WO2010007484A1 - Alliage d’aluminium, procédé de coulage d’alliage d’aluminium et procédé de production d’un produit d’alliage d’aluminium - Google Patents

Alliage d’aluminium, procédé de coulage d’alliage d’aluminium et procédé de production d’un produit d’alliage d’aluminium Download PDF

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Publication number
WO2010007484A1
WO2010007484A1 PCT/IB2009/006171 IB2009006171W WO2010007484A1 WO 2010007484 A1 WO2010007484 A1 WO 2010007484A1 IB 2009006171 W IB2009006171 W IB 2009006171W WO 2010007484 A1 WO2010007484 A1 WO 2010007484A1
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Prior art keywords
aluminum alloy
mass
less
casting
alloy
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PCT/IB2009/006171
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English (en)
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WO2010007484A8 (fr
Inventor
Hiroshi Kawahari
Hideaki Matsuoka
Hiroaki Iwahori
Taiki Kanou
Chikatoshi Maeda
Tokujiro Konishi
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Toyota Jidosha Kabushiki Kaisha
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Priority to CN2009801273997A priority Critical patent/CN102089450A/zh
Priority to US13/003,124 priority patent/US20110116966A1/en
Publication of WO2010007484A1 publication Critical patent/WO2010007484A1/fr
Publication of WO2010007484A8 publication Critical patent/WO2010007484A8/fr

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • C22C21/04—Modified aluminium-silicon alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent

Definitions

  • the present invention relates to an aluminum alloy that has excellent castability, workability, and mechanical characteristics, a method of casting the aluminum alloy, and a method of producing a product of the aluminum alloy.
  • Forged products of 6061 alloy aluminum which has excellent strength and toughness and high corrosion resistance, are used for wheels, suspension arms and so on for weight reduction of vehicles.
  • 6061 alloy has poor castability, near-net-shape blanks with complicated shapes are difficult to obtain and extrusion products are often used as blanks instead.
  • the production cost tends to increase when parts with complicated shapes are produced.
  • casting aluminum alloys such as AC4C alloy and AC4CH alloy are used in some cases.
  • net-shape castings that are formed by casting such a casting aluminum alloy, or near-net-shape blanks that are produced from such a casting aluminum alloy are formed into final shape by forging by taking advantage of their castability, products with complicated shapes can be produced at low production cost.
  • the above casting aluminum alloys have poor workability, compared to the 6061 alloy.
  • JP-A-9-125181 discloses an Al-Si-Mg-Fe based alloy that has improved hot forgeability.
  • JP- A-7- 109537 discloses an Al-Si-Mg-Ti-B based alloy that has improved mechanical characteristics.
  • a solute element such as Mg is often added to Al-Si based alloys to obtain mechanical strength, especially proof strength, comparable to that of the 6061 alloy.
  • Cu has been added in combination with Mg for improved strength.
  • Cu compounds may precipitate or crystallize and decrease the corrosion resistance of the Al-Si based alloys.
  • the addition of Cu tends to segregation in casting products and may impair the corrosion resistance thereof.
  • the present invention provides a novel aluminum alloy which has excellent castability and workability and has high mechanical characteristics.
  • the present invention also provides a method of producing a casting that is formed from the aluminum alloy of the present invention and has high mechanical characteristics, and a method of producing an aluminum alloy product that has high mechanical characteristics which is obtained by machining the casting.
  • a first aspect of the present invention relates to an aluminum alloy that is composed of 3.5% or more and 7.5% or less by mass of silicon (Si); 0.45% or more and 0.8% or less by mass of magnesium (Mg); 0.05% or more and 0.35% or less by mass of chromium (Cr); and aluminum (Al).
  • the aluminum alloy having the above composition has excellent castability and can be cast into a complicated net or near-net shape.
  • the Mg contained in an effective amount in the aluminum alloy contributes to grain refinement of eutectic Si
  • grain refinement of eutectic Si can be achieved without relying on the property improving elements such as Sr as described above.
  • the aluminum alloy exhibits high ductility and has excellent workability.
