Consolidation of a Part From Separate Metallic Components

This application is a continuation-in-part of my prior application Ser. No. 633,508, filed July 23, 1984.

This invention relates generally to metal powder consolidation as applied to one or more metallic bodies, and more particularly to joining or cladding of such bodies employing powdered metal consolidation techniques.

As described in U.S. Pat. Nos. 3,356,496 and 3,689,259, it is known to utilize a pressurizing medium consisting of refractory particulate matter and high temperatures to consolidate (or densify) a metallic object. In this approach, the pressure applied by a press is transmitted through a hot ceramic particle bed to the hot preformed part having a density less than that of its theoretical density. The pressurization of the part occurring in all directions causes voids, gaps or cavities within the part to collapse and heal, the part being densified to a higher density which may be equal to its theoretical density.

Conventional powder metallurgy techniques are limited to the production of parts having shapes that can be produced by closed die pressing in forming of the powder preform. Attempts to produce more complex shapes having 100% density have required the use of lengthy canning procedures to protect the part from the pressurizing gas. Another approach to powdered metal consolidation utilizes preforms requiring no canning in HIP (i.e. hot isostatic pressing) yet it is limited to the shapes that can be produced by powder pressing in a die. In all cases, the preform consolidation takes place in a gas pressurized autoclave (HIP) which, as mentioned earlier, is suitable for consolidation or products whose properties are not sensitive to long time exposures to high temperatures.

It is seen, therefore, that development of a practical powdered metal process able to consolidate 100% dense shapes, too complex to produce by die pressing, utilizing short time high temperature exposure and without the need for canning would satisfy a need existent in the metal forming industry. Such a process would also meet the need for substantially lower parts costs. Prior patents relating to the subject of isostatic pressing of metal workpieces teach that if the parts being consolidated, or to be joined, have cavities or cracks or clearances between the pieces accessed by the pressurizing gas, complete densification can not take place. Parts to be consolidated or joined must, therefore, be isolated from the pressurizing gas by an impermeable casing.

It is a major object of the invention to provide a process or processes meeting the above needs, and otherwise providing unusual advantages as will appear. Joining and cladding processes to be described do not require canning or casings which can be extremely expensive. Further novelty exists in the use of fugitive organic binders and volatile solvents to apply a layer of metallic powders over the surface openings of the voids or clearances between the pieces to be joined or to be clad. Major objectives include the provision of:

1. Methods of joining two or more metallic objects with the object of making a bigger and more complexly shaped shaped object,

2. methods of cladding a metallic object with a layer of another metallic material with or without a layer of third material between the two,

3. a method of combinining two or more metallic and ceramic objects as in 1 and 2 above and afterward chemically removing the ceramic to provide a predesigned cavity.

The basic method of consolidating metallic body means in accordance with the invention includes the steps:

(a) applying to the body means a mixture of

(i) metallic powder

(ii) fugitive organic binder

(iii) volatile solvent

(b) drying the mixtures, and

(c) burning out the binder and solvent at elevated temperature,

(d) and applying pressure to the powdered metal to consolidate same on the body means.

The third mixture may be applied to the body means by dipping, painting or spraying; the body means may have cladding consolidated thereon by the above method; body means may comprise multiple bodies joined together by the consolidated powder metal in the mixture; one or more of the bodies to be joined may itself be consolidated at the same time as the applied powder metal in the mixture is consolidated; and the consolidation may take place in a bed of grain (as for example ceramic particulate) adjacent the mixture.

Further, one of the bodies may comprise a drilling bit core on which cladding is consolidated; and/or to which another body (such as a nozzle or cutter) is joined by the consolidation technique; and one of the bodies may comprise a stabilizer sleeve useful in a well bore, and to the exterior of which wear resistant cladding is consolidated, or to which a wear resistant pad or pads are joined by the method of the invention.

