HIGH-STRENGTH, HIGHLY FORMABLE ALUMINUM ALLOYS AND METHODS OF MAKING THE SAME

CROSS-REFERENCE TO RELATED APPLICATION This application claims the benefit of U.S. Provisional Application No. 62/575,573, filed October 23, 2017, which is incorporated herein by reference in its entirety.

FIELD

The present disclosure relates to the fields of material science, materials chemistry, metal manufacturing, aluminum alloys, and aluminum manufacturing. In particular, the present disclosure relates to high-strength and highly formable aluminum alloys and methods of making and processing the same.

BACKGROUND

Aluminum alloys can exhibit high strength due, in part, to the elemental content of the alloys. For example, high strength 6xxx series aluminum alloys can be prepared by including high concentrations of certain elements, such as magnesium (Mg), silicon (Si), and/or copper (Cu). However, such aluminum alloys containing high concentrations of these elements display poor formability properties. In particular, precipitates can form along grain boundaries in an aluminum matrix. Precipitate formation along grain boundaries can increase strength in the alloy but negatively affect alloy deformation (e.g., reduce bendability, formability, or any suitable desired deformation). In addition, the alloys can exhibit reduced yield strength after artificial aging.

SUMMARY

Covered embodiments of the invention are defined by the claims, not this summary. This summary is a high-level overview of various aspects of the invention and introduces some of the concepts that are further described in the Detailed Description section below. This summary is not intended to identify key or essential features of the claimed subject matter, nor is it intended to be used in isolation to determine the scope of the claimed subject matter. The subject matter should be understood by reference to appropriate portions of the entire specification, any or all drawings, and each claim.

Described herein are aluminum alloys comprising about 0.8 - 1.5 wt. % Si, 0.1 - 0.5 wt. % Fe, 0.5 - 1.0 wt. % Cu, 0.5 - 0.9 wt. % Mg, up to 0.1 wt. % Ti, up to 0.5 wt. % Mn, up to 0.5 wt. % Cr, up to 0.5 wt. % Zr, up to 0.5 wt. % V, up to 0.15 wt. % impurities, and Al. In some cases, the aluminum alloys can comprise about 0.9 - 1.4 wt. % Si, 0.1 - 0.35 wt. % Fe, 0.6 - 0.9 wt. % Cu, 0.6 - 0.9 wt. % Mg, 0.01 - 0.09 wt. % Ti, up to 0.3 wt. % Mn, up to 0.3 wt. % Cr, up to 0.3 wt. % Zr, up to 0.3 wt. % V, up to 0.15 wt. % impurities, and Al. In some cases, the aluminum alloys can comprise about 1.0 - 1.3 wt. % Si, 0.1 - 0.25 wt. % Fe, 0.7 - 0.9 wt. % Cu, 0.6 - 0.8 wt. % Mg, 0.01 - 0.05 wt. % Ti, up to 0.2 wt. % Mn, up to 0.2 wt. % Cr, up to 0.2 wt. % Zr, up to 0.2 wt. % V, up to 0.15 wt. % impurities, and Al. Optionally, the aluminum alloy comprises at least one of Mn, Cr, Zr, and V. In some examples, a combined content of Mn, Cr, Zr, and/or V is at least about 0.14 wt. % (e.g., from about 0.14 wt. % to about 0.4 wt. % or from about 0.15 wt. % to about 0.25 wt. %). Optionally, the aluminum alloy comprises about 0.01 - 0.3 wt. % V. In some examples, the aluminum alloy comprises excess Si and the excess Si content is from about 0.01 to about 1.0.

Also described herein are aluminum alloy products comprising the aluminum alloy as described herein. Optionally, the aluminum alloy products comprise a rotated cube crystallographic texture at a volume percent of at least about 5 %. The aluminum alloy products can comprise dispersoids. Optionally, the dispersoids are present in the aluminum alloy in an amount of at least about 1,500,000 dispersoids per mm ² . Optionally, the dispersoids occupy an area ranging from about 0.5 % to about 5 % of the aluminum alloy products. In some cases, the aluminum alloy products comprises Fe-constituents. The Fe-constituents can comprise Al(Fe,X)Si phase particles. Optionally, the average particle size of the Fe-constituents is up to about 4 μπι. The aluminum alloy products can exhibit a yield strength of at least about 300 MPa when in a T6 temper and/or a uniform elongation of at least about 20 % and a minimum bend angle of at least about 120° when in a T4 temper.

Further described herein are methods of producing an aluminum alloy product. The methods comprise casting an aluminum alloy as described herein to provide a cast article, homogenizing the cast article in a two-stage homogenization process, hot rolling and cold rolling the cast article to provide a final gauge aluminum alloy product, solution heat treating the final gauge aluminum alloy product, and pre-aging the final gauge aluminum alloy product. The two-stage homogenization process can comprise heating the cast article to a first stage homogenization temperature and holding the cast article at the first stage homogenization temperature for a period of time and further heating the cast article to a second stage homogenization temperature and holding the cast article at the second stage homogenization temperature for a period of time. Optionally, the first stage homogenization temperature is from about 470 °C to about 530 °C and the second stage homogenization temperature is from about 525 °C to about 575 °C. In some examples, the second stage homogenization temperature is higher than the first stage homogenization temperature.

Further aspects, objects, and advantages will become apparent upon consideration of the detailed description and figures that follow.

BRIEF DESCRIPTION OF THE FIGURES

Figure 1 is a graph showing tensile properties of aluminum alloys according to certain aspects of the present disclosure.

Figure 2 is a micrograph showing the grain structure of aluminum alloys according to certain aspects of the present disclosure.

Figure 3 is a graph showing mechanical properties of aluminum alloys according to certain aspects of the present disclosure.

Figure 4 is a graph showing mechanical properties of aluminum alloys according to certain aspects of the present disclosure.

Figure 5 is a graph showing mechanical properties of aluminum alloys according to certain aspects of the present disclosure.

Figure 6 is a graph showing the distribution of recrystallization textures of aluminum alloys according to certain aspects of the present disclosure.

Figure 7 is a series of micrographs of aluminum alloys according to certain aspects of the present disclosure.

Figure 8 is a graph showing dispersoid number density and dispersoid area fraction of aluminum alloys according to certain aspects of the present disclosure.

Figure 9 is a series of micrographs of aluminum alloys according to certain aspects of the present disclosure.

Figure 10 is a graph showing size distribution of Fe-constituents of aluminum alloys according to certain aspects of the present disclosure.

Figure 11 is a series of micrographs of aluminum alloys according to certain aspects of the present disclosure. DETAILED DESCRIPTION

Described herein are novel aluminum alloys and products and methods of preparing the same. The alloys exhibit high strength and high formability. As further described herein, solute elements, including Cu, Mg, and Si, are combined with transition elements (e.g., Mn, Cr, Zn, and V) for a synergistic effect of increasing both the strength and formability of the alloys. The transition elements aid in preventing precipitate formation along grain boundaries in the aluminum alloys, as further described below. In addition, the processing methods used to prepare the alloys and products contribute to the high strength and formability exhibited by the alloys and products.

Definitions and Descriptions:

The terms "invention," "the invention," "this invention" and "the present invention" used herein are intended to refer broadly to all of the subject matter of this patent application and the claims below. Statements containing these terms should be understood not to limit the subject matter described herein or to limit the meaning or scope of the patent claims below.

In this description, reference is made to alloys identified by aluminum industry designations, such as "series" or "AA6xxx ." For an understanding of the number designation system most commonly used in naming and identifying aluminum and its alloys, see "International Alloy Designations and Chemical Composition Limits for Wrought Aluminum and Wrought Aluminum Alloys" or "Registration Record of Aluminum Association Alloy Designations and Chemical Compositions Limits for Aluminum Alloys in the Form of Castings and Ingot," both published by The Aluminum Association.

As used herein, the meaning of "a," "an," or "the" includes singular and plural references unless the context clearly dictates otherwise.

As used herein, the meaning of "room temperature" can include a temperature of from about 15 °C to about 30 °C, for example about 15 °C, about 16 °C, about 17 °C, about 18 °C, about 19 °C, about 20 °C, about 21 °C, about 22 °C, about 23 °C, about 24 °C, about 25 °C, about 26 °C, about 27 °C, about 28 °C, about 29 °C, or about 30 °C.

As used herein, a plate generally has a thickness of greater than about 15 mm. For example, a plate may refer to an aluminum product having a thickness of greater than 15 mm, greater than 20 mm, greater than 25 mm, greater than 30 mm, greater than 35 mm, greater than 40 mm, greater than 45 mm, greater than 50 mm, or greater than 100 mm.

As used herein, a shate (also referred to as a sheet plate) generally has a thickness of from about 4 mm to about 15 mm. For example, a shate may have a thickness of 4 mm, 5 mm, 6 mm, 7 mm, 8 mm, 9 mm, 10 mm, 11 mm, 12 mm, 13 mm, 14 mm, or 15 mm.

As used herein, a sheet generally refers to an aluminum alloy product having a thickness of less than about 4 mm. For example, a sheet may have a thickness of less than 4 mm, less than 3 mm, less than 2 mm, less than 1 mm, less than 0.5 mm, less than 0.3 mm, or less than 0.1 mm.