  • the strength of the aluminum alloy is improved when it contains an effective amount of Mg and contains Cr. Therefore, the aluminum alloy has improved strength and excellent corrosion resistance even if it is free from Cu.
  • the aluminum alloy according to this aspect may further contain unavoidable impurities.
  • the unavoidable impurities may include iron (Fe), and the content of iron in the aluminum alloy may be 0.3 % or less by mass.
  • the aluminum alloy according to this aspect may further contain 0.05% or more and 0.3% or less by mass of titanium (Ti).
  • the aluminum alloy according to this aspect may be free from copper.
  • the aluminum alloy according to this aspect may further contain at least one of 0.003% or more and 0.05% or less by mass of strontium (Sr); 0.001% or more and 0.03% or less by mass of sodium (Na); and 0.05% or more and 0.15% or less by mass of antimony (Sb).
  • Sr strontium
  • Na sodium
  • SB antimony
  • crystallized silicon when the silicon is crystallized via eutectic reaction, crystallized silicon may have an average grain size of 5 ⁇ m or smaller.
  • a second aspect of the present invention relates to a casting method of an aluminum alloy.
  • the casting method includes: pouring molten alloy comprising 3.5% or more and 7.5% or less by mass of silicon; 0.45% or more and 0.8% or less by mass of magnesium; 0.05% or more and 0.35% or less by mass of chromium; and aluminum; and allowing the molten alloy to cool and solidify.
  • the alloy may further contain unavoidable impurities.
  • the unavoidable impurities may include iron, and the content of iron in the aluminum alloy may be 0.3% or less by mass.
  • the alloy may further contain at least one of 0.003% or more and 0.05% or less by mass of strontium; 0.001% or more and 0.03% or less by mass of sodium; and 0.05% or more and 0.15% or less by mass of antimony (Sb).
  • solidification of the molten alloy may be achieved by cooling the molten alloy at a cooling rate of l°C/sec or faster.
  • a third aspect of the present invention relates to a method of producing an aluminum alloy product including performing cold worldng and/or hot working on an aluminum alloy casting manufactured by using the casting method according to the second aspect.
  • an aluminum alloy casting and an aluminum alloy product having excellent castability and workability and having high mechanical characteristics can be obtained.
  • a solution heat treatment and an aging heat treatment are performed on the aluminum alloy casting or aluminum alloy product, spheroidization of eutectic Si is promoted and greater ductility develops, and the Mg is precipitated as magnesium suicide (Mg 2 Si) and mechanical strength such as tensile strength and proof strength improves.
  • the cold working and/or hot working are performed on the aluminum alloy casting at a processing rate that provides a cumulative area reduction of 30% or more.
  • FIG. 1 is a photograph that is substituted for a drawing and shows the metallic structure of test sample 4-3 of this embodiment
  • FIG. 2 is a graph that shows the changes in ductility which were observed when an casting (blank) formed from a high-strength aluminum alloy according to this embodiment was hot-rolled at different rolling reductions.
  • the present inventors have found that the strength of an aluminum alloy containing silicon can be significantly improved without addition of copper (Cu) by adding chromium to the aluminum alloy in addition to adding magnesium in such an amount that the ductility of the aluminum alloy is not adversely affected to improve strength.
  • the present inventors have also found that magnesium contributes not only to improvement of the strength of the aluminum alloy but also to grain refinement of eutectic Si. [0025] Description is hereinafter made of an embodiment to implement the present invention.
  • An aluminum alloy according to this embodiment is an aluminum alloy that has excellent castability and workability, and contains, assuming that the total amount of the alloy is 100% by mass, 3.5% or more and 7.5% or less by mass of silicon (Si), 0.45% or more and 0.8% or less by mass of magnesium (Mg), 0.05% or more and 0.35% or less by mass of chromium (Cr), and the remainder of aluminum (Al) and unavoidable impurities.
  • the Si content is not within the above range, the aluminum alloy has low castability.
  • the Si. content is less than 3.5% by mass, the amount of shrinkage during casting increases. Then, casting defects tend to. occur and defects such as casting cracks tends to occur in the casting.
