EP4043601A1 - Alliage d'aluminium - Google Patents

Alliage d'aluminium Download PDF

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Publication number
EP4043601A1
EP4043601A1 EP20873687.6A EP20873687A EP4043601A1 EP 4043601 A1 EP4043601 A1 EP 4043601A1 EP 20873687 A EP20873687 A EP 20873687A EP 4043601 A1 EP4043601 A1 EP 4043601A1
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EP
European Patent Office
Prior art keywords
aluminum alloy
alloy material
less
orientation density
strength
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Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Pending
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EP20873687.6A
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German (de)
English (en)
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EP4043601A4 (fr
Inventor
Tomohito KUROSAKI
Tadashi Minoda
Mitsuhiro Tamaki
Jin-Gyo Kim
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UACJ Corp
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UACJ Corp
Glolnix Co Ltd
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Publication of EP4043601A1 publication Critical patent/EP4043601A1/fr
Publication of EP4043601A4 publication Critical patent/EP4043601A4/fr
Pending legal-status Critical Current

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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
    • C22C21/06—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
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
    • 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

Definitions

  • the present invention relates to a high-strength aluminum alloy material having reduced strength anisotropy.
  • Typical high-strength aluminum alloys include, for example, a 6000 series alloy and a 7000 series alloy.
  • the above-described alloys are heat-treatable alloys, which require solution treatment and aging heat treatment, and thus have a problem of low production efficiency.
  • the 7000 series alloy contains Zn and Cu in a large amount, and thus have a problem of causing corrosion to easily occur depending on usage environments.
  • non-heat-treatable aluminum alloys are used in some cases.
  • Typical non-heat-treatable aluminum alloys include a 5000 series alloy, which has the highest strength.
  • the 5000 series alloy which typically has excellent corrosion resistance, does not require the solution treatment and the aging heat treatment, so that the 5000 series alloy is produced with high efficiency.
  • increase in the amount of an element added to the 5000 series alloy makes it possible to achieve the 5000 series alloy having strength not less than that of a 6000 series alloy.
  • a 5000 series aluminum alloy material containing not less than 5% by weight of Mg, which is a major additive element (see Patent Literatures 1 to 3).
  • Patent Literatures 1 to 3 The contents of Mg in the aluminum alloy materials described in the above Patent Literatures 1 to 3 are increased to an amount of not less than 5% by weight to make the aluminum alloy material stronger. However, Patent Literatures 1 to 3 do not give any consideration to strength anisotropy of the aluminum alloy materials.
  • an end product has low rigidity in a particular direction, so that the reliability of the end product could decrease.
  • failure in dimension accuracy or other accuracy could occur in a production process such as press forming.
  • an aluminum alloy material (O tempered material) which has been annealed is required to have high formability, and therefore, the O tempered material having high strength anisotropy could lead to the occurrence of cracking in a press forming process.
  • an aluminum alloy material in accordance with an aspect of the present invention contains Mg: 7.0% to 10.0% (% by mass, the same applies hereinafter) and Ca: not more than 0.1%, the aluminum alloy material containing a remainder constituted by aluminum and an inevitable impurity, the aluminum alloy material having a tensile strength of not less than 300 MPa and less than 500 MPa and an elongation of not less than 20%.
  • An aspect of the present invention makes it possible to produce an aluminum alloy material which has both high strength and reduced strength anisotropy.
  • Fig. 1 is a view illustrating measurement directions of tensile strengths of an aluminum alloy material in the present embodiment.
  • the inventors of the present invention diligently investigated and studied alloy composition and metal structure which enable reduction in the strength anisotropy of a high-strength aluminum alloy material containing Mg (magnesium) in a large amount.
  • the inventors eventually found that it is possible to reduce the strength anisotropy by controlling an appropriate metal structure through adjustments to the alloy composition and to a production process.
  • Mg manganesium
  • the content of Mg in the aluminum alloy being not less than 7.0% makes it possible to sufficiently obtain the effect of improving strength.
  • the content of Mg in the aluminum alloy exceeding 10.0% causes occurrence of cracking during hot rolling, and thus could lead to difficulty in production. Accordingly, the content of Mg in the aluminum alloy is preferably in a range of not less than 7.5% and not more than 9.0%, and more preferably in a range of not less than 7.5% and not more than 8.5%.