The invention is also concerned with provision of cutting elements which are made integral with roller bit cone structure, as by consolidation techniques. As the bit is rotated, the cones roll around the bottom of the hole, each tooth intermittently penetrating into the rock, crushing, chipping and gouging it. The cones are designed so that the teeth intermesh, to facilitate cleaning. In soft rock formations, long, widely-spaced steel teeth are used which easily penetrate the formation.

These and other objects and advantages of the invention, as well as the details of an illustrative embodiment, will be more fully understood from the following specification and drawings, in which:

FIG. 1 is an elevation, in section, showing a two-cone rotary drill bit, with intermeshing teeth to facilitate cleaning;

FIG. 2 is an elevation, in section, showing a milled tooth conical cutter;

FIG. 2a is a cross section taken through a tooth insert;

FIG. 3 is a flow diagram showing steps of a manufacturing process for the composite conical drill bit cutter;

FIGS. 4(a) and 4(c) are perspective views of a conical cutter tooth according to the invention, respectively before and after downhole service use; and

FIGS. 4(b) and 4(d) are perspective views of a prior design hardfaced tooth, respectively before and after downhole service;

FIGS. 5(a)-5(d) are elevations, in section, showing various bearing inserts employed to form interior surfaces of proposal conical cutters; and

FIG. 6 is an elevation, in section, showing use of powdered metal bonding layer between a bearing insert and the core piece;

FIGS. 7 and 8 show process steps;

FIG. 9 is a side elevation showing a drill bit to which wear resistant cladding has been applied and to which nozzle and cutter elements have been bonded;

FIG. 10 is a side elevation of a stabilizer sleeve processed in accordance with the invention;

FIG. 11 is a horizontal section through the FIG. 10 sleeve;

FIG. 12 is an enlarged view showing a part of the FIGS. 10 and 11 sleeve;

FIG. 12a is a fragmentary view;

FIG. 13 is a section showing joining of two bodies.

In FIG. 1, the illustrated improved roller bit cutter 10 processed in accordance with the invention includes a tough, metallic, generally conical and fracture resistant core 11. The core has a hollow interior 12 and defines a central axis 13 of rotation. The bottom of the core is tapered at 14, and the interior includes multiple successive zones 12a, 12b,12c and 12e concentric to axis 13, as shown. An annular metallic radial (sleeve type) bearing layer 15 is carried by the core at interior zone 12a to support the core for rotation. Layer 15 is attached to annular surface 11a of the core, and extends about axis 13. It consists of a bearing alloy, as will appear.

An impact and wear resistant metallic inner layer 16 is attached to the core at its interior zones 12b-12e, to provide an axial thrust bearing; as at end surface 16a. A plurality of hard metallic teeth 17 are carried by the core, as for example integral therewith at the root ends 17a of the teeth. The teeth also have portions 17b that protrude outwardly, as shown, with one side of each tooth carrying an impact and wear resistant layer 17c to provide a hard cutting edge 17d as the bit cutter rotates about axis 13. At least some of the teeth extend about axis 13, and layers 17c face in the same rotary direction. One tooth 17' may be located at the extreme outer end of the core, at axis 13. The teeth are spaced apart.

Finally, a wear resistant outer metallic skin or layer 19 is on and attached to the core exterior surface, to extend completely over that surface and between the teeth 17.

In accordance with an important aspect of the invention, at least one or two layers 15, 16 and 19 consists essentially of consolidated powder metal, and preferably all three layers consist of such consolidated powder metal. A variety of manufacturing schemes are possible using the herein disclosed hot pressing technique and the alternative means of applying the surface layers indicated in FIG. 2. It is seen from the previous discussion that surface layers 15, 16 and 19 are to have quite different engineering properties than the interior core section 11. Similarly, layers 16 and 19 should be different than 15, and even 16 should differ from 19. Each of these layers and the core piece 11 may, therefore, be manufactured separately or applied in place as powder mixtures prior to cold pressing. Thus, there may be a number of possible processing schemes as indicated by arrows in FIG. 3. The encircled numbers in this figures refer to the possible processing steps (or operations) listed in below Table 1. Each continuous path in the figure, starting from Step No. 1 and ending at Step No. 15, defines separate processing schemes which, when followed, are capable of producing integrally consolidated composite conical cutters.

