METHOD OF AND APPARATUS FOR HOT PRESSING PARTICULATES

Abstract: Articles (11) are formed by hot pressing metal or metallic particulates (12) at temperatures between about the recrystallization temperature and about the solidus temperature for the metal or alloy after first preheating the particulates and the die (14). The particulates are hot pressed for a very short period of time, usually less than five seconds at about 12 tons per square inch or greater to compact and weld the particles together into a wrought metal article (11) having substantially greater tensile strength and a better isotropic strength than a conventional cast or powder metallurgy article of the same metal or alloy. Additionally, the articles (11) can be made with 99+ percent of theoretical density and with substantially no gas porosity. The article's surfaces may be smooth and held to relatively close tolerances with a good uniformity of surface hardness. Articles can be formed using conventional die presses to press articles repetitively without welding of the articles to die walls even when using aluminum particulates. The preferred particulates are substantially larger in size than the conventional powder materials used in powder metallurgy nd appear to be strain hardened during the hot pressing thereof.

Description: METHOD OF AND APPARATUS FOR HOT PRESSING PARTICULATES This invention relates to the formation of precision metal articles from metal or metallic particles and to a method of and apparatus for compacting and -consolidating such particles at elevated pressures and -temperatures. From a commercially significant standpoint, -the use of particulate metals to form articles has been limited principally to aluminum powder or other powder __etallurgy materials and products therefrom. The present invention is directed to expanding the horizons for the ■ use of particulate materials beyond the powder metallurgy technology and beyond the metals commonly used therein to encompass iron, lead, magnesium, copper, molybdenum, •and other materials as well as aluminum. Also, with the present invention, hot pressed particulates are formed into articles with such superior properties that -enable the use of such articles in applications heretQ- fore not thought possible. As will be explained in -greater detail, it is possible to manufacture directly by a hot pressing technique precision parts with sufficient strength, dimensional precision, and surface characteristics that the parts may be used directly or with a minimum of machining operations. The most common and hence proper reference for -the state of the art of forming articles from particu¬ late metal is the art of aluminum powder metallurgy. Typically, the aluminum powder metallurgy process requires the use of pure aluminum metal powder which may be coated with a lubricant and cold pressed in a die to form a green product. Then the green product is sintered for 20 minutes in a protective atmosphere. The sintered ■ product, somewhat distorted, is later repressed or coined in a press to the finished article. The aluminum powder metallurgy article made with such a process is generally brittle and has some porosity and lacks the high tensile -strength of products machined from annealed and forged aluminum bars. On the other hand,, the hot pressing method of the present invention allows the use of either pure metal aluminum or alloy aluminum materials and the use of ■aluminum alloy scrap commonly called "swarf". The use of scrap as a raw material provides a major reduction in the -cost of raw materials for the product. With the hot pressing method of the present invention, aluminum or -aluminum alloy particles may be hot pressed directly and -quickly into a desired shape with precision dimensional -surfaces in contrast to the cold pressing, sintering, and -coining operations used for powdered aluminum metallurgy, as above described. Additionally, it has been found possible to strain harden the particles as they are being hot pressed into' precision dimensioned products to provide increased .mechanical properties more akin to cast-wrought annealed products but without the expense of an annealing process. Some work has heretofore been done with hot pressing of aluminum particles into sheets, as disclosed in U.S. Patent No. 3,076,706. The hot pressing method disclosed therein is substantially different in that different pressure and temperature relationships were used and further in that the sheet.was formed between OM xolls having an opening pass at the ends thereof. More • specifically, the sheet was formed between water-cooled rolls with the temperature of the rolls at the nip being -about one-half the temperature to which the aluminum particles were preheated. Further, the calculated pres¬ sure was about 12,000 psi and the resulting sheet had a generally fibrous character. Typically, the sheet was ' reduced in thickness by cold rolling subsequent to for¬ mation and then annealed and crystallized at about 600°F to obtain the desired physical characteristics for the .sheet. In the present invention, however, the pressures are significantly higher, for example, 12,000 to 100,000 psi and the temperatures employed are higher and result in a non-fibrous product. Grain growth is avoided and the metal article has properties more akin to a wrought- annealed aluminum- article than a cold-worked fibrous -metal article as made in U.S. Patent 3,076,706. Further, products made with the hot pressing technique of the pressing invention may give the appearance of- being annealed although they have not been annealed. The present invention also has a preferred apparatus which has the capability of forming articles with relatively thick cross sections, e.g., 1/2 inch or greater, at elevated temperatures and pressures without the articles welding or otherwise sticking to the die. With the present invention, aluminum particles may be hotpressed in dies made of ordinary tool steel which can withstand the relatively low temperatures of 400° to 600 β C employed in the hot pressing process. The material sticking to the die problem is further alleviated by the use of die lubricants such as graphite or other materials. For the thicker cross-sectional articles, the hot pressing process may employ a two-step or phase compaction in a single die with an initial compaction of the particles to remove substantially the main voids therebetween within a first portion of the die. Preferably, the apparatus vill have an automatic die lubrication system. Further, it has been found that the large particles are preferably agitated or otherwise kept moving while they are being preheated so that they do not agglomerate and will freely mix and pour to fill the cavities in the hot pressing die. " If desired, the heated aluminum particles may be kept in a protective atmosphere within a feed box for the die but the actual pressing may be done in an ambient atmosphere because of the relatively short pressing times used in the compacting operation. Accordingly, the general object of the invention • is to provide a new and improved hot pressed particulate article and to provide a method of and an apparatus fcr manufacturing such an article. A more specific object of the invention is to provide a new and improved wrought article made from -compacted particles of aluminum or aluminum alloys hot pressed at elevated temperatures and pressures to provide a strain hardened product. A further object of the invention is to provide •a method and apparatus which can mold precision products with good mechanical properties from low-cost particulate xaw materials and in time periods of 30 seconds or . less. These and other objects of the invention will become apparent from the following detailed description -taken in connection with the accompanying drawings in -which: FIGURE 1 is a diagrammatic view of an apparatus for practicing the method of hot pressing metal or etal- lie particles into articles in accordance with ' thepresent invention; FIGUEE 2 is a graph illustrating the effect of temperature changes on the thickness differential articles made with the invention? FIGURE 3 is a graph illustrating the effect of a change of temperature on the surface finish of hot pressed articles made in accordance with the invention; FIGURE 4 is a graph illustrating the effect of pressure on the surface finish of