  • Ca (Calcium) is present in the aluminum alloy mainly in the form of a compound. Even trace amounts of Ca cause cracking during hot working, and thus could lower workability.
  • the content of Ca in the aluminum alloy being not more than 0.1% makes it possible to prevent cracking during hot working.
  • the content of Ca in the aluminum alloy is more preferably not more than 0.05%.
  • Si forms mainly second phase particles (for example, single Si, Al-Si-Fe-Mn-based compound), and has an effect of making crystal grains finer by acting as a nucleation site for recrystallization.
  • the content of Si in the aluminum alloy being not less than 0.02% makes it possible to successfully obtain the effect of making crystal grains finer.
  • the content of Si in the aluminum alloy exceeding 0.3% cause generation of a large amount of coarse second phase particles, and thus could lower the elongation of a produced aluminum alloy material. Accordingly, the content of Si in the aluminum alloy is preferably in a range of not less than 0.02% and not more than 0.2%, and more preferably in a range of not less than 0.02% and not more than 0.15%.
  • Fe (iron) is present mainly in the form of second phase particles (such as an Al-Fe-based compound), has an effect of making crystal grains finer by acting as a nucleation site for recrystallization.
  • the content of Fe in the aluminum alloy being not less than 0.02% makes it possible to obtain the effect of making crystal grains finer.
  • the content of Fe in the aluminum alloy exceeding 0.5% causes generation of a large amount of coarse second phase particles, and thus could lower the elongation of a produced aluminum alloy material. Accordingly, the content of Fe in the aluminum alloy is preferably in a range of not less than 0.02% and not more than 0.25%, and more preferably in a range of not less than 0.02% and not more than 0.2%.
  • Cu copper
  • the content of Cu in the aluminum alloy being not less than 0.05% makes it possible to sufficiently obtain the effect of improving strength.
  • the content of Cu in the aluminum alloy exceeding 1.0% causes occurrence of cracking during hot rolling, and thus could lead to difficulty in production. Accordingly, the content of Cu in the aluminum alloy is preferably in a range of not less than 0.05% and not more than 0.5%, and more preferably in a range of not less than 0.10% and not more than 0.3%.
  • Mn manganese
  • Al-Mn-based compound an Al-Mn-based compound
  • the content of Mn in the aluminum alloy being not less than 0.05% makes it possible to sufficiently obtain the effect of making crystal grains finer.
  • the content of Mn in the aluminum alloy exceeding 1.0% causes generation of a large amount of coarse second phase particles, and thus lower the elongation of a produced aluminum alloy material. Accordingly, the content of Mn in the aluminum alloy is preferably in a range of not less than 0.1% and not more than 0.5%, and more preferably in a range of not less than 0.15% and not more than 0.3%.
  • Cr chromium
  • V vanadium
  • Zr zirconium
  • second phase particles such as an Al-Fe-Mn-based compound, an Al-Cr-based compound, an Al-V-based compound, and an Al-Zr-based compound
  • the content of Cr or V in the aluminum alloy being not less than 0.05% or the content of Zr in the aluminum alloy being not less than 0.02% makes it possible to sufficiently obtain the effect of making crystal grains finer.
  • the content of Cr or V in the aluminum alloy exceeding 0.3%, or the content of Zr exceeding 0.2% causes generation of a large amount of coarse second phase particles, and thus could lower the elongation of a produced aluminum alloy material.
  • the content of Cr or V in the aluminum alloy is preferably not more than 0.2%.
  • the content of Zr in the aluminum alloy is preferably 0.1%.
  • the contents of Cr, V, and Zr in the aluminum alloy are not limited to the above respective contents, provided that at least one of Cr, V, and Zr is contained in the aluminum alloy.
  • Ti titanium inhibits the growth of a solidified phase of aluminum formed during casting and makes a cast structure finer, thus having an effect of preventing a defect such as cracking during casting.
  • an excessively high content of Ti in the aluminum alloy makes second phase particles coarse, and thus could decrease the elongation of a produced aluminum alloy material.
