Aluminum alloy, continuously cast aluminum alloy rod, method for manufacturing a continuously cast aluminum alloy rod

Abstract

This invention provides an aluminum alloy, a continuously cast aluminum alloy rod, and a method for manufacturing a continuously cast aluminum alloy rod, which contribute to the efficient use of resources at low cost by increasing the proportion of scrap containing a high amount of iron (e.g., 0.4% by mass or more). [Solution] An aluminum alloy having an alloy composition in which Si is contained in a range of 0.6 mass% or less, Fe in a range of 1.0 mass% or less, Cu in a range of 0.2 mass% or less, Mn in a range of 1.0 mass% or more and 1.5 mass% or less, Zn in a range of 0.30 mass% or less, and Sr in a range of 0.001 mass% or more and 0.01 mass% or less, with the remainder being Al and unavoidable impurities, wherein in a rectangular cross section of size 40 μm × 30 μm at any position inside the outer surface, when the total area of ​​particles of substances other than Al is taken as 100%, the area of ​​Al-Mn alloy particles accounts for 1% or more.

Description

Technical Field

[0001] The present invention relates to an aluminum alloy, a continuously cast bar of an aluminum alloy, and a method for manufacturing a continuously cast bar of an aluminum alloy.

Background Art

[0002] A3003, which is an aluminum alloy defined in JIS, has slightly higher strength than pure aluminum and has excellent formability, weldability, and corrosion resistance by adding Mn as an additive element. Such A3003 aluminum alloy is widely used in building materials such as aluminum containers, photosensitive drums, panels, shipbuilding materials, fin materials, aluminum cans, etc.

[0003] Generally, when manufacturing an aluminum alloy, from the viewpoints of cost and effective use of resources, recycled aluminum alloy (scrap) is often used. However, most of such scrap contains more than 0.7% by mass of Fe. When casting A3003 aluminum alloy using such scrap containing more than 0.7% by mass of Fe, excessive Fe combines with Al to form a metal compound such as Al6Fe.

[0004] Since Al6Fe has a higher hardness than Al, there has been a problem that the workability deteriorates due to a partial change in hardness caused by the generation of Al6Fe. Also, when the amount of the α-phase Al-Fe-Mn-Si alloy, which has a higher hardness than Al6Fe, increases, there has been a problem that the workability deteriorates due to a partial change in hardness. For example, the micro-Vickers hardness is 740 MHv for Al6Fe and 950 MHv for the α-phase Al-Fe-Mn-Si alloy.

[0005] On the other hand, Al6Fe causes a fir-like structure (Tannen-baumgefuge) to form on the longitudinal cross-section of cast A3003 aluminum alloy rods (see, for example, Figure 5). When this fir-like structure occurs in aluminum alloys, it does not disappear even after post-processing steps such as drawing and heat treatment, and when chemical conversion treatment or anodizing treatment is applied, the color of that part changes, creating a pattern on the surface. Thus, the presence of this fir-like structure also presented a problem in that it impaired the aesthetic appearance of the manufactured product.

[0006] For this reason, for example, Patent Document 1 describes that when adding Ca, Ti, and B to the molten metal during the casting of aluminum alloy, the formation of fir wood-like structures can be stably suppressed by setting the molten metal temperature to 675-740°C. [Prior art documents] [Patent Documents]

[0007] [Patent Document 1] Japanese Patent Publication No. 2011-174182 [Overview of the Initiative] [Problems that the invention aims to solve]

[0008] However, Patent Document 1 specifies that the Fe content should be between 0.03 and 2.5% by mass. Since many scrap materials exceed this Fe content, it became necessary to use a very small proportion of scrap in the molten metal, requiring the use of a large amount of pure aluminum that does not contain Fe. This increased the manufacturing cost of A3003 aluminum alloy and hindered the effective utilization of scrap.

