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WO2004065043A2 - Procede de reduction de la duree de production de pieces moulees en alliage d'aluminium traitees par la chaleur - Google Patents

Procede de reduction de la duree de production de pieces moulees en alliage d'aluminium traitees par la chaleur Download PDF

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Publication number
WO2004065043A2
WO2004065043A2 PCT/US2004/001921 US2004001921W WO2004065043A2 WO 2004065043 A2 WO2004065043 A2 WO 2004065043A2 US 2004001921 W US2004001921 W US 2004001921W WO 2004065043 A2 WO2004065043 A2 WO 2004065043A2
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Prior art keywords
aluminum alloy
heat treatable
heat
artificial aging
temperature
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Ceased
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PCT/US2004/001921
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WO2004065043A3 (fr
Inventor
Rajeev G. Kamat
William D. Bennon
Shawn J. Murtha
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Alcoa Corp
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Alcoa Corp
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Priority claimed from US10/347,948 external-priority patent/US7503986B2/en
Application filed by Alcoa Corp filed Critical Alcoa Corp
Publication of WO2004065043A2 publication Critical patent/WO2004065043A2/fr
Publication of WO2004065043A3 publication Critical patent/WO2004065043A3/fr
Anticipated expiration legal-status Critical
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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
    • 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 the field of thermomechanical processing of aluminum alloys.
  • the invention is particularly useful for shortening the production time of heat treatable aluminum alloys, while maintaining the required mechanical properties of the alloy.
  • Heat treatable aluminum alloys rely on the controlled precipitation of solute alloying elements to achieve desired mechanical properties such as tensile yield strength, ultimate tensile strength and elongation. This is referred to by those skilled in the art as precipitation hardening. It is also recognized by practitioners of the art that hardening phases in the heat treatable alloys include solute clusters or Guinier-Preston (GP) zones, transition precipitates, transition phase particles, and to a lesser degree, equilibrium phase precipitates.
  • GP Guinier-Preston
  • as-cast heat treatable aluminum alloys typically contain secondary phase particles, which are also known in the metal arts as intermetallic precipitates, equilibrium phase precipitates or simply precipitates.
  • the precipitates found in as-cast alloys are typically coarse and incoherent with the lattice of the aluminum crystals or grains. Further, the as-cast precipitates may exist at grain boundaries. These forms of precipitates do not generally impart significant strength to the aluminum alloy, and may be detrimental to properties such as fatigue and fracture resistance.
  • a thermal processing step used to strengthen the heat treatable alloys is called “solution heat treatment” (“SHT”) or solutionizing treatment.
  • SHT solution heat treatment
  • the SHT is conducted at an elevated temperature, or solutionizing temperature, at which the alloying elements have maximum solubility in the aluminum solid solution, while avoiding equilibrium melting.
  • the solution heat treated alloy is cooled, the solid solution becomes supersaturated; the equilibrium solubility of the alloying element in the aluminum solid solution is exceeded. This provides a thermodynamic driving force for the precipitation of the second phase particles.
  • Precipitation of solute alloying elements is further controlled by the diffusion rate of the solute. Diffusion is a kinetic phenomenon, and the diffusion rate decreases as the temperature decreases. The effect of slowing diffusion rates due to cooling is to decrease the precipitation rate of second phase particles. Therefore, as the alloy is cooled, precipitation is favored by supersaturation of solute, but opposed by slower solute diffusion rates.
  • the alloys For some aluminum-magnesium-silicon alloys, designated 6xxx series (or 6000 series) aluminum alloys, such as but not limited to 6061 and 6063, it is possible to attain specified T6 properties when there is no separate furnace SHT. When these alloys are cooled from an elevated- temperature, mechanical working, or shaping process, and they can be artificially aged to attain T6 properties, the alloys may be designated as being in a T5 temper, although T6 is also considered an appropriate designation, providing the mechanical properties meet T6 specifications.
  • the quench rate or cooling rate of this practice will depend upon the geometry of the extruded form, but for a 0.25-inch thick extruded shape, the air quench rate is about 5-10°F per second.
  • the process of extruding and exiting a die at a temperature similar to the solutionizing temperature followed by quenching is known in the art as "press quenching.” After quenching, the extrusion may be stretched by 0.5-1% in order to eliminate any thermal stress distortion, which may have occurred during the quenching process. Typically, the extrusion naturally ages for eight hours or longer, during handling within the production facility. After natural aging, the extrusion is heated in a conventional furnace to a typical artificial aging temperature, which is about 350- 400°F for aluminum alloy 6061.
