EP4098382B1 - Lingot d'alliage d'aluminium et son procédé de fabrication - Google Patents

Lingot d'alliage d'aluminium et son procédé de fabrication Download PDF

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EP4098382B1
EP4098382B1 EP21750895.1A EP21750895A EP4098382B1 EP 4098382 B1 EP4098382 B1 EP 4098382B1 EP 21750895 A EP21750895 A EP 21750895A EP 4098382 B1 EP4098382 B1 EP 4098382B1
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tib
aggregates
aluminum
melt
crystal
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German (de)
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EP4098382A4 (fr
EP4098382B9 (fr
EP4098382A1 (fr
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Akihiro Minagawa
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UACJ Corp
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UACJ Corp
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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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
    • B22D21/002—Castings of light metals
    • B22D21/007—Castings of light metals with low melting point, e.g. Al 659 degrees C, Mg 650 degrees C
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D7/00—Casting ingots, e.g. from ferrous metals
    • B22D7/005—Casting ingots, e.g. from ferrous metals from non-ferrous metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/026—Alloys based on aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/06—Making non-ferrous alloys with the use of special agents for refining or deoxidising

Definitions

  • the present invention relates to an aluminum-alloy ingot and to a manufacturing method thereof.
  • a crystal-grain refining agent is sometimes added to the melt of the aluminum alloy for the purpose of refining the crystal particles in the ingot.
  • An Al-Ti-B refining agent in which a Ti-B (titanium-boron) compound, such as TiB 2 , has been dispersed in a base composed of aluminum, is used as the crystal-grain refining agent (Patent Document 1).
  • CN 106 086 538 A and CN 104 264 001 A disclose aluminum-alloy ingots comprising an aluminum matrix and TiB 2 dispersed in the aluminum matrix, which TiB 2 is not aggregated.
  • Patent Document 1 JP 2001-191654 A
  • the present invention was conceived considering this background, and an object of the present invention is to provide an aluminum-alloy ingot, comprising fine grain sizes and in which the occurrence of linear defects when performing flattening work can be curtailed, and a manufacturing method thereof.
  • the object is achieved by an aluminum-alloy ingot according to claim 1 or a method according to claim 2.
  • the aluminum-alloy ingot has TiB 2 aggregates, in which TiB 2 particles are the primary particles, in an aluminum matrix.
  • the average value of the circle-equivalent diameters and the average value of the circularities of the TiB 2 aggregates are within the above-mentioned specific ranges, respectively. This means that the aluminum-alloy ingot will be manufactured by casting a melt that contains the above-mentioned specific TiB 2 aggregates.
  • the performance of the TiB 2 aggregates in which the average value of the circle-equivalent diameters and the average value of the circularities are within the respective specific ranges, in refining the crystal particles in the aluminum matrix is high. Consequently, by forming the TiB 2 aggregates in the melt, the crystal particles in the aluminum matrix can be sufficiently refined. In addition, because the particle sizes of the TiB 2 aggregates are comparatively small, the occurrence of linear defects when performing flattening work on the aluminum-alloy ingot can be curtailed.
  • an aluminum-alloy ingot having a fine grain size and in which the occurrence of linear defects during flattening work can be curtailed, can be provided.
  • the ingot is manufactured by solidifying the melt.
  • the crystal-grain refining agent which has the above-mentioned specific composition
  • TiB 2 aggregates for which the average value of the circle-equivalent diameters and the average value of the circularities are within the respective specific ranges, can be formed in the melt.
  • solidifying such a melt the crystal particles of the ultimately obtained aluminum-alloy ingot can be easily refined, and the occurrence of linear defects when performing flattening work on the aluminum-alloy ingot can be curtailed.
  • the quality of the aluminum-alloy ingot can be improved by using methods performed in the past, that is, by melting the crystal-grain refining agent in the melt of the aluminum alloy, there is no need to add special steps or equipment to refine the crystal particles of the aluminum matrix. Therefore, according to the method of manufacturing the aluminum alloy, an aluminum-alloy ingot having excellent quality can be obtained while avoiding an increase in the cost of manufacturing the aluminum-alloy ingot.