  • the content of Ti in the aluminum alloy being not more than 0.2% makes it possible to prevent a decrease in the elongation of the produced aluminum alloy material.
  • the content of Ti in the aluminum alloy is more preferably not more than 0.1%. Note that substances other than the elements described above are basically Al and an inevitable impurity.
  • the present embodiment enables production of an aluminum alloy material (H tempered material) having a tensile strength of not less than 300 MPa and less than 500 MPa and an elongation of not less than 20%, by performing production treatments (which will be discussed later) on the aluminum alloy of the above composition.
  • H tempered material H tempered material
  • This makes it possible to prevent an end product from having poor strength due to the aluminum alloy having a tensile strength falling below 300 MPa. It is also possible to prevent the occurrence of a defect such as cracking during working on the end product due to the aluminum alloy having an elongation falling below 20%.
  • the tensile strength of the aluminum alloy material is more preferably not less than 350 MPa. Further, the elongation of the aluminum alloy material is more preferably not less than 25%.
  • an aluminum alloy material 1 of the present embodiment is set such that, in a plane defined by a rolling direction (a final working direction) during a final rolling using a set of rolls 2 and a transverse direction, a standard deviation of tensile strengths is not more than 10 [MPa], wherein the tensile strengths are: a tensile strength in a 0° direction forming an angle of 0° with the rolling direction toward the transverse direction, a tensile strength in a 45° direction forming an angle of 45° with the rolling direction toward the transverse direction, and a tensile strength in a 90° direction forming an angle of 90° with the rolling direction towards the transverse direction.
  • the standard deviation of the tensile strengths of the aluminum alloy material 1 is preferably not more than 5 [MPa], and more preferably not more than 3 [MPa].
  • the aluminum alloy material of the present embodiment is set to have a ⁇ 013 ⁇ 100> orientation density and a ⁇ 011 ⁇ 100> orientation density which are calculated using a Crystallite Orientation Distribution Function (ODF) and which are each not more than 5 (for example, approximately 1).
  • ODF Crystallite Orientation Distribution Function
  • the aluminum alloy material of the present embodiment is set to have a ⁇ 123 ⁇ 634> orientation density of not more than 5 and a ⁇ 001 ⁇ 100> orientation density of not more than 5.
  • Such a setting is made in consideration of the fact that the ⁇ 123 ⁇ 634> orientation density and the ⁇ 001 ⁇ 100> orientation density both exceeding 5 could make the strength anisotropy remarkable.
  • the following description will discuss a method for producing the aluminum alloy material in accordance with the present embodiment.
  • the method for producing the aluminum alloy material of the present embodiment is carried out in the order of a casting step, a homogenization step, a hot rolling step, a cold rolling step, and an anneal step. Steps of the production method are not limited to these steps, which are illustrated by way of example.
  • a slab is casted in the casting step by a semi-continuous casting process such as a Direct Chill (DC) casting process and a hot top process.
  • the casting speed in the casting step is preferably 20 mm/min to 100 mm/min to prevent formation of coarse second phase particles.
  • the treatment temperature is set to not less than 400°C and not more than 490°C. This is because (i) the treatment temperature being not more than 400°C could cause insufficient homogenization, and (ii) the treatment temperature exceeding 490°C could cause melting of an AI-Mg-based compound remaining without dissolving as a solid solution, and thus cause a defect such as cracking during the hot rolling. Further, coarsening of second phase particles excessively progresses, and crystal grains in a particular orientation tend to preferentially grow in the subsequent recrystallization process, so that the strength anisotropy could decrease.
  • a two-stage homogenization treatment may be carried out.
  • the treatment temperature for the first stage is set to not less than 400°C and not more than 450°C. This is because (i) the treatment temperature for the first stage being not more than 400°C could cause insufficient homogenization, and (ii) the treatment temperature for the first stage exceeding 450°C could cause melting of an AI-Mg-based compound remaining without dissolving as a solid solution, and thus cause a defect such as cracking during the hot rolling.