  • the Si content is preferably 4.5% or more by mass, more preferably 5.5% or more by mass.
  • shrinkage defects tend to aggregate in the portions of the casting that solidify last.
  • the Si content is too high, crystallization of brittle Si grains increases, and the ductility and mechanical strength decreases.
  • the Si content is preferably 7% or less by mass, more preferably 6.5% or less by mass.
  • the content of Mg in the aluminum alloy is 0.45% or more and 0.8% or less by mass, assuming that the total amount of the aluminum alloy is 100% by mass.
  • the Mg undergoes eutectic reaction and contributes to grain refinement of Si crystals in the aluminum alloy. The reason for it is not fully understood, but it is considered that the existence of Mg changes the interfacial energy between Al and Si, and concentration of Mg 1 . occurs at the growth interface of Si and inhibits the growth of Si crystals.
  • the Mg precipitates as Mg 2 Si during a heat treatment step, which is described later, and improves the mechanical strengths such as tensile strength and proof strength.
  • the aluminum alloy needs to contain an appropriate amount of Mg to strengthen the ⁇ -Al matrix phase (the structure of which is described later).
  • Mg content is less than 0.45% by mass, the grain refinement of eutectic Si cannot be fully achieved and the matrix phase does not have sufficient strength.
  • the Mg content is preferably 0.5% or more by mass, more preferably 0.55% or more by mass.
  • the Mg content is preferably 0.7% or less by mass, more preferably 0.65% or less by mass.
  • Cr is contained in an amount of 0.05% or more and 0.35% or less by mass, assuming that the total amount of the aluminum alloy is 100% by mass.
  • the Cr forms solid solution or precipitates as Cr compounds in the ⁇ -Al matrix phase and strengthens the matrix phase to improve the mechanical strengths such as tensile strength and proof strength. While it is considered that the improvement of the aluminum alloy is mainly due to precipitation of Mg 2 Si phase, it is also considered that precipitation of Cr compounds produces a synergistic effect or the existence of Cr influences the precipitation state of the Mg 2 Si phase.
  • Cr is an effective element to prevent recrystallization during machining.
  • the Cr content is preferably 0.1% or more by mass, more preferably 0.12% or more by mass.
  • the Cr content is preferably 0.25% or less by mass, more preferably 0.2% or less by mass.
  • the aluminum alloy of this embodiment may contain various property improving elements as long as the advantages and effects of this embodiment are not impaired.
  • Specific examples of the property improving elements includes titanium (Ti), strontium (Sr), sodium (Na), antimony (Sb), and iron (Fe).
  • Ti is preferably contained in an amount of 0.05% or more by mass and 0.3% or less by mass, assuming that the total amount of the aluminum alloy is 100% by mass.
  • the Ti aids in the formation of fine crystal grains, and provides solid solution strengthening or precipitation strengthening of the ⁇ -Al matrix phase.
  • the Ti content is 0.05% or more by mass, sufficiently fine crystal grains are formed and crystallized grains tends to be isotropically distributed in the alloy. Since columnar crystals tend to grow when the directionality from the casting mold is strong, Ti may be added in view of the workability in using the resulting casting as a machining blank.
  • the Ti content is 0.05% or more by mass, the mechanical characteristics are improved since shrinkage and so on are distributed finely in the alloy.
  • More preferred Ti content is 0.1% or more by mass.
  • the Ti content is preferably 0.3% or less by mass, more preferably 0.25% or less by mass, much more preferably 0.2% or less by mass.
  • Sr, Na, and Sb aid in grain refinement of eutectic Si. While grain refinement of eutectic Si is achieved by adding Mg in the aluminum alloy of this embodiment, grain refinement of eutectic Si is promoted and the mechanical characteristics are further improved when one or more of these elements are added. Especially, when a casting of the aluminum alloy of this embodiment is used as a machining blank, it exhibits excellent workability.
