IMPROVED GOLF CLUB AND OTHER STRUCTURES, AND NOVEL METHODS FOR MAKING SUCH STRUCTURES

Abstract: Golf club structures, including club heads (105) and shafts, composed of composites comprised of a matrix of metal, such as an aluminum alloy, or a plastic material and a fiber such as graphite or a ceramic, which may be whiskerized, and which may also be selectively weighted as in the toe and heel of a club head (105), with heavy particles such as tungsten metal (151-152). The club structure may also be surface hardened by applying a coating of fullerenes to a metal club structure and heat treating it to produce a hard coating of metal carbide, preferably by coating a titanium golf club structure with fullerenes and heat treating the coated structure to produce a titanium carbide surface.

Description: IMPROVED GOLF CLUB AND OTHER STRUCTURES, AND NOVEL METHODS FOR MAKING SUCH STRUCTURES BACKGROUND OF THE INVENTION The present invention relates to improvements in the composition and manufacture of golf club heads and golf club shafts, both of which are composed of composites comprised of a metal or plastic matrix and a fiber such as graphite or a ceramic, which may be whiskerized, and which may be selectively weighted with tungsten particles and the like and may also be surface hardened using fullerenes to apply a hard coating such as titanium carbide DESCRIPTION OF THE PRIOR ART Heretofore golf club head materials have consisted of woods, including persimmon, laminates of various woods and woods filled with resins, etc; metals of aluminum, stainless steel, brass, bronze, titanium, various alloys of these and other metals; graphite fiber reinforced plastics of various kinds; and ceramic particle or whisker reinforced metals containing up to 50 volume percent ceramic phases such as described in U.S patent 5, 037, 102 in which the metal is aluminum with a variety of ceramic particles. The golf club shaft heretofore has consisted of monolithic metal alloy tubes such as carbon steel, stainless steels, high alloyed steels, titanium and aluminum alloys and plastic matrix composites reinforced with graphite fiber, boron fiber and various metal wires such as titanium. An ideal golf club material is lightweight, high strength, high hardness; good wear resistance, good impact strength or toughness and high modulus or resistance to bending. The shaft, and especially composite shafts, should have high shear strength and torsional modulus, which is high resistance to torquing or twisting. Present materials do not process the ideal blend of these desired properties. For example, up to 50 v/o ceramic particle reinforced aluminum does not process as high modulus, hardness and wear resistance as desired and that can be achieved with a higher ceramic particle content. Graphite fiber reinforced plastics lack hardness and wear resistance. Graphite fiber reinforced resin shafts without or with boron fibers lack high torsional modulus as well as abrasion resistance. The present invention cures the above-described deficiencies of golf club heads and shafts heretofore in use. The present invention can also be utilized to improve the performance of existing golf clubs through the utilization of many of the materials as an integral part of the existing clubs that includes the category of "irons". OBJECTS AND ADVANTAGES OF PRESENT INVENTION It is an object of the present invention to provide novel and improved golf club structures that overcome the above-described deficiencies of prior art golf club heads and shafts and to provide novel methods of producing such structures It is a further object of the present invention to provide novel methods and structures for improving the performance of existing golf clubs, including both irons and woods as well as shafts It is a still further object of this invention to provide novel methods for making improved golf club structures, characterized by relatively light weight while providing high strength and hardness, enabhng the construction of larger club heads with selective weighting in various sections of the club that can provide unique performance advantages SUMMARY OF THE INVENTION One aspect of the present invention provides improved golf club structures composing one or more of fiber reinforced metals, ceramic particle or whisker reinforced metal matnces, tubular reinforcements, graphite or ceramic fibers with whiskers growing off the fiber as reinforcement for the golf club Another aspect of the invention provides improved golf club structures comprising one or more of the following a carbon matπx with graphite or ceramic reinforcement in particle or fiber form, a graphite or ceramic reinforcement in particle or fiber form with a plastic matπx containing a select elemental or compound additive that forms a carbide or other hard matnx plus when the matπx is pyrolyzed (carbonized) Another aspect of the invention provides improved golf club structures compπsmg one or more of the following hybπde composite containing more than one reinforcement type, such as fiber and particles, and matπx, such as carbon and metal, ceramic or plastic A further aspect of the invention provides improved golf club structure compnsing of multilaminate composites which compnse adjacent layers of matenals such as metal-metal, metal-plastic, metal-wood, metal- ceramic, or metal-composite or which may compnse alternate combinations of layers of plastic composite- ceramic, composite-composite, metal-ceramic-plastic, composite-wood-ceramic, or metal-metal-composite A still further aspect of the invention provides improved golf club and other structures embodying a coating containing carbon in the form of fullerenes ("buckyballs"), such as C^, and higher homologs that functions as a bonding layer along with composite compositions with metals or plastics or when heat treated forms a carbide surface which is harder than the ongmal metal A still further aspect of the invention is achieving enhanced performance through the size and concentration of the constituent components of particle size, fiber size or laminate thickness including combinations thereof A still further aspect of the invention is the concurrence of two matenals integral to each other including ceramic-metal, metal-metal, plastic-ceramic, plastic-metal, metal-composite, plastic-composite and combinations thereof A still further aspect of the invention is the provision of novel methods for making golf club structures involving the infiltration of a matπx matenal such as a metal into a porous array of another mateπal such as ceramic particles or fibers and/or heavy metal particles such as tungsten to achieve special properties such as hardness and weight and/or controlling the weight of the club in specific areas to influence the center of gravity, or expand or lower the "sweet" spot Still further aspects of the invention involve processes for making composite structures, such as golf club heads, works of art and mechanical structures, wherein the preform or reinforcement is a naturally occurring starting product, such as wood, paper, cotton or wool, that contains one or more of a cellulose, semi cellulose or lignin, which is subjected to heat under pyrolizing conditions to form a porous char that is infiltrated with a matrix forming material, such as molten metal, alumina sol gel, or a resin which can be a thermoplastic or thermoset Further novel aspects of this invention include golf club structures comprising the following 1. A golf club that contains more than 50% ceramic phase 1 A golf club that contains a continuous ceramic phase 2 A golf club that contains both a continuous ceramic and metal phase. 3 A golf club consisting of multilayer composites 4 A golf club containing two or more multilayers of wood, metal/intermetallic, ceramics, plastic, composite 5 A golf club containing fiber reinforced metal 6 A golf club containing whiskers in a matrix of metal/intermetallic, ceramic, plastic. 7 A golf club containing fibers and whiskers in any matrix 8. A golf club containing whiskers attached to fibers or particles in any matrix 9 A golf club from a material containing an intermetallic phase 10 A golf club containing carbon or graphite as a reinforcement or matrix 11 A composite golf club in which the reinforcement or matrix contains a form of silicon carbide 12 A golf club or shaft containing a multiplicity of hollow forms 13 A golf club or shaft consisting of a composite made from hollow forms 14 A golf club utilizing a fullerene molecular structure 15 A golf club with a carbide containing alloy composition in its surface 16 Ibid 16 from a fullerene containing precursor 17 A golf club with a diamond-like carbon or diamond coating 18 Ibid 18 from a fullerene-containing precursor 19 A golf club containing a carbide as at least one constituent 20 A golf club utilizing a graphite structure as a monolith or composite, which has its surface, converted to a single or mixed carbide 21 Ibid 21 in which the graphites structure contains whiskers which may or may not be attached to a graphite fiber A carbon-carbon composite reimpregnated with a plastic or metal A golf club contaimng tungsten selectively distnbuted the club head to control center of gravity, which is produced by molten metal encapsulation and/or infiltration A composite golf club head or shaft formed by squeeze casting A composite golf club composition contaimng distnbuted tungsten or other heavy element with a density greater than 10 g/cc formed in-situ to form the golf club in which the tungsten is encapsulated and integral therein A golf club contaimng particularate tungsten which becomes encapsulated and/or infiltrated dunng the club fabπcation process A golf club contaimng sintered ceramic preform bound with a second phase, which is encapsulated in a matnx metal by casting fabπcation process A golf club contaimng an element heavier than the matnx or binder metal which is used to form the club A composite matenal consisting of at least two elements or different matenals compositions mixed together and formed to produce a composite with little to no remaining porosity which is fabπcated into a golf club compπsmg the hitting portion and/or shaft Either composition may be metallic or non-metallic that includes carbon or ceramics which may consist of particularate or fibrous forms with at least one phase of the composite continuous throughout the component One phase may be advantageously concentrated in select portions or areas of the golf club The composite composition may be formed m the absence of any molten phase via solid state reactions, however, m some select cases wherein an intermetallic is formed, a molten phase may be advantageous A molten phase may also be advantageous to encapsulate a non-reactive component such as a heavy element, carbon or ceramic A composite contaimng fullerenes that forms a subcomponent or the entire golf club with the fullerenes in the form of B) fullerenes contaimng soot, as produced, for example, by the Huffman Kratchner process B) refined into select molecular weight from C 60 to C^ C) fullerene nanotubular shapes contaimng singular and multiwalled D) fullerenes of all types mixed with other reinforcements in matπces of plastic, metal or ceramic A golf club subcomponent such as a club face insert or sole produced from multilayers of the same or alternate matenals including alternate soft and hard layers DESCRIPTION OF THE FIGURES Figure 1 is a photomicrograph illustrating the uniform distribution of nanoparticles in a squeeze cast aluminum matrix. Figure 2 is a schematic illustration showing a cut-away side view of a casting set-up suitable for carrying out the process developed in Example 10 for making a shaped metal matrix composite body integrally bound to a piece of metal matrix and suitable for making a golf club or component thereof. Figure 3 is a schematic illustration, generally like Figure 2, showing another set-up suitable for carrying out the process described in Example 11 for making a golf club or component thereof. Figure 4 is a schematic illustration, generally like Figures 2 and 3, suitable for carrying out the process described in Example 12 for making a golf club or component thereof. Figure 5 is a schematic illustration generally like Figures 2-4, suitable for carrying out the process described in Example 13, for making a golf club or component thereof. Figure 6a is a photographic representation illustrating whiskers growing off graphite fibers. Figure 6b is a photographic representation in greater magnification than 6a, showing whiskers growing off a single graphite fiber. Figure 7 is a scanning electron Micrograph (SEM) of A1 2 0 3 whiskers growing off the surface of particles. Figure 8 is a schematic illustration of one form of squeeze casting to form a composite club as described in Example 16. Figure 9 is a representation of a golf club iron as described in Example 22. DETAD ED DESCRIPTION OF THE INVENTION FIBER REINFORCED METALS A hollow cathode plasma sputtering system is utilized to produce metal or metal alloy coatings on select reinforcing fibers to be incorporated in golf club structures. The hollow cathode plasma sputtering system can be used to apply a coating of any desired composition to select fibers. Multilayer coatings can be applied as desired. Fiber materials may be select organic fibers, glass or quartz fibers, ceramic fibers such as oxides (alumina based), carbides (e.g. SiC, B 4 C, etc.), borides (e.g. TiB 2 ), boron, graphite, etc. The fibers are passed in a spread condition through the sputter coater and single or multilayer coatings are applied to a thickness that will provide the desired volume loading when subsequently consolidated. An example of a multilayer coating is with the use of graphite fibers and a bonding or barrier layer such as titanium, molybdenum, zirconium, etc. followed by a matrix coating such as aluminum, magnesium, copper, titanium, steel, etc. In the case of an aluminum matrix the initial coating not only provides bonding between the fiber and matrix but also prevents adverse reaction between aluminum and graphite to form the moisture sensitive aluminum carbide that will degrade the composite. In the case of a copper matrix, a metal such as molybdenum will form a bond with the graphite and alloy with the copper during subsequent diffusion bonding with heat in the consolidation step. The metal-coated fiber is then laid up in the desired fiber architecture for making a golf club component and subjected to heat and pressure to cause the metal to bond into a solid continuous matrix phase. If the fiber is an organic, it must have the thermal stability to permit the consolidation step. Since aluminum and magnesium can be consolidated at relatively low temperatures, they are the most appropriate matrix materials for organic fiber reinforced metal matrix composites. The metal-coated fibers that are molded into a composite golf club structure may be the face of a club, the sole of a club, the entire club head (either "wood" or "iron"), the shaft or the shaft and club molded together as one piece. The ratio of fibers to metal matrix will determine the performance of the club as well as the type of fiber and metal of the matrix. Graphite fibers are lightweight and can be obtained with high strength and stifihess, but generally have relatively poor wear resistance, which is of concern for head materials but generally is not a problem for shaft materials. In contrast, a ceramic fiber possesses excellent wear resistance and hardness, but it is heavier than the graphite. Excellent combinations of matrix and reinforcement materials for a golf club head (wood or iron) as well as a clubface or sole are Matrix Reinforcement Aluminum Graphite Copper Graphite Aluminum Ceramic (oxide or carbide) Copper Ceramic (oxide or carbide) Aluminum Organic Titanium Ceramic (oxide or carbide) Steel Graphite or Ceramic Shaft materials combinations include: Matrix Reinforcement Aluminum Graphite Aluminum Organic Aluminum Ceramic Titanium Ceramic Steel Graphite or Ceramic An alternative to utilizing fibers that are separately formed such as graphite, ceramic or organic, is a fibrous preform can be produced from naturally grown or produced materials comprised of one or more of cellulose, semi-cellulose or lignin An example is plants or wood which contains nature produced fibrous contents Paper is also a fibrous material that has been extracted from wood or plant materials other examples are cotton staple and wood staple These natural fibrous products can be heat treated to remove the low temperature volatiles and produce a charred fibrous remains The heat treatment or pyrolysis temperature should be high enough to remove all water type substance which generally can be achieved at 100°C (212°F), but to produce a char or carboneous residue the pyrolysis temperature should be higher There is no limit to the maximum heat treatment temperature when carried out in an inert atmosphere that prevents the carbon from oxidizing The cellulosly fibrous materials will begin to form carboneous chars in the range of 350°C (662°F) and becomes complete carbon char by 850°C (1562°F) in the absence of air The volatile substance leaves a void in the wood or natural grown material which can be reinfϊltrated with plastics, ceramics and metals After the wood or other natural grown material, or molded paper has been heat treated to produce a char, its flammability has been reduced and it is no longer subject to rotting, termites or other degradation or corrosion When ceramics or metals are reinfiltrated into the charred body the composite is completely fire resistant and is corrosion resistant to virtually all environments The reinfiltration of a plastic, ceramic or metal into a charred preform produces a carboneous reinforced composite with a matnx of the infiltrated matenal The infiltration process can be by known means such as resin transfer molding, sol-gel or organo-metallic precursor for the