  • the treatment time for the first stage is set to be in a range of not less than five hours and not more than 20 hours. This is because (i) the treatment time for the first stage being less than five hours causes insufficient homogenization, and (ii) the treatment time for the first stage exceeding 20 hours causes decrease in productivity. Carrying out the homogenization treatment in the first stage with the treatment temperature and the treatment time being appropriately set as described above makes it possible to cause the AI-Mg-based compound to dissolve as a solid solution, and thus enables homogenization at a higher temperature.
  • the treatment temperature for the second stage is set to not less than 450°C and not more than 490°C. This is because (i) the treatment temperature for the second stage being less than 450°C causes insufficient homogenization, and (ii) the treatment temperature for the second stage exceeding 490°C causes oxidization of Mg on the surface to progress and thus could decrease concentration of Mg on the surface.
  • the treatment time for the second stage is set to be in a range of not less than five hours and not more than 20 hours. This is because (i) the treatment time for the second stage being less than five hours causes insufficient homogenization, and (ii) the treatment time for the second stage exceeding 20 hours causes coarsening of second phase particles to excessively progress, causes crystal grains in a particular orientation to tend to preferentially grow in the subsequent recrystallization process, and thus could decrease the strength anisotropy.
  • the hot rolling step is carried out.
  • the starting temperature for the hot rolling is set to be in a range of not less than 350°C and not more than 480°C. This is because (i) the treatment temperature for the hot rolling being less than 350°C could make the rolling difficult due to excessively high deformation resistance, and (ii) the treatment temperature for the hot rolling exceeding 480°C causes the material to partially melt, and thus could lead to the occurrence of cracking. Note that the hot rolling step may be carried out with the homogenization step omitted.
  • the cold rolling step is carried out.
  • the cold rolling is carried out such that a rolling reduction from the plate thickness at the time of completion of the hot rolling step to the plate thickness at the time of completion of the cold rolling step (a ratio of a plate thickness after working to a plate thickness before the working) is not less than 50%.
  • the rolling reduction only needs to be not less than 50%, and may be changed as appropriate.
  • an intermediate annealing may be carried out before or in the middle of the cold rolling step.
  • the cold rolling is also carried out such that the rolling reduction from the plate thickness at the time of completion of the intermediate annealing to the plate thickness at the time of completion of the cold rolling is not less than 50%.
  • a treatment temperature for the intermediate annealing is preferably in a range of not less than 300°C and not more than 400°C.
  • a retention time for the intermediate annealing is preferably in a range of not less than one hour and not more than 10 hours. This is because carrying out the intermediate annealing at a high temperature for a long time could cause deterioration in appearance quality due to progression of oxidization on the surface.
  • an annealing temperature is preferably not less than 300°C and not more than 400°C, and a retention time is preferably not less than one hour and not more than five hours.
  • the treatment temperature falling below 300°C could cause insufficient annealing effect.
  • the treatment temperature exceeding 400°C causes oxidization on the surface to progress and thus could cause deterioration in appearance quality.
  • the aluminum alloy material of the present embodiment described above it is possible to produce an aluminum alloy material having both high strength and reduced strength anisotropy by appropriately controlling the metal structure through adjustments to the composition of the aluminum alloy and the production process for the aluminum alloy. This enables improvement in productivity of the aluminum alloy material and improvement in reliability of an end product.
  • Example 1 of the present embodiment will discuss Example 1 of the present embodiment with reference to Table 1 and Table 2.
  • Table 1 shows the composition of the aluminum alloy used in Example 1.
  • Present Invention Composition of Aluminum Alloy [% by Mass] Fe Si Cu Mn Mg Cr Ti V Zr Ca Al
  • Example 1 0.22 0.10 ⁇ 0.01 0.40 7.6 0.02 0.03 0.01 ⁇ 0.01 ⁇ 0.01 Remaining Percentage
  • the composition of the aluminum alloy of Example 1 is within a predetermined range.
  • the predetermined range means that the content of Mg is in a range of 7.0% to 10.0%, and the content of Ca is in a range of not more than 0.1%.
  • the homogenization step, the hot rolling step, the cold rolling step, and the final annealing step are carried out.
  • the plate thickness of the aluminum alloy material after completion of the cold rolling step is assumed to be 1.0 mm.