the articles made in accordance with the invention; 5 - FIGURE 5 is a graph illustrating the effect of pressure on a Rockwell Hardness differential between different portions of an article made in accordance with . the inventions FIGURE 6 is a graph illustrating the effect of 10 a change in temperature on the Rockwell Hardness for the articles made in accordance with the invention * FIGURE 7 is a graph illustrating the effect of the change of temperature on the ultimate tensile strength of articles made in accordance with the 15. invention ? • FIGURE 8 is a graph illustrating the effect of citanges in pressure on flash thickness for articles made in accordance with the invention; - FIGURE 9 is a graph illustrating the effect on 20 Rockwell Hardness of articles hot pressed at temperatures -below and substantially above the solidus temperature; FIGURE 10 is a graph illustrating the effect on ultimate tensile strength of hot pressing at temperatures below and above the solidus temperature; ■25 FIGURES 11, 12, 13 and 14 are magnified photo¬ micrographs of etched sections of hot pressed articles formed by hot pressing particulates in accordance with the invention; — FIGURE 15 is a magnified photomicrograph of an -30 etched section of a hot pressed article formed by hot pressing magnesium particulates as described in Example 5 hereinafter; FIGURE 16 is a magnified photomicrograph of an etched section of a hot pressed article formed by hot 35 pressing magnesium particulates as described in Example 6 hereinafter; and FIGURE 17 is amagnified pho_cιrdc_-θgraph of an etched section of a hot pressed article formed by hot pressing particulates of copper as described in Example 7 hereinafter. 5 As shown in the drawings for purposes of illustration, articles 11 may be formed by hot pressing heated particles 12 in a hot pressing apparatus having " a heated die 14. The illustrated die comprises a heated die body 16 having an internal cavity 18 which -is filled 10 with preheated particulates from a heated feed means or box 22 in which are stored the preheated particulates. The die may take various shapes and forms but herein is illustrated as having an upper top punch 24 connected to a conventional press for downward movement into_ the die 15 cavity to compress a charge of particulates at a desired pressure and for a given amount of time. A bottom punch .26 is movable upwardly in the die cavity to eject the compacted article 11 from the die cavity. The ejected article may be shifted transversely from the die by a -20 transfer means 28 which may shift the article into a quenching tank 32, if a quenching is desired. In accordance with the present invention, articles 11 formed of hot pressed metal or metallic particulates may be made by a unique hot pressing process 25 with strength and other properties superior to properties obtained from directly cast metals and with properties ■ such as tensile strength greater than those of cast articles and approaching those of wrought articles formed Jby working the cast article. Moreover, the articles 30 appear to have more isotropic tensile strengths than do cast articles of the same metal. The articles appear to be cold worked and annealed to provide a wrought article even though the articles have not been given a conven¬ tional annealing or heat treatment subsequent to the 35 formation thereof. The particulates used in the pre¬ ferred hot pressing process are relatively large as O -compared to powder particles and it is thought that these larger particulates afford sufficient volume of metal to be worked when being consolidated under elevated tempera¬ tures and pressures within a die. It appears although it 5 is not certain that particles are strain hardened when • -deformed and compressed to eliminate the voids there¬ between. The preferred articles are formed with high densities approaching substantially theoretical density. Further, the exterior surfaces of the articles may be 10 smoother and held to closer tolerances than exterior surfaces of cast articles. In accordance with the present invention, •articles 11 can be produced economically and repetitively from the die 14 when using current die presses to hot i5 press articles 11 at relatively high speeds and with materials, such as aluminum or aluminum alloys, which are normally thought to weld themselves to dies or to pre¬ clude the formation of relatively thick cross-sectional articles. •20 __ore specifically and in accordance with the present invention, the preferred method comprises the . -steps of: providing particulates 12 of metal or metal¬ lic alloy (preferably having a surface area to volume xelationship in the range of 3 to 1,000) and being free 25 flowing to fill the die cavity 18, preheating the parti¬ culates (as within the preheat box 22) to a temperature within the range of between about the recrystallization temperature for the metal or alloy and about the solidus temperature for the alloy (i.e., the melting point of 30 the metal) , heating the die cavity 18 to a temperature sufficient to maintain the particulates within said temperature range during a subsequent hot pressing, hot pressing the preheated particulates by the application of sufficient pressure (e.g., 12,000 to 100,000 psi) to 35 consolidate the particulates into a high density article for a. time period of less than 30 seconds while main- ' BUR_46r _ . OMPI ^ - taining the particulates within said temperature range, removing the article 11 from the heated die cavity 18. -The preferred process and articles formed therefrom are made with particulates in the form of particles larger in size than conventional powder particles because such larger' size particles do not tend to sinter weld to each other when preheated and because it is thought that the larger size particles are able to cold work and/or strain harden whereas the very fine powder particles may not. As used herein, the term "particulates" is generic to the preferred larger size particles having (SA V) surface -area to volume relationships in the range of about 3 to 1000 and to the powders, such as aluminum powders, which typically have SA/V relationships of 1500 or larger. Thus, as used herein, the term "particulates" is used in a generic sense to refer to both larger size particles .and the smaller size powders and the term "particles" is used to indicate metal pieces having an SA/V relationship of about 3 to 1000. Metal pieces with SA/V relationships substantially above 1000 will be termed "powders" hereinafter. As used herein, the surface area to volume re¬ lationship is defined by dividing the surface area in square inches by the volume in cubic inches. The rela- tionship will thus be expressed in terms of inches to the 10 "1 power. Of course, a similar division may be •performed for a metric area in square millimeters divid¬ ed by a volume in cubic millimeters. In the preferred method, the products may be compressed with sufficient pressure to obtain a density of about 99% of theoretical density. Further, particles may be heated and hot pressed at about the solution annealing temperature for the metal or alloy and then subsequently age hardened to pro¬ vide a further strengthening of the article. * It is an important aspect of the process that the particles are hot pressed while at a temperature -above their recrystallization temperature and below their melting or solidus temperature for a short period of time (30 seconds or less) and then cooled below the recrystal¬ lization temperature before the grains in the particles 5 can recrystallize and grow or anneal. For example, for aluminum alloy particles, the article may be hot pressed for less than 4 seconds at a temperature above the re¬ crystallization temperature but below the solidus tem¬ perature and removed and cooled quickly below the re- 10 crystallization temperature so as to prevent substantial -grain growth or any substantial annealing. Surprisingly, it has been found that the hot pressed article is hard rather than soft. If one allows the hot pressing tem¬ perature to go above "about the solidus temperature" or 15 above the melting temperature to the extent that a sig¬ nificant portion of the particles attain a liquid state before or during hot pressing, the hardness and tensile strength will be significantly diminished. As used here¬ in, the term "about the solidus temperature" is intended 20 to include temperatures which may be as much as 10% or - -even 20% higher than the theoretical solidus temperature for a given alloy for the reason that at these tempera- rtures slightly above the theoretical or exact "solidus •temperature" for the alloy there is insufficient liquid -25 from the particles present to substantially adversely .