U.S. patent application number 10/409728 was filed with the patent office on 2004-07-22 for method for shortening production time of heat treated aluminum alloy castings.
Invention is credited to Bennon, William D., Kamat, Rajeev G., Murtha, Shawn J..
Application Number | 20040140026 10/409728 |
Document ID | / |
Family ID | 32775617 |
Filed Date | 2004-07-22 |
United States Patent
Application |
20040140026 |
Kind Code |
A1 |
Kamat, Rajeev G. ; et
al. |
July 22, 2004 |
Method for shortening production time of heat treated aluminum
alloy castings
Abstract
A method for producing a heat-treated aluminum alloy casting in
a shortened period of time, the method comprising: (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 the heat treatable aluminum alloy casting
is negligible, wherein the first stage cooling comprises a first
stage cooling rate from about 15.degree. F. per second to about
100.degree. F. per second; (c) second stage cooling said heat
treatable aluminum alloy casting to ambient temperature; (d)
heating said heat treatable aluminum alloy casting to an artificial
aging temperature; and (e) artificially aging said heat treatable
aluminum alloy casting at said artificial aging temperature for a
predetermined artificial aging time to form said heat-treated
aluminum alloy casting.
Inventors: |
Kamat, Rajeev G.;
(Murrysville, PA) ; Bennon, William D.;
(Kittanning, PA) ; Murtha, Shawn J.; (Monroeville,
PA) |
Correspondence
Address: |
ECKERT SEAMANS CHERIN & MELLOTT, LLC
ALCOA TECHNICAL CENTER
100 TECHNICAL DRIVE
ALCOA CENTER
PA
15069-0001
US
|
Family ID: |
32775617 |
Appl. No.: |
10/409728 |
Filed: |
April 9, 2003 |
Related U.S. Patent Documents
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Application
Number |
Filing Date |
Patent Number |
|
|
10409728 |
Apr 9, 2003 |
|
|
|
10347948 |
Jan 21, 2003 |
|
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Current U.S.
Class: |
148/698 |
Current CPC
Class: |
C22F 1/04 20130101; C22F
1/047 20130101 |
Class at
Publication: |
148/698 |
International
Class: |
C22F 001/04 |
Claims
We claim:
1. A method for producing a heat-treated aluminum alloy casting in
a shortened period of time, said method comprising: (a) providing a
heat treatable aluminum alloy casting at a solutionizing
temperature; (b) first stage cooling said 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 said first stage cooling comprises a
first stage cooling rate from about 15.degree. F. per second to
about 100.degree. F. per second; (c) second stage cooling said heat
treatable aluminum alloy casting to ambient temperature; (d)
heating said heat treatable aluminum alloy casting to an artificial
aging temperature; and (e) artificially aging said heat treatable
aluminum alloy casting at said artificial aging temperature for a
predetermined artificial aging time to form said heat-treated
aluminum alloy casting.
2. The method of claim 1, wherein said heat treatable aluminum
alloy casting of (a) is selected from the group consisting of 2xxx
series, 6xxx series, and 7xxx series aluminum alloys.
3. The method of claim 1, wherein said heat treatable aluminum
alloy casting of (a) is selected from 6xxx series aluminum
alloys.
4. The method of claim 1, wherein said heat treatable aluminum
alloy casting of (a) is selected from the group consisting of
aluminum alloys 6061, 6063, 6022, 6111, 6082, 6013, 6005, 6009,
6016, 6181, 6260, 6963, and 6060.
5. The method of claim 1, wherein said heat treatable aluminum
alloy casting of (a) is aluminum alloy 6061.
6. The method of claim 1, wherein said heat treatable aluminum
alloy casting of (a) is selected from the group consisting of
aluminum casting alloys A356, A357, and A319.
7. The method of claim 1, wherein said heat treatable aluminum
alloy casting of (a) is selected from the group consisting of
aluminum alloys 2024, 2026, and 2124.
8. The method of claim 1, wherein said heat treatable aluminum
alloy casting of (a) is selected from the group consisting of
aluminum alloys 7050, 7055, 7075, 7085, and 7150.
