Devices and Methods for Performing Shear-Assisted Extrusion and Extrusion Processes

Abstract

A method for preparing a shear-assisted extruded material from a powder billet is provided, the method comprising providing a billet of material in substantially powder form; applying both axial and rotational pressure to the material to deform at least some of the contacted material; and extruding the material to form an extruded material. A method for preparing shear-assisted extruded material is provided, the method comprising applying both axial and rotational pressure to stock material to form an extruded material at a rate between 2 and 13 m/min. A method for preparing shear-assisted extruded material is provided. The method comprises applying both axial and rotational pressure to stock material to form an extruded material; and aging the extruded material for less than 3 hours. A method for preparing shear-assisted extruded material is provided. The method comprises providing a stock material for shear-assisted extrusion; and applying both axial and rotational force to the stock material to form an extruded material, wherein the axial force does not decrease during the extrusion.

Claims

1. A method for preparing an extruded material by shear assisted processing and extrusion from a powder billet, the method comprising: providing a billet of material in substantially powder form; applying both axial and rotational pressure to the material to deform at least some of the material; and extruding the material to form an extruded material.

2. The method of claim 1 wherein the billet material is loose powder.

3. The method of claim 1 wherein the billet material comprises Al.

4. The method of claim 1 wherein the billet material comprises one or more of Al, Mg, Fe, Si, and/or Zr.

5. The method of claim 4 wherein the extruded material comprises an alloy.

6. The method of claim 1 wherein the billet material in powder form can have a maximum particle size of 100 um.

7. The method of claim 1 wherein the billet material in powder form can have a particle size greater than 100 um.

8. The method of claim 1 further comprising using an extrusion die defining spiral grooves.

9. The method of claim 1 wherein individual particles of the powder include an oxide or ceramic component.

10. The method of claim 1 wherein the extruded material has a tensile strength from about 220 MPa to about 360 MPa.

11-20. (canceled)

21. A method for preparing extruded material by shear assisted processing and extrusion, the method comprising: applying both axial and rotational pressure to stock material to form an extruded material; and aging the extruded material for less than 3 hours.

22. The method of claim 21 wherein the stock material is in powder form.

23. The method of claim 21 wherein the stock material is defined by castings.

24. The method of claim 21 wherein the stock material comprises powder, flake, chip, or scrap.

25. The method of claim 21 wherein the stock material comprises Al.

26. The method of claim 21 wherein the extruded material has a hardness of at least 155 HV after the 3 hrs.

27. The method of claim 21 further comprising solution heating the extruded material before the aging.

28. A method for preparing extruded material by shear assisted processing and extrusion, the method comprising: providing a stock material for shear-assisted extrusion; and applying both axial and rotational force to the stock material to form an extruded material, wherein the axial force does not decrease during the extrusion.

29. The method of claim 28 further comprising initiating an initial axial force upon a stock material; maintaining a steady state axial force upon the stock material; and reducing the axial force upon stock material depletion.

30. The method of claim 29 wherein the stead state axial force is greater than the initial axial force.

31. The method of claim 29 further comprising a transition between the initial axial force and the steady state axial force, the transition having a position slope when plotted.

32. The method of claim 28 further comprising ramping the initial axial force to the steady state axial force.

33. The method of claim 32 further comprising decreasing rotational rpms while increasing ramping of ram speed.

34. The method of claim 29 further comprising maintaining a die face temperature during steady force application at a substantially constant temperature.

35. The method of claim 34 wherein the temperature is about 400° C.

Description

DRAWINGS

[0044] Embodiments of the disclosure are described below with reference to the following accompanying drawings.

[0045] FIG. 1 provides a general overview of the state of the art of extrusion that includes ingot formation, stress relief, phase conversion, homogenization, billet pre-heating, extrusion, solution heating, and aging.

[0046] FIG. 2A shows a ShAPE setup for extruding hollow cross section pieces.

[0047] FIG. 2B shows another configuration for extruding hollow cross-sectional pieces.

[0048] FIG. 3A shows a top perspective view of a modified scroll face tool for a portal bridge die.

[0049] FIG. 3B shows a bottom perspective view of a modified scroll face that operates like a portal bridge die.

[0050] FIG. 3C shows a side view of the modified portal bridge die.

[0051] FIG. 4 shows an illustrative view of material separated using at least some of the devices shown in FIGS. 2A-3C.

[0052] FIG. 5A shows a ShAPE set up for consolidating high entropy alloys (HEAs) from arc melted pucks into densified pucks.

[0053] FIG. 5B shows an example of the scrolled face of the rotating tool in FIG. 5A.

[0054] FIG. 5C shows an example of HEA arc melted samples crushed and placed inside the chamber of the ShAPE device prior to processing.

[0055] FIG. 6 shows back scatter electron—scanning electron microscope (BSE-SEM) image of cross section of the HEA arc melted samples before ShAPE processing, showing porosity, intermetallic phases and cored, dendritic microstructure.

[0056] FIG. 7A shows BSE-SEM images at the bottom of the puck resulting from the processing of the material in FIG. 5C.

[0057] FIG. 7B shows BSE-SEM images halfway through the puck

[0058] FIG. 7C shows BSE-SEM images of the interface between high shear region un-homogenized region (approximately 0.3 mm from puck surface)

[0059] FIG. 7D shows BSE-SEM images of a high shear region

[0060] FIG. 8 is a depiction of a series of different die face configurations according to embodiments of the disclosure.

[0061] FIG. 9 is an isometric view of a die face tool according to an embodiment of the disclosure.

[0062] FIGS. 10A-10C are depictions of a die face according to an embodiment of the disclosure.

[0063] FIGS. 11A-11C are depictions of a die face according to an embodiment of the disclosure.

[0064] FIGS. 12A-12C are depictions of a die face according to an embodiment of the disclosure.

[0065] FIGS. 13A-13C are depictions of a die face according to an embodiment of the disclosure.

[0066] FIGS. 14A-14C are depictions of a die face according to an embodiment of the disclosure.

[0067] FIGS. 15A-15B are depictions of the use of a die face on starting materials according to an embodiment of the disclosure.

[0068] FIG. 16 is a depiction of the use of a die face on starting material according to an embodiment of the disclosure.

[0069] FIG. 17 is a depiction of a die according to an embodiment of the disclosure.

[0070] FIG. 18 is a depiction of extruded material as well as a remnant of the starting material according to an embodiment of the disclosure.

[0071] FIG. 19 is a depiction of a die according to an embodiment of the disclosure.

[0072] FIG. 20 is a depiction of a die according to an embodiment of the disclosure. Die for purposes of this disclosure refers to scroll face or incorporated die, for example.

[0073] FIG. 21 is data demonstrating reduced extrusion force utilizing die configurations of the present disclosure.

[0074] FIG. 22 is a depiction of data depicting reduced motor torque utilizing dies of the present disclosure.

[0075] FIG. 23 is a depiction of two dies, one having a flat face and one having a conical face according to an embodiment of the disclosure.

[0076] FIG. 24 is a depiction of data demonstrating reduced force utilizing dies according to an embodiment of the disclosure.

[0077] FIG. 25 again is data demonstrating reduced torque utilizing dies according to an embodiment of the disclosure.

[0078] FIG. 26 is a depiction of data demonstrating reduced temperature utilizing dies according to an embodiment of the disclosure.

[0079] FIG. 27 is a depiction of dies corresponding to extruded materials according to an embodiment of the disclosure.

[0080] FIGS. 28-29 are depictions of dies corresponding to extruded materials according to an embodiment of the disclosure.

[0081] FIGS. 30-31 depict extruded product materials utilizing different dies according to an embodiment of the disclosure.

[0082] FIG. 32 is a die according to an embodiment of the disclosure.

[0083] FIG. 33 is another die according to an embodiment of the disclosure.

[0084] FIG. 34 is a depiction of extruded materials produced utilizing dies according to an embodiment of the disclosure.

[0085] FIG. 35 is data for different dies according to an embodiment of the disclosure.

[0086] FIG. 36 is data acquired utilizing dies according to an embodiment of the disclosure.

[0087] FIG. 37 is a series of photographs of extrusion of Mg—Al with consolidated cross sections, and in (B) showing gradient in composition between Mg and Al with absence of a Mg.sub.17Al.sub.12 interfacial layer at dissimilar interface (C).

