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WO2002012582A1 - Alliage d'aluminium forme par durcissage par precipitation et procede de traitement thermique de cet alliage - Google Patents

Alliage d'aluminium forme par durcissage par precipitation et procede de traitement thermique de cet alliage Download PDF

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Publication number
WO2002012582A1
WO2002012582A1 PCT/JP2001/006157 JP0106157W WO0212582A1 WO 2002012582 A1 WO2002012582 A1 WO 2002012582A1 JP 0106157 W JP0106157 W JP 0106157W WO 0212582 A1 WO0212582 A1 WO 0212582A1
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Prior art keywords
alloy
less
temperature
heat treatment
solution treatment
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PCT/JP2001/006157
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English (en)
Japanese (ja)
Inventor
Takayuki Sakai
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Asahi Tec Corp
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Asahi Tec Corp
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Filing date
Publication date
Priority claimed from JP2000240139A external-priority patent/JP2001316786A/ja
Priority claimed from JP2000242069A external-priority patent/JP2002060879A/ja
Application filed by Asahi Tec Corp filed Critical Asahi Tec Corp
Priority to AU2001269533A priority Critical patent/AU2001269533A1/en
Priority to US10/344,271 priority patent/US20040011434A1/en
Priority to KR10-2003-7001519A priority patent/KR100533242B1/ko
Priority to EP01948037A priority patent/EP1327696A1/fr
Publication of WO2002012582A1 publication Critical patent/WO2002012582A1/fr
Anticipated expiration legal-status Critical
Priority to US11/065,000 priority patent/US20050139299A1/en
Ceased 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
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • 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
    • 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

Definitions

  • the present invention relates to a precipitation hardening type A1 alloy and a heat treatment method thereof.
  • a 1 -Si type A 1 alloy containing several weight% of Si in A 1 is known.
  • a multi-element A 1 -Si based alloy containing an A 1 -Si based A 1 alloy as a basic composition and further containing other elements such as Cu and Mg is used. This is because the fluidity of the molten metal, the mold filling property, etc., which are important properties in the production of wrought materials and wrought materials such as metals and die-casting, are superior to other alloys. This is because cracks hardly occur, an alloy with high strength and elongation can be obtained by combining with other elements, the thermal expansion coefficient is small, and the wear resistance is good.
  • AC4A, AC4C As an alloy obtained by adding a small amount of Mg in A 1-S i based alloy, AC4A, AC4C, there is AC 4 CH, these alloys which to enhance the strength in the heat treatment effect due to precipitation of the intermediate phase of Mg 2 S i It is.
  • AC4C and AC4CH which has improved toughness by limiting Fe to 0.20 mass% or less, are used as alloys for vehicle wheels of automobiles and the like.
  • alloys in which a small amount of Mg and Cu are added to A1-Si alloys are also used, and precipitation hardening due to the intermediate phase of Mg 2 Si and solid solution hardening of Cu, and the intermediate phase of Al 2 Cu The strength is improved by precipitation hardening or the like.
  • the heat treatment for the aging precipitation involves solution treatment and aging treatment.
  • Consists of The solution treatment is a heat treatment in which a non-equilibrium phase crystallized during solidification is solidified at a high temperature and then cooled with water to obtain a uniform solid solution at room temperature.
  • the aging treatment following the solution treatment is performed at a relatively low temperature, Is precipitated and hardened as an intermediate precipitation phase, and the mechanical properties of the A 1 alloy are improved by these heat treatments.
  • such a solution treatment and aging treatment of the A1 alloy have been performed using an atmosphere furnace such as a tunnel furnace using air as a heat medium.
  • the temperature is large, ⁇ 5 ° C, which causes problems such as the inability to perform solution treatment at a higher temperature.
  • the mechanical properties of the obtained A1 alloy have a tensile strength of about 290 MPa, The 0.2% proof stress was about 20 OMPa, and the elongation was about 8%.
  • the rate of temperature rise to the solution temperature is slow, and it takes time to raise the temperature.
  • the solution treatment is performed by maintaining the solution temperature for more than 3 hours.