ceramic matπx and casting a molten metal Vacuum differential transfer is an excellent method of infiltrating the liquid matnx precursor into a charred preform Squeeze casting is particularly advantageous for liquid metals smce it freezes rapidly and does not cause a large temperature πse in the charred preform In the case of aluminum which melts at 660 °C, the preform need not necessarily be heat treated to 660 °C or above in order to infiltrate with aluminum by squeeze casting For example, a wood preform could be charred to 450°C and placed in a squeeze cast die that is preheated up to 450°C Molten aluminum with a superheat of 100° C that is 760 °C could be squeeze cast into the preform wherein the aluminum freezes within seconds and the preform does not expenence a temperature nse much above the 450°C char temperature Of course the wood preform could have been heat treated to a much higher temperature that provides more porosity that will be filled with aluminum In the instant invention wood and cellulose preforms have been charred up to 3000°C (5432°F) and then reinfiltrated with plastics, ceramics and metals Example plastics have been thermoset resins and thermoplastic matenals Ceramics have included oxides, carbides, and nitndes, and mixtures of these produced from sol-gels and metal organic after heat treatment or pyrolysis In the case of metals the light metals such as magnesium and aluminum, casting compositions such as zinc based casting alloys, copper and alloys such as brasses and bronzes, steels, titamum and even the refractory metals can be cast into the pyro zed preforms Other reinforcement mfiltrants can also be utilized such as small particles of ceramics or metals in the charred preforms For example, a nanoparticle suspension can be vacuum infiltrated into the char preform and the earner volatilized followed by infiltration of one of the matπx types such as plastics, ceramics or metals Of course the paniculate can also be earned by the matnx filler matenal This is particularly desirable for a golf club A block of wood may be fashioned to form a golf club, charred and then infiltrated with ceramic particles with a high concentration on the face The preform can then be squeeze cast with a metal such as aluminum, copper or steel alloys and the face is hardened due to the ceramic particles Heavier metals such as tungsten particles can be infiltrated into select portions of the club to provide weighting as desired for performance enhancement The charred natural product can exhibit mechanical properties substantially enhanced over the oπgmal For example wood is not very stiff compared to metals Thus when a metal is infiltrated into the wood char the composite possesses much higher stiffness and also increased strength which is proportional to the metal content and the metal type Thus steel is stiffer than aluminum as well as stronger Ceramics are even stiffer than metals and combinations of metals and ceramics as matπces are of course in between stiffness and strength of each component Thus wood or other natural grown fibrous matenals can be heated to a char that provides a porous fibrous array which can be reinfiltrated with plastics, ceramics and metals to produce a composite that is stiffer and stronger as well as fire resistant and corrosion or degration resistant compared than the oπginal wood Such a composite is an excellent product for structural, artistic and many uses including golf clubs. CERAMIC PARTICLES IN METAL MATRIX Ceramic particles that constitute more than 50 v/o are preformed into the desired reinforcement configuration using an organic binder or consolidated without a binder such as by die pressing or isostatic pressing in soft tooling. The preform is contained within a die cavity configured to form the desired golf club structure that will permit infiltration with a molten alloy. Any organic binder residue from the preform is removed by solvent extraction or thermally and the desired metal alloy is then infiltrated in a molten state into the preformed ceramic particles. After full penetration of the molten metal matrix into the preform, the die is cooled to result in a ceramic particle reinforced metal matrix containing greater than 50 v/o ceramic particles. The shape, size and composition of the ceramic particles can be adjusted to produce composites with very high quality mechanical properties; particularly stiffness, strength, hardness and wear resistance. The metal alloy influences the properties of the composite through its inherent properties as well as its ability to wet the ceramic particle and provide good infiltration into the preform but preventing any adverse interface reactions between the ceramic particle and metal. The concentration of the ceramic phase in the molten metal can be selectively graded to the surface to provide a very hard wear resistant surface. This can also be accomplished through a preferred reaction that occurs during the matrix metal infiltration. A further aspect of the present invention involves treatment of the ceramic preform to cause whiskers to form in the void space between particles that will provide an improved composite for golf club applications. Particles can be ceramic or metallic. In the case of metallic particles, they may react with the matrix to form a new material, such as given in Example 9 described below, that formed titanium aluminide or non-reactive metals such as tungsten. In the latter case, the selective placement, i.e. concentration, of the heavy tungsten can be used to adjust the center of gravity of the club making it heavier in the toe, head, sole, etc. The size of the ceramic hard particles can have a major influence on the properties and performance of the composite. For example, if relatively large particles, that is approximately 20 microns or larger, are used a soft metal matrix can be damaged between particles which is referred to as birnelling. The smaller the ceramic particle, the smaller the distance between particles. However, heretofore it has not been possible to infiltrate a molten metal in highly dense small particle arrays. The force required for infiltration is described by Darcey's law. Using forced metal infiltrating in accordance with one aspect of the present invention, it is possible to infiltrate ceramic particle arrays with particle sizes in the low micron size as well as submicron size also referred to as nanometer size. A composite consisting of 50% or greater of small particle size and particularly in the submicron/nanometer size infiltrated with aluminum by pressure infiltration produces a very hard wear resistance composite surface that does not suffer from birnelhng or damage of the matπx between the particles CONTINUOUS CERAMIC AND METAL PHASE COMPOSITES The metal-ceramic composite discussed below in Examples 10 to 24 have a continuous metal phase and the ceramic phase is discontinuous Another type of metal-ceramic composite is one in which the metal phase and ceramic phase are both continuous The composite of Example 25 has a continuous phase of both the metal and ceramic This type of composite is produced by forming a ceramic preform similar to that descπbed in Examples 10 to 24 After the ceramic particle preform has been produced, it is raised in temperature until sintenng is initiated between the particles Smtenng is continued until a ceramic bond is formed between the particles, but sintenng is stopped before the pores are closed The object is to achieve smtenng between the ceramic particles but to maintain an open pore structure in which the molten metal will be subsequently infiltrated to form the continuous metal phase A sinteπng aid may be used to increase the sinterability of any ceramic and especially the covalent bonded particle matenals such as SiC, Sι 3 N 4 , B 4 C, etc , that otherwise will not self sinter After the ceramic phase is sintered, it will have considerable strength over any non-sintered ceramic phase composite The size of the particles, particle distnbution and the degree of sinteπng can be controlled to achieve the volume fraction of the ceramic phase In general, a particle sintered ceramic which maintains an open pore structure will have a density in the range of about 40 to 90% of theoretical which leaves 60 to 10% metal phase Lower ceramic phase compositions may be obtained through the use of ceramic foams such as reticulated structures or the use of short fiber materials whose packing density can be as low as about 10% and as high as about 60 to 70% Thus, through the use of ceramic phase configuration and the degree of smtenng, the ceramic phase fraction can be controlled over a wide range of about 10% up to about 90% After the ceramic phase has been produced into a continuous sintered body with a remaining open pore structure, molten metal infiltration can be accomplished to produce a continuous metal phase The metal infiltration step for continuous phase ceramic-metal composites, as prepared in Example 25, can be accomplished in the same manner as the continuous metal phase infiltration for Examples 10 to 24 TUBULAR (HOLLOW) REINFORCEMENT COMPOSITES One objective of the present invention is to provide a golf club or shaft that possesses as low a density as possible in order to achieve a desirable size club with a prescnbed weight The weight per unit area or aenal density of any matenal can be lowered with the use of hollow or thin walled matenal An example can be given using a section of a steel golf club shaft If a steel shaft is 0 5 inches diameter with a wall thickness of 0.016 inches, the weight will be 0.08924 lb. per foot. If a small diameter steel tube 0.008 inches diameter with a wall thickness of 0.002 inches were utilized in a thickness of two layers to make up a 0.5 inch diameter larger tube, the calculated weight saving per foot is approximately 41%. If aluminum were used as a bonding agent, or braze to join the small steel tubes into the 0.5-inch diameter steel tube, the weight savings per foot would be reduced to approximately 33%. If the steel tubes were slightly larger than the 0.008 inches with the same wall thickness, the weight savings would be greater and similarly if the steel tubes were slightly smaller, e.g. 0.006 inches with the same wall thickness, the weight savings would be slightly reduced. Greater or lessor weight savings would similarly be achieved with a larger steel tube diameter than 0.5 inches or that tube's wall thickness differing from 0.016 inches thick. The above compares the weight savings of using an array of small steel tubes to replace a solid wall steel tube. The effective stiffness of the array of small steel tubes will be greater than with the single wall steel tube. Lighter weight and increased stiffness is a desirable feature in a golf shaft. The array of hollow steel tubes is also an effective way to reduce the weight of the club itself. Thus, it is possible to produce a golf club utilizing the hollow tube concept for both the club and the shaft. Hollow components other than steel tubes can also be utilized in the golf club or shaft. Other potential hollow articles can be hollow glass fibers, hollow ceramic fibers such as SiC or other carbides, and many oxides, nitrides and borides, and hollow spheres in a variety of materials such as glasses, carbon, ceramics and metals. These hollow articles can be utilized in plastic, metal, ceramic or carbon matrices to produce golf club components that are lighter and stiffer. Polycapillaries can be made in many materials, which are a parallel array of small capillary tubes typically joined to each other. It is possible to arrange polycapillaries in layers in which the direction can be at some angle to the preceding layer such as 45°, 90°, etc. Polycapillaries in lightweight ceramic compositions such as alumina, silicon nitride, etc. can be filled with plastics or metals to form golf club heads or shafts. WHISKERIZED FIBER REINFORCED COMPOSITES One of the major limitations of composites is the shear strength at the matrix reinforcement interface. This is particularly true for fiber reinforced composites. For example, it is well known with glass fiber or graphite fiber reinforced plastics, there is extensive technology required in coupling agents, which enhance bonding between the fiber and the plastic matrix. The quality of a composite is measured in the shear strength, which is in effect the bonding strength between the fiber and matrix. Many if not most design limitations are limited by the shear strength of the composites. And in golf clubs, and particularly the shafts, the torsional modulus and strength are limitations which in part also relate to the bonding between the fiber and matrix. An approach to improve the shear strength of composites no matter the matrix as well as the torsional strength and modulus is to grow whiskers off the surface of graphite or other ceramic fibers. This whisker growth off the surface such as illustrated in Figure 7 provides mechanical attachment as well as a different fiber surface chemistry to enhance the bonding between the matrix and fiber. For example, the shear strength of a plastic or metal matrix graphite fiber composite is generally in the range of a few hundred psi to a very few thousand psi (e.g. 500-2000 psi) but when SiC whiskers are grown on the surface of graphite fibers the shear strength equals the strength of the plastic matrix and in the case of metals can be in the range of 8,000-30,000 psi. In addition, to the enhancement of mechanical properties of whiskerized graphite composites other properties such as wear resistance, hardness, etc. are substantially improved. CARBON MATRIX COMPOSITES Carbon is a very light weight material and is quite wear resistant unless converted to the graphite crystal structure which is a layered structure that is quite soft, lubricating and has poor wear resistance. Carbon as a matrix in composites is typically produced by pyrolyzing a select plastic material or pitch. If the reinforcement is graphite fiber, the composite is referred to as carbon-carbon composites. Typical carbon matrix precursors are pitch and resins such as phenolics. A carbon-carbon composite is generally produced by impregnating a reinforcement such as graphite fibers as well as particularate reinforcements with the carbon precursor followed by pyrolyzing as known in the art to produce carbon as the matrix. Since pitch or resins produce only about 50-65% carbon on pyrolysis, the carbon matrix is porous from the shrinkage and mass loss from the valatities of the carbon precursor. Reimpregnation is generally conducted for two to five times to produce a near theoretically dense carbon matrix (carbon-carbon composites). In the case of Example 30 described below, when the phenolic resin is impregnated into the reinforcement (graphite fiber, ceramic fiber or particularate without or with whiskers) the resin may contain very small particles (preferably submicron in diameter). When the resin is pyrolyzed as given in Example 30, the particle can form a carbide that will provide a very hard wear resistant matrix material that is excellent for a golf club head. Examples of suitable particles are metals that form carbides such as boron, silicon, tantalum, niobium, molybdenum, tungsten, etc., or compounds such as B 2 0 3 , SiO, Si0 2 , Mo0 3 , etc., that react with the carbon to form carbides. The light carbides such as B 4 C and SiC are most desirable since a lightweight golf club head is desired. The remaining porosity of the carbon matrix can be infiltrated with a metal to form a hybride composite such as aluminum, silicon, copper, etc. MULTILAMINAR COMPOSITES Since a golf club head must sustain substantial impact (possess high toughness) as well as process high hardness and wear resistance, another type of composite other than fiber or particle reinforced composite can meet these demands. In accordance with the present invention, multilaminar composites which consist of alternate layers of different materials is a complex composite type which can possess exceptional high toughness, hardness, wear resistance, strength, stiffness, etc. The alternate layers can vary considerably in their individual thickness as well as compositions. Layer thickness can vary from a few microns to several thousand microns and compositions can be metal, ceramic, plastic, wood or composites utilized in virtually any alternate layer combination. Examples of suitable combinations of the respective layers are metal-metal, metal-plastic, metal-wood, metal-ceramic, metal-composite, ceramic-plastic, ceramic-composite, or virtually any combination of the fiber materials. Moreover, in accordance with this invention the complex composite structure is not limited to binary combinations. Thus, the complex structure may comprise tri-combinations of e.g. metal-plastic-ceramic, or composite-wood-ceramic, metal- metal-ceramic, etc. Each layer thickness in the multilayer composite may vary from the other layer thicknesses. Composites of the same composition can also be formed such as soft and hard compositions of the same material. One problem with a golf club face is that the grooves wear, including uneven wear from the top to bottom or upper and lower surface of a groove. Not only with alternate materials but with the same material soft and hard alternate layers can be used. The soft layer can erode or wear and the hard will not which will maintain the groove in excellent condition for repeated use whereas grooves in the same hardness face will wear unevenly. Examples include soft chemically pure titanium in an alternate layer with a much harder titanium alloy and/or a titanium compound such as a carbide, boride, nitride, etc. Another example could include soft mild steel with alternate layers of hard steel such as tool steel, armor steel, etc. The soft and hard alternate layers can be the same alloy type such as steel-steel, Ti-Ti or alternate materials such as Ti-epoxy-Ti, Al composite-Al-Al