Patent Grant
10435774
Heat treatable aluminum alloys, such as the 2xxx series aluminum alloys, may be solution heat treated and artificially aged to produce high strength tempers. Strength may be further increased by cold working the product between the solution heat treating and artificial aging steps. However, some wrought product forms may be unable to realize uniform cold work due to the shape of the product. This generally results in high strength differential across the final product. For example, as illustrated in
Broadly, the present disclosure relates to wrought 2xxx aluminum lithium alloy products that achieve a low strength differential across such products, and methods for producing such alloy products. Generally, the wrought 2xxx aluminum lithium alloy products disclosed herein achieve a low strength differential across the product when they contain the alloying elements described herein, as well as have a certain ratio of copper-to-magnesium.
Generally, the new 2xxx alloys have from about 2.75 to about 5.0 wt. % Cu, from about 0.2 to about 0.8 wt. % Mg, from about 0.1 to 1.10 wt. % Li, from 0.3 to about 2.0 wt. % Ag, from about 0.4 to 1.5 wt. % Zn, and up to about 1.0 wt. % Mn, the balance being aluminum, optional incidental elements, and impurities. The alloys generally have a copper-to-magnesium ratio (Cu/Mg) in the range of from about 6.1 to about 17. In some embodiments, an alloy consists of, or consists essentially of, these alloying ingredients, the balance being aluminum, optional incidental elements, and impurities.
Wrought products incorporating such alloys generally achieve a small strength differential across the product, such as a strength differential of not greater than 8 ksi across the wrought aluminum alloy product. These wrought products are generally solution heat treated, cold worked, and artificially aged. Cold work is sometimes known as effective cold work strain (called “effective strain” herein for purposes of simplicity). Due to the cold working, a first portion of the wrought product may realize a first amount of cold work (e.g., a high amount of cold work) and a second portion of the wrought product may realize a second amount of cold work (e.g., a low amount of cold work or even no cold work). The first amount of cold work is generally at least about 0.5% higher than the second amount of cold work. For example, and with reference now to
In some embodiments, the first portion may be associated with the portion of the wrought product having the highest amount of cold work. In these embodiments, the second portion may be associated with the portion of the wrought product having the lowest amount of cold work or lowest effective strain (e.g., no strain). In these embodiments, the strength differential across the entire wrought product may be not greater than about 8 ksi, or less, such as any of the strength differential values noted above.
The low strength differential between the first and second portions is generally achieved with short aging times, such as not greater than about 64 hours of aging at a temperature of about 310° F., or a substantially equivalent artificial aging temperature and duration. As appreciated by those skilled in the art, aging temperatures and/or times may be adjusted based on well known aging principles and/or formulas. Thus, those skilled in the art could increase the aging temperature but decrease the aging time, or vice-versa, or only slightly change only one of these parameters, and still achieve the same result as “not greater than 64 hours of aging at a temperature of about 310° F.”. The amount of artificial aging practices that could achieve the same result as “not greater than 64 hours of aging at a temperature of about 310° F.” is numerous, and therefore all such substitute aging practices are not listed herein, even though they are within the scope of the present invention. The use of the phrase “or a substantially equivalent artificial aging temperature and duration” or the phrase “or a substantially equivalent practice” is used to capture all such substitute aging practices. As may be appreciated, these substitute artificial aging steps can occur in one or multiple steps, and at one or multiple temperatures.
In one embodiment, the low strength differential is achieved with not greater than about 60 hours of artificial aging at a temperature of about 310° F., or a substantially equivalent artificial aging practice. In other embodiments, the low strength differential is achieved with not greater than about 55 hours of artificial aging, or not greater than about 50 hours of artificial aging, or not greater than about 45 hours of artificial aging, or not greater than about 40 hours of artificial aging, or not greater than about 35 hours of artificial aging, or not greater than about 30 hours of artificial aging, or not greater than about 25 hours of artificial aging, or even less, at a temperature of about 310° F., or a substantially equivalent artificial aging practice.