  • the thickness of the automobile wheel can be further reduced. Since the weight of the vehicle can be reduced and the rolling resistance is reduced, it is extremely effective because it contributes not only to improved fuel efficiency and improved exhaust gas purification performance but also to improved steering stability.
  • the present inventor focused on the microstructure of the obtained A1 alloy as a result of examination from various angles, and when the eutectic structure present in the A1 alloy was smaller than a predetermined value, the mechanical properties were The inventors have found that the present invention is improved, and have reached the present invention.
  • an object of the present invention is to provide an A1 alloy having three mechanical properties of tensile strength, heat resistance, and elongation in a well-balanced manner and excellent fatigue strength.
  • Another object of the present invention is to provide a solution treatment using a fluidized bed to increase the solid solution ratio of Si and Mg to a predetermined value or more, thereby obtaining the strength and elongation of the obtained A1 alloy.
  • a precipitation hardening type A1 alloy wherein A precipitation hardening type A1 alloy characterized by having an average area of a crystal structure of less than 4 m 2 is provided.
  • Si is preferably contained in an amount of 6.5 to 7.5% by mass and Mg in an amount of 0.36% by mass or less. More preferably, the content is 0 to 70 ppm. Further, the precipitation hardening type A1 alloy of the present invention is suitably used as a vehicle wheel.
  • a precipitation hardening type A1 alloy which improves the mechanical properties of the workpiece by subjecting a workpiece made of the precipitation hardening type A1 alloy to a solution treatment and then performing an aging treatment.
  • the solution treatment is performed by causing the workpiece to exist in a fluidized bed, and the solid solution rate of Si and / or Mg in the phase is reduced to 60% in the solution treatment.
  • the present invention provides a heat treatment method for a precipitation hardening type A1 alloy, wherein the aging treatment is performed at 150 ° C. or more and less than 200 ° C.
  • the temperature is raised to the solution heat treatment temperature within 30 minutes and the heating rate is increased so that the holding time at the solution heat temperature is 25 minutes to 3 hours. Is preferred. It is desirable that the solution treatment temperature is 540 to 550 ° C.
  • the fluidized bed is preferably formed by direct blowing of hot air.
  • FIG. 1 is a schematic view showing one example of a fluidized bed of a hot air blowing system used in the present invention.
  • FIG. 2 is a schematic view showing an example of a fluidized bed type solution treatment furnace used in the present invention.
  • FIG. 3 is a perspective view showing the vehicle aluminum wheel used in the first embodiment.
  • FIG. 4 is a graph showing a heat treatment schedule in Example 1.
  • FIG. 5 is a rough drawing showing the results of the tensile test in Example 1.
  • FIG. 6 is a graph showing the results of the impact and hardness tests in Example 1.
  • FIG. 7 is a graph showing the relationship between the eutectic structure average area and the solution treatment time.
  • FIG. 8 is an explanatory view showing the shape and dimensions of a test piece used in the rotating bending fatigue test of Example 2.
  • FIG. 9 is a graph showing fatigue strength (inner rim) in Example 2 and Comparative Example 2.
  • FIG. 10 is a graph showing the fatigue strength (outer rim) in Example 2 and Comparative Example 2.
  • FIG. 11 is a graph showing the results of a tensile test (tensile strength, 0.2% resistance to heat, elongation) in Example 3 and Comparative Example 1.
  • FIG. 12 is a graph showing the results of differential calorimetric analysis of the absorption energy released when Si and / or Mg solid-dissolved in the solid phase during the solution treatment.
  • FIG. 13 is a graph showing a heat treatment schedule in Example 4.
  • FIG. 14 is a graph showing tensile test results in Example 4 and Comparative Examples 5 and 6.
  • FIG. 15 is a graph showing the results of impact and hardness tests in Example 4.
  • FIG. 16 is a graph showing a tensile test result in Comparative Example 3.
  • FIG. 17 is a plan view showing another example of the vehicle aluminum wheel.
