of the 111 plane is the average value of the degree of orientation of the 111 plane at all measurement points. The dispersion of the degree of orientation of the 111 plane is obtained from the above averaged value.
- X-ray 6 for example, BL16 existing in the synchrotron radiation facility SAGA-LS can be used.
- a slit width of, for example, 0.5 mm square can be used.
- the detector 52 for example, a commercially available two-dimensional detector, PILATUS 100K by Dectris can be used. The distance from the cross section 30 of the sample 3 to the two-dimensional detector is 0.512 m.
- a commercially available computer can be used as the arithmetic unit 53 .
- the angles .theta. and 2.theta. are selected according to the wavelengths mentioned above.
- the angles ⁇ and 2 ⁇ are the following values when ⁇ is 0.0919 nm, for example.
- the predetermined plane index F is the 111 plane
- the angle ⁇ between the 111 plane of the sample 3 and the X-ray 6 is 11.3 degrees.
- the angle 2 ⁇ between the predetermined direction D and the diffracted X-ray 60 is 22.6 degrees.
- FIG. 6 shows ⁇ and 2 ⁇ larger than their actual values.
- the predetermined plane index F is the 200th plane
- the angle ⁇ between the 200th plane of the sample 3 and the X-ray 6 is 13 degrees.
- the angle 2 ⁇ between the predetermined direction D and the diffracted X-ray 60 is 26 degrees.
- the angle ⁇ between the 220th plane of the sample 3 and the X-ray 6 is 18.6 degrees.
- the angle 2 ⁇ between the predetermined direction D and the diffracted X-ray 60 is 37.2 degrees.
- Tensile strength (MPa) is measured according to JIS Z 2241:2011. Here, the tensile strength at room temperature is measured.
- composition of the aluminum alloy wire of each sample obtained is the same as the composition in Table 1. That is, the aluminum alloy constituting the aluminum alloy wire of each sample contains the elements shown in Table 1 within the range shown in Table 1, and the balance is Al and unavoidable impurities.
- a known method can be used to analyze the composition of the aluminum alloy wire. For example, an energy dispersive X-ray spectrometer or the like can be used to analyze the composition.
- sample No. 1 to sample no. 9, No. 11 to No. 19, No. 21 to No. 29 may be collectively referred to as the first sample group.
- Sample no. 101 to No. 104 may be collectively referred to as a second sample group.
- the aluminum alloy wires of the first sample group have higher tensile strength than the aluminum alloy wires of the second sample group.
- the aluminum alloy wire of the first sample group has a tensile strength of over 425 MPa.
- Many samples have a tensile strength of 440 MPa or higher.
- Some samples have a high tensile strength of 470 MPa or more depending on the composition.
- the average value of the degree of orientation of the 111 plane is larger and the dispersion of the degree of orientation of the 111 plane is smaller than that of the aluminum alloy wire of the second sample group.
- the average value of the degree of orientation of the 111 plane is 50% or more, and the dispersion of the degree of orientation of the 111 plane is 45% or less.
- Many of the samples have an average value of 60% or more of the degree of orientation of the 111 plane and a dispersion of the degree of orientation of the 111 plane of 35% or less.
- the average value of the degree of orientation of the 111 plane is 70% or more and the dispersion of the degree of orientation of the 111 plane is 30% or less. This will be explained visually with reference to FIGS. 2 to 5.
- FIG. 2 and 3 are for sample no. 3 shows the distribution of the degree of orientation of the 111 plane for the aluminum alloy wire of No. 3.
- 4 and 5 are for sample no. 1 shows the orientation distribution of the 111 plane for the aluminum alloy wire of No. 1.
- FIG. 2 and 4 are diagrams obtained by converting the degree of orientation of the 111 plane for each of the above-described measurement points into grayscale shading over the entire cross section of the aluminum alloy wire.
- the bars shown on the right side of FIG. 2 and the right side of FIG. 4 show gradation according to the count number.
- the degree of orientation of the 111 plane at each measurement point is converted into a count number from zero to 100, for example. Black means zero counts. White means that the count number is 100.
- the greater the degree of orientation of the 111 plane the greater the count number, that is, the closer to white.
- Figures 3 and 5 show the distribution of the degree of orientation of the 111 plane by contour lines. Each contour line connects measurement points where the degree of orientation of the 111 plane is the same. 2 and 4 show the following four types of contour lines.
- a thin solid line is a contour line connecting measurement points where the degree of orientation of the 111 plane is 20%.
- a thin dashed line is a contour line connecting measurement points where the degree of orientation of the 111 plane is 40%.
- a thin dotted line is a contour line connecting measurement points where the degree of orientation of the 111 plane is 60%.
- a thick solid line is a contour line connecting measurement points at which the degree of orientation of the 111 plane is 80%.
- Sample No. with a high tensile strength of 470 MPa In the aluminum alloy wire No. 3, as shown in FIG. 2, there are many white measurement points, some light gray measurement points, and almost no black measurement points. That is, there are many measurement points with large counts, and the variation in the counts is small. The fact that there are many measurement points with large counts is also supported by the fact that the area surrounded by the thick solid line has a large area as shown in FIG. Here, the shape and size of the region enclosed by the thick solid line are those of sample No. The shape and size of the cross section of the aluminum alloy wire of No. 3 are fairly close to each other. In addition, almost no other area surrounded by contour lines is included in this area having a large area.
- this test shows the following. (1) The aluminum alloy wire having the first composition and the second composition tends to have a larger average value of the degree of orientation of the 111 plane and a smaller dispersion of the degree of orientation of the 111 plane than the aluminum alloy wire having the third composition. . From this point of view, the aluminum alloy wire having the first composition and the second composition has higher strength.
- An aluminum alloy wire having a large average value of the degree of orientation of the 111 plane and a small dispersion of the degree of orientation of the 111 plane in the state of being subjected to solution treatment and aging treatment is a manufacturing method that satisfies the above ⁇ conditions>.
- the workability of the second wire drawing is smaller than that of the aluminum alloy wires of the first sample group.
- the working degree of the second wire drawing is smaller than the working degree of the first wire drawing or the same as the working degree of the first wire drawing. From these facts, it is considered that dislocations are not sufficiently accumulated in the aluminum alloy wires of the second sample group after the second wire drawing.
- Test Example 1 it is possible to change the composition of the aluminum alloy, or to change the manufacturing conditions such as the workability of wire drawing and the conditions of softening treatment.
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Abstract
Description
本出願は、2021年5月27日付の日本国出願の特願2021-089504に基づく優先権を主張し、前記日本国出願に記載された全ての記載内容を援用するものである。 The present disclosure relates to aluminum alloys, aluminum alloy wires, and methods of manufacturing aluminum alloy wires.
This application claims priority based on Japanese Patent Application No. 2021-089504 filed in Japan on May 27, 2021, and incorporates all the content described in the Japanese application.
上述のように溶体化処理及び時効処理が施された状態で使用されるアルミニウム合金部材には更なる強度の向上が望まれている。また、このような高強度なアルミニウム合金部材を構成することができるアルミニウム合金が望まれている。 [Problems to be Solved by the Present Disclosure]
Further improvement in strength is desired for aluminum alloy members that are used after being subjected to solution treatment and aging treatment as described above. Further, an aluminum alloy that can constitute such a high-strength aluminum alloy member is desired.
本開示のアルミニウム合金及び本開示のアルミニウム合金線は溶体化処理及び時効処理が施された状態において高強度である。本開示のアルミニウム合金線の製造方法は、本開示のアルミニウム合金線を製造できる。 [Effect of the present disclosure]
The aluminum alloy of the present disclosure and the aluminum alloy wire of the present disclosure have high strength in the solution treated and aged condition. The aluminum alloy wire manufacturing method of the present disclosure can manufacture the aluminum alloy wire of the present disclosure.
最初に本開示の実施態様を列記して説明する。
(1)本開示の一態様に係るアルミニウム合金は、シリコンを0.6質量%以上1.5質量%以下、マグネシウムを0.5質量%以上1.3質量%以下、銅を0.1質量%以上1.2質量%以下、マンガンを0.2質量%以上1.15質量%以下含み、残部がアルミニウム及び不可避不純物からなる組成を備える。このアルミニウム合金では溶体化処理及び時効処理が施された状態において断面の全域をX線回折して求められた111面の配向度の平均値が50%以上であり、前記111面の配向度の分散が45%以下である。 [Description of Embodiments of the Present Disclosure]
First, the embodiments of the present disclosure are listed and described.