Copper (Cu) is included in the new alloy, and generally in the range of from about 2.75 wt. % to about 5.0 wt. % Cu. As illustrated in the below examples, when copper goes below about 2.75 wt. % or exceeds about 5.0 wt. %, the alloy may not realize a small strength differential across the product and/or may have a low overall strength. In one embodiment, a new alloy includes at least about 3.0 wt. % Cu. In other embodiments, a new alloy includes at least about 3.25 wt. % Cu, or at least about 3.5 wt. % Cu, or at least about 3.75 wt. % Cu. In one embodiment, a new alloy includes not greater than about 4.9 wt. % Cu. In other embodiments, a new alloy may include not greater than about 4.8 wt. % Cu, or not greater than about 4.7 wt. % Cu, or not greater than about 4.6 wt. % Cu, or not greater than about 4.5 wt. % Cu. In one embodiment, a new alloy includes Cu in the range of from about 3.0 wt. % to about 4.7 wt. %. Other Cu ranges using the above-described limits may be used.
Magnesium (Mg) is included in the new alloy, and generally in the range of from about 0.2 wt. % to about 0.8 wt. % Mg. As illustrated in the below examples, when magnesium goes below about 0.2 wt. % or exceeds about 0.8 wt. %, the alloy may not realize a small strength differential across the product and/or may have a low overall strength. In one embodiment, a new alloy includes at least about 0.25 wt. % Mg. In other embodiments, a new alloy may include at least about 0.3 wt. % Mg, or at least about 0.35 wt. % Mg. In one embodiment, a new alloy includes not greater than about 0.70 wt. % Mg. In other embodiments, a new alloy may include not greater than about 0.60 wt. % Mg, or not greater than about 0.55 wt. % Mg, or not greater than about 0.5 wt. % Mg, or not greater than about 0.45 wt. % Mg. In one embodiment, a new alloy includes Mg in the range of from about 0.20 wt. % to about 0.50 wt. %. Other Mg ranges using the above-described limits may be used.
Similarly, the ratio of copper-to-magnesium (Cu/Mg ratio) may be related to alloy properties. For example, when the Cu/Mg ratio is less than about 6.1 or is more than about 17, the alloy may not realize a small strength differential across the product and/or may have a low overall strength. In one embodiment, the Cu/Mg ratio of the new alloy is at least about 6.5. In other embodiments, the Cu/Mg ratio of the new alloy is at least about 7.0, or at least about 7.5, or at least about 8.0, or at least about 8.5, or at least about 9.0. In one embodiment, the Cu/Mg ratio of the new alloy is not greater than about 16. In other embodiments, the Cu/Mg ratio of the new alloy is not greater than about 15, or not greater than about 14.5, or not greater than about 14.0, or is not greater than about 13.5, or is not greater than about 13.0, or is not greater than about 12.5, or is not greater than about 12.0. In one embodiment, the Cu/Mg ratio in the range of from about 8.0 to about 15.0. In another embodiment, the Cu/Mg ratio in the range of from about 8.5 to about 14.5. In yet another embodiment, the Cu/Mg ratio is in the range of from about 9.0 to about 12.5. Other Cu/Mg ratio ranges using the above-described limits may be used.
Lithium (Li) is included in the new alloy, and generally in the range of from about 0.1 wt. % to 1.10. Lithium helps reduce the density of the product. However, as shown below, alloys that include more than 1.10 wt. % may not realize work insensitive properties. In one embodiment, a new alloy includes not greater than about 1.05 wt. % Li. In other embodiments, a new alloy may include not greater than about 1.00 wt. % Li, or not greater than about 0.95 wt. % Li, or not greater than about 0.9 wt. % Li, or not greater than about 0.85 wt. % Li. To achieve lower density, the new alloy generally includes at least about 0.1 wt. % Li. In one embodiment, a new alloy includes at least about 0.2 wt. % Li. In other embodiments, a new alloy includes at least about 0.3 wt. % Li, or at least about 0.4 wt. % Li, or at least about 0.5 wt. % Li, or at least about 0.55 wt. % Li, or at least about 0.60 wt. % Li, or at least about 0.65 wt. % Li, or at least about 0.7 wt. % Li, or at least about 0.75 wt. % Li. In one embodiment, a new alloy includes Li in the range of from about 0.70 wt. % to about 0.90 wt. %. In another embodiment, a new alloy includes Li in the range of from about 0.75 wt. % to about 0.85 wt. %. Other Li ranges using the above-described limits may be used.