[0009] This invention has been made in view of the above technical background, and aims to provide an aluminum alloy, a continuously cast aluminum alloy rod, and a method for manufacturing a continuously cast aluminum alloy rod that contribute to the effective use of resources at low cost by improving the proportion of scrap containing a large amount of iron (for example, 0.4% by mass or more). [Means for solving the problem]

[0010] To solve the above problems, the following means are proposed in the aluminum alloy, the continuously cast aluminum alloy rod, and the method for manufacturing the continuously cast aluminum alloy rod according to one embodiment of the present invention. (1) The aluminum alloy according to embodiment 1 of the present invention is an aluminum alloy having an alloy composition in which Si is contained in a range of 0.6 mass% or less, Fe in a range of 1.0 mass% or less, Cu in a range of 0.2 mass% or less, Mn in a range of 1.0 mass% or more and 1.5 mass% or less, Zn in a range of 0.30 mass% or less, and Sr in a range of 0.001 mass% or more and 0.01 mass% or less, with the remainder being Al and unavoidable impurities, wherein in a rectangular cross section of size 40 μm × 30 μm at any position inside the outer surface, when the total area of ​​particles of substances other than Al is taken as 100%, the area of ​​Al-Mn alloy particles accounts for 1% or more.

[0011] (2) Embodiment 2 of the present invention is an aluminum alloy of Embodiment 1 in which, when the total area of ​​particles of substances other than Al is taken as 100% in the rectangular cross-section, the area of ​​Al-Mn alloy particles accounts for 10% or more.

[0012] (3) Embodiment 3 of the present invention is an aluminum alloy according to Embodiment 1 or 2, wherein in the rectangular cross-section, when the total area of ​​particles of substances other than Al is taken as 100%, the area of ​​the α-phase Al-Fe-Mn-Si alloy is less than 30%.

[0013] (4) Embodiment 4 of the present invention further comprises an aluminum alloy according to any one of embodiments 1 to 3, wherein Ti is included in an amount of 0.005% by mass or more and 0.10% by mass or less.

[0014] (5) Embodiment 5 of the present invention further comprises B in any one of embodiments 1 to 4 in an amount of 0.001% by mass or more and 0.02% by mass or less.

[0015] (6) The continuously cast aluminum alloy rod of embodiment 6 of the present invention is made of any one of the aluminum alloys of embodiments 1 to 5, is a cylindrical continuously cast rod, has a diameter in the range of 30 mm to 300 mm, contains Fe in the range of 0.5% by mass to 1.0% by mass, and does not contain Al6Fe intermetallic compounds.

[0016] (7) A method for manufacturing a continuously cast aluminum alloy rod according to aspect 7 of the present invention is a method for manufacturing a continuously cast aluminum alloy rod according to aspect 6, comprising: a molten metal injection step of injecting molten alloy having the alloy composition of the aluminum alloy into the mold body of a continuous casting mold; a lubrication step of supplying lubricating oil and gas into the mold body; a primary cooling step of circulating a cooling medium through a cavity formed in the mold body to solidify the molten alloy and form the continuously cast rod; and a secondary cooling step of directly spraying the cooling medium toward the continuously cast rod after the primary cooling step, wherein the casting speed at the center of the continuously cast rod from the molten metal injection step to the completion of the primary cooling step is controlled to be within the range of 150 mm / min or more and 450 mm / min or less.

[0017] (8) Embodiment 8 of the present invention is a method for manufacturing a continuously cast aluminum alloy rod according to Embodiment 7, wherein in the lubrication step, the temperature of the gas is controlled to be within the range of 5°C to 50°C and the temperature of the lubricating oil is controlled to be within the range of 5°C to 45°C.

[0018] (9) Embodiment 9 of the present invention is a method for manufacturing a continuously cast aluminum alloy rod according to Embodiment 7 or 8, wherein in the lubrication step, the lubricating oil used has a viscosity of 80 (mPa·s (25℃)) or more and 1100 (mPa·s (25℃)). [Effects of the Invention]

[0019] According to the present invention, it is possible to improve the proportion of scrap containing a large amount of iron (for example, 0.4% by mass or more) and provide an aluminum alloy, a continuously cast aluminum alloy rod, and a method for manufacturing a continuously cast aluminum alloy rod that contribute to the effective use of resources at low cost.