A list of major processing steps which may be included in the processing:

1. Blend powders.

2. Cold press powder to pre-form green interior core piece 11 (see FIG. 2 for location), which includes teeth 17.

3. Cold press and sinter or hot press powder to pre-form, less than fully dense, core piece 11. Sintering or hot pressing can usually be done at a preferred temperature range 1800.degree. F. to 1250.degree. F. If sintered, typical sintering times may be 0.5 to 4 hours depending on temperature.

4. Forge or cast fully dense core piece 11.

5. Apply powdered hard metal compound skin 19; i.e., by painting, slurry dipping or cold spraying a hard metal powder mixed with a fugitive organic binder and a volatile solvent.

6. Place tungsten carbide inserts 17c on teeth faces.

7. Apply thrust-bearing alloy powder layer 16; i.e., by painting, slurry dipping or cold spraying an alloy-binder mixture as in Step 5 above.

8. Apply powdered radial bearing alloy 15 in the core piece; i.e., by painting, slurry dipping or cold spraying an alloy-binder mixture as in Step 5 above.

9. Apply powdered radial blaring alloy 15 in the cold piece; i.e., by painting, slurry dipping or cold spraying an alloy-binder mixture as in Step 5 above.

10. Place wrought, cast or sintered powder metal radial bearing alloy 15 in the core piece 11.

11. Bake or dry to remove binder from powder layers 15, 16 and/or 19. Drying may be accomplished at room temperature overnight. If slurry applied layers are thick the preform may be baked in non oxidizing atmosphere at 70.degree.-300.degree. F. for several hours to assure complete volatilization of the volatile portion of the binder.

12. Hot press to consolidate the composite into a fully dense (99+ of theoretical density) conical cutter. Typically, hot pressing temperature range of 1900.degree.-2300.degree. F. and pressures of 20 to 50 tons per square inch may be required.

13. Weld deposit radial-bearing alloy 15 in the densified cone.

14. Final finish; i.e., grind or machine ID profile, finish grind bearings, finish machine seal seat, inspect, etc.

The processing outlined include only the major steps involved in the flow of processing operations. Other secondary operations that are routinely used in most processing schemes for similarly manufactured products, are not included for sake of simplicity. These may be cleaning, manual patchwork to repair small defects, grit blasting to remove loose particles or oxide scale, dimensional or structural inspections, etc.

All of the processing steps are unique, as may easily be recognized by those who are familiar with the metallurgical arts in the powder metals processing filed. Each scheme provides a number of benefits from the processing point of view, and some of which are listed as follows:

(1) All assembly operations; i.e., painting, spraying, placing, etc., in preparing the composite cutter structure for the hot-pressing operation (Step No. 12 in Table 1) are performed at or near room temperature. Thus, problems associated with thermal property differences or low strength, unconsolidated state of the composite cone prior to hot densification, are avoided. Repair work, geometrical or dimensional control, and in-process handling are greatly simplified.

(2) Application of powdered metal or alloy or metal compound surface layers, using volatile binders, such as cellulose acetate, corn starch and various distilled products, provide sturdy powder layers strongly held together by the binding agent, thus adding to the green strength of the total unconsolidated cone structure. This makes it easy to control surface layer thickness, handling of the assembly in processing and provides mechanical support for the carbide inserts.

(3) Low-temperature application of aforementioned surface layers avoids pitfalls associated with high-temperature spraying of powders.

(4) The proposed schemes in every case produce a near-net-shape product, greatly reducing the labor-intensive machining operations required in the conventional conical cutter production.

Various sections of the cone cross-section have been identified in FIG. 2, each requiring different engineering properties to best function in service. Consequently, materials for each section should be selected separately.