[0088] FIG. 38 is a depiction of an example extrusion assembly according to an embodiment of the disclosure and also a depiction of feedstock material engagements and/or feedstock interfaces according to an embodiment of the disclosure.

[0089] FIG. 39 is a depiction of extruded material having no Mg.sub.17Al.sub.12 interfacial layer.

[0090] FIG. 40 is a depiction of extrusion material having a graded interface layer prepared using engaged feedstock materials according to an embodiment of the disclosure.

[0091] FIG. 41 is a depiction of two components, AA7075 and AA6061, bonded at an abrupt transition layer according to an embodiment of the disclosure.

[0092] FIG. 42 is an example rolling mill assembly according to an embodiment of the disclosure.

[0093] FIG. 43 demonstrates the process steps for preparing an extruded fabricated tube, the open tube, and the rolling of the tube according to an embodiment of the disclosure.

[0094] FIGS. 44A and 44B depict an example extrusion assembly according to an embodiment of the disclosure as well as example extruded material according to an embodiment of the disclosure.

[0095] FIG. 45 demonstrates the process steps for preparing a metal sheet through to 16 passes according to an embodiment of the disclosure.

[0096] FIG. 46 demonstrates a 0.005 inch thick sheet in various configurations according to an embodiment of the disclosure.

[0097] FIG. 47 shows reduction per rolling pass according to an embodiment of the disclosure.

[0098] FIGS. 48A-48C demonstrate front end methods of preparing billets for extrusion. These methods are shown in FIG. 48A with ingot formation, stress relief, phase conversion, billet pre-heating, and extrusion; FIG. 48B with ingot formation, stress relief, phase conversion, homogenization, and extrusion; and FIG. 48C with ingot formation and extrusion.

[0099] FIGS. 49A and 49B depict prior art methods of billet homogenization according to ASTM methods. As shown, a substantial amount of the time, at least 20 hours, is removed from the homogenization step.

[0100] FIG. 50 is data of extruded product according to embodiments of the present disclosure.

[0101] FIG. 51 is depiction of extruded product according to embodiments of the present disclosure.

[0102] FIG. 52 is a stepwise depiction of extrusion and solution heating according to embodiments of the present disclosure.

[0103] FIG. 53 is data acquired utilizing methods according to embodiments of the present disclosure.

[0104] FIG. 54 is data acquired utilizing methods according to embodiments of the present disclosure.

[0105] FIG. 55 is data acquired utilizing methods according to embodiments of the present disclosure.

[0106] FIGS. 56A-56B depict extrusion to aging techniques and extrusion solution heating and aging techniques according to embodiments of the present disclosure.

[0107] FIG. 57 depicts data acquired utilizing methods according to embodiments of the present disclosure.

[0108] FIG. 58 depicts material change upon application of ShAPE to powder Al according to an embodiment of the disclosure.

[0109] FIG. 59 depicts another view of material change upon application of ShAPE to powder Al according to an embodiment of the disclosure.

[0110] FIG. 60 depicts views of material changes upon application of ShAPE to powder Al, Fe, Ti and Cr according to an embodiment of the disclosure.

[0111] FIG. 61 depicts ShAPE axial forces in the context of traditional extrusion forces with “No Breakthrough” indicating the breakthrough force that is eliminated with ShAPE.

[0112] FIG. 62 depicts ShAPE rotational rpms and axial forces of ShAPE.

[0113] FIG. 63 depicts Aluminum (AA 6063) ShAPE processes parameters.

[0114] FIG. 64 depicts Aluminum (AA 7075) ShAPE processes parameters.

[0115] FIG. 65 depicts alloy (Mg ZK60) ShAPE processes parameters.

DESCRIPTION

[0116] This disclosure is submitted in furtherance of the constitutional purposes of the U.S. Patent Laws “to promote the progress of science and useful arts” (Article 1, Section 8).

[0117] The following description including the attached pages provide various examples of the present invention. It will be clear from this description of the invention that the invention is not limited to these illustrated embodiments but that the invention also includes a variety of modifications and embodiments thereto. Therefore, the present description should be seen as illustrative and not limiting. While the invention is susceptible to various modifications and alternative constructions, it should be understood, that there is no intention to limit the invention to the specific form disclosed, but, on the contrary, the invention is to cover all modifications, alternative constructions, and equivalents falling within the spirit and scope of the invention as defined in the claims.

[0118] In the previously described and related applications various methods and techniques are described wherein the described technique and device (referred to as ShAPE) is shown to provide a number of significant advantages including the ability to control microstructure such as crystallographic texture through the cross sectional thickness, while also providing the ability to perform various other tasks. In this description we provide information regarding the use of the ShAPE technique to form materials with non-circular hollow profiles as well as methods for creating high entropy alloys that are useful in a variety of applications such as projectiles. Exemplary applications will be discussed on more detail in the following.

[0119] Referring first now to FIGS. 2A and 2B, examples of the ShAPE device and arrangement are provided. In an arrangement such as the one shown in FIG. 2A, rotating die 10 is thrust into a material 20 under specific conditions whereby the rotating and shear forces of the die face 12 and the die plunge 16 combine to heat and/or plasticize the material 20 at the interface of the die face 12 and the material 20 and cause the plasticized material to flow in desired direction in either a direct or indirect manner. (In other embodiments the material 20 may spin and the die 10 pushed axially into the material 20 so as to provide this combination of forces at the material face.) In either instance, the combination of the axial and the rotating forces plasticize the material 20 at the interface with the die face 12. Flow of the plasticized material can then be directed to another location wherein a die bearing surface 24 of a preselected length facilitates the recombination of the plasticized material into an arrangement wherein a new and more refined grain size and texture control at the micro level can take place. This then translates to an extruded product 22 with desired characteristics. This process enables better strength, ductility, and corrosion resistance at the macro level together with increased and better performance. This process can eliminate the need for additional heating, and the process can utilize a variety of forms of material including billet, powder or flake without the need for extensive preparatory processes such as “steel canning”, billet pre-heating, de-gassing, de-canning and other process steps can be utilized as well. This arrangement also provides for a methodology for performing other steps such as cladding, enhanced control for through wall thickness and other characteristics, joining of dissimilar materials and alloys, and beneficial feedstock materials for subsequent rolling operations.

[0120] This arrangement is distinct from and provides a variety of advantages over the prior art methods for extrusion. First, during the extrusion process the force rises to a peak in the beginning and then falls off once the extrusion starts. This is called breakthrough. In this ShAPE process the temperature at the point of breakthrough is very low. For example for Mg tubing, the temperature at breakthrough for the 2″ OD, 75 mil wall thickness ZK60 tubes is <150 C. This lower temperature breakthrough is believed in part to account for the superior configuration and performance of the resulting extrusion products.

[0121] Another feature is the low extrusion coefficient kf which describes the resistance to extrusion (i.e. lower kf means lower extrusion force/pressure). Kf is calculated to be 2.55 MPa and 2.43 MPa for the extrusions made from ZK60-T5 bar and ZK60 cast respectively (2″ OD, 75 mil wall thickness). The ram force and kf are remarkably low compared to conventionally extruded magnesium where kf ranges from 68.9-137.9 MPa. As such, the ShAPE process achieved a 20-50 times reduction in kf (as thus ram force) compared to conventional extrusion. This assists not only with regard to the performance of the resulting materials but also reduced energy consumption required for fabrication. For example, the electrical power required to extrude the ZK60-T5 bar and ZK60 cast (2″ OD, 750 mil wall thickness) tubes is 11.5 kW during the process. This is much lower than a conventional approach that uses heated containers/billets. Similar reductions in kf have also been observed when extruding high performance aluminum powder directing into wire, rod, and tubing.

[0122] The ShAPE process is significantly different than Friction Stir Back Extrusion (FSBE). In FSBE, a spinning mandrel is rammed into a contained billet, much like a drilling operation. Scrolled grooves force material outward and material back extrudes around and onto the mandrel to form a tube, not having been forced through a die. As a result, only very small extrusion ratios are possible, the tube is not fully processed through the wall thickness, the extrudate is not able to push off of the mandrel, and the tube length is limited to the length of the mandrel. In contrast, ShAPE utilizes spiral grooves on a die face to feed material inward through a die and around a mandrel that is traveling in the same direction as the extrudate. As such, a much larger outer diameter and extrusion ratio are possible, the material is uniformly process through the wall thickness, the extrudate is free to push off the mandrel as in conventional extrusion, and the extrudate length is only limited only by the starting volume of the billet. ShAPE can be scalable to the manufacturing level, while the limitations of FSBE have kept the technology as a non-scalable academic interest since FBSE was first reported.