(1) The aluminum alloy according to one aspect of the present disclosure contains 0.6% by mass or more and 1.5% by mass or less of silicon, 0.5% by mass or more and 1.3% by mass or less of magnesium, and 0.1% by mass of copper. % or more and 1.2 mass % or less, manganese of 0.2 mass % or more and 1.15 mass % or less, and the balance being aluminum and unavoidable impurities. In this aluminum alloy, the average value of the degree of orientation of the 111 plane obtained by X-ray diffraction of the entire cross section in a state of being subjected to solution treatment and aging treatment is 50% or more, and the degree of orientation of the 111 plane is 50% or more. Dispersion is 45% or less.
本開示においてアルミニウム合金の断面は例えば以下の断面である。アルミニウム合金が線、パイプ、板等のようにある程度長い形状を有する場合、上記断面はアルミニウム合金の長手方向に直交する平面で切断した断面である。
本開示において溶体化処理の条件及び時効処理の条件は以下の通りである。
(溶体化処理の条件)
加熱温度は530℃以上580℃以下の範囲から選択される温度である。加熱時間は15分以上120分以下の範囲から選択される時間である。
(時効処理の条件)
加熱温度は150℃以上180℃以下の範囲から選択される温度である。加熱時間は4時間以上100時間以下の範囲から選択される時間である。 The 111 plane in this disclosure means the crystal plane denoted as (111) in crystallography. The degree of orientation of the 111 plane in the present disclosure is determined using values obtained by normalizing the following three diffraction intensities obtained by X-ray diffraction over the entire cross section. The degree of orientation of the 111 plane in the present disclosure is the ratio of the normalized value of the diffraction intensity of the 111 plane to the total value of the three normalized values. The three diffraction intensities are the diffraction intensity on the 111th plane, the diffraction intensity on the 200th plane, and the diffraction intensity on the 220th plane. The 200 plane and 220 plane mean crystal planes denoted as (200) and (220) in crystallography. The average value of the degree of orientation of the 111 planes in the present disclosure is the average value of the above ratios at each measurement point over the entire cross section. The dispersion of the degree of orientation of the 111 plane in the present disclosure is a value obtained from the above average value. A method for measuring the average value and dispersion of the orientation degree of the 111 planes in the present disclosure will be described later. In the measurement method described later, the entire cross section is subjected to X-ray diffraction measurement, and the orientation state of the 111 plane is specified using the value obtained by normalizing the diffraction intensity. can appropriately evaluate the degree of orientation of
In the present disclosure, the cross section of the aluminum alloy is, for example, the following cross sections. When the aluminum alloy has a somewhat long shape such as a wire, pipe, plate, etc., the cross section is taken along a plane orthogonal to the longitudinal direction of the aluminum alloy.
In the present disclosure, the conditions for the solution treatment and the conditions for the aging treatment are as follows.
(Conditions for solution treatment)
The heating temperature is a temperature selected from the range of 530°C or higher and 580°C or lower. The heating time is selected from the range of 15 minutes or more and 120 minutes or less.
(Conditions for aging treatment)
The heating temperature is a temperature selected from the range of 150°C or higher and 180°C or lower. The heating time is selected from the range of 4 hours or more and 100 hours or less.
以下、図面を適宜参照して、本開示の実施形態を具体的に説明する。 [Details of the embodiment of the present disclosure]
Hereinafter, embodiments of the present disclosure will be specifically described with reference to the drawings as appropriate.
(概要)
実施形態のアルミニウム合金は以下の組成と以下の断面組織とを備える。実施形態のアルミニウム合金の組成は、シリコンとマグネシウムと銅とマンガンとをそれぞれ後述する範囲で含み、残部がアルミニウム及び不可避不純物からなる。実施形態のアルミニウム合金は更に鉄、クロム、亜鉛、チタン、及びジルコニウムからなる群より選択される1種以上の元素を後述する範囲で含んでもよい。実施形態のアルミニウム合金の断面組織は、溶体化処理及び時効処理が施された状態において結晶粒の111面が断面の法線方向に配向している。特に、アルミニウム合金の断面を構成する結晶粒のうち多くの結晶粒において111面が断面の法線方向に配向している。以下、組成、組織を順に説明する。 [Aluminum alloy]
(Overview)
The aluminum alloy of the embodiment has the following composition and cross-sectional structure. The composition of the aluminum alloy of the embodiment contains silicon, magnesium, copper, and manganese within the ranges described later, with the balance being aluminum and unavoidable impurities. The aluminum alloy of the embodiment may further contain one or more elements selected from the group consisting of iron, chromium, zinc, titanium, and zirconium within the range described below. In the cross-sectional structure of the aluminum alloy of the embodiment, the 111 planes of the crystal grains are oriented in the normal direction of the cross section in a state in which solution treatment and aging treatment have been performed. In particular, the 111 plane is oriented in the normal direction of the cross section in many crystal grains among the crystal grains forming the cross section of the aluminum alloy. The composition and structure will be described in order below.
シリコン、マグネシウム、銅、及びマンガンをまとめて第一元素と示す。鉄、クロム、亜鉛、チタン、及びジルコニウムをまとめて第二元素と示す。
各元素を元素記号によって示す。Siはシリコンを意味する。Mgはマグネシウムを意味する。Cuは銅を意味する。Mnはマンガンを意味する。Alはアルミニウムを意味する。Feは鉄を意味する。Crはクロムを意味する。Znは亜鉛を意味する。Tiはチタンを意味する。Zrはジルコニウムを意味する。
アルミニウム合金に溶体化処理及び時効処理が施された状態を熱処理後の状態と示す。 In the following description, the following notation may be used.
Silicon, magnesium, copper, and manganese are collectively referred to as primary elements. Iron, chromium, zinc, titanium, and zirconium are collectively referred to as secondary elements.
Each element is indicated by an element symbol. Si means silicon. Mg means magnesium. Cu means copper. Mn means manganese. Al means aluminum. Fe means iron. Cr means chromium. Zn means zinc. Ti means titanium. Zr means zirconium.
A state in which the aluminum alloy is subjected to solution treatment and aging treatment is referred to as a state after heat treatment.
実施形態のアルミニウム合金では第一元素は必須元素であり、第二元素は任意元素である。定量的には実施形態のアルミニウム合金はシリコンを0.6質量%以上1.5質量%以下、マグネシウムを0.5質量%以上1.3質量%以下、銅を0.1質量%以上1.2質量%以下、マンガンを0.2質量%以上1.15質量%以下、鉄を0質量%以上0.8質量%以下、クロムを0質量%以上0.35質量%以下、亜鉛を0質量%以上0.5質量%以下、チタンを0質量%以上0.2質量%以下、ジルコニウムを0質量%以上0.2質量%以下含み、残部がアルミニウム及び不可避不純物からなる組成を備える。1種以上の第二元素を含む実施形態のアルミニウム合金において鉄の含有割合は0質量%超0.8質量%以下である。クロムの含有割合は0質量%超0.35質量%以下である。亜鉛の含有割合は0質量%超0.5質量%以下である。チタンの含有割合は0質量%超0.2質量%以下である。ジルコニウムの含有割合は0質量%超0.2質量%以下である。 (composition)
In the aluminum alloy of the embodiment, the first element is an essential element and the second element is an optional element. Quantitatively, the aluminum alloy of the embodiment contains 0.6 mass % to 1.5 mass % of silicon, 0.5 mass % to 1.3 mass % of magnesium, and 0.1 mass % to 1.3 mass % of copper. 2% by mass or less, 0.2% to 1.15% by mass of manganese, 0% to 0.8% by mass of iron, 0% to 0.35% by mass of chromium, 0% by mass of zinc % or more and 0.5 mass % or less, 0 mass % or more and 0.2 mass % or less of titanium, 0 mass % or more and 0.2 mass % or less of zirconium, and the balance being aluminum and unavoidable impurities. The content of iron in the aluminum alloy of the embodiment containing one or more secondary elements is more than 0% by mass and 0.8% by mass or less. The content of chromium is more than 0% by mass and 0.35% by mass or less. The zinc content is more than 0% by mass and 0.5% by mass or less. The content of titanium is more than 0% by mass and 0.2% by mass or less. The content of zirconium is more than 0% by mass and 0.2% by mass or less.
〈第一組成〉
第一組成は、シリコンを1.0質量%以上1.3質量%以下、マグネシウムを0.5質量%以上1.2質量%以下、鉄を0.3質量%以上0.8質量%以下、銅を0.1質量%以上0.4質量%以下、マンガンを0.2質量%以上0.5質量%以下、クロムを0質量%超0.3質量%以下、チタンを0.001質量%以上0.1質量%以下、ジルコニウムを0質量%以上0.2質量%以下含み、残部がアルミニウム及び不可避不純物からなる。 Specific examples of the composition containing the second element in addition to the first element include the following first composition, second composition, and third composition.