-affect the results. __dditionally, articles made with generally ^uniformly shaped and sized particles and hot pressed in accordance with this invention may provide more uniform 30 isotropic properties such as transverse and longitudinal tensile strength than is the case with cast or wrought • -articles of the same metal or alloy. By preheating and then hot pressing uniform particles such as needles or spheres of substantially uniform size, the particles de- 35 form and join to form a uniformly appearing matrix or a lamellar cross section which provides better isotropic OMPI fa -qualities for the article. In contrast to usual porosity found in powder metallurgy articles, the articles 11 may be made with substantially zero porosity and full density, that is, a density equal to about 100% of the theoretical density. These high density articles are also found to be signif¬ icantly more leak-proof to oil or gas than the more po- xous sintered powdered aluminum metallurgy articles or die cast aluminum articles. The microstructure of the article is similar to that of an article that is fully annealed even though no annealing has taken place. The surface characteristics of the articles are very good, being very uniform and highly reproducible as to hardness -and dimensional tolerances. Referring now in greater detail to the pre¬ ferred process, one form of particle which has been -successfully used is a needle-shaped aluminum particle formed by pouring molten aluminum into a perforated ' spin¬ ning cup and using centrifugal- force to snap off particu- late needles emerging from the apertures. A general description of one process for forming aluminum particles is disclosed in U.S. Patent No. 3,241,948. The preferred particles are fairly uniform in size and have a minimum -of oxidation. Aluminum needles having ' lengths ranging from 0.1 to 0.250 inch and a maximum diameter of about 0.015 inch have been used. Apparent densities for the .aluminum needles range from about 1.3 gram/cc for the •coarser needles to 1.1 gram/cc for the finer needles, the latter being close to the apparent density for con- ventional aluminum powder of 1.1 grams per cc. The raw material used to form the aluminum needles may be scrap aluminum which will usually have some alloying metal therein. The scrap (commonly called "swarf") can be cleaned and degreased prior to being melted within a furnace and poured into the perforated rotating cup to be spun out as needles. By spinning at -a constant speed and temperature, the aluminum particles -obtained may be uniform in size and possess a high degree of luster with nearly 100% utilization of the molten aluminum being poured into the cup. Aluminum particles of about 1/4 inch in length have been used successfully. " Other much larger aluminum particles , such as 3/16 inch cubes , also have been hot pressed in accordance. with the method described herein. It is considered that spherical particles may be even more advantageous because of their lower surface area to volume relationship and their good packing and filling characteristics within the ie. The uniformity of particles as to both size and ■shape is preferred to obtain more isotropic qualities for the hot pressed article. . Rather than melting the scrap and reforming the same into acicularly or spherically shaped particles , scrap machine shop drillings or cuttings may be broken up _Ln a hammer mill to the desired size and then hot pressed in the die. That is , the swarf , if small enough in size, may be used directly for the hot pressing process . The particles are preheated to about their hot pressing temperature prior to being inserted into the die cavity 18. Preferably, the particles are preheated . within a means such as a feed box 22 by resistance heaters (rot shown) and an inert hot gas flows through the feed box to prevent substantial oxidation of the particles while in residence in the feed box. Also, the particles may be agitated while in the feed box by sliaking them with a v___ ating means (not shown) to prevent their sticking to one another while in the feed box. Preferably, the particles will be at or slightly warmer than the temperature at which the .subsequent hot pressing occurs to account for any tetrjpeiaturε loss during transfer frαn the feed box into the heated die 14. The very short periods of time to compact the particles and to remove the article from the die and to cool the same below the recrystallization temperature is a key factor not only to the properties obtained for the -BU REA U OMPI > fa WIPO Λ> , ^ - -article itself but also is a key factor in the economics of producing parts cheaper than heretofore. In contrast, the typical time period for sintering powder compact in powder metallurgy is 20 minutes or more and later heat 5 treating operations require hours or fractions of hours. Quenching in water or other liquid will obtain a supersaturated solution and then the article may be allowed to naturally age at room temperature. For example, aluminum alloy particles may be hot pressed 10 quickly and then immediately ejected and quenched. The hot pressed aluminum article may then be allowed to naturally age for four days at room temperature to pro- . vide a T-4 heat treated aluminum article. The aluminum -article may, if desired, be further heat treated to T-6 15 condition by placing the article in a temperature of about 250?F for a period of about 18 hours. For most metals, the number and kinds of alloying agents used for pre¬ cipitation hardening are well known. Although only aluminum has been mentioned specifically as being hardened -20 by precipitation, it is to be understood that other alloyed metals, such as magnesium or steel, may be precipitation hardened. Consideration now will be given in greater detail to the various parameters of temperature, pressure 25 and time for one specific example, namely, aluminum alloys, and other parameters for other metals may be obtained and ascertained. For ~ _uτ.emetal aluminum parti¬ cles, the temperature will not exceed the melting temper¬ ature of 660°C at which some melting of aluminum will 30 occur. Likewise, the temperature will be above the re¬ crystallization temperature for aluminum. For aluminum alloys, the temperature of recrystallization and the solidus temperature will vary with the amount of alloying material. Generally speaking, the temperatures used in 35 the process will be from about a recrystallization temper¬ ature of about 400°C for aluminum alloys to the solidus BUREA 0MP1 , IPO -cαrve temperature of about 600°C. The solution anneal¬ ing temperature will be closer to the solidus curve than the recrystallization temperature for aluminum alloys. Better mechanical properties are obtained when hot pressing aluminum alloy particles at higher tempera¬ tures closer to the solidus temperature because the particles will be more plastic and will consolidate and fill any crevices or fine details in the mold, as will be explained for aluminum alloys being hot pressed at tem- peratures of about 800°F to 900°F, in connection with the graphs of FIGURES 2 to 10, than when hot pressing at lower temperatures, such as 600° to 800°F. That is, it appears that the particles are more plastic and flow and - weld easier when at the higher temperatures than at lower temperatures near the recrystallization temperature. However, it will be recognized that a temperature of about 900°F is still below the solidus temperature and that there is a marked fall-off of properties if the particles are hot pressed at temperatures above the solidus and at which a significant amount of the parti¬ cles have become molten. The ability to hot press the aluminum particles at temperatures of 900 β F or lower for a time period of only several seconds permits the use of dies constructed from ordinary tool steel. This is in contrast to higher cost superalloy metals that must be used for processes in which higher temperatures and longer pressing time -periods at higher temperatures are required. Likewise, because