Interior core piece 11 should be made of an alloy possessing high strength and toughness, and preferably require thermal treatments below 1700.degree. F. (to reduce damage due to cooling stresses) to impart its desired mechanical properties. Such restrictions can be met by the following classes of materials:

(1) Hardening grades of low-alloy steels (ferrous base) with carbon contents ranging nominally between 0.1 and 0.65%, manganese 0.25 to 2.0%, silicon 0.15 to 2.2%, nickel to 3.75%, chromium to 1.2%, molybdenum to 0.40%, vanadium to 0.3% and remainder substantially iron, total of all other elements to be less than 1.0% by weight.

(2) Castable alloy steels having less than 8% total alloying element content; most typically ASTM-Al48-80 grades.

(3) Ultra-high strength steels most specifically known in the industry as: D-6A, H-11, 9Ni-4Co, 18-Ni maraging, 300-M, 4130, 4330 V, 4340. These steels nominally have the same levels of C, Mn, and Si as do the low-alloy steels described in (1) above. However, they have higher contents of other alloying elements: chromium up to 5.0%, nickel to 19.0%, molybdenum to 5.0%, vanadium to 1.0%, cobalt to 8.0%, with remaining substantially iron, and all other elements totaling less than 1.0%.

(4) (Ferrous) powder metal steels with nominal chemistries falling within: 79 to 98% iron, 0-20% copper, 0.4 to 1.0 carbon, and 0.4.0% nickel.

(5) Age hardenable and martensitic stainless steels whose compositions fall into the limits described in (3) above, except that they may have chromium up to 20%, aluminum up to 2.5%, titanium up to 1.5%, copper up to 4.0%, and columbium plus tantalum up to 0.5%.

In all cases, the core piece mechanical properties should exceed the following:

130 ksi ultimate tensile strength

80 ksi yield strength

5% tensile elongation

15% reduction in area

10 ft-lb (izod) impact strength

Wear-resistant exterior skin 19, which may have a thickness within 0.01 to 0.20 inch range, need not be uniform in thickness. Materials suitable for the cone exterior include:

(1) A composite mixture of particles of refractory hard compounds in a binding metal or alloy where the refractory hard compounds have a micro-hardness of higher than 1,000 kg/mm.sup.2 (50-100 g testing load), and a melting point of 1600.degree. C. or higher in their commercially pure forms, and where the binding metal or alloy may be those based on iron, nickel, cobalt or copper. Examples of such refractory hard compounds include carbides, oxides, nitrides and borides (or their soluble mixtures) of the T, W, Al, V, Zr, Cr, Mo, Ta, Nb and Hf.

(2) Specialty tool steels, readily available in powder form, having large amounts of strong carbide formers such as Ti, V, Nb, Mo, W and Cr, and a carbon content higher than 2.0% by weight.

(3) Hardfacing alloys based on transition elements Fe, Ni, or Co, with the following general chemistry ranges:

(4) Wear-resistant intermetallic (Laves phase) materials based on cobalt or nickel as the primary constituent and having molybdenum (25-35%), chromium (8-18%), silicon (2-4%) and carbon 0.08% maximum.

Thrust-bearing 16 may be made of any metal or alloy having a hardness above 35 R.sub.c. They may, in such cases, have a composite structure where part of the structure is a lubricating material such as molybdenum disulfide, tin, copper, silver, lead or their alloys, or graphite.

Cobalt-cemented tungsten carbide inserts 17c cutter teeth 17 in FIG. 2, are to be readily available cobalt-tungsten carbide compositions whose cobalt content usually is within the 5-18% range.

Bearing alloy 15, if incorporated into the cone as a separately-manufactured insert, may either be a hardened or carburized or nitrided or borided steel or any one of a number of readily available commercial non-ferrous bearing alloys, such as bronzes, If the bearing is weld deposited, the material may still be a bronze. If, however, the bearing is integrally hot pressed in place from a previously applied powder, or if the insert is produced by any of the known powder metallurgy techniques, then it may also have a composite structure having dispersed within it a phase providing lubricating properties to the bearing.