<First composition>
The first composition contains 1.0% by mass to 1.3% by mass of silicon, 0.5% by mass to 1.2% by mass of magnesium, 0.3% by mass to 0.8% by mass of iron, 0.1% by mass or more and 0.4% by mass or less of copper, 0.2% by mass or more and 0.5% by mass or less of manganese, 0.3% by mass or more of chromium, and 0.001% by mass of titanium 0.1% by mass or less, 0% by mass or more and 0.2% by mass or less of zirconium, and the balance being aluminum and unavoidable impurities.
第二組成は、シリコンを0.6質量%以上1.5質量%以下、マグネシウムを0.7質量%以上1.3質量%以下、鉄を0.02質量%以上0.4質量%以下、銅を0.5質量%以上1.2質量%以下、マンガンを0.5質量%以上1.1質量%以下、クロムを0質量%超0.3質量%以下、亜鉛を0.005質量%以上0.5質量%以下、チタンを0.01質量%以上0.2質量%以下、ジルコニウムを0.05質量%以上0.2質量%以下含み、残部がアルミニウム及び不可避不純物からなる。第二組成は更にストロンチウムを0.005質量%以上0.05質量%以下含んでもよい。 <Second composition>
The second composition contains 0.6% to 1.5% by mass of silicon, 0.7% to 1.3% by mass of magnesium, 0.02% to 0.4% by mass of iron, 0.5 to 1.2% by mass of copper, 0.5 to 1.1% by mass of manganese, more than 0 to 0.3% by mass of chromium, and 0.005% by mass of zinc 0.5% by mass or less, 0.01% by mass or more and 0.2% by mass or less of titanium, 0.05% by mass or more and 0.2% by mass or less of zirconium, and the balance being aluminum and unavoidable impurities. The second composition may further contain 0.005 mass % or more and 0.05 mass % or less of strontium.
第三組成は、シリコンを0.9質量%以上1.3質量%以下、マグネシウムを0.8質量%以上1.2質量%以下、鉄を0質量%超0.4質量%以下、銅を0.65質量%以上1.1質量%以下、マンガンを0.55質量%以上1.15質量%以下、クロムを0質量%超0.35質量%以下、亜鉛を0.12質量%以上0.25質量%以下、チタンを0質量%超0.075質量%以下、ジルコニウムを0.05質量%以上0.17質量%以下含み、残部がアルミニウム及び不可避不純物からなる。第三組成は国際合金記号A6056で示される合金の組成に概ね相当する。 <Third composition>
The third composition contains 0.9% by mass to 1.3% by mass of silicon, 0.8% by mass to 1.2% by mass of magnesium, more than 0% by mass and 0.4% by mass or less of iron, and copper 0.65% by mass or more and 1.1% by mass or less, manganese of 0.55% by mass or more and 1.15% by mass or less, chromium of 0% by mass or more and 0.35% by mass or less, zinc of 0.12% by mass or more and 0 0.075% by mass or less of titanium, 0.05% by mass or more and 0.17% by mass or less of zirconium, and the balance being aluminum and inevitable impurities. The third composition roughly corresponds to the composition of the alloy indicated by the international alloy symbol A6056.
〈第一組成〉
シリコンの含有割合は1.0質量%超1.3質量%以下、1.1質量%以上1.3質量%以下でもよい。
マグネシウムの含有割合は0.6質量%以上1.1質量%以下、0.7質量%以上1.0質量%以下でもよい。
鉄の含有割合は0.3質量%以上0.7質量%以下、0.3質量%以上0.6質量%以下でもよい。
銅の含有割合は0.2質量%以上0.4質量%以下でもよい。
マンガンの含有割合は0.2質量%以上0.4質量%以下、0.2質量%以上0.3質量%以下でもよい。
クロムの含有割合は0.005質量%以上0.20質量%以下、0.01質量%以上0.10質量%以下でもよい。
チタンの含有割合は0.005質量%以上0.05質量%以下、0.01質量%以上0.05質量%以下でもよい。
ジルコニウムを含む場合にはジルコニウムの含有割合は0.001質量%以上0.20質量%以下、0.005質量%以上0.10質量%以下でもよい。
チタンとジルコニウムとの合計の含有割合は0.01質量%以上0.10質量%以下でもよい。 Hereinafter, the content range of the first element and the content range of the second element are exemplified in the first composition, the second composition, and the third composition.
<First composition>
The silicon content may be more than 1.0% by mass and 1.3% by mass or less, or 1.1% by mass or more and 1.3% by mass or less.
The content of magnesium may be 0.6% by mass or more and 1.1% by mass or less, or 0.7% by mass or more and 1.0% by mass or less.
The content of iron may be 0.3% by mass or more and 0.7% by mass or less, or 0.3% by mass or more and 0.6% by mass or less.
The content of copper may be 0.2% by mass or more and 0.4% by mass or less.
The content of manganese may be 0.2% by mass or more and 0.4% by mass or less, or 0.2% by mass or more and 0.3% by mass or less.
The content of chromium may be 0.005% by mass or more and 0.20% by mass or less, or 0.01% by mass or more and 0.10% by mass or less.
The content of titanium may be 0.005% by mass or more and 0.05% by mass or less, or 0.01% by mass or more and 0.05% by mass or less.
When zirconium is included, the content of zirconium may be 0.001% by mass or more and 0.20% by mass or less, or 0.005% by mass or more and 0.10% by mass or less.
The total content of titanium and zirconium may be 0.01% by mass or more and 0.10% by mass or less.
シリコンの含有割合は0.8質量%以上1.4質量%以下、1.1質量%以上1.3質量%以下でもよい。
マグネシウムの含有割合は0.8質量%以上1.3質量%以下、0.8質量%以上1.0質量%以下でもよい。
鉄の含有割合は0.05質量%以上0.40質量%以下でもよい。
銅の含有割合は0.8質量%以上1.2質量%以下でもよい。
マンガンの含有割合は0.7質量%以上1.1質量%以下でもよい。
クロムの含有割合は0.01質量%以上0.30質量%以下、0.05質量%以上0.30質量%以下でもよい。
亜鉛の含有割合は0.05質量%以上0.25質量%以下でもよい。
チタンの含有割合は0.01質量%以上0.15質量%以下でもよい。
ジルコニウムの含有割合は0.08質量%以上0.2質量%以下でもよい。
チタンとジルコニウムとの合計の含有割合は0.10質量%以上0.20質量%以下でもよい。
ストロンチウムを含む場合にはストロンチウムの含有割合は0.005質量%以上0.04質量%以下でもよい。 <Second composition>
The content of silicon may be 0.8% by mass or more and 1.4% by mass or less, or 1.1% by mass or more and 1.3% by mass or less.
The content of magnesium may be 0.8% by mass or more and 1.3% by mass or less, or 0.8% by mass or more and 1.0% by mass or less.
The iron content may be 0.05% by mass or more and 0.40% by mass or less.
The content of copper may be 0.8% by mass or more and 1.2% by mass or less.
The manganese content may be 0.7% by mass or more and 1.1% by mass or less.
The content of chromium may be 0.01% by mass or more and 0.30% by mass or less, or 0.05% by mass or more and 0.30% by mass or less.
The content of zinc may be 0.05% by mass or more and 0.25% by mass or less.
The content of titanium may be 0.01% by mass or more and 0.15% by mass or less.
The content of zirconium may be 0.08% by mass or more and 0.2% by mass or less.
The total content of titanium and zirconium may be 0.10% by mass or more and 0.20% by mass or less.
When strontium is included, the content of strontium may be 0.005% by mass or more and 0.04% by mass or less.
シリコンの含有割合は0.9質量%以上1.2質量%以下でもよい。
マグネシウムの含有割合は0.8質量%以上1.0質量%以下でもよい。
鉄の含有割合は0.10質量%以上0.25質量%以下でもよい。
銅の含有割合は0.65質量%以上0.85質量%以下でもよい。
マンガンの含有割合は0.55質量%以上0.80質量%以下、0.55質量%以上0.65質量%以下でもよい。
クロムの含有割合は0.01質量%以上0.10質量%以下、0.02質量%以上0.05質量%以下でもよい。
亜鉛の含有割合は0.13質量%以上0.25質量%以下でもよい。
チタンの含有割合は0.001質量%以上0.075質量%以下、0.01質量%以上0.075質量%以下でもよい。
ジルコニウムの含有割合は0.10質量%以上0.17質量%以下でもよい。
チタンとジルコニウムとの合計の含有割合は0.11質量%以上0.20質量%以下でもよい。 <Third composition>
The silicon content may be 0.9% by mass or more and 1.2% by mass or less.