  • Example 1 heating at 465°C for 12 hours is carried out in the homogenization step prior to the hot rolling step.
  • the rolling reduction from the plate thickness at the time of completion of the hot rolling to the plate thickness at the time of completion of the cold rolling is assumed to be 80%.
  • the final annealing step heating at 360°C for two hours is carried out.
  • Table 2 shows the strength property, the strength anisotropy, and the productivity of an aluminum alloy material produced by performing the above treatment on the aluminum alloy of Example 1 having the composition shown in Table 1.
  • Table 2 Present Invention Tensile Strength [MPa] Elongation [%] Strength Anisotropy [MPa] ⁇ 001 ⁇ 100> Orientation Density ⁇ 011 ⁇ 100> Orientation Density ⁇ 123 ⁇ 634> Orientation Density ⁇ 001 ⁇ 100> Orientation Density Productivity
  • Example 1 364 32 1 G G G G G G G G
  • the aluminum alloy material produced in Example 1 has a tensile strength and an elongation within the respective predetermined ranges.
  • the aluminum alloy material produced in Example 1 has a tensile strength of not less than 300 MPa and an elongation of not less than 20%.
  • the tensile strength and the elongation of the produced aluminum alloy material are measured in conformity with JIS Z-2241-2011.
  • tensile strengths and elongations of the produced aluminum alloy material 1 are measured in a 0° direction, which is the rolling direction, in a 45° direction forming an angle of 45° with the 0° direction from the rolling direction toward the transverse direction, and in a 90° direction forming an angle of 90° with the 0° direction from the rolling direction toward the transverse direction.
  • the tensile strength and the elongation of the produced aluminum alloy material 1 are defined respectively as the average value for the measured tensile strengths and the average value for the measured elongations.
  • Tensile strengths are measured, in the plane defined by the rolling direction (final working direction) and the transverse direction, in the 0° direction, which is the rolling direction, in the 45° direction forming an angle of 45° with the 0° direction from the rolling direction toward the transverse direction, and in the 90° direction forming an angle of 90° with the 0° direction from the rolling direction toward the transverse direction.
  • the strength anisotropy is defined as a standard deviation [MPa] calculated by using the following Formula (1).
  • TS i [MPa] represents a tensile strength of each direction
  • TS [MPa] represents the average value for the tensile strengths in the respective directions
  • n represents the total number of pieces of the tensile strength data.
  • the three-dimensional orientation analyzing method using the crystallite orientation distribution function (ODF) described above is applied to the aluminum alloy material of Example 1 to calculate an orientation density. Specifically, a cross section of a portion of the produced aluminum alloy material in a plane perpendicular to the working direction (rolling direction) of the aluminum alloy material is measured with an X-ray diffractometry. In this measurement, after incomplete pole figures of the (111), (220), and (200) planes are measured using the above Schlz reflection method in an inclination angle range of 15 degrees to 90 degrees, a series expansion is performed to determine the crystallite orientation distribution function (ODF).
  • ODF crystallite orientation distribution function
  • the orientation density of each orientation thus obtained is calculated as a ratio with respect to the orientation density of a standard sample having a random crystallographic texture.
  • Table 2 shows results of evaluations performed such that an aluminum alloy material having a ⁇ 013 ⁇ 100> orientation density of not more than 5 and a ⁇ 011 ⁇ 100> orientation density of not more than 5 is rated as "G (good)" and an aluminum alloy material having a ⁇ 013 ⁇ 100> orientation density exceeding 5 and a ⁇ 011 ⁇ 100> orientation density exceeding 5 is rated as "P (poor)".
  • an aluminum alloy material having a ⁇ 123 ⁇ 634> orientation density of not more than 5 and a ⁇ 001 ⁇ 100> orientation density of not more than 5 is rated as "G”
  • an aluminum alloy material having the ⁇ 123 ⁇ 634> orientation density exceeding 5 and the ⁇ 001 ⁇ 100> orientation density exceeding 5 is rated as "P”.
  • Example 1 successfully reduced strength anisotropy.
  • Example 1 shows the results that indicate no problem with productivity.