  • FIG. 18 is a graph showing a heat treatment schedule in Comparative Example 3. BEST MODE FOR CARRYING OUT THE INVENTION
  • the present invention relates to a precipitation hardening type A1 alloy in which the strength is improved by precipitation hardening due to an intermediate phase of Mg 2 Si or precipitation hardening due to an intermediate phase of Al 2 Cu, and specifically, average area of the eutectic structure present in a 1 alloy 4; is a 1 alloy of less than m 2.
  • the average surface product is less than 4 tm 2 eutectic tissue present in the alloy structure, preferably l ⁇ 3 m 2, particularly preferably of 1. 2 ⁇ 3 ⁇ 2 It is a thing.
  • A1 alloy having such a structure has three mechanical properties such as tensile strength, heat resistance, and elongation in a well-balanced manner.
  • the tensile strength is 310 MPa or more, preferably 32 OMPa.
  • the 0.2% proof stress is 24 OMPa or more, preferably 26 OMPa or more
  • the elongation is 10% or more, preferably 12% or more.
  • the mechanical properties such as tensile strength, 0.2% heat resistance and elongation of the A1 alloy were determined according to the test method specified in JISZ2241.
  • the A1 alloy of the present invention having the above-mentioned predetermined mechanical properties has a composition based on A1 with Si of 6.5 to 7.5% by mass and Mg of 0.36%. It is preferable that the content of Sr be 20% by mass or less, and it is further preferable that the content of Sr be 20 to 70 ppm. That is, when the Si content is in the range of 6.5 to 7.5% by mass, the formability of the A1 alloy is improved, and the range of 6.8 to 7.2% by mass is more preferable.
  • the content of Mg is preferably 0.36% by mass or less.
  • Mg precipitates an intermediate phase called Mg 2 Si phase together with Si by heat treatment, and this precipitation causes remarkable age hardening.
  • the content exceeds 0.36% by mass, the tensile strength is large.
  • the A1 alloy of the present invention is intended for alloys based on AC4C and AC4CH.
  • the A1 alloy of the present invention has excellent mechanical properties such as tensile strength, 0.2% heat resistance, and elongation of a predetermined value or more, and also has three properties in a well-balanced manner. Can be used very effectively.
  • the precipitation hardening type A1 alloy of the present invention having the above-mentioned fine eutectic structure can be produced, for example, by the following heat treatment method.
  • a material (workpiece) of an A1 alloy manufactured by a normal manufacturing method is subjected to a solution treatment, then generally rapidly cooled, and then subjected to an aging treatment.
  • a solution treatment is subjected to a solution treatment, then generally rapidly cooled, and then subjected to an aging treatment.
  • the mechanical properties of the A1 alloy can be improved so that it can be applied to a desired use such as a vehicle wheel.
  • the treatment time (including the heating time) at the solution treatment temperature of 540 to 550 ° C is preferably within 4 hours (240 minutes), more preferably 3 hours 30 minutes ( By setting the average area of the eutectic structure as described above to less than 4 m 2 , a precipitation hardening type A1 alloy can be obtained. You.
  • the eutectic structure can be made spherical and the eutectic structure can be coarsened by raising the temperature up to the solution treatment temperature of 540 to 550 ° C within 30 minutes. It is desirable from the viewpoint of prevention of
  • the temperature is raised to 540 to 550 ° C in about 3 to 10 minutes. It is preferred to warm. This is particularly desirable from the viewpoint of miniaturization of the eutectic structure.
  • the workpiece can be rapidly heated, and there is no particular limitation on the method. That is, it is only necessary to control the temperature of the atmosphere so that the workpiece can be rapidly heated. For example, high-frequency heating, low-frequency heating, and far-infrared heating can be applied, but the temperature control is simple. Therefore, rapid heating using a fluidized bed is more preferable.
  • the specific method of the aging treatment is not particularly limited, and a conventional atmosphere furnace (tunnel furnace) using air as a heat medium may be used, but it is preferable to use a fluidized bed as in the solution treatment. . This is because, in addition to shortening the aging treatment time, when using a fluidized bed for solution treatment, it is preferable to use the same fluidized bed from the viewpoint of control and operation of the entire process. '
  • a solution treatment is applied to a green or wrought material (workpiece) of A1 alloy manufactured by a normal manufacturing method, and then an aging treatment is performed. ⁇
  • an aging treatment is performed.