  • the chemical composition of the above-mentioned aluminum-alloy ingot is not particularly limited and may be any kind of aluminum alloy. It is noted that the "aluminum alloy" described above is a concept that encompasses pure aluminum.
  • the above-mentioned aluminum-alloy ingot may have a chemical composition classified as A1000-series aluminum or may have a chemical composition classified as A2000-series alloys, A3000-series alloys, A4000-series alloys, A5000-series alloys, A6000-series alloys, A7000-series alloys, or A8000-series alloys.
  • the above-mentioned aluminum-alloy ingot preferably has a chemical composition that contains one or two or more of elements selected from the group consisting of Si (silicon): 0.01 mass% or more and 14.0 mass% or less, Fe (iron): 0.01 mass% or more and 2.0 mass% or less, Cu (copper): 0.01 mass% or more and 7.0 mass% or less, Mg (magnesium): 0.01 mass% or more and 7.0 mass% or less, Mn (manganese): 0.01 mass% or more and 2.0 mass% or less, and Ti (titanium): 0.003 mass% or more and 0.3 mass% or less, the remainder being Al (aluminum) and unavoidable impurities.
  • the aluminum-alloy ingot contains an aluminum matrix and TiB 2 aggregates. Depending on the chemical composition, the aluminum-alloy ingot may contain crystallized products. In addition, the aluminum-alloy ingot may contain unaggregated TiB 2 particles.
  • the aluminum matrix contains aluminum atoms and solid-solution elements in accordance with the chemical composition of the above-mentioned aluminum-alloy ingot.
  • the aluminum matrix is composed of numerous crystal particles.
  • the crystal-particle sizes of the aluminum matrix vary in accordance with the chemical composition of the above-mentioned aluminum-alloy ingot; in an aluminum-alloy ingot that contains the above-mentioned specific TiB 2 aggregates, the mean particle size of the aluminum matrix is usually within the range of 50 ⁇ m or more and 5,000 ⁇ m or less.
  • the TiB 2 aggregates are dispersed in the aluminum matrix, in which aggregates of the TiB 2 particles serve as primary particles.
  • the particle size of each individual TiB 2 particle contained in the TiB 2 aggregates may be, for example, 0.1 ⁇ m or more and 5.0 ⁇ m or less.
  • the average value of the circle-equivalent diameters of the above-mentioned TiB 2 aggregates in the state in which the TiB 2 aggregates are exposed from the above-mentioned aluminum matrix is 3.0 ⁇ m or less.
  • the lower limit of the average value of the circle-equivalent diameters of the TiB 2 aggregates is not particularly limited, but the average value of the circle-equivalent diameters of the TiB 2 aggregates formed by the manufacturing method of the above-mentioned aspect is usually 1.0 ⁇ m or more.
  • the average value of the circle-equivalent diameters of the TiB 2 aggregates described above is a value that is calculated by the following method. First, a test piece is collected from the interior of the aluminum-alloy ingot. Subsequently, the aluminum matrix on the surface of the test piece is removed by a method such as dip etching. By observing the surface of the test piece using an electron microscope or the like, an enlarged photograph of the TiB 2 aggregates is taken. The circle-equivalent diameter of each individual TiB 2 aggregate is calculated based on the projection-surface area of the TiB 2 aggregate in the enlarged photograph that was taken.
  • the average value of the circle-equivalent diameters of the TiB 2 aggregates can be obtained.
  • the number of TiB 2 aggregates used when calculating the average value of the circle-equivalent diameters should be, for example, 3 or more.
  • the average value of the circularities of the above-mentioned TiB 2 aggregates in the state in which the TiB 2 aggregates are exposed from the above-mentioned aluminum matrix is 0.20 or more.
  • the circularity of a TiB 2 aggregate is a value that becomes an indication of whether the shape of the TiB 2 aggregate is close to a sphere and means that, the closer the circularity is to 1, the closer the shape of the TiB 2 aggregate is to a sphere.
  • TiB 2 aggregates having a variety of shapes are usually formed in the melt. Furthermore, the more that the TiB 2 aggregates in the melt have a shape in which the circularity is large and therefore the shape is close to a sphere, the more the TiB 2 aggregates have the property of tending to function as heterogenous nuclei. Accordingly, by setting the average value of the circularities of the TiB 2 aggregates to 0.20 or more, it is possible to increase the proportion of the TiB 2 aggregates, among the TiB 2 aggregates formed during casting, that can function as heterogenous nuclei.