of these low temperatures and because of the relatively short time in the die, the metal particles are not highly oxidized. It is to be understood that particles may be heated in other and various ways from that disclosed herein. Preferably, the heated metallic alloy particles are heated in the box to a temperature and for a sufficient time for the alloy constituents to go into solid solution for a later precipitation hardening. The preferred hot pressing operation is accom¬ plished in ambient atmosphere, but if a reduction in the -oxidation is desired, particularly for ferrous particles heated to higher temperatures, such as 1800 β F, a pro¬ tective atmosphere may be used about the heated particles when being transferred into and while being hot pressed in the die 14. Usually, a vacuum need not be employed at the die, as this adds to the expense of the process, although some conventional hot pressing techniques use a vacuum. When hot pressing ferrous particles at tempera¬ tures of 1800°F or higher, the heated die 14 should be made of more expensive superalloy materials to provide the requisite strength and longevity for the die at these higher pressing temperatures. The temperature ranges for hot pressing other particles may be varied but it is preferred to hot press copper or copper alloy particles at about 600°-800°C. The magnesium particles can be hot pressed at about the same temperatures used for aluminum or aluminum alloy particles. -Generally speaking, the process is preferably isothermal with the die 14 and the particles being pre¬ heated to the hot pressing temperature. This preheating is necessary because the time of hot pressing is usually so short that the articles could not be heated uniformly throughout in the very short period of the pressing time. " Herein, the upper and lower pressing rams were not heated with only the mold walls defining the cavity being pre- heated. Of course, it is possible to heat the rams as well as the mold walls. The hot pressing pressures may be varied depending upon the particles being used and the density desired ' for the product. For aluminum alloy particles, pressures in the range of 12,000 psi to 100,000 psi are sufficient to press the aluminum particles into articles OMP WIP having substantially 100 percent full theoretical den¬ sity. For lower densities, the pressures may be on the lower side. Once full density has been achieved for the -article by application of a given pressure, the applica- tion of additional higher pressures merely serves to cause the article to tend to bind or weld to the side walls of the die. Also, the higher and excessive pres¬ sures force the hot pressed metal further into the die clearance openings and result in greater thicknesses of flash or burrs which will usually be removed. The increase in flash or burr thickness with increases in hot pressing pressure is illustrated in FIGURE 8. The pres¬ sures used for aluminum of about 12,000 to 50,000 psi at temperatures of 950°F or less do not readily damage tool steel dies and the die may be used repetitively for the. production-like manufacture of particles. Aluminum and aluminum alloys have an affinity for welding or alloying themselves to the die walls at elevated temperatures and pressures used in hot pressing or powder metallurgy processing. The walls of the die cavity 18 are lubricated.with a conventional graphite or lubricant to reduce the likelihood of the article adher¬ ing to the die walls. The movement of the particles in the die during hot pressing is considerable as the height of the hot pressed article is about one-half the height of the particles filling the die prior to compaction. A significant movement of the particles along the die wall -during hot pressing has been found to wipe the die lubri¬ cant from the die wall- leaving the die walls generally unprotected during the final pressing portion of the cycle. In accordance with the present invention, the problem of welding or adhering of the hot pressed parti¬ cles to the die wall has been overcome by a multi-step hot pressing method in which an initial and major com¬ paction is made in a first portion of the die and a final higher density consolidation is made in another _tnd second portion of the die. The initial compaction of the particles reduces the fill volume in the die to about the final size for the article with the particles under- going more gross movements and hence- to scraping some of the die lubricant from the die walls. The welding of the article to the non-lubricated areas of the die walls is avoided by shifting the initially and partially consoli¬ dated article in the die to a portion which was not filled with particles and hence not scraped of the die lubricant thereon. Then the final and usually higher pressure is applied in this second portion of the die. The final pressure consolidates the article to its full and final density usually at r- close to theoretical density and the final pressure is usually significantly higher. By way of example only, scrap metal aluminum particles were compacted at 950°F by .very low pressure of 4,000 psi to about 85 percent of. theoretical density and then shifted upwardly into the die cavity where lu— bricant was still present. At this time, the upper die further compacted the particles to 99 percent plus of theoretical density with the particles undergoing rela¬ tively small movement along the die walls during this final 15 percent compaction which takes up most of the internal voids and may be made at about 24,000 psi. The entire process may still be made in under ten seconds with the initial pressure taking only one second or two and the final pressure application likewise taking only one or two seconds. The difference between the one and two-step process of hot pressing is noticeable in that articles made with a one-step process tend to be scored on the outer surface thereof when contrasted with arti¬ cles made with the two-step process. Typical lubricants are graphite or boron nitride. The residue of the lubricant on the outer surface of the articles made by the two-step process may even be advantageous with the lubricant again being used during a subsequent forging in a forging press. By way of example, the following examples will be given for illustrative purposes: Example 1 EC aluminum scrap containing 2 to 3% copper as an impurity was converted into needle-like particles by melting the scrap and pouring it into a spinning cup of 3 inch diameter having holes of 0.052 inch diameter. "EC" aluminum refers to aluminum typically found in elec¬ trical cables as a current-carrying conductor. The mol¬ ten metal was at 1300°F and the cup was spun at 1500 rpm. The needles were cooled and collected. The needles had a good luster. A charge of needles about 0.5 inch in depth was inserted into a split die formed of tool steel con¬ taining a tool body having a cavity opening measuring 1-7/8 inch by 3/8 inch. The die was placed in a stain¬ less steel closed chamber evacuated to 28 inches σf .mer¬ cury and heated to 950°F. At this temperature, the ram was actuated to apply 30,000 psi pressure to the needles for about two seconds. The die was then taken from the chamber and split open and the resulting compacted article having a thickness of abou 0.25 inch was readily removed. The article quickly air cooled at ambient room temperatures to a temperature below the recrystallization temperature. The needles were found to be thoroughly compacted, welded and intermeshed into a unitary article having a density equal to almost 100% of theoretical density. The Rockwell Hardness value varied from R/H 82 to 85 across the various sides of the article. A tensile specimen from the article had an ultimate tensile strength of 21,875 psi and a yield tensile strength of 19,320 psi. The elongation appeared to be about 4.2%. The structure was clean with a precise smooth exterior with virtually no holes therein. When cut in cross section, some elonga¬ tion Of the needles was observed and many fine grains were seen within the individual needles. There was no significant grain growth observed. Example 2 Needles produced as above described in connec- tion with Example 1 were loaded as an 8 gram charge into the lubricated, split, tool steel die having the same size of cavity. Using the same conditions above except that pressure which was increased to 