An example for the processing of roller cutters includes the steps 1, 3, 5, 6, 7, 10, 11, 12 and 14 provided in Table 1. A low alloy steel composition was blended to produce the final chemical analysis: 0.22% manganese, 0.23% molybdenum, 1.84% nickel, 0.27% carbon and remainder substantially iron. The powder was mixed with a very small amount of zinc stearate, for lubricity, and cold pressed to the shape of the core piece 11 (FIG. 2) under a 85 ksi pressure. The preform was then sintered for one hour at 2050.degree. F. to increase its strength.

A slurry was prepared of Stellite No. 1 alloy powder and 3% by weight cellulose acetate and acetone in amounts adequate to provide the desired viscosity to the mixture. The Stellite No. 1 nominal chemistry is as follows: 30% chromium (by weight), 2.5% carbon, 1% silicon, 12.5% tungsten, 1% maximum each of iron and nickel with remainder being substantially cobalt. The slurry was applied over the exterior surfaces of the core piece using a painter's spatula, excepting those teeth surfaces where in service abrasive wear is desired in order to create self-sharpening effect. Only one side of the teeth was thereby covered with the slurry and before the slurry could dry to harden, 0.08" thick cobalt cemented (6% cobalt) tungsten carbide inserts (FIG. 4, a) were pressed into the slurry. Excess slurry at the carbide insert edges were removed and interfaces smoothed out using the spatula.

A thin layer of an alloy steel powder was similarly applied, in a slurry state, on thrust bearing surfaces identified as 16 in FIG. 2. The thrust bearing alloy steel was identical in composition to the steel used to make the core piece, except the carbon content was 0.8% by weight. Thus, when given a hardening and tempering heat treatment the thrust bearing surfaces would harden more than the core piece and provide the needed wear resistance.

An AISI 1055 carbon steel tube having 0.1" wall thickness was fitted into the radial bearing portion of the core piece by placing it on a thin layer of slurry applied alloy steel powder used for the core piece.

The preform assembly, thus prepared, was dried in an oven at 100.degree. F. for overnight, driving away all volatile constituents of the slurries used. It was then induction heated to about 2250.degree. F. within four minutes and immersed in hot ceramic grain, which was also at 2250.degree. F., within a cylindrical die. A pressure of 40 tons per square inch was applied to the grain by way of an hydraulic press. The pressurized grain transmitted the pressure to the preform in all directions. The peak pressure was reached within 4-5 seconds, and the peak pressure was maintained for less than two seconds and released. The die content was emptied, separating the grain from the now consolidated roller bit cutter. Before the part had a chance to cool below 1600.degree. F., it was transferred to a furnace operating at 1565.degree. F., kept there for one hour and oil quenched. To prevent oxidation the furnace atmosphere consisted of non-oxidizing cracked ammonia. The hardened part was then tempered for one hour at 1000.degree. F. and air cooled to assure toughness in the core.

A similarly processed tensile test bar when tensile tested exhibited 152 ksi ultimate tensile strength, 141 ksi yield strength, 12% elongation and 39% reduction of area. Another test bar which was processed inthe same manner as above, except tempered at 450.degree. F., exhibited 215 ksi ultimate tensile strength, 185 ksi yield strenght, 7% elongation and 21% reduction of area. Thus, it is apparent that one may easily develop a desired set of mechanical properties in the consolidated core piece by tempering at a selected temperature.

In another example, powder slurry for the wear resistant exterior skin and the thrust bearing surface was prepared using a 1.5% by weight mixture of cellulose acetate with Stellite alloy No. 1 powder. This preform was dried at 100.degree. F. for overnight instead of 250.degree. F. for two hours, and the remaining processing steps were identical to the above example. No visible differences were detected between the two parts produced by the two experiments.