  • the cycle time for artificial aging includes the steps of heating the extrusion to the artificial aging temperature and holding or "soaking" the extrusion at the artificial aging temperature for a predetermined artificial aging time.
  • the cycle times required to reach a peak strength temper, which meets the specifications for 6061- T6, or 6061-T5, is about 6-10 hours.
  • the objects of the current invention are met by: (a) providing a heat treatable aluminum alloy casting at a solutionizing temperature; (b) first stage cooling the heat treatable aluminum alloy casting to a critical temperature at which precipitation of second phase particles of said heat treatable aluminum alloy casting is negligible, wherein the first stage cooling comprises a first stage cooling rate from about 15°F per second to about 100°F per second; (c) second stage cooling the heat treatable aluminum alloy casting to ambient temperature; (d)heating the heat treatable aluminum alloy casting to an artificial aging temperature; and (e) artificially aging the heat treatable aluminum alloy casting at the artificial aging temperature for a predetermined artificial aging time to form a heat-treated aluminum alloy casting.
  • FIG. 1 is a flowchart for shortening the production time and rapid aging of heat treatable aluminum alloys according to the present invention.
  • FIG. 2 is a flowchart of another embodiment for shortening the production time and rapid aging of heat treatable aluminum alloys according to the present invention.
  • FIG. 3 is a flowchart of prior art for the production of heat treatable aluminum alloys.
  • FIG. 4 is schematic representation of a temperature - time plot for one preferred embodiment of this invention showing two-stage cooling to ambient temperature using different cooling rates.
  • FIG. 5 is a schematic representation of a temperature - time plot for another preferred embodiment of this invention showing two stage cooling to ambient temperature using the same cooling rate.
  • FIG. 6 is a schematic representation of a temperature - time plot for yet another preferred embodiment showing cooling to aging temperature.
  • FIG. 7 are plots of mechanical testing data showing tensile yield strengths for aluminum alloy 6061 processed according to the method of this invention with two minutes of unintentional natural aging and prior art method with eight hours of intentional natural aging.
  • FIG. 8 are plots of mechanical testing data showing ultimate tensile strengths for aluminum alloy 6061 processed according to the method of this invention with two minutes of unintentional natural aging and prior art method with eight hours of intentional natural aging.
  • FIG. 9 are plots of mechanical testing data showing percent elongation for aluminum alloy 6061 processed according to the method of this invention with two minutes of unintentional natural aging and a prior art method with and eight hours of intentional natural aging.
  • FIG. 10 are plots of mechanical testing data showing the effect of changing cooling rates after solution heat treatment of aluminum alloy 6061 with two minutes unintentional natural aging prior to artificial aging on tensile yield strengths.
  • FIG. 11 are plots of mechanical testing data showing the effect of changing cooling rates after solution heat treatment of aluminum alloy 6061 with two minutes unintentional natural aging prior to artificial aging on ultimate tensile strengths.
  • FIG. 12 are plots of mechanical testing data showing the effect of changing cooling rates after solution heat treatment of aluminum alloy 6061 with two minutes unintentional natural aging prior to artificial aging on percent elongation.
  • FIG. 13 is a flowchart for shortening the production time and rapid aging of heat treatable aluminum alloy castings according to the present invention.
  • the inventive method is effective at significantly reducing the amount of time required for artificial aging of heat treatable aluminum alloys in order to achieve peak or maximum mechanical strengths.
  • alloy refers to heat treatable aluminum alloys, as described in the Background Section herein, unless otherwise specified.
  • FIG. 1 and FIG. 4 there is illustrated a process flowchart and a temperature versus time schematic diagram, respectively, for shortening the production time and rapid aging of heat treatable aluminum alloys according to the present invention.
  • the essential steps of this invention are outlined in the central vertical trunk of the flowchart of FIG 1.
  • Optional processing steps are presented in the lateral branches of the flowchart of FIG. 1.
  • a heat treatable aluminum alloy is subjected to hot working at a solutionizing temperature to form a wrought product, product form, or simply a product.
  • a solutionizing temperature is defined as a temperature at which the alloying elements have maximum solubility in the aluminum solid solution, while avoiding equilibrium melting.