  • the upper limit of the average value of the circularities of the TiB 2 aggregates is not particularly limited, but the average value of the circularities of the TiB 2 aggregates formed by the manufacturing method of the above-mentioned aspect is usually 0.8 or less.
  • the average value of the circularities of the TiB 2 aggregates described above specifically is a value that is calculated by the following method.
  • the average value of the circularities of the TiB 2 aggregates can be obtained.
  • the number of TiB 2 aggregates used when calculating the average value of the circularities should be, for example, 3 or more.
  • the functions and effects thereof described above can be increased, and the amount of the crystal-grain refining agent added in the casting process can be decreased while ensuring the effect of refining the crystal particles.
  • the average value of the circle-equivalent diameters and the average value of the circularities of the TiB 2 aggregates are set to within the above-mentioned specific ranges, respectively. Accordingly, in casting processes of the above-mentioned aluminum-alloy ingot, by setting the average value of the circle-equivalent diameters and the average value of the circularities of the TiB 2 aggregates to within the above-mentioned specific ranges, respectively, the number of TiB 2 aggregates that can function as heterogenous nuclei can be made large and, in turn, the effect of refining the crystal particles in the aluminum matrix can be increased.
  • the effect due to the decrease in the circle-equivalent diameters and the effect due to the increase in circularity can be made to function synergistically.
  • the amount of the crystal-grain refining agent added during casting can be decreased more than in the past while maintaining the effect of refining the crystal particles.
  • the content of the TiB 2 aggregates in the aluminum-alloy ingot is set to 0.0001 mass% or more and 0.0010 mass% or less based on the boron atoms.
  • a method can be used that comprises: a melting step, in which the crystal-grain refining agent is caused to melt in the melt of the aluminum alloy; and, after the melting step, a casting step that casts the melt.
  • the crystal-grain refining agent added into the melt in the above-mentioned manufacturing method has a base composed of aluminum.
  • the shape of the base is not particularly limited and may have, for example, a rod shape, a plate shape, or the like.
  • the base contains TiB 2 particles.
  • the TiB 2 particles are dispersed within the base and may exist in an unaggregated state.
  • TiB 2 aggregates may be formed in the base by aggregation of a plurality of the TiB 2 particles. More specifically, all the TiB 2 particles in the base may exist in an unaggregated state, or all the TiB 2 particles in the base may exist in a TiB 2 aggregate state. Furthermore, both TiB 2 particles and TiB 2 aggregates may exist in the base in an unaggregated state.
  • the TiB 2 particles in the base after the crystal-grain refining agent has melted into the melt in the melting step, the TiB 2 particles aggregate in the melt to form TiB 2 aggregates.
  • the TiB 2 aggregates in the base when the crystal-grain refining agent has melted in the melt in the melting step, the TiB 2 aggregates migrate into the melt while maintaining the aggregated state. For that reason, by causing the crystal-grain refining agent, which contains TiB 2 particles, to melt in the aluminum melt, TiB 2 aggregates can be formed in the melt.
  • the crystal-grain refining agent according to any of the aspects below can be melted in the melt. That is, in a first aspect of the crystal-grain refining agent, the average value of the center-to-center distances of adjacent TiB 2 particles is 0.60 ⁇ m or more in an arbitrary cross section of the above-mentioned crystal-grain refining agent.
  • the center-to-center distances of the TiB 2 particles in the crystal-graining agent to within the above-mentioned specific range, the aggregation of TiB 2 particles and the growth of TiB 2 aggregates when the crystal-grain refining agent has been melted in the melt can be curtailed.
  • the average value of the circle-equivalent diameters and the average value of the circularities of the TiB 2 aggregates formed in the melt can be easily set to within the above-mentioned specific ranges, respectively.
  • the average value of the center-to-center distances of the TiB 2 particles described above is a value that is calculated by the following method.