In yet another example, radial bearing alloy was affixed on the interior wall of the core through the use of a nickel powder slurry similarly prepared as above. Once again the bond between the radial bearing alloy and the core piece was extremely strong as determined by separately conducted bonding experiments.

The term "composite" is used both in the micro-structural sense or from an engineering sense, whichever is more appropriate. Thus, a material made up of discrete fine phase(s) dispersed within another phase is considered a composite of phases, while a structure made up of discrete, relatively large regions joined or assembled by some means, together is also considered a "composite." An alloy composed of a mixture of carbide particles in cobalt, would micro-structurally be a composite layer, while a cone cutter composed of various distinct layers, carbide or other inserts, would be a composite part.

The term "green" in Table 1, line 2, refers to a state where the powder metal part is not yet fully densified but has sufficient strength to be handled without chipping or breakage. Sintering (the same table, line 3) is a process by which powdered (or otherwise) material is put in intimate contact and heated to cause a metallurgical bond between them.

This invention introduces, for the first time, the following novel features to a drill bit cone:

(1) A "high-temperature-short-heating cycle" means of consolidation of a composite cone into a nearly finished product, saving substantial labor time and allowing the use of multiple materials tailored to meet localized demands on their properties.

(2) Application of material layers at or near room temperature, which eliminates thermally-induced structural damage if a thermally-activated process wereto be used.

(3) A "high-temperature-high-pressure-short-time" processing scheme, as outlined in FIG. 3, where time-temperature dependent diffusion reactions are substantially reduced.

(4) A rock bit conical cutter having a hard, wear-resistant exterior skin and an interior profile which may consist of a layer bearing alloy or two different alloys, one for each radial and thrust bearings; all of which substantially surround a high-strength, tough core piece having protruding teeth.

(5) A conical cutter same as in Item (4), but having teeth partially covered on one side with an insert, preferably a cobalt-cemented tungsten carbide insert, which is bonded onto the interior core piece 11 by a thin layer of a carbide-rich hard alloy similar to those used for the exterior skin 19. This is illustrated in FIGS. 4(a) and 4(c), and is intended to provide a uniform, hard-cutting edge to the cutting teeth as they wear in downhole service; i.e., self-sharpening of teeth (see FIG. 4(c). This is to be contracted with problems of degradation of the cutting edge encountered in hardfaced teeth (see FIGS. 4(b) and 4(d))

(6) A conical cutter, as in Item (5), but having interior bearing surfaces provided by pre-formed and shaped inserts prior to hot consolidation of the composite cone. These inserts may be one or more pieces, at least one of which is the radial-bearing piece. Thrust bearing may be provided in the form of a single insert, or two or more inserts, depending on the cone interior design. These variations are illustrated in FIGS. 5(a)-5(d). FIG. 5(a) shows one insert 30; FIG. 5(b) shows a second insert 31 covering all interior surfaces, except for insert 30; FIG. 5(c) shows a third insert 32 combined with insert 30 and a modified second insert 31'; and FIG. 5(d) shows modified second and third inserts 31" and 32".

(7) A conical cutter, as in Item (6), but having interior bearing inserts 33 and 34 bonded onto the interior core piece 11 by a thin layer or layers 33a and 34a of a ductile alloy, as illustrated in FIG. 6.

(8) A conical cutter same as in (5), but interior bearings surface is provided by a powder metallurgically applied layer of a bearing alloy.

FIG. 1 shows a bit body 40, threaded at 40a, with conical cutters 41 mounted to journal pins 42, with ball bearings 43 and thrust bearings 44.

Step 3 of the process as listed in Table I is for example shown in FIG. 7, the arrows 100 and 101 indicating isostatic pressurization of both interior and exterior surfaces of the core piece 11. Note that the teeth 17 are integral with the core-piece and are also pressurized. Pressure application is effected for example by the use of rubber molds or ceramic granules packed about the core and teeth, and pressurized. Step 12 of the process as listed in Table 1 is for example shown in FIG. 8. The part as shown in FIG. 2 is embedded in hot ceramic grain or particulate 102, contained within a die 103 having bottom and side walls 104 and 105. A plunger 106 fits within the cylindrical bore 105a and presses downwardly on the hot grain 102 in which consolidating force is transmitted to the part, generally indicated at 106. Accordingly, the core 11 all components and layers attached thereto as referred to above are simultaneously consolidated and bonded together.