  • the aluminum alloy of this embodiment preferably contains at least one of 0.003% or more and 0.05% or less by mass of Sr, 0.001% or more and 0.03% or less by mass of Na, and 0.05% or more and 0.15% or less by mass of Sb, assuming that the total amount of the aluminum alloy is 100% by mass.
  • Fe is an unavoidable impurity which may be derived from the raw material.
  • the Fe content is preferably 0.3% or less by mass,- or 0.2% or less by mass, assuming that the total amount of the aluminum alloy is 100% by mass.
  • the Fe content is more than 0.3% by mass, crystallization of Fe compounds increases and the ductility decreases.
  • the aluminum alloy of this embodiment has improved mechanical strength and is substantially free from copper (Cu), which decreases corrosion resistance as described before. If.it is necessary to determine the Cu content, it should be less than 0.01% by mass.
  • the aluminum alloy is preferably free from Cu in view of its corrosion resistance.
  • Manganese (Mn) is generally used to prevent recrystallization of aluminum alloys.
  • the aluminum alloy of this embodiment may be free from Mn since it contains Cr. This is because Mn decreases the amount of Si in solid solution in the ⁇ -Al matrix phase.
  • Boron (B) is generally used in combination with Ti as an additive element which contributes to grain refinement of metallic structure.
  • the aluminum alloy of this embodiment may be free from B since it forms TiB, which decreases machinability.
  • the aluminum alloy of this embodiment has a metallic structure that is composed of ⁇ -Al matrix phase, and crystallized phase that contains fine eutectic Si crystallized in a network structure that surrounds the matrix phase.
  • the crystallized phase contains crystallized Fe compounds and so on in addition to the eutectic Si.
  • the matrix phase contains precipitated compound grains (such as precipitated grains of Mg compounds and Cr compounds) in addition to the alloy elements (Si, Mg, Cr 5 Ti, etc.) in a state of solid solution,
  • the eutectic Si contained in the crystallized phase preferably has an average grain size of 5 ⁇ m or smaller, more preferably 4 ⁇ m or smaller, much more preferably 3.5 ⁇ m or smaller.
  • the average grain size of the eutectic Si is the arithmetic average of the values of the maximum length (maximum diameter) of a plurality of eutectic Si that is measured by image analysis of a microscope image obtained by metallo graphic observation under an optical microscope.
  • a method of producing a casting of the aluminum alloy of this embodiment is described below.
  • the method of producing a casting of the aluminum alloy of this embodiment essentially includes a pouring step and a solidifying step.
  • the pouring step is a step of pouring molten alloy that is composed of, assuming that the total amount of the alloy is 100% by mass, 3.5% or more and 7.5% or less by mass of silicon (Si), 0.45% or more and 0.8% or less by mass of magnesium
  • the method of producing a casting of the aluminum alloy of this embodiment is not limited to typical gravity casting and pressurized casting, and may be die-casting.
  • the casting mold for use in the casting may be of any type such as a sand mold or metal mold.
  • the solidifying step is a step of cooling the molten alloy after the pouring step to solidify it.
  • Grain refinement of eutectic Si can be achieved by properly selecting the material and wall thickness of the casting mold, the dimensions of the casting (or dimensions of the mold cavity of the casting mold), the cooling method and so on to increase the cooling rate (solidification rate).
  • the average grain size of eutectic Si can be reduced by selecting a cooling rate of, for example, l°C/sec or higher, preferably 5°C/sec or higher.
  • the method preferably further includes a heat treatment step of subjecting the aluminum alloy after the solidifying step to a solution heat treatment and/or an aging heat treatment.
  • the heat treatment step promotes the spheroidization of the eutectic Si and improves the ductility of the aluminum alloy after the solidifying step.
  • the solution heat treatment is a heat treatment in which the aluminum alloy is maintained at a high temperature and then cooled rapidly to form super-saturated solid solution.
  • the aging heat treatment is a heat treatment in which the aluminum alloy is heated and maintained at a relatively low temperature to cause the elements in the super-saturated solid solution to precipitate in order to impart the aluminum alloy with a suitable degree of hardness.