  • the solid solution rate of Si, Z or Mg in the solid phase is 60% or more.
  • the temperature is rapidly raised to the solution treatment temperature in a short time of 30 minutes or less.
  • the temperature is rapidly raised in a short time of preferably 20 minutes or less, particularly preferably 3 to 10 minutes.
  • the holding time at the solution heat treatment temperature is preferably 25 minutes to 3 hours, more preferably 30 minutes to 2 hours.
  • the solution treatment it is preferable to carry out the solution treatment under the above conditions in order to make the solid solution rate of Si and / or Mg into the solid phase 60% or more.
  • the temperature is raised to the solution temperature for more than 30 minutes, the eutectic structure of the A1 alloy becomes coarse. If the holding time at the solution treatment temperature is too short, less than 25 minutes, the solid solution rate of Si and / or Mg in the ⁇ phase is less than 60%, as shown in Fig. 12.
  • the AI alloy obtained has poor mechanical properties and the retention time exceeds 3 hours, the solid solution ratio of Si and Mg exceeds 60%, but the eutectic of A1 alloy The structure becomes coarse and the mechanical properties of the A1 alloy similarly decrease.
  • the solution treatment temperature of the A1 alloy is in the range of 530 to 550 ° C, and more preferably 540 to 550 ° C.
  • the heating time to the solution treatment temperature is short, and the holding time at the solution treatment temperature is also within a predetermined time.
  • the entire solution treatment time is 4 hours. (240 minutes), preferably within 3 hours 30 minutes (2 10 minutes).
  • the workpiece is generally rapidly cooled to room temperature, and then the workpiece is aged.
  • the temperature is preferably raised to less than 150 to 200 ° C. in several minutes, and the temperature is preferably kept at that temperature for 30 to 360 minutes.
  • the aging temperature is more preferably 170 to 190 ° C. If the aging temperature exceeds 200 ° C., the ductility of the obtained A1 alloy decreases.
  • the A1 alloy targeted in the present invention is a precipitation hardening type A1 alloy that precipitates an intermediate phase such as an Mg 2 Si phase by heat treatment, and is not limited as long as it is used. Therefore, it is suitable for both A1 alloy wrought and wrought materials manufactured by the normal manufacturing method. Can also be applied.
  • the forged material of A1 alloy is a solid, die-cast, etc.
  • the wrought material refers to plates, foils, profiles, tubes, rods, wires, forged products, etc.
  • Each A1 alloy has improved properties such as strength by adding various elements, and Al_Mg—Si-based alloy, Al—Cu—Mg-based alloy, A1-Cu- Si-based alloys and the like.
  • Al_Mg—Si-based alloy, Al—Cu—Mg-based alloy, A1-Cu- Si-based alloys and the like for example, as a structural material, an A1 alloy of AC4C or AC4CH specified in JIS can be effectively applied.
  • the wrought material include a 200-based alloy such as 20017, which is known as a duralumin and contains a relatively large amount of copper and has improved strength, and a 600-based alloy and a 700-based alloy. A system alloy or the like can be applied.
  • a fluidized bed when the workpiece is rapidly heated. Rapid heating by a fluidized bed is performed by placing the workpiece in the fluidized bed.
  • the fluidized bed is formed by heating and uniformly mixing particulate matter such as powder and granules, and has the characteristics that the temperature inside the fluidized bed is substantially uniform and the heat transfer efficiency is good. ing.
  • the temperature inside the fluidized bed can be made uniform (about ⁇ 2 to 3 ° C), and the solution treatment at a higher temperature becomes possible.
  • the heat transfer efficiency is high, the time required to raise the temperature to the solution treatment temperature can be reduced.
  • the aging treatment may be of the fluidized bed type as described above or any of the conventionally known atmosphere furnaces.
  • fluidized bed systems include indirect heating systems such as a container heating system in which a fluidized bed vessel is heated from the outside and a radiant tube system in which a radiant tube is built in the fluidized bed, and a direct heating system by direct blowing of hot air.