Silver (Ag) is included in the new alloy, and the new alloys generally include at least about 0.30 wt. % Ag. In one embodiment, a new alloy includes at least about 0.35 wt. % Ag. In other embodiments, a new alloy may include at least about 0.40 wt. % Ag, or at least about 0.45 wt. % Ag. Ag may be included in the alloy up to its solubility limit. However, Ag may be expensive, and thus the new alloy generally includes not greater than about 2.0 wt. % Ag. In one embodiment, a new alloy includes not more than about 1.5 wt. % Ag. In other embodiments, a new alloy includes not greater than about 1.0 wt. % Ag, or not greater than about 0.8 wt. % Ag, or not greater than about 0.75 wt. % Ag, or not greater than about 0.7 wt. % Ag, or not greater than about 0.65 wt. % Ag, or not greater than about 0.60 wt. % Ag, or not greater than about 0.55 wt. % Ag. In one embodiment, a new alloy includes Ag in the range of from about 0.40 wt. % to about 0.60 wt. %. In another embodiment, a new alloy includes Ag in the range of from about 0.45 wt. % to about 0.55 wt. %. Other Ag ranges using the above-described limits may be used.
Zinc (Zn) is included in the new alloy, and generally the new alloys include at least about 0.40 wt. % Zn. As illustrated in the below examples, when Zn goes below about 0.40 wt. %, the alloy may not realize a small strength differential across the product and/or may have a low overall strength. Preferably, the alloys include at least about 0.50 wt. % Zn to realize lower strength differential properties (e.g., ≤5 ksi, ≤3 ksi, or ≤1 ksi, or less) in shorter aging times (e.g., ≤50 hours of aging). In one embodiment, a new alloy includes at least about 0.55 wt. % Zn. In other embodiments, a new alloy may include at least about 0.6 wt. % Zn, or at least about 0.65 wt. % Zn, or at least about 0.7 wt. % Zn, or at least about 0.75 wt. % Zn. Zn may be included in the alloy up to its solubility limit, however Zn is generally maintained below about 1.5 wt. % to restrict its negative effect on density. In one embodiment, a new alloy includes not greater than about 1.4 wt. % Zn. In other embodiments, a new alloy may include not greater than about 1.3 wt. % Zn, or not greater than about 1.2 wt. % Zn, or not greater than about 1.1 wt. % Zn, or not greater than about 1.0 wt. % Zn, or not greater than about 0.9 wt. % Zn, or not greater than about 0.85 wt. % Zn. In one embodiment, a new alloy includes Zn in the range of from about 0.70 wt. % to about 0.90 wt. %. In another embodiment, a new alloy includes Zn in the range of from about 0.75 wt. % to about 0.85 wt. %. Other Zn ranges using the above-described limits may be applied.
Manganese (Mn) may optionally be included in the new alloy, and in an amount up to 1.0 wt. %. In one embodiment, a new alloy includes at least about 0.01 wt. % Mn. In other embodiments, a new alloy includes at least about 0.10 wt. % Mn, or at least about 0.15 wt. % Mn, or at least about 0.2 wt. % Mn, or at least about 0.25 wt. % Mn. In one embodiment, a new alloy includes not greater than about 0.8 wt. % Mn. In other embodiments, a new alloy includes not greater than about 0.7 wt. % Mn, or not greater than about 0.6 wt. % Mn, or not greater than about 0.5 wt. % Mn, or not greater than about 0.4 wt. % Mn. In one embodiment, a new alloy includes Mn in the range of from about 0.20 wt. % to about 0.40 wt. %. In another embodiment, a new alloy includes Mn in the range of from about 0.25 wt. % to about 0.35 wt. %. Other Mn ranges using the above-described limits may be used.
As noted above, the new alloys generally include the stated alloying ingredients, the balance being aluminum, optional incidental elements, and impurities. As used herein, “incidental elements” means those elements or materials, other than the above listed elements, that may optionally be added to the alloy to assist in the production of the alloy. Examples of incidental elements include grain structure control elements and casting aids, such as grain refiners and deoxidizers. Optional incidental elements may be include in the alloy in a cumulative amount of up to 1.0 wt. %.
As used herein, “grain structure control element” means elements or compounds that are deliberate alloying additions with the goal of forming second phase particles, usually in the solid state, to control solid state grain structure changes during thermal processes, such as recovery and recrystallization. For purposes of the present patent application, grain structure control elements includes Zr, Sc, Cr, V, and Hf, to name a few, but excludes Mn.
In the alloying industry, manganese may be considered both an alloying ingredient and a grain structure control element—the manganese retained in solid solution may enhance a mechanical property of the alloy (e.g., strength), while the manganese in particulate form (e.g., as Al6Mn, Al12Mn3Si2—sometimes referred to as dispersoids) may assist with grain structure control. However, since Mn is separately defined with its own composition limits in the present patent application, it is not within the definition of “grain structure control elements” for the purposes of the present patent application.