9. The method of claim 1, wherein said critical temperature of (b)
is about 500.degree. F.
10. The method of claim 1, wherein said artificial aging
temperature of (d) is from about 350.degree. F. to about
400.degree. F.
11. The method of claim 1, wherein said artificial aging time of
(e) is from about 5 minutes to about 120 minutes.
12. The method of claim 1, wherein said heat-treated aluminum alloy
casting of (e) is in a peak strength temper.
13. The method of claim 1, further comprising cooling said
heat-treated aluminum alloy product of (e) to said ambient
temperature.
14. A method for producing a heat-treated aluminum alloy casting in
a shortened period of time, said method comprising: (a) providing a
heat treatable aluminum alloy casting at a solutionizing
temperature; (b) cooling said heat treatable aluminum alloy casting
to a predetermined artificial aging temperature, wherein a cooling
rate is from about 15.degree. F. per second to about 100.degree. F.
per second; and (c) artificially aging said heat treatable aluminum
alloy casting at said artificial aging temperature for a
predetermined artificial aging time to form said heat-treated
aluminum alloy casting.
15. The method of claim 14, wherein said heat treatable aluminum
alloy casting of (a) is selected from the group consisting of 2xxx
series, 6xxx series, and 7xxx series aluminum alloys.
16. The method of claim 14, wherein said heat treatable aluminum
alloy casting of (a) is selected from 6xxx series aluminum
alloys.
17. The method of claim 14, wherein said heat treatable aluminum
alloy casting of (a) is selected from the group consisting of
aluminum alloys 6061, 6063, 6022, 6111, 6082, 6013, 6005, 6009,
6016, 6181, 6260, 6963, and 6060.
18. The method of claim 14, wherein said heat treatable aluminum
alloy casting of (a) is aluminum alloy 6061.
19. The method of claim 14, wherein said heat treatable aluminum
alloy casting of (a) is selected from the group of aluminum casting
alloys A356, A357, and A319.
20. The method of claim 14, wherein said heat treatable aluminum
alloy casting of (a) is selected from the group consisting of
aluminum alloys 2024, 2026, and 2124.
21. The method of claim 14, wherein said heat treatable aluminum
alloy casting of (a) is selected from the group consisting of
aluminum alloys 7050, 7055, 7075, 7085, and 7150.
22. The method of claim 14, wherein said artificial aging
temperature of (b) is about 350-400.degree. F.
23. The method of claim 14, wherein said artificial aging time of
(c) is from about 5 minutes to about 120 minutes.
24. The method of claim 14, wherein said heat-treated aluminum
alloy casting of (c) is in a peak strength temper.
25. The method of claim 14, further comprising cooling said
heat-treated aluminum alloy product of (d) to said ambient
temperature.
Description
CROSS-REFERENCE TO RELATED APPLICATION
[0001] This is a continuation-in-part of U.S. patent application
Ser. No. 10/347,948, filed Jan. 21, 2003 entitled "Method for
Shortening Production Time of Heat Treated Aluminum Alloys".
FIELD OF THE INVENTION
[0002] 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.
BACKGROUND OF THE INVENTION
[0003] 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. [Hatch,
John E., ed., Aluminum Properties and Physical Metallurgy, ASM, OH
(1984)] With the exception of equilibrium phase precipitates, these
hardening phases are not present to a significant degree in as-cast
aluminum, and in order to strengthen the alloy, several thermal
and/or mechanical treatments are typically employed.
[0004] The amounts of soluble alloying elements in heat treatable
aluminum alloys exceed the room temperature or near room
temperature solid solution solubility limits. Therefore, 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.
[0005] A thermal processing step used to strengthen the heat
treatable alloys, is called "solution heat treatment" ("SHT") or
solutionizing 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. When 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.
[0006] 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.