Referring now to FIG. 9, drill bit body 200 (typically of hardened steel) includes an upper thread 201 threadably attachable to drill pipe 202. The lower extent of the body is enlarged and fluted, as at 204, the flutes having outer surfaces 204a on which cladding layers 205 are formed, in accordance with the invention. The consolidated cladding layer 205 may for example consist of tungsten carbide formed from metallic powder, the method of application including the steps:

(a) applying to the body means a mixture of:

(i) metallic powder

(ii) fugitive organic binder

(iii) volatile solvent

(b) drying the mixture, and

(c) burning out the binder and solvent at elevated temperature,

(d) and applying pressure to the powdered metal to consolidate same on the body means.

In this regard, the binder may consist of cellulose acetate, and the solvent may consist of acetone. Representative formulations are set forth below:

Other usable powdered metals include Co--Cr--W--C alloys, Ni--Cr--B alloys; other usable binders include waxes, polyvinyl-butyral (PVB); and other usable solvents include dibutyl phthalate (DPB). Typically formulations are as follows:

FIG. 9 also shows annularly spaced cutters 207, and a nozzle 208 (other bodies) bonded to the main body of the bit 200, by the process referred to above. The cutters are spaced to cut into the well bottom formation in response to rotation of the bit about axis 209; and the nozzle 208 is angled to jet cutting fluid (drilling mud) angularly outwardly toward the cutting zones. Such fluid is supplied downwardly as via the drill pipe 202 and the axial through opening 200a in the bit. Accordingly, this invention can be used to attach various wear resistant or cutting members to a rock drill bit or it may be used to consolidate a rock bit in its totality integral with cutters, grooves, wear pads and nozzles. Other types of rock bits, such as roller bits, and shear bits, may also be manufactured using this invention.

FIGS. 10-12 show application of the invention to fabrication of drill string stabilizers 220 and including a sleeve 221 comprising a steel core 222, and an outer cylindrical member 223 attached to the core, i.e. at interface 224. Powdered metal cladding 225 (consolidated as per the above described method) is formed on the sleeve member 223, i.e. at the sleeve exterior, to define wear resistant local outer surfaces, which are spaced apart at 227 and spiral about central axis 228 and along the sleeve length, thereby to define well fluid circulation passages in spaces 227. Also, other bodies in the form of wear resistant pads 229 are joined (as by the process to the sleeve member 223, and specifically to the spiraling lands 223a). FIG. 12a, for example, shows how the consolidated metal interface 230 forms between a pad 229 (or other metal body) and land 223a (or one metal body). See for example ceramic grain 231 via which pressure is exerted on the mixture (powdered metal and dried binder) to consolidate the powdered metal at elevated pressure (45,000 to 80,000 psi) and temperature (1950.degree. F. to 2250.degree. F.) The powdered metal may comprise hard, wear resistant metal such as tungsten carbide, and steel).

FIG. 13 shows application of the method of the invention to the joining of two (or more) separate steel bodies 240 and 241, at least one of which is less than 100% dense. Part 241 is placed in a die 242 and supported therein. A layer of a mixture (powdered steel, binder and solvent, as described) is then applied at the interface 243 between parts 240 and 241, and the parts may be glued together, for handling ease. The assembly is then heated, (1000.degree. F. to 1200.degree. F.) to burn out the binder (cellulose acetate). Ceramic grain 244 is then introduced around and within the exposed part of body 240, and pressure is exerted as via a plunger 245 in an outer container on cylinder 246. The pressure is sufficient to consolidate the powdered metal layer between parts 240 and 241, and also to further consolidate the part or parts (240 and 241) which was or were not 100% dense. The parts 240 and 241 may be heated to temperatures between 1900.degree. F. to 2100.degree. F. to facilitate the consolidation.