  • the crystal-grain refining agent is cut to expose a cut surface. This cut surface is observed using an electron microscope or the like, and an enlarged photograph of the cut surface is taken. With regard to the enlarged photograph that was taken, the center of gravity of each TiB 2 particle present in the enlarged photograph is determined. It is noted that both the TiB 2 particles present in an undispersed state and the TiB 2 particles that constitute a portion of the TiB 2 aggregates are included in the TiB 2 particles present in the enlarged photograph.
  • the TiB 2 particles that will become the objects to be measured for the center-to-center distances are determined from among the TiB 2 particles present in the enlarged photograph. Furthermore, the distance between the center of gravity of the TiB 2 particle that is the object to be measured and the center of gravity of the TiB 2 particle closest to the TiB 2 particle that is the object to be measured is measured, and that value is set as the center-to-center distance of the TiB 2 particle that is the object to be measured. By performing the above operation on all TiB 2 particles present in the enlarged photograph, the arithmetic-mean value of the obtained center-to-center distances is set as the average value of the center-to-center distances of the TiB 2 particles.
  • the TiB 2 aggregates in the crystal-grain refining agent have a particle-size distribution in which the average value of the circle-equivalent diameters of the TiB 2 aggregates, which have a projection-surface area in the 95 th percentile or higher, is 3.0 ⁇ m or less.
  • the TiB 2 aggregates having large circle-equivalent diameters effectively function as heterogenous nuclei in the aluminum melt.
  • the possibility that the crystal-grain refining agent will contain coarse TiB 2 aggregates can be made low and, in turn, the mixing of the coarse TiB 2 aggregates into the melt can be curtailed.
  • the average value of the circle-equivalent diameters and the average value of the circularities of the TiB 2 aggregates formed in the melt can be set easily to within the above-mentioned specific ranges, respectively.
  • the average value of the circle-equivalent diameters of the TiB 2 aggregates described above is a value calculated by the following method.
  • the crystal-grain refining agent is cut to expose a cut surface.
  • the cutting direction of the crystal-grain refining agent is not particularly limited.
  • the crystal-grain refining agent should be cut through its center in a plane perpendicular to the longitudinal direction.
  • the TiB 2 aggregates are exposed from the base by removing a peripheral portion of the TiB 2 aggregates at the base.
  • a method such as dip etching can be used as the method of removing the base.
  • the TiB 2 aggregates that have been exposed from the base are observed using an electron microscope or the like, and an enlarged photograph of the TiB 2 aggregates is taken.
  • the surface area of each TiB 2 aggregate in the enlarged photograph is taken as the projection-surface area of the TiB 2 aggregate. It is noted that an image-analyzing apparatus or the like can be used in the calculation of the projection-surface area and the calculation of the circle-equivalent diameter of each TiB 2 aggregate.
  • the above operation is performed for 2,000 or more TiB 2 aggregates randomly selected from the TiB 2 aggregates present at the cut surface of the crystal-grain refining agent. Based on the projection-surface areas of the TiB 2 aggregates obtained in this manner, the 95 th percentile of the projection-surface areas is calculated. It is noted that, in the situation in which a plurality of numerical values is sorted in order from the smallest numerical value to the largest numerical value, the percentile is a numerical value in which the number of numerical values counting from the smallest numerical value is the desired percentage of the total number of numerical values.
  • the largest value of the values in which the number of numerical values counting from the smallest numerical value is less than the desired percentage of the total number of the numerical values, is taken as the percentile.
  • the 95 th percentile of the projection-surface areas is the value in which the number of TiB 2 aggregates having a projection-surface area in the 95 th percentile or higher is 5% of the total number of TiB 2 aggregates for which the projection-surface area was measured.
  • the circle-equivalent diameters of the TiB 2 aggregates having a projection-surface area in the 95 th percentile or higher are calculated. It is noted that a circle-equivalent diameter is the diameter of a circle having a surface area equal to the projection-surface area of a TiB 2 aggregate. Furthermore, by calculating the mean average of the circle-equivalent diameters of the obtained TiB 2 aggregates, the average value of the circle-equivalent diameters of the TiB 2 aggregates having a projection-surface area in the 95 th percentile or higher can be obtained.
