Classifications

• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES, PROFILES OR LIKE SEMI-MANUFACTURED PRODUCTS OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
  • B21C23/00—Extruding metal; Impact extrusion
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES, PROFILES OR LIKE SEMI-MANUFACTURED PRODUCTS OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
  • B21C23/00—Extruding metal; Impact extrusion
  • B21C23/002—Extruding materials of special alloys so far as the composition of the alloy requires or permits special extruding methods of sequences
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES, PROFILES OR LIKE SEMI-MANUFACTURED PRODUCTS OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
  • B21C23/00—Extruding metal; Impact extrusion
  • B21C23/02—Making uncoated products
  • B21C23/04—Making uncoated products by direct extrusion
  • B21C23/08—Making wire, rods or tubes
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES, PROFILES OR LIKE SEMI-MANUFACTURED PRODUCTS OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
  • B21C23/00—Extruding metal; Impact extrusion
  • B21C23/02—Making uncoated products
  • B21C23/04—Making uncoated products by direct extrusion
  • B21C23/08—Making wire, rods or tubes
  • B21C23/085—Making tubes
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES, PROFILES OR LIKE SEMI-MANUFACTURED PRODUCTS OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
  • B21C23/00—Extruding metal; Impact extrusion
  • B21C23/02—Making uncoated products
  • B21C23/20—Making uncoated products by backward extrusion
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES, PROFILES OR LIKE SEMI-MANUFACTURED PRODUCTS OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
  • B21C23/00—Extruding metal; Impact extrusion
  • B21C23/02—Making uncoated products
  • B21C23/20—Making uncoated products by backward extrusion
  • B21C23/205—Making products of generally elongated shape
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES, PROFILES OR LIKE SEMI-MANUFACTURED PRODUCTS OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
  • B21C23/00—Extruding metal; Impact extrusion
  • B21C23/21—Presses specially adapted for extruding metal
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES, PROFILES OR LIKE SEMI-MANUFACTURED PRODUCTS OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
  • B21C23/00—Extruding metal; Impact extrusion
  • B21C23/21—Presses specially adapted for extruding metal
  • B21C23/218—Indirect extrusion presses
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES, PROFILES OR LIKE SEMI-MANUFACTURED PRODUCTS OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
  • B21C25/00—Profiling tools for metal extruding
  • B21C25/02—Dies
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES, PROFILES OR LIKE SEMI-MANUFACTURED PRODUCTS OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
  • B21C25/00—Profiling tools for metal extruding
  • B21C25/04—Mandrels
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES, PROFILES OR LIKE SEMI-MANUFACTURED PRODUCTS OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
  • B21C26/00—Rams or plungers for metal extruding; Discs therefor

Definitions

• 16/028,173 is also a Continuation-In-Part of and claims priority to U.S. Patent Application Serial No. 14/222,468 filed March 21, 2014 , which claims the benefit of U.S. Provisional Application Serial No. 61/804,560 filed March 22, 2013 , the contents of all of the foregoing are hereby incorporated by reference.
• What is needed is a process and device that enables the production of items such components in automobile or aerospace vehicles with hollow cross sections that are made from materials such as magnesium or aluminum with or without the inclusion of rare earth metals.
• What is also need is a process and system for production of such items that is more energy efficient, capable of simpler implementation, and produces a material having desired, grain sizes, structure and alignment so as to preserve strength and provide sufficient corrosion resistance.
• What is also needed is a simplified process that enables the formation of such structures directly from billets, powders or flakes of material without the need for additional processing steps.
• What is also needed is a new method for forming high entropy alloy materials that is simpler and more effective than current processes. The present disclosure provides a description of significant advance in meeting these needs.
• the present description provides examples of shear-assisted extrusion processes for forming non-circular hollow-profile extrusions of a desired composition from feedstock material. At a high-level this is accomplished by simultaneously applying a rotational shearing force and an axial extrusion force to the same location on the feedstock material using a scroll face with a plurality of grooves defined therein. These grooves are configured to direct plasticized material from a first location, typically on the interface between the material and the scroll face, through a portal defined within the scroll face to a second location, typically upon a die bearing surface. At this location the separated streams of plasticized material are recombined and reconfigured into a desired shape having the preselected characteristics.