100,000 pounds per square inch, the article was found to have the same exterior and observable properties as above described and tested out to an ultimate yield tensile strength of 21,555 psi; a yield tensile strength of 19,205 psi; elongation of 4.4% and a Rockwell Hardness of R/H 81 to - 83 about the article. There was no"observable grain growth as the axticle had been allowed to cool quickly below its recrystallization temperature after removal from the die. # Example 3 Clean aluminum 7075 machine shop drillings were broken up and loaded into the 1-7/8 inch by 3/8 inch die cavity. An 8 gram charge was heated to 900°F and the preheated swarf particles were hot pressed at. a pressure of 100,000 psi for a period of less than 5 seconds. The ejected article was allowed to air cool immediately to a temperature less than its recrystallization temperature. The compact article was well bonded and had about a 99.1% of theoretical density and an R/H hardness of 94.9. The compact was cleaned by a vibratory cleaner and then ball burnished to a mirror-like finish. Example 4 - Needles of the type set forth in Example 1 were made into 250-300 gram charges and placed into a cylin¬ drical die cavity of about two inches in diameter and about two inches in length. The die and the particles were heated to a temperature of 950°F and then the needles were initiallycompacted at a pressure of 4,000 pounds per square inch for about one second to consoli¬ date into a compact particle having a first predetermined low density, for example, about 85% of theoretical densi¬ ty. The low density cylindrical slug was uniform and almost "loose" in the die with this initially applied pressure principally collapsing-the plastic needles with a gross movementof needles occurring within the die. During this initial hot pressing, no great lubricant re¬ moval from the die walls was seen and no galling appeared to have taken place. This initially hot press slug was removed from the die, the same die relubricated and the low density slug was re-hot-pressed at 950 β F at 48,000 psi for 5 seconds. The article was then allowed to air cool quickly below its recrystallization temperature. The final hot pressed article had become significantly more dense as its density shifted from about 85% to about 100% of full theoretical density. Some of the aluminum ex¬ truded into the die clearance during the second pressure application. However, no die galling or slug scoring was evident after the second hot pressing operation. The article finally produced was generally uniform in appear¬ ance and its Rockwell Hardness R/H was varied by only two points along the sides thereof. Similar size slugs of 2 inches in diameter and up to 2 inches in length have been produced with the initial pressing at 950°F and to 85% theoretical density at 4,000 psi. These slugs were removed from the die and then re-hot-pressed in the same die (now relubricated) with a pressure of 24,000 psi for a period of 5 seconds to produce articles having full density. These articles were also air cooled to below their recrystallization temperature. In addition to the above-described examples, further rectangular bars measuring 1.875 inch x .375 inch x .25 inch dimensions were produced generally in accordance with the procedure set forth in Example 1 and examined to determine the effect of variations of temperature and pressure on the formation of the hot pressed article. Photomicrographs of such further examples produced generally in accordance with Example 1 are shown in FIGURES 11-14. As explained, temperature is the main variable and additional pressure beyond that needed to compact the article to 99% or greater of theo-r retical density is relatively unimportant. Generally, the time period was not varied significantly beyond five seconds with most of the articles being formed in only the time it takes to assure actual application of the pressure indicated, e.g., 15 tsi; 30 tsi; or 50 tsi. In actual production of parts on a commercial scale, the time of application need only be that to apply pressure to consolidate the particles and fill all of the die crevices. It has been found that the particle material # flows better at higher temperatures, for example, 900°F, than at lower temperatures, for example 650 β F. The • plastic flow characteristic is important in order that the particle material fill the spline, crevices, or narrow cavities as well as to eliminate any internal voids within the article so that the article is dense and relatively leak proof when contrasted with the usual powder metallurgy articles. Another outcome of poor plastic flow is failure to provide a uniform thickness throughout the article when hot pressing the flat rectan¬ gular bar specimens. It was found that when forming these bars at 650°F that the thickness variation was as much as .008 inch, as illustrated in the graph shown in FIGURE 2. By increasing the hot pressing temperature, the plasticity of the heated particles increased and the thickness variation was dropped substantially and to almost zero at 925 β F at a pressure of 30 tsi. To provide a better understanding of how the factors of temperature and pressure affected the relative surface finish, the above-described rectangularly-shaped O , A, axticles were made at temperatures of 650°F, 800°F and 950°F, and also at three different pressures, namely, 15 tsi, 30 tsi and 50 tsi. A purely arbitrary scale of 1 to 10 was chosen with a 10 score being given to surfaces which were smooth, flat and generally solid appearing and with the particle outlines being discernible only with . difficulty. At the other end of the scale, a score of 4 or less indicated tht the surface of the rectangular bar was irregular and not smooth and flat with the parti- cle outlines clearly shown. With such poor surface conditions, the particles appear loosely joined rather than fully intermeshed and integrated with one another. Generally speaking, at the lower temperature of 650°F, and particularly at the lower pressures, for example, 15 tsi, the surface finish ratings were low, e.g., 4 and 6, as best seen in the graph of FIGURE 3. At these lower temperatures and pressures, the articles appeared some-, what porous with the needles clearly outlined and not fully meshed together as they are at the higher tempera- ture and pressure. At thehigher t__πaperat_res and pressures of 950°F and 30 tsi plus, the surface finish ratings were 8 to 10; and and the articles appeared, to be fully dense and have zero porosity and have their needles so well integrated that only with some difficulty is it possible to see the outline of the needles, particularly after the articles have been cleaned. If the pressure used is sufficiently high, such .as 30 tsi to 50 tsi, then the surface finish is found to be good, e.g., 8 or greater, even though the temperature is varied from about 650°F to 950°F, as depicted in FIGURE 3. The pressing temperature becomes significant at lower pressures, e.g., 15 tsi, for the reason that the particles will not experience the desired plastic flow at temperatures of less than about 700°F to afford a surface finish of 8 or greater, as depicted in FIGURE 3. Like¬ wise, if a pressing temperature of 650°F is used, good plastic flow is not achieved until a pressure of about 30 tsi is used, as shown in FIGURE 4. Sufficient plas¬ tic flow to provide a good surface finish,- i.e., 8 or more, was obtained at temperatures 650°F to 950°F at the higher pressures of 30 tsi and 50 tsi with the best surface finishes being obtained for the higher pressure of 50 tsi, as depicted in FIGURE 3. Thus, it appears ' that higher pressures and temperatures provide more plas¬ tic flow and more dense articles with the best surface finishes, and this is depicted in FIGURES 3 and 4. At the lowest pressures and temperatures illustrated in FIGURES 3 and 4, the articles appear porous with the particles clearly outlined and not fully meshed together. The Rockwell Hardness may be substantially uniform when the article has been pressed to be sub¬ stantially fully dense. As will be explained in connec¬ tion with FIGURES 5 and 6, the differential of about two to four points for a fully dense, hot pressed article is achieved and this is acceptable commercially. Thus, the graph in FIGURE 5 shows that a Rockwell Hardness spread of less than four is obtainable when hot pressing at 