The invention makes possible the ready interconnection and/or cladding of bodies which are complexly shaped, and otherwise difficult to machine as one piece, or clad.

To demonstrate that separately manufactured metal shapes can be joined without canning and without special joint preparation, slugs measuring 3/4 inches in height were prepared and joined. The common approach in these experiments involved the use of a powder metal-cement mixture as disclosed which when applied around the joint allowed the two slugs to be joined to be easily handled during processing.

The first experiment involved the use of two slugs of cold pressed and partially sintered (to 20% porosity) 4650 powder. The dry cut surfaces of the slugs were put together after partial application of 416 stainless steel powder-cementing mixture on the interface. The powder-cement mixture acted as a bonding agent as well as a marker to located the interface after consolidation.

The cementing mixture at and around the joint was allowed to dry in an oven at 350.degree. F. The assembly of two 4650 slugs were then heated in a reducing atmosphere (dissociated ammonia) to 2050.degree. F. for about 10 minutes and pressed in hot ceramic grain using 25 tons/sq. in. load at 2000.degree. F. Visual examination of the joined slugs indicated complete welding had taken place. Microstructural examination showed no evidence of an interface where no 416 powder markers were present, indicating an excellent weld.

A similar experiment without the use of 416 powder as marker at the interface, showed complete bonding of the two 4650 slugs.

In another experiment two wrought slugs of the A1S1 1018 carbon steel were joined by using a layer of 4650 alloy steel powder in between the two pieces. The heating and hot pressing procedure was the same as above. The joint obtained indicated 100% bonding and could easily be located in the microstructure due to the difference in response to etching solution by the two steels.

A Rockwell-C hardness indentation, made under 150 kg load, right on the interface between 1018 and 4650 alloys dramatically demonstrated the strength of the bond between these two materials. No separation occured after the indentation. In fact, a tensile bar fabricated from a bar (formed by joining pressed and partially sintered 4650 and 416 stainless steel slugs) when pulled in tension, broke within the weaker member, 416 stainless, and the joint interface remainder undisturbed. The break occured at 73,400 psi near the annealed tensile strength of wrought 416 stainless steel.

Experiments to date have shown that metal parts having 100% dense structures with wrought metal mechanical properties can be manufactured without canning, by utilizing heating-pressing cycles that last only few minutes. The process is also capable of producing complex shaped parts that cannot be produced by closed die pressing. This can be accomplished through joining of separately produced shapes having the following processing histories:

1. Cold pressed powder preform

2. Cold pressed and lightly sintered powder preform

3. Wrought or cast preform

4. Powder metal coating applied with a cement

Structures highly complex in shapes can be produced through joining of such preforms in any combination.

In addition, each piece being joined may consist of a different alloy. Experiments indicate that there should be no major problems in bonding alloys based on iron including stainless steels, tool steels, alloy and carbon steels. Alloys belonging to other alloy systems, i.e., those based on nickel, cobalt and copper, may also be joined in any combination, provided care is taken to prevent oxidation at the interface.

The joint bond strength appears to be at least equal to the strength of the weakest component of the structure. This is much superior to the joint strengths obtained in any of the conventional cladding/coating processes, i.e., plasma spraying, chemical or physical vapor deposition, brazing, Conforma-Clad process (Trademark of Imperial Clevite), d-gun coating (Trademark of Union Carbide). As a cladding process, therefore, the present invention is superior in terms of interfacial bond strength.

As a joining process, the bond strengths obtainable are comparable to those typically obtained by fusion welding, except that there is practically no dilution expected at the interface due to short time processing cycle, and the low bonding temperatures used. Thus, joint properties obtainable by joining appear superior to even the best (low dilution) fusion welding processes such as laser or electron beam welding.