  • heat treatable aluminum alloys After exposing a heat treatable aluminum alloy at a solutionizing temperature for a sufficient period to dissolve the alloying elements into solid solution, the alloy is solutionized.
  • heat treatable aluminum alloys can be solutionized at temperatures above about 900°F.
  • Hot working includes extruding, rolling, and forging the alloy, or any other form of thermomechanical processing that is available to one skilled in the art.
  • Product forms include extrusions of various shapes, sheet, plate, and forgings.
  • first stage cooling or quenching As depicted in FIG. 1 and FIG. 4.
  • the first stage cooling rate is chosen to be rapid enough to keep the alloying elements in solution at temperatures closer to ambient temperature. In this condition, the solid-state solution of the alloy is said to be in a supersaturated condition.
  • the minimum first stage cooling rate should be about 15°F per second, and preferably is about 25 °F per second.
  • First stage cooling should proceed to a lower temperature or critical temperature at which precipitation of second phase particles does not significantly occur.
  • a first stage cooling lower temperature also referred to as a first stage critical temperature or simply as a critical temperature, that is suitable for many heat treatable aluminum alloys is about 500°F, but it is recognized that the first stage cooling lower temperature can be any temperature at which second phase precipitation is negligible. It is further recognized that the quenching or cooling means and medium are not critical to this invention. As long as the minimum cooling rate is met, the cooling can be achieved by immersing, flooding, spraying or other cooling means that is known to those skilled in the art; or by air quenching, water quenching, aqueous solution quenching, oil quenching, molten metal quenching or quenching with any other medium that is familiar to those skilled in the art.
  • a maximum cooling rate is not specified. However, it is realized that a range of optimum first stage cooling rates can exist.
  • An optimum first stage cooling rate is one in which the requirement of keeping the alloying elements in solid state solution is met, while further providing that the cooling rate is not high enough for thermal stresses, which occur in the alloy during cooling, to cause distortion or deformation of the alloy product form. Quenching at high cooling rates can cause thermal stresses that are of greater magnitude than the inherent mechanical strength of the alloy. For example, a press-quenched extrusion can be significantly deformed or warped by thermal stresses. Deformed extrusions must be stretched to relieve the thermally induced stresses and strains and to return the product form to the originally intended shape.
  • Stretching adds additional costs to the final product, including process costs from the additional stretching step and associated handling, and capital costs incurred by requiring a stretching machine.
  • adding a stretching step in the process flow path is not required.
  • the alloy is subjected to a second " stage cooling to ambient temperature.
  • the rate of second stage cooling is not critical for the practice of this invention.
  • the second stage cooling need not reduce the temperature of the alloy entirely to ambient or room temperature, and that second stage cooling could proceed to any desired temperature below that of the critical first stage temperature.
  • the invention specifies two stages of cooling, it should be additionally recognized that the second stage cooling rate could be the same as the first stage cooling rate, as long as the equivalent cooling rates are sufficiently high enough to minimize precipitation of second phase particle at temperatures above the first stage critical temperature.
  • FIG. 5 a time temperature plot is presented for the embodiment of the instant invention where the first and second stage cooling rates are equivalent and sufficiently high to prevent precipitation.
  • the alloy is then heated to an artificial aging temperature. It is desirable to begin heating to artificial aging temperature as soon as possible after second stage cooling in order to minimize natural aging. Any natural aging that might occur before heating to the artificial aging temperature should be inadvertent, and occur during optional steps in the practice of this invention. For example, natural aging could occur during sawing and stretching processes.
  • any inadvertent natural aging should be limited to less than about eight hours.
  • the step of heating to artificial aging temperature should occur within eight hours after second stage cooling.
  • heating to artificial aging temperature should begin within four hours after second stage cooling. More preferably, heating to artificial aging temperature should begin within one hour after second stage cooling. Most preferably, heating to artificial aging temperature should begin immediately after second stage cooling.
  • the heating rate to artificial aging temperatures is not specified for this invention, but it is realized that faster heating rates will shorten the time required to practice this invention.
  • the product is soaked or held at the artificial aging temperature for a predetermined artificial aging time.
  • Preferred artificial aging temperatures used in this invention are temperatures from about 350°F to about 400°F, inclusive, including all fractional values of temperature within this range. Further, it is to be appreciated that optimum artificial aging temperatures are dependent in part upon the composition of the specific alloy that is to be artificially aged.