As used herein, terms such as "cast metal article," "cast article," "cast aluminum alloy," and the like are interchangeable and refer to a product produced by direct chill casting (including direct chill co-casting) or semi-continuous casting, continuous casting (including, for example, by use of a twin belt caster, a twin roll caster, a block caster, or any other continuous caster), electromagnetic casting, hot top casting, or any other casting method.

Reference is made in this application to alloy condition or temper. For an understanding of the alloy temper descriptions most commonly used, see "American National Standards (ANSI) H35 on Alloy and Temper Designation Systems." An F condition or temper refers to an aluminum alloy as fabricated. An O condition or temper refers to an aluminum alloy after annealing. A TI condition or temper refers to an aluminum alloy cooled from hot working and naturally aged (e.g., at room temperature). A T2 condition or temper refers to an aluminum alloy cooled from hot working, cold worked and naturally aged. A T3 condition or temper refers to an aluminum alloy solution heat treated, cold worked, and naturally aged. A T4 condition or temper refers to an aluminum alloy solution heat treated and naturally aged. A T5 condition or temper refers to an aluminum alloy cooled from hot working and artificially aged (at elevated temperatures). A T6 condition or temper refers to an aluminum alloy solution heat treated and artificially aged. A T7 condition or temper refers to an aluminum alloy solution heat treated and artificially overaged. A T8x condition or temper refers to an aluminum alloy solution heat treated, cold worked, and artificially aged. A T9 condition or temper refers to an aluminum alloy solution heat treated, artificially aged, and cold worked.

The following aluminum alloys are described in terms of their elemental composition in weight percentage (wt. %) based on the total weight of the alloy. In certain examples of each alloy, the remainder is aluminum, with a maximum wt. % of 0.15 % for the sum of the impurities.

Alloy Compositions

Described herein are novel aluminum alloys. The alloys exhibit high strength and high formability. In some cases, the properties of the alloys can be achieved due to the elemental composition of the alloys. The aluminum alloys can be precipitation hardened or precipitation hardenable alloys. Optionally, the aluminum alloys can be aluminum alloys classified as 2xxx series aluminum alloys (e.g., wherein copper is a predominant alloying element), 6xxx series aluminum alloys (e.g., wherein magnesium and silicon are predominant alloying elements), or 7xxx series aluminum alloys (e.g., wherein zinc is a predominant alloying element). In some cases, the aluminum alloys can be modified 2xxx series, 6xxx series, or 7xxx series aluminum alloys. As used herein, the term "modified" as related to a series of aluminum alloys refers to an alloy composition that would typically be classified within a particular series, but the modification of one or more elements (types or amounts) results in a different predominant alloying element. For example, a modified 6xxx series aluminum alloy can refer to an aluminum alloy in which copper and silicon are the predominant alloying elements rather than magnesium and silicon.

In some cases, an aluminum alloy can have the following elemental composition as provided in Table 1 :

Table 1

In other examples, the alloy can have the following elemental composition as provided Table 2.

Table 2

Ti 0.01-0.09

Mn 0.01-0.3

Cr 0.01-0.3

Zr 0.01-0.3

V 0.01-0.3

0 - 0.05 (each)

Others

0-0.15 (total)

Al example, the alloy can have the following elemental composition <

Table 3.

Table 3

Element Weight Percentage (wt. %)

Si 1.0-1.3

Fe 0.1-0.25

Cu 0.7-0.9

Mg 0.6-0.8

Ti 0.01-0.05

Mn 0.05-0.2

Cr 0.05-0.2

Zr 0.05-0.2

V 0.05-0.2

0 - 0.05 (each)

Others

0-0.15 (total)

Al

In certain examples, the alloy described herein includes silicon (Si) in an amount from about 0.8 % to about 1.5 % (e.g., from about 0.9 % to about 1.45 %, from about 0.9 % to about 1.4 %, from about 0.9 % to about 1.35 %, from about 0.9 % to about 1.3 %, from about 0.9 % to about 1.25 %, from about 0.9 % to about 1.2 %, from about 0.95 % to about 1.5 %, from about 0.95 % to about 1.45 %, from about 0.95 % to about 1.4 %, from about 0.95 % to about 1.35 %, from about 0.95 % to about 1.3 %, from about 0.95 % to about 1.25 %, from about 0.95 % to about 1.2 %, from about 1.0 % to about 1.5 %, from about 1.0 % to about 1.45 %, from about 1.0 % to about 1.4 %, from about 1.0 % to about 1.35 %, from about 1.0 % to about 1.3 %, from about 1.0 % to about 1.25 %, or from about 1.0 % to about 1.2 %) based on the total weight of the alloy. For example, the alloy can include 0.8 %, 0.81 %, 0.82 %, 0.83 %, 0.84 %, 0.85 %, 0.86 %, 0.87 %, 0.88 %, 0.89 %, 0.9 %, 0.91 %, 0.92 %, 0.93 %, 0.94 %, 0.95 %, 0.96 %, 0.97 %, 0.98 %, 0.99 %, 1.0 %, 1.01 %, 1.02 %, 1.03 %, 1.04 %, 1.05 %, 1.06 %, 1.07 %, 1.08 %, 1.09 %, 1.1 %, 1.11 %, 1.12 %, 1.13 %, 1.14 %, 1.15 %, 1.16 %, 1.17 %, 1.18 %, 1.19 %, 1.2 %, 1.21 %, 1.22 %, 1.23 %, 1.24 %, 1.25 %, 1.26 %, 1.27 %, 1.28 %, 1.29 %, 1.3 %, 1.31 %, 1.32 %, 1.33 %, 1.34 %, 1.35 %, 1.36 %, 1.37 %, 1.38 %, 1.39 %, 1.4 %, 1.41 %, 1.42 %, 1.43 %, 1.44 %, 1.45 %, 1.46 %, 1.47 %, 1.48 %, 1.49 %, or 1.5 % Si. All expressed in wt. %.

In certain aspects, the alloy described herein includes iron (Fe) in an amount from about 0.1 % to about 0.5 % (e.g., from about 0.1 % to about 0.45 %, from about 0.1 % to about 0.4 %, from about 0.1 % to about 0.35 %, from about 0.1 % to about 0.3 %, from about 0.1 % to about 0.25 %, from about 0.1 % to about 0.2 %, from about 0.15 % to about 0.45 %, from about 0.15 % to about 0.4 %, from about 0.15 % to about 0.35 %, from about 0.15 % to about 0.3 %, from about 0.15 % to about 0.25 %, from about 0.15 % to about 0.2 %, from about 0.2 % to about 0.45 %, from about 0.2 % to about 0.4 %, from about 0.2 % to about 0.35 %, from about 0.2 % to about 0.3 %, from about 0.2 % to about 0.25 %, from about 0.25 % to about 0.45 %, from about 0.25 % to about 0.4 %, from about 0.25 % to about 0.35 %, from about 0.25 % to about 0.3 %, from about 0.3 % to about 0.45 %, from about 0.3 % to about 0.4 %, or from about 0.3 % to about 0.35 %) based on the total weight of the alloy. For example, the alloy can include 0.1 %, 0.11 %, 0.12 %, 0.13 %, 0.14 %, 0.15 %, 0.16 %, 0.17 %, 0.18 %, 0.19 %, 0.2 %, 0.21 %, 0.22 %, 0.23 %, 0.24 %, 0.25 %, 0.26 %, 0.27 %, 0.28 %, 0.29 %, 0.3 %, 0.31 %, 0.32 %, 0.33 %, 0.34 %, 0.35 %, 0.36 %, 0.37 %, 0.38 %, 0.39 %, 0.4 %, 0.41 %, 0.42 %, 0.43 %, 0.44 %, 0.45 %, 0.46 %, 0.47 %, 0.48 %, 0.49 %, or 0.5 % Fe. All expressed in wt. %.

In certain examples, the alloy described herein includes copper (Cu) in an amount from about 0.5 % to about 1.0 % (e.g., from about 0.55 % to about 1.0 %, from about 0.6 % to about 1.0 %, from about 0.65 % to about 1.0 %, from about 0.7 % to about 1.0 %, from about 0.75 % to about 1.0 %, from about 0.8 % to about 1.0 %, from about 0.5 % to about 0.95 %, from about 0.55 % to about 0.95 %, from about 0.6 % to about 0.95 %, from about 0.65 % to about 0.95 %, from about 0.7 % to about 0.95 %, from about 0.75 % to about 0.95 %, from about 0.8 % to about 0.95 %, from about 0.5 % to about 0.9 %, from about 0.55 % to about 0.9 %, from about 0.6 % to about 0.9 %, from about 0.65 % to about 0.9 %, from about 0.7 % to about 0.9 %, from about 0.75 % to about 0.9 %, from about 0.8 % to about 0.9 %, from about 0.5 % to about 0.85 %, from about 0.55 % to about 0.85 %, from about 0.6 % to about 0.85 %, from about 0.65 % to about 0.85 %, from about 0.7 % to about 0.85 %, from about 0.75 % to about 0.85 %, from about 0.8 % to about 0.85 %, from about 0.5 % to about 0.8 %, from about 0.55 % to about 0.8 %, from about 0.6 % to about 0.8 %, from about 0.65 % to about 0.8 %, from about 0.7 % to about 0.8 %, or from about 0.75 % to about 0.8 %) based on the total weight of the alloy. For example, the alloy can include 0.5 %, 0.51 %, 0.52 %, 0.53 %, 0.54 %, 0.55 %, 0.56 %, 0.57 %, 0.58 %, 0.59 %, 0.6 %, 0.61 %, 0.62 %, 0.63 %, 0.64 %, 0.65 %, 0.66 %, 0.67 %, 0.68 %, 0.69 %, 0.7 %, 0.71 %, 0.72 %, 0.73 %, 0.74 %, 0.75 %, 0.76 %, 0.77 %, 0.78 %, 0.79 %, 0.8 %, 0.81 %, 0.82 %, 0.83 %, 0.84 %, 0.85 %, 0.86 %, 0.87 %, 0.88 %, 0.89 %, 0.9 %, 0.91 %, 0.92 %, 0.93 %, 0.94 %, 0.95 %, 0.96 %, 0.97 %, 0.98 %, 0.99 %, or 1.0 % Cu. All expressed in wt. %.