  • fine precipitates are uniformly distributed and the eutectic Si are spheroidized, whereby an aluminum alloy having highly balanced strength, ductility and toughness can be obtained.
  • the conditions of the heat treatments may be selected based on the composition and required properties and so on of the casting.
  • the casting may be heated and maintained at 450°C to 55O 0 C for 0.5 to 10 hours and then cooled rapidly in the solution heat treatment process.
  • the heating temperature and retention time are preferably 490°C to 535°C and 0.5 to 3 hours, respectively, for a good balance between cost and properties.
  • the casting may be heated and maintained at 140°C to 250 0 C for 1 to 20 hours in the aging heat treatment process.
  • the heating temperature and retention time are preferably 160 to 200 0 C and 1 to 5 hours, respectively, for a good balance between cost and properties.
  • An aluminum alloy product is obtained by subjecting the aluminum casting that is obtained by the above procedure to a processing step. That is, the method of producing an aluminum alloy product of this embodiment essentially include a pouring step and a solidifying step as described above and a processing step. The pouring step and the solidifying step are the same as described above.
  • the processing step involves cold-working and/or hot-working the aluminum alloy casting after the solidifying step to obtain an aluminum alloy product.
  • the method of cold working and/or hot working is not particularly limited.
  • the cold working and/or hot working may be by forging (extend forging, swaging, etc.), rolling , spinning or the like.
  • the cold working and/or hot working may be either performed once or repeated twice or more. Either cold working or hot working may be performed, or cold working may be performed after hot working.
  • the processing step is preferably a step in which the aluminum alloy casting is processed at a processing rate that provides a cumulative area reduction of 30% or more, preferably 50% or more.
  • the cumulative area reduction after all the stages of processing is 30% or more, preferably 50% or more.
  • the method of producing an aluminum alloy product of this embodiment preferably further includes a heat treatment step of subjecting the aluminum alloy product after the processing step to a solution heat treatment and an aging heat treatment.
  • the heat treatment step is the same as described before.
  • a homogenizing treatment may be performed on the aluminum alloy casting before the processing step as needed.
  • the homogenizing treatment is a treatment for incorporation of crystallized phase that is not incorporated in the solid solution and spheroidization of the crystallized phase, and improves the workability in the processing step thereafter.
  • the aluminum alloy casting may be heated and maintained at 45O 0 C to 550°C for 0.5 to 10 hours. Cooling after the heating is not particularly limited.
  • the heating temperature and retention time are preferably 490°C to 535 0 C and 0.5 to 3 hours, respectively, for good balance between cost and properties.
  • the aluminum alloy of this embodiment is suitably used for a casting product or forged product which is required to have high strength and corrosion resistance or a material (such an ingot) from which they are formed.
  • examples of such products include suspension systems of vehicles.
  • suspension systems include upper arm, lower arm, knuckle, axle carrier, disk wheel, and cross member.
  • test samples 1-1 to 1-9 composed of aluminum alloys having different compositions as shown in Table 1 were prepared and their mechanical characteristics were evaluated.
  • the ingredients were mixed to obtain different alloy compositions, and each mixture was melted to prepare molten alloy, which was then pored into a copper mold with cavity dimensions of 80 mm x 70 mm x 15 mm and was allowed to cool and solidify to obtain an aluminum alloy casting.
  • a heat treatment designated as T6 was performed on the obtained castings.
  • the castings were subjected to a solution treatment at 535°C for 1 hour and then quenched into warm water at 5O 0 C, followed by an aging heat treatment at 170 0 C for 3 hours, thereby obtaining castings as test samples 1-1 to 1-9.
  • Test Composition [% by mass] sample Si Cu Mg Fe Ti Cr Al No.
  • test samples 1-1 to 1-5 which had a composition within the composition range of the aluminum alloy of this embodiment (Si: 3.5 to 7.5%, Mg: 0.45 to 0.8%, Cr: 0.05 to 0.35%), had a tensile strength of 320 MPa or more, a 0.2% proof strength of 280 MPa or more, and an elongation of 8.0% or more, which indicates that the aluminum alloy casting had both high mechanical strength and high ductility.