[0123] An example of an arrangement using a ShAPE device and a mandrel 18 is shown in FIG. 2B. This device and associated processes have the potential to be a low-cost, manufacturing technique to fabricate variety of materials. As will be described below in more detail, in addition to modifying various parameters such as feed rate, heat, pressure and spin rates of the process, various mechanical elements of the tool assist to achieve various desired results. For example, varying scroll patterns 14 on the face of extrusion dies 12 can be used to affect/control a variety of features of the resulting materials. This can include control of grain size and crystallographic texture along the length of the extrusion and through-wall thickness of extruded tubing and other features. Alteration of parameters can be used to advantageously alter bulk material properties such as ductility and strength and allow tailoring for specific engineering applications including altering the resistance to crush, pressure or bending. Scrolls patterns have also been found to affect grain size and texture through the thickness of the extrusion.

[0124] The ShAPE process has been utilized to form various structures from a variety of materials including the arrangement as described in the following table.

TABLE-US-00001 TABLE 1 Alloy Material Class Precursor Form PUCKS Bi.sub.2Te.sub.3 Thermoelectric Powder Fe—Si Magnet Powder Nd.sub.2Fe.sub.11B/Fe Magnet Powder Nd.sub.2Fe.sub.14B Magnet Powder MA956 ODS Steel Powder Nb 0.95 Ti 0.05 Thermoelectric Powder Fe 1 Sb 1 Mn—Bi Magnet Powder Al—Si Model Binary Alloy Powder Cu—Ni Model Binary Alloy Powder Cu—Nb Model Binary Alloy Powder PM 2000 ODS Steel Powder Eurofer 97 ODS Steel Powder 14YWT ODS Steel Powder TUBES ZK60 Magnesium Alloy Barstock, Casting AZ31 Magnesium Alloy Barstock AZ91 Magnesium Alloy Flake, Casting AZS312 Magnesium Alloy Casting Mg-7 wt % Si Magnesium Alloy Casting AZ91- 1, 5 and 10 Mg MMC Mechanically wt. % Al.sub.2O.sub.3 Alloyed Flake AZ91- 1, 5 and 10 Mg MMC Mechanically wt. % Y.sub.2O.sub.3 Alloyed Flake AZ91- 1, 5 and 10 Mg MMC Mechanically and 5 wt. % SiC Alloyed Flake AA2024 Structural Aluminum Cast, Barstock AA6061 Structural Aluminum Cast, Barstock AA6063 Structural Aluminum Casting, Barstock and Chip AA7075 High Strength Aluminum Casting, barstock Al-12.4TM High Strength Aluminum Powder A356 Structural Aluminum Chip AA2024/1100 Aluminum Cladding Casting, barstock AA7075/AA6061 Aluminum Cladding Casting, barstock 1100/7075/1100 Aluminum Cladding Casting, barstock RODS Al—Mn wt. 15% Aluminum Manganese Casting Alloy Al—Mg Mg Al Coextrusion Barstock Mg—Dy—Nd—Zn—Zr Magnesium Rare Earth Barstock Cu Pure Copper Barstock ODS-Cu Oxide Dispersion Powder Strengthened Cu Cu-Graphite Conductive Copper Powder Cu-Graphene Conductive Copper Powder + Film Cu-Graphene Conductive Copper Barstock + Film Cu-Graphene Conductive Copper Foil + Film Al-Graphene Conductive Aluminum Powder + Film Al-Reduced Graphene Conductive Aluminum Barstock + Flake Al-Graphite Conductive Aluminum Barstock + Powder CP-Mg Pure Magnesium Barstock, casting AA6061 Aluminum Casting, barstock AA7075 Aluminum Casting, barstock Al—Ti—Mg—Cu—Fe High Entropy Alloy Casting Al- 1, 5, 10 at. % Mg Magnesium Alloy Casting Al-12.4TM High Temperature/ Powder Strength Aluminum Rhodium Pure Rhodium Barstock Al—Ce High Temperature/ Casting Strength Aluminum AA1100 Aluminum Alloy Barstock AA7XXX High Strength Aluminum Proprietary Powder 14YWT ODS Steel Powder MA956 ODS Steel Powder Bi.sub.2Te.sub.3 Thermoelectric Casting and Sintered Powder Mixed Plastic Plastic Scrap and Pellets

[0125] In addition, to the pucks, rods and tubes described above, the present disclosure also provides a description of the use of a specially configured scroll component referred by the inventors as a portal bridge die head which allows for the fabrication of ShAPE extrusions with non-circular hollow profiles. This configuration allows for making extrusion with non-circular, and multi-zoned, hollow profiles using a specially formed portal bridge die and related tooling.

[0126] FIGS. 3A-3C show various views of a portal bridge die design with a modified scroll face that unique to operation in the ShAPE process. FIG. 3A shows an isometric view of the scroll face on top of the portal bridge die and FIG. 3B shows an isometric view of the bottom of the portal bridge die with the mandrel visible.

[0127] In the present embodiment grooves 13, 15 on the face 12 of the die 10 direct plasticized material toward the aperture ports 17. Plasticized material then passes through the aperture ports 12 wherein it is directed to a die bearing surface 24 within a weld chamber similar to conventional portal bridge die extrusion. In this illustrative example, material flow is separated into four distinct streams using four ports 17 as the billet and the die are forced against one another while rotating.

[0128] While the outer grooves 15 on the die face feed material inward toward the ports 17, inner grooves 13 on the die face feed material radially outward toward the ports 17. In this illustrative example, one groove 13 is feeding material radially outward toward each port 17 for a total of four outward flowing grooves. The outer grooves 15 on the die surface 12 feed material radially inward toward the port 17. In this illustrative example, two grooves are feeding material radially inward toward each port 17 for a total of eight inward feeding grooves 15. In addition to these two sets of grooves, a perimeter groove 19 on the outer perimeter of the die, shown in FIG. 3C, is oriented counter to the die rotation so as to provide back pressure thereby minimizing material flash between the container and die during extrusion.

[0129] FIG. 3B shows a bottom perspective view of the portal bridge die 12. In this view, the die shows a series of full penetration of ports 17. In use, streams of plasticized material funneled by the inward 15 and outward 13 directed grooves described above pass through these penetration portions 17 and then are recombined in a weld chamber 21 and then flow around a mandrel 18 to create a desired cross section. The use of scrolled grooves 13, 15, 19 to feed the ports 17 during rotation—as a means to separate material flow of the feedstock (e.g. powder, flake, billet, etc.) into distinct flow streams has never been done to our knowledge. This arrangement enables the formation of items with noncircular hollow cross sections.

[0130] FIG. 4 shows a separation of magnesium alloy ZK60 into multiple streams using the portal bridge die approach during ShAPE processing. (In this case the material was allowed to separate for effect and illustration of the separation features and not passed over a die bearing surface for combination). Conventional extrusion does not rotate and the addition of grooves would greatly impede material flow. But when rotation is present, such as in ShAPE or friction extrusion, the scrolls not only assist flow, but significantly assist the functioning of a portal bridge die extrusion 17 and the subsequent formation of non-circular hollow profile extrusions. Without scrolled grooves feeding the portals, extrusion via the portal bridge die approach using a process where rotation is involved, such as ShAPE, would be ineffective for making items with such a configuration. The prior art conventional linear extrusion process teach away from the use of surface features to guide material into the portals 17 during extrusion.

[0131] In the previously described and related applications various methods and techniques are described wherein the ShAPE technique and device is shown to provide a number of significant advantages including the ability to control microstructure such as crystallographic texture through the cross sectional thickness, while also providing the ability to perform various other tasks. In this description we provide information regarding the use of the ShAPE technique to form materials with non-circular hollow profiles as well as methods for creating high entropy alloys that are useful in a variety of applications. These two exemplary applications will be discussed on more detail in the following.

[0132] FIG. 5A shows a schematic of the ShAPE process which utilizes a rotating tool to apply load/pressure and at the same time the rotation helps in applying torsional/shear forces, to generate heat at the interface between the tool and the feedstock and within the material, thus helping to consolidate the material. In this particular embodiment the arrangement of the ShAPE setup is configured so as to consolidate high entropy alloy (HEA) arc-melted buttons into densified pucks. In this arrangement the rotating ram tool is made from an Inconel alloy and has an outer diameter (OD) of 25.4 mm, and the scrolls on the ram face were 0.5 mm in depth and had a pitch of 4 mm with a total of 2.25 turns. In this instance the ram surface incorporated a thermocouple to record the temperature at the interface during processing. (see FIG. 5B) The setup enables the ram to spin at speeds from 25 to 1500 RPM.