  • Preferred artificial aging times for this invention can be as low as about 5 minutes and up to about 120 minutes. This artificial aging time is significantly less than the prior art artificial aging time of 6 to 8 hours (FIG. 3), and hence the artificial aging time of this invention is termed rapid aging.
  • the heat-treated aluminum alloy of this invention is typically allowed to air cool to ambient temperature.
  • the products of this invention can be inspected, tested for properties, packed, and shipped to customers or end- users.
  • the products of this invention can be subjected to further fabrication steps known to those of ordinary skill in the art, such as but not limited to, anodizing, machining and forming, and then can be resold as finished or semi-finished parts.
  • FIG. 2 and FIG. 6 An additional preferred embodiment of this invention is summarized by the flowchart presented in FIG. 2 and FIG. 6.
  • the alloy undergoes that steps of: 1) hot working at a solutionizing temperature and 2) first stage cooling to a critical temperature using a minimum cooling rate of about 15°F per second.
  • the second stage cooling step takes the temperature of the product to its predetermined artificial aging temperature.
  • the product is then artificially aged for about 5 to 120 minutes.
  • the instant invention is suitable for all types of wrought heat treatable aluminum alloys.
  • the center trunk of the flow chart could describe the manufacture of alloy extrusions or rolled plate.
  • the optional steps of annealing, cold working, and a furnace solution heat treatment may be employed, as shown on FIG. 1 and FIG. 2.
  • Extrusions, and other wrought forms may be sawed and/or stretched, typically before the artificial aging step of this invention, but it is conceivable that these optional steps could occur after artificial aging, as long as the capacity of the stretcher machine was sufficient to stretch the artificially aged products.
  • Preferred as-cast wrought aluminum alloys for use with this invention include 2000, 6000 and 7000 series alloys, and more specifically aluminum alloys: 2024, 2026, 2124, 6061, 6063, 6022, 6111, 6082, 6013, 6005, 6009, 6016, 6181, 6260, 6963, 6060, 7050, 7055, 7075, 7085, and 7150.
  • FIG. 13 there is illustrated a process flowchart for shortening the production time and rapid aging of heat treatable aluminum alloy castings according to the present invention.
  • the essential steps of this invention are outlined in the central vertical trunk of the flowchart of FIG 13.
  • Optional processing steps are presented in the lateral branches of the flowchart of FIG. 13.
  • a heat treatable aluminum alloy casting is brought to a solutionizing temperature either by cooling from the melt or by heating from a lower temperature.
  • a solutionizing temperature is defined as a temperature at which the alloying elements have maximum solubility in the aluminum solid solution, while avoiding equilibrium melting.
  • heat treatable aluminum alloy castings After exposing a heat treatable aluminum alloy casting at a solutionizing temperature for a sufficient period to dissolve the alloying elements into solid solution, the alloy is solutionized.
  • heat treatable aluminum alloy castings can be solutionized at temperatures above about 900°F. The heat treatable aluminum alloy casting is not substantially hot worked.
  • the alloy After solutionizing, the alloy is subjected to first stage cooling or quenching, as depicted in FIG. 13.
  • the first stage-cooling rate is chosen to be rapid enough to keep the alloying elements in solution at temperatures. closer to ambient temperature. In this condition, the solid-state solution of the alloy is said to be in a supersaturated condition.
  • the minimum first stage-cooling rate should be about 15°F per second, and preferably is about 25 °F per second.
  • First stage cooling should proceed to a lower temperature or critical temperature at which precipitation of second phase particles does not significantly occur.
  • a first stage cooling lower temperature also referred to as a first stage critical temperature or simply as a critical temperature, that is suitable for many heat treatable aluminum alloys is about 500°F, but it is recognized that the first stage cooling lower temperature can be any temperature at which second phase precipitation is negligible. It is further recognized that the quenching or cooling means and medium are not critical to this invention. As long as the minimum cooling rate is met, the cooling can be achieved by immersing, flooding, spraying or other cooling means that is known to those skilled in the art; or by air quenching, water quenching, aqueous solution quenching, oil quenching, molten metal quenching or quenching with any other medium that is familiar to those skilled in the art.
  • a maximum cooling rate is not specified. However, it is realized that a range of optimum first stage cooling rates can exist.