composite, etc. The multilayer composites of the complex structure can be produced by diffusion bonding, any plating or deposition process, sintering, brazing, gluing or joining procedure. Forming in the shape of a golf club head, face insert, sole, hozel or any subcomponent of a golf club head is the objective of this case. BUCKYBALL/FULLERENE/BUCKYTUBE AND ALLOYED SURFACES Current metal golf clubs including "irons" and "metal woods" performance can be improved at least in cosmetics if the surface is hardened. Many processes for alloying or hardening the surface of steel and or titanium golf club heads are well known. In the case of steel, carbiding, boriding and nitriding can readily be accomplished and thereby increase the hardness of 17-4 pH stainless steel from about Re 40-50 to Re 60-65. Such surface alloying and coating processes have long been known for other purposes, but have not been used to treat golf clubs. Harder coating compositions such as the nitrides and carbides of boron, silicon, the refractory metals and rare earths and some oxides such as the oxides of elements in Group II through VI and the rare earths are much harder by a factor of 3 to 5 than the nitrided or carbided steel. However, it is difficult to apply these harder carbides or other compositions to steel and particularly to withstand the impact associated with golf club usage For comparative hardness, Rc60 is approximately 732 on the Knoop scale and TiC is 2500-3500 Knoop depending on how it is produced However, if TiC is apphed directly to steel, it generally will not adhere and will crack during impact TiC is a precipitant in some steels but its surface composition is typically too low to enhance the surface hardness In accordance with a further aspect of the present invention, it has surpnsingly been found that "buckyballs," genencally known as fullerenes, which is the third form of carbon, in addition to graphite and diamond, can very easily be evaporated into thin layers that are applied to the surface of metal alloys such as steel, the iron group metals and titanium that contain alloying elements that include titanium, chromium, vandium, silicon, yttnum and the rare earths in the 4f and 5f senes and the refractory group metals The fullerene coated metal may be caused to react with the metal alloy surface by heating generally in a furnace or heated directly on the surface with a plasma, ion beam, electron beam, or laser, whereby a carbide contaimng the buckyball is formed or alloyed on the surface of the metal golf club Alternatively the fullerene carbide surface may be formed by applying the fullerene to the metal alloy surface and applying a second coating of the carbide forming element As an example a fullerene thin film can be applied to a steel surface followed by a titamum film applied by a deposition method or powder which on heat treatment or surface irradiation will form a hard carbide surface consisting pnmanly of titamum carbide in this example By this method, the buckyball carbide becomes alloyed to a metal golf club surface or any component surface and is very hard, in the range of 3000 Knoop, and is not generally cracked by the impact associated with a golf club stnking a golf ball To improve the toughness and impact resistance of the buckyball carbide, other alloying metals that do not form carbides such as copper can be added with the carbide former in percentage of a few percent up to about 50% The important discovery is that the buckyballs provide an alloying bndge to the steel or titamum golf club surface and produces a carbide alloy surface that can be quite hard The buckyball alloying layer can be applied by evaporation to the metal surface or by solution precipitation, since buckyballs are soluble in a vanety of solvents known in the art, notably organic solvents such as toluene Alternatively, the fullerenes or buckyballs can be utilized in vanous matπces to form a golf club, shaft or face insert The fullerenes which includes single and multi-walled nanotube shapes can be preformed and vanous plastic, metal or ceramic matnces infiltrated to produce a composite or mixed with the matnx to form the composites An example is a preform of a fullerene (buckyball, buckytube or mixture of each) and then infiltrated with either a plastic matnx or metal matπx The preform can be in the shape of a club, shaft or face insert to a club Alternatively, these same matnces can be mixed with the fullerene and then formed by casting or other forming techniques to produce a club, face insert or shaft The fullerene can constitute the entire reinforcement or can be mixed with other reinforcements such as ceramic particles or fibers, graphite particles or fibers including amorphorous forms of carbon and metal particles or wires, or combinations of these other reinforcements A plastic matπx can be soft for putter type golf club inserts or hard for irons or woods Metal matπces can include aluminum, copper alloys (I e brasses, bronzes etc) and steels or any of the iron group metas Titamum can be used as a matπx but it is known to form carbides which can cause bnttleness if in high concentration The use of buckyballs to produce improved golf clubs is further descnbed in Examples 45-51 below Buckyballs or fullerenes can be produced by well known methods in the art as descnbed in U S Patent No 07/930,818 "Methods and Apparati For Producing Fullerenes" Filed on 08/14/92 by Withers et al, including the Hufiman/Kratchner process descnbed therein and m the article Kratschner, W Lamb, L D , Fostiropoulos, K & Huffman, Dr Nature 347, 354-358, (1990), cited in said U S Patent Application INTERMETALLICSASGOLFCLUBHEADSANDGOLFCLUBSHAFTS The desirable features of a golf club head and shaft have been stated in the above descnptions One of the most important properties is lightweight in addition to hardness and wear resistance A class of matenals which possess these properties and which offer excellent potential as a golf club or shaft matenal in accordance with the present invention is lntermetallics Intermetal cs consist of two metallic elements, which form a new compound that has properties diffeπng from either metal components and generally has improved hardness, strength, modulus, etc Examples of lntermetallic compounds are crystal structures that include B2, DO- j , L12, C15, A15, L10, DO, 9 , D0 22 but is not limiting to all possible intermetalhcs lntermetallic compounds or alloys include Fe x Al, Ni-Al, Tι_Al, where x= 1 or 3, NiTi, MoSι 2 , Tι 5 Sι 3 , Al 5 CuTι 2 , Nb λ Al where x = 2 or 3, NbAl 3 , Be 12 Nb, Be I7 Nb 2 , Be 12 Tι, Cr 2 Nb, Cr 3 Sι, Cr 3 Sι 3 , Cr-Ti, SιV 3 , Sι 2 V, Sι 3 V 5 , etc The intermetalhcs may be utilized as pure compounds or alloyed to enhance select properties such as ductility, hardness, etc It is not unusual for one to five elements to be micro and macro alloyed to produce select properties Some examples of such allovs are Tι25Al-l lNb Tι-22Al-27 b N.-12A1- 40Fe, Nι-20Al-30Fe, Tι-48Al-2Mn and which may contain macro and micro alloying elements to improve corrosion, hardness, elongation (ductility), fracture toughness, etc An example includes adding boron to increase hardness and ductility of Nι,Al, and when boron is added to Ti-Al-Nb alloys a TiB- precipitate in the form of whiskers or particles occurs which substantially improves hardness and wear The density of many of these alloys are quite favorable for golf club and shaft applications compared to the often used golf club matenals of steel and copper *depends on alloy composition The properties of intermetalhcs as a class of matenals are excellent for golf clubs due to their light weight, high strength, high hardness and they can be processed by conventional metallurgy of casting, hot and cold working, powder molding and sinteπng, and as previously discussed, squeeze castmg aluminum into the elements that form aluminides EXAMPLES A metal coating was applied to a ceramic fiber array by passing the fiber array through a molten bath of the metal matnx followed by diffusion bonding of the metal coated fibers in a mold to form a composite of the ceramic fibers and the metal In particular, an array of ceramic fiber, namely, alumina based, ceramic fibers, sold under the trademark Nextel from 3M Company, was passed through a molten aluminum bath and the coated fibers were hot pressed in a mold mto a composite at a temperature of at least 400 °C to form a continuous aluminum matπx The metal coating thickness was controlled to achieve a fiber composition of 40% Different aluminum coating thicknesses can provide reinforcement controls in the range of 20% to 80% The resultant composite formed of the ceramic fiber and aluminum matπx can be formed into a golf club configuration dunng diffusion bonding in a mold configured to form a golf club iron, insert to an iron, dnver or in tubular shape to form a shaft A metal coating was applied to a ceramic fiber array as in Example 1 , using three different metal powders, each of which was compnsed of very small diameter metal particles in an organic binder The orgamc binder used in carrying out the Example was an acryllic, but other such binders could be used, for example, waxes, and a vanety of polymers. The diameter of the particles compπsing the metal powder should generally be less than 100 microns, preferably less than 40 microns and desirably less than 10 microns and most preferably less than 2 microns Ideally, submicron metal particle sizes are used Dunng the hot consolidation stage the organic binder was burned off before the metal particles were diffusion bonded into a continuous matrix phase with the ceramic fiber The metal powders, each in separate expenmental cases, were aluminum, copper and titamum The resultant composite of the respective metal and the ceramic fiber can be used as a component of a golf club such as an iron, insert, wood or shaft of a golf club by using an appropnately configured mold dunng the consolidation and diffusion bonding step Graphite fiber, Hercules IM9, was pneumatically spread to form an array and coated in a hollow cathode plasma sputter coater with an initial layer of 0 05 to 0 1 micron of molybdenum followed by a layer of 1 2 microns of copper The coated graphite fibers of the array were laid up in a pattern of 0-90-0-45-0-45 tow onentation and diffusion bonded at 925 °C and 2,000 psi for one hour using a mold configured so that the resulting composite was molded into the shape of a sole and face of a golf club head The resultant composite contained 60 v/o graphite fiber and 40 v/o copper The molybdenum initial coatmg layer bonded well to the graphite fiber dunng the diffusion bonding and alloyed with the copper to provide a well-bonded composite Without an terlayer, such as molybdenum, copper does not bond or wet graphite and a poor composite results The interface bonding layer can be any metal or compound that wets, bonds or reacts with the graphite and has solubility or alloys with the matnx or copper in this case Metals that are known to bond well to graphite are molybdenum, tungsten, titamum, niobium, mckel, cobalt, iron, titamum, zirconium and compounds such as molybdenum oxide, tungsten oxide, boron and boron oxide Graphite fiber coated with copper using an mterlayer of molybdenum as descnbed in Example 3 was combined with 15 micron SiC fiber which had a two-micron copper coating to make a lay-up for a golf club The fiber ratios were 50 coated graphite and 50 coated SiC The combined copper coated graphite fiber and copper coated SiC fiber lay-up was diffusion-bonded, as m Example 3 to produce a composite golf club sole and face The resultant composite was determined to have improved hardness and wear resistance over the all coated graphite fiber composite of Example 3 and can be used as any component in a golf club, as mentioned in Example 1 Graphite fiber, Hercules IM9, was pneumatically spread and coated with titamum to a thickness of 0 05 to 0 1 micron followed by one micron coating of 6061 aluminum The coated fiber was hot consolidated at 550°C and 5000 psi for one hour into a tubular shaped mold to form a golf club shaft Graphite fiber of Example 5 was coated only with titamum (I e without the aluminum of Examples 1 and 2) and aligned in a mold with molten aluminum poured into the mold and solidified The titamum coating provided excellent wetting of the aluminum and provided a barrier that prevented reaction of the molten aluminum with the graphite This Example involved applying a titanium coating on graphite fiber as descnbed m Example 5, but usmg titanium that is thicker than that of Example 5 such as one micron or more, then the titamum coated graphite fiber was placed in a mold shaped to form a golf club shaft as in Example 5 and molten aluminum was poured into the coated fiber array to form a titamum aluminide matnx through reaction of the molten aluminum with the titamum The coating operation of infiltrating the aluminum in the fiber array can be accomplished by pressureless infiltration, or by centnfugal or squeeze casting A prewoven graphite fiber architecture, graphite cloth, was coated with titamum m the hollow cathode plasma sputter coater and placed in a mold the shape of an "iron" into which molten aluminum was poured, whence an aluminum alloy was cast The titamum coatmg provided excellent wetting of the aluminum and prevented the molten aluminum from reacting with the graphite and produced a composite golf club "iron" shaped structure A preform for a golf club head was wound in the shape of a golf club head with a mixture of PBO fiber and the ceramic fiber Nextel 610 The preform was placed in a mold and squeeze-cast with molten aluminum The fiber content of the resulting golf club head was 65% and the strength was 1 5 GPa Such a fiber-reinforced composite metal is excellent for the club itself, iron or wood, as well as the shaft The ceramic fiber Nicalon (silicon carbide) tow was wound on a mandrel followed by vacuum impregnation with a slurry of titanium powder less than 40-micron diameter in an alcohol solvent The solvent was evaporated leaving a fibrous preform impregnated with paniculate titanium The resultant titanium impregnated fibrous preform then was squeeze cast in molten aluminum to produce a composite in the form of the golf club mold The final composite was a silicon carbide fiber reinforced titanium aluminide matrix casting suitable for a golf club structure, e g an iron, wood or shaft This Example demonstrates that it is possible to utilize the pressureless infiltration of a molten metal into a shaped preform to obtain a shaped metal matrix composite body which is integrally attached to a solid piece of matrix metal Referring to Figure 2, an ingot of matrix metal 101, measuring approximately 5 cm by 5 cm by 3 cm and composed by weight of approximately 9% Si, 3% Mg and the balance aluminum, was placed on top of a preform 102 having approximate dimensions 5 cm in diameter and 3 cm in thickness The preform 102 was produced by mixing 220 grit and 500 grit SiC particles from Norton and polyvinyl alcohol (PVA) binders from Monsanto The weight of PVA binder utilized was approximately 3% by weight of SiC The SiC/binder mixtures were pressed in a steel die to -1000 psi, which resulted in a preform 102 composed of -65 vol% of SiC and 35 vol% of porosity The preform 102 and matrix metal ingot 101 assembly was placed on top of an approximately 1 cm thick layer 103 of boron carbide powders from Johnson Mathey within a graphite boat 104 Additional boron carbide was then added to the graphite boat 104 until the surface of the boron carbide bed was approximately level with the upper surface of the matnx metal ingot 101 The setup, consisting of the graphite boat 104 and its contents were placed within a conventional controlled atmosphere electric resistance heated vacuum furnace (not illustrated) at room temperature A vacuum of approximately 5 torr was created within the furnace and maintained as the temperature within the furnace was raised from room temperature to about 200°C The furnace and its contents were held at 200 °C for 30 minutes before pure nitrogen gas was backfilled into the furnace to approximately 1 atmosphere and a continuous flow rate of approximately 2 1 min was established The furnace temperature was then ramped up to about 800 °C over about 2 hours, held at 800 °C for about 3 hours, and ramped down to room temperature in about 2 hours During the temperature excursion, the aluminum alloy of the matrix metal ingot 101 was melted and infiltrated into the porous SiC preform 102 The boron carbide powder 103 was not infiltrated by this procedure and acted as a banner to the molten metal penetration Upon reaching room temperature, the setup was removed from the furnace and disassembled A metal matπx composite compπsmg the SiC preform 102 infiltrated by the aluminum alloy matπx metal of the ingot 101 with an additional layer of pure matnx metal on the surface was recovered This Example demonstrates that through the use of pressureless infiltration it is possible to create a shaped metal matπx composite body, which is integrally bonded to a solid piece of excess matπx metal Such a composite is excellent for an iron, wood, or shaft The following Example demonstrates that it is possible to spontaneously infiltrate a bed of filler matenal with matnx metal to produce a macrocomposite which compπses excess matπx metal which is integrally attached or bonded to a metal matπx composite which is, in turn, integrally attached or bonded to a ceramic body Referring to Figure 3, an ingot of matnx metal, 111 measunng approximately 5 cm by 5 cm by 3 cm and composed by weight of approximately 9% Si, 3% Mg and the balance aluminum, was placed on top of SiC fillers 113 inside an alumina refractory boat 114 The filler composed of 70% 220 gπt and 30% 500 gnt SiC particles from Norton were well mixed and poured into the alumina boat 114 The thickness of the filler 113 is approximately 2 cm, and is