  • the content of the TiB 2 particles in the crystal-grain refining agent can be set to, for example, 0.5 mass% or more and 3.2 mass% or less. In this situation, the average value of the center-to-center distances of adjacent TiB 2 particles tends to become large. As a result, the effect of curtailing the aggregation of the TiB 2 particles when the crystal-grain refining agent has been melted in the melt can be exhibited more reliably.
  • the above-mentioned crystal-grain refining agent is melted in the melt of an aluminum alloy having a desired chemical composition.
  • the melt may be stirred as needed to evenly disperse the TiB 2 particles in the crystal-grain refining agent in the melt.
  • the aluminum-alloy ingot can be manufactured by casting the melt.
  • the casting method is not particularly limited; for example, methods such as semicontinuous casting, continuous casting, and the like can be used.
  • An aluminum-alloy ingot manufactured by these methods can be used in the manufacture of flattened materials such as rolled plates, extruded materials, and the like.
  • by cooling the aluminum-alloy melt described above after the melt has been poured into a mold or a sand mold it is also possible to obtain an ingot having a desired article shape or a shape close to the desired article shape.
  • the crystal-grain refining agent after the crystal-grain refining agent has been melted into the melt, it is preferable to cast the melt within 30 min.
  • the specific gravity of the TiB 2 particles is greater than that of the melt. Consequently, when the elapsed time since the point in time when the crystal-grain refining agent was melted into the melt becomes long, the TiB 2 particles precipitate owing to their intrinsic weight, and the TiB 2 particles tend to aggregate at the lower portion of the crucible. As a result, there is a risk that coarse TiB 2 aggregates will tend to be formed.
  • the aluminum-alloy ingot and the manufacturing method thereof described above can also be understood as the invention of a crystal-grain refining agent in which the distribution state of TiB 2 particles is specified.
  • a first aspect of the crystal-grain refining agent comprises:
  • the crystal-grain refining agent comprises:
  • crystal-grain refining agent can be manufactured by, for example, the following manufacturing method.
  • TiB 2 particles having a narrow particle-size distribution range As the TiB 2 particles that are blown into the melt, and it is more preferable to use TiB 2 particles having a particle-size standard deviation of 0.5 ⁇ m or less.
  • nitrogen gas, argon gas, or the like can be used as the inert gas.
  • the standard deviation of the particle sizes of the TiB 2 particles is a value that is calculated based on the particle-size distribution on a volume basis.
  • a laser-diffracting, particle-size-distribution measuring apparatus can be used.
  • Working Examples 1, 2 and Comparative Examples 1, 2 are examples of aluminum-alloy ingots composed of pure aluminum.
  • a melt was prepared by melting aluminum metal having a purity of 99.7 mass%. After the temperature of the melt was set to 718°C, a crystal-grain refining agent, in which TiB 2 particles are dispersed in a base composed of aluminum, was added such that the boron atoms reached 10 mass ppm.
  • Crystal-grain refining agents used in the present example specifically had a chemical composition containing Ti: 1.0 mass% or more and 5.5 mass% or less and B: 0.1 mass% or more and 1.5 mass% or less, the remainder being Al and unavoidable impurities, and had a base composed of aluminum and TiB 2 particles present in the base. Some of the TiB 2 particles existed in an unaggregated state, the remainder being composed of TiB 2 aggregates.
  • the center-to-center distances between adjacent TiB 2 particles in an arbitrary cross section of the crystal-grain refining agent of the present example are the values shown in Table 1.
  • the TiB 2 aggregates in the crystal-grain refining agent had particle-size distributions in which the average values of the circle-equivalent diameters of the TiB 2 aggregates, which have a proj ection-surface area in the 95 th percentile or higher, are the values shown in Table 1.
  • the melt was stirred for 30 seconds using a graphite rod in the state in which the temperature of the melt was maintained at 718°C, and the crystal-grain refining agent was sufficiently melted.
  • the melt was once again stirred for 15 seconds using a graphite rod.
  • a ladle which was made of iron and prepared in accordance with the AA-TP1 standard, was immersed into the melt, and the cup portion of the ladle was filled with the melt. Furthermore, at the point in time when 10 min had elapsed since the point in time when the crystal-grain refining agent was added, the ladle was lifted up from the melt, thereby scooping up the melt in the cup portion. Subsequently, the cup portion of the ladle was cooled using a water-cooling apparatus that is compliant with the AA-TP1 standard, and the melt was caused to solidify.