  • An optimum first stage cooling rate is one in which the requirement of keeping the alloying elements in solid state solution is met, while further providing that the cooling rate is not high enough for thermal stresses, which occur in the alloy during cooling, to cause distortion or deformation of the alloy casting. Quenching at high cooling rates can cause thermal stresses that are of greater magnitude than the inherent mechanical strength of the alloy. For example, a press-quenched extrusion can be significantly deformed or warped by thermal stresses. Deformed extrusions must be stretched to relieve the thermally induced stresses and strains and to return the product form to the originally intended shape.
  • Stretching adds additional costs to the final product, including process costs from the additional stretching step and associated handling, and capital costs incurred by requiring a stretching machine.
  • adding a stretching step in the process flow path is not required.
  • the alloy is subjected to a second stage cooling to ambient temperature.
  • the rate of second stage cooling is not critical for the practice of this invention. Furthermore, it is recognized that the second stage cooling need not reduce the temperature of the alloy entirely to ambient or room temperature, and that second stage cooling could proceed to any desired temperature below that of the critical first stage temperature. While the invention specifies two stages of cooling, it should be additionally recognized that the second stage-cooling rate could be the same as the first stage-cooling rate, as long as the equivalent cooling rates are sufficiently high enough to minimize precipitation of second phase particle at temperatures above the first stage critical temperature.
  • the alloy is then heated to an artificial aging temperature. It is desirable to begin heating to artificial aging temperature as soon as possible after second stage cooling in order to minimize natural aging. Any natural aging that might occur before heating to the artificial aging temperature should be inadvertent, and occur during optional steps in the practice of this invention. For example, natural aging could occur during sawing and stretching processes.
  • any inadvertent natural aging should be limited to less than about eight hours.
  • the step of heating to artificial aging temperature should occur within eight hours after second stage cooling.
  • heating to artificial aging temperature should begin within four hours after second stage cooling. More preferably, heating to artificial aging temperature should begin within one hour after second stage cooling. Most preferably, heating to artificial aging temperature should begin immediately after second stage cooling.
  • the heating rate to artificial aging temperatures is not specified for this invention, but it is realized that faster heating rates will shorten the time required to practice this invention.
  • the casting is soaked or held at the artificial aging temperature for a predetermined artificial aging time.
  • Preferred artificial aging temperatures used in this invention are temperatures from about 350°F to about 400°F, inclusive, including all fractional values of temperature within this range. Further, it is to be appreciated that optimum artificial aging temperatures are dependent in part upon the composition of the specific alloy that is to be artificially aged.
  • Preferred artificial aging times for this invention can be as low as about 5 minutes and up to about 120 minutes. This artificial aging time is significantly less than the prior art artificial aging time of 6 to 8 hours (FIG. 3), and hence the artificial aging time of this invention is termed rapid aging.
  • the heat-treated aluminum alloy casting of this invention is typically allowed to air cool to ambient temperature. Upon cooling, the castings of this invention can be inspected, tested for properties, packed, and shipped to customers or end- users.
  • the castings of this invention can be subjected to further fabrication steps known to those of ordinary skill in the art, such as but not limited to, machining and forming, and then can be resold as finished or semi-finished parts.
  • aluminum alloy 6061 extrusions were subjected to the methods of this invention.
  • a billet of aluminum alloy 6061 was extruded to a 1-inch rod.
  • Tensile test specimens were machined per ASTM Method B557. Duplicate specimens were machined next to each other from the 1 " rod.
  • the tensile specimens were subjected to a furnace solution heat treatment at 1000°F for 3 minutes at temperature. The specimens were then first stage cooled to about 500°F by quenching in water. For these specimens, the water quench rate is greater than 400°F per second. The specimens were then second stage cooled in water to ambient temperature. In Examples 1-9, tensile specimens were allowed to naturally age at ambient temperature for 15 minutes, and then the specimens were further grouped and rapidly heated to different artificial aging temperatures in a Wood's metal bath.
  • tensile specimens were naturally aged at ambient temperature for 8 hours, and then the specimens were further grouped and rapidly heated to different artificial aging temperatures in a Wood's metal bath. Artificial aging temperatures of 350°F, 375°F and 400°F were used in these examples. All of the artificially aged samples were tensile tested according to ASTM Method B557 for mechanical properties. The results of the tensile tests are found in FIG. 7 - FIG. 9 and Table 1.
  • FIG. 7-FIG. 9 The graphic representation of the tensile test data in FIG. 7-FIG. 9 demonstrate the validity of rapid aging of the current invention, and demonstrate the detriment of lengthy natural aging to this invention. As described above, any natural aging that occurs during the practice of this invention should be inadvertent and minimal.