[0133] In use, both an axial force and a rotational force are applied to a material of interest causing the material to plasticize. In extrusion applications, the plasticized material then flows over a die bearing surface dimensioned so as to allow recombination of the plasticized materials in an arrangement with superior grain size distribution and alignment than what is possible in traditional extrusion processing. As described in the prior related applications this process provides a number of advantages and features that conventional prior art extrusion processing is simply unable to achieve.

[0134] High entropy alloys are generally solid-solution alloys made of five or more principal elements in equal or near equal molar (or atomic) ratios. While this arrangement can provide various advantages, it also provides various challenges particularly in forming. While conventional alloys can comprise one principal element that largely governs the basic metallurgy of that alloy system (e.g. nickel-base alloys, titanium-base alloys, aluminum-base alloys, etc.) in an HEA each of the five (or more) constituents of HEAs can be considered as the principal element. Advances in production of such materials may open the doors to their eventual deployment in various applications. However, standard forming processes have demonstrated significant limitations in this regard. Utilization of the ShAPE type of process demonstrates promise in obtaining such a result.

[0135] In one example a “low-density” AlCuFe(Mg)Ti HEA was formed. Beginning with arc-melted alloy buttons as a pre-cursor, the ShAPE process was used to simultaneously heat, homogenize, and consolidate the HEA resulting in a material that overcame a variety of problems associated with prior art applications and provided a variety of advantages. In this specific example, HEA buttons were arc-melted in a furnace under 10.sup.−6 Torr vacuum using commercially pure aluminum, magnesium, titanium, copper and iron. Owing to the high vapor pressure of magnesium, a majority of magnesium vaporized and formed Al1Mg0.1Cu2.5Fe1Ti1.5 instead of the intended Al1Mg1Cu1Fe1Ti1 alloy. The arc melted buttons described in the paragraph above were easily crushed with a hammer and used to fill the die cavity/powder chamber (FIG. 5C), and the shear-assisted extrusion process initiated. The volume fraction of the material filled was less than 75%, but was consolidated when the tool was rotated at 500 RPM under load control with a maximum pressure set at 85 MPa and at 175 MPa.

[0136] Comparison of the arc-fused material and the materials developed under the ShAPE process demonstrated various distinctions. The arc melted buttons of the LWHEA exhibited a cored dendritic microstructure along with regions containing intermetallic particles and porosity. Using the ShAPE process these microstructural defects were eliminated to form a single phase, refined grain and no porosity LWHEA sample

[0137] FIG. 6 shows the backscattered SEM (BSE-SEM) image of the as-cast/arc-melted sample. The arc melted samples had a cored dendritic microstructure with the dendrites rich in iron, aluminum and titanium and were 15-30 μm in diameter, whereas the inter-dendritic regions were rich in copper, aluminum and magnesium. Aluminum was uniformly distributed throughout the entire microstructure. Such microstructures are typical of HEA alloys. The inter-dendritic regions appeared to be rich in Al—Cu—Ti intermetallic and was verified by XRD as AlCu.sub.2Ti. XRD also confirmed a Cu.sub.2Mg phase which was not determined by the EDS analysis and the overall matrix was BCC phase. The intermetallics formed a eutectic structure in the inter-dendritic regions and were approximately 5-10 μm in length and width. The inter-dendritic regions also had roughly 1-2 vol % porosity between them and hence was difficult to measure the density of the same.

[0138] Typically such microstructures are homogenized by sustained heating for several hours to maintain a temperature near the melting point of the alloy. In the absence of thermodynamic data and diffusion kinetics for such new alloy systems the exact points of various phase formations or precipitation is difficult to predict particularly as related to various temperatures and cooling rates. Furthermore, unpredictability with regard to the persistence of intermetallic phases even after the heat treatment and the retention of their morphology causes further complications. A typical lamellar and long intermetallic phase is troublesome to deal with in conventional processing such as extrusion and rolling and is also detrimental to the mechanical properties (elongation).

[0139] The use of the ShAPE process enabled refinement of the microstructure without performing homogenization heat treatment and provides solutions to the aforementioned complications. The arc melted buttons, because of the presence of their respective porosity and the intermetallic phases, were easily fractured into small pieces to fill in the die cavity of the ShAPE apparatus. Two separate runs were performed as described in Table 1 with both the processes' yielding a puck with diameter of 25.4 mm and approximately 6 mm in height. The pucks were later sectioned at the center to evaluate the microstructure development as a function of its depth. Typically in the ShAPE consolidation process; the shearing action is responsible for deforming the structure at interface and increasing the interface temperature; which is proportional to the rpm and the torque; while at the same time the linear motion and the heat generated by the shearing causes consolidation. Depending on the time of operation and force applied near through thickness consolidation can also be attained.

TABLE-US-00002 TABLE 2 Consolidation processing conditions utilized for LWHEA Pressure Process Run # (MPa) Tool RPM Temperature Dwell Time 1 175 500 180 s 2 85 500 600° C. 180 s

[0140] FIGS. 7A-7D show a series of BSE-SEM images ranging from the essentially unprocessed bottom of the puck to the fully consolidated region at the tool billet interface. There is a gradual change in microstructure from the bottom of the puck to the interface where shear was applied. The bottom of the puck had the microstructure similar to one described in FIG. 6. But as the puck is examined moving towards the interface the size of these dendrites become closely spaced (FIG. 7B). The intermetallic phases are still present in the inter-dendritic regions but the porosity is completely eliminated. On the macro scale the puck appears more contiguous and without any porosity from the top to the bottom ¾.sup.th section. FIG. 7C shows the interface where the shearing action is more prominent. This region clearly demarcates the as-cast cast dendritic structure to the mixing and plastic deformation caused by the shearing action. A helical pattern is observed from this region to the top of the puck. This is indicative of the stirring action and due to the scroll pattern on the surface of the tool. This shearing action also resulted in the comminution of the intermetallic particles and also assisted in the homogenizing the material as shown in FIGS. 7C and 7D. It should be noted that this entire process lasted only 180 seconds to homogenize and uniformly disperse and comminute the intermetallic particles. The probability that some of these intermetallic particles were re-dissolved into the matrix is very high. The homogenized region was nearly 0.3 mm from the surface of the puck.

[0141] The use of the ShAPE device and technique demonstrated a novel single step method to process without preheating of the billets. The time required to homogenize the material was significantly reduced using this novel process. Based on the earlier work, the shearing action and the presence of the scrolls helped in comminution of the secondary phases and resulted in a helical pattern. All this provides significant opportunities towards cost reduction of the end product without compromising the properties and at the same time tailoring the microstructure to the desired properties. Similar accelerated homogenization has also been observed in magnesium and aluminum alloys during ShAPE of as-cast materials.

[0142] In as much as types of alloys exhibit high strength at room temperature and at elevated temperature, good machinability, high wear and corrosion resistance, such materials could be seen as a replacement in a variety of applications. A refractory HE-alloy could replace expensive super-alloys used in applications such as gas turbines and the expensive Inconel alloys used in coal gasification heat exchanger. A light-weight HE-alloy could replace aluminum and magnesium alloys for vehicles and airplanes. Use of the ShAPE process to perform extrusions would enable these types of deployments.

[0143] Referring next to FIG. 8, a device for performing shear-assisted extrusion is disclosed with reference to different implementations A, B, and C. In accordance with example implementations, device 100 can be a scroll having a scroll face 110 that includes an inner diameter portion 104 as well as outer diameter portions 106. Accordingly, these 3 scroll faces are shown in accordance with one cross section. As shown and depicted herein, viewed from the face they would have a circular formation. Accordingly, inner diameter portion 104 can extend beyond a surface 110 of outer diameter portion 106. Devices 100 can include apertures 115 arranged within the outer diameter portion and extending through the device. As shown and depicted, inner portion 104, as well as 114 and 116 can be defined by the member extending from surface 110. In accordance with alternative implementations, this member may not occupy all of inner portion 104, but only a portion. In accordance with example implementations, portion 104 can be rectangular in one cross section, and with reference implementation B, portion 114 can be trapezoidal in one cross section, and with reference to implementation C, portion 116 can be conical in one implementation. In each of these implementations, the member can have sidewalls, and these sidewalls can define structures thereon, for example, these structures can be groves and/or extensions that provide for the transition of material away towards the perimeter of the scroll face, which then would direct the material being processed through apertures 115.