Brief Description of the Drawings

[0020] [Figure 1] It is a schematic cross-sectional view showing an example of a vertical casting apparatus used in the method for manufacturing a continuously cast bar of an aluminum alloy according to the present embodiment. [Figure 2] It is a flowchart showing step by step the method for manufacturing a continuously cast bar of an aluminum alloy according to the present embodiment. [Figure 3] It is a schematic diagram showing the position of the observation surface of the continuously cast bar. [Figure 4] It is a photograph of the observation surface of Example 1 and Comparative Example 1. [Figure 5] It is a schematic diagram showing an example of a fir tree structure.

Embodiments for Carrying Out the Invention

[0021] Hereinafter, embodiments of the present invention will be described in detail with reference to the drawings. Note that the drawings used in the following description may show, for the sake of clarity of the features, some parts that are characteristic enlarged for convenience, and the dimensional ratios of each component are not necessarily the same as the actual ones. Also, the materials, dimensions, etc. exemplified in the following description are merely examples, and the present invention is not necessarily limited thereto, and it can be appropriately modified and implemented within the range that does not change the effects.

[0022] [Aluminum Alloy] An aluminum alloy according to an embodiment of the present invention will be described. The aluminum alloy according to an embodiment of the present invention corresponds to A3003 aluminum alloy in that it contains Mn and Cu.

[0023] The aluminum alloy according to an embodiment of the present invention contains Si within the range of 0.6% by mass or less, Fe within the range of 1.0% by mass or less, Cu within the range of 0.2% by mass or less, Mn within the range of 1.0% by mass or more and 1.5% by mass or less, Zn within the range of 0.30% by mass or less, and Sr within the range of 0.001% by mass or more and 0.01% by mass or less, and the balance consists of Al and unavoidable impurities.

[0024] Furthermore, the aluminum alloy of one embodiment of the present invention has a metallic structure in which, in a rectangular cross-section of size 40 μm × 30 μm at any position inside the outer surface of an aluminum alloy of any shape, when the total area of ​​particles of substances other than Al is taken as 100%, the area of ​​Al-Mn alloy particles accounts for 1% or more.

[0025] This rectangular cross-section at any given location can be any plane that extends in any direction inside the outer surface of an aluminum alloy of any shape, and is not limited to specific crystal planes or the like.

[0026] (Si: 0.6% by mass or less) Si improves both the mechanical properties at room temperature and corrosion resistance. However, excessive addition of Si to aluminum alloys can lead to the crystallization of coarse primary Si grains, potentially reducing the tensile strength of the aluminum alloy. By limiting the Si content to 0.6% by mass or less, the crystallization of primary Si can be suppressed.

[0027] (Fe: 1.0% by mass or less) Fe (Fe) improves the tensile strength of aluminum alloys by crystallizing as fine precipitates containing intermetallic compounds such as Al-Mn-Fe-Si, Al-Fe-Si, Al-Cu-Fe, and Al-Mn-Fe in aluminum alloys. On the other hand, excess Fe can generate hard intermetallic compounds such as Al6Fe, which may reduce workability. By keeping the Fe content within the range of 1.0 mass% or less, along with the addition of Sr (Sr) described later, the formation of Al6Fe, which causes the formation of the fir-like structure, can be suppressed.

[0028] (Cu: 0.2% by mass or less) Cu has the effect of finely dispersing Mg-Si compounds in aluminum alloys and improving the tensile strength of aluminum alloys by precipitating as Al-Cu-Mg-Si compounds, including the Q phase. However, excess Cu can cause the formation of unnecessary intermetallic compounds. By keeping the Cu content within the above range, it is possible to improve the room-temperature mechanical properties of the aluminum alloy forged product 1a without forming unnecessary intermetallic compounds.

[0029] (Mn: 1.0 mass% or more and 1.5 mass% or less) Mn improves the tensile strength of aluminum alloys by forming fine granular precipitates containing intermetallic compounds such as Al-Mn-Fe-Si. By keeping the Mn content within the specified range, the mechanical properties of the aluminum alloy at room temperature can be improved.

[0030] (Zn: 0.30% by mass or less) The Zn content should be 0.30% by mass or less. If the Zn content exceeds 0.30% by mass, intergranular corrosion is more likely to occur, leading to a decrease in corrosion resistance. For this reason, it is preferable that the Zn content be 0.250% by mass or less, or that it be completely absent.