  • test samples 1-6 to 1-9 were not satisfactory in terms of mechanical strength and/or ductility.
  • the test sample 1-6 which contained an excessive amount of Si, had a much lower elongation than the test samples 1-1 to 1-5.
  • the test sample 1 -7 which contained an excessive amount of Mg, also had a lower elongation than the test samples 1-1 to 1--5.
  • the test sample 1-8 which was substantially free from Cr, was satisfactory in terms of elongation but deficient in mechanical strength (tensile strength and proof strength).
  • the test sample 1-9 was an Al-Si-Mg based casting alloy (AC4CH) provided in JIS.
  • test sample 1-9 was not satisfactory in terms of both mechanical strength and ductility as compared to the test samples 1-1 to 1-5.
  • the test samples 1-1 to 1-5 had almost no defect in the castings and high castability, but the test sample 1-1, which had a Si content of 3.5% by mass, was inferior in castability to the test samples 1-2 to 1-5, which had a Si content of 5.6% or more by mass.
  • test samples 2-1 to 2-4 that were composed of aluminum alloys having different compositions as shown in Table 3 were prepared, and their mechanical characteristics were evaluated.
  • a plate-shaped blank with dimensions of 70 mm x 15 mm x 15 mm was cut from each of the obtained castings, and its surfaces were wet-polished up to the grit #600. Then, the plate-shaped blanks were hot-rolled. The plate-shaped blanks were heated by maintaining them in an electric furnace at 380°C for 30 minutes and passed between rolls at room temperature. Each of the plate-shaped blanks was passed between rolls ' seven times in total to obtain aluminum alloy products. Adjustment was made so that the final rolling reduction rate after the seven passes of rolling was approximately 65%.
  • test samples 2-1 and 2-2 which had a composition within the composition range of the aluminum alloy of this embodiment, had a tensile strength of 360 MPa or more, a 0.2% proof strength of 310 MPa or more, and an elongation of 14% or more, which indicates that the aluminum alloy product had highly balanced strength and ductility. Also, since the aluminum alloy products were processed at a cumulative area reduction of approximately 65% or more, the tensile strength, proof strength, and ductility were all improved compared to the castings of Test Example 1 (which were not subjected to any processing).
  • the test sample 2-3 which contained an excessive amount of Mg, exhibited high tensile strength, proof strength, and hardness values. However, the test sample 2-3 exhibited a lower elongation value than the 6061 alloy and did not show significant improvement in ductility in spite of the fact that it. was processed at a high processing rate.
  • the test sample 2-4 was the same in composition as AC4CH as in the case with the .test sample 1-9 and had excellent ductility, but exhibited lower tensile strength and proof strength values than the 6061 alloy.
  • test samples 3-1 to 3-5 composed of aluminum alloys having different compositions as shown in Table 5 were prepared in the same manner as in Test Example 1, and evaluation was conducted to show how the hardness of castings depends on the Cr content.
  • test samples 3-2 to 3-4 which had a composition within the composition " range of the aluminum alloy of this embodiment, had a HV of 120 or greater.
  • the test sample 3-1 which was substantially free from Cr, was deficient in hardness.
  • the test sample 3-5 which contained an excessive amount of Cr, exhibited a high hardness value but coarse Cr compounds (not shown) were observed when its metallic structure was examined under an optical microscope. Thus, it is considered that the test sample 3-5 had low ductility and toughness.
  • test samples 4-1 to 4-4 that were composed of aluminum alloys having different compositions as shown in Table 6 were prepared in the same manner as in Test Example 1, and evaluation was conducted to show how the average grain size of eutectic Si depends on the Mg content.
  • the average grain size of eutectic Si was obtained by observing the metallic structure in a section taken through a thick central portion of each casting under an optical microscope. Several fields of view of the metallic structure were photographed at a 200 fold magnification (600 ⁇ im x 480 ⁇ m) and a 400 fold magnification (300 ⁇ m ⁇ 240 ⁇ im) by an optical microscope. One sample photograph is shown in FIG. 1.