composed of approximately 55 v/o SiC and 45 v/o open pore void The setup, consisting of the alumina refractory boat 114 and its contents were placed within a conventional controlled atmosphere electnc resistance heated vacuum furnace (not illustrated) at room temperature A vacuum of approximately 5 torr was created within the furnace and maintained as the temperature was raised from room temperature to about 200°C and maintained at that temperature for 30 minutes before a mixture or argon and hydrogen gas was backfilled into the furnace to approximately one atmosphere and a continuous flow rate of approximately 21/πun was established The furnace temperature was then ramped up to about 800 °C over about 2 hours, held at 800 °C for about 3 hours, and ramped down to room temperature in about 2 hours Upon reaching room temperature, the setup was removed from the furnace and disassembled A metal matrix composite compπsing the SiC preform filler 1 13 at approximately 55 v/o infiltrated by aluminum alloy matnx metal from the ingot 111 was recovered The metal matnx composite is integrally bonded with both the alumina refractory boat 114 and a control layer of excess aluminum alloy matnx metal The bond is evidenced by the fact that both the excess matπx metal and ceramic alumina boat 114 can not be removed without machining or destroying the composite The ceramic layer provides a very hard surface to a composite golf club A vaπation is to utilize a ceramic polycapillary on the bottom of the alumina container and it can form the base of the golf club This Example demonstrates that it is possible to utilize pressureless infiltration to create a composite compπsing excess matπx metal which is integrally bonded to a metal matπx composite body which is in turn integrally bonded to a ceramic body The following Example demonstrates that it is possible to spontaneously infiltrate a shape of filler material with matrix metal to produce a shaped macrocomposite. Referring to Figure 4, an ingot of matrix metal 121, measuring approximately 5 cm by 5 cm by 3 cm and composed by weight of approximately 3% Mg and the balance aluminum, was placed on top of SiC fillers 123 inside a graphite crucible 124. An insert 125 made of porous alumina was placed in the center of the boat 124. The graphite boat 124 was lined with a thin layer of Grafoil 126 from Union Carbide. The filler composed of 70% 220 grit and 30% 500 grit SiC particles from Norton were filled into the spaces generated between the graphite boat 124 and the alumina insert 125. The thickness of the molded SiC filler is approximately 3 mm, to demonstrate that very thin wall materials can be produced. The setup, consisting of the graphite boat 124 and its contents were placed within a conventional controlled atmosphere electric heated vacuum furnace (not illustrated) at room temperature. A vacuum of approximately 5 torr was created within the furnace and maintained as the temperature was raised from room temperature to about 200°C. The furnace and its contents were held at 200°C for 30 minutes before a mixture of nitrogen and hydrogen gas was backfilled into the furnace to approximately one atmosphere and a continuous flow rate of approximately 21 /min was established. The furnace temperature was then ramped up to about 800 ° C over about 2 hours, held at 800 ° C for about 3 hours, and ramped down to room temperature in about 2 hours. Upon reaching room temperature, the setup was removed from the furnace and disassembled. A metal matrix composite comprising the SiC preform of approximately 65 v/o infiltrated by the matrix metal was recovered. The composite was removed from the graphite boat 124 and the porous alumina insert 125 was removed by sand blasting leaving a cup shaped composite. Alternatively, the porous alumina or a polycapillary ceramic can be used and left integrally bonded to the silicon carbide reinforced aluminum alloy and the ceramic layer becomes the surface of the club. This Example demonstrates that it is possible to utilize pressureless infiltration to create a high volume loaded composite of complicated shape such as golf club head shapes. 13. The following demonstrates that it is possible to produce by pressureless metal infiltration, a macrocomposite comprising a metal matrix composite, which uses different types of fillers such as A1 2 0 3 , A1N, TiB 2 , etc. Referring to Figure 5, an ingot of matrix metal, 131 measuring approximately 5 cm by 5 cm by 3 cm and composed by weight of approximately 10% Mg and the balance aluminum, was placed on top of a preform 132 having approximate dimensions 5 cm in diameter and 3 cm in thickness. The preform 132 was produced by 325 mesh alumina powders from Norton and polyvinyl alcohol (PVA) binders from Monsanto. The weight of PVA binder utilized was approximately 3% by weight of alumina. The alumina binder mixture was pressed in a steel die to -5,000 psi, which resulted in a preform composed of -65 vol% of alumina and 35 vol% of porosity. Virtually any ceramic powder or mixture of powders such as TLB- and A1N can be produced in a preform by pressing, injection molding, slip casting, etc., but may require a different type of binder, such as polyvinyl butyl B76 from Monsanto or others, depending on the forming method. The preform 132 and matnx metal ingot 131 assembly was placed on top of approximately 1 cm thick barπer layer 133 of boron carbide powders from Johnson Mathey within a graphite boat 134 Boron carbide will not be infiltrated by this metal composition and procedure Additional boron carbide was then added to the graphite boat 134 until the surface of the boron carbide bed 133 was approximately level with the upper surface of the matnx metal ingot 131 The setup consisting of the graphite boat 134 and its contents were placed within a conventional controlled atmosphere electπc resistance heated vacuum furnace (not illustrated) at room temperature A vacuum of approximately 5 torr was created within the furnace and maintained as the temperature was raised from room temperature to about 200 °C The furnace and its contents were held at 200 °C for 30 minutes before pure mtrogen gas was backfilled into the furnace to approximately one atmosphere and a contmuous flow rate of approximately 21/mιn was established The furnace temperature was then ramped up to about 800 ° C over about 2 hours, held at 800 °C for about 10 hours, and ramped down to room temperature in about 2 hours Upon reaching room temperature, the setup was removed from the furnace and disassembled A metal matnx composite compnsing the A1 2 0 3 preform infiltrated by aluminum alloy matπx metal was recovered This Example demonstrates that it is possible to form a macrocomposite compπsing a matπx metal different types of fillers such as alumina, A1N and TιB 2 The following Example demonstrates the utilization of pressureless infiltration technique to form a macrocomposite body compπsing particles with alumina whiskers m the mterstices The method of Example 11 for forming alumina was substantially repeated, except that a preform contaimng alumina and aluminum powder was used The preform was formed by slip castmg of alumina and aluminum powders into a plaster of pans mold followed by heating the alumina/aluminum preform and plaster mold m an oxidation furnace ramped from room temperature to ~1000°C in air over a peπod of 3 hours and maintained at 1000°C for 2 hours The aluminum powder was oxidized and transformed into alumina whiskers, which grew in-situ between the particles of the alumina powder This preform was infiltrated with aluminum alloy matπx metal by the process descnbed in Example 13 The resultant composite contains a higher alumina content from the presence of both the alumina powder and alumina whiskers, for example, 50 v/o or greater This composite has higher hardness, greater strength and stiffness and greater shear or torsional strength and modulus which is ideally suited for golf club applications The following Example demonstrates the utilization of a pressureless infiltration method to form a graded ceramic macrocomposite body compπsing a relatively hard aluminum mtnde πch surface around the composite surface The method of Example 10 was substantially repeated, except that, rather than using a SiC preform by itself, the SiC preform was sprayed with fine powders of silicon nitride Under the process conditions, the matπx metal (aluminum) alloy infiltrated the SiC filler matenal as well as the silicon mtnde coating The reaction between aluminum and silicon mtnde results in a hard surface composed of Si and A1N (Sι,N 4 + 4A1 = 4A1N + 3 Si) This reaction provides a very hard composite surface consisting of the AIN ceramic and Si metal alloyed with the aluminum matnx After reaching room temperature, the setup was removed from the furnace and disassembled The resultant structure compnsed a shaped metal matnx composite body compnsmg the SiC preform infiltrated with aluminum and the sihcon mtnde coating infiltrated by the aluminum matnx metal having a surface consistmg of pnmanly AIN with silicon metal and aluminum alloy which possesses very high hardness This Example demonstrated that through the use of pressureless infiltration, it is possible to create a shaped metal matnx composite body which is composed of a graded composite that has a lower ceramic content intenor for increased toughness which is graded to the surface to a much higher ceramic content for a harder more wear resistant surface ideal for golf club applications Each of Examples 10 through 15 was repeated, but instead of pressureless infiltration, squeeze casting was utilized to form the aluminum matπx Squeeze casting was conducted utilizing the processing pnncipals illustrated m Figure 8 In the case of squeeze casting, as illustrated m Figure 8, the die mold, 141, which is formed of appropnate matenal, such as steel, can be m the shape of a club head or shaft contaimng the preform 142 The die mold 141 is heated to a temperature up to about the melting point of aluminum (660 °C) or the aluminum alloy 143 utilized to form the matnx The aluminum alloy matπx 143 is heated up to about 50-300 °C above its melting point, termed superheat The superheated aluminum is poured or injected into the preheated die/mold 141 and pressure is apphed with a plunger, ram or piston 144 The pressure causes the superheated aluminum in the die mold 141 to immediately solidify Pressure up to about 70 MPa is typically used in squeeze casting Although pressures in the range of 10 to 400 MPa may be used which will depend on the forces necessary to squeeze the aluminum into the preform As shown in figure 8, a porous, ceramic filter 145 be used as a lmer of the die mold 141, if desirable The time of the squeeze casting is only a few seconds, typically under five seconds and may be as low as one second or under After the pressure has solidified the superheated molten aluminum 143 forming the matnx of the composite structure 146 it can be immediately ejected from the die/mold Another preheated preform can then be placed in the die/mold 141 before it looses its desired preheat and the process is repeated, to rapidly produce composite golf club parts/golf clubs The reinforcement array 142 in the mold 141 can be in the geometry of particles or fibers (solid or hollow) in compositions of metals, ceramics, carbon/graphite or plastic and the casting metal 143 can be magnesium, aluminum, copper, mckel, iron and complex alloys of these A preform of TιB 2 powder, compnsed of particles in the 1 to 20 micron size range, was mixed with titamum metal powder and the mixture was die pressed and preheated to 600 °C under inert atmosphere to prevent the titamum powder from oxidizing Aluminum with a superheat of 200° C, l e 200°C above the melting pomt of the aluminum, was squeeze cast, which resulted m the titamum powder reacting with the molten aluminum to form a titanium aluminide matnx contaimng titamum diboπde powder 18 Example 17 was repeated with a mixture of TιB 2 powder and titamum metal powder using very small diameter particle size titanium powder m the 1-10 micron size range Unlike the procedure used in Example 17, the preform was not preheated and was squeeze cast with 250°C-superheat aluminum to form a titamum alumimde matnx contaimng titamum diboπde powder It was found by x-ray diffraction that the matπx was TiAl Thus, the TiAl matπx was formed from small diameter titamum powder without the necessity of preheating or postheatmg 19 A preform consisting of SiC particles less than one micron in diameter was suspended m deiomzed water and pressed in a die/mold which forced the water out, thereby producing a particle compact contaimng 85% SiC The SiC preform was then infiltrated by squeeze castmg with molten aluminum that produced a composite that could not be scratched by a hardened steel file Such a composite provides an excellent club or club face insert that retains the groove edge in the face and is not scratched by use, moreover, its hard surface produces higher ball velocity An entire club or shaft can likewise be produced when using the proper mold design 20. An SiC preform for a golf club head was produced which was compnsed of SiC that was size graded from nanoparticle size SiC on the front surface of the golf club head to lower volume course gπd particles of SiC on the rear club face that does not stnke the ball The overall volume loading of SiC particles compnsing the preform was greater than 50% The gradation preform of SiC was infiltrated with molten aluminum using squeeze casting to produce a casting of a golf club head that consisted of a higher density of nanoparticle sized SiC particles on the club face, with the density of such nanoparticle sized SiC particles gradually reduced at succession distances toward the rear of the club head 21 Example 20 was repeated with nickel particles mixed with the SiC particles, which produced a mckel alumimde matnx after molten aluminum squeeze casting that featured a golf club head casting with size graded density of SiC nanoparticles as in Example 20, but in a nickel alumimde matπx 22 Tungsten particles were prepressed m separate dies to form a straight bar in one case, and a curved piece that matched the curve on the bottom toe of a golf club iron 150, as illustrated in Figure 9 These prepressed tungsten pieces were placed in the toe 151 of a golf club head die/mold to form a preform for a golf club head at the hozel of the die/mold and then SiC particles were placed in the same die/mold with the tungsten preforms The hybπd particle preform was then squeeze cast with molten aluminum that produced a molded club head 150 with selective weighting in the toe 151 and heel 152 of the composite club that contained the SiC particles in the face 153 and sole of the club 150 as illustrated in Figure 9 23 Tungsten powder was placed in a mold m the shape of a golf club head without preforming, but its location was restπcted to the toe, sole and heel of the golf club mold SiC and diamond powder mixture was added to the die and the hybnd powder pressed m the mold to produce a combined loading of greater than 50% The preformed powder was then squeeze cast with molten aluminum to produce a composite club head that was selectively weighted in the toe, sole and heel to achieve improved golf club performance in addition to producmg a hard, composite club head face consistmg of both SiC and diamond Ceramic powder preforms were fixed into a centrifugal castmg system that contained a die/mold in the shape of a golf club The centnfugal castmg system was heated to 600 °C Molten aluminum with a 250 °C superheat was added to the mold which infiltrated the ceramic particle preform The aluminum remained molten before freezing for a sufficient penod that the centnfugal force caused the ceramic particles to migrate to the outer surface of the molten aluminum, thereby providing a higher concentration of particles at and near the surface of the resulting casting This resulted in gradation of the ceramic particles from the outer surface to the inner surface of the molded club head due to the centrifugal force The club dies/molds were oπented in respect of the centnfugal forces exerted on the molten aluminum impregnated matπx such that the highest concentration of ceramic particles in the molten aluminum was on the face and sole of the molded club The methods of the previous Examples were substantially repeated, except that, rather than using a particularate noncontinuous preform, the ceramic particles were sintered, thereby producing a continuous ceramic preform which was used for the infiltration process with the matnx metal A ceramic preform was produced by pressing 325-mesh alumina The pressed preform was placed in an oxidation furnace at room temperature and ramped up to ~1200°C in 3 hours and maintained at 1200°C for 2 hours and ramped down to room temperature m 3 hours The alumina preform was partially sintered between the particles, which resulted in a higher green body strength and density The sintered preform was then placed mside the graphite crucible for infiltration by the matnx metal in an electπc resistance vacuum furnace using a procedure identical to that of Example 13 The resulting metal matnx composite was removed from the crucible after infiltration, it was observed that the formed macrocomposite compnsed a continuous aluminum alloy metal matnx composite body integrally attached to the excess continuous matnx metal phase This Example demonstrates that it is possible to form a macrocomposite which compnses a continuous ceramic and continuous metal phase which may be produced by a pressureless process or alternately pressure can be applied such as in the squeeze casting processing Umon carbide HCT-S TiB- powder was dispersed in an orgamc solvent, notably toluene, to a solids content of 80% with an adjusted viscosity of 50 cps A binder, namely, B-76 from Monsanto, was mixed with a plasticizer, namely SI 60 from Monsanto, in a 1 1 ratio and added to the suspension to an 8% concentration The viscosity was adjusted at 500 cps and the mixture deaerated by vacuum to remove any trapped gases The slurry was cast mto a desired mold having a golf club head shape and air dned until a strong flexible green body was obtained Typically, drying time is 1-24 hours depending on the cross section that was cast The green body had approximately 60-65% solids content. The club head shaped green body was delubed (binder/plasticizer removed) by heating, slowly increasing temperature at a rate of about 2°C/min. with holding of 1 hour at 200°C and 550°C. After delubing the heating rate of 2°C/hour was continued until 1750°C and held at that temperature for 2 hours. The sintered TiB 2 club head shaped body was cooled to room temperature at a rate of approximately 2°C/min. The density of the sintered body is approximately 80-85% of theoretical. After sintering the TiB 2 body was ultrasonicated to remove any unsintered particles within the body. The porous sintered TiB- body was then subjected to pressureless molten metal infiltration like that used in Examples 10-15, except that the sintered TiB- body was placed in a graphite crucible coated with boron nitride and the necessary volume of stainless steel or other alloy was placed on top of the porous sintered TiB 2 , and stainless steel. The graphite crucible with the sintered club head shaped body was then placed in an electric resistance heated vacuum furnace. In the case of stainless steel, the crucible was heated in a non-oxidizing atmosphere to 1450°C and held for one hour then cooled to room temperature. The resultant golf club head composite is a continuous phase of TiB 2 at 80-85% density and a continuous phase of stainless steel at 20-15% density and a void content of less than 1%. The density of the composite is 5.05 g/cc, the hardness of the composite is 2200 Knoop, a strength of one GPa and a fracture toughness of 22 Mpam' 2 . This is an excellent composite for a golf club. 27. Example 26 was repeated, except that the presintered TiB 2 body was squeeze cast infiltrated with molten aluminum similar to Examples 16-23. 