In certain examples, the alloy described herein includes magnesium (Mg) in an amount from about 0.5 % to about 0.9 % (e.g., from about 0.55 % to about 0.9 %, from about 0.6 % to about 0.9 %, from about 0.65 % to about 0.9 %, from about 0.7 % to about 0.9 %, from about 0.75 % to about 0.9 %, from about 0.8 % to about 0.9 %, from about 0.5 % to about 0.85 %, from about 0.55 % to about 0.85 %, from about 0.6 % to about 0.85 %, from about 0.65 % to about 0.85 %, from about 0.7 % to about 0.85 %, from about 0.75 % to about 0.85 %, from about 0.8 % to about 0.85 %, from about 0.5 % to about 0.8 %, from about 0.55 % to about 0.8 %, from about 0.6 % to about 0.8 %, from about 0.65 % to about 0.8 %, from about 0.7 % to about 0.8 %, or from about 0.75 % to about 0.8 %) based on the total weight of the alloy. For example, the alloy can include 0.5 %, 0.51 %, 0.52 %, 0.53 %, 0.54 %, 0.55 %, 0.56 %, 0.57 %, 0.58 %, 0.59 %, 0.6 %, 0.61 %, 0.62 %, 0.63 %, 0.64 %, 0.65 %, 0.66 %, 0.67 %, 0.68 %, 0.69 %, 0.7 %, 0.71 %, 0.72 %, 0.73 %, 0.74 %, 0.75 %, 0.76 %, 0.77 %, 0.78 %, 0.79 %, 0.8 %, 0.81 %, 0.82 %, 0.83 %, 0.84 %, 0.85 %, 0.86 %, 0.87 %, 0.88 %, 0.89 %, or 0.9 % Mg. All expressed in wt. %.

In certain aspects, the alloy described herein includes titanium (Ti) in an amount up to about 0.1 % (e.g., from about 0.01 % to about 0.09 %, from about 0.02 % to about 0.09 %, from about 0.03 % to about 0.09 %, from about 0.04 % to about 0.09 %, from about 0.05 % to about 0.09 %, from about 0.01 % to about 0.08 %, from about 0.02 % to about 0.08 %, from about 0.03 % to about 0.08 %, from about 0.04 % to about 0.08 %, from about 0.05 % to about 0.08 %, from about 0.01 % to about 0.07 %, from about 0.02 % to about 0.07 %, from about 0.03 % to about 0.07 %, from about 0.04 % to about 0.07 %, from about 0.05 % to about 0.07 %, from about 0.01 % to about 0.06 %, from about 0.02 % to about 0.06 %, from about 0.03 % to about 0.06 %, from about 0.04 % to about 0.06 %, from about 0.05 % to about 0.06 %, from about 0.01 % to about 0.05 %, from about 0.02 % to about 0.05 %, from about 0.03 % to about 0.05 %, or from about 0.04 % to about 0.05 %) based on the total weight of the alloy. For example, the alloy can include 0.01 %, 0.02 %, 0.03 %, 0.04 %, 0.05 %, 0.06 %, 0.07 %, 0.08 %, 0.09 %, or 0.1 % Ti. In some examples, Ti is not present in the alloy (i.e., 0 % Ti). All expressed in wt. %.

In certain examples, the alloy described herein includes manganese (Mn) in an amount up to about 0.5 % (e.g., from about 0.01 % to about 0.5 %, from about 0.01 % to about 0.4 %, from about 0.01 % to about 0.3 %, from about 0.01 % to about 0.2 %, from about 0.01 % to about 0.1 %, from about 0.06 % to about 0.5 %, from about 0.06 % to about 0.4 %, from about 0.06 % to about 0.3 %, from about 0.06 % to about 0.2 %, from about 0.06 % to about 0.1 %, from about 0.1 % to about 0.5 %, from about 0.1 % to about 0.4 %, from about 0.1 % to about 0.3 %, or from about 0.1 % to about 0.2 %) based on the total weight of the alloy. For example, the alloy can include 0.01 %, 0.02 %, 0.03 %, 0.04 %, 0.05 %, 0.06 %, 0.07 %, 0.08 %, 0.09 %, 0.1 %, 0.11 %, 0.12 %, 0.13 %, 0.14 %, 0.15 %, 0.16 %, 0.17 %, 0.18 %, 0.19 %, 0.2 %, 0.21 %, 0.22 %, 0.23 %, 0.24 %, 0.25 %, 0.26 %, 0.27 %, 0.28 %, 0.29 %, 0.3 %, 0.31 %, 0.32 %, 0.33 %, 0.34 %, 0.35 %, 0.36 %, 0.37 %, 0.38 %, 0.39 %, 0.4 %, 0.41 %, 0.42 %, 0.43 %, 0.44 %, 0.45 %, 0.46 %, 0.47 %, 0.48 %, 0.49 %, or 0.5 % Mn. In some examples, Mn is not present in the alloy (i.e., 0 % Mn). All expressed in wt. %.

In certain aspects, the alloy described herein includes chromium (Cr) in an amount up to about 0.5 % (e.g., from about 0.01 % to about 0.5 %, from about 0.01 % to about 0.4 %, from about 0.01 % to about 0.3 %, from about 0.01 % to about 0.2 %, from about 0.01 % to about 0.1 %, from about 0.06 % to about 0.5 %, from about 0.06 % to about 0.4 %, from about 0.06 % to about 0.3 %, from about 0.06 % to about 0.2 %, from about 0.06 % to about 0.1 %, from about 0.1 % to about 0.5 %, from about 0.1 % to about 0.4 %, from about 0.1 % to about 0.3 %, or from about 0.1 % to about 0.2 %) based on the total weight of the alloy. For example, the alloy can include 0.01 %, 0.02 %, 0.03 %, 0.04 %, 0.05 %, 0.06 %, 0.07 %, 0.08 %, 0.09 %, 0.1 %, 0.11 %, 0.12 %, 0.13 %, 0.14 %, 0.15 %, 0.16 %, 0.17 %, 0.18 %, 0.19 %, 0.2 %, 0.21 %, 0.22 %, 0.23 %, 0.24 %, 0.25 %, 0.26 %, 0.27 %, 0.28 %, 0.29 %, 0.3 %, 0.31 %, 0.32 %, 0.33 %, 0.34 %, 0.35 %, 0.36 %, 0.37 %, 0.38 %, 0.39 %, 0.4 %, 0.41 %, 0.42 %, 0.43 %, 0.44 %, 0.45 %, 0.46 %, 0.47 %, 0.48 %, 0.49 %, or 0.5 % Cr. In some examples, Cr is not present in the alloy (i.e., 0 % Cr). All expressed in wt. %. In certain aspects, the alloy described herein includes zirconium (Zr) in an amount up to about 0.5 % (e.g., from about 0.01 % to about 0.5 %, from about 0.01 % to about 0.4 %, from about 0.01 % to about 0.3 %, from about 0.01 % to about 0.2 %, from about 0.01 % to about 0.1 %, from about 0.06 % to about 0.5 %, from about 0.06 % to about 0.4 %, from about 0.06 % to about 0.3 %, from about 0.06 % to about 0.2 %, from about 0.06 % to about 0.1 %, from about 0.1 % to about 0.5 %, from about 0.1 % to about 0.4 %, from about 0.1 % to about 0.3 %, or from about 0.1 % to about 0.2 %) based on the total weight of the alloy. For example, the alloy can include 0.01 %, 0.02 %, 0.03 %, 0.04 %, 0.05 %, 0.06 %, 0.07 %, 0.08 %, 0.09 %, 0.1 %, 0.11 %, 0.12 %, 0.13 %, 0.14 %, 0.15 %, 0.16 %, 0.17 %, 0.18 %, 0.19 %, 0.2 %, 0.21 %, 0.22 %, 0.23 %, 0.24 %, 0.25 %, 0.26 %, 0.27 %, 0.28 %, 0.29 %, 0.3 %, 0.31 %, 0.32 %, 0.33 %, 0.34 %, 0.35 %, 0.36 %, 0.37 %, 0.38 %, 0.39 %, 0.4 %, 0.41 %, 0.42 %, 0.43 %, 0.44 %, 0.45 %, 0.46 %, 0.47 %, 0.48 %, 0.49 %, or 0.5 % Zr. In certain aspects, Zr is not present in the alloy (i.e., 0 %). All expressed in wt. %.