  • the grain size of eutectic Si was measured on photographs substituted for drawings as FIG. 1 using image analysis software "Image-Pro.”
  • the maximum lengths (maximum diameters) of eutectic Si grains in the fields of view were measured and an average grain size was calculated by obtaining the arithmetic average thereof. The result is summarized in Table 6.
  • the average grain size of eutectic Si was as small as approximately 3 ⁇ im.
  • the average grain size of eutectic Si was as large as 6 ⁇ m.
  • the average grain size of eutectic Si was as small as 2.5 ⁇ m, but metallographic observation reveals that Mg compounds, which did not incorporated into the solid solution by the heat treatment, were present in the metallic structure.
  • the ductility of the test sample 4-4 was low as in the case with the test sample 1-7 (Table 2).
  • test samples 5-1 to 5-8 that were composed of aluminum alloys having different compositions as shown in Table 7 were prepared, and evaluation was conducted to show how the average grain size of eutectic Si depends on the cooling rate.
  • the average grain size of eutectic Si was smaller than 9 ⁇ m. Above all, the average grain size of eutectic Si was smaller than 5 ⁇ m for the test samples, which were cooled at a cooling rate of l°C/sec or higher, and 3 ⁇ m or smaller for the test samples, which were cooled at a cooling rate of 5°C/sec or higher.
  • Test Example 6 a test sample 6-1 that was composed of aluminum alloys having a compositions shown in Table 8 was prepared, and evaluation was conducted to show how the ductility depends on the rolling reduction in the rolling process.
  • T6 heat treatment was performed in the same manner as in Test Example 1.
  • the aluminum alloy of this embodiment is suitable for castings or machining blanks that have complicated shapes.
  • aluminum alloy castings include near-net-shape machining blanks as well as net-shape castings.

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Abstract

Un alliage d’aluminium est composé de 3,5 % en masse ou plus et de 7,5 % en masse ou moins de silicium, de 0,45 % en masse ou plus et de 0,8 % en masse ou moins de magnésium, de 0,05 % en masse ou plus et de 0,35 % en masse ou moins de chrome, et d’aluminium, en supposant que la quantité totale de l’alliage représente 100 % en masse.
PCT/IB2009/006171 2008-07-14 2009-07-06 Alliage d’aluminium, procédé de coulage d’alliage d’aluminium et procédé de production d’un produit d’alliage d’aluminium WO2010007484A1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
CN2009801273997A CN102089450A (zh) 2008-07-14 2009-07-06 铝合金、铸造铝合金的方法和制造铝合金产品的方法
US13/003,124 US20110116966A1 (en) 2008-07-14 2009-07-06 Aluminum alloy, method of casting aluminum alloy, and method of producing aluminum alloy product

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JP2008-182975 2008-07-14
JP2008182975A JP2010018875A (ja) 2008-07-14 2008-07-14 高強度アルミニウム合金、高強度アルミニウム合金鋳物の製造方法および高強度アルミニウム合金部材の製造方法

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WO2010007484A1 true WO2010007484A1 (fr) 2010-01-21
WO2010007484A8 WO2010007484A8 (fr) 2011-01-20

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EP4101941A1 (fr) * 2021-06-07 2022-12-14 Dubai Aluminium PJSC Alliage de moulage aluminium-silicium et pièces moulées fabriquées à partir dudit alliage

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DE102015111020A1 (de) * 2014-07-29 2016-02-04 Ksm Castings Group Gmbh Al-Gusslegierung
JP6617065B2 (ja) * 2016-03-21 2019-12-04 株式会社豊田中央研究所 鋳造用アルミニウム合金およびアルミニウム合金鋳物
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CN102312137B (zh) * 2011-09-09 2016-06-22 深圳市中兴康讯电子有限公司 铝硅镁系铸造铝合金及铸造工艺
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EP4101941A1 (fr) * 2021-06-07 2022-12-14 Dubai Aluminium PJSC Alliage de moulage aluminium-silicium et pièces moulées fabriquées à partir dudit alliage

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