[0031] (Sr: 0.001 mass% or more and 0.01 mass% or less) Sr can suppress the formation of a fir-like structure caused by metallic compounds such as Al6Fe, even when the proportion of Fe-containing scrap and other materials used as raw materials for aluminum alloy production is increased. By keeping the Sr content within the above range, for example, the formation of a fir-like structure can be suppressed even if the Fe content is 1.0 mass%.

[0032] The aluminum alloy of one embodiment of the present invention may further contain Ti in an amount of 0.005% by mass or more and 0.10% by mass or less.

[0033] (Ti: 0.005 mass% or more and 0.10 mass% or less) Ti has the effect of refining the crystal grains of aluminum alloys and improving their wroughtability. If the Ti content is less than 0.005 mass%, the grain refinement effect may not be sufficiently obtained. On the other hand, if the Ti content exceeds 0.10 mass%, coarse precipitates may form, which may reduce wroughtability. In addition, if a large amount of coarse precipitates containing Ti are mixed into the aluminum alloy, the toughness may decrease.

[0034] The aluminum alloy of one embodiment of the present invention may further contain B in an amount of 0.001% by mass or more and 0.02% by mass or less.

[0035] (B: 0.001 mass% or more, 0.02 mass% or less) B has the effect of refining the crystal grains of aluminum alloys and improving their wroughtability. Adding B to aluminum alloys together with Ti, as described above, enhances the crystal grain refinement effect. If the B content is less than 0.001 mass%, the crystal grain refinement effect may not be sufficiently obtained. On the other hand, if the B content exceeds 0.02 mass%, coarse precipitates may form and be mixed into the aluminum alloy as inclusions. Furthermore, if a large amount of coarse precipitates containing B are mixed into the final aluminum alloy product, the toughness may decrease.

[0036] (The area of ​​Al-Mn alloy particles is 1% or more) In aluminum alloys, by ensuring that the area of ​​Al-Mn alloy particles in any rectangular cross-section accounts for 1% or more, preferably 10% or more, of the metals excluding aluminum, the area occupied by α-phase Al-Fe-Mn-Si alloy can be relatively reduced. α-phase Al-Fe-Mn-Si alloy has higher hardness than pure Al, and if a large amount of this α-phase Al-Fe-Mn-Si alloy is present in the aluminum alloy, the workability decreases due to localized hardness variations (hardness unevenness). Therefore, by setting the area of ​​Al-Mn alloy particles to 1% or more, preferably 10% or more, and keeping the area occupied by α-phase Al-Fe-Mn-Si alloy to less than 30%, the decrease in workability due to hardness unevenness can be suppressed.

[0037] The aluminum alloy of one embodiment of the present invention preferably contains no Al6Fe compound at all. Al6Fe causes a fir-like structure in aluminum alloys. This fir-like structure not only impairs the aesthetic appearance of the manufactured product, but also reduces workability due to localized changes in hardness caused by the formation of Al6Fe. In the aluminum alloy of this embodiment, by including Sr in the range of 0.001% by mass or more and 0.01% by mass or less, even if Fe is included at a high content, such as 1.0% by mass, the formation of Al6Fe compounds is suppressed, resulting in an aluminum alloy in which no fir-like structure is formed at all.

[0038] With the aluminum alloy of this embodiment configured as described above, by making the area of ​​Al-Mn alloy particles in any rectangular cross-section of the metal excluding aluminum 1% or more, preferably 10% or more, the area occupied by the α-phase Al-Fe-Mn-Si alloy can be relatively reduced, thereby suppressing a decrease in workability due to hardness unevenness.

[0039] Furthermore, according to the aluminum alloy of this embodiment, even if scrap with a Fe content exceeding 0.3 mass% is used as a raw material, the formation of Al6Fe compounds is suppressed by including Sr in a range of 0.001 mass% to 0.01 mass%, resulting in an aluminum alloy that does not develop a fir tree structure.

[0040] This makes it possible to create an aluminum alloy that produces aesthetically pleasing aluminum products without localized color variations. Furthermore, it is possible to create an aluminum alloy with excellent workability that does not exhibit localized hardness changes due to the formation of Al6Fe compounds.