950 β F with pressures of 15, 30 and.50 tsi. Likewise, for articles hot pressed at 800°F, the Rockwell Hardness spread is below five for each of the pressing pressures of 15, 30 and 50 tsi. On the other hand, when the arti¬ cle is not fully dense as when compressed at 10 tsi and at 650°F, the hardness of the article varies substantial¬ ly from one area to another area, as indicated by the differential of 24 between different Rockwell Hardness readings in FIGURE 5. However, at the higher pressure of 50 tsi and a 650°F pressing temperature, the article may be compacted to be fully dense and provide an accept¬ ably uniformly hard product. It has been found that as density of the arti- cle increases, the Rockwell surface- hardness of the article also increases. As shown in the graph of FIGURE 6, when hot pressing at constant pressure of 15 psi and with an increase in temperature of pressing from about 500°F to 950°F, the density of the product increased and the Rockwell R/H increased from about 75 to 85 R/H. The temperature used during the hot pressing has a significant effect on the tensile strength of the article with the higher tensile strengths being obtained for the higher temperature hot pressing operations when using the constant pressure. This is because the product will be more dense with higher temperature pressings if a low and constant pressing pressure, e.g., 15 tsi, is used. When about 100% density is achieved, the articles had ul¬ timate tensile strengths of 22,700 psi for scrap EC alu¬ minum (with 2 to 3% copper as an impurity pickup) needle hot pressed article, as indicated for a 950°F pressing temperature in FIGURE 7. These articles having the 22,700 psi UTS had a 6.4% elongation and appeared to have microstructures of fully annealed parts although they had not been held at elevated temperatures for a time period sufficiently long enough for an annealing operation to have occurred. The above-described graphs were made from data using these EC aluminum articles. Testing of articles made by hot pressing of• 7075 aluminum swarf articles likewise showed increased tensile strengths obtainable with increased temperature until a temperature exceeded "about the solidus tempera¬ ture". More specifically, the ultimate tensile strength increases significantly with an increase in temperature from about 750° to 900°F at 50 tsi. Above 900°F for this alloy, melting of the particles began and this re¬ sulted in a remarkable and significant decline in ten¬ sile strength as shown in FIGURE 10. Specifically, 7075-0 aluminum scrap chips hot-pressed at 900°F and 50 tsi for five seconds had an ultimate tensile strength of 52,000 psi. However, the ultimate tensile .strength dropped to less than 35,000 when these particles were -24- heated to 950 β F and hot-pressed at 50 tsi. The 52,000 psi tensile strength is about 160 percent greater than that of bar stock of 7075-0 aluminum. Looking different¬ ly at the ultimate tensile strength of 52,000 psi, this is about two-thirds that which could be obtained for this alloy after a T-6 full heat treatment which involves a solution heat treating at 850 β F and aging at 250°F for 25 hours. When the particles are heated and compressed at temperatures above about the. solidus temperature at which some of the particles melt, the hardness average drops rapidly and significantly. Thus, swarf of 7075 aluminum " when hot pressed at 50 tsi for two seconds at tempera¬ tures between 900°F to 950°F experiences a rapid drop- off into a range of 95 to 70 average Rockwell E-hardness, as illustrated in FIGURE 9. On the other hand, the Rockwell Hardness average increased substantially with temperature increases from 800°F to 900°F as the arti¬ cles became more dense and hard at the higher tempera- tures u to about the solidus temperature. A photomicrograph of an article formed by hot pressing 7075 aluminum swarf pressed at 900°F at 50 tsi for five seconds is shown in FIGURE 13. The photo¬ micrograph of FIGURE 13 is made of a longitudinal cross section etched at 100 X. A lamellar construction is visible in FIGURE 13 showing the outlines of the swarf particles within which outlines are fine equiaxed grains. Unlike the structures disclosed in U.S. Patent 3,076,706, there is no fibrous character shown in FIGURES 13 or 14 for a metal section. A transverse cross section (not shown) discloses no particular directionality which points up the isotropic property found for these articles. The particle outlines are also visible in the 50 X photomicrograph (FIGURES 11 and 12) of sections taken of articles formed of EC aluminum needle-like particles hot pressed at 950 β F and 15 tsi for five seconds in accordance with the method of the invention. FIGURE 11 is a longitudinal section showing sound struc¬ ture with particles fully inter eshed without holes and FIGURE 12 is a transverse section likewise showing visible outlines as shown in the 200 X etched photo¬ micrograph of FIGURE 14 which is a section of an article formed of hot pressed EC aluminum needle-like particles. It should be noted that for each bf the illus- trated photomicrographs the structures are sound with virtually no holes therein. The matrices appear to be clean. This is in contrast to powder metallurgy compacts which are porous and generally show some holes therein. Sound nonporous articles may be used in pres- surized fluid applications whereas porous and leaking articles cannot be used. For instance, dense, hot pressed articles may be used in hydraulic lines or pneu¬ matic lines which must be relatively leak-proof to the pressurized fluids carried therein. Generally speaking, articles made of aluminum by a sintered powder metal¬ lurgy process or by a die casting process have leaked and have not been used in such applications. By way of example only, hot pressed aluminum test samples having only about a 1/8 inch wall thickness were tested and found to be leak-proof to pressurized hydraulic oil at 2500 psi therein and also to pressurized helium gas at 400 psi therein. Such a leak-proof characteristic along with improved strength characteristics make such hot pressed articles (with or without a subsequent forging into shape) usable in applications heretofore not poss¬ ible with conventional die cast or powder metallurgy parts of aluminum. Most of the work has been done with aluminum or aluminum alloy particles. However, such tests have been run to indicate that other metals can also be hot pressed in accordance with the invention and these metals OMPI include, but are not limited to, magnesium, copper and iron. Further examples will be given for illustrative purposes. Example 5 The substantially pure magnesium was chopped into 1/16 inch to 1/8 inch long pieces with the pieces having a surface area to volume relationship of about 360. The split mold used and described above was used with a charge of about 3.105 grams with magnesium. The particles were preheated to about 900°F and the particles were pressed between the top and bottom rings while placed in a stainless steel closed chamber evacuated to 28 inches of mercury vacuum. Bars were pressed in the preheated die at about 900°F and 24 tsi pressure for " two seconds. The die was then taken from the chamber and split open with the ' compacted article removed and allowed to air cool to ambient room temperature which is below the recrystallization temperature. The surface finish was good. An elongation of 5.2% in 1/4 inch was obtained. The compacted density of about 97.6 and a Rockwell Hard¬ ness on the H scale of 28. A test bar measuring about 1.8 inch in length by .37 inch in width by .15 inch thick¬ ness was pulled and provided an ultimate tensile strength of about 27,200 psi. The structure appeared clean and with virtually no holes therein. When using the same magnesium material and changing only the pressure to 12 tsi, the ultimate ten¬ sile strength was found to be considerably less, namely, 8,960 psi, the hardness 65, and the density 98.9% for a hot pressed magnesium article. FIGURE 15 is a photo¬ micrograph of a section etched at 100 X of the magnesium article pressed at 12 tsi. Example 6 A magnesium wire which appears to be of duplex alloy consisting predominantly of magnesium was also hot pressed to form test bars which measured aboμt 1.8 inches TU O in length by .37 inch in width by .16 inch thickness. The bars were also pressed at 900°F under 24 tsi pressure for two seconds. The wire particles had a surface area to volume relationship of about 50. The particles were preheated to 900°F as was the split die. The resulting test bar had a weight of about 3.1 grams and a volume of 1.8 cc. The bar had a smooth exterior surface. An elon¬ gation of 3.2% in 1/4 inch was obtained. The bar had a density of about 102.1% and a Rockwell B Hardness of about 34. This density value of over 100% was caused by the inclusion of oxide in the article being weighed. The tensile specimen from the article had an ultimate tensile strength of about 12,100 psi. When using the same magnesium wire and hot pressing at 900°F for . 