[0007] To achieve desired mechanical properties of the heat
treatable aluminum alloy, it is desirable to maintain the
supersaturation of the alloy as it is cooled to ambient room
temperature. It is possible to maintain a supersaturated condition
at room temperature by cooling the alloy at a rate that is fast
enough to minimize diffusion and thus minimize precipitation of
solute atoms. Cooling after SHT is referred to in the art as
"quenching." Quenching to room temperature is typically practiced
in the trade as: air quenching, where the alloy is cooled in
ambient air (either with or without a fan) or water quenching,
where the alloy is immersed in water or an aqueous solution or
sprayed with water or an aqueous solution.
[0008] After quenching, many solution heat-treated alloys will
exhibit increases in mechanical properties at room temperature, due
to precipitation of hardening phases. This is referred to by
practitioners of the art as "natural aging." Natural aging, to a
point where the mechanical properties of the alloy are stable and
do not change with time, puts the alloy into what is known as a T4
temper. Controlled precipitation hardening of other alloys requires
heating for periods at temperatures above room temperature. This
practice is known as "artificial aging." Artificial aging for an
artificial aging time period, where peak strength is obtained and
where the mechanical properties do not change with further
artificial aging puts the alloy into what is known as T6 temper,
which is also known as peak strength temper. 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.
[0009] In the extrusion of heat treatable alloys from the 6xxx
series, such as aluminum alloy 6061, it is a known practice to heat
or "homogenize" a billet of cast aluminum to change the as-cast
microstructure, thus allowing better extrusion performance. The
homogenized billet is cooled and then reheated before extruding the
billet through a die to obtain a desired extruded form, extrusion,
or product. The extrusion is then quenched to room temperature
either in air, in water, or by using a water mist. 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.degree. 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.degree. 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. A flowchart that summarizes this current
commercial practice is presented in FIG. 3.
[0010] From the description of a known extrusion process of heat
treatable aluminum alloy 6061 presented above, it is seen that
current practice requires long cycle times of heating and cooling
the alloy to obtain a product in peak strength temper.
Inventory-on-demand type of manufacturing is not amenable to the
current process, and an inventory must be warehoused to meet
unexpected customer orders. The current practice is also expensive
in that it involves significant labor-intensive metal handling
between processing steps.
[0011] It is clear that a process for manufacturing heat-treated
aluminum alloy products in a shorter period of time, which could
also be operated in a continuous or semi-continuous fashion, is
desirable. Such a process would be beneficial for improving
productivity and would provide significant cost savings.
[0012] Accordingly, it is a primary object of the current invention
to provide a method of manufacture of a heat-treated aluminum alloy
product in a shortened period.
[0013] It is a further object of the current invention to provide a
rapid aging method of manufacturing a heat-treated aluminum alloy
product in a peak strength temper, which requires shorter
artificial aging time.
[0014] It is another object of this invention to provide a
semi-continuous or continuous method of manufacturing a peak
strength extruded product.
[0015] It is still a further object of the current invention to
provide a rapid aging method of manufacturing a heat-treated
aluminum alloy casting in a peak strength temper, which requires
shorter artificial aging time.
[0016] These and other objects and advantages of the present
invention will be more fully understood and appreciated with
reference to the following description.
SUMMARY OF THE INVENTION
[0017] 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.degree.
F. per second to about 100.degree. 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.
BRIEF DESCRIPTION OF THE DRAWINGS
[0018] Further features, objectives and advantages of the present
invention will be made clearer by reference to the accompanying
drawings in which:
[0019] FIG. 1 is a flowchart for shortening the production time and
rapid aging of heat treatable aluminum alloys according to the
present invention.
[0020] 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.
[0021] FIG. 3 is a flowchart of prior art for the production of
heat treatable aluminum alloys.
[0022] 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.
[0023] 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.
[0024] FIG. 6 is a schematic representation of a temperature--time
plot for yet another preferred embodiment showing cooling to aging
temperature.
[0025] 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.
[0026] 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.
[0027] 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.
[0028] 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.
[0029] 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.
[0030] 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.
[0031] FIG. 13 is a flowchart for shortening the production time
and rapid aging of heat treatable aluminum alloy castings according
to the present invention.
DETAILED DESCRIPTION OF PREFERRED EMBODIMENTS
[0032] 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. In the context of this invention, the term "alloy"
refers to heat treatable aluminum alloys, as described in the
Background Section herein, unless otherwise specified.