In certain aspects, the alloy described herein includes vanadium (V) in an amount up to about 0.5 % (e.g., from about 0.01 % to about 0.5 %, from about 0.01 % to about 0.4 %, from about 0.01 % to about 0.3 %, from about 0.01 % to about 0.2 %, from about 0.01 % to about 0.1 %, from about 0.06 % to about 0.5 %, from about 0.06 % to about 0.4 %, from about 0.06 % to about 0.3 %, from about 0.06 % to about 0.2 %, from about 0.06 % to about 0.1 %, from about 0.1 % to about 0.5 %, from about 0.1 % to about 0.4 %, from about 0.1 % to about 0.3 %, or from about 0.1 % to about 0.2 %) based on the total weight of the alloy. For example, the alloy can include 0.01 %, 0.02 %, 0.03 %, 0.04 %, 0.05 %, 0.06 %, 0.07 %, 0.08 %, 0.09 %, 0.1 %, 0.11 %, 0.12 %, 0.13 %, 0.14 %, 0.15 %, 0.16 %, 0.17 %, 0.18 %, 0.19 %, 0.2 %, 0.21 %, 0.22 %, 0.23 %, 0.24 %, 0.25 %, 0.26 %, 0.27 %, 0.28 %, 0.29 %, 0.3 %, 0.31 %, 0.32 %, 0.33 %, 0.34 %, 0.35 %, 0.36 %, 0.37 %, 0.38 %, 0.39 %, 0.4 %, 0.41 %, 0.42 %, 0.43 %, 0.44 %, 0.45 %, 0.46 %, 0.47 %, 0.48 %, 0.49 %, or 0.5 % V. In certain aspects, V is not present in the alloy (i.e., 0 % V). All expressed in wt. %.

Optionally, the alloy compositions can further include other minor elements, sometimes referred to as impurities, in amounts of about 0.05 % or below, 0.04 % or below, 0.03 % or below, 0.02 % or below, or 0.01 % or below each. These impurities may include, but are not limited to, Ni, Sc, Sn, Ga, Ca, Hf, Sr, or combinations thereof. Accordingly, Ni, Sc, Sn, Ga, Ca, Hf, or Sr may be present in an alloy in amounts of 0.05 % or below, 0.04 % or below, 0.03 % or below, 0.02 % or below, or 0.01 % or below. In certain aspects, the sum of all impurities does not exceed 0.15 % (e.g., 0.1 %). All expressed in wt. %. The alloy composition also includes aluminum. In certain aspects, the remaining percentage of the alloy is aluminum.

One non-limiting example of a suitable alloy includes 1.20 % Si, 0.18 % Fe, 0.80 % Cu, 0.70 % Mg, 0.02 % Ti, 0.13 % Mn, 0.07 % Cr, and up to 0.15 % total impurities, with the remainder Al. In some cases, another non-limiting example of a suitable alloy includes 1.20 % Si, 0.18 % Fe, 0.80 % Cu, 0.70 % Mg, 0.02 % Ti, 0.14 % Cr, and up to 0.15 % total impurities, with the remainder Al. In some cases, another non-limiting example of a suitable alloy includes 1.20 % Si, 0.18 % Fe, 0.80 % Cu, 0.70 % Mg, 0.02 % Ti, 0.07 % Cr, 0.11 % Zr, and up to 0.15 % total impurities, with the remainder Al. In some cases, another non-limiting example of a suitable alloy includes 1.20 % Si, 0.18 % Fe, 0.80 % Cu, 0.70 % Mg, 0.02 % Ti, 0.08 % Cr, 0.11 % V, and up to 0.15 % total impurities, with the remainder Al. In some cases, another non-limiting example of a suitable alloy includes 1.20 % Si, 0.18 % Fe, 0.80 % Cu, 0.70 % Mg, 0.02 % Ti, 0.09 % Zr, 0.10 % V, and up to 0.15 % total impurities, with the remainder Al. In some cases, another non-limiting example of a suitable alloy includes 1.20 % Si, 0.18 % Fe, 0.80 % Cu, 0.70 % Mg, 0.02 % Ti, 0.09 % Mn, 0.10 % V, and up to 0.15 % total impurities, with the remainder Al.

Alloy Microstructure and Properties

In certain aspects, the Si, Mg, and Cu content and ratios are controlled to enhance strength and formability. Optionally, the transition element (e.g., Mn, Cr, Zr, and/or V) content is controlled to enhance strength and formability.

In some cases, the alloy described herein includes excess Si. Optionally, the Si and Mg content are controlled such that excess Si is present in the alloy as described herein. Excess Si content can be calculated according to the method described in U.S. Patent No. 4,614,552, col. 4, lines 49-52, which is incorporated herein by reference. Briefly, Mg and Si combine as Mg ₂ Si, imparting a considerable strength improvement after age-hardening. In addition, Si-containing constituents, such as Al(FeMn)Si, can form. Excess Si is present when the Si content is above the stoichiometric ratio of Mg ₂ Si and above the amount included in Al(FeMn)Si constituents. The excess Si content can be calculated by subtracting from the total Si content the Si needed for Mg ₂ Si (Mg/1.73) and the Fe-containing phase (Fe/3). The excess Si content can be 1.0 or less (e.g., from about 0.01 to about 1.0, from about 0.1 to about 0.9, or from about 0.5 to 0.8). For example, the excess Si content can be 0.01, 0.02, 0.03, 0.04, 0.05, 0.06, 0.07, 0.08, 0.09, 0.10, 0.15, 0.20, 0.25, 0.30, 0.35, 0.40, 0.45, 0.50, 0.55, 0.60, 0.65, 0.70, 0.75, 0.80, 0.85, 0.90, 0.95, 1.0, or anywhere in between. In some aspects, the alloys described herein include at least one transition element (e.g., at least one of Mn, Cr, Zr, and/or V). Optionally, the combined content of the transition elements in the alloys described herein is at least about 0.14 wt. %. For example, the combined content of Mn, Cr, Zr, and/or V can be from about 0.14 wt. % to about 0.40 wt. % (e.g., from about 0.15 wt. % to about 0.35 wt. % or from about 0.25 wt. % to about 0.30 wt. %). In some cases, the combined content of Mn, Cr, Zr, and/or V is about 0.14 %, 0.15 %, 0.16 %, 0.17 %, 0.18 %, 0.19 %, 0.2 %, 0.21 %, 0.22 %, 0.23 %, 0.24 %, 0.25 %, 0.26 %, 0.27 %, 0.28 %, 0.29 %, 0.3 %, 0.31 %, 0.32 %, 0.33 %, 0.34 %, 0.35 %, 0.36 %, 0.37 %, 0.38 %, 0.39 %, or 0.4 %. In some cases, one or more of the transition elements may not be present, as long as the total weight percentage of the present transition elements is at least 0.14 wt. %.

The presence of one or more of the transition elements, such as Mn, Cr, Zr, and/or V, can advantageously form dispersoids during the processing methods described herein, such as during the homogenization step. The dispersoids can function as heterogeneous nucleation sites for precipitates during processing steps, such as during the solution heat treatment step. In certain aspects, grain boundary (GB) precipitation occurs due to GB misorientation that is favorable for precipitate nucleation. The dispersoids reduce or eliminate GB precipitates and also reduce strain localization, thus diffusing strain distribution during deformation. The reduced or eliminated GB precipitates and/or the diffused strain distribution during deformation result in an improved bendability of the resulting alloys and alloy products.

In some non-limiting examples, the dispersoids described herein can contain Al and one or more of the alloying elements found in the alloy composition as described above. In some examples, the dispersoids can have a composition according to one or more of the following formulae: A1X, A1XX, AlXSi, Al(Fe,X), Al(Fe,X)Si, or the like, wherein each X is selected from the group consisting of Fe, Si, Mn, Cr, V, or Zr.

The dispersoid average size and distribution are important factors that result in the desirable strength and formability properties displayed by the alloys and alloy products described herein. The size and distribution are influenced by the presence of transition elements, as described above, and also by the methods of processing the alloys, as further described below. In some examples, the dispersoids can be present in the aluminum alloy in an average amount of at least about 1,500,000 dispersoids per square millimeter (mm ² ). For example, the dispersoids can be present in an amount of at least about 1,600,000 dispersoids per mm ² , at least about 1,700,000 dispersoids per mm ² , at least about 1,800,000 dispersoids per mm ² , at least about 1,900,000 dispersoids per mm ² , at least about 2,000,000 dispersoids per mm ² , at least about 2,100,000 dispersoids per mm ² , at least about 2,200,000 dispersoids per mm ² , at least about 2,300,000 dispersoids per mm ² , at least about 2,400,000 dispersoids per mm ² , at least about 2,500,000 dispersoids per mm ² , at least about 2,600,000 dispersoids per mm ² , at least about 2,700,000 dispersoids per mm ² , at least about 2,800,000 dispersoids per mm ² , at least about 2,900,000 dispersoids per mm ² , or at least about 3,000,000 dispersoids per mm ² . In some examples, the average number of dispersoids present in the aluminum alloy can be from about 1,500,000 dispersoids per mm ² to about 5,000,000 dispersoids per mm ² (e.g., from about 1,750,000 dispersoids per mm ² to about 4,750,000 dispersoids per mm ² or from about 2,000,000 dispersoids per mm ² to about 4,500,000 dispersoids per mm ² ). The dispersoids in the aluminum alloy can occupy an area ranging from about 0.5 % to about 5 % of the alloy (e.g., from about 1 % to about 4 % or from about 1.5 % to about 2.5 % of the alloy).