The amount of grain structure control material utilized in an alloy is generally dependent on the type of material utilized for grain structure control and/or the alloy production process. In one embodiment, the grain structure control element is Zr, and the alloy includes from about 0.01 wt. % to about 0.25 wt. % Zr. In some embodiments, Zr is included in the alloy in the range of from about 0.05 wt. %, or from about 0.08 wt. %, to about 0.12 wt. %, or to about 0.15 wt. %, or to about 0.18 wt. %, or to about 0.20 wt. % Zr. In one embodiment, Zr is included in the alloy and in the range of from about 0.01 wt. % to about 0.20 wt. % Zr. In another embodiment, Zr is included in the alloy and in the range of from about 0.05 wt. % to about 0.15 wt. % Zr. Other Zr ranges using the above-described limits may be applied.
Scandium (Sc), chromium (Cr), and/or hafnium (Hf) may be included in the alloy as a substitute (in whole or in part) for Zr, and thus may be included in the alloy in the same or similar amounts as Zr. In one embodiment, the grain structure control element is at least one of Sc and Hf. However, Sc and Hf may be expensive. Thus, in some embodiments, the new alloys are free of Sc and Hf (i.e., include less than 0.02 wt. % each of Sc and Hf).
Grain refiners are inoculants or nuclei to seed new grains during solidification of the alloy. An example of a grain refiner is a ⅜ inch rod comprising 96% aluminum, 3% titanium (Ti) and 1% boron (B), where virtually all boron is present as finely dispersed TiB2 particles. During casting, the grain refining rod is fed in-line into the molten alloy flowing into the casting pit at a controlled rate. The amount of grain refiner included in the alloy is generally dependent on the type of material utilized for grain refining and the alloy production process. Examples of grain refiners include Ti combined with B (e.g., TiB2) or carbon (TiC), although other grain refiners, such as Al—Ti master alloys may be utilized. Generally, grain refiners are added in an amount of ranging from about 0.0003 wt. % to about 0.005 wt. % to the alloy, depending on the desired as-cast grain size. In addition, Ti may be separately added to the alloy in an amount up to 0.03 wt. % to increase the effectiveness of grain refiner. When Ti is included in the alloy, it is generally present in an amount of from about 0.01 wt. %, or from about 0.03 wt. %, to about 0.10 wt. %, or to about 0.15 wt. %. In one embodiment, the aluminum alloy includes a grain refiner, and the grain refiner is at least one of TiB2 and TiC, where the wt. % of Ti in the alloy is from about 0.01 wt. % to about 0.1 wt. %.
Some incidental elements may be added to the alloy during casting to reduce or restrict (and is some instances eliminate) ingot cracking due to, for example, oxide fold, pit and oxide patches. These types of incidental elements are generally referred to herein as deoxidizers. Examples of some deoxidizers include Ca, Sr, and Be. When calcium (Ca) is included in the alloy, it is generally present in an amount of up to about 0.05 wt. %, or up to about 0.03 wt. %. In some embodiments, Ca is included in the alloy in an amount of about 0.001-0.03 wt % or about 0.05 wt. %, such as 0.001-0.008 wt. % (or 10 to 80 ppm). Strontium (Sr) may be included in the alloy as a substitute for Ca (in whole or in part), and thus may be included in the alloy in the same or similar amounts as Ca. Traditionally, beryllium (Be) additions have helped to reduce the tendency of ingot cracking, though for environmental, health and safety reasons, some embodiments of the alloy are substantially Be-free. When Be is included in the alloy, it is generally present in an amount of up to about 20 ppm.
Incidental elements may be present in minor amounts, or may be present in significant amounts, and may add desirable or other characteristics on their own without departing from the alloy described herein, so long as the alloy retains the desirable characteristics described herein. It is to be understood, however, that the scope of this disclosure should not/cannot be avoided through the mere addition of an element or elements in quantities that would not otherwise impact on the combinations of properties desired and attained herein.
As used herein, impurities are those materials that may be present in the new alloy in minor amounts due to, for example, the inherent properties of aluminum and/or leaching from contact with manufacturing equipment, among others. Iron (Fe) and silicon (Si) are examples of impurities generally present in aluminum alloys. The Fe content of the new alloy should generally not exceed about 0.25 wt. %. In some embodiments, the Fe content of the alloy is not greater than about 0.15 wt. %, or not greater than about 0.10 wt. %, or not greater than about 0.08 wt. %, or not greater than about 0.05 or 0.04 wt. %. Likewise, the Si content of the new alloy should generally not exceed about 0.25 wt. %, and is generally less than the Fe content. In some embodiments, the Si content of the alloy is not greater than about 0.12 wt. %, or not greater than about 0.10 wt. %, or not greater than about 0.06 wt. %, or not greater than about 0.03 or 0.02 wt. %.