[0033] Turning first to 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. In this preferred embodiment, 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. 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. Typically, heat treatable
aluminum alloys can be solutionized at temperatures above about
900.degree. 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.
[0034] After hot working, the alloy is subjected to 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.degree. F. per second,
and preferably is about 25.degree. 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.degree. 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.
[0035] For purposes of this invention, 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. By using an
optimum first stage cooling rate, as defined herein, adding a
stretching step in the process flow path is not required.
[0036] In an embodiment of the invention depicted in FIG. 1 and
FIG. 4, after the first stage cooling, 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. Referring to 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.
[0037] With continuing reference to FIG. 1, FIG. 4 and FIG. 5, it
is seen that following second stage cooling to ambient, or near
ambient 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.
[0038] Data that are presented later in the Examples indicate that
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.
Preferably, 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.
[0039] As seen in FIG. 1 and FIG. 4 after heating to artificial
aging temperature, 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.degree. F. to about 400.degree. 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.
[0040] It is recognized by those skilled in the art that useful or
optimum artificial aging temperatures may vary out of the stated
preferred range, and that any experimentally determined useful or
optimum artificial aging temperature for a particular heat
treatable aluminum alloy is anticipated by and incorporated into
this invention.
[0041] 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.
[0042] In certain instances, however, it may be desirable to use
artificially aging times longer than 120 minutes. For example, in
certain 7xxx series aluminum alloys (aluminum-zinc alloys),
artificial aging for a period of time that is longer than what is
required to attain peak strength is purposely practiced to increase
the corrosion resistance of the alloy, or make the alloy less
susceptible to stress corrosion cracking. This practice is referred
to as "overaging." The overaged product usually exhibits a slight
decrease in strength, but also a significant decrease in
susceptibility to stress corrosion cracking.
[0043] It is recognized that artificial aging times for this
invention can exceed the upper bound of the preferred range stated
previously, and in such instance, the practice would still be
covered by the teachings of the instant invention.
[0044] After artificial aging, the heat-treated aluminum alloy of
this invention is typically allowed to air cool to ambient
temperature. Upon cooling, 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.
[0045] An additional preferred embodiment of this invention is
summarized by the flowchart presented in FIG. 2 and FIG. 6. As per
the previously described embodiment, 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.degree. F. per second. In this embodiment, 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 discussions about
cooling means, cooling media, artificial aging times and artificial
aging temperatures, which were included with the previously
described preferred embodiments (FIG. 1, FIG. 4 and FIG. 5), also
apply to the current preferred embodiment (FIG. 2 and FIG. 6).
[0046] As previously indicated, the instant invention is suitable
for all types of wrought heat treatable aluminum alloys. For
example, referring to FIG. 1 and FIG. 2, the center trunk of the
flow chart could describe the manufacture of alloy extrusions or
rolled plate. For the production of rolled sheet, after hot working
and before first stage cooling, 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. For forged products, it may be
beneficial to employ the optional steps of annealing and cold
forging after either first stage or second stage cooling.
[0047] It should be realized that the total duration of any
optional steps after second stage cooling are not exceed 8 hours.
The hot worked and cooled product of this invention should be
heated to artificial aging temperature within 8 hours of
cooling.
[0048] It is additionally anticipated that the objects of this
invention can be met with aluminum casting alloys or with as-cast
wrought aluminum alloys (for brevity, collectively referred to as
"castings"), which are not substantially hot worked. A process
flowchart for use of this invention for aluminum alloy castings is
presented in FIG. 13. When an aluminum alloy casting is cooled from
a solutionizing temperature, utilizing a minimum first stage
cooling rate that is rapid enough to keep the alloying elements in
solution at temperatures closer to ambient temperature, the rapid
artificial aging practice of this invention can be used to
strengthen the cast alloy. Examples of aluminum casting alloys
appropriate for this invention include, but are not limited to:
A356, A357, and A319. 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.
[0049] Returning to 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. In this preferred embodiment, 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.
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.