Optionally, the dispersoids can have an average diameter of from about 10 nm to about 600 nm (e.g., from about 50 nm to about 500 nm, from about 100 nm to about 450 nm, from about 200 nm to about 400 nm, from about 10 nm to about 200 nm, or from about 500 nm to about 600 nm). For example, the dispersoids can have a diameter of about 10 nm, 20 nm, 30 nm, 40 nm, 50 nm, 60 nm, 70 nm, 80 nm, 90 nm, 100 nm, 110 nm, 120 nm, 130 nm, 140 nm, 150 nm, 160 nm, 170 nm, 180 nm, 190 nm, 200 nm, 210 nm, 220 nm, 230 nm, 240 nm, 250 nm, 260 nm, 270 nm, 280 nm, 290 nm, 300 nm, 310 nm, 320 nm, 330 nm, 340 nm, 350 nm, 360 nm, 370 nm, 380 nm, 390 nm, 400 nm, 410 nm, 420 nm, 430 nm, 440 nm, 450 nm, 460 nm, 470 nm, 480 nm, 490 nm, 500 nm, 510 nm, 520 nm, 530 nm, 540 nm, 550 nm, 560 nm, 570 nm, 580 nm, 590 nm, 600 nm, or anywhere in between.

The alloys described herein also include Fe-constituents, which are also referred to herein as Fe-containing particles. Optionally, in addition to Fe, the Fe-constituents can include one or more of Al, Mn, Si, Cu, Ti, Zr, Cr, and/or Mg. In some examples, the Fe-constituents can be Al(Fe,X)Si phase particles, wherein X can be Mn, Cr, Zr, and/or V, and/or AlFeSi phase particles. For example, the Fe-constituents can include one or more of Al ₃ Fe, Al _x (Fe,Mn), Al ₃ Fe, Ali ₂ CFe,Mn) ₃ Si, Al ₇ Cu ₂ Fe, Al(Fe,Mn) ₂ Si ₃ , Al _x (Mn,Fe), and Ah ₂ ( 7,Fe) ₃ Si. The presence of the transition elements described herein results in the transformation of AlFeSi particles into Al(Fe,X)Si particles. In some examples, the number of Al(Fe,X)Si phase particles, which are spheroid particles, is greater than the number of AlFeSi phase particles, which are flake or needle type particles. Optionally, at least 50 % of the Fe-constituents are present as Al(Fe,X)Si particles (e.g., at least 55 %, at least 60 %, at least 65 %, at least 70 %, at least 75 %, at least 80 %, at least 85 %, at least 90 %, or at least 95 % of the Fe-constituents are present as Al(Fe,X)Si particles). The Fe-constituents can have an average particle size of up to about 4 μιη. For example, the Fe-constituents, on average, can range in size from about 0.1 μιη to about 4 μιη (e.g., from about 0.5 μιη to about 3.5 μιη or from about 1 μιη to about 3 μιη).

Optionally, the Cr, Mn, Zr, and/or V content and ratios are controlled to form the desired size, type, and distribution of dispersoids, which leads to improved formability and strength. In some non-limiting examples, a ratio of Cr to Mn (also referred to herein as the Cr/Mn ratio) can be from about 0.15:1 to about 0.7:1 (e.g., from about 0.3:1 to about 0.6:1 or from about 0.4:1 to about 0.55:1). For example, the Cr/Mn ratio can be about 0.15:1, 0.16:1, 0.17:1, 0.18:1, 0.19:1, 0.20:1, 0.21:1, 0.22:1, 0.23:1, 0.24:1, 0.25:1, 0.26:1, 0.27:1, 0.28:1, 0.29:1, 0.30:1, 0.31:1, 0.32:1, 0.33:1, 0.34:1, 0.35:1, 0.36:1, 0.37:1, 0.38:1, 0.39:1, 0.40:1, 0.41:1, 0.42:1, 0.43:1, 0.44:1, 0.45:1, 0.46:1, 0.47:1, 0.48:1, 0.49:1, 0.50:1, 0.51:1, 0.52:1, 0.53:1, 0.54:1, 0.55:1, 0.56:1, 0.57:1, 0.58:1, 0.59:1, 0.60:1, 0.61:1, 0.62:1, 0.63:1, 0.64:1, 0.65:1, 0.66:1, 0.67:1, 0.68:1, 0.69:1, or0.70:l.

In some non-limiting examples, a ratio of Cr to V (also referred to herein as the Cr/V ratio) can be from about 0.5:1 to about 1.5:1 (e.g., from about 0.6:1 to about 1.4:1 or from about 0.7:1 to about 1.3:1). For example, the Cr/V ratio can be about 0.50:1, 0.51:1, 0.52:1, 0.53:1, 0.54:1, 0.55:1, 0.56:1, 0.57:1, 0.58:1, 0.59:1, 0.60:1, 0.61:1, 0.62:1, 0.63:1, 0.64:1, 0.65:1, 0.66:1, 0.67:1, 0.68:1, 0.69:1, 0.70:1, 0.71:1, 0.72:1, 0.73:1, 0.74:1, 0.75:1, 0.76:1, 0.77:1, 0.78:1, 0.79:1, 0.80:1, 0.81:1, 0.82:1, 0.83:1, 0.84:1, 0.85:1, 0.86:1, 0.87:1, 0.88:1, 0.89:1, 0.90:1, 0.91:1, 0.92:1, 0.93:1, 0.94:1, 0.95:1, 0.96:1, 0.97:1, 0.98:1, 0.99:1, 1.0:1, 1.1:1, 1.2:1, 1.3:1, 1.4:1, or 1.5:1.

In some non-limiting examples, a ratio of Cr to Zr (also referred to herein as the Cr/Zr ratio) can be from about 0.5:1 to about 1.5:1 (e.g., from about 0.6:1 to about 1.4:1 or from about 0.7:1 to about 1.3:1). For example, the Cr/Zr ratio can be about 0.50:1, 0.51:1, 0.52:1, 0.53:1, 0.54:1, 0.55:1, 0.56:1, 0.57:1, 0.58:1, 0.59:1, 0.60:1, 0.61:1, 0.62:1, 0.63:1, 0.64:1, 0.65:1, 0.66:1, 0.67:1, 0.68:1, 0.69:1, 0.70:1, 0.71:1, 0.72:1, 0.73:1, 0.74:1, 0.75:1, 0.76:1, 0.77:1, 0.78:1, 0.79:1, 0.80:1, 0.81:1, 0.82:1, 0.83:1, 0.84:1, 0.85:1, 0.86:1, 0.87:1, 0.88:1, 0.89:1, 0.90:1, 0.91:1, 0.92:1, 0.93:1, 0.94:1, 0.95:1, 0.96:1, 0.97:1, 0.98:1, 0.99:1, 1.0:1, 1.1:1, 1.2:1, 1.3:1, 1.4:1, or 1.5:1.

In some non-limiting examples, a ratio of V to Mn (also referred to herein as the V/Mn ratio) can be from about 0.8:1 to about 1.4: 1 (e.g., from about 0.9: 1 to about 1.3 : 1 or from about 0.9:1 to about 1.2:1). For example, the V/Mn ratio can be about 0.80:1, 0.81:1, 0.82:1, 0.83:1, 0.84:1, 0.85:1, 0.86:1, 0.87:1, 0.88:1, 0.89:1, 0.90:1, 0.91:1, 0.92:1, 0.93:1, 0.94:1, 0.95:1,

0.96:1, 0.97:1, 0.98:1, 0.99:1, 1.0:1, 1.1:1, 1.2:1, 1.3:1, or 1.4:1.

In some non-limiting examples, a ratio of V to Zr (also referred to herein as the V/Zr ratio) can be from about 0.8: 1 to about 1.4: 1 (e.g., from about 0.9: 1 to about 1.3 : 1 or from about 0.9:1 to about 1.2:1). For example, the V/Zr ratio can be about 0.80:1, 0.81:1, 0.82:1, 0.83:1,

0.84:1, 0.85:1, 0.86:1, 0.87:1, 0.88:1, 0.89:1, 0.90:1, 0.91:1, 0.92:1, 0.93:1, 0.94:1, 0.95:1,

0.96:1, 0.97:1, 0.98:1, 0.99:1, 1.0:1, 1.1:1, 1.2:1, 1.3:1, or 1.4:1.