2 seconds but at a lower pressure of 12 tsi, the magnesium hot pressed articles had a density of 98.2%, a hardness of 41, and an ultimate ten¬ sile strength of 3,400 psi. The structure was generally clean with no holes therein being observable, as can be seen in FIGURE 16, which is a photomicrograph from this magnesium hot pressed article. Magnesium particles having a SA/V relationship of about 180 were also hot pressed as described above in connection with Examples 5 and 6 and the articles formed had a good surface finish 8 and Rockwell Hardness of about 67. The ultimate tensile strength was about 12,970 psi. .The article had an elongation of 2.8% in 1/4 inch. When the same magnesium particles having a SA/V relationship of about 180 were pressed at 900°F for 2 seconds but at 12 tsi, the ultimate tensile strength was found to be only about 1,280 versus the 12,970 psi for the article pressed at 24 tsi apparently due to the less complete welding of the particles when hot pressed at the pressure. In other examples, magnesium powders having SA/V relationships of about 3500 were hot pressed at 900°F and 12 tons per square inch pressure. These latter articles made from magnesium powder were too soft having Rockwell Hardness ratings of -3 on the H scale. There was a considerable difference in U.T.S. ranging between 1280 and 9860 psi and it appears that the presence of large amounts of surface oxide and other impurities caused this problem. At 24 tsi, the articles made from powder had a hardness of 95, a density of 105.2, an ultimate tensile strength of 18,630 psi and an elongation of 2.0% in 1/4 inch. Generally speaking, it appears that better results can be obtained by hot pressing particulates at higher pressures, e.g., 24 tons per square inch, and with ~ particulates which are more oxide free than the powders used and described above. When increasing the pressure from 12 tsi to 24 tsi, the ultimate tensile strengths generally increased from by 90% to over 900%, while the hardness and density values did not change appreciably. Turning to the hot pressing of copper, in accordance with the invention, a further example is as . follows: Example 7 Generally spherical pieces of copper shot of substantially pure copper metal having an SA/V relation- ship of about 100 were preheated to about 950°F and the split mold die was likewise heated to 950°F. A charge of particles weighing 24.03 grams was inserted into the die and * pressed at about 50 tsi for a period of about one second at 950 β F. Articles had a surface finish rating of about 7 and these articles had densities of about 96.2%. The hardness on the Rockwell B scale was 23. Test bars havingdimensions of about 1.863 inches in length by 0.381 inch in width by .240 inch in thickness having a volume of about -2.792 cc were pulled. It appears that the copper shot particles had too much oxide and that better results would have been obtained with BVJR OM cleaner copper particles. The oxide appears to make the articles more brittle. Also, it appears desirable to hot press the copper particles at higher temperatures than the 950°F used herein. Furthermore, powders of copper were pressed and were found to give good clean looking structures ' with densities in the range of about 95.7 to 98.7% and Rockwell B hardnesses of 12 to 51. No tensile test data is available for the hot pressed copper arti¬ cles. A cross section is shown in FIGURE 17. It has been found iron powder may also be hot pressed in accordance with the method of the invention. More specifically, preheated carbonyl powders having an SA/V relationship of 50,800 were hot pressed after being preheated to 950°F at 50 tsi for about one second in a die preheated to 950°F. The density obtained was about 95.5 of theoretical full density and the article had a Rockwell hardness on the RC scale of about 48. A tensile specimen weighing about 24,483 grams and having a length of 1.867 inch, a width of 0.380 inch, and a thickness of 0.280 inch was pulled. It appears some excess carbon was picked up in the process making the test specimens ex¬ tremely brittle. The article fractured repeatedly in the test grips of the tensile testing machine; with the gauge length region withstanding pulls of.35,690 psi. A coarser powder of carbonyl having a SA/V relationship of 15,200 was also preheated to 950 β F and was hot pressed in a die heated to 950°F under 50 tsi for one second. The articles formed had a density of about 98.6 of theoretical density and a hardness of. about 13 on the Rockwell C scale. Tensile test bars of about the same size as described above were pulled to a U.T.S. of 96,240 psi which is high for an essentially pure iron article. The results seem to indicate that particles of iron other than carbonyl iron at higher temperatures of about 1800°F to 2000°F would give satisfactory results. -βU RbΛ T OMPI ^ From the work performed, other metal particles such as nickelat 1800 β F to 2000 β F appear to be capable of being hot pressed to form a wrought nickel article with an isothermal heating of the particles and dies. Also, molybdenum and tungsten particles preheated to about 3000°F should be capable of being hot pressed at dies heated to about 3000°F. The pressures used should be in excess of 12,000 tsi and better results should be obtained with higher pressures of about 50,,000 tsi. To withstand such temperatures and pressures, the die materials will have to be built of refractory materials. The time of high pressure application should be less than several seconds in contrast to the long time sintering processes of the prior art in which the pressure was applied for at least several minutes and as much as one- half hour. As used herein, the term "hot pressing" refers to a simultaneous application of heat and pressure over a short period of time as distinguished from a longer term sintering process. Likewise, the hot press- ing process should be distinguished from a rolling process for rolling particles in which the particles are extruded or stretched as they go into and through the nip of the -rollers and from a fibrous structure for the metal s described in the aforementioned patent. The hot pressing method disclosed above may be further implemented by adding other materials to either the particles themselves or to the die cavity. For instance, the cost of metal may be lowered by the addi¬ tion of lower cost filler material to the metal prior to formation of the metallic particles. Preferably, such fillers would have a density close to that of the molten metal into which the fillers are added so as to provide a more homogenous- character to the filled metal particles which are to be later hot pressed. Additional strength can be obtained by adding strengthening materials into the die for incorporation into the article. For example. -31- carbon fibers could be added into the mold in layers or groups for being interlocked into the metallic article thereby providing additional strength to the article. Herein, the carbon fibers would remain elongated to give their maximum strength to the article. It is thought carbon fibers of about 10% to 40% of the volume could be added into the mold and hot pressed suitably. The preferred larger size particles usually provide better results than do smaller size powders as evidenced by the higher tensile strengths as hardness obtained when increasing the aluminum particulate size from SA/V of 1500 down to about 3. The SA/V relation¬ ships disclosed herein are all derived by measuring the nominal diameter in inches, for generally rounded parti- cles, and then calculating the surface area and volume. The numbers for the SA/V relationship all have a unit of 10 inch which has not tteen