[0144] Referring next to FIG. 9, an example scroll face device is depicted in isometric view having inner portion 104 and outer portion 106. Accordingly, the device can include raised portions 140, 142, and/or 144. These portions can provide for a flow of material in predetermined direction. For example, portions 140 can be configured to provide material to within apertures 115, while portions 142 can be configured to provided material to within the same apertures 115, thereby providing for flow of materials toward one another. Portions 144 can be provided for mechanicals needs as the device is utilized.

[0145] In accordance with example implementations, Shear assisted processing and extrusion (ShAPE™) can be used to join magnesium and aluminum alloys in a butt joint configuration. Joining can occur in the solid-phase and in the presence of shear, brittle Mg.sub.17Al.sub.12 intermetallic layers can be eliminated from the Mg—Al interface. The joint composition can transition gradually from Mg to Al, absent of Mg.sub.17Al.sub.12, which can improve mechanical properties compared to joints where Mg.sub.17Al.sub.12 interfacial layers are present.

[0146] As alluded to joining Mg—Al is difficult to perform without forming a brittle Mg.sub.17Al.sub.12 interfacial layer at the dissimilar interface. Example applications for material having been joined using the processes of the present disclosure include, but are not limited to: [0147] Lightweight of rivets and bolts (i.e. Al shank with Mg head or vice versa) [0148] Multi-material extrusion for structural members (tailor welded extrusions) [0149] Mg—Al tailor welded blanks formed by slitting and rolling thin-walled tubes [0150] Corrosion resistant joints due to galvanically graded Mg—Al interface [0151] Dissimilar Mg alloy or Al alloy joint pairs (i.e. AA6061 to AA7075) Referring to FIGS. 10A-10C, different views of a scroll face or die face of an extrusion die tool are shown including cross sectional views. In accordance with example implementations, the die tool can also be configured with or without scrolls in the die face. For example, when processing high temperature materials like steels, Tungsten Rhenium can be used as the die tool material. This material can engage the feedstock material to the extent that friction or shear is provided thereby producing sufficient deformational heating.

[0152] Die tool 200 can include tool sidewalls 202 as well as die face rim 204. In FIG. 10B, die face 208 can have an opening 206 configured to receive and extrude feedstock material mixed and provided during the process. Referring next to FIG. 10C, from opening 206 can extend die face 208. As shown, die face 208 can be extended at an angle in relation to rim 204 or sidewall 202. This angle can be greater than zero degrees as shown in table 3; as an example for tubes fabricated with 12 mm outer diameter and 1 mm and 2 mm wall thickness. In accordance with example implementations this angle can form a portion of the die face, a substantial portion of the die face (for example extending greater than 50% of the radius of the die face), and/or an entirety of the die face from rim 204 to opening 206.

TABLE-US-00003 TABLE 3 Extrusions fabricated with differing degrees of angled scroll faces. Wall Thickness 6 Scroll 1 and 2 mm 4 Scroll, 0 deg 1 and 2 mm 4 Scroll, 14 deg 1 and 2 mm 4 Scroll, 26 deg 1 and 2 mm 4 Scroll, 45 deg 1 and 2 mm

[0153] Referring next to FIG. 11A, in accordance with another example implementation, die 200 can have an outer rim 204 can have a portion that is substantially planar in relation to face 208 thereby providing a substantially normal relationship between face 204 and sidewall 202. As can be seen with respect to FIG. 11C, face 208 can extend at an angle from this rim to opening 206, and this angle can be measured to an imaginary extension 212 as angle 210.

[0154] Referring next to FIG. 12A, a die 200 is shown with sidewalls 202 and rim 204. Referring to FIG. 12B, die 200 can have a recess 214 therein about opening 206. Recess or bore 214 can be contiguous with opening 206. In accordance with example implementations and with reference to FIG. 12C, recess 214 can extend from the face 208 into the die along member or face 216 to a ledge 218, and then to opening 206. Opening 206 has been described in relation to a single extrusion; however, opening 206 can also be a larger opening that can be used in conjunction with a mandrel to provide tubed material as extrusion products, for example

[0155] In accordance with example implementations and with reference to FIGS. 13A-13C, die face 200 can include sidewall 202 and rim 204. As can be seen in FIG. 13B, recess 214 can be defined within die 200, and as shown in FIG. 13C, face 208 can be angled in relation to sidewall 202 and also include recess 214 having side face 216 extending to ledge 218.

[0156] Referring next to FIG. 14A, die face 200 can include sidewall 202 and rim 204. As can be seen, rim 204 can be substantially planar as shown in FIGS. 14B and 14C.

[0157] Referring next to FIGS. 15A-15B, in accordance with example implementations, die 200 can be used to process feedstock material 220. Material 220 can be a single material or a mix of material as shown with # *, and as the ShAPE process proceeds, the material is sheared and/or plasticized to continue to form extrusion product 222. As can be seen, within recess 214 the material can mix. This mixing can provide for a more homogeneous or stable extrusion product 222.

[0158] Referring next to FIG. 16, in accordance with another example implementation, a die 200 is shown processing feedstock material 220. This die can have an angled face as well as shorter extensions extending to a mandrel configuration, wherein mandrel 224 extends between extensions 226. This mandrel configuration with the shorter extensions can provide for a more stable extrusion product 222 in the form of a tube, for example. These extensions can be considered a bearing surface.

[0159] Referring next to FIGS. 17 and 18, an example die 200 is shown having face 208 as well as opening 206. In accordance with example implementations, an extrusion product 222 is shown that can be provided utilizing this die 200. Additionally, the feedstock material can be seen, and the extrudate can be seen in accordance with FIG. 18.

[0160] Referring next to FIG. 19, an example die face is shown having a long bearing surface and without a counterbore or recess 214. As depicted FIGS. 19 and 20 represent two different scroll die configurations. FIG. 19 depicts a die tool having a long bearing surface 1004 and no counterbore 1006, while FIG. 20 depicts a die tool with a counterbore 1002 and short bearing surface 226. As shown in FIG. 20, the die face has a short bearing surface 226 as well as a recess 214 within face 208. In accordance with example implementations and with reference to FIG. 21, utilizing these die faces with the angles and counterbores can provide for reduced extrusion force. As shown in FIG. 22, these die faces can provide reduced motor torque.

[0161] Referring next to FIG. 23, a pair of die faces are compared, one having a flat scrolled die face with a counterbore, and one including a conical die face or angled die face having angle 210 with a counterbore. Utilizing these die faces, reduced force is provided as shown in FIG. 24; reduced torque is provided as shown in FIG. 25; and reduced temperature is provided as shown in FIG. 26.

[0162] Referring next to FIG. 27, utilizing the counterbore 214 and a short bearing surface, a tubular extrusion product having a straight nice finish can be provided as compared to a die face having a longer bearing surface shown above.

[0163] Referring next to FIGS. 28-29, again with a long bearing surface as shown in FIG. 28, the extrusion product is fragile and twisted with a rough surface, whereas the extrusion product prepared using a short bearing surface and a recess is considered fully consolidated and a straight surface.

[0164] Referring next to FIGS. 30-31, a comparison of extrusion products having different millimeters and different degrees is shown ranging from greater than 0 degrees to at least 45 degrees. Referring next to FIGS. 32-34, an example die face is shown in FIG. 32, and an improved die face is shown in FIG. 33 having a flat or planar rim 204 resulting in an improved product as shown in FIG. 34. Referring next to FIGS. 35 and 36, data utilizing the scrolls of the present invention is disclosed.

[0165] In accordance with example implementations, materials can be engaged using the ShAPE technology of the present disclosure. For example, Mg alloy ZK60 can be joined to Al alloy 6061, without forming an Mg.sub.17Al.sub.12 interfacial layer. To accomplish this, the ShAPE™ process can be modified to mix ZK60 and AA6061 into a fully consolidated rod having an Al rich coating as a corrosion barrier. Referring next to FIG. 37, a 5 mm diameter rod extruded from distinct Mg and Al pucks is shown in FIG. 37 (A) with full consolidation shown in FIG. 37 (B), and FIG. 37 (C) shows a gradient in the composition (magenta Al map) between the Al rich surface and rod interior. Analysis showed the critical result that the Mg.sub.17Al.sub.12 β-phase did not exist as an interfacial layer, rather the IMC was highly refined and dispersed throughout the extrusion.