  • indirect heating systems such as a container heating system in which a fluidized bed vessel is heated from the outside and a radiant tube system in which a radiant tube is built in the fluidized bed
  • direct heating system by direct blowing of hot air.
  • Figure 1 is a schematic diagram showing an example of a fluidized bed of the hot air direct blowing method used for the heat treatment method. It is.
  • Numeral 10 denotes a container.
  • a granular material 12 such as a granular material is filled on a perforated plate 16, and the granular material 12 is fluidized by hot air 14 blown from below the perforated plate 16 to be uniform.
  • a fluidized bed 18 is formed.
  • FIG. 2 is a schematic diagram showing an example of a fluidized bed type solution treatment furnace.
  • reference numeral 20 denotes a hot-air generator, and the air sent from a blower (not shown) is heated to 700-800 ° C. hot air by the flame from the parner 22.
  • the hot air is blown into a fluidized bed type solution treatment furnace 26 through a hot air temperature monitoring device 24.
  • hot air is blown into the fluidized bed 30 from the perforated pipe 28 to fluidize the granular material 32 and heat the granular material 32. In this way, the fluidized bed
  • the inside of the furnace 30 is heated to 540 to 550 ° C, and the fluctuation of the furnace temperature is about 6 ° C ( ⁇ 3 ° C), and the fluctuation of the furnace temperature at one point is about 3 ° C.
  • Reference numeral 36 denotes a particulate matter discharge valve, which discharges the particulate matter 32 to the outside as appropriate.
  • FIGS. 1 and 2 a fluidized bed as shown in FIGS. 1 and 2 can be used for the aging treatment.
  • the present invention will be described more specifically based on examples and comparative examples.
  • a fluidized bed type solution treatment furnace was used, and an aging treatment furnace was an atmosphere furnace.
  • the heat treatment method was performed on the structure of the 4 CH A1 alloy wheel.
  • the fluidized bed type solution treatment furnace has a rectangular tank shape with a side of 1500 mm X I 500 mm, a straight body height of 1800 mm, and a lower portion formed of a trapezoidal fluidized bed vessel.
  • a conventionally known tunnel furnace atmosphere furnace
  • Silica sand with an average particle size of 50 to 500 m was used as the granular material.
  • the object of the heat treatment was a fabricated aluminum wheel for vehicles (14 kg) as shown in Fig. 3, and the test pieces were collected at three locations: the outer rim 'flange, the inner rim flange, and the spokes.
  • the composition of the aluminum wheel made of A1 alloy of AC 4 CH is 7.0 mass% of Si, 0.33 mass% of Mg, and 40 mass% of Sr. ppm, 0.001% by mass of ⁇ ⁇ 1,? 6 was contained in an amount of 0.11% by mass, and the balance was A1.
  • the solution treatment schedule shown in FIG. The aging treatment was performed under the condition of holding at 190 ° C for 53 minutes (the total aging time including the heating time was 85 minutes).
  • the impact value was measured using the Charpy test method specified by JIS.
  • Rockwell hardness was measured using a test method specified in JIS Z 2245.
  • FIG. 7 shows the relationship between the eutectic structure average area and the solution treatment time at this time.
  • the eutectic structure average area was measured as follows.
  • a test piece (FIG. 8) was sampled from a vehicle aluminum wheel obtained in the same manner as in Example 1, and a rotary bending fatigue test was performed to determine the fatigue strength.
  • the rotating bending fatigue test is performed by using an Ono-type rotating bending fatigue tester and applying a stress at a stress ratio of -1 while rotating the test piece 1 at 3600 rpm at room temperature and in the air to break.
  • the fatigue strength was measured from the relationship between the stress and the number of repetitions. The results are shown in Figs.
  • Example 1 test pieces were collected from aluminum wheels for vehicles obtained at a solution treatment temperature of 550 ° C. and a holding time of 60 minutes, and the average area of the eutectic structure was measured in the same manner as in Example 1.
  • Table 1 shows the results.
  • Fig. 11 shows the results of the tensile test (tensile strength, 0.2% strength, elongation).