28. A mixture of hollow glass fibers, steel capillary tubing and graphite fibers were bundled and formed into a tubular shape and squeeze cast with molten aluminum to form the matrix of the hybrid reinforcement composite. This hybrid composite tube was found to be an excellent lightweight golf club shaft. 29. Hercules IM9 graphite fiber, 6000 fiber tow, was subjected to a SiO and carbon atmosphere at 1500°C, as described in the U.S. Patent application No. 60/050715 and 09/007573 to grow SiC whiskers from the surface of the graphite fiber. The whiskenzed surface of the graphite fibers are illustrated in Figure 7. The whiskerized graphite fiber was laid up into two golf club shaft configurations and positioned in respective molds. One was impregnated with epoxy and the other with molten aluminum by squeeze casting in molds configured to produce two golf club shafts. The shear strength of the epoxy composite golf club shaft was determined to be 3,000 psi and that of the aluminum matrix composite golf club shaft was 18,000 psi. 30. A woven cloth of graphite T-300 from Amoco, Inc. was impregnated with thermoset phenolic resin in a pressure mold, the shape of a golf club head, known in the art for producing carbon-carbon composites. The schedule used in this Example was to flash-heat the mold to 165°C, place the graphite cloth in the mold and impregnate the cloth with the phenolic resin, then hold that temperature for 20 minutes. This thermal treatment in the mold hardened the thermoset phenolic, of the golf club head structure, which was removed from the mold and placed in a controlled atmosphere furnace The resm impregnated graphite cloth molded structure was then pyrolyzed by subjecting it to heat in a non-oxidizing atmosphere In particular, the temperature was then raised to 1800°C in two hours and held at 1800 ° C for one hour and then cooled to room temperature under no particular cooling schedule The resultant molded golf club head compnsed a composite that was a carbon matnx with graphite fibers The density of the pyrolyzed carbon matnx golf club structure can be increased (filling of voids left from the pyrolysis of the phenolic) by reimpregnation with the resin followed by further pyrolysis Typically, the first impregnation and pyrolysis will produce a composite density of about 1 0-1 4 g/cc and 3 -4 impregnations with pyrolysis following each one will increase the density to about 1 6-1 7 g/cc The pyrolysis temperature need not be 1800°C Any temperature above about 850°C will provide complete pyrolysis of the phenolic matnx precursor or pitch and the higher the temperature of pyrolysis, the nearer to graphitization occurs which will provide a softer carbon matnx After the first pyrolysis of the composite golf club head produced in this Example, the density was determined to be 1 1 g/cc Another such composite was also formed by the same process in the shape of a golf club shaft, which was reimpregnated with epoxy resm and cured following the impregnation of the graphite cloth with phenolic resin and heat treatment descnbed above The cured shaft was lightweight and the carbon m the matπx provided energy absorption not achieved with graphite fiber-epoxy composites used in golf club shafts Another such composite made of graphite cloth, impregnated with phenolic resm and subjected to heat treatment as descnbed above was also formed in the shape of a golf club shaft which was then reimpregnated with molten aluminum metal using squeeze casting The golf club shaft compnsed of the hybnd composite of carbon-carbon with an aluminum matnx also provided substantial energy absorption over golf club shafts compnsed of all metal or graphite fiber-epoxy composites Example 31 was repeated to produce a custom golf club head using four successive phenolic resin impregnations each followed by pyrolysis, except that in the second phenolic impregnation the phenolic contained 25-volume percent submicron particle size silicon powder Dunng the pyrolysis step, the silicon reacted with the carbon graphite to produce SiC Dunng the third impregnation step the phenolic contained 50 v/o submicron particle size silicon powder which produced a greater amount of SiC during the pyrolysis step A final and fourth phenolic impregnation which contained sufficient submicron sihcon particle size to produce 100% SiC with the available carbon on pyrolysis was conducted and that produced a pure SiC matπx at the surface of the golf club head This Example was conducted like Example 30, to produce another golf club head, except that after the first pyrolysis of the phenolic in Example 30, the phenolic resin impregnated graphite composite golf club head was removed from the mold and placed in a non-oxidizing furnace and the temperature was raisedto 1900°C Silicon metal granules were melted at the 1900°C temperature and the molten silicon infiltrated the porous carbon-carbon composite Some SiC was formed with some silicon on the surface This formed a very hard golf club face This process can be used to form clubface inserts as well as the processes described in the previous examples A high hardness steel alloy with a hardness of Rc70 in a thickness of 0 125 inches was alternately laid up in layers with a brass alloy in a thickness of 0.080 inch and the adjacent layers were diffusion bonded to one another in a mold press having the shape of a golf club face and sole. The diffusion bonding was achieved at 900°C and 2,000 psi for two hours The laminar lay-up was such that the alternate thickness of the respective layers of the hard steel alloy and soft brass alloy was perpendicular to the face of the golf club head with a steel layer as the sole of the club head Thus, the outer surfaces of the club face of the club presented alternate strips of the hard steel alloy and the soft brass alloy, of 0 125 inch and 0 080 inch thicknesses, respectively Example 33 was repeated to form a golf club head except that an aluminum alloy layer was utilized in the place of the brass alloy of Example 33 and in the same thickness as the steel Diffusion bonding of the laminar lay up was accomplished at 600 °C for two hours at 2,000 psi Example 34 was repeated to form a golf club head using alternate layers of 0 0625 inch thick aluminum and 0 040 inch thick alumina, which had been tape cast The diffusion bonding was accomplished at 620°C and 1,000 psi for three hours Example 35 was repeated to form a golf club head using alternate layers of 0 040 inch thick alumina and thermoplastic nylon, which bonded together at 100° C and 600 psi Example 36 was repeated to form a golf club head using alternate layers of 0 125 inch thick steel and thermoset epoxy, which was pressed together under 100 psi dunng the epoxy cure cycle Example 37 was repeated to form a golf club head in which the nylon layer was replaced by a composite formed of nylon with a filler of SiC High hardness steel layers in a thickness of 0 1875 inches were alternately bonded using epoxy binder with oak wood layers in a thickness of 0 625 inches The molding pressure was 350 psi during the heat cure cycle of the epoxy A golf club head was thus formed by this process The configuration of the club head layers was similar to that described in Example 33, with the relatively hard steel layers and relatively soft oak layers alternately presented to the face of the club head with a steel layer as the sole A golf club head was formed of alternate layers, essentially as in Example 33, except that composite consisting of 20 v/o SiC in an aluminum matrix in a thickness of 0 0625 inch was laid in a mold in layers alternately with layers of titanium in a thickness of 0 125 inch which had been nitrided to a depth of 20 microns and a layer of beryllium copper in a thickness of 0 03 inches The respective layers were diffusion bonded at 625 °C for four hours at 3,000 psi The layers of the club head were oπented as in Examples 34 and 40, except that the sequence of layers presented to the club head face was soft aluminum, hard titanium, soft aluminum, hard beryllium copper, soft aluminum, etc A hard layer of titanium formed the sole of the golf club head In a sputter deposition system, a layer of stainless steel alloy was deposited to a thickness of eight microns alternately with layers of titamum carbide havmg a thickness of 1 5 microns usmg known in the art deposition processing The alternate layers were built-up to an aggregate thickness of 625 microns, which was used in sheet form and bonded with a silver braze to the face and sole of an aluminum metal golf club dπver head The layer of stainless steel alloy was bonded against the aluminum face of the metal dπver and the outer face of the layered composite sheet compnsed a layer of titamum carbide, which thereby became the outward or surface layer of the face and sole of the dnver The multilayer laminate compnsed of alternate layers of 8 microns thick stainless steel alloy and 1 5 micron thick titamum carbide, produced as in Example 41 was cut into stnps with a diamond saw and the stnps were then stacked such that the edge was facing outward and bonded usmg epoxy bonding layers into the form of a golf club face and sole of a golf club head including a built up edge with a hole to accept the golf club shaft A graphite fabπc was treated to grow whiskers on the individual fiber surfaces and m the mterstices of the fabπc The SiC whisker fabnc was impregnated with epoxy to produce a thickness of 0 125 inches and layers of the epoxy impregnated fabnc were laid alternately with a titamum sheet that was 0 0625 inch in thickness to form a laminated structure that was molded under pressure in a mold having the shape of a golf club dπver head to cure the epoxy and bond the alternate layers together The molded and cured structure resulted in a golf club dπver compnsed of alternate layers of whiskered graphite fabnc and titamum, bonded together with epoxy resin The alternate layers were positioned such that the club face was compnsed of alternate stnps of the epoxy impregnated graphite fabnc with SiC whiskers and titamum Layers of low carbon mild steel were laid alternately in a mold with layers of a hardened tool steel which in this case was H13 The mild steel was 1/16 inch thick and the H13 hardened tool steel was 3/16 inch thick Multilayer composites formed of alternate layers of the mild steel and hardened steel were fabπcated without a braz/bondmg matenal, which was accomplished by diffusion bonding the alternate layers together at 1000°C and 2,000 psi in an inert atmosphere Similar composites were made using a brazing power at the interface of the respective steel layers to aid in the bonding layer After diffusion bonding, the composite was machined to form an iron insert configuration and subjected to gπt blasting on one side The soft mild steel was eroded while the hardened steel was substantially unaffected The mild steel erosion formed the grooves for a golf club face while the hardened steel provided a hard surface substantially free of erosion providing grooves that remained unaffected by use and was suitable for imparting excellent spin to the golf ball Club faces of the same material expeπence uneven groove wear and thus reduced performance over time A buckyball, I e , fullerenes of mixed molecular weights, pnmanly C 60 and C 70 , as produced by the Huffman/Kratschmer process known in the fullerenes art, was evaporated onto a titamum golf club to a thickness of about 2-4 microns Following the buckyball layer, a similar thickness layer of titamum was evaporated onto the golf club An electron beam was used to scan the surface and cause reaction between the titamum golf club surface, buckyball layers and titamum layers to form an adherent layer of buckyball titamum carbide on the titamum golf club This method is also useful to produce a titamum carbide layer on other metal structures or metal coated structures, thereby enhancing their surface hardness Example 45 was repeated and after the titamum layer had been deposited on the buckyball layer, a thick layer of submicron particle size boron powder was sprayed on as a coatmg After the electron beam scan of the thus coated titamum club, to react the coatings and titamum on the golf club surface, the alloy surface contained buckyball carbides of titamum and boron and titamum diboπde These hard coatmgs formed an excellent wear resistant surface on the golf club and can also be applied to similar surfaces on structures other than golf clubs usmg the same process A steel substrate for a golf club head structure was coated by sputteπng with a layer of titamum about 3-5μ thick The titamum-coated steel was utilized as a substrate and in an argon plasma, a layer of buckyballs were evaporated on the substrate that formed a hard TiC coating on the steel substrate This process is also useful to enhance the surface of metal surfaced structures other than golf clubs Buckyball soot, as produced by the Huffman/Kratchner process, unrefined was mixed with a soft plastic epoxy from United Resm Corporation, (F-82 Resin, 117 hardness, 1 1 wt /ratio) and utilized as an insert in a golf club putter face Likewise, this method can be used to produce other than golf club structures A mixture of buckytubes contaimng single and multiwalled fullerenes with soot that also contained other fullernes was preformed to about 50% and aluminum squeeze cast in a mold forming a golf club head insert with molten aluminum into the preform that produced an insert for use m a golf club iron or wood A mixture of unrefined fullerenes and petroleum coke was mixed with a polyurethane that was used to form an insert for a putter face A fullerene mix which contained buckytubes and SiC nanoparticles was preformed in a mold to the shape of a golf club iron, which had tungsten particles that had been prepressed and placed in the toe sole and hozel of the club iron preform structure and squeeze cast with molten aluminum to form an iron compπsing a composite contaimng all reinforcement types An lntermetallic alloy, namely, Fe-40Al-'/2Mo, which has a density of 5 9 g/cc and which is 25% lighter than 17-4pH stainless steel, the usual pπor art metallic alloy for golf club "irons," was cast into an "iron" which was 20% larger than a typical stainless iron plus additional weight was put into the sole and toe of the lntermetallic casting by loading the sole and toe of the iron with tungsten to improve the accuracy of the iron, and performance even if the golf ball contact with the face of the iron occurs off center The larger club size and additional selective distribution of weight could be obtained because of the lighter lntermetallic alloy compared to the usual stainless steel, yet the lntermetallic alloy club maintained the same weight as that of a standard stainless steel club The typical hardness of a stainless steel club is Re 50-60 and the hardness of the Fe-Al-Mo was Re 64 An mtermetalhc alloy consisting of Tι-25Al-17Nb-3B-0 3Nd which has a density of 4 35 g/cc which is 45% lighter than stainless steel head was cast into a "wood" club or dπver that was 33% larger than a typical stainless steel "dπver " The hardness of the mtermetalhc alloy dnver was Re 75 A second casting of this mtermetalhc alloy was hot extruded into a golf club shaft and utilized in the dπver head made of the same lntermetallic alloy An mtermetalhc alloy consistmg of Tι-22Al-27Nb, which has a density of 4 5 g/cc, which is 43% lighter than stainless steel, was cast mto an ingot and hot extruded into a tube to serve as a shaft for a golf club "iron" or "wood " This particular alloy had a modulus of 35 million psi, which provides a much higher modulus to density ratio than steels An SHS reaction was used to produce Tι-24Al-14Nb-0 5Mo-3V metal particles A solution of buckyballs consisting of fullerenes m an organic solvent, namely toulene, was used to coat the metal particles and the solvent was evaporated leaving about 1% buckyballs The fullerene coated particles were hot consolidated and forged to produce a golf club head compnsed of an alloy which had a density of 4 9 g/cc and a hardness of 2500 Knoop Tungsten powder was pressed into shapes to fit mto the toe, sole and heel of a golf club head These preformed tungsten powder pieces were placed in a die/mold and the mtermetalhc alloy of Example 55 was squeeze cast to produce an mtermetalhc alloy golf club with selectively distnbuted tungsten weighting A solid piece of oak wood was heat-treated slowly to 1000°C in an inert atmosphere After heat treating the volume charge was approximately 40% which produces a porous carbonaceous char This heat-treated oak was placed in a steel die that was preheated to 450°C Aluminum with a superheat of 100° C (760 °F) was poured into the steel die and a steel ram immediately pressed the aluminum which forced it into the oak preform After removing from the steel die the oak preform was completely infiltrated with aluminum metal which has a strength of 30,000 psi and a modulus of 5 x 10 6 psi compared to the oπginal oak wood of 3200 psi and 0065 x 10 6 psi This same expeπment was repeated with other woods that includes pine, fir, redwood, hickory and balsa wood A laminated persimmon wood in the form of a golf club wood was pyro zed to 1200°C in an inert atmosphere The charred product was then placed in a vacuum chamber contaimng a suspension of isopropyl alcohol and silicon carbide in the size range of less than 10 microns down to less than one micron in a ratio of 5 to 1 with diamond particles in a size range of approximately 20 microns The porous charred wood was lowered into the paniculate suspension for the face and sole only to be impregnated with the paniculate The isopropyl alcohol was evaporated when the wood preform was placed in a steel die heated to 400 °C. Aluminum was squeeze cast onto the preform producing a metal-wood golf club with ceramic paniculate in the face and sole. This example was repeated but a portion of the wood sole was removed and a pre-pressed piece of tungsten powder was inserted. Tungsten particles were impregnated in the remainder of the sole and clubface instead of the SiC particles. Aluminum was squeeze cast into the charred preform to produce a club containing the tungsten weighting of the un-sintered tungsten particles. 