Typically, heat treatable aluminum alloy castings can be
solutionized at temperatures above about 900.degree. F. The heat
treatable aluminum alloy casting is not substantially hot
worked.
[0050] 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.degree. F. per second,
and preferably is about 25.degree. 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.degree. 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.
[0051] For purposes of this invention, 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. By using an
optimum first stage-cooling rate, as defined herein, adding a
stretching step in the process flow path is not required.
[0052] In an embodiment of the invention depicted in FIG. 13, after
the first stage cooling, 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.
[0053] With continuing reference to FIG. 13, it is seen that
following second stage cooling to ambient, or near ambient
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.
[0054] 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. Preferably, 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.
[0055] As seen in FIG. 13, after heating to artificial aging
temperature, 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.degree. F. to about 400.degree. 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.
[0056] It is recognized by those skilled in the art that useful or
optimum artificial aging temperatures may vary out of the stated
preferred range, and that any experimentally determined useful or
optimum artificial aging temperature for a particular heat
treatable aluminum alloy casting is anticipated by and incorporated
into this invention.
[0057] 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.
[0058] In certain instances, however, it may be desirable to use
artificially aging times longer than 120 minutes. For example, in
certain 7xxx series aluminum alloys (aluminum-zinc alloys),
artificial aging for a period of time that is longer than what is
required to attain peak strength is purposely practiced to increase
the corrosion resistance of the alloy, or make the alloy less
susceptible to stress corrosion cracking. This practice is referred
to as "averaging." The overaged product usually exhibits a slight
decrease in strength, but also a significant decrease in
susceptibility to stress corrosion cracking.
[0059] It is recognized that artificial aging times for this
invention can exceed the upper bound of the preferred range stated
previously, and in such instance, the practice would still be
covered by the teachings of the instant invention.
[0060] After artificial 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.
[0061] The benefit of the present invention is illustrated in the
following examples.
EXAMPLES 1-18
[0062] To demonstrate the practice of the present invention and the
advantages thereof, 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.
[0063] In order to solutionize the tensile specimens, and to
simulate extruding at a solutionizing temperature, the tensile
specimens were subjected to a furnace solution heat treatment at
1000.degree. F. for 3 minutes at temperature. The specimens were
then first stage cooled to about 500.degree. F. by quenching in
water. For these specimens, the water quench rate is greater than
400.degree. 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. In Examples 10-18, 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 35020 F., 375.degree. F. and 400.degree. 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.
1TABLE 1 First Stage Natural Artificial Tensile Ultimate Cooling
Aging Aging Artificial Yield Tensile Example Curve in Rate Time
Temp. Aging Strength Strength Percent Number (.degree. F./s) (min.)
(.degree. F.) Time (h) (ksi) (ksi) Elongation 1 A >400 15 350 1
43.3 50.0 21.5 2 A >400 15 350 2 45.2 51.1 21.0 3 A >400 15
350 4 46.3 51.5 20.5 4 B >400 15 375 1 45.4 50.0 20.0 5 B
>400 15 375 2 46.3 50.5 19.5 6 B >400 15 375 4 46.5 50.3 19.0
7 C >400 15 400 1 45.3 48.7 18.5 8 C >400 15 400 2 45.5 48.8
18.5 9 C >400 15 400 4 45.4 48.6 17.0 10 A' >400 480 350 1
28.2 41.1 28.5 11 A' >400 480 350 2 35.0 44.4 25.0 12 A' >400
480 350 4 40.4 46.9 22.5 13 B' >400 480 375 1 43.3 47.0 18.5 14
B' >400 480 375 2 44.3 47.5 18.0 15 B' >400 480 375 4 44.1
47.2 19.0 16 C' >400 480 400 1 37.7 44.8 23.0 17 C' >400 480
400 2 42.6 47.1 20.0 18 C' >400 480 400 4 45.0 48.2 19.0
[0064] 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.degree. F. and
400.degree. F. was required to provide tensile strengths around 45
ksi (thousand-pounds per square inch). These values of tensile
strength are significantly higher than the minimum yield strength
specification of 35 ksi for alloy 6061-T6. The advantage of the
instant invention is clear when it is recognized that to achieve
comparable mechanical properties, the prior art practice (see FIG.