In some non-limiting examples, a ratio of V to Cr (also referred to herein as the V/Cr ratio) can be from about 0.8:1 to about 1.4: 1 (e.g., from about 0.9: 1 to about 1.3 : 1 or from about 0.9:1 to about 1.2:1). For example, the V/Cr ratio can be about 0.80:1, 0.81:1, 0.82:1, 0.83:1,

0.84:1, 0.85:1, 0.86:1, 0.87:1, 0.88:1, 0.89:1, 0.90:1, 0.91:1, 0.92:1, 0.93:1, 0.94:1, 0.95:1,

0.96:1, 0.97:1, 0.98:1, 0.99:1, 1.0:1, 1.1:1, 1.2:1, 1.3:1, or 1.4:1.

The mechanical properties of the aluminum alloy can be controlled by various aging conditions depending on the desired use. As one example, the alloy can be produced (or provided) in a T4 temper or a T6 temper. In some non-limiting examples, the proposed alloy has very high formability and bendability in the T4 temper and very high strength in the T6 temper. In certain aspects, the aluminum alloy may have a T4 yield strength ranging from about

150 MPa to about 250 MPa (e.g., about 150 MPa, about 160 MPa, about 170 MPa, about 180

MPa, about 190 MPa, about 200 MPa, about 210 MPa, about 220 MPa, about 230 MPa, about 240 MPa, or about 250 MPa). In some cases, the yield strength is from about 185 MPa to about

195 MPa.

In certain aspects, the alloy in the T4 temper provides a uniform elongation of at least about 20 % (e.g., from about 20% to about 30% or from about 22 % to about 26%). For example, the uniform elongation can be about 20 %, about 21 %, about 22 %, about 23 %, about 24 %, about 25 %, about 26 %, about 27 %, about 28 %, about 29 %, or about 30 %. Optionally, the uniform elongation is measured in the longitudinal (L) direction.

Optionally, the alloy in the T4 temper provides a bend angle, as tested according to VDA 238-100, of at least 120°. For example, the bend angle can be from about 120° to about 140° (e.g., 120°, 121°, 122°, 123°, 124°, 125°, 126°, 127^128^129°, 130°, 131°, 132°, 133°, 134°, 135°, 136°, 137^138^ 139°, or 140°). In some non-limiting examples, including V can improve the formability of the alloys. For example, alloys that include V exhibit an increase in bend angle of up to 10° (e.g., showing an improvement of at least about 5°, at least about 6°, at least about 7°, at least about 8°, at least about 9°, at least about 10°, or anywhere in between) as compared to alloys that do not contain V.

In certain aspects, the aluminum alloy may have a T6 yield strength of at least about 200 MPa. In non-limiting examples, the yield strength is at least about 200 MPa, at least about 210 MPa, at least about 220 MPa, at least about 230 MPa, at least about 240 MPa, at least about 250 MPa, at least about 260 MPa, at least about 270 MPa, at least about 280 MPa, at least about 290 MPa, or at least about 300 MPa, at least about 310 MPa, at least about 320 MPa, at least about 330 MPa, at least about 340 MPa, at least about 350 MPa, at least about 360 MPa, at least about 370 MPa, or at least about 375 MPa. In some cases, the yield strength is from about 200 MPa to about 400 MPa (e.g., about 200 MPa, about 210 MPa, about 220 MPa, about 230 MPa, about 240 MPa, about 250 MPa, about 260 MPa, about 270 MPa, about 280 MPa, about 290 MPa, about 300 MPa, about 310 MPa, about 320 MPa, about 330 MPa, about 340 MPa, about 350 MPa, about 360 MPa, about 370 MPa, or about 375 MPa).

In certain aspects, the alloy in the T6 temper provides a uniform elongation of at least about 5 % (e.g., from about 5 % to about 10 % or from about 6 % to about 9 %). For example, the uniform elongation can be about 5 %, about 6 %, about 7 %, about 8 %, about 9 %, or about 10 %. Optionally, the uniform elongation is measured in the longitudinal (L) direction.

The alloy products also include recrystallization texture components at a surface of the alloy products. For example, the alloy products include one or more of the following recrystallization texture components: cube, goss, brass, S, Cu, and rotated cube (referred to as "RC"). Optionally, at least about 5 volume % of the rotated cube texture component is present in the alloy product (e.g., from about 5 vol. % to about 20 vol. %, from about 6 vol. % to about 18 vol. %, from about 8 vol. % to about 15 vol. %, from about 10 vol. % to about 13 vol. %, or from about 5 vol. % to about 6 vol. %). Such a rotated cube texture component can result in desirable bending in the alloy product.

Methods of Preparing the Aluminum Alloys

Without intending to limit the invention, aluminum alloy properties are partially determined by the formation of microstructures during the alloy's preparation. In certain aspects, the method of preparation for an alloy composition may influence or even determine whether the alloy will have properties adequate for a desired application.

Casting

The alloy described herein can be cast into a cast article using any suitable casting method. For example, the casting process can include a direct chill (DC) casting process. Optionally, the casting process can include a continuous casting (CC) process. The cast article can then be subjected to further processing steps. For example, the processing methods as described herein can include the steps of homogenizing, hot rolling, cold rolling, and solutionizing. In some cases, the processing methods can also include a pre-aging step and/or an artificial aging step.

Homogenization

The homogenization step can include a two-stage heating process. In a first stage of the homogenization process, a cast article prepared from an alloy composition described herein can be heated to a first stage homogenization temperature (e.g., the dispersoid nucleation temperature). The first stage homogenization temperature can be from about 470 °C to about 530 °C (e.g., about 470 °C, about 480 °C, about 490 °C, about 500 °C, about 510 °C, about 520 °C, about 530 °C, or anywhere in between). In some cases, a heating rate to the first stage homogenization temperature can be about 100 °C/hour or less, about 75 °C/hour or less, about 50 °C/hour or less, about 40 °C/hour or less, about 30 °C/hour or less, about 25 °C/hour or less, about 20 °C/hour or less, or about 15 °C/hour or less. In other cases, the heating rate to the first stage homogenization temperature can be from about 10 °C/min to about 100 °C/min (e.g., from about 15 °C/min to about 90 °C/min, from about 20 °C/min to about 80 °C/min, from about 30 °C/min to about 80 °C/min, from about 40 °C/min to about 70 °C/min, or from about 45 °C/min to about 65 °C/min).

The cast article is then allowed to soak (i.e., held at the indicated temperature) for a period of time. According to one non-limiting example, the cast article is allowed to soak for up to about 6 hours (e.g., from about 30 minutes to about 6 hours, inclusively). For example, the cast article can be soaked at a temperature of from about 470 °C to about 530 °C for 30 minutes, 1 hour, 2 hours, 3 hours, 4 hours, 5 hours, 6 hours, or anywhere in between.

In the second stage of the homogenization process, the temperature of the cast article is increased to a temperature higher than the temperature used for the first stage of the homogenization process. The cast article temperature can be increased, for example, to a temperature at least 5 °C higher than the aluminum alloy cast article temperature during the first stage of the homogenization process. For example, the cast article can be further heated to a second stage homogenization temperature (e.g., a dispersoid coarsening temperature) of from about 525 °C to about 575 °C (e.g., from about 530 °C to about 570 °C or from about 535 °C to about 565 °C). In some examples, the second stage homogenization temperature can be about 525 °C, about 530 °C, about 535 °C, about 540 °C, about 545 °C, about 550 °C, about 555 °C, about 560 °C, about 565 °C, about 570 °C, about 575 °C, or anywhere in between) in a second homogenization step. In some cases, a heating rate to the second stage homogenization temperature can be about 50 °C/hour or less, 30 °C/hour or less, or 25 °C/hour or less.

The cast article is then allowed to soak for a period of time during the second stage. According to one non-limiting example, the cast article is allowed to soak for up to about 5 hours (e.g., from about 20 minutes to about 5 hours, inclusively). For example, the cast article can be soaked at a temperature of from about 525 °C to about 575 °C for about 15 minutes, about 20 minutes, about 30 minutes, about 45 minutes, about 1 hour, about 1.5 hours, about 2 hours, about 3 hours, about 4 hours, about 5 hours, or anywhere in between. Hot Rolling

Following the homogenization step, a hot rolling step can be performed. In certain cases, the cast articles are laid down and hot-rolled with an entry temperature range of about 500 °C to 560 °C (e.g., from about 510 °C to about 550 °C or from about 520 °C to about 540 °C). The entry temperature can be, for example, about 505 °C, 510 °C, 515 °C, 520 °C, 525 °C, 530 °C, 535 °C, 540 °C, 545 °C, 550 °C, 555 °C, 560 °C, or anywhere in between. In certain cases, the hot roll exit temperature can range from about 250 °C to about 380 °C (e.g., from about 275 °C to about 370 °C or from about 300 °C to about 360 °C). For example, the hot roll exit temperature can be about 255 °C, 260 °C, 265 °C, 270 °C, 275 °C, 280 °C, 285 °C, 290 °C, 295 °C, 300 °C, 305 °C, 310 °C, 315 °C, 320 °C, 325 °C, 330 °C, 335 °C, 340 °C, 345 °C, 350 °C, 355 °C, 360 °C, 365 °C, 370 °C, 375 °C, or 380 °C.