• the scroll face has multiple portals, each portal configured to direct plasticized material through the scroll face and to recombine at a desired location either unified or separate.
• the scroll face has two sets of grooves one set to direct material from the outside in and another configured to direct material from the inside out.
• a third set of grooves circumvolves the scroll face to contain the material and prevent outward flashing.
• This processes provides a number of advantages including the ability to form materials with better strength and corrosion resistance characteristics at lower temperatures, lower forces, and with significantly lower energy intensity than required by other processes.
• the extrusion of the plasticized material is performed at a die face temperature less than 150 °C.
• the axial extrusion force is at or below 50 MPa.
• a magnesium alloy in billet form was extruded into a desired form in an arrangement wherein the axial extrusion force is at or below 25 MPa, and the temperature is less than 100 °C. While these examples are provided for illustrative reasons, it is to be distinctly understood that the present description also contemplates a variety of alternative configurations and alternative embodiments.
• this device has a scroll face configured to apply a rotational shearing force and an axial extrusion force to the same preselected location on material wherein a combination of the rotational shearing force and the axial extrusion force upon the same location cause a portion of the material to plasticize.
• the scroll face further has at least one groove and a portal defined within the scroll face.
• the groove is configured to direct the flow of plasticized material from a first location (typically on the face of the scroll) through the portal to a second location (typically on the back side of the scroll and in some place along a mandrel that has a die bearing surface). Wherein the plasticized material recombines after passage through the scroll face to form an extruded material having preselected features at or near these second locations.
• this process provides for a significant number of advantages and industrial applications. For example, this technology enables the extrusion of metal wires, bars, and tubes used for vehicle components with 50 to 100 percent greater ductility and energy absorption over conventional extrusion technologies, while dramatically reducing manufacturing costs. This while being performed on smaller and less expensive machinery that what is used in conventional extrusion equipment. Furthermore, this process yields extrusions from lightweight materials like magnesium and aluminum alloys with improved mechanical properties that are impossible to achieve using conventional extrusion, and can do directly from powder, flake, or billets in just one single step, which dramatically reduces the overall energy consumption and process time compared to conventional extrusion.
• the present technology could find ready adaptation in the making of lightweight magnesium components for automobiles such as front end bumper beams and crush cans.
• deployments of the present invention can drive further innovation and development in a variety of industries such as aerospace, electric power industry, semiconductors and more.
• this technique could be used to produce creep-resistant steels for heat exchangers in the electric power industry, and high-conductivity copper and advanced magnets for electric motors.
• It has also been used to produce high-strength aluminum rods for the aerospace industry, with the rods extruded in one single step, directly from powder, with twice the ductility compared to conventional extrusion.
• the solid-state cooling industry is investigating the use of these methods to produce semiconducting thermoelectric materials.
• the process of the present description allow precise control over various features such as grain size and crystallographic orientation-characteristics that determine the mechanical properties of extrusions, like strength, ductility and energy absorbency.
• the technology produces a grain size for magnesium and aluminum alloys at an ultrafine regime ( ⁇ 1 micron), representing a 10 to 100 times reduction compared to the starting material.
• the crystallographic orientation can be aligned away from the extrusion direction, which is what gives the material such high energy absorption. A shift of 45 degrees has been achieved, which is ideal for maximizing energy absorption in magnesium alloys. Control over grain refinement and crystallographic orientation is gained through adjustments to the geometry of the spiral groove, the spinning speed of the die, the amount of frictional heat generated at the material-die interface, and the amount of force used to push the material through the die.
• ShAPE described technique and device
• FIG. 1a examples of the ShAPE device and arrangement are provided.
• a 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 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.
• 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.
• 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 better 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 and corrosion resistance at the macro level together with increased and better performance.
• This process eliminates the need for additional heating and curing, and enables the functioning of the process with a variety of forms of material including billet, powder or flake without the need for extensive preparatory processes such as "steel canning".
• This arrangement also provides for a methodology for performing other steps such as cladding, enhanced control for through wall thickness and other characteristics.
• 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, 75mil wall thickness).
• the ram force and kf are remarkably low compared to conventionally extruded magnesium where kf ranges from 68.9-137.9 MPa.
• 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.
• the electrical power required to extrude the ZK60-T5 bar and ZK60 cast (2" OD, 750mil wall thickness) tubes is 11.5 kW during the process. This is much lower than a conventional approach that uses heated containers/billets.