included herein. Of course, if the measurements are made in the metric system then the numbers defining the particle size range will change and the unit will be 10~^ centimeters. Generally, it will be possible to use powders in the process so long as the powder particulates do not sinter weld when pre¬ heated, this being particularly a problem when trying to use extremely fine aluminum powders; and, so long as one can accept a lesser strength, hardness and/or other property. In some instances, a lesser strength or less hard article is adequate and powders may be used in the process of the present invention and fall within the ambit of some of the claims of the present invention. From the foregoing it will be seen that a new process has been found for the production of wrought metal articles having good strength, close dimensional tolerances, and good surface characteristics. The process is economically attractive in that scrap metals may be used and in that alloy metals, such as aluminum alloys, may be used as well as pure metals for the particles. Further, additives may be added to the metal particles, such as carbon fiber additives, to increase the strength of the article or, in the case of filler additives, to decrease the cost of the metal in the article. The process lends itself to high production from a press and the articles, such as preforms, may be immediately transferred from the hot press for further treating, such as a heat treating or a forging thereof in a forging press, while still hot. On the other hand, the hot articles may be allowed to air cool or be quenched to return quickly below their recrystallization temperature to prevent substantial grain growth that would decrease their hardness and tensile strengths. IjU E OM

Claims: CLAIMS : 1. A method for the manufacture bf hot pressed articles from metal or metallic alloy particles which have been preheated and are pressed in a heated die cavity, said method being characterized by the steps of: providing particles having a dimension in one direction of at least 1,000 microns and having a surface area to volume relationship in the range of between about 3 and about 2,000, preheating the particles to a temperature above the recrystallization temperature for the metal or alloy and close to the solidus temperature for the metal or alloy, heating a " die cavity to a temperature suffi¬ cient to maintain the particles at said temperature close to said solidus temperature during subsequent hot pressing, introducing the heated particles into the heated die cavity, hot pressing the preheated particles in the die for a time period of less than 30 seconds while the particles are heated to a temperature close to said solidus temperature at a sufficient pressure to consolidate the particles into a high density article, and removing the article from said heated die cavity. 2. A method in accordance with Claim 1 includ¬ ing the further steps of hot pressing the preheated particles within said temperature range with sufficient pressure to form an article having a density of at least 99% of theoretical density for the article and cooling the article to a temperature below the recrystallization temperature before substantial recrystallization and grain growth occurs. 3. A method in accordance with Claim 2 in which the hot pressing of the particles comprises an initial low pressure pressing during which the particles are compressed to substantially the final volume for said article followed by higher pressure pressing to the desired density. 4. A method in accordance with Claim 1 in -zhich the metallic particles are aluminum or aluminum alloy particles having at least one cross-sectional ______nsion exceeding 1,000 microns. 5- A method in accordance with Claim 4 in *_______ said particles and said die are each preheated to a ■ temperature in the range of between about 400°C and about 600 β C_ δ_ A process in accordance with Claim 5 in which the pressure applied to compress the heated parti¬ cles to their final density is within the range of be- -tsreen about 12,000 and about 100,000 tsi. 7. A method in accordance with Claim 1 in which the hot pressing of the particles is effected with¬ in a time of less than about 5 seconds. 8. A method in accordance with Claim 1 includ¬ ing the further step of lubricating the walls of said -die before the particles are hot. pressed to prevent * weld¬ ing of the particles or of the article to the side walls of said die cavity. 9. A method in accordance with Claim 1 includ¬ ing hot pressing the particles in ambient atmosphere with¬ out a protective atmosphere -thereabout. 10- A method in accordance with Claim 1 in which said article is removed from said die cavity at a sufficiently high temperature that said article may be -quenched and including the further step of quickly ■ --quenching -the article after removal from said die. 11- A- method in accordance with Claim 1 in -which said hot pressing step consolidates said particles to substantially full theoretical density and with substantially no gas porosity. 12. A method in accordance with Claim 11 in¬ cluding the step of hot pressing the particles at about the solution annealing temperature for the metal or alloy and subsequently age hardening heat treating said article. OMPI A, 13- A method for the manufacture of closely dimensioned articles from a metallic or metallic alloy particulates which are preheated and in a heated die, said method being characterized by the steps of: pre¬ heating the particulates to a temperature within the xange of between about the recrystallization temperature fox the metal or alloy and the solidus for the metal or -alloy, agitating said particulates to keep the same free flowing when heated and fed to a die cavity ' , lubricating the walls of a die cavity, introducing the heated partic¬ ulates into a first portion of said die cavity, hot pressing the particulates in said first portion of said die at a first pressure to substantially compress the paxticulates into an article, shifting the article to -another portion of said die, and pressing the article at a second pressure greater than said first pressure. 14. A method in accordance with Claim 13 wherein said particulates are aluminum or aluminum alloy particles having a minimum dimension in one direction of -at least 1,000 microns and after the pressing step per¬ forming the further step of cooling said article to below said recrystallization temperature before recrystalliza¬ tion and grain growth (annealing) occurs. 15. A method in accordance with Claim 14 in -which said particles and said die are each preheated to a temperature in the range of about between about 400°C and about 600 β C. 2.6 • A wrought metal compact formed from hot pressed metal or metallic particulates with the joined particulates defining a cross section with most of said joined particulates being outlined therein, said compact being characterized by the outlined particulates having grains contained therein iner than said particulates outlined, said particulates being strain hardened and annealed, to form a wrought article without having been subjected to an annealing process, said compact having IJU EAI / - OMPI substantially no gas porosity and a high density, an exterior surface on said compact being smooth and held to relatively close dimensional tolerances and having a relatively constant surface hardness, said compact having tensile strengths being generally isotropic with the transverse tensile strength being close to the longitu¬ dinal tensile strength. 17. A wrought metal compact in accordance with Claim 16 in which-said compact is a precipitation hardened, alloy having solid precipitated solutes. 18. A wrought metal compact in accordance with Claim 16 in which said particulates are particles of aluminum or aluminum alloy having a minimum cross-sec¬ tional dimension in-one direction of at least 1,000 microns and in which said compact has a density sub¬ stantially equal to. theoretical density. 19. A wrought metal compact in accordance with Claim 16 in which said metal or metallic particu¬ lates are selected from a group consisting of aluminum, copper, magnesium, iron, nickel, zinc, molybdenum and tungsten. j- EAt OMPI V_ - W1P0 -.

Inventors: STORCHHEIM S
Applicants: IIT RES INST, IIT RES INSTITUTE
Application year: 1979
Main classification: B22F3
IPC codes: B22F3, C22F1