3) utilizes 8-24 hours of natural aging combined with 6-10 hours of
artificial aging, whereas the practice of the instant invention
eliminates or minimizes natural aging and requires only about 5 to
about 120 minutes of artificial aging.
[0065] When the alloys were naturally aged for 8 hours, and
subsequently artificially aged for 1 or 2 hours at 350.degree. F.,
the Examples 10-11 (curve A' of FIG. 7) did not meet minimum the
specification of 35 ksi. While the 8-hour naturally aged specimens
that were artificially aged at 375.degree. F. and 400.degree. F.
(Examples 13-15 and 16-18, curves B' and C', respectively) met
minimum specification at all temperatures, the values were
generally lower than those with only 15 minutes natural aging
(Examples 1-9). The detrimental effect of natural aging on yield
stress is clear from the data presented in FIG. 7.
[0066] 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).
[0067] 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.
EXAMPLES 19-30
[0068] To further demonstrate the practice of the present invention
and particularly the effect of first stage cooling rate on
mechanical strengths, 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-inch rod. In order to solutionize the tensile specimens,
and to simulate extruding at a solutionizing temperature, the
tensile specimens were subjected to a furnace solution heat
treatment at 1025.degree. F. for 2 minutes at temperature.
[0069] The specimens were then first stage cooled to about
500.degree. F. by quenching in ambient air or in water maintained
at different temperatures. For example, to achieve a first stage
cooling rate of about 80.degree. F./s (Examples 28-30, curve G in
FIGS. 10-12), the specimens were immersed in water maintained at
100.degree. F. Other first stage cooling rates were approximately
5.degree. F./s, 25.degree. F./s and 38.degree. 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.degree. F. in a Wood's metal bath. All of the
artificially aged samples were tensile tested according to ASTM
Method B557 for mechanical properties.
[0070] 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.degree. F./s or greater, and which exhibited
significantly higher yield strengths and ultimate tensile strengths
than the minimum specifications for 6061-T6.
[0071] FIG. 12 shows that all specimens had sufficient percent
elongation to meet the 6061-T6 specification for elongation.
[0072] The data in FIGS. 10-12 and Table 2 predict that when first
stage cooling is about 15.degree. F./s or greater and when natural
aging is short and inadvertent, rapid artificial aging for as
little as 5 minutes at 400.degree. F. is sufficient to provide
mechanical strengths that meet specifications for 6061-T6.
[0073] The data in FIGS. 10-12 and Table 2 demonstrate that when
first stage cooling is about 25.degree. F./s or greater and when
natural aging is short and inadvertent, rapid artificial aging for
as little as 15 minutes at 400.degree. F. is sufficient to provide
mechanical strengths that meet specifications for 6061-T6.
2TABLE 2 First Stage Natural Artificial Tensile Ultimate Curve in
Cooling Aging Aging Artificial Yield Tensile Example FIGS. Rate
Time Temp. Aging Strength Strength Percent Number 10-12 (.degree.
F./s) (min.) (.degree. F.) Time (h) (ksi) (ksi) Elongation 19 D 5 2
400 0.25 17.1 31.2 23.0 20 D 5 2 400 0.5 19.2 32.0 22.0 21 D 5 2
400 1 20.5 31.8 21.0 22 E 25 2 400 0.25 40.8 46.7 15.0 23 E 25 2
400 0.5 43.1 48.0 14.5 24 E 25 2 400 1 44.0 48.4 14.0 25 F 38 2 400
0.25 40.3 45.5 17.0 26 F 38 2 400 0.5 42.8 47.1 17.0 27 F 38 2 400
1 43.0 46.8 17.0 28 G 80 2 400 0.25 41.3 45.7 20.0 29 G 80 2 400
0.5 43.8 47.8 17.5 30 G 80 2 400 1 44.8 48.3 20.0
[0074] Having described the presently preferred embodiments, it is
to be understood that the invention may be otherwise embodied
within the scope of the claims.
* * * * *