The content of magnesium may be 0.8% by mass or more and 1.0% by mass or less.
The content of iron may be 0.10% by mass or more and 0.25% by mass or less.
The content of copper may be 0.65% by mass or more and 0.85% by mass or less.
The content of manganese may be 0.55% by mass or more and 0.80% by mass or less, or 0.55% by mass or more and 0.65% by mass or less.
The content of chromium may be 0.01% by mass or more and 0.10% by mass or less, or 0.02% by mass or more and 0.05% by mass or less.
The content of zinc may be 0.13% by mass or more and 0.25% by mass or less.
The content of titanium may be 0.001% by mass or more and 0.075% by mass or less, or 0.01% by mass or more and 0.075% by mass or less.
The content of zirconium may be 0.10% by mass or more and 0.17% by mass or less.
The total content of titanium and zirconium may be 0.11% by mass or more and 0.20% by mass or less.
チタンを含む場合には実施形態のアルミニウム合金は更に硼素を50質量ppm以下の範囲で含んでもよい。 <Other elements>
When titanium is included, the aluminum alloy of the embodiment may further include boron in the range of 50 ppm by mass or less.
本発明者らは、熱処理後の状態において高い引張強さを有するアルミニウム合金は以下の組織を有することが好ましいとの知見を得た。アルミニウム合金の断面の全域において結晶粒の111面が結晶粒における他の結晶面よりも配向していることが好ましい。つまりアルミニウム合金の断面を構成する結晶粒のうち多くの結晶粒では111面が配向していることが好ましい。定量的には実施形態のアルミニウム合金では、熱処理後の状態において断面の全域をX線回折して求められた111面の配向度の平均値が50%以上である。また、上記111面の配向度の分散が45%以下である。このような断面を複数備えると共に複数の断面が一つの断面に垂直な方向に並んでいるアルミニウム合金は上記垂直な方向を引張方向として引っ張られても破断し難い。 (organization)
The present inventors have found that an aluminum alloy having high tensile strength after heat treatment preferably has the following structure. It is preferable that the 111 planes of the crystal grains are more oriented than the other crystal planes of the crystal grains over the entire cross section of the aluminum alloy. In other words, it is preferable that most of the crystal grains forming the cross section of the aluminum alloy have the 111 plane orientation. Quantitatively, in the aluminum alloy of the embodiment, the average value of the degree of orientation of the 111 plane obtained by X-ray diffraction of the entire cross section after heat treatment is 50% or more. Further, the dispersion of the degree of orientation of the 111 plane is 45% or less. An aluminum alloy having a plurality of such cross sections and having the plurality of cross sections aligned in a direction perpendicular to one cross section is unlikely to break even when pulled in the direction perpendicular to the cross section.
実施形態のアルミニウム合金は例えば熱処理後の状態における常温での引張強さが425MPa超である。ここでの常温は5℃以上35℃以下である。引張強さが425MPa超である実施形態のアルミニウム合金は強度に優れる。引張強さが427MPa超、430MPa以上、更に440MPa以上である実施形態のアルミニウム合金は強度により優れる。組成や製造条件によっては実施形態のアルミニウム合金は450MPa以上、460MPa以上、更には470MPa以上という高い引張強さを有する。 (Tensile strength)
The aluminum alloy of the embodiment has, for example, a tensile strength of more than 425 MPa at room temperature after heat treatment. The normal temperature here is 5° C. or higher and 35° C. or lower. The aluminum alloy of the embodiment having a tensile strength of more than 425 MPa is excellent in strength. The aluminum alloy of the embodiment having a tensile strength of more than 427 MPa, 430 MPa or more, or even 440 MPa or more is superior in strength. Depending on the composition and manufacturing conditions, the aluminum alloy of the embodiment has a high tensile strength of 450 MPa or more, 460 MPa or more, and further 470 MPa or more.
実施形態のアルミニウム合金は種々の形状を有することができる。例えば、実施形態のアルミニウム合金はある程度長い形状を有する。このような実施形態のアルミニウム合金はその長手方向に垂直な平面からなる端面と上記長手方向に延びた延伸部とを備える。延伸部における上記長手方向に沿った長さは、端面の外周輪郭の面積と等しい面積を有する円の直径よりも長い。上記延伸部を有する実施形態のアルミニウム合金では、上述の111面の配向度を測定する対象となる断面は、上記長手方向に垂直な平面で延伸部を切断することで得られる。 (Usage form)
The aluminum alloys of embodiments can have various shapes. For example, the aluminum alloys of the embodiments have somewhat long shapes. The aluminum alloy of such an embodiment has an end surface which is a plane perpendicular to its longitudinal direction and an extension extending in the longitudinal direction. The length of the extension along the longitudinal direction is greater than the diameter of a circle having an area equal to the area of the outer contour of the end face. In the aluminum alloy of the embodiment having the stretched portion, the cross section to be measured for the degree of orientation of the 111 plane is obtained by cutting the stretched portion along a plane perpendicular to the longitudinal direction.
実施形態のアルミニウム合金線1は実施形態のアルミニウム合金からなる。実施形態のアルミニウム合金線1は図1に示すように端面10と延伸部11とを備える。ここでの端面10はアルミニウム合金線1の長手方向に垂直な面である。延伸部11は上記長手方向に延びている。実施形態のアルミニウム合金線1は代表的には図1に示すように延伸部11の全長にわたって外周輪郭が同じであると共に線径が同じである。ここでの線径は端面10の面積又は上記長手方向に垂直な平面で切断した断面の面積と同じ面積を有する円の直径とする。図1は端面10の外周輪郭及び上記長手方向に垂直な平面で切断した任意の断面の外周輪郭が円形である場合を例示する。端面10の外周輪郭及び上記断面の外周輪郭は四角等の多角形でもよいし楕円等の曲面形状でもよい。実施形態のアルミニウム合金線1の線径は特に問わない。上記線径は例えば3mm以上15mm以下程度である。 <wire>
An
実施形態のアルミニウム合金は、アルミニウム合金部材を構成することができる。例えばアルミニウム合金部材は、実施形態のアルミニウム合金からなり、溶体化処理及び時効処理が施されたものである。具体例は、実施形態のアルミニウム合金線1に塑性加工が施された後に溶体化処理及び時効処理が施されたアルミニウム合金部材である。別例は、実施形態のアルミニウム合金からなる板材に塑性加工が施された後に溶体化処理及び時効処理が施されたアルミニウム合金部材である。ここでの塑性加工は、溶体化処理及び時効処理後においてアルミニウム合金部材の断面が上述の特定の配向性を有するように行う。更に別例は、実施形態のアルミニウム合金線1に溶体化処理及び時効処理が施されたアルミニウム合金部材である。つまりアルミニウム合金部材は線状、又は棒状でもよい。その他、アルミニウム合金部材は筒状でもよい。 <Aluminum alloy member>
The aluminum alloy of the embodiment can constitute an aluminum alloy member. For example, the aluminum alloy member is made of the aluminum alloy of the embodiment and subjected to solution treatment and aging treatment. A specific example is an aluminum alloy member obtained by subjecting the
本発明者らは上述の特定の組成を有するアルミニウム合金であって溶体化処理及び時効処理が施された状態において強度に優れるアルミニウム合金の製造方法を検討した。その結果、本発明者らは、溶体化処理の直近に行われる塑性加工は冷間加工であると共に大きい加工度であることが好ましいとの知見を得た。この知見から、実施形態のアルミニウム合金を製造する場合には例えば以下のアルミニウム合金の製造方法を利用することができる。 (Method for producing aluminum alloy)
The inventors of the present invention have investigated a method for producing an aluminum alloy having the specific composition described above and having excellent strength when subjected to solution treatment and aging treatment. As a result, the inventors of the present invention have found that it is preferable that the plastic working performed immediately after the solution treatment be cold working and have a large degree of working. Based on this knowledge, when manufacturing the aluminum alloy of the embodiment, for example, the following method for manufacturing an aluminum alloy can be used.
上記素材は第一塑性加工が施された加工材である。上記冷間加工は加工度が20%以上である第二塑性加工である。
上記アルミニウム合金は上述の第一元素に加えて第二元素を上述の範囲で含む組成を有してもよい。 A method for producing an aluminum alloy includes a step of cold working a raw material made of an aluminum alloy to produce a cold-worked material. The above-mentioned aluminum alloy has a composition containing the above-mentioned first element within the above-mentioned range, with the balance being aluminum and unavoidable impurities.