  • the aluminum-alloy ingots for Working Examples 1, 2 and Comparative Examples 1, 2 were obtained by the above. These aluminum-alloy ingots all exhibited a circular, truncated-cone shape.
  • the aluminum-alloy ingot was cut at a cross section, from among the circular end surfaces of the aluminum-alloy ingot, at which the height from the plane having a small diameter (that is, the plane that is adjacent to the bottom surface of the ladle) was 38 mm, thereby exposing the cut surface. After this cut surface was polished, aluminum matrix was removed by performing dip etching, thereby exposing the entirety of the TiB 2 aggregates.
  • FIG. 1 shows an enlarged photograph of TiB 2 aggregates contained in an aluminum-alloy ingot of Working Example 1
  • FIG. 2 shows an enlarged photograph of TiB 2 aggregates contained in an aluminum-alloy ingot of Comparative Example 2.
  • a TiB 2 aggregate 2 in the aluminum matrix 1 exhibits a lump shape, in which numerous TiB 2 particles 3 are aggregated.
  • the surface area of each of the TiB 2 aggregates 2 in the enlarged photographs was calculated using image-analyzing software, and the circle-equivalent diameter of each TiB 2 aggregate was calculated based on the surface area of the TiB 2 aggregate 2.
  • the above operation was performed on eight randomly selected TiB 2 aggregates, and the value of the arithmetic mean of these circle-equivalent diameters was taken as the average value of the circle-equivalent diameters of the TiB 2 aggregates.
  • Table 1 shows the average value of the circle-equivalent diameters of the TiB 2 aggregates for each of the aluminum-alloy ingots.
  • each of the TiB 2 aggregates 2 in the enlarged photograph described above was calculated using image-analyzing software. Furthermore, the circularity of each of the TiB 2 aggregates was calculated based on the surface area and the circumferential length of each of the TiB 2 aggregates 2. The above operation was performed on three or more randomly selected TiB 2 aggregates, and the value of the arithmetic mean of these circularities was taken as the average value of the circularities of the TiB 2 aggregates. Table 1 shows the average value of the circularities of the TiB 2 aggregates for each of the aluminum-alloy ingots.
  • Working Example 3 is an example of an aluminum-alloy ingot composed of an A3000-series alloy.
  • a melt composed of an A3000-series alloy was prepared using a heating furnace, after which a crystal-grain refining agent was added to the melt such that the boron atoms reached 10 mass ppm.
  • the crystal-grain refining agent used in the present example is the same as that in Working Example 1 except for: the point that it had a chemical composition containing Ti: 5.0 mass% and B: 1.0 mass%, the remainder being Al and unavoidable impurities; the point that the center-to-center distances between adjacent TiB 2 particles at an arbitrary cross section of the crystal-grain refining agent are the values shown in Table 1; and the point that the average value of the circle-equivalent diameters of the TiB 2 aggregates, which have a projection-surface area in the 95 th percentile or higher, is the value shown in Table 1.
  • the melt was stirred for 30 seconds using a graphite rod. Subsequently, the melt was cast using a DC-casting method. Thus, the aluminum-alloy ingot of Working Example 3 was obtained.
  • the aluminum-alloy ingot of Working Example 3 exhibits a rectangular-parallelepiped shape.
  • Working Example 4 is an example of an aluminum-alloy ingot composed of an A1000-series aluminum.
  • the melt of the aluminum alloy was cast using the same method as that in Working Example 3, except for the point that the melt composed of the A1000-series aluminum was prepared using a heating furnace. Thereby, the aluminum-alloy ingot of Working Example 4 was obtained.
  • the aluminum-alloy ingot of Working Example 4 exhibited a rectangular-parallelepiped shape, the same as in Working Example 3.