The new alloy may be substantially free of impurities other than Fe and Si, meaning that the alloy contains no more than about 0.25 wt. % of any other element, except the alloying elements, optional incidental elements, and Fe and Si impurities described above. Further, the total combined amount of these other elements in the alloy does not exceed about 0.5 wt. %. The presence of other elements beyond these amounts may affect the basic and novel properties of the alloy, such as its strength, toughness, and/or cold work sensitivity, to name a few. In one embodiment, each one of these other elements, individually, does not exceed about 0.10 wt. % in the alloy, and the total combined amount of these other elements does not exceed about 0.35 wt. %, or about 0.25 wt. % in the alloy. In another embodiment, each one of these other elements, individually, does not exceed about 0.05 wt. % in the alloy, and the total combined amount of these other elements does not exceed about 0.15 wt. % in the alloy. In another embodiment, each one of these other elements, individually, does not exceed about 0.03 wt. % in the alloy, and the total combined amount of these other elements does not exceed about 0.1 wt. % in the alloy.
Except where stated otherwise, the expression “up to” when referring to the amount of an element means that that elemental composition is optional and includes a zero amount of that particular compositional component. Unless stated otherwise, all compositional percentages are in weight percent (wt. %).
In addition to a low strength differential, the wrought products produced from the new alloys may realize high strength. In one embodiment, a product achieves a typical longitudinal tensile yield strength (TYS—0.2% offset) of at least about 60 ksi when tested in accordance with ASTM E8 and B557. In other embodiments, a product achieves a typical TYS at least about 62 ksi, or at least about 64 ksi, or at least about 66 ksi, or at least about 68 ksi, or at least about 70 ksi, or at least about 72 ksi, or at least about 74 ksi, or at least about 76 ksi, or at least about 78 ksi, or at least about 80 ksi, or at least about 82 ksi, or more.
The alloy products may also be corrosion resistant, tough, and/or have a high fatigue resistance, among other properties. For example, in one embodiment, a wrought product may achieve a KIC (plane strain) fracture toughness of at least about 20 ksi√in. in the long-transverse (L-T) direction, when tested in accordance with ASTM E399. In other embodiments, a wrought product may achieve a KIC fracture toughness of at least about 21 ksi√in., or at least about 22 ksi√in., or at least about 23 ksi√in., or at least about 24 ksi√in., or at least about 25 ksi√in., or at least about 26 ksi√in., or at least about 27 ksi√in., or at least about 28 ksi√in., or at least about 29 ksi√in., or at least about 30 ksi√in., or at least about 31 ksi√in., or at least about 32 ksi√in., or at least about 33 ksi√in., or at least about 34 ksi√in., or more, in the long-transverse (L-T) direction.
In one embodiment, a wrought product may achieve a fracture toughness that is at least about 3% higher in the T8 temper relative to a comparable product in the T6 temper. In other embodiments, a wrought product may achieve a fracture toughness that is at least about 4% higher, or at least about 6% higher, or at least about 8% higher, or at least about 10% higher, or at least about 15% higher, or at least about 20% higher, or at least about 25% higher, or at least about 30% higher, or at least about 35% higher, or at least about 40% higher, or more, in the T8 temper relative to a comparable product in the T6 temper.
The new alloys may be used in all wrought product forms, but are especially applicable to wrought product forms that realize cold work differential across the product due to differing parts of the product being cold worked differing amounts, resulting in variable effective strain across the product. An example of a prior art product having variable effective strain is shown in
Forged products are generally die forged or hand forged products. Some forged products may have a first portion that receives a first amount of cold work, and a second portion that receives a second, different amount of cold work. Previously, 2xxx aluminum lithium forged products may realize high strength differential across the product strength due to the difference in cold work between the first and second portions of the product. However, when produced in accordance with the present disclosure, such 2xxx aluminum lithium forged products may realize a small strength differential across the product (i.e., are work insensitive), as described above.