  • Table 4 shows properties of aluminum alloy materials produced by performing a treatment similar to that for Example 1 on aluminum alloys of Comparative Example 1 to Comparative Example 4 having their respective compositions shown in Table 3. Note that, for Comparative Examples 1 and 2, a treatment at 500°C and for eight hours was performed as the homogenization treatment.
  • Comparative Example 1 in which the content of Mg is too low, results in a produced aluminum alloy material having a tensile strenght falling below the predetermined range, and thus fails to yield good mechanical properties. In addition, since the homogenization treatment temperature is too high, the strength anisotropy exceeds the predetermined range, so that Comparative Example 1 fails to yield good mechanical properties.
  • Comparative Example 2 in which the content of Mg is too low, results in a produced aluminum alloy material having a tensile strength falling below the predetermined range, and thus fails to yield good mechanical properties. Further, since the homogenization treatment temperature is too high, the strength anisotropy exceeds the predetermined range, so that Comparative Example 2 fails to yield good mechanical properties.
  • Comparative Example 3 in which the content of Mg is too high, causes occurrence of cracking during the hot rolling. This makes rolling difficult, so that the production is impossible.
  • Comparative Example 4 in which the content of Ca is too high, causes occurrence of cracking during the hot rolling. This makes rolling difficult, so that the production is impossible.
  • An aluminum alloy material in accordance with an aspect of the present invention contains Mg: 7.0% to 10.0% (% by mass, the same applies hereinafter) and Ca: not more than 0.1%, the aluminum alloy material containing a remainder being constituted by aluminum and an inevitable impurity, the aluminum alloy material having a tensile strength of not less than 300 MPa and less than 500 MPa and an elongation of not less than 20%.
  • the aluminum alloy material preferably contains Mn: 0.05% to 1.0%.
  • the aluminum alloy material has a standard deviation of tensile strengths of not more than 10, in a plane defined by a final working direction and a transverse direction of the aluminum alloy material, wherein the tensile strengths are a tensile strength in a 0° direction, which is the final working direction, a tensile strength in a 45° direction forming an angle of 45° with the 0° direction from the final working direction toward the transverse direction, and a tensile strength in a 90° direction forming an angle of 90° with the 0° direction from the final working direction toward the transverse direction.
  • the aluminum alloy material preferably has a ⁇ 013 ⁇ 100> orientation density of not more than 5 and a ⁇ 011 ⁇ 100> orientation density of not more than 5, wherein the ⁇ 013 ⁇ 100> orientation density and the ⁇ 011 ⁇ 100> orientation density are calculated using a crystallite orientation distribution function (ODF).
  • ODF crystallite orientation distribution function
  • the aluminum alloy material preferably has a ⁇ 123 ⁇ 634> orientation density of not more than 5 and a ⁇ 001 ⁇ 100> orientation density of not more than 5, wherein the ⁇ 123 ⁇ 634> orientation density and the ⁇ 001 ⁇ 100> orientation density are calculated using a crystallite orientation distribution function (ODF).
  • ODF crystallite orientation distribution function

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EP20873687.6A 2019-10-08 2020-10-08 Alliage d'aluminium Pending EP4043601A4 (fr)

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JP2019185299A JP7414453B2 (ja) 2019-10-08 2019-10-08 アルミニウム合金材及びその製造方法
PCT/JP2020/038087 WO2021070890A1 (fr) 2019-10-08 2020-10-08 Alliage d'aluminium

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RU2639203C2 (ru) * 2016-05-31 2017-12-20 Общество с ограниченной ответственностью "Объединенная Компания РУСАЛ Инженерно-технологический центр" Способ совмещенного непрерывного литья, прокатки и прессования металлической заготовки и устройство для его реализации
JP7421783B1 (ja) 2023-06-14 2024-01-25 株式会社寺方工作所 内部異形筐体およびその製造方法並びに製造装置

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KR20220078525A (ko) 2022-06-10
CN117737525A (zh) 2024-03-22
JP7414453B2 (ja) 2024-01-16
CN113557314A (zh) 2021-10-26
TW202120707A (zh) 2021-06-01
JP2021059763A (ja) 2021-04-15
US20220127702A1 (en) 2022-04-28
EP4043601A4 (fr) 2023-11-01

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