The above material is a worked material that has undergone the first plastic working. The cold working is the second plastic working with a degree of working of 20% or more.
The aluminum alloy may have a composition containing the second element within the above range in addition to the above first element.
〈素材〉
上述のアルミニウム合金からなる素材は鋳造材に第一塑性加工が施されたものである。第一塑性加工は例えば圧延加工等である。第一塑性加工は例えば熱間加工である。 A method for producing the aluminum alloy described above will be specifically described below.
<material>
The raw material made of the aluminum alloy described above is a cast material subjected to the first plastic working. The first plastic working is, for example, rolling. The first plastic working is, for example, hot working.
上述の素材には以下の条件の軟化処理を施すことができる。以下、素材に施す軟化処理を初期軟化処理と呼ぶことがある。
《軟化処理の条件》
加熱温度は250℃以上500℃未満の範囲から選択される温度である。保持時間は1時間以上100時間以下の範囲から選択される時間である。軟化時の雰囲気は例えば大気雰囲気、非酸化性雰囲気である。非酸化性雰囲気は例えば減圧雰囲気、不活性ガス雰囲気、還元ガス雰囲気等である。
加熱温度は300℃以上480℃以下、更に300℃以上460℃以下でもよい。 <Initial softening>
The materials described above can be subjected to a softening treatment under the following conditions. Hereinafter, the softening treatment applied to the material may be referred to as initial softening treatment.
《Conditions for softening treatment》
The heating temperature is a temperature selected from the range of 250°C or higher and lower than 500°C. The retention time is a time selected from the range of 1 hour or more and 100 hours or less. The softening atmosphere is, for example, an air atmosphere or a non-oxidizing atmosphere. The non-oxidizing atmosphere is, for example, a reduced pressure atmosphere, an inert gas atmosphere, a reducing gas atmosphere, or the like.
The heating temperature may be 300° C. or higher and 480° C. or lower, and further 300° C. or higher and 460° C. or lower.
素材に施す第二塑性加工は上述のように冷間加工である。第二塑性加工は例えば伸線加工、圧延加工、押出加工等である。第二塑性加工が伸線加工であれば線材が得られる。第二塑性加工が圧延加工であれば代表的には板材が得られる。第二塑性加工が押出加工であれば押出ダイスの形状によって線材や板材、パイプ等が得られる。
《加工度》
第二塑性加工の加工度が大きいほど111面の配向性が高められる。強度の向上の観点から第二塑性加工の加工度は30%以上、40%以上、60%以上でもよい。ここでの加工度は、第二塑性加工前の断面積と第二塑性加工後の断面積との差を第二塑性加工前の断面積で除した割合である。 <Second plastic working>
The second plastic working applied to the material is cold working as described above. The second plastic working is, for example, wire drawing, rolling, extrusion, or the like. If the second plastic working is wire drawing, a wire is obtained. If the second plastic working is rolling, a plate material is typically obtained. If the second plastic working is extrusion, wire rods, plate materials, pipes and the like can be obtained depending on the shape of the extrusion die.
《Processing degree》
The higher the working degree of the second plastic working, the higher the orientation of the 111 plane. From the viewpoint of improving the strength, the workability of the second plastic working may be 30% or more, 40% or more, or 60% or more. The workability here is a ratio obtained by dividing the difference between the cross-sectional area before the second plastic working and the cross-sectional area after the second plastic working by the cross-sectional area before the second plastic working.
第二塑性加工の途中に軟化処理を施すことができる。以下、第二塑性加工の途中に行う軟化処理を中間軟化処理と呼ぶことがある。中間軟化処理の条件は上述の初期軟化処理の条件を参照するとよい。中間軟化処理の前後に冷間加工を行うことで上述のように温間加工や熱間加工を行う場合に比較してアルミニウム合金に転位が蓄積され易い。また、中間軟化処理を行うことで中間軟化処理後の冷間加工の加工度を大きくすることができる。そのため、中間軟化処理後の冷間加工によってアルミニウム合金に転位を蓄積することができる。中間軟化処理後の冷間加工の加工度が大きいほど111面の配向性が高められる。また、中間軟化処理を行う場合には、中間軟化処理後の冷間加工における加工度は中間軟化処理前の冷間加工における加工度よりも大きいことが好ましい。特に中間軟化処理後の冷間加工における加工度は30%以上、40%以上、更に60%以上でもよい。 <Intermediate softening>
A softening treatment can be applied during the second plastic working. Hereinafter, the softening treatment performed during the second plastic working may be referred to as an intermediate softening treatment. As for the conditions of the intermediate softening treatment, it is preferable to refer to the conditions of the initial softening treatment described above. By performing cold working before and after the intermediate softening treatment, dislocations are more likely to accumulate in the aluminum alloy than in the case of performing warm working or hot working as described above. Further, by performing the intermediate softening treatment, it is possible to increase the degree of cold working after the intermediate softening treatment. Therefore, dislocations can be accumulated in the aluminum alloy by cold working after the intermediate softening treatment. The higher the degree of cold working after the intermediate softening treatment, the higher the orientation of the 111 plane. Further, when the intermediate softening treatment is performed, the working degree in the cold working after the intermediate softening treatment is preferably larger than the working degree in the cold working before the intermediate softening treatment. In particular, the degree of cold working after the intermediate softening treatment may be 30% or more, 40% or more, or even 60% or more.
発明者らは、実施形態のアルミニウム合金線1を製造するには以下の条件を満たすことが好ましいとの知見を得た。この知見から、実施形態のアルミニウム合金線の製造方法は以下の第一工程と第二工程と第三工程と第四工程とを備える。
〈条件〉
冷間で伸線加工を行う。伸線加工の途中に軟化処理を行う。上記軟化処理後の伸線加工の加工度が20%以上であると共に軟化処理前の伸線加工における加工度よりも大きい。 (Manufacturing method of aluminum alloy wire)
The inventors have found that it is preferable to satisfy the following conditions in order to manufacture the
<conditions>
Cold drawing is performed. A softening treatment is performed during wire drawing. The workability of the wire drawing after the softening treatment is 20% or more and is greater than the workability of the wire drawing before the softening treatment.
第二工程は、上記加工材に冷間で第一伸線加工を施すことで第一伸線材を製造する工程である。
第三工程は、上記第一伸線材に軟化処理を施すことで軟化材を製造する工程である。
第四工程は、上記軟化材に冷間で第二伸線加工を施すことで第二伸線材を製造する工程である。
実施形態のアルミニウム合金線の製造方法では、上記第二伸線加工における加工度は20%以上である。また、上記第二伸線加工における加工度は上記第一伸線加工における加工度よりも大きい。
第一工程の塑性加工は上述の第一塑性加工に相当する。第三工程の軟化処理は上述の中間軟化処理に相当する。第一伸線加工及び第二伸線加工は上述の第二塑性加工に相当する。 The first step is a step of manufacturing a processed material by subjecting a cast material of an aluminum alloy containing the first element in the above range and the balance being aluminum and inevitable impurities to plastic working. In addition to the first element, the aluminum alloy forming the cast material may further contain the second element within the range described above.
The second step is a step of manufacturing the first drawn wire material by subjecting the worked material to the first cold wire drawing process.
The third step is a step of manufacturing a softened material by subjecting the first drawn wire material to a softening treatment.
The fourth step is a step of manufacturing a second drawn wire material by subjecting the softened material to a second cold wire drawing process.
In the method for manufacturing an aluminum alloy wire of the embodiment, the workability in the second wire drawing is 20% or more. Further, the degree of working in the second wire drawing is greater than the degree of working in the first wire drawing.
The plastic working of the first step corresponds to the first plastic working described above. The softening treatment in the third step corresponds to the intermediate softening treatment described above. The first wire drawing and the second wire drawing correspond to the second plastic working described above.
〈第一工程〉
第一工程において鋳造材は例えば金型鋳造法、連続鋳造法等を利用して製造する。第一工程において塑性加工は例えば熱間圧延加工であり、加工材は例えば連続鋳造圧延材である。加工材が連続鋳造圧延材であれば、連続した長いアルミニウム合金線を製造することができる。この点で、加工材が連続鋳造圧延材である場合には実施形態のアルミニウム合金線1を量産することができる。 Each step will be described below. For basic operations in the method for manufacturing an aluminum alloy wire of the embodiment, reference can be made to a known method for manufacturing an aluminum alloy wire.