59. A piece of pine board that is referced to as one by four was heat-treated to 1800°C in an inert atmosphere. The charced preform was placed in a steel die and aluminum squeeze cast therein. The finished composite could be sawed like normal wood and could be nailed or screwed like normal wood. However it was not flammable when placed in a gas flame and could be expected to not be attacked by termites or other normal wood degradation processes. The strength and stiffness was over ten times that of the original wood. Such a composite is an excellent structural member. 60. A block of particle laminated wood was carved into an architecture representing a starfish and charred to 800° C. The char preform was placed in a mold and bronze was squeeze cast to fill the porous char. 61. A paper preform was made by laminated object modeling rapid prototype preforming. This preform was pyrolyzed in an inert atmosphere to 625 °C. The char preform was then placed in a steel die and infiltrated with aluminum by squeeze casting. 62. Rice paper was shredded and soaked in water with a wetting agent and water-soluble glue. The liquid was filtered and the remaining softened paper shred was placed in a mold that formed a piston for an internal combustion engine. The mold was heated to 200°C under a pressure of 1000 psi. The molded piston was then heat-treated to 870°C in an inert atmosphere. The charred piston was then placed in a steel die and magnesium was squeeze cast to produce a carbon fibrous reinforced magnesium piston. 63. A hickory wood was heat-treated to 1400°C in an inert atmosphere. The porous charred preform was then vacuum impregnated with the preceramic polymer ceraset from DuPont. The preceramic polymer impregnated preform was then heat-treated to 1400°C, which produced a ceramic matrix of sihcon carbide. Two additional reimpregnation steps with 1400°C pyrolysis was conducted that resulted in a carbon fibrous reinforced silicon carbide matrix composite. This example was repeated except an alumina sol-gel was used to form the matrix instead of the preceramic polymer ceraset. The example was repeated except the matrix was formed by the chemical vapor infiltration known in the art to deposit a silicon carbide matrix using methyltrichlorosilane. 64. Example 63 was repeated to form the porous char. The carbon char was then subjected to chemical vapor reaction processing as described in U.S. Patent Application 09/007,573 "Carbon Composites" (filing date 1/15/98) that converted the carbon char to silicon carbide. The silicon carbide fibrous preform was then vacuum impregnated with ceraset and pyrolized to produce a sihcon carbide matrix This processing resulted in a silicon carbide/silicon carbide composite Example 62 was repeated to form the filtered softened paper shred In this case a layer of carbon fabric in a square weave was laid alternately on layers of the soft paper shred. This layered preform was then laid into a square die and pressed at 1000 psi while heating to 200 °C The cured pressed preform was then heated to 1000°C in the absence of air which produced a carbonaceous preform consisting of alternate layers of carbon fabric and fibrous materials from the paper char. This preform was then infiltrated with aluminum by squeeze casting The Example was repeated except the aluminum infiltrant was replaced with the thermoplastic nylon The Example was repeated except that thermoset phenolic resin was infiltrated instead of nylon and heated to 165°C to cure the resin The Example was repeated except a catalyzed cured epoxy resin was infiltrated into the chaned preform which the resin cured in one hour This Example was repeated except instead of using carbon fabric, chopped and milled carbon fiber was mixed with the softened paper shred and fully mixed After molding and pyrolyzing to produce a char which now contains random discontinuous carbon fiber, the preform was infiltrated with molten magnesium by squeeze casting Cotton staple was mixed in water with a wetting agent and water soluble glue The slurry was molded to the shape of a rectangle two inches by four inches by V* inch thick at a pressure of 1,000 psi while heating to 250°C After removing from the mold, the formed piece was subjected to pyrolysis in absence of air to 870 ° C that produced a carbonaceous char in fibrous form The porous char was placed in a mold and squeeze cast infiltrated with molten aluminum The composite was then utilized as a putter face of a golf club Such a reinforced composite is also applicable to many other component uses including structural The Example was repeated and a mixture of small particle silicon carbide and diamond was infiltrated into the char followed by infiltration with aluminum using squeeze casting This provided a very hard surface suitable for an insert to a golf club iron or wood The example was repeated and the char subjected to chemical conversion to silicon carbide as described in Example 64 The SiC preform was then infiltrated with aluminum by squeeze casting This Example was repeated except wool staple was used instead of cotton

Claims: What is claimed is as follows 1 A method of making a golf club structure that compnses providing a ceramic fiber array, applying a metal coatmg to said array, hot pressing said metal coated fiber array by subjecting it to heat and pressure in a mold configured to form said golf club structure, maintaining the temperature of said coated fiber anay dunng said hot pressing such that the metal coatmg is diffusion bonded to the ceramic fiber of said anay, whereby a golf club structure compπs g a composite of said ceramic fiber and metal coatmg is formed in said mold 2 The method of claiml, wherein the ceramic fiber array is coated with said metal by passing the anay through a bath of the molten metal 3 The method of claim 2 wherein the metal is aluminum 4 The method of claim 3, wherein the temperature at which said coated anay is maintained dunng said hot pressing is at least 400 °C 5 The method of claim 4, wherein the thickness of the metal coating is controlled dunng the coating step so as to provide a ceramic fiber content m the range of 20% to 80% by weight of the composite structure 6 The method of claim 1 wherein the metal coatmg is applied to said ceramic fiber anay in the form of a metal powder of small diameter particles in an organic binder and wherein the organic binder is burned off during the hot pressing process pπor to diffusion bonding of the particles of the metal coating to said ceramic fiber anay 7 The method of claim 6 wherein the metal powder is selected from among aluminum, copper and titamum 8 The method of claim 6, wherein the particle size of the metallic powder is less than one micron in diameter 9 A method of making a golf club structure that compπses providing a fiber array compnsmg graphite, applying a metal coating to said anay, placing the metal coated fiber anay in a mold configured to form a golf club structure and subjecting said metal coated array to heat and pressure sufficient to cause diffusion bonding of the metal coating to the graphite fiber anay, thereby producing a composite of said metal and graphite m the form of said golf club structure 10 The method of claim 9 wherein the metal coating compnses an inner layer compπsing a first metal that bonds to the graphite fiber and an outer layer compπsing a second metal that does not bond well to the graphite, but which forms a composite by diffusion bonding to graphite 11 The method of claim 10 wherein the matenal of the inner layer is selected from among molybdenum, tungsten, titamum, niobium, nickel, cobalt, iron, titamum, zirconium, boron, and oxides thereof 12 The method of claim 10, wherein the matenal of the outer layer is copper 13 The method of claim 1 1, wherein the matenal of the outer layer is copper 14 The method of claim 13, wherein the matenal of the outer layer is copper and the inner layer compπses a metal that forms an alloy with copper dunng the diffusion bonding process The method of claim 9 wherein the metal coatmg is apphed to the graphite fiber array by a plasma sputter coatmg process The method of claim 10, wherein the inner layer of the metal coating is apphed to the graphite fiber anay by a plasma sputter coatmg process The method of claim 14, wherein the matenal of the inner layer is molybdenum and wherein the diffusion bonding is earned out at a temperature of 925 °C and a pressure of 2,000 psi for about one hour The method of claim 17 wherein the resultant composite contains about 60 v/o graphite fiber and 40 v/o copper The method of claim 10 wherein the fiber anay compnses a mixture of graphite fiber to which a metal coating compnsmg an inner layer of molybdenum and an outer layer of copper and SiC fiber havmg a copper coating thereon, and wherein the array compnsmg said mixture of coated fibers is subjected to heat and pressure to cause diffusion bonding of said fibers and coatings The method of claim 9 wherein the metal coating compπses an inner layer of titamum and an outer layer of aluminum The method of claim 20 wherein the coated fiber is subjected to consolidation by applying heat at 550°C and pressure at 5,000 psi for about one hour The method of claim 20 wherem the mold is configured to form a golf club shaft The method of makmg a golf club structure that compπses providing a fiber anay comprising graphite, applying a coating of titamum metal to the fibers of said array placing said titamum coated fiber anay m a mold configured to form a golf club structure, introducing molten aluminum into said mold in contact with the titamum coated fibers of said anay, whereby a titamum alumimde matπx is formed through reaction of the molten aluminum with the titamum of said coated anay The method of claim 23 wherein the titamum coating applied to the graphite fibers of said array is at least one micron thick, thereby reducing the opportunity for reaction of the graphite fibers with the molten aluminum The method of claim 24 wherein the titanium is coated to the graphite fibers by a plasma sputter coating process The method of claim 25 wherein the mold is configured to form a golf club iron The method of making a golf club structure that compπses prepaπng a preform array compnsmg a ceramic fiber, placing said preform in a mold configured to form a golf club structure, squeeze casting said preform with molten aluminum to form a fiber reinforced metal composite golf club structure The method of 27 wherein the preform anay includes PBO fiber m a mixture with said ceramic fiber The method of claim 27 wherein the ceramic fiber preform is impregnated with titamum powder particles pπor to the squeeze casting step 30 The method of claim 29 wherein the ceramic fiber comprises silicon carbide, whereby the resulting squeeze cast golf club structure is formed of a composite comprising a silicon carbide fiber reinforced titanium aluminide matrix 31. The method of claim 29 wherein the preform is impregnated with titanium by vacuum impregnation of the fiber preform with a slurry of titamum powder in an alcohol solvent, followed by evaporation of the solvent 32 A method of making a golf club structure that comprises forming a relatively porous ceramic preform shaped to form the golf club structure placing the shaped ceramic preform golf club structure in a container with an ingot of matrix metal in contact with the ceramic preform structure and a quantity of boron carbide powder positioned to separate the preform structure from the container thereby serving as a barrier to molten matrix metal, subjecting the contents of the container to heat in a non- oxidizing atmosphere, the heat being of sufficient temperature and time to melt the matrix metal, whereby it infiltrates the porous preform structure with matrix metal 33 The method of claim 32, wherein the preform is comprised essentially of SiC particles 34 The method of claim 33 wherein the SiC particles are contained in a polyvinyl alcohol binder mixture and wherein this mixture is formed into the shape of the golf club structure by pressing in a shaped die at elevated temperature to produce a porous SiC preform structure having the desired shape 35 The method of claim 32 wherein the matrix metal is comprised primarily of aluminum 36 The method of claim 35 wherein the matrix metal is comprised of aluminum, silicon and magnesium 37 The method of claim 33 wherein the matrix metal is comprised primarily of aluminum 38 The method of claim 37 wherein the container is comprised essentially of graphite 39 The method of claim 36 wherein the matrix metal is comprised by weight of 9% Si, 3% Mg and the balance Al 40 The method of claim 34 wherein the SiC particles comprise a mixture of 220 gnt and 500 gnt particles and wherein the porosity of the resultant pressed preform is about 35% by volume 1 The method of claim 32 wherein the matπx metal is selected from among A 1 , Mg, Cu, Ni, Co, Fe and their respective alloys and intermetallics including aluminides of Ti, Ni, and Fe 2 The method of claim 32 wherein the preform is comprised of one or more of the following Al-O, AIN, TiB 2 SiC, TiC, MgO, TiN, TiCN, TiAIN, BN, and TiO, 3 The method of claim 41 wherein the metal matrix micro-composite forming powder is contained in a binder and formed into the shape of the golf club structure by pressing in a shaped die at elevated temperature to produce a porous ceramic preform structure having the desired shape 4 The method of claim 41 wherein the matrix metal is comprised primarily of Al 5 The method of claim 44 wherem the matrix metal is comprised of about 10% Mg and the balance Al by weight 6 The method of claim 33 wherein the SiC preform is coated with silicon nitride powder prior to the step of heating to melt the metal matrix, and wherein the metal matrix is comprised primarily of aluminum, whereby when the metal matrix is melted it infiltrates both the SiC and the sihcon nitride resulting in a reaction between the aluminum and sihcon nitride thereby producing a hard surface compound of Si, AIN, namely, Si 3 N 4 +4Al= 4AlN+3Si, providing the AIN ceramic and Si metal alloyed with the aluminum matrix metal. 47. The method of claim 32 wherein the preform is comprised essentially of a mixture of alumina powder and powdered aluminum metal in a binder. 48. The method of claim 47 wherein the preform mixture is formed into the shape of the golf club structure by slip casting in a mold configured to form the golf club structure, followed by heating in an oxidation furnace at elevated temperatures and pressure sufficient to oxidize the aluminum powder and transform it into alumina whiskers that grow in-situ between the particles of the alumina powder. 49. The method of claim 48 wherein the matrix metal is comprised primarily of aluminum. 50. The method of claim 49 wherein the matrix metal is comprised primarily of an aluminum alloy. 51. The method of making a golf club structure that comprises placing a relatively porous preform in a squeeze casting die configured to form the golf club structure, subjecting the mold to heat to bring it to a temperature above room temperature but no higher than the melting point temperature of a selected matrix metal to be introduced into the mold, subjecting a quantity of the selected matrix metal to sufficient heat to bring its temperature above its melting point to its superheat temperature point, and introducing the superheated matrix metal into the mold under sufficient pressure to cause it to penetrate the porous preform and to rapidly solidify. 