  • a conventional tunnel furnace (atmosphere furnace) was used as the solution treatment furnace and the aging treatment furnace, and the solution treatment temperature was 540 ° C (:, and the aging temperature was 1550 ° C (total aging time was 17 ° C). (4 minutes), the heat-up time to the solution heat treatment temperature was 1 hour and 12 minutes, and the holding time at the solution heat treatment temperature was 4 hours, and the manufactured aluminum wheels for vehicles were subjected to heat treatment. Is the same as in Example 1.
  • a test piece (FIG. 8) was sampled from a vehicle aluminum wheel obtained in the same manner as in Comparative Example 1, and a rotary bending fatigue test was performed to determine the fatigue strength.
  • the results are shown in FIGS. Examples 1 to 3 and Comparative Examples 1 to As apparent from the test results of 2, an average area of 4 m 2 and less than fine aluminum vehicle wheel of woven KyoAkiragumi a tensile strength, 0.2% proof mosquitoes, and elongation becomes more than the predetermined amount, these values are meets all ⁇ values of tensile test was greatly improved in comparison with what the average area of a conventional eutectic structure exceeds 4 m 2 It has been found. Also, the fatigue strength has been greatly improved compared to the past.
  • the heat treatment method was performed using the fluidized bed solution treatment furnace shown in Fig. 2 and the atmosphere furnace as the aging treatment furnace.
  • the fluidized bed type solution treatment furnace is a square tank with a side of 150 Omm X 150 Omm. It has a straight body height of 1800 mm and a lower part composed of a trapezoidal fluidized bed vessel.
  • a conventional tunnel furnace atmosphere furnace
  • Silica sand with an average particle size of 50 to 500 m was used as the granular material.
  • the object of the heat treatment was a fabricated aluminum wheel for vehicles (13 kg) as shown in Fig. 17, and the test pieces were collected at two locations: the outer rim, the flange, and the spokes.
  • the composition of the aluminum wheel was 7.0 mass% of Si, 0.34 mass% of Mg, 50 ppm of Sr, and the balance was A1.
  • the heat treatment conditions were: solution treatment temperature of 540 ° C and 550 ° C, aging treatment temperature of 190 ° C and 220 ° C, heating time to solution treatment temperature, holding time at solution treatment temperature, In addition, the temperature rise time and the holding time of the aging treatment were performed according to the schedule shown in Fig. 13 (when the solution treatment temperature was 550 ° C).
  • FIG. 12 shows the results of differential calorimetric analysis, in which the absorbed energy when Si and Mg were dissolved in the ⁇ phase in the solution treatment was measured.
  • the solution treatment setting the solid solution rate of Si and / or Mg in the ⁇ ; phase to 60% or more is not necessary when the solution treatment temperature is 540 ° C.
  • the time (total of the heating time and the holding time) is equivalent to 18 minutes or more.
  • the solution treatment time is equivalent to 7 minutes or more.
  • the solid solution rate becomes 100% when the solution heat treatment temperature is 540 ° C, the solution heat treatment time is 180 minutes, and when the solution heat treatment temperature is 550 ° C, the solution heat treatment time is 60%. Minutes.
  • a conventional tunnel furnace (atmosphere furnace) was used as the solution treatment furnace and the aging treatment furnace.
  • the solution treatment temperature was 540
  • the aging temperature was 155 ° C
  • the vehicle was constructed using the schedule shown in Fig. 18.
  • Heat treatment was applied to aluminum wheels. Other conditions are the same as in the fourth embodiment.
  • Figure 16 shows the obtained results.
  • Figure 14 shows the obtained results.
  • Example 4 Performed except that the solution heat treatment temperature was 550 ° C, the solid solution rate of Si and / or Mg in the solid phase was 50%, the aging temperature was 220 ° C, and the aging time was 35 minutes.
  • the aluminum wheel for a vehicle obtained in Example 4 has a It was found that the tensile strength was at least 326.2 MPa, the 0.2% proof stress was at least 261.3 MPa, and the elongation was at least 12.9%.
  • the aluminum wheel obtained by the conventional tunnel furnace shown in Comparative Example 3 was inferior to Example 4 in mechanical properties such as tensile strength, heat resistance and elongation, and Comparative Examples 3 to 4
  • the solid solution rate in the solution treatment is as low as 50% as in the above, it can be seen that the tensile strength, 0.2% power resistance and elongation are inferior to those of the example.