[0166] Referring to FIG. 38, an example solid-phase method for joining Mg to Al extrusions in a butt configuration is shown. In accordance with example implementations, separate Mg and Al billets can be interlocked to form a single billet that will be extruded using the ShAPE process for example. As the die rotates and plunges to the right, an Mg alloy extrusion forms as the material is consumed. The rotating die then penetrates into the interlocking region of the two feedstock materials where Mg and Al are mixed and extruded simultaneously to form the dissimilar joint. Once the die penetrates past the interlocking region of the two feedstock materials, an Al alloy extrusion forms as material continues to be consumed. As shown in FIG. 39, a multi-material rod or hollow-section extrusion can be fabricated absent of a brittle Mg.sub.17Al.sub.12 interfacial layer is shown. The method can be used for rods and/or tubes of varying diameters.

[0167] The geometry of the interlocking region can be tailored to control the composition and transition length of the Mg—Al joint region. The geometric possibilities are many but two examples are shown in FIG. 38; one abrupt (flat pie shaped interface having complimentary portions 162a and 162b that interlock to form interlocking region 163), and one gradual (triangular spokes interface having complimentary portions 164a and 164b that interlock to form interlocking region 165). The most abrupt interface can be achieved with a flat interface between the Mg and Al billets.

[0168] In accordance with at least one implementation, with triangular spoked interlocks 165, the composition of Mg in Al goes from 0% to 100% at a rate depending on the number of spokes and angle of the triangle's vertex. This method has been used to demonstrate a transition length of 37 mm to illustrate the concept. Because the joint is formed by mixing in the solid phase, an Mg.sub.17Al.sub.12 interfacial layer will not form. Rather, a gradient in chemical composition and also possibly grain size will form across the dissimilar interface with the intense shear refining and dispersing any Mg.sub.17Al.sub.12 second phase formations. The composition gradient at the Mg—Al interface has a secondary benefit of also being a galvanically graded interface which can improve corrosion resistance. Referring to FIG. 40 Mg—Al tailor welded blanks are shown, with a galvanically graded interface, made by slitting and rolling tubes. In accordance with example implementations, rolling of 75 mil thick ZK60 tubes down to 3 mil foils can be achieved using these tailor welded blanks. Referring to FIG. 41, using interlocked feed material of AA7075 and AA6061, using the methods of the present disclosure, AA7075 can be butt jointed with AA6061 as shown with an abrupt (pictured) or extended transition length.

[0169] Accordingly, an extrusion process for forming extrusion of a desired composition from a feedstock is provided. The process can include providing feedstock for extrusion, and the feedstock comprising at least two different materials. The process can further include engaging the materials with one another within a feedstock container, with the engaging defining an interface between the two different materials as described herein. The process can include extruding the feedstock to form an extruded product. This extruded product can include a first portion that includes one of the two materials bound to a second portion that can include one of the other two materials.

[0170] Accordingly, the interface between the two materials can interlock the one material with the other material and the geometry of the interlock can define a ratio of the two materials where they are bound. This ratio can be manipulated through manipulating the geometry of the engagement. For example, there could be a small amount of one of the materials entering into a perimeter defined by the other of the two materials, and vice versa. In accordance with example implementations and specific examples, one of the materials can be Mg and the other can be Al. The process can also include where the one material is Mg ZK60 and the other material is Al 6061. Accordingly, there could be one material that has one grade and another that has another grade. For example, the material can be AA7075 and the other material can be AA6061. In accordance with example implementations, these billets can be part of the feedstock and the billets can be interlocked.

[0171] The extrusion feedstock materials may have a geometry that defines a ratio of the two materials when they are extruded as bound extrusions. The feedstock materials can be aligned along a longitudinal axis, and according to example implementations this can be the extrusion axis. The interlock of the billets can reside along a plane extending normally from the axis, and accordingly, the plane can intersect with both materials.

[0172] In order to improve the formability of magnesium sheet materials, the inventors believe that the grain sizes should be less than 5 microns and/or a weakened texture is desirable. It has been demonstrated that the novel Shear Assisted Processing and Extrusion (ShAPE) technology can not only attain the aforementioned microstructure but also help with the alignment of the basal planes (i.e. texture). This technology can also reduce the size and uniformly distribute the second phase particles, which are believed to impede the formability of sheets. In accordance with example implementations, extruded tubes of Mg can be slit open and rolled into the sheet. Extruded tubes of magnesium (ZK60 alloy) using the ShAPE process can be provided which can be 50 mm in diameter and 2 mm in wall thickness, or another diameter and wall thickness. These tubes can be slit open in a press and then rolled parallel to the extrusion axis, for example.

[0173] Referring next to FIG. 42, in particular embodiments, Mg sheets can be provided that are not common in mass produced vehicles, for example. The production of these sheets can include the use of rolling of ShAPE produced and open extruded tubes. In accordance with example implementations, and with reference to FIG. 42, an example rolling mill 130 is shown. In accordance with example implementations, rolling mill 130 can have conveyer 132 but have a sheet 134 of a first thickness and after passing through mill 130, the sheet 134 can be a sheet 136 of a second thickness. In accordance with example implementations, this rolling can be cold rolling, hot rolling, or twin rolling. ShAPE extrusions such as ShAPE tubing can provide a feedstock for subsequent rolling that can provide differentiated and/or advantageous grain size, second phase size and distribution, and/or crystallographic texture when compared to conventional feedstocks for rolling.

[0174] Referring next to FIG. 43, a series of depictions are shown demonstrating a ShAPE fabricated Mg ZK60 tube and the open tube thickness as well as the rolled tube rolled hot to a desired thickness. In accordance with example implementations, the rolled tube can be annealed between passes at between 420° C. and 450° C. for 5 minutes, and can be performed without a twin roll casting if desirable.

[0175] Referring next to FIGS. 44A and 44B, in accordance with example implementations and as described herein, these Mg billets such as the ZK60 billet can be produced about a chilled mandrel as disclosed herein, with frictional heat to produce a tube having an extrusion direction and basal planes about that extrusion direction. In accordance with example implementations, these materials can be anisotropic which can make them quite robust.

[0176] Referring next to FIG. 45, a series of passes are shown from zero passes all the way to 16 passes of a Mg sheet. In FIG. 46 a 0.005 inch thickness sheet is shown and demonstrated the flexibility and robustness in the accompanying two figures. In accordance with example implementations and with reference to FIG. 47, reduction per rolling pass has been plotted, and as can be seen, after about 5 rolling passes, the thickness remains uniform, but after 10 rolling passes, there can be a reduction in thickness of up to 60%. Such large reductions per pass are difficult to impossible to achieve with hot rolling of conventional Mg feedstocks intended for subsequent rolling operations.

[0177] Referring next to FIG. 48A, according to an example implementation of the present disclosure, upon ingot formation of an as-cast billet, for example, the as-cast billet can be heated prior to extrusion, or not heated prior to extrusion. As FIG. 48A shows, this series of steps does not include a homogenization step. To the extent it may include homogenization as detailed with reference to FIG. 48B, that homogenization will not be performed to the length and extent that the prior art methods dictate and billet pre-heating in a furnace may be eliminated and accomplished entirely by the ShAPE process.

[0178] Accordingly, the methods of the present disclosure for preparing an extruded product from a solid billet can include providing an as-cast billet for extrusion. These as-cast billets are billets that have not been prepared to remove microfissures, convert phases, homogenize the billet to have a more uniform consistency throughout prior to extrusion. Billets with some amount of stress relief and phase conversion may also be used. To have a uniform consistency, convert phases, and removal of microfissures, the present disclosure provides applying a simultaneous rotational shear and axial extrusion force to the as-cast billet to plasticize the as-cast billet. During this performance of the method, the materials themselves are homogenized and/or plasticized, and the method can include extruding the plasticized as-cast billet with an extrusion die to form an extruded product. As such the metallurgical functions of stress relief, phase conversion, and homogenization may in part, or entirely, be accomplished by the ShAPE process.