52. The method of claim 51 wherein the preform is comprised essentially of one or more of metal, ceramic, carbon or plastic. 53. The method of claim 51 wherein the matrix metal is comprised of one or more of magnesium, aluminum, copper, nickel or iron metal or a complex alloy of one or more of these metals. 54. The method of claim 27 wherein the ceramic fiber of the preform alloy is TiB- powder, wherein the TiB 2 powder is mixed with titanium metal powder, wherein the mixture of the TiB 2 powder is die pressed and pre heated to about 600 °C in an inert non-oxidizing atmosphere prior to the step of squeeze casting the preform with molten superheated aluminum to cause the titanium powder to react with the molten aluminum to form a titanium aluminide matrix containing titanium boride powder, said matrix being molded to form the golf club structure. 55. The method of claim 27 wherein the ceramic fiber of the preform anay is TiB 2 powder, wherein the TiB 2 powder is mixed with titanium metal powder comprised of metal particles in the 1-10 micron size range, wherein the squeeze casting step is carried out, without preheating, using molten superheated aluminum to form a titanium aluminide matrix golf structure containing titanium diboride powder. 56. The method of claim 27 wherein the ceramic fiber of the preform is SiC powder comprised of particles of less than one micron in diameter suspended in deionized water and pressed in a die mold configured to form the golf club structure in order to force out the water from the resulting preform which is then subjected to the squeeze casting step using molten aluminum. 57. The method of claim 27 wherein the ceramic fiber of the preform is SiC powder comprised of particles size graded from nanoparticle size to course grid particle size, wherein the golf club structure is a golf club head having a front surface defining the striking areas and a rear surface that does not strike the ball, wherein the ceramic particles are dispersed in the preform in a size graduated manner with a higher density of the smaller particle toward the front surface and lower density of smaller particles toward the rear and, conversely, with a higher density of the larger particles toward the rear surface and lower density of the larger particles toward the front surface, whereby the squeeze casting step results in an aluminum metal matrix golf club head structure having a higher density of smaller diameter SiC particles dispersed toward the front striking surface and a higher density of larger diameter SiC particles dispersed toward the rear non striking surface. 58. The method of claim 57 wherein powdered nickel particles are mixed with the size graded SiC powder particles forming the preform, whereby the molten aluminum squeeze casting step results in the production of a nickel aluminide matrix golf club head with the size graded SiC particles dispersed therein. 59. The method of making a golf club structure that comprises preparing a component preform of such structure by pressing a quantity of tungsten metal particles in a first die mold configured to form a preform of such component, placing said preform in a selected region of a second die mold configured to form the club structure together with a quantity of ceramic particles that are less dense than the tungsten particles to form a hybrid preform in said second die mold comprising the tungsten component preform and the ceramic particles and squeeze casting said hybrid preforms in the second die mold with a molten metal matrix material to produce a composite molded golf club structure that is selectively weighted as determined by the placement of the tungsten component preform in the mold employed to form said club structure 60. The method of claim 59 wherein the die mold is configured to form a golf club head structure, the component preform is configured by the first mold to conform to a selected region of the second die mold where it is desired to provide greater weight in the corresponding region of the molded golf club head. 61. The method of claim 59 wherein the ceramic particles are comprised essentially of SiC. 62. The method of claim 60 wherein the ceramic particles are comprised essentially of SiC. 63. The method of claim 59 wherein the tungsten metal component preform is configured to conform to the toe and head region of the molded golf club head and is placed in the corresponding region of the second mold. 64. The method of claim 62 wherein the tungsten metal component preform is configured to conform to the toe and head region of the molded golf club head and is placed in the conesponding region of the second mold The method of claim 64 wherein a second component preform conesponding to a second selected region of the second mold is prepared by pressing another quantity of tungsten metal particles in a mold configured to form such second component preform, and wherein the second component preform is placed in the second selected region of the second mold pπor to the squeeze castmg step The method of making a golf head club structure that compnses selectively placing quantities of tungsten metal powder in each of the toe, sole and heel regions of a mold configured to form a golf club head, placing a powder mixture of ceramic SiC particles and diamond particles in the remaining space of said mold, pressing the contents of the mold to produce a combined loading of greater than 50% by volume, thereby producing a hybπd powder preform of the golf club head, squeeze castmg the hybπd powder preform with molten aluminum to produce a composite club head that is selectively weighted m the toe, sole and heel and having a hard club head face compnsed of both SiC and diamond The method of makmg a golf club structure that compπses a golf club head havmg face and sole sides, placing a ceramic powder preform in a mold configured to form the golf club structure in a centnfugal casting system, heating the mold to about 600 °C and introducing superheated molten aluminum matnx metal mto the mold while subjecting it to centnfugal force to cause the particles of the ceramic preform to migrate to the outer surface of the molten aluminum, said mold being onented in the centnfugal system such that the face and sole sides of the club head are located at the outer surfaces of the molten aluminum in the mold, whereby the highest concentration of the ceramic particles in the aluminum matnce occurs in the face and sole of the resultant club head The method of claim 67, wherein the ceramic powder preform is compnsed essentially of SiC The method of claim 32 wherein the ceramic preform structure is sintered pπor to infiltration by the matnx metal The method of claim 69 wherein the preform is compnsed essentially of a metal matnx macro- composite forming powder The method of claim 70 wherein the metal matπx macro-composite forming powder is selected from among A1 2 0 3 , AIN, TιB 2 The method of claim 69 wherein the matπx metal is compnsed pnmanly of aluminum The method of claim 72 wherem the matnx metal compnses by weight, approximately 10% Mg, and the balance Al The method of claim 72 wherein the preform is compnsed essentially of alumina The method of claim 73 wherein the preform is compnsed essentially of alumina The method of claim 69 wherein the ceramic preform is produced by pressing powdered alumina of approximately 325 mesh particle size and sintered by subjecting it to heat in an oxidation furnace at a temperature in excess of 1000 ° C for sufficient time to produce partial sintenng between the alumina particles, whereby increased green body strength and density is produced in the ceramic preform pnor to infiltration by the matnx metal 77 The method of claim 76 wherein the matπx metal is pnmanly aluminum 78 A method of makmg a golf club structure that compnses forming a relatively porous ceramic preform shaped to form the golf chib structure, said ceramic preform bemg formed essentially of TιB 2 powder that is incorporated in a slurry and cast in a mold configured to form the golf club structure and dπed to produce a green body structure that is subjected to heat under appropnate temperatures and atmosphere conditions to sinter the green body structure and produce a porous sintered TiB-body having the desired golf club structure shape, subjecting the porous sintered TιB 2 structure to infiltration with matnx metal to produce the final golf club structure formed of a composite compnsmg a continuous phase of TιB 2 and a continuous phase of matnx metal 79 The method of claim 78 wherem the ceramic preform is prepared by dispersing the TιB 2 powder in an organic solvent, mixing a binder with a plasticizer and adding this mixture to the TιB 2 dispersion to form the slurry that is cast in the mold to form the green body structure that is used to produce the porous smtered TιB 2 body 80 The method of claim 78 wherein the porous sintered TiB- body is infiltrated with matnx metal by placing it in a container with an ingot of the matnx metal in contact therewith and subjecting the contents of the container to heat in a non oxidizing atmosphere, the heat being of sufficient temperature and for sufficient time to melt the matπx metal whereby it infiltrates the porous TιB 2 smtered preform structure and produces a golf club structure composite compnsed of a continuous phase of TιB 2 and a contmuous phase of the matπx metal 81 The method of claim 79 wherein the porous sintered TιB 2 body is infiltrated with matπx molded metal by placing it in a container with an ingot of the matπx metal in contact therewith and subjecting the contents of the container to heat in a non oxidizing atmosphere, the heat being of sufficient temperature and for sufficient time to melt the matπx metal whereby it infiltrates the porous TιB 2 sintered preform structure and produces a golf club structure composite compnsed of a continuous phase of TιB 2 and a continuous phase of the matnx metal 82 The method of claim 80 wherein the matnx metal is a stainless steel alloy 83 The method of claim 81 wherem the matπx metal is a stainless steel alloy 84 The method of claim 78 wherein the porous sintered TιB 2 body is infiltrated with the matπx metal by a squeeze casting process using molten matπx metal compnsed pnmanly of aluminum 85 The method of claim 79, wherein the porous TιB 2 body is infiltrated with the matrix metal by a squeeze casting process using molten matπx metal compnsed pnmanly of aluminum 86 The method of claim 78 wherein the golf club structure is a club head 87 The method of claim 82 wherein the golf club structure is a club head 88 The method of claim 83 wherein the golf club structure is a club head 89 The method of claim 84 wherem the golf club structure is a club head 90 The method of claim 85 wherem the golf club structure is a club head 91 The method of making a golf club structure compnsmg a club shaft that compnses assembling a bundle of hollow glass fibers, steel capillary tubes and graphite fibers, squeeze castmg the bundle with molten aluminum in a mold configured to form the golf club structure to produce a hybnd composite tube configured as a golf club shaft 92 The method of makmg a golf club shaft wherem a quantity of whiskenzed graphite fibers is laid up into a golf club structure compπsing a golf club shaft and impregnated with an epoxy resm to form a golf club shaft 93 The method of makmg a golf club structure that compπses laying up a quantity of whiskenzed graphite fibers to provide a preform in a mold configured to form the golf club structure, infiltrating the whiskenzed graphite fibers with matπx metal by squeeze casting with molten aluminum in the mold to produce aluminum matπx composite golf club structure 94 The method of claim 93 wherein the mold is configured to produce a golf shaft structure 95 A method of making a golf club structure that compπses, placing a fiber anay compnsed of graphite in a pressure mold configured to form the golf club structure impregnatmg the fiber anay with thermosetting phenolic resm, subjecting the resin impregnated graphite anay to thermal treatment in the mold to harden the molded golf structure, removing the hardened golf club structure from the mold and placing it in a controlled atmosphere furnace and subjecting it to heat in a pyrolizmg atmosphere and temperature for sufficient time to pyrolize the hardened golf club structure formed of a carbon-carbon composite compnsed of carbon matnx with graphite fibers 96 The method of claim 95 wherein the fiber anay is formed of woven graphite cloth 97 The method of claim 96 wherein the process of molding the phenolic impregnated graphite fiber array involves preheating the mold to about 165°C before placing and impregnating the fiber array in the mold 98 The method of claim 95 wherein the density of the pyrolyzed carbon composite golf club structure is increased by impregnating the composite structure a second time with thermosetting of phenolic resin followed by the further step of pyro zing the composite structure a second time by subjecting it to heat in a pyrolizmg atmosphere and temperature for sufficient time to pyrolize the reimpregnated structure 99 The method of claim 98 wherem the first pyrolysis is earned out by subjecting the hardened resin impregnated fiber structure to heat of about 1800°C temperature and wherein the second pyrolysis of the structure is earned out by subjecting the resin reimpregnated structure to heat above about 850°C 100 The method of claim 98 wherein the golf club structure is a golf club head 101. The method of claim 98 wherein the carbon composite golf club structure is formed in the shape of a golf club shaft. 102. The method of claim 95 wherein the composite golf club structure is subjected to the further step of impregnating it with epoxy resin followed by curing of the resin. 103. The method of claim 95 wherein the composite golf chib structure is subjected to the further step of impregnation by molten aluminum metal by molten aluminum squeeze casting. 104. The method of claim 98 wherein the second impregnation ofthe composite structure by the phenolic resin involves the use of a phenolic resin containing submicron particle size silicon powder which reacts with the carbon ofthe composite structure to form SiC. 105. The method of claim 104 wherein the carbon composite structure is subjected to third and fourth impregnations by phenolic resin, each of which involves the use of a phenolic resin containing silicon powder particles and each of which is followed by the step of pyrolyzing the impregnated structure by subjecting it to pyrolyzing heat treatment. 106. The method of claim 105 the second phenolic impregnation of the structure involved the use of phenolic resin containing about 25 volume percent of submicron size silicon carbon particles, the third phenolic resin impregnation involved the use of phenolic resin containing about 50 volume percent of submicron size silicon particles and the fourth phenolic resin impregnation involved the use of phenolic resin containing sufficient submicron size silicon particles to produce substantially 100% silicon carbide with the available carbon on pyrolysis and that produced a substantially pure silicon carbide matrix at the surface ofthe golf club structure. 107. The method of claim 95 wherein the pyrolized composite golf club structure is subjected to heat in a non oxidizing atmosphere in the presence of silicon metal grannules, the heat being raised at a temperature sufficiently high to melt the silicon metal whereby molten silicon infiltrates the porous carbon-carbon composite golf club structure and whereby some silicon carbide is formed with some silicon on the surface ofthe club structure. 108. The method of claim 107 wherein the mold is configured to form a golf club head. 109. The method of making a golf club structure that comprises: assembling a multilayer structure comprised of alternate layers of relatively hard metal and relatively soft metal, disposing the multilayer assembly in a mold configured to form a golf club structure including the face and sole of a golf club head wherein the multilayer assembly is oriented within the mold such that the ends ofthe respective alternate layers are presented as alternate strips of hard and soft metal ofthe club head face and the hard metal is presented as the club hard sole, and bonding the adjacent layers ofthe laminar assembly to one another by subjecting the assembly in the mold to heat and pressure adequate to cause diffusion bonding thereof. 110. The method of claim 109 wherein the relatively hard metal is a steel alloy and the relatively soft metal is a brass alloy. 