  • the aging treatment temperature is as high as 220 ° C. as in Comparative Examples 5 and 6, it can be seen that the mechanical properties of the obtained aluminum wheel are further inferior.
  • the present invention it is possible to provide an A1 alloy having three mechanical properties of tensile strength, heat resistance, and elongation in a well-balanced manner and excellent fatigue strength.
  • the solution treatment is performed using a fluidized bed, the solid solution ratio of Si and Mg is increased to a predetermined value or more, and the aging treatment temperature is set to a predetermined value or less.
  • the strength and elongation of the precipitation hardening type A1 alloy can be improved.

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Abstract

L'invention concerne un alliage d'aluminium formé par durcissage par précipitation dont la structure eutectique présente une surface moyenne inférieure à 4 νm2. Cet alliage contient 6,5 à 7,5 % en poids de silicium, jusqu'à 0,36 % en poids de magnésium, et 20 à 70 ppm de strontium, et peut servir à la fabrication d'une roue automobile. Le procédé de traitement thermique de l'alliage d'aluminium formé par durcissage par précipitation consiste à réaliser un traitement de solution par disposition de la pièce dans un lit fluidisé de manière qu'au moins 60 % du silicium et/ou du magnésium forment une solution solide dans une phase α, et à réaliser un traitement de vieillissement à une température supérieure à 150 °C mais inférieure à 200 °C. L'alliage d'aluminium ainsi obtenu présente un bon compromis des trois propriétés mécaniques, c.-à-d. résistance à la traction, tension d'essai, et élongation, et présente une excellente résistance à la fatigue.
PCT/JP2001/006157 2000-08-08 2001-07-17 Alliage d'aluminium forme par durcissage par precipitation et procede de traitement thermique de cet alliage Ceased WO2002012582A1 (fr)

Priority Applications (5)

Application Number Priority Date Filing Date Title
AU2001269533A AU2001269533A1 (en) 2000-08-08 2001-07-17 Aluminum alloy formed by precipitation hardening and method for heat treatment thereof
US10/344,271 US20040011434A1 (en) 2000-08-08 2001-07-17 Aluminum alloy formed by precipitation hardening and method for heat treatment thereof
KR10-2003-7001519A KR100533242B1 (ko) 2000-08-08 2001-07-17 석출경화형 알루미늄 합금과 그의 열처리방법
EP01948037A EP1327696A1 (fr) 2000-08-08 2001-07-17 Alliage d'aluminium forme par durcissage par precipitation et procede de traitement thermique de cet alliage
US11/065,000 US20050139299A1 (en) 2000-08-08 2005-02-25 Method for heat treatment of precipitation hardening Al allot

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JP2000-240139 2000-08-08
JP2000240139A JP2001316786A (ja) 2000-03-01 2000-08-08 析出硬化型Ａｌ合金の熱処理方法
JP2000-242069 2000-08-10
JP2000242069A JP2002060879A (ja) 2000-08-10 2000-08-10 析出硬化型Ａｌ合金

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DE102007042506B4 (de) * 2007-09-07 2010-06-17 Norbert Gatzweiler Verfahren zur Abschreckung von Aluminiumbauteilen
FR2944030B1 (fr) * 2009-04-02 2012-10-26 Peugeot Citroen Automobiles Sa Procede de traitement thermique et piece en alliage d'aluminium coulee sous-pression
DE102012017711B4 (de) 2011-09-10 2018-10-18 Audi Ag Verfahren zum Wärmebehandeln eines Bauteils
CN103014569B (zh) * 2012-12-24 2015-04-08 中国科学院金属研究所 一种铝合金枕梁材料热处理方法
CN108998652A (zh) * 2018-09-25 2018-12-14 株洲市九洲传动机械设备有限公司 一种铸造铝合金齿轮箱的热处理方法

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US20050139299A1 (en) 2005-06-30
EP1327696A1 (fr) 2003-07-16
CN1468320A (zh) 2004-01-14

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