Stepped-extruded products are those extruded products that have a change in profile along their length. These stepped-extruded products generally have a first portion having a first cross-sectional area that receives a first amount of cold work, and a second portion having a second cross-sectional portion that receives a second amount of cold work (e.g., no cold work). Like the forged products, previous 2xxx aluminum lithium stepped-extruded products may realize a high strength differential due to the difference in cold work between the first and second portions of the product. However, when produced in accordance with the present disclosure, such 2xxx aluminum lithium stepped-extruded products may realize a small strength differential across the product, as described above.
Stretch-formed products are products where a part (typically a sheet or extrusion) is pulled over a die to impart a permanent deformation. The die is designed such that a desired shape is achieved. Some stretch-formed products may have a first portion that receives a first amount of cold work, and a second portion that receives a second, different amount of cold work. Previously, such 2xxx aluminum lithium stretch-formed products may realize a high strength differential due to the difference in cold work between the first and second portions of the product. However, when produced in accordance with the present disclosure, such stretch-formed products may realize a small strength differential across the product (i.e., are work insensitive), as described above.
The new alloy can be prepared into wrought form, and in the appropriate temper, by more or less conventional practices, some examples of which are illustrated in
After the selecting step (500), a casting step is completed (520), where an ingot is cast having the selected composition, the balance being aluminum and impurities. From the ingot, a wrought aluminum alloy product is prepared (540). The wrought aluminum alloy product may realize at least about 0.5% differential in cold work, but no more than an 8 ksi longitudinal strength differential across the wrought product.
With respect to the preparing step (540), and referring now to
Regarding the post-SHT cold working step (560), as mentioned above, this step may introduce a variable amount of cold work (561) into the product (e.g., at least about 0.5%), as illustrated in
Although the present technology has been described relative to wrought products having variable post-SHT cold work, it is anticipated that the alloys described herein may find use in applications having generally uniform post-SHT cold work or no post-SHT cold work. Examples of such products include forged wheels and landing gear components, as well as rolled products, such as sheet, plate and conventional extrusions.
Unless otherwise indicated, the following definitions apply to the present application:
“Wrought aluminum alloy product” means an aluminum alloy product that is hot worked after casting, and includes rolled products, such as sheet and plate, forged products, extruded products, stepped-extruded products, and stretch-formed products, among others.
“Forged aluminum alloy product” means a wrought aluminum alloy product that is either die forged or hand forged.
“Solution heat treating” means exposure of an aluminum alloy to elevated temperature for the purpose of placing solute(s) into solid solution.
“Cold working” means working the aluminum alloy product at temperatures that are not considered hot working temperatures, generally below about 250° F.
“Artificially aging” means exposure of an aluminum alloy to elevated temperature for the purpose of precipitating solute(s). Artificial aging may occur in one or a plurality of steps, which can include varying temperatures and/or exposure times.
“A strength differential of not greater than about XX ksi across the wrought aluminum alloy product”, where XX is a numerical value of not greater than 8, means that the longitudinal tensile yield strength of a representative first portion of the wrought aluminum alloy product is not more than about XX ksi higher than the longitudinal tensile yield strength of a representative second portion of the wrought aluminum alloy product, where the difference in cold work between the first and second portions is at least about 0.5%. Representative portions of the wrought aluminum alloy product exclude surfaces that are later removed (e.g., by machining) or surface recrystallization layers, among others, as known to those skilled in the art. Non-representative portions of the wrought aluminum alloy product are not included in the determination of the 8 ksi strength differential.
The longitudinal direction means the direction associated with the main grain flow direction developed during the hot working of the wrought aluminum alloy product. A wrought product generally has a main grain flow direction in the predominate direction of hot working. For example, a rolled product generally has a main grain flow direction in the direction of rolling, and an extruded product generally has a main grain flow direction in the direction of extruding.
These and other aspects, advantages, and novel features of this new technology are set forth in part in the description that follows and will become apparent to those skilled in the art upon examination of the following description and figures, or may be learned by practicing one or more embodiments of the technology provided for by the present disclosure.
Reference will now be made in detail to the accompanying drawings, which at least assist in illustrating various pertinent embodiments of the new technology provided for by the present disclosure.
Eight aluminum alloys of varying composition are bookmold cast, with final dimensions of 1.375″×4″×11″. The composition of each of the alloys is provided in Table 1, below. All values are in weight percent.
All of these alloys also contain about 0.3-0.4 wt. % Mn, about 0.5 wt. % Ag, about 0.01-0.03 wt. % Ti, about 0.11-0.14 wt. % Zr, 0-0.11 wt. % V, less than about 0.04 wt. % Si, and less than about 0.06 wt. % Fe, the balance being aluminum and impurities (e.g., ≤0.05 wt. % of any other element, and ≤0.15 wt. % total of all other elements).