In certain cases, the cast article is hot rolled to an about 4 mm to about 15 mm gauge (e.g., from about 5 mm to about 12 mm gauge), which is referred to as a hot band. For example, the cast article can be hot rolled to a 15 mm gauge, a 14 mm gauge, a 13 mm gauge, a 12 mm gauge, an 11 mm gauge, a 10 mm gauge, a 9 mm gauge, an 8 mm gauge, a 7 mm gauge, a 6 mm gauge, a 5 mm gauge, or a 4 mm gauge. The temper of the as-rolled hot band is referred to as F-temper.

Cold Rolling

A cold rolling step can optionally be performed before the solutionizing step. In certain aspects, the hot band is cold rolled to a final gauge aluminum alloy sheet. In some examples, the final gauge aluminum alloy sheet has a thickness of 4 mm or less, 3 mm or less, 2 mm or less, 1 mm or less, 0.9 mm or less, 0.8 mm or less, 0.7 mm or less, 0.6 mm or less, 0.5 mm or less, 0.4 mm or less, 0.3 mm or less, 0.2 mm or less, or 0.1 mm. Solutionizing

The solutionizing step can include heating the aluminum alloy sheet or other rolled article from room temperature to a peak metal temperature. Optionally, the peak metal temperature can be from about 520 °C to about 590 °C (e.g., from about 520 °C to about 580 °C, from about 530 °C to about 570 °C, from about 545 °C to about 575 °C, from about 550 °C to about 570 °C, from about 555 °C to about 565 °C, from about 540 °C to about 560 °C, from about 560 °C to about 580 °C, or from about 550 °C to about 575 °C). The aluminum alloy sheet can soak at the peak metal temperature for a period of time. In certain aspects, the aluminum alloy sheet is allowed to soak for up to approximately 2 minutes (e.g., from about 10 seconds to about 120 seconds inclusively). For example, the sheet can be soaked at the temperature of from about 520 °C to about 590 °C for 10 seconds, 15 seconds, 20 seconds, 25 seconds, 30 seconds, 35 seconds, 40 seconds, 45 seconds, 50 seconds, 55 seconds, 60 seconds, 65 seconds, 70 seconds, 75 seconds, 80 seconds, 85 seconds, 90 seconds, 95 seconds, 100 seconds, 105 seconds, 110 seconds, 115 seconds, 120 seconds, or anywhere in between. Aging

The aluminum alloy sheet can optionally undergo a pre-aging heat treatment. In some examples, pre-aging can include heating the aluminum alloy sheet to a temperature of from about 80 °C to about 120 °C (e.g., about 80 °C, about 85 °C, about 90 °C, about 95 °C, about 100 °C, about 105 °C, about 110 °C, about 115 °C, about 120 °C, or anywhere in between) and coiling the aluminum alloy sheet. The coiled aluminum alloy sheet can be cooled (i.e., coil cooling is performed) for a period of up to about 24 hours (e.g., about 1 hour, about 2 hours, about 6 hours, about 12 hours, about 18 hours, about 24 hours, or anywhere in between).

The aluminum alloy sheet can then be naturally aged and/or artificially aged. In some examples, the aluminum alloy sheet can be naturally aged for a period of time to result in a T4 temper. For example, the aluminum alloy sheet can be naturally aged for 1 week or more, 2 weeks or more, 3 weeks or more, or 4 weeks or more.

In certain aspects, the aluminum alloy sheet in the T4 temper can be artificially aged at a temperature of from about 180 °C to about 225 °C (e.g., 185 °C, 190 °C, 195 °C, 200 °C, 205 °C, 210 °C, 215 °C, 220 °C, or 225 °C) for a period of time to result in a T6 temper. For example, the aluminum alloy sheet can be artificially aged for a period from about 15 minutes to about 3 hours (e.g., 15 minutes, 30 minutes, 60 minutes, 90 minutes, 105 minutes, 2 hours, 2.5 hours, 3 hours, or anywhere in between) to result in a T6 temper. Methods of Using

The alloys, products, and methods described herein can be used in automotive, electronics, and transportation applications, such as commercial vehicle, aircraft, or railway applications. For example, the alloys can be used for chassis, cross-member, and intra-chassis components (encompassing, but not limited to, all components between the two C channels in a commercial vehicle chassis) to gain strength, serving as a full or partial replacement of high- strength steels. In certain embodiments, the alloys can be used in F, T4, T6, or T8x tempers. In certain aspects, the alloys are used with a stiffener to provide additional strength. In certain aspects, the alloys are useful in applications where the processing and operating temperature is approximately 150 °C or lower.

In certain aspects, the alloys and methods can be used to prepare motor vehicle body part products. For example, the disclosed alloys and methods can be used to prepare automobile body parts, such as bumpers, side beams, roof beams, cross beams, pillar reinforcements (e.g., A-pillars, B-pillars, and C-pillars), inner panels, side panels, floor panels, tunnels, structure panels, reinforcement panels, inner hoods, or trunk lid panels. The disclosed aluminum alloys and methods can also be used in aircraft or railway vehicle applications, to prepare, for example, external and internal panels.

The described alloys and methods can also be used to prepare housings for electronic devices, including mobile phones and tablet computers. For example, the alloy can be used to prepare housings for the outer casing of mobile phones (e.g., smart phones) and tablet bottom chassis, with or without anodizing. Exemplary consumer electronic products include mobile phones, audio devices, video devices, cameras, laptop computers, desktop computers, tablet computers, televisions, displays, household appliances, video playback and recording devices, and the like. Exemplary consumer electronic product parts include outer housings (e.g., facades) and inner pieces for the consumer electronic products.

ILLUSTRATIONS

Illustration 1 is an aluminum alloy, comprising about 0.8 - 1.5 wt. % Si, 0.1 - 0.5 wt. % Fe, 0.5 - 1.0 wt. % Cu, 0.5 - 0.9 wt. % Mg, up to 0.1 wt. % Ti, up to 0.5 wt. % Mn, up to 0.5 wt. % Cr, up to 0.5 wt. % Zr, up to 0.5 wt. % V, up to 0.15 wt. % impurities, and Al.

Illustration 2 is the aluminum alloy of any preceding or subsequent illustration, comprising about 0.9 - 1.4 wt. % Si, 0.1 - 0.35 wt. % Fe, 0.6 - 0.9 wt. % Cu, 0.6 - 0.9 wt. % Mg, 0.01 - 0.09 wt. % Ti, up to 0.3 wt. % Mn, up to 0.3 wt. % Cr, up to 0.3 wt. % Zr, up to 0.3 wt. % V, up to 0.15 wt. % impurities, and Al.

Illustration 3 is the aluminum alloy of any preceding or subsequent illustration, comprising about 1.0 - 1.3 wt. % Si, 0.1 - 0.25 wt. % Fe, 0.7 - 0.9 wt. % Cu, 0.6 - 0.8 wt. % Mg, 0.01 - 0.05 wt. % Ti, up to 0.2 wt. % Mn, up to 0.2 wt. % Cr, up to 0.2 wt. % Zr, up to 0.2 wt. % V, up to 0.15 wt. % impurities, and Al.

Illustration 4 is the aluminum alloy of any preceding or subsequent illustration, wherein the aluminum alloy comprises at least one of Mn, Cr, Zr, and V.

Illustration 5 is the aluminum alloy of any preceding or subsequent illustration, wherein a combined content of Mn, Cr, Zr, and/or V is at least about 0.14 wt. %.

Illustration 6 is the aluminum alloy of any preceding or subsequent illustration, wherein the combined content of Mn, Cr, Zr, and/or V is from about 0.14 wt. % to about 0.4 wt. %.

Illustration 7 is the aluminum alloy of any preceding or subsequent illustration, wherein the combined content of Mn, Cr, Zr, and/or V is from about 0.15 wt. % to about 0.25 wt. %.

Illustration 8 is the aluminum alloy of any preceding or subsequent illustration, wherein the aluminum alloy comprises about 0.01 - 0.3 wt. % V.

Illustration 9 is the aluminum alloy of any preceding or subsequent illustration, wherein the aluminum alloy comprises excess Si and wherein an excess Si content is from about 0.01 to about 1.0.

Illustration 10 is an aluminum alloy product, comprising the aluminum alloy of any preceding or subsequent illustration.

Illustration 11 is the aluminum alloy product of any preceding or subsequent illustration, wherein the aluminum alloy product comprises a rotated cube crystallographic texture at a volume percent of at least about 5 %.

Illustration 12 is the aluminum alloy product of any preceding or subsequent illustration, wherein the aluminum alloy product comprises dispersoids in an amount of at least about 1,500,000 dispersoids per mm ² .

Illustration 13 is the aluminum alloy product of any preceding or subsequent illustration, wherein the dispersoids occupy an area ranging from about 0.5 % to about 5 % of the aluminum alloy.

Illustration 14 is the aluminum alloy product of any preceding or subsequent illustration, wherein the aluminum alloy product comprises Fe-constituents. Illustration 15 is the aluminum alloy product of any preceding or subsequent illustration, wherein the Fe-constituents comprise Al(Fe,X)Si phase particles.