[0179] As detailed herein, this can include the ShAPE technology described above. In accordance with an example implementation, the as-cast billet can be heated for approximately 17 hours between about 200° C. and 490° C. without a subsequent homogenization step prior to applying the simultaneous rotational shear and axial force. Additionally, where heat is applied, it can be applied in steps at predefined temperatures for predefined durations of time. For example, the temperature change between two of the steps can be about 260° C., or between two of the steps can be about 30° C. in temperature change, or other temperature differences combinations. Even when applying this heat for this time, the as-cast billet may not be homogenized prior to applying the simultaneous rotational shear and axial extrusion force to the as-cast billet. Accordingly, the as-cast billet can include intermetallic and/or distinct microstructures prior to the application of the rotational shear and axial extrusion force.

[0180] Referring to FIG. 48B, ingot formation can be performed, and then the as-cast billet can be homogenized prior to extrusion with or without pre-heating. For example, the billet can be provided for extrusion, but while maintaining a majority of the billet below 100° C. prior to extrusion, a simultaneous rotational shear and axial extrusion force can be applied to one end of the billet to plasticize the one end of the billet. The plasticized one end of the billet can form an extruded product using the die. The billet itself may be as-cast or it may be homogenized in accordance with prior art techniques. However, the billet itself will not be heated to greater than 100° C. before being extruded. In accordance with example implementations, the billet can be maintained at about ambient temperature prior to starting the extrusion process.

[0181] With regard to FIG. 48C, the ingots can be formed and then extrusion can take place. Accordingly, as shown, ingot formation can provide an as-cast billet complete with microstructures and portions that are non-homogenous, and then provided directly for extrusion utilizing the methods of the present disclosure without stress relief, phase conversion or pre-heating the as-cast billet to a temperature great than 100° C. prior to starting the extrusion process.

[0182] Referring next to FIG. 49A, as is shown, in at least one example implementation a portion of homogenization can be performed but a significant amount of time can be removed. As can be seen, at least 20 hours is removed. FIG. 49B shows an additional thermal treatment sequence where homogenization is also eliminated and only stress relief and phase conversion are needed.

[0183] Referring next to FIG. 50, data of material prepared from AA7075 as-cast billets is provided with ultimate yield and strength, and elongation percentage, and a die temperature as shown when heat treated to the T6 condition after extrusion. As is shown, the die temperature can be as low as approximately 340° C. but can be as high as 480° C. Extrusion below 340° C. is also possible. However, this temperature range does not apply to the entirety of the billet; it only applies to the very end of the billet as it is being extruded and plasticized. Additionally, these methods can be performed on any number of materials, but these example specific materials are AA7075 materials where ASTM and ASM standard values are exceeded for T6 properties. As detailed in this specification, a range of materials can be utilized for these processes and include magnesium, aluminum, and all others listed herein.

[0184] As described above, in a conventional linear force extrusion process, the billet itself is pre-heated in a furnace such as a jet billet log furnace to soften the billet to assist with the plasticization of the billet during extrusion. The present disclosure does not require such billet pre-heating in a furnace, and the only heating taking place occurs at one end of the billet as a result of the heat generated by the extrusion process, while a portion of the remainder of the billet remains at a lower temperature than the die/billet interface, for example.

[0185] Referring next to FIG. 51, an example extruded product is shown which demonstrates the uniformity and surface finish of the product in the as-extruded condition having been extruded from as-cast billets that did not undergo homogenization or billet pre-heating.

[0186] Referring next to FIG. 52, an example extrusion process includes extrusion and solution heating. However, this solution heating is substantially different than the solution heating of the prior art. As can be seen in FIG. 53, the solution heating with aluminum alloy 6063 with T6 heat treatment can include solution heat treating for 1 hour at 530° C. quenching, and then artificially aging at 177° C. for 8 hours. With T5 heat treatment, there is no solution heat treating, and there is no quench, and the artificial aging can take place at 177° C. for less than 8 hours.

[0187] Now it must be noted that typically in the prior art, a requirement of substantially more time is required for the artificial aging. In accordance with example implementations of the present disclosure, peak hardness can be obtained after artificially aging the extruded product for less than 10 hours and in general lower time than is standard and solution heat treat times and temperature below that specified in ASTM standards.

[0188] In effect, the ShAPE process is able to manufacture AA6063 in the T5 condition that has strength properties well above the ASTM and ASM standards for AA6063 in the T5 condition. Strength properties of AA6063 made by ShAPE in the T5 condition exceed the ASTM strength values for AA6063 in the T6 condition and approach the ASM strength properties of AA6063 in the T6 condition. Accordingly, excellent properties are obtained without the need for solution heat treating and quenching when extruding with ShAPE.

[0189] Additionally, these methods can be performed on any number of materials, but these example specific materials are AA6063 materials and near T6 properties can be achieved using the T5 conditions. As indicated in this specification, a range of materials can be utilized for these processes and include magnesium, aluminum, and all others listed herein.

[0190] Referring next to FIG. 53, data is shown that demonstrates the reduction in solution heat treating time and temperature when solution heat treating is performed at 450° C. for 15 minutes by flash annealing, while the conventional ASTM standard is heat treating at 465° C. for 40 minutes. Flash annealing is performed on the extruded product under UV radiation from lamps such as high energy lamps.

[0191] As shown, the ShAPE extruded product can perform as well with lower temperature and time. As shown in FIG. 53, AA7075 Rod extrusion is provided, demonstrating like preparation without the additional time and at a lower temperature.

[0192] Referring to FIG. 54, Rod extrusion for AA6061 is shown that demonstrates a much shorter solution heat treatment time, 530° C. for 15 minutes rather than the ASTM standard of 530° C. for 120 minutes is possible with flash annealing of ShAPE extrusions. As can be seen, that when the solution heat-treatment time has been reduced from 2 hours to 15 minutes at 530° C. by flash annealing that like material hardness is achieved after the same artificial aging time at 530° C. for longer times.

[0193] Referring next to FIG. 55, data for two different extrusion trials is shown that demonstrates the decreasing of artificial aging time using the ShAPE process from 24 hours to 5-10 hours for AA7075 after a typical solution heat treatment of 480° C. for 24 hours for both of the extrusion trials shown. Accordingly, the present disclosure provides for aging the extruded product for approximately 3-10 hours or as contemplated.

[0194] Referring next to FIGS. 56A and 56B, the extrusion is shown in FIG. 56A to go right to aging, and then also in FIG. 56B, solution heat treating and aging can be used as well.

[0195] Referring next to FIG. 57, data is presented that demonstrates the peak hardness of the material can be achieved after 3 hours of aging at 120° C. It must be noted that the ASTM handbook specifies a minimum of 22 hours at 120° C. for peak artificial aging of AA7075. Accordingly, the present disclosure provides methods that can be used to significantly reduce aging. In accordance with example implementations, the present disclosure provides methods that significantly reduce the temperature and energy required and time necessary to prepare satisfactory extrusion products.

[0196] While the largest applications of aluminum alloys is as cast or wrought articles, the powder metallurgy (PM) route has recently been utilized to produce net- or near-net-shape parts. This route is economically competitive for relatively small parts which would otherwise require extensive machining if fabricated from a bulk alloy. Additionally, aluminum PM benefits from more homogenous microstructures than wrought articles, and unique chemistries realized by rapid solidification or mechanical alloying. However, the conventional press-and-sinter approach presents great difficulty for aluminum alloys due to a tenacious oxide layer preventing full powder bonding, resulting in comparatively low strength and ductility. Other more complicated powder densification processes, which typically require multiple steps (canning, degassing, compaction, and extrusion or forging), break the powder oxide layers by severe deformation, thus resulting in near-theoretical density and good mechanical properties.

[0197] Referring next to FIGS. 56A-57, extruded material using the apparatus and/or methods described herein can be utilized without additional costly post extrusion treatment processes, although typical quenching can be employed during the extrusion process. As is shown in FIGS. 56A and 56B, extruded material can be treated with aging and/or solution heating and then aging. The aging process for each of these methods takes a substantial amount of time. As shown in FIG. 57, peak hardness of material extruded using ShAPE can be achieved after 3 hours at 120° C.

[0198] The stock material extruded using ShAPE can include powder material, casting material, and/or flake, powder, or scrap material. The material can be a solid billet or mixture of solid billets. The solid material can include one or more of the materials listed herein.

[0199] The extruded material can have a hardness of at least 155 HV after 3 hours of aging. Additionally, the extruded material may be solution heated and then aged. However, the aging of the extruded material after solution heating is performed for less than 3 hrs.