After casting, the alloys are homogenized, reheated, hot rolled to 0.2″ gauge, solution heat treated, and quenched. Each sheet is then cut in half, with one piece of each sheet remaining in the as-quenched condition, while the other half of each sheet is stretched (about 3%). All sheets are then artificially aged, after which the as-quenched sheets are in the T6 temper, and the stretched sheets are in the T8 temper. For all sheets and in both tempers, longitudinal blanks are produced. After at least 4 days of natural aging, the blanks are artificially aged at 310° F. for about 16, 24, 40, 64, and 96 hours. Tensile testing for each alloy in the T6 and T8 condition is conducted in accordance with ASTM B557. Aging curves for each alloy in the T6 and T8 condition are illustrated in
The T8 temper is a product that is solution heat-treated, cold worked, and then artificially aged, and applies to products that are cold worked to improve strength, or in which the effect of cold work in flattening or straightening is recognized in mechanical property limits. For the purposes of the T8-type alloys tested in this Example 1, the T8 temper was a product that included about 3% cold work in the form of stretch. However, it will be appreciated by those skilled in the art that many variations of the T8 temper exist, and that the present application applies to all such variations of the T8 temper.
The T6 temper is a product that is solution heat-treated and then artificially aged, and applies to products that are not cold worked after solution heat-treatment, or in which the effect of cold work in flattening or straightening may not be recognized in mechanical property limits. For the purposes of the T6-type alloys tested in this application, the T6 temper was a product that was not cold worked. However, it will be appreciated by those skilled in the art that many variations of the T6 temper exist, and that the present application applies to all such variations of the T6 temper.
As illustrated in
Alloy 6 has a Cu/Mg ratio of about 10.3 and includes about 0.8 wt. % Zn. Alloys 7, which has about the same amount of Li and Zn as alloy 6, but has a Cu/Mg ratio of about 6.4, does not achieve a small strength differential in not greater than about 40 hours of aging, but does achieve a small strength differential in not greater than about 64 hours of aging (4.6 ksi). Alloy 8, which has about the same amount of Li and Zn as alloy 6 and has a Cu/Mg ratio of about 6, does not achieve a small strength differential even with 96 hours of aging. These results indicate that a Cu:Mg ratio of at least about 6.1, and preferably of at least about 6.5, in combination with increased Zn and/or Cu levels, may result in the production of wrought products having a low longitudinal TYS differential and in not greater than about 64 hours of artificial aging.
Twenty-one aluminum alloys of varying composition are cast as bookmolds. The composition of each of the alloys is provided in Table 3, below. All values are in weight percent.
Unless otherwise indicated, all of these alloys also contained about 0.2-0.3 wt. % Mn, about 0.5 wt. % Ag, about 0.8 wt. % Li, about 0.8 wt. % Zn, about 0.01-0.03 wt. % Ti, about 0.11-0.14 wt. % Zr, less than about 0.04 wt. % Si, and less than about 0.06 wt. % Fe, the balance being aluminum and impurities (e.g., ≤0.05 wt. % of any other element, and ≤0.15 wt. % total of all other element). Alloy U is similar to Alloy 6 of Example 1. After casting, all alloys were processed similar to Example 1 to test the strength difference between the T6 and T8 tempers. Those results are illustrated in
As illustrated in
Alloys that do not have a Cu/Mg ratio of at least about 6.1 may not achieve a small strength differential. This is illustrated by Alloys A, B, E, F, and Q, particularly Alloy F, as well as
Alloys that have a Cu/Mg ratio of more than about 15 may not achieve a small strength differential and/or may not have high strength. This is illustrated by Alloys D, H, K, O, R, and S, particularly Alloys H and K, as well as
As shown, Alloy H does achieve a small strength differential (about 5.4 ksi) in not greater than about 64 hours of aging. Thus, in some embodiments, alloys similar to Alloy H may be beneficial in some circumstances, despite their potentially lower overall strength. Thus, in some embodiments, alloys having a Cu/Mg ratio as high as about 16 or 17 may be useful.