Illustration 16 is the aluminum alloy product of any preceding or subsequent illustration, wherein an average particle size of the Fe-constituents is up to about 4 μιη.

Illustration 17 is the aluminum alloy product of any preceding or subsequent illustration, wherein the aluminum alloy product comprises a yield strength of at least about 300 MPa when in a T6 temper.

Illustration 18 is the aluminum alloy product of any preceding or subsequent illustration, wherein the aluminum alloy product comprises a uniform elongation of at least about 20 % and a minimum bend angle of at least about 120° when in a T4 temper.

Illustration 19 is a method producing an aluminum alloy product according to any preceding or subsequent illustration, comprising: casting an aluminum alloy according to Illustration 1 to provide a cast article; homogenizing the cast article in a two-stage homogenization process, wherein the two-stage homogenization process comprises heating the cast article to a first stage homogenization temperature and holding the cast article at the first stage homogenization temperature for a period of time and further heating the cast article to a second stage homogenization temperature and holding the cast article at the second stage homogenization temperature for a period of time; hot rolling and cold rolling to provide a final gauge aluminum alloy product; solution heat treating the final gauge aluminum alloy product; and pre-aging the final gauge aluminum alloy product.

Illustration 20 is the method of any preceding illustration, wherein the first stage homogenization temperature is from about 470 °C to about 530 °C and the second stage homogenization temperature is from about 525 °C to about 575 °C, and wherein the second stage homogenization temperature is higher than the first stage homogenization temperature.

The following examples will serve to further illustrate the present invention without, however, constituting any limitation thereof. On the contrary, it is to be clearly understood that resort may be had to various embodiments, modifications, and equivalents thereof which, after reading the description herein, may suggest themselves to those skilled in the art without departing from the spirit of the invention. During the studies described in the following examples, conventional procedures were followed, unless otherwise stated. Some of the procedures are described below for illustrative purposes. EXAMPLES

Example 1: Aluminum Alloy Properties

Alloys were prepared for strength and formability testing. The compositions for these alloys are provided in Table 4 below. In each of the alloy compositions in Table 4, the remainder is Al.

Table 4

Elemental values in wt. %. *Excess Si values obtained according to calculation methods described herein. The alloys were prepared by DC casting the components into ingots and homogenizing the ingots in a two-step homogenization step as described herein. The first step provided nucleation of a maximum amount of fine dispersoids (e.g., dispersoids having a diameter of less than about 10 nm). The second step coarsened the fine dispersoids. The homogenized ingots were then laid down and hot rolled according to the methods as described herein to a 10 mm gauge. The hot band was coiled and cooled and was then cold rolled to a 2 mm gauge. A solution heat treatment step was then performed at 560 °C for 35 seconds. A pre-aging step was performed by heating the sheet to 100 °C and soaking for 1 hour (e.g., to simulate coil cooling as described above), followed by natural aging to achieve the T4 temper. The T6 temper was then achieved by aging the T4 alloys at 200 °C for 30 minutes.

The properties of the D 1 - D6 alloys in T4 temper, including the yield strength, uniform elongation, and bend angle, were determined. Tensile testing was performed according to ASTM B557 in three directions relative to a rolling direction of the alloy sheets to evaluate anisotropic properties that can occur during recrystallization. Yield strength (referred to as "YS" and indicated by histograms) and uniform elongation (referred to as "UE" and indicated by points) are shown in Figure 1 for a longitudinal direction along the rolling direction (referred to as "L" and indicated by vertical stripes), a transverse direction 90° to the rolling direction (referred to as "T" and indicated by horizontal stripes), and a diagonal direction 45° to the rolling direction (referred to as "D" and indicated by cross-hatching). Evident in the graph based on the yield strength and uniform elongation, the alloys exhibited isotropic behavior in all three directions subjected to tensile testing even with elongated recrystallized grain structures as observed in Figure 2. The uniform elongation values ranged from 24 % to 26 % and the yield strengths were from 185 MPa to 195 MPa.

Figure 3 shows the yield strengths and uniform elongations for alloys Dl - D6 in T4 and T6 tempers. For alloys Dl - D6 in T4 temper, the composition had a negligible effect on yield strength and uniform elongation. For alloys Dl - D6 in T6 temper, the composition had a negligible effect on uniform elongation and a decrease in yield strength of about 10 MPa for alloys including V in the composition. The decrease in yield strength can be attributed to solute loss (e.g., Si, Mg, and/or Cu) during solutionizing by heterogeneous nucleation of solute precipitates on V-containing dispersoids.

Figure 4 is a graph showing bend angle test results for alloys Dl - D6 in a T4 temper. Addition of Cr and V produced a large number of fine dispersoids which improves bending by diffusing strain distribution during deformation (e.g., bending, forming, stamping, or any suitable deformation process). In some cases, Mn combined with Fe and Si to form and spheroidize Fe- constituents, rather than forming dispersoids, due to the high diffusivity of Mn as compared to Zr, Cr, and/or V. Spheroidization of the Fe-constituents improved bending by eliminating elongated (i.e., needle-like) particulates that can initiate cracking during deformation. Additionally, V-containing alloys (e.g., alloys D4 - D6) exhibited improved bending compared to V-free variants due to Fe-constituent spheroidization. Figure 5 compares yield strength (YS) and bend angle (VDA) for alloys Dl - D6 in T4 and T6 tempers.

Example 2: Aluminum Alloy Microstructure

Figure 6 shows recrystallization texture components for alloys Dl - D6, including cube, goss, brass, S, Cu, and rotated cube (referred to as "RC"). Each alloy Dl - D6 exhibited a similar distribution of texture components, and composition had a negligible effect on recrystallization texture. Surprisingly, each alloy exhibited a relatively high amount of rotated cube texture, resulting in the significantly improved bending angles shown in Figure 4 and Figure 5.

Figure 7 shows transmission electron microscopy (TEM) images of alloys Dl - D6 in T4 temper. Evident in the TEM images is dispersoid formation (shown as bright white particulates) in each alloy. Alloy D4 (including Cr and V) exhibited a higher dispersoid amount due to the relatively low diffusivities of Cr and V. Likewise, alloys D5 and D6 exhibited a lower number of dispersoids due to the relatively higher diffusivities of Mn and Zr. Accordingly, alloy D6 exhibited a lesser amount of dispersoids attributed to an affinity of Mn to be incorporated in Fe-constituents and to not solely form Mn dispersoids. Figure 8 shows dispersoid number density (histograms) and area fraction (open circles) for alloys Dl - D6 in T4 temper. Alloys not containing V (alloys Dl - D3) exhibited similar dispersoid number density. Alloy D2 (incorporating only Cr as a transition metal alloying element) exhibited a higher dispersoid area fraction compared to alloys Dl and D3 (incorporating Mn and Cr (Dl) and Zr and Cr (D3)). Alloy D4 (incorporating Cr and V) exhibited the highest dispersoid number density and the highest dispersoid area fraction.

Figure 9 shows scanning electron microscopy (SEM) images of alloys Dl - D6 in a T4 temper. Evident in the SEM images is Fe-constituent formation (shown as bright white elongated particulates). Each of the alloys Dl - D6 exhibited similar amounts of Fe-constituent formation, and similar Fe-constituent particle size distribution as shown in Figure 10. As described above, employing transition metal alloying elements reduced the formation of Fe- constituents (e.g., AlFeSi) by replacing a portion of the Fe, thus forming spherical Al(Fe,X)Si constituents. Each alloy continued to exhibit AlFeSi (elongated particulates) due to the presence of excess Si and processing at a low homogenization temperature (e.g., about 500 °C), with a reduced size and size distribution in alloys not employing the transition metal alloying elements. In some aspects, the AlFeSi constituents in alloys not containing the transition metal alloying elements exhibited a larger size than the AlFeSi constituents observed in the alloys containing the transition metal alloying elements. Fe-constituent size and size distribution was evaluated at a depth of about 0.5 mm from a surface of the aluminum alloy sheet (referred to as quarter thickness, indicated "QT" in the graph).

Figure 1 1 shows optical microscopy (referred to as "OM") and SEM images of alloy

Dl . Alloy Dl was subjected to a one-step homogenization after casting, including a thermal ramp of 50 °C per hour to 560 °C, soaked for 2 hours, and subsequently hot rolled, cold rolled, solutionized, pre-aged, and naturally aged as described above. Evident in the OM images is incipient and/or eutectic melting of Mg ₂ Si in alloy Dl (shown as dark areas). SEM images show the dark areas are voids that formed in the alloy during homogenization. Energy dispersive X-ray spectroscopy (EDXS) showed Fe-constituents present in the voids (shown as bright particulates). Employing the exemplary two-step homogenization as described herein can eliminate the incipient and/or eutectic melting when transition metal alloying elements are incorporated in the aluminum alloy compositions.

All patents, publications, and abstracts cited above are incorporated herein by reference in their entireties. Various embodiments of the invention have been described in fulfillment of the various objectives of the invention. It should be recognized that these embodiments are merely illustrative of the principles of the present invention. Numerous modifications and adaptions thereof will be readily apparent to those skilled in the art without departing from the spirit and scope of the present invention as defined in the following claims.