• the ShAPE process is significantly different than Friction Stir Back Extrusion (FSBE).
• FSBE Friction Stir Back Extrusion
• a spinning mandrel is rammed into a contained billet, much like a drilling operation. Scrolled grooves force material outward and material back extrudes around the mandrel to form a tube, not having been forced through a die.
• 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.
• 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.
• FIG. 1b An example of an arrangement using a ShAPE device and a mandrel 18 is shown in Figure 1b .
• This device and associated processes have the potential to be a low-cost, manufacturing technique to fabricate variety of materials.
• various mechanical elements of the tool assist to achieve various desired results.
• 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.
• 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 1 PUCKS Alloy Material Class Precursor Form BbTe3 Thermoelectric Powder Fe-Si Magnet Powder Nd2Fe11B/Fe MaQnet Powder MA956 ODS Steel Powder Nb 0.95 Ti 0.05 Fe 1 Sb 1 Thermoelectric Powder Mn-Bi Magnet Powder AlCuFe(Mg)Ti High Entropy Alloy Chunks TUBES Alloy Material Class Precursor Form ZK60 Magnesium Alloy Barstock, As-Cast Ingot AZ31 Magnesium Alloy Barstock AZ91 MaQnesium Alloy Flake, Barstock, As-Cast InQot Mg2Si Magnesium Alloy As-Cast Ingot Mg1Si Magnesium Alloy As-Cast Ingot AZ91- 1, 5 and 10 wt.%AbO3
• 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.
• 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.
• Figures 2a-2c show various views of a portal bridge die design with a modified scroll face that unique to operation in the ShAPE process.
• Figure 2a shows an isometric view of the scroll face on top of the a portal bridge die and
• Figure 2b shows an isometric view of the bottom of the portal bridge die with the mandrel visible.
• 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.
• 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.
• 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.
• 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.
• two grooves are feeding material radially inward toward each port 17 for a total of eight inward feeding grooves 15.
• a perimeter groove 19 on the outer perimeter of the die shown in Figure 2c , is oriented counter to the die rotation so as to provide back pressure thereby minimizing material flash between the container and die during extrusion.
• Figure 2b shows a bottom perspective view of the portal bridge die 12.
• the die shows a series of full penetration of ports 17.
• 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.8) into distinct flow streams has never been done to our knowledge. This arrangement enables the formation of items with noncircular hollow cross sections.
• Figure 3 show a separation of magnesium alloy ZK60 into multiple streams using the portal bridge die approach during ShAPE processing.
• 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.
• ShAPE technique and device 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.
• 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. These two exemplary applications will be discussed on more detail in the following.
• both an axial force and a rotational force are applied to a material of interest causing the material to plasticize.
• 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.
• this process provides a number of advantages and features that conventional prior art extrusion processing is simply unable to achieve.
• 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 a conventional alloys is typically 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.
• the arc melted buttons described in the paragraph above were easily crushed with hammer and used to fill the die cavity/ powder chamber ( Figure 4c ), 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 load set at 85 MPa and at 175 MPa.
• Figure 5a 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 ⁇ m 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 2 Ti. XRD also confirmed a Cu 2 Mg 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 ⁇ m 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.
• microstructures are homogenized by sustained heating for several hours to maintain a temperature near the melting point of the alloy.
• exact points of various phase formations or precipitation is difficult to predict particularly as related to various temperatures and cooling rates.
• 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 conventional processing such as extrusion and rolling and is also detrimental to the mechanical properties (elongation).
• 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.
• 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.
• Table 2 Consolidation processing conditions utilized for LWHEA Run# Pressure (MPa) Tool RPM Process Temperature Dwell Time 1 175 500 180 s 2 85 500 600°C 180 s
• Figures 6a-6d 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 appears to be a gradual change in microstructure from the bottom of the puck to the interface. The bottom of the puck had the microstructure similar to one described in Figure 5 . But as the puck is examined moving towards the interface the size of these dendrites become closely spaced ( Figure 6b ). 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 3/4 th section. Figure 6c 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 Figure 6c and 6d . 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 getting intermetallic particles re- dissolved into the matrix is very high.
• the homogenized region was nearly 0.3 mm from the surface of the puck.
• 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.
• 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.

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