[0041] [Continuously cast aluminum alloy rods] A continuously cast aluminum alloy rod according to one embodiment of the present invention can be obtained by casting an aluminum alloy having the above-described alloy composition, for example, using a vertical continuous casting apparatus. Such a continuously cast aluminum alloy rod may have the above-described alloy composition, be cylindrical in shape, and have a diameter in the range of, for example, 30 mm to 300 mm.

[0042] By using an aluminum alloy with an alloy composition containing Sr in the range of 0.001% to 0.01% by mass as the casting material, even if Fe is contained in the range of 0.5% to 1.0% by mass, the formation of Al6Fe intermetallic compounds is suppressed, and by not containing Al6Fe intermetallic compounds, it is possible to produce a continuously cast aluminum alloy rod that does not develop a fir tree structure.

[0043] [Method for manufacturing continuously cast aluminum alloy rods] Next, an embodiment of the method for manufacturing a continuous cast aluminum alloy rod according to this embodiment will be described. First, an example of a vertical casting apparatus used in the manufacturing method of the continuously cast aluminum alloy rod according to this embodiment will be described. Figure 1 is a schematic cross-sectional view showing an example of a vertical casting apparatus used in the manufacturing method of continuously cast aluminum alloy rods according to this embodiment.

[0044] The vertical continuous casting apparatus 10 for continuous casting has a continuous casting mold 100. The continuous casting mold 100 has a cylindrical mold body 100A, one end of which is an inlet 12 for molten alloy and the other end of which is an outlet 13 for the continuous casting rod (ingot) S. The mold body 100A is made of an aluminum alloy containing a large amount of Mg. Alternatively, a Cu alloy can also be suitably used.

[0045] The mold body 100A has a cavity 21 through which a cooling medium, such as cooling water C, flows. An inlet 22 to the cavity 21 is provided at the top, and a nozzle 23 surrounds the casting outlet 13. The cooling water (cooling medium) C introduced from the inlet 22 flows through the cavity 21 and cools the molten metal M in the molding hole 11 through the mold body 100A, causing the molten alloy to solidify (primary cooling). Furthermore, this cooling water C is ejected from the nozzle 23 and sprayed onto the continuously cast rod S as it is being cast, cooling the continuously cast rod S (secondary cooling).

[0046] Furthermore, a carbon ring 30 is provided above (upstream of) the cavity 21 of the mold body 100A, facing the inner circumferential surface 100Aa of the molding hole 11. This carbon ring 30 has a lubricating oil supply path 31 and a gas supply path 32 positioned spaced apart from the lubricating oil supply path 31.

[0047] Lubricating oil Q is supplied to the inside of the mold body 100A from the lubricating oil supply path 31. The type of lubricating oil Q is not particularly limited, but it is preferable to use one with a viscosity in the range of 80 (mPa·s (25℃)) to 1100 (mPa·s (25℃)).

[0048] Furthermore, gas G is supplied to the inside of the mold body 100A from the gas supply path 32. Examples of the supplied gas include air, a gas mixture (e.g., oxygen + inert gas), and an inert gas. In this embodiment, air was used as the gas supplied from the gas supply path 32.

[0049] Figure 2 is a flowchart illustrating the step-by-step method for manufacturing a continuous cast aluminum alloy rod according to this embodiment. The method for manufacturing a continuously cast aluminum alloy rod according to this embodiment includes, for example, a molten metal injection step S1 in which molten metal M having the alloy composition of the aluminum alloy described above is injected into the inside of a mold body 100A using a vertical continuous casting apparatus 10 as described above; a lubrication step S2 in which lubricating oil Q and gas G are supplied to the inside of the mold body 100A; a primary cooling step S3 in which cooling water C, which is a cooling medium, is circulated in the cavity 21 to solidify the molten metal M and form a continuously cast rod S; and a secondary cooling step S4 in which cooling water C is directly sprayed onto the continuously cast rod S that has gone through the primary cooling step S3.

[0050] Then, the casting speed at the center E of the continuous casting rod S from the molten metal injection process S1 to the completion of the primary cooling process S3 is controlled to be within the range of 150 mm / min to 450 mm / min. In this embodiment, the cooling speed was set to 300 mm / min.

[0051] Furthermore, the cooling rate at the center E of the continuous casting rod S from the molten metal injection process S1 to the completion of the primary cooling process S3 is controlled to be within the range of 2°C / second to 20°C / second. In this embodiment, the cooling rate was set to 10°C / second.