<First step>
In the first step, the cast material is manufactured using, for example, a die casting method, a continuous casting method, or the like. In the first step, the plastic working is, for example, hot rolling, and the material to be worked is, for example, continuously cast and rolled material. If the processed material is a continuously cast rolled material, a continuous long aluminum alloy wire can be produced. In this regard, the
第二工程において第一伸線加工の加工度は30%以上であることが好ましい。第一伸線加工の加工度が30%以上であれば、第一伸線加工によって導入された転位が軟化処理後においてある程度残存し易い。結果として、最終的に転位が多く蓄積されたアルミニウム合金線が得られ易い。第一伸線加工の加工度は35%以上、40%以上でもよい。第一伸線加工の加工度は最終線径にもよるが例えば30%以上80%以下の範囲から選択する。第一伸線加工の加工度は、第一伸線加工前の断面積と第一伸線加工後の断面積との差を第一伸線加工前の断面積で除した割合である。 <Second process>
In the second step, the workability of the first wire drawing is preferably 30% or more. If the workability of the first wire drawing is 30% or more, the dislocations introduced by the first wire drawing tend to remain to some extent after the softening treatment. As a result, it is easy to finally obtain an aluminum alloy wire in which many dislocations are accumulated. The working ratio of the first wire drawing may be 35% or more, or 40% or more. The working ratio of the first wire drawing is selected from a range of, for example, 30% or more and 80% or less, although it depends on the final wire diameter. The working degree of the first wire drawing is a ratio obtained by dividing the difference between the cross-sectional area before the first wire drawing and the cross-sectional area after the first wire drawing by the cross-sectional area before the first wire drawing.
第三工程の軟化処理の条件は上述の初期軟化処理の条件を参照するとよい。第三工程で軟化処理を行うことで軟化処理後の軟化材の加工性が高められる。そのため、第四工程における第二伸線加工の加工度を大きくすることができる。特に第四工程における第二伸線加工の加工度を第二工程における第一伸線加工の加工度よりも大きくすることできる。その結果、第二伸線加工によってアルミニウム合金に転位を蓄積することができる。 <Third process>
For the conditions of the softening treatment in the third step, the conditions of the initial softening treatment described above may be referred to. By performing the softening treatment in the third step, the workability of the softened material after the softening treatment is enhanced. Therefore, the working degree of the second wire drawing in the fourth step can be increased. In particular, the working degree of the second wire drawing in the fourth step can be made larger than the working degree of the first wire drawing in the second step. As a result, dislocations can be accumulated in the aluminum alloy by the second wire drawing.
第四工程における第二伸線加工の加工度が大きいほど111面の配向性が高められる。第二伸線加工の加工度が20%以上であれば、最終的に転位が多く蓄積されたアルミニウム合金線が得られ易い。第二伸線加工の加工度が第一伸線加工の加工度よりも大きいことからも、最終的に転位が多く蓄積されたアルミニウム合金線が得られ易い。上述のように第一伸線加工の加工度は30%以上であることが好ましいことから、第二伸線加工の加工度は30%超、40%以上、更に60%以上でもよい。第二伸線加工の加工度は所定の最終線径を有する第二伸線材が得られるように20%以上99.9%以下の範囲から選択する。第二伸線加工の加工度は、第二伸線加工前の断面積と第二伸線加工後の断面積との差を第二伸線加工前の断面積で除した割合である。 <Fourth step>
The higher the workability of the second wire drawing in the fourth step, the higher the orientation of the 111 plane. If the workability of the second wire drawing is 20% or more, it is easy to finally obtain an aluminum alloy wire in which many dislocations are accumulated. Since the working degree of the second wire drawing is higher than the working degree of the first wire drawing, it is easy to finally obtain an aluminum alloy wire in which many dislocations are accumulated. As described above, the working ratio of the first wire drawing is preferably 30% or more, so the working ratio of the second wire drawing may be more than 30%, 40% or more, or even 60% or more. The working ratio of the second wire drawing is selected from the range of 20% or more and 99.9% or less so that a second wire drawing having a predetermined final wire diameter can be obtained. The working degree of the second wire drawing is a ratio obtained by dividing the difference between the cross-sectional area before the second wire drawing and the cross-sectional area after the second wire drawing by the cross-sectional area before the second wire drawing.
上述のアルミニウム合金部材を製造する方法は例えば以下の加工工程と熱処理工程とを備える。
加工工程は、上述の第二塑性加工が施された第二塑性加工材又は上述の第二伸線材に第三塑性加工を施すことで第三加工材を製造する工程である。
熱処理工程は、上記第三加工材に溶体化処理及び時効処理を順に施して時効材を製造する工程である。
第三塑性加工は例えば押出加工、鍛造加工、伸線加工等である。溶体化処理及び時効処理の条件は上述の通りである。 (Manufacturing method of aluminum alloy member)
A method for manufacturing the aluminum alloy member described above includes, for example, the following processing steps and heat treatment steps.
The working step is a step of manufacturing the third worked material by applying the third plastic working to the second plastic working material subjected to the second plastic working or the second drawn wire material.
The heat treatment step is a step of sequentially subjecting the third processed material to solution treatment and aging treatment to produce an aged material.
The third plastic processing includes, for example, extrusion processing, forging processing, wire drawing processing, and the like. The conditions for solution treatment and aging treatment are as described above.
実施形態のアルミニウム合金及び実施形態のアルミニウム合金線1は溶体化処理及び時効処理が施された状態において高い引張強さを有する。以下の試験例1では実施形態のアルミニウム合金線1を例にして上記の効果を具体的に説明する。 [Main effects of the embodiment]
The aluminum alloy of the embodiment and the
表1に示す組成を有するアルミニウム合金線に溶体化処理及び時効処理を施した状態において組織観察を行うと共に引張強さを調べた。アルミニウム合金線の製造条件及び調べた結果を表2から表4に示す。 [Test Example 1]
The structures of the aluminum alloy wires having the compositions shown in Table 1 were subjected to solution treatment and aging treatment, and the tensile strength was examined. Tables 2 to 4 show the conditions for manufacturing the aluminum alloy wires and the results of the investigation.
各試料のアルミニウム合金線は基本的には連続鋳造圧延材に冷間で伸線加工を施すことで製造する。連続鋳造圧延材は例えば公知のプロペルチ式連続鋳造圧延機によって製造することができる。試料のうち一部の試料を除いて、伸線加工の途中に軟化処理を行う。
表2から表4において組成の項目における第一組成、第二組成、第三組成は表1に示す第一組成、第二組成、第三組成にそれぞれ相当する。
表2から表4において軟化処理の項目は加熱温度(℃)と保持時間(時間)とを示す。例えば「380℃×10h」は加熱温度が380℃であり、保持時間が10時間であることを意味する。 (Preparation of sample)
The aluminum alloy wire of each sample is basically produced by cold drawing a continuously cast and rolled material. A continuously cast rolled material can be produced by, for example, a known Propertit type continuous casting and rolling mill. Except for some of the samples, softening treatment is performed during the wire drawing process.
In Tables 2 to 4, the first composition, second composition, and third composition in the item of composition correspond to the first composition, second composition, and third composition shown in Table 1, respectively.
In Tables 2 to 4, the item of softening treatment indicates heating temperature (° C.) and holding time (hour). For example, "380° C.×10 h" means that the heating temperature is 380° C. and the holding time is 10 hours.
表2から表4において第一伸線加工の加工度(%)にハイフン「-」が記載されており、軟化処理及び第二伸線加工の加工度(%)の二つの項目に条件が記載された試料を説明する。これらの試料のアルミニウム合金線は、連続鋳造圧延材に軟化処理が施された後、第二伸線加工の加工度(%)で冷間の伸線加工が施されることで製造される。これらの試料のアルミニウム合金線は連続鋳造圧延材に初期軟化処理が施された後に冷間の伸線加工が連続的に施されており、中間軟化処理が施されていない。
表2から表4において第一伸線加工の加工度(%)及び第二伸線加工の加工度(%)の二つの項目に条件が記載されており、軟化処理にハイフン「-」が記載された試料を説明する。これらの試料のアルミニウム合金線は、連続鋳造圧延材に第一伸線加工の加工度(%)で冷間の伸線加工が施された後、中間軟化処理が施されることなく第二伸線加工の加工度(%)で冷間の伸線加工が施されることで製造される。つまりこれらの試料のアルミニウム合金線は連続鋳造圧延材に冷間の伸線加工が連続的に施されており、初期軟化処理及び中間軟化処理の双方が施されていない。この冷間の伸線加工における総加工度は表2から表4において第二伸線加工の加工度(%)の項目に記載される加工度よりも大きい。
連続鋳造圧延材の線径は5mm以上30mm以下の範囲から選択される。第二伸線加工後に製造される第二伸線材の線径は加工度によって概ね1.0mm以上21mm以下の範囲から選択される値である。 In Tables 2 to 4, the samples whose conditions are described in the three items of working degree (%) of the first wire drawing, softening treatment, and working degree (%) of the second wire drawing will be described. The aluminum alloy wires of these samples are manufactured by sequentially subjecting a continuously cast rolled material to a first cold drawing process, a softening treatment, and a second cold drawing process. The aluminum alloy wires of these samples were not subjected to initial softening treatment.