[0200] Powder metallurgy (PM) of high strength aluminum (Al) alloys typically requires multiple process steps prior to extrusion. In general, compacting powder into a densified billet or canning powder in a sealed container are the primary methods used to ready material for PM extrusion and have endured as the most widely utilized approaches for high strength Al alloys. For powder canning, typical steps include loading powder into a can, degassing, sealing the can, and heating. For powder compaction, typical steps include degassing, hot or cold isostatic pressing, and heating the densified billet. Eliminating any of these steps could make PM more cost effective. The compaction and canning processes have been researched extensively for high strength PM Al alloys.

[0201] Utilizing the apparatus and/or methods of the present disclosure, frictional heating of billet material in substantially powder form (most, if not all of the billet material is in powder form) can be localized to the die face, and spiral grooves, or a flat face without grooves, draw billet material towards the hollow center of the die utilizing (ShAPE). As the powdered billet is consolidated by compressive and shear forces within the deforming material (plasticizing) and frictional heating at the die face and within the deforming material, solid material is extruded. In accordance with at least some embodiments of the disclosure, low extrusion forces are required compared to conventional extrusion. Additionally, by directly creating solid extrudate from loose powder, many of the complicated processing steps necessary for the other methods are eliminated, presenting a scalable method to produce high strength aluminum alloys. These methods can be utilized successfully to extrude magnesium flakes and/or a gas-atomized aluminum alloy powder containing 12.4 wt. % transition metal. The ShAPE process can extrude hollow tubular profiles directly from powder which is not readily possible with conventional powder metallurgy extrusion.

TABLE-US-00004 TABLE 4 Mechanical properties of extruded powder materials (ShAPE and non-ShAPE) Temperature Yield Strength Method (° C.) (MPa) Elongation (%) PM Extrusion Ambient 375-405 4.5-9.0 ShAPE Extrusion Ambient 380 ± 13 15.74 ± 2.5 ShAPE Extrusion 200/300 314/238 9.5/9.4 Testing performed per ASTM B557

[0202] As shown above in Table 4, the ShAPE materials demonstrated superior mechanical properties when compared to non-ShAPE extruded materials. In accordance with example implementations and with reference to FIGS. 58-60, the ShAPE materials improved the mechanical properties of the powdered materials they were manufactured from. For example, all materials were refined with ShAPE to allow for more mechanically strong realignment of elements. This alignment of elements provides superior strengthened matrices as shown.

[0203] Accordingly, methods for preparing an extruded material by shear assisted processing and extrusion from a powder billet are provided. The method can include providing a billet of material in substantially powder form. This powder can be considered a loose powder (unpacked, or noncompacted). The powder can include one or more of Al, Mg, Fe, Si, and/or Zr. The billet material can have a maximum particle size of 100 um, but particle sizes greater than 100 um can be utilized as well. The powder can include an oxide or powder component

[0204] The method can include applying both axial and rotational pressure to the material to deform at least some of the material, and extruding the material to form an extruded material as described herein. Particularly, an extrusion die defining spiral grooves can be used.

[0205] The extruded material include an alloy and/or can have a tensile strength from about 220 MPa to about 360 MPa. Additionally, the extruded material can have a hollow profiles (i.e. hollow tubes that are circular, non-circular, or even have multiple hollow zones), as shown and described herein.

[0206] The ShAPE process can be used to prepare product materials from Al—Mg—Zr powder. The application of ShAPE to high performance aluminum powders can eliminate process steps used during PM extrusion. Specifically, canning, degassing, sealing, charge pre-heating, cold/hot isostatic pressing, extrusion, and decanning used in PM extrusion can be eliminated and replaced by container filling, compaction, and subsequent ShAPE processing. Process parameters (rpm, feed rate, forge force and temperature) can provide for the extrusion of fully consolidated extrudates (extruded material).

[0207] High performance bulk material from aluminum powders that include alloys can be fabricated. By combining the versatility of the ShAPE process and the far-from-equilibrium microstructures of the gas-atomized Al—Mg—Zr Addalloy powders, PM parts can be designed and developed for mass applications from precipitation-strengthened aluminum alloys with outstanding coarsening resistance that have high thermal stability.

[0208] ShAPE can increase extrusion speeds, for example in the preparation of aluminum alloys. The ShAPE process parameters and tooling enable fast extrusion speed for aluminum alloys, which traditionally have been difficult to extrude. Conventional extrusion speed(s) for aluminum alloys in series 2XXX and 7XXX are generally 1-2 meters/minute.

[0209] The ShAPE processes and methods described herein increase extrusion speed(s), which can, in some examples, reduce the cost of 7XXX (7 series), 2XXX (2 series), and other alloy extrusions, aluminum and non-aluminum. The ShAPE process has been advanced for fabrication of AA7075 extrusions at extremely high speed(s) compared to conventional extrusion. For example, a speed of 7.4 meters/minute has been achieved with mechanical properties equal to, or in excess of, properties achieved from slow speed conventional extrusion (i.e., the ASTM B241 standard and/or consistent with the typical values in the ASM handbook).

[0210] Accordingly, methods for preparing extruded material by shear assisted processing and extrusion are provided that can include applying both axial and rotational pressure to stock material to form an extruded material at a rate between 2 and 13 m/min in some implementations, 3 and 13 m/min in others, and 7 and 13 m/min in still others. As described herein, the stock material or billet material can be defined by castings, or chunks of material randomly aligned. This material can be sourced as recycled material and can include Al and/or any of the materials listed herein.

[0211] The methods can include maintaining a temperature of the die face below 420° C.

[0212] The extruded material has a tensile strength between 500 and 580 MPa, a yield strength between 420 and 500 MPa, and/or an elongation % between 12 and 18.

[0213] Homogenized AA 7075 castings were machined into billets having an inner diameter (ID) of 10.1 mm, outer diameter (OD) of 31.8 mm, a length of 100 mm. Extrusions were fabricated using a ShAPE machine manufactured by BOND Technologies capable of 900 kN axial force and torque of 3000 Nm at 500 rpm. The linear speed of tailstock is 0.36 meters/min which gives an extrusion speed of 7.4 meters/min for the extrusion ratio of 20.6, for example. Speeds up to 12.2 meters per minute and beyond have been achieved for 7XXX and 2XXX. In conventional extrusion, a high peak force is required at the beginning of direct and indirect extrusion processes, which is known as the breakthrough force. This is because a given pressure is required to start deforming the material, which drops to a lower pressure once the material starts flowing. This is not desirable because the peak breakthrough force dictates the required capacity of the extrusion press. Lower force means a smaller extrusion press and lower operating cost. The origin of the work is that the research team was trying to keep the force as low as possible to get the highest speed extrusion possible out of the research scale ShAPE machine which is limited to 900 kN.

[0214] Breakthrough force was eliminated by ramping ram speed (generally ramping up) and rotational speed of the die (generally ramping down). In doing so, these parameters are balanced to generate heat sufficient to locally soften the billet material ahead of the die. Because the material that the die encounters is always soft from the very beginning of the stroke, the force gently rises to steady state for shear extrusion. This is in contrast to conventional extrusion where force rises quickly to a peak force as the die encounters cooler material and then reduces to lower the steady state value.

[0215] As can be seen in FIGS. 61 and 62, the initial axial force can be ramped to a steady state axial force, and/or the rotational rpms can be decreased during the ramping. This data is shown with speed, power, and torque data in FIGS. 62-65. Particularly, in these FIGS., as the axial force is decreased, the tool temperature increases.

[0216] Table 5 below provides a list of example alloys and a rating of extrusion difficulty.

TABLE-US-00005 TABLE 5 Alloy Difficulty 1000 77 1100 86 6063 100 3005 106 3003 112 6105 134 4047 128 3105 126 6061 151 5005 154 7004 157 2011 171 3004 180 6082 197 2014 202 5052 229 5056 232 2024 247 5054 265 7150 269 7050 280 5083 281 5182 293 5456 300 7075 316

[0217] In compliance with the statute, embodiments of the invention have been described in language more or less specific as to structural and methodical features. It is to be understood, however, that the entire invention is not limited to the specific features and/or embodiments shown and/or described, since the disclosed embodiments comprise forms of putting the invention into effect. The invention is, therefore, claimed in any of its forms or modifications within the proper scope of the appended claims appropriately interpreted in accordance with the doctrine of equivalents.