[0052] Furthermore, in the lubrication process S2, the temperature of the air G supplied from the gas supply path 32 is controlled to be within the range of 5°C to 50°C, and the temperature of the lubricating oil Q supplied from the lubricating oil supply path 31 is controlled to be within the range of 5°C to 45°C. It is preferable to use a lubricating oil Q with a viscosity in the range of 80 (mPa·s (25°C)) to 1100 (mPa·s (25°C)).

[0053] The molten alloy injected in the molten metal injection process S1 is made by melting an aluminum material having the alloy composition of the aluminum alloy described above. By including Sr in this alloy composition within the range of 0.001% by mass or more and 0.01% by mass or less, even if the molten alloy contains a high concentration of Fe, for example 10% by mass, Al6Fe compounds will not be formed. Therefore, the continuously cast aluminum alloy rod S obtained by casting does not develop the fir wood structure shown in Figure 5.

[0054] The continuously cast aluminum alloy rod S produced by the manufacturing method of the aluminum alloy rod of this embodiment does not contain a fir wood structure, making it possible to produce aluminum products with excellent aesthetics and no color unevenness. Furthermore, since Al6Fe compounds, which are harder than aluminum, are not formed, it is possible to maintain good workability.

[0055] Furthermore, in the aluminum alloy continuous cast rod S manufactured by the manufacturing method of the aluminum alloy continuous cast rod of this embodiment, the area of ​​Al-Mn alloy particles in any rectangular cross-section is 1% or more, preferably 10% or more, of the metals excluding aluminum in the aluminum alloy. As a result, the area occupied by the highly hard α-phase Al-Fe-Mn-Si alloy is relatively reduced, making it possible to prevent a decrease in machinability due to localized hardness variations (hardness unevenness).

[0056] Although one embodiment of the present invention has been described above, these embodiments are presented as examples and are not intended to limit the scope of the invention. These embodiments can be carried out in various other forms, and various omissions, substitutions, and modifications can be made without departing from the spirit of the invention. These embodiments and their variations are included in the scope and spirit of the invention, as well as in the claims and their equivalents. [Examples]

[0057] The effects of the present invention were verified. For verification, continuous casting rods of Examples 1-6 and Comparative Examples 1-9 were cast using aluminum alloy materials with the compositions shown in Table 1, employing the vertical continuous casting apparatus 10 shown in Figure 1. Casting conditions such as casting speed, cooling rate, gas supply temperature, and lubricating oil supply temperature were the same for both Examples 1-6 and Comparative Examples 1-9, as shown in Table 2; only the composition of the aluminum alloy forming the molten metal was varied. Note that the numerical values ​​for elemental composition percentages in Table 1 are in mass percent.

[0058] [Table 1] [Table 2]

[0059] The continuous cast rods obtained from Examples 1-6 and Comparative Examples 1-9 were cut from the center along the casting direction, and the cross-sections were etched with a sodium hydroxide solution to form observation surfaces (see Figure 3). Each observation surface was then visually inspected to confirm the presence or absence of fir wood structure. The area of ​​the Al-Mn alloy was also checked, and 1% or more was marked with "○" and less than 1% with "×". Figure 4 also shows photographs of the observation surfaces of Example 1 and Comparative Example 1.

[0060] According to the results shown in Table 1, no fir-like tissue was generated in Examples 1-5, where 0.0048% by mass of Sr was added, and in Example 6, where 0.0095% by mass of Sr was added. On the other hand, in comparative examples 1-9, where Sr was not added, fir tree tissue was observed in all cases. Therefore, it was confirmed that the generation of fir tree tissue can be reliably suppressed by including Sr in a range of 0.001% by mass or more and 0.01% by mass or less.

[0061] Furthermore, in Examples 1-5, where 0.0048 mass% of Sr was added, and in Example 6, where 0.0095 mass% of Sr was added, the area ratio of the Al-Mn alloy excluding aluminum was 1% or more, whereas in Comparative Examples 1-9, the area ratio of the Al-Mn alloy was less than 1% in all cases.