In Tables 2 to 4, a hyphen "-" is described in the working degree (%) of the first wire drawing, and the conditions are described in the two items of the softening treatment and the working degree (%) of the second wire drawing. I will explain the sample that was made. The aluminum alloy wires of these samples are manufactured by applying a softening treatment to the continuously cast and rolled material, and then applying a cold wire drawing process at the reduction ratio (%) of the second wire drawing process. The aluminum alloy wires of these samples were continuously subjected to cold wire drawing after being subjected to initial softening treatment of continuously cast and rolled material, and were not subjected to intermediate softening treatment.
In Tables 2 to 4, the conditions are described in two items, the working degree (%) of the first wire drawing and the working degree (%) of the second wire drawing, and the softening treatment is indicated by a hyphen "-". I will explain the sample that was made. The aluminum alloy wires of these samples were obtained by subjecting the continuously cast and rolled material to cold wire drawing at the degree of reduction (%) of the first wire drawing, and then to the second drawing without intermediate softening treatment. It is manufactured by applying cold wire drawing with a working degree (%) of wire working. In other words, the aluminum alloy wires of these samples were obtained by continuous cold drawing of continuously cast and rolled materials, and were not subjected to both initial softening and intermediate softening. The total working ratio in this cold wire drawing is larger than the working ratio described in the item of working ratio (%) in the second wire drawing in Tables 2 to 4.
The wire diameter of the continuously cast rolled material is selected from the range of 5 mm or more and 30 mm or less. The wire diameter of the second drawn wire manufactured after the second wire drawing is a value selected from the range of approximately 1.0 mm or more and 21 mm or less depending on the degree of working.
〈111面の配向度〉
得られた各試料のアルミニウム合金線に上述の条件で溶体化処理及び時効処理を施して熱処理線を製造する。得られた熱処理線を熱処理線の長手方向に垂直な平面で切断することで円盤状の試料を得る。試料は二つの円形状の横断面を有する。二つの横断面のうち一方の横断面の全域を機械研磨によって平滑にする。研磨後の横断面の表面粗さは算術平均粗さRaで0.2μm程度である。機械研磨には例えば2000番の耐水ペーパーを利用することができる。研磨した横断面の全域を以下のようにX線回折する。 (Organization observation)
<Orientation degree of 111 plane>
The obtained aluminum alloy wire of each sample is subjected to solution treatment and aging treatment under the conditions described above to produce a heat treated wire. A disc-shaped sample is obtained by cutting the obtained heat-treated wire along a plane perpendicular to the longitudinal direction of the heat-treated wire. The sample has two circular cross-sections. The entire area of one of the two cross-sections is smoothed by mechanical polishing. The surface roughness of the cross section after polishing is about 0.2 μm in terms of arithmetic mean roughness Ra. For example, 2000 water resistant paper can be used for mechanical polishing. X-ray diffraction is performed across the polished cross section as follows.
所定の面指数Fが111面である場合、試料3の111面とX線6とがなす角度θは11.3度を用いる。所定の方向Dと回折したX線60とがなす角度2θは22.6度を用いる。なお、図6はθ及び2θを実際の値よりも大きく示す。
所定の面指数Fが200面である場合、試料3の200面とX線6とがなす角度θは13度を用いる。所定の方向Dと回折したX線60とがなす角度2θは26度を用いる。
所定の面指数が220面である場合、試料3の220面とX線6とがなす角度θは18.6度を用いる。所定の方向Dと回折したX線60とがなす角度2θは37.2度を用いる。 The angles .theta. and 2.theta. are selected according to the wavelengths mentioned above. The angles θ and 2θ are the following values when λ is 0.0919 nm, for example.
When the predetermined plane index F is the 111 plane, the angle θ between the 111 plane of the
When the predetermined plane index F is the 200th plane, the angle θ between the 200th plane of the
When the predetermined plane index is the 220th plane, the angle θ between the 220th plane of the
引張強さ(MPa)は、JIS Z 2241:2011に準拠して測定する。ここでは常温での引張強さを測定する。 <Tensile strength>
Tensile strength (MPa) is measured according to JIS Z 2241:2011. Here, the tensile strength at room temperature is measured.
得られた各試料のアルミニウム合金線の組成は表1の組成と同じである。即ち各試料のアルミニウム合金線を構成するアルミニウム合金は表1に示す元素を表1に示す範囲で含み残部がAl及び不可避不純物からなる。アルミニウム合金線の組成の分析には公知の手法が利用できる。上記組成の分析には例えばエネルギー分散型X線分析装置等が利用できる。 <Component analysis>
The composition of the aluminum alloy wire of each sample obtained is the same as the composition in Table 1. That is, the aluminum alloy constituting the aluminum alloy wire of each sample contains the elements shown in Table 1 within the range shown in Table 1, and the balance is Al and unavoidable impurities. A known method can be used to analyze the composition of the aluminum alloy wire. For example, an energy dispersive X-ray spectrometer or the like can be used to analyze the composition.
図2及び図4はアルミニウム合金線の横断面の全域において上述の測定点ごとの111面の配向度をグレースケールの濃淡に変換した図である。図2の右及び図4の右に示すバーはカウント数に応じた濃淡を示す。各測定点の111面の配向度を例えばゼロから100までのカウント数に変換する。黒色はカウント数がゼロであることを意味する。白色はカウント数が100であることを意味する。111面の配向度が大きいほど、カウント数が大きくなる、即ち白色に近くなる。 2 and 3 are for sample no. 3 shows the distribution of the degree of orientation of the 111 plane for the aluminum alloy wire of No. 3. 4 and 5 are for sample no. 1 shows the orientation distribution of the 111 plane for the aluminum alloy wire of No. 1. FIG.
2 and 4 are diagrams obtained by converting the degree of orientation of the 111 plane for each of the above-described measurement points into grayscale shading over the entire cross section of the aluminum alloy wire. The bars shown on the right side of FIG. 2 and the right side of FIG. 4 show gradation according to the count number. The degree of orientation of the 111 plane at each measurement point is converted into a count number from zero to 100, for example. Black means zero counts. White means that the count number is 100. The greater the degree of orientation of the 111 plane, the greater the count number, that is, the closer to white.
(1)第一組成、第二組成を有するアルミニウム合金線は第三組成を有するアルミニウム合金線よりも111面の配向度の平均値が大きく、かつ111面の配向度の分散が小さい傾向にある。この点から、第一組成、第二組成を有するアルミニウム合金線はより高強度である。 In addition, this test shows the following.
(1) The aluminum alloy wire having the first composition and the second composition tends to have a larger average value of the degree of orientation of the 111 plane and a smaller dispersion of the degree of orientation of the 111 plane than the aluminum alloy wire having the third composition. . From this point of view, the aluminum alloy wire having the first composition and the second composition has higher strength.