Alloys that do not contain sufficient amounts of Cu and/or Mg may not achieve good strength properties. This is illustrated by Alloys A-D, and F, particularly Alloys C and F, as well as
Alloys that do not contain a sufficient amount of Zn may not achieve good strength properties. This is illustrated by Alloys L-O, particularly Alloys L and M, as well as
Alloys that do not contain a sufficient amount of Ag may not achieve good strength properties. This is illustrated by Alloy T and
Based on the foregoing,
Additional bookmold testing is completed. Thirteen aluminum alloys of varying composition are cast as bookmolds. The composition of each of the alloys is provided in Table 4, below. All values are in weight percent.
Unless otherwise indicated, all of these alloys also contained about 0.2-0.3 wt. % Mn, about 0.5 wt. % Ag, about 0.8 wt. % Li, about 0.8 wt. % Zn, about 0.01-0.03 wt. % Ti, about 0.11-0.14 wt. % Zr, less than about 0.04 wt. % Si, and less than about 0.06 wt. % Fe, the balance being aluminum and impurities (e.g., ≤0.05 wt. % of any other element, and ≤0.15 wt. % total of all other element). After casting, all alloys were processed similar to Example 1 to test the strength difference between the T6 and T8 tempers, except, unlike Example 1, the T8 products were produced with both 3% and 6% cold work for each alloy. The mechanical properties are tested, and results are illustrated in
As shown in
As shown in
As shown in
Additional bookmold testing is completed. Three aluminum alloys of varying composition are cast as bookmolds. The composition of each of the alloys is provided in Table 5, below. All values are in weight percent.
Unless otherwise indicated, all of these alloys also contained about 0.2-0.3 wt. % Mn, about 0.01-0.03 wt. % Ti, about 0.11-0.14 wt. % Zr, less than about 0.04 wt. % Si, and less than about 0.06 wt. % Fe, the balance being aluminum and impurities (e.g., ≤0.05 wt. % of any other element, and ≤0.15 wt. % total of all other element). After casting, all alloys were processed similar to Example 1 to test the strength difference between the T6 and T8 tempers, except, unlike Example 1, the T8 products were produced with 1.5% cold work for each alloy, and by a two-step artificial aging practice, with the second step occurring at 320° F.
The mechanical properties are tested, and results are illustrated in
Two ingots are cast, having the composition listed in Table 6, below. The ingots are homogenized. The ingots are then sawed into smaller billets. These billets are subjected to a series of die forging operations, including upsetting the as-cast billet, preforming and the final finish operation. All of the hot forming operations are carried out between 700-900° F. The forged parts are then solution heat treated and quenched. Half of these forged parts are then artificially aged, resulting in T6 temper pieces. The remaining forged pieces cold worked 6% by compression, and then artificial aged, resulting in T852 temper pieces.
All of these alloys also contained about 0.3 wt. % Mn, about 0.5 wt. % Ag, about 0.8 wt. % Li, about 0.8 wt. % Zn, about 0.03 wt. % Ti, about 0.12 wt. % Zr, less than about 0.04 wt. % Si, and less than about 0.06 wt. % Fe, the balance being aluminum and impurities (e.g., ≤0.05 wt. % of any other element, and ≤0.15 wt. % total of all other element).
The mechanical properties are tested in the T6 and T8 tempers, the T8 temper having about 6% cold work, the results of which are illustrated in
The toughness properties of the alloys are also tested, the results of which are provided in Table 7, below.
This data shows that a good combination of strength-toughness can be achieved in wrought aluminum alloy products, and with a low strength differential across such products.
While various embodiments of the present disclosure have been described in detail, it is apparent that modifications and adaptations of those embodiments will occur to those skilled in the art. However, it is to be expressly understood that such modifications and adaptations are within the spirit and scope of the present disclosure.
This patent application is a divisional of U.S. patent application Ser. No. 13/084,451, now U.S. Pat. No. 8,845,827, filed Apr. 11, 2011, which claims priority to U.S. Provisional Patent Application No. 61/323,224, filed Apr. 12, 2010, entitled, “2XXX Series Aluminum Lithium Alloys Having Low Strength Differential,” and is also related to PCT Patent Application No. PCT/US2011/031975, each of which are incorporated herein by reference in their entirety.
| Number | Date | Country |
|---|---|---|
| WO 2009036953 | Mar 2009 | WO |
| Number | Date | Country | |
|---|---|---|---|
| 20150000799 A1 | Jan 2015 | US |
| Number | Date | Country | |
|---|---|---|---|
| 61323224 | Apr 2010 | US |
| Number | Date | Country | |
|---|---|---|---|
| Parent | 13084451 | Apr 2011 | US |
| Child | 14486209 | US |