  • Tensile yield strength data found in FIG. 7 show that with 15 minutes of natural aging (Examples 1-3, 4-6, and 7-9; corresponding to curves A, B, and C respectively), only 1 hour of artificial aging at temperatures between 350°F and 400°F was required to provide tensile strengths around 45 ksi (thousand-pounds per square inch).
  • FIG. 8 illustrates that the same trends are observed for ultimate tensile strengths.
  • Minimum specified ultimate tensile strength is 38 ksi for 6061 -T6 and the rapid aging practice of this invention provides ultimate tensile strengths that are greater than 48 ksi (Examples 1-3, 4-6, and 7-9; curves A, B, and C, respectively).
  • the detrimental effect of lengthy natural aging to the practice of this invention is also observed as lower ultimate tensile strengths (Examples 10-12, 13-15, 16-18; curves A', B', and C, respectively).
  • FIG. 9 illustrates that the both the rapid aging practice and prior art practice resulted in adequate percent elongation.
  • the minimum specification for this property for 6061-T6 is 10 %. All of the Examples 1-18 met this specification.
  • first stage cooling rate of about 80°F/s (Examples 28-30, curve G in FIGS. 10-12)
  • the specimens were immersed in water maintained at 100°F.
  • Other first stage cooling rates were approximately 5°F/s, 25°F/s and 38°F/s (Examples 19-21, 22-24, 25-7; curves D, E, and F, respectively, in FIGS. 10-12).
  • the specimens were then second stage cooled to ambient temperature. All tensile specimens in this experiment were allowed to naturally age at ambient temperature for no longer than 2 minutes, and then the specimens were rapidly heated to an aging temperature of 400°F in a Wood's metal bath. All of the artificially aged samples were tensile tested according to ASTM Method B557 for mechanical properties.
  • FIGS . 10- 12 and Table 2 provide data that demonstrate the effect of first stage cooling rate on the practice of this invention.
  • Examples 19-21 (curve D) were first stage cooled at 5°/s. None of the specimens in this group met the minimum specifications for yield strength (FIG. 10) or ultimate tensile strength (FIG. 11).
  • Examples 22-24, 25-27, and 28-30 (curves E, F, and G, respectively) show data from specimens that were first stage cooled at 25°F/s or greater, and which exhibited significantly higher yield strengths and ultimate tensile strengths than the minimum specifications for 6061-T6.
  • FIG. 12 shows that all specimens had sufficient percent elongation to meet the 6061-T6 specification for elongation.

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Abstract

L'invention concerne un procédé de production d'une pièce moulée en alliage d'aluminium traitée par la chaleur pendant une période réduite de temps, le procédé consistant : (a) à fournir une pièce moulée en alliage d'aluminium que l'on peut traiter par la chaleur à une température de solutionisation ; (b) à refroidir le premier étage de la pièce moulée en alliage d'aluminium susceptible d'être traitée par la chaleur à une température critique à laquelle la précipitation de particules de seconde phase de la pièce moulée en alliage d'aluminium susceptible d'être traitée par la chaleur est négligeable, le refroidissement du premier étage comprenant une vitesse de refroidissement du premier à étage allant d'environ 15 °F par seconde à environ 100 °F par seconde ; (c) à refroidir le second étage de la pièce moulée en alliage d'aluminium susceptible d'être traitée par la chaleur à une température ambiante ; (d) à chauffer ladite pièce moulée en alliage d'aluminium susceptible d'être traitée par la chaleur à une température de vieillissement artificiel ; et (e) à vieillir de manière artificielle ladite pièce moulée en alliage d'aluminium susceptible d'être traitée par la chaleur à une température de vieillissement artificiel pendant une durée de vieillissement artificiel prédéterminée afin d'obtenir ladite pièce moulée en alliage d'aluminium traitée par la chaleur.
PCT/US2004/001921 2003-01-21 2004-01-21 Procede de reduction de la duree de production de pieces moulees en alliage d'aluminium traitees par la chaleur Ceased WO2004065043A2 (fr)

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US10/347,948 2003-01-21
US10/347,948 US7503986B2 (en) 2003-01-21 2003-01-21 Method for shortening production time of heat treated aluminum alloys
US10/409,728 US20040140026A1 (en) 2003-01-21 2003-04-09 Method for shortening production time of heat treated aluminum alloy castings
US10/409,728 2003-04-09

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