10 端面、11 延伸部、30 横断面
6,60 X線
51 可動ステージ、51f 表面、52 検出器、53 演算装置
D 方向、F 面指数、θ,2θ 角度 1 aluminum alloy wire, 3
Claims (8)
- シリコンを0.6質量%以上1.5質量%以下、
マグネシウムを0.5質量%以上1.3質量%以下、
銅を0.1質量%以上1.2質量%以下、
マンガンを0.2質量%以上1.15質量%以下含み、残部がアルミニウム及び不可避不純物からなる組成を備え、
溶体化処理及び時効処理が施された状態において断面の全域をX線回折して求められた111面の配向度の平均値が50%以上であり、前記111面の配向度の分散が45%以下である、
アルミニウム合金。 0.6% by mass or more and 1.5% by mass or less of silicon,
0.5% by mass or more and 1.3% by mass or less of magnesium,
0.1% by mass or more and 1.2% by mass or less of copper,
A composition containing 0.2% by mass or more and 1.15% by mass or less of manganese, with the balance being aluminum and inevitable impurities,
The average value of the degree of orientation of the 111 plane obtained by X-ray diffraction of the entire cross section in the state of being subjected to solution treatment and aging treatment is 50% or more, and the dispersion of the degree of orientation of the 111 plane is 45%. is the following
aluminum alloy. - 更に、鉄、クロム、亜鉛、チタン、及びジルコニウムからなる群より選択される1種以上の元素を含み、
鉄の含有割合は0質量%超0.8質量%以下であり、
クロムの含有割合は0質量%超0.35質量%以下であり、
亜鉛の含有割合は0質量%超0.5質量%以下であり、
チタンの含有割合は0質量%超0.2質量%以下であり、
ジルコニウムの含有割合は0質量%超0.2質量%以下である、請求項1に記載のアルミニウム合金。 Furthermore, containing one or more elements selected from the group consisting of iron, chromium, zinc, titanium, and zirconium,
The iron content is more than 0% by mass and 0.8% by mass or less,
The content of chromium is more than 0% by mass and 0.35% by mass or less,
The content of zinc is more than 0% by mass and 0.5% by mass or less,
The content of titanium is more than 0% by mass and 0.2% by mass or less,
2. The aluminum alloy according to claim 1, wherein the content of zirconium is more than 0% by mass and 0.2% by mass or less. - シリコンを1.0質量%以上1.3質量%以下、
マグネシウムを0.5質量%以上1.2質量%以下、
鉄を0.3質量%以上0.8質量%以下、
銅を0.1質量%以上0.4質量%以下、
マンガンを0.2質量%以上0.5質量%以下、
クロムを0質量%超0.3質量%以下、
チタンを0.001質量%以上0.1質量%以下含み、残部がアルミニウム及び不可避不純物からなる組成を備える、請求項2に記載のアルミニウム合金。 1.0% by mass or more and 1.3% by mass or less of silicon,
0.5% by mass or more and 1.2% by mass or less of magnesium,
0.3% by mass or more and 0.8% by mass or less of iron,
0.1% by mass or more and 0.4% by mass or less of copper,
0.2% by mass or more and 0.5% by mass or less of manganese,
More than 0% by mass and 0.3% by mass or less of chromium,
3. The aluminum alloy according to claim 2, comprising 0.001% by mass or more and 0.1% by mass or less of titanium, with the balance being aluminum and unavoidable impurities. - シリコンを0.6質量%以上1.5質量%以下、
マグネシウムを0.7質量%以上1.3質量%以下、
鉄を0.02質量%以上0.4質量%以下、
銅を0.5質量%以上1.2質量%以下、
マンガンを0.5質量%以上1.1質量%以下、
クロムを0質量%超0.3質量%以下、
亜鉛を0.005質量%以上0.5質量%以下、
チタンを0.01質量%以上0.2質量%以下、
ジルコニウムを0.05質量%以上0.2質量%以下含み、残部がアルミニウム及び不可避不純物からなる組成を備える、請求項2に記載のアルミニウム合金。 0.6% by mass or more and 1.5% by mass or less of silicon,
0.7% by mass or more and 1.3% by mass or less of magnesium,
0.02% by mass or more and 0.4% by mass or less of iron,
0.5% by mass or more and 1.2% by mass or less of copper,
0.5% by mass or more and 1.1% by mass or less of manganese,
More than 0% by mass and 0.3% by mass or less of chromium,
0.005% by mass or more and 0.5% by mass or less of zinc,
0.01% by mass or more and 0.2% by mass or less of titanium,
3. The aluminum alloy according to claim 2, comprising 0.05% by mass or more and 0.2% by mass or less of zirconium, with the balance being aluminum and unavoidable impurities. - 溶体化処理及び時効処理が施された状態において引張強さが425MPa超である、請求項1から請求項4のいずれか1項に記載のアルミニウム合金。 The aluminum alloy according to any one of claims 1 to 4, which has a tensile strength of more than 425 MPa in the solution heat treated and aged condition.
- 請求項1から請求項5のいずれか1項に記載のアルミニウム合金からなる、
アルミニウム合金線。 Made of the aluminum alloy according to any one of claims 1 to 5,
aluminum alloy wire. - シリコンを0.6質量%以上1.5質量%以下、マグネシウムを0.5質量%以上1.3質量%以下、銅を0.1質量%以上1.2質量%以下、マンガンを0.2質量%以上1.15質量%以下含み、残部がアルミニウム及び不可避不純物からなる組成を有するアルミニウム合金の鋳造材に塑性加工を施すことで加工材を製造する工程と、
前記加工材に冷間で第一伸線加工を施すことで第一伸線材を製造する工程と、
前記第一伸線材に軟化処理を施すことで軟化材を製造する工程と、
前記軟化材に冷間で第二伸線加工を施すことで第二伸線材を製造する工程とを備え、
前記第二伸線加工における加工度は20%以上であると共に前記第一伸線加工における加工度よりも大きい、
アルミニウム合金線の製造方法。 0.6 mass % to 1.5 mass % of silicon, 0.5 mass % to 1.3 mass % of magnesium, 0.1 mass % to 1.2 mass % of copper, and 0.2 mass % of manganese A step of producing a worked material by subjecting a cast material of an aluminum alloy having a composition containing not less than 1.15% by mass and the balance consisting of aluminum and unavoidable impurities to plastic working;
a step of manufacturing a first drawn wire material by subjecting the worked material to a first cold wire drawing process;
a step of manufacturing a softened material by subjecting the first drawn wire material to a softening treatment;
a step of manufacturing a second wire drawn material by subjecting the softened material to a second cold wire drawing process,
The degree of processing in the second wire drawing is 20% or more and is greater than the degree of processing in the first wire drawing,
A method for producing an aluminum alloy wire. - 前記アルミニウム合金は、更に、鉄、クロム、亜鉛、チタン、及びジルコニウムからなる群より選択される1種以上の元素を含み、
鉄の含有割合は0質量%超0.8質量%以下であり、
クロムの含有割合は0質量%超0.35質量%以下であり、
亜鉛の含有割合は0質量%超0.5質量%以下であり、
チタンの含有割合は0質量%超0.2質量%以下であり、
ジルコニウムの含有割合は0質量%超0.2質量%以下である、請求項7に記載のアルミニウム合金線の製造方法。 The aluminum alloy further contains one or more elements selected from the group consisting of iron, chromium, zinc, titanium, and zirconium,
The iron content is more than 0% by mass and 0.8% by mass or less,
The content of chromium is more than 0% by mass and 0.35% by mass or less,
The content of zinc is more than 0% by mass and 0.5% by mass or less,
The content of titanium is more than 0% by mass and 0.2% by mass or less,
The method for producing an aluminum alloy wire according to claim 7, wherein the content of zirconium is more than 0% by mass and 0.2% by mass or less.
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JP2007177308A (en) * | 2005-12-28 | 2007-07-12 | Sumitomo Light Metal Ind Ltd | High strength and high toughness aluminum alloy extruded material and forged material having excellent corrosion resistance, and methods for producing the extruded material and forged material |
JP2012097321A (en) * | 2010-11-02 | 2012-05-24 | Furukawa-Sky Aluminum Corp | High-strength aluminum alloy forged product excellent in stress corrosion cracking resistance and forging method for the same |
JP2013104122A (en) * | 2011-11-16 | 2013-05-30 | Sumitomo Electric Ind Ltd | Aluminum alloy wire for bolt, the bolt and methods for manufacturing the same |
JP2015124409A (en) | 2013-12-26 | 2015-07-06 | 住友電気工業株式会社 | Aluminum alloy wire material, production method of it, and aluminum alloy member |
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JP2013234389A (en) * | 2013-07-24 | 2013-11-21 | Sumitomo Electric Ind Ltd | Aluminum alloy wire for bolt, bolt and methods of manufacturing the same |
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JP2007177308A (en) * | 2005-12-28 | 2007-07-12 | Sumitomo Light Metal Ind Ltd | High strength and high toughness aluminum alloy extruded material and forged material having excellent corrosion resistance, and methods for producing the extruded material and forged material |
JP2012097321A (en) * | 2010-11-02 | 2012-05-24 | Furukawa-Sky Aluminum Corp | High-strength aluminum alloy forged product excellent in stress corrosion cracking resistance and forging method for the same |
JP2013104122A (en) * | 2011-11-16 | 2013-05-30 | Sumitomo Electric Ind Ltd | Aluminum alloy wire for bolt, the bolt and methods for manufacturing the same |
JP2015124409A (en) | 2013-12-26 | 2015-07-06 | 住友電気工業株式会社 | Aluminum alloy wire material, production method of it, and aluminum alloy member |
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