  • the aluminum-alloy ingot is cut and a test piece is collected from a center portion in the width direction and the thickness direction. A surface of the test piece is polished, after which the test piece is subject to dip etching to remove aluminum matrix, thereby exposing the entirety of the TiB 2 aggregates. Thereafter, the average value of the circle-equivalent diameters and the average value of the circularities of the TiB 2 aggregates should be calculated using the same method as in Working Example 1, etc. Table 1 shows these values for the aluminum-alloy ingots of Working Examples 3, 4.
  • the average value of the circle-equivalent diameters and the average value of the circularities of the TiB 2 aggregates contained in the aluminum-alloy ingots of Working Examples 1-4 were within the above-mentioned specific ranges, respectively. For this reason, with regard to these aluminum-alloy ingots, the crystal particles in the aluminum matrix were sufficiently refined, there were few coarse TiB 2 aggregates, and the occurrence of linear defects when performing processing such as rolling could be curtailed.

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Claims (3)

  1. Lingot d'alliage d'aluminium comprenant :
    une matrice d'aluminium (1) ; et
    des agrégats de TiB2 (2), qui sont dispersés dans la matrice d'aluminium (1) et où sont agrégées des particules de TiB2 (3) ;
    dans lequel la valeur moyenne des diamètres de cercle équivalents des agrégats de TiB2 (2) dans l'état dans lequel les agrégats de TiB2 (2) sont exposés à partir de la matrice d'aluminium (1), mesurée et calculée par le procédé décrit dans la description, est de 3,0 µm ou moins et la valeur moyenne des circularités, mesurée et calculée par le procédé décrit dans la description, est de 0,20 ou plus, dans lequel la teneur des agrégats de TiB2 (2) est de 0,0001 % en masse ou plus, et 0,0010 % en masse ou moins sur la base des atomes de bore.
  2. Procédé de fabrication du lingot d'alliage d'aluminium selon la revendication 1, comprenant :
    une étape de fusion, au cours de laquelle un agent d'affinage de grain cristallin est fondu dans un alliage d'aluminium ; et
    une étape de coulée, au cours de laquelle, après l'étape de fusion, la matière fondue est coulée,
    dans lequel l'agent d'affinage de grain cristallin a une base composée d'aluminium contenant des agrégats de TiB2 (2) dans lesquels des particules de TiB2 (3) sont agrégées et la valeur moyenne des distances centre à centre entre des particules de TiB2 adjacentes (3) dans une section transversale arbitraire, mesurée et calculée par le procédé décrit dans la description, est égale ou supérieure à 0.60 µm ou plus, et
    dans lequel, dans la situation où les surfaces de projection de 2 000 agrégats de TiB2 (2) ou plus ont été mesurées dans l'état dans lequel les agrégats de TiB2 (2) ont été exposés à partir de la base, mesurées et calculées par le procédé dans la description, les agrégats de TiB2 (2) dans l'agent d'affinage de grain cristallin ont une distribution granulométrique dans laquelle la valeur moyenne des diamètres de cercle équivalents des agrégats de TiB2 (2), qui ont une surface de projection dans le 95ème percentile ou plus, est de 3.0 µm ou moins.
  3. Procédé de fabrication d'un lingot d'alliage d'aluminium selon la revendication 2, dans lequel la matière fondue est coulée dans les 30 minutes qui suivent la fusion de l'agent d'affinage de grain cristallin de cristal dans la matière fondue.
EP21750895.1A 2021-02-05 Lingot d'alliage d'aluminium et son procédé de fabrication Active EP4098382B9 (fr)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
JP2020018896 2020-02-06
JP2020109517A JP2021123789A (ja) 2020-02-06 2020-06-25 アルミニウム合金鋳塊及びその製造方法
PCT/JP2021/004225 WO2021157683A1 (fr) 2020-02-06 2021-02-05 Lingot d'alliage d'aluminium et son procédé de fabrication

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EP4098382A1 EP4098382A1 (fr) 2022-12-07
EP4098382A4 EP4098382A4 (fr) 2022-12-21
EP4098382B1 true EP4098382B1 (fr) 2024-04-03
EP4098382B9 EP4098382B9 (fr) 2024-07-10

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CN114761152A (zh) 2022-07-15
US20230075358A1 (en) 2023-03-09
EP4098382A1 (fr) 2022-12-07
WO2021157683A1 (fr) 2021-08-12

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