[0062] Furthermore, using the same component composition as in Example 1, the percentage of aluminum-free particles in a 40 μm × 30 μm rectangular cross-section was measured for aluminum alloys cast as follows: no Sr added, with 0.005 wt% Sr added, and with 0.01 wt% Sr added.

[0063] Particle area was measured using a FE-SEM (JSM-7900F: manufactured by JEOL Ltd.), and particle diffraction was performed using a TEM detector (X-Max). N (Oxford Instruments) was used. The measurement results are shown in Table 3.

[0064] [Table 3]

[0065] As shown in Table 3, the sample without Sr added contained a high area ratio of 69.1% for the hard α-phase Al-Fe-Mn-Si alloy, whereas the samples with 0.005 wt% Sr added and 0.01 wt% Sr added showed a significant decrease in the α-phase Al-Fe-Mn-Si alloy, to 15.9% and 27.8%, respectively. Therefore, it was confirmed that adding Sr increases the proportion of Al-Mn alloy and reduces the hard α-phase Al-Fe-Mn-Si alloy that degrades workability. [Explanation of symbols]

[0066] 10…Vertical continuous casting apparatus 12...Inlet 13…Casting outlet 21... Cavity 31… Lubrication oil supply route 32...Gas supply path 100... Mold for continuous casting

Claims

1. An aluminum alloy having an alloy composition containing Si in a range of 0.6 mass% or less, Fe in a range of 1.0 mass% or less, Cu in a range of 0.2 mass% or less, Mn in a range of 1.0 mass% or more and 1.5 mass% or less, Zn in a range of 0.30 mass% or less, and Sr in a range of 0.001 mass% or more and 0.01 mass% or less, with the remainder being Al and unavoidable impurities, An aluminum alloy in which, in a rectangular cross-section of size 40 μm × 30 μm at any position inside the outer surface, the area of ​​Al-Mn alloy particles accounts for 1% or more of the total area of ​​particles of materials other than Al, when the total area of ​​particles of materials other than Al is taken as 100%.

2. The aluminum alloy according to claim 1, wherein, in the rectangular cross-section, when the total area of ​​particles of substances other than Al is taken as 100%, the area of ​​Al-Mn alloy particles accounts for 10% or more.

3. The aluminum alloy according to claim 1 or 2, wherein, in the rectangular cross-section, when the total area of ​​particles of substances other than Al is taken as 100%, the area of ​​the α-phase Al-Fe-Mn-Si alloy is less than 30%.

4. The aluminum alloy according to claim 1, further comprising Ti in an amount of 0.005% by mass or more and 0.10% by mass or less.

5. The aluminum alloy according to claim 1 or 2, further comprising B in an amount of 0.001% by mass or more and 0.02% by mass or less.

6. A cylindrical continuous cast rod made of the aluminum alloy described in claim 1 or 2, having a diameter in the range of 30 mm to 300 mm, containing Fe in the range of 0.5% to 1.0% by mass, Al ６ A continuously cast aluminum alloy rod that does not contain Fe intermetallic compounds.

7. A method for manufacturing a continuous cast aluminum alloy rod according to claim 6, A molten metal injection step in which molten alloy having the alloy composition of the aluminum alloy is injected into the mold body of a mold for continuous casting, A lubrication step in which lubricating oil and gas are supplied into the mold body, A primary cooling step involves circulating a cooling medium through a cavity formed within the mold body to solidify the molten alloy and form the continuous casting rod, The process includes a secondary cooling step in which the cooling medium is directly injected onto the continuous casting rod that has undergone the primary cooling step, A method for manufacturing a continuously cast aluminum alloy rod, comprising controlling the casting speed at the center of the continuously cast rod from the molten metal injection step to the completion of the primary cooling step so that it is within a range of 150 mm / min to 450 mm / min.

8. The method for manufacturing a continuously cast aluminum alloy rod according to claim 7, wherein in the lubrication step, the temperature of the gas is controlled to be within a range of 5°C to 50°C and the temperature of the lubricating oil is controlled to be within a range of 5°C to 45°C.

9. The method for manufacturing a continuously cast aluminum alloy rod according to claim 7, wherein in the lubrication step, the lubricating oil has a viscosity in the range of 80 (mPa·s (25°C)) to 1100 (mPa·s (25°C)).

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