111 The method of claim 110 wherem the steel alloy layers have thickness of about 0 125 mches and the brass alloy layers have a thickness of about 0 080 mches, whereby the alternate stnps of hard and soft metal compπsing the golf club head face are about 0 125 inches wide and 0 080 mches wide, respectively 112 The method of claim 109 wherein the relatively hard metal is a steel alloy and the relatively soft metal is an aluminum alloy 113 The method of claim 112 wherein both the steel alloy layers and the aluminum alloy layers have the same thickness of about 0 125 inches 114 The method of claim 110 wherein the diffusion bonding is earned out at a temperature of about 900° C and a pressure of about 2,000 psi for about 2 hours 115 The method of claim 112 wherein the diffusion bonding is earned out at a temperature of about 600°C and a pressure of about 2,000 psi for about 2 hours 116 The method of claim 109 wherein the relatively hard metal is compnsed of alumina the relatively soft metal is compnsed of aluminum and wherein the laminar assembly is a cast pπor to the diffusion bonding step 117 The method of claim 116 where the alumina layers have a thickness of about 0 040 inches and the aluminum layers have a thickness of about 0 625 mches 118 The method of claim 116 wherein the diffusion bonding is earned out at a temperature of about 620°C and a pressure of about 1,000 psi for about 3 hours 119 The method of making a golf club structure that compnses assembling a multilayer structure compnsed of alternate layers of a relatively hard metal contaimng matenal and a relatively soft non- metallic matenal, forming the multilayer structure to the shape of a golf club head including the face and toe of a golf club head, wherein the multilayer assembly is oπented such that the ends ofthe respective alternate layers are presented as alternate stnps of hard and soft matenal ofthe club head face and the hard matenal is presented as the club head sole, and bonding the adjacent hard and soft layers ofthe laminar assembly to one another 120 The method of claim 119 wherein the relatively hard metal contaimng matenal is alumina and the relatively soft non metallic matenal is thermoplastic nylon, and wherem said adjacent layers are bonded together by subjecting the laminar assembly to heat of about 100°C and pressure of about 121 The method of claim 119 where the relatively hard metal contaimng layer compπses steel and the relatively soft non metallic material layer is compnsed of thermoset epoxy resm, and wherein said adjacent layers are bonded together by pressing the laminar assembly together dunng the epoxy cure cycle 122 The method of claim 119 wherein steel layers are about 0 125 inches thick 123 The method of claim 119 wherein the relatively hard metal contaimng matenal is steel and the relatively soft non metallic material is comprised of a nylon composite with a filler of sihcon carbide. 124. The method of claim 123 wherein the steel layers are about 0.125 inches thick. 125. The method of claim 119 wherein the relatively hard metal containing material is high hardness steel and the relatively soft non metallic material is oak wood and wherein the adjacent layers ofthe laminar assembly are bonded together by an epoxy resin binder under molding pressure of about 350 psi during the heat cure cycle ofthe epoxy resin. 126. The method of claim 125 wherein the thickness ofthe steel layers is about 0.1875 inches and the thickness ofthe oak layers is about 0.625 inches. 127. The method of claim 109 wherein the relatively hard metal layers are comprised of titanium which has been nitrided to a depth of about 20 microns and the relatively soft metal layers are comprised of a composite of an aluminum matrix containing SiC, and wherein the laminar assembly includes alternate layers of a third material comprised of relatively hard beryllium copper, wherein the sequence of the successive layers is soft aluminum, hard titanium, soft aluminum, hard beryllium copper, etc. 128. The method of claim 127, wherein the aluminum matrix composite layers are about 0.0625 inches thick and the titanium layers are about 0.125 inches thick and the layers of beryllium copper are about 0.03 inches thick. 129. The method of making a golf club structure that comprises a multilayer structure formed of alternate layers of a relatively hard metal containing layers and a relatively soft metal containing layer, said structure being configured in the shape of a golf club head including the face and sole of a driver head wherein the multilayer structure is assembled and oriented such that the ends of the respective alternate layers are presented as alternate strips of hard and soft metal containing materials and the relatively hard metal containing material is presented as the sole of the driver head, wherein the respective hard and soft layers are formed by depositing successive layers of hard and soft metallic materials alternately on top of one another to build up a multilayer sheet formed ofthe hard and soft layers and wherein a plurality of such sheets are stacked and bonded together such that the edges of the respective stacked sheets form the alternate hard and soft strips ofthe driver club face and the relatively hard metal material forms the sole ofthe driver club. 130. The method of claim 129 wherein the relatively hard metal containing layer is titanium carbide and the relatively soft metal containing layer is stainless steel alloy, wherein the respective successive alternating layers ofthe metal containing materials are deposited by a sputter deposition process, and wherein the adjacent stacked multilayered sheets of soft and hard material are bonded to one another with epoxy resin to form the golf club driver. 131. The method of claim 130 wherein the titanium carbide layers are about 1.5 microns thick and the stainless steel alloy layers are about 8 microns thick. 132. The method of enhancing an aluminum driver head by providing a titanium carbide face and sole thereon that comprises forming a multilayer sheet formed of a plurahty of alternate layers of relatively hard titanium carbide and relatively soft stainless steel alloy, wherein the layer on one side ofthe sheet is comprised of titanium carbide and the layer on the opposite side ofthe sheet is comprised of steel alloy, bonding the steel alloy side of said multilayer sheet against the aluminum face and sole ofthe metal driver head, whereby the opposite side ofthe multilayer sheet comprised of titanium carbide becomes the face ofthe driver head and the outer surface ofthe sole ofthe driver. 133. The method of claim 132 wherein the multilayer sheet is bonded to the metal driver by a silver braze process. 134. The method of claim 132 wherein the aggregate thickness of the multilayer sheet is about 625 microns. 135. The method of making a golf club structure including the face of a golf club having grooves therein, comprising: assembling a multilayer assembly comprised of alternate layers of low carbon mild steel and hardened tool steel in a mold configured to form a golf club structure including the face of a golf club head wherein the multilayer assembly is oriented such that the ends ofthe respective alternate layers are presented as the face ofthe golf club structure, bonding the adjacent layers ofthe multilayer assembly to one another by subjecting the assembly in the mold to conditions of heat and pressure in an inert atmosphere adequate to cause diffusion bonding ofthe adjacent layers, and subjecting the club face portion ofthe bonded multilayer structure to grit blasting to selectively erode the mild steel, thereby forming grooves in the face ofthe club structure between adjacent layers ofthe hard steel. 136. The method of claim 135 wherein the golf club structure is a golf club head insert comprising the grooved face ofthe club head. 137. The method of claim 135 wherein the mild steel layers are about 1/16 inch thick and the hardened steel layers are about 3/16 inch thick. 138. The method of enhancing a titanium golf club structure that comprises: coating the golf structure with fullerenes, coating the fullerene coated golf club structure with titanium, causing the titanium coating and titanium ofthe golf club structure to react with the fullerene thereby forming an adherent coating of fullerene titanium carbide on the titanium surface ofthe golf club structure. 139. The method of claim 138 wherein the reaction between the titanium and the fullerenes is caused by inadiating the fullerene and titanium coated golf club structure with electrons. 140. The method of claim 138 wherein the golf club structure is coated with fullerenes by evaporative deposition process and the fullerene coated golf club structure is also coated with titanium by an evaporative deposition process. 141. The method of claim 138 wherein subsequent to coating the fullerene coated golf club structure with fullerene prior to causing the titanium to react with the fullerenes, a coating of submicron particle size boron powder is applied to the fullerene and titanium coated structure, and wherein the reaction of the fullerene and titanium is caused by inadiating the boron coated structure with electrons, whereby the alloy surface ofthe golf club structure comprises fullerene carbides of titanium and boron and titanium diboride. 142. The method of claim 138 wherein the fullerenes are comprised primarily of C w and C 70 as produced by the Hufl-man Kratschner process. 143. The method of claim 139 wherein the fullerenes are comprised primarily of C^ and C 70 as produced by the Huffinan/Kratschner process. 144. The method of claim 141 wherein the fullerenes are comprised primarily of C^ and C 70 as produced by the Huffinan/Kratschner process. 145. The method of enhancing a steel golf club structure by forming a hard TiC coating on a surface thereof that comprises sputter coating the steel surface with a layer of titanium and coating the titanium coated steel surface with a layer of fullerenes by evaporative coating a layer of fullerenes thereon in an argon plasma whereby a hard TiC coating is produced on the steel surface. 146. The method of claim 145 wherein the fullerenes coating is comprised primarily of C ω and a lessor amount of C 70 . 147. The method of making an insert for a golf club structure in the form of a putter face that comprises preparing a mixture of fullerenes with a soft plastic epoxy resin and forming said mixture into the shape ofthe putter face insert. 148. The method of claim 147 wherein the fullerenes are comprised primarily of C^ and a lessor amount ofC 70 . 149. The method of making a golf club structure that comprises: preparing a preform comprising a mixture of buckytubes containing single and multiwalled fullerenes with soot that also contains other fullerenes, placing the preform in a mold configured to form the golf club structure, and introducing molten aluminum into the mold with the preform and squeeze casting the contents ofthe mold to produce a composite golf club structure. 150. The method of making a golf club structure in the form of an insert for a putter club face that comprises: preparing a mixture of unrefined fullerenes as produced by the Huff an-Kratchner process and petroleum coke together with polyurethane and forming said mixture into the shape ofthe putter face insert. 151. The method of making a golf club structure in the form of a golf club head that comprises: preparing a mixture of fullerenes containing buckytubes and SiC powder consisting of nanoparticles, placing the prepared mixture in a mold configured to form the golf club structure together with tungsten particles that are selectively positioned in the toe, sole and hozel regions ofthe mold, and introducing molten aluminum into the mold with the preform comprising the fullerene mixture and tungsten particles, and squeeze casting the contents of the mold to produce a composite golf club head structure. 152. The method of making a golf club structure in the form of a golf club head that comprises: introducing an intermetallic alloy, namely, Fe40Al- 1 /_Mo, into a mold configured to form the golf club structure together with tungsten particles that are selectively positioned in the sole and toe regions ofthe mold and casting the contents ofthe mold to produce a golf club head formed of said intermetallic alloy and selectively weighted by the tungsten particles 153 The method of claim 152 wherein the mold is configured to form a golf club iron. 154. The method of making a golf club structure that comprises introducing an intermetallic alloy, namely, Ti-25Al-17Nb-3B-0.3Nd into a mold configured to form the golf club structure and casting the contents ofthe mold to produce a golf club structure formed of said intermetallic alloy 155 The method of claim 154 wherein the mold is configured to form a golf club driver 156 The method of producing a golf club structure comprising a golf club shaft that comprises hot extruding an intermetallic alloy, namely, Ti-25 Al -17Nb-3B-0.3Nd, through a die configured to form a golf club shaft 157 The method of producing a golf club structure comprising a golf club shaft that comprises, hot extruding an intermetallic alloy, namely, Ti-22Al-29Nb, through a die configured to form a golf club shaft 158 The method of producing a golf club structure that comprises, coating a quantity of metal particles comprised of Ti-24Al-14Nb-0.5Mo-3V with fullerene, and hot consolidating and forging the fullerene coated metal particles to produce a golf club structure formed ofthe resultant alloy 159 The method of claim 158 wherein the metal particles are coated with fullerenes by mixing the metal particles with a solution of buckyballs in an organic solvent and evaporating off the solvent 160 The method of making a golf club structure in the form of a golf club head using a mold configured to form the club head that comprises, preparing preformed tungsten components for selectively weighting the toe, sole and heel areas ofthe club head by pressing quantities of tungsten powder into preformed shaped components to fit into the conesponding areas of the mold and placing these shaped tungsten composites in such corresponding areas ofthe mold, introducing into the mold an intermetallic alloy, namely, Ti-22Al-27Nb and squeeze casting the contents ofthe mold to produce an intermetallic alloy golf club head with selectively distributed weighting 161 A golf club structure produced by the method of claim 1 comprising at least 50% ceramic phase by volume 162 A golf club structure produced by the method of claim 1 163 A golf club structure produced by the method of claim 23 164 A golf club structure produced by the method of claim 32 comprising a composite formed of a discontinuous ceramic phase in a continuous metal phase matrix 165 A golf club structure as defined in claim 164 wherein the ceramic phase is essentially SiC 166 A golf club structure as defined in claim 164 wherein the metal phase is primarily Al 167 A golf club structure as defined in claim 166 wherein the metal phase is primarily Al 168 A golf club structure produced by the method of Claim 69 comprising a composite formed in a continuous ceramic phase in a continuous metal phase matrix 169 A golf club structure as defined in claim 168 wherein the matrix metal is primarily aluminum. 170 A golf club as defined in claim 170 wherein the ceramic phase is formed essentially of alumina 171. A golf club structure produced by the method of claim 59 172 A golf club structure as defined in claim 171 wherein the golf club structure comprises, a composite formed of tungsten metal particles and a ceramic phase in a metal matrix comprised primarily of aluminum 173. A golf club structure as defined in claim 172 wherein the ceramic phase is comprised essentially of SiC 174 A golf club structure produced by the method of claim 66 175 A golf club structure produced by the method of claim 67 176. A golf club structure as defined in claim 175 wherein the golf club structure comprises a composite formed of a ceramic that is essentially SiC and an aluminum metal matrix 177 A golf club structure formed by the method of claim 78 178 A golf club structure as defined in claim 177 wherein the golf club structure comprises: a composite formed of a continuous phase of TiB- and a continuous phase of metal that is essentially stainless steel alloy 179. A golf club structure comprising: a hybrid composite golf club shaft formed of abundle of a plurality of hollow glass fibers and steel capillary tubes in an aluminum metal matrix 180 A golf club structure formed of a preform of whiskerized graphite fibers impregnated with an epoxy resin binder and configured in the form of a golf club shaft 181 A golf club structure comprised of a preform of whiskerized graphite fibers infiltrated with aluminum in the form of a golf club structure 182 A golf club structure produced by the method of claim 95 183 A golf club structure produced by the method of claim 104 184 A golf club structure comprises a composite formed of a carbon-carbon composite in an aluminum metal matrix 185. A golf club structure comprising a carbon-carbon composite formed of graphite fiber impregnated with thermoset phenolic resin 186 A golf club as defined in claim 185 wherein the composite further includes silicon carbide 187 A golf club structure produced by the method of claim 106 188 A golf structure comprising a golf club head having a club face defining the ball-hitting surface and a club sole defining the bottom surface as the head strikes a golf ball, said golf head comprising a multilayer structure comprised of alternate layers of relatively hard metallic multilayer and relatively soft metallic material onented such that the ends ofthe respective alternate layers as presented as alternate hard and soft metallic strips ofthe club head face and the hard metallic material is presented as the club head sole 189 A golf club head structure as defined in claim 188 wherein the hard metallic material is a steel alloy and the soft metallic material is brass alloy 190 A golf club head structure as defined in claim 188 wherein the hard metallic material is a steel alloy and the soft metallic material is an aluminum alloy 191 A golf club head structure as defined in claim 188, wherein the relatively hard metallic material comprises titanium and the relatively soft metallic material is comprised of an aluminum matrix containing SiC 192 A golf club head structure as defined in claim 191 wherein the multilayer structure further includes layers of relatively hard beryllium copper wherein the sequence ofthe successive layers is as follows relatively soft aluminum, relatively hard titanium, relatively soft aluminum, relatively hard beryllium copper, etc 193 A golf club structure as defined in claim 188 wherein the relatively hard metallic material comprises titamum carbide and the relatively soft metallic material compπses a stainless steel alloy 194 A golf structure produced by the method of claim 135 195 A golf club structure comprising the combination of a titanium golf club structure and a coating of fullerene titanium carbide adherent thereon 196 A golf club structure produced by the method of claim 138 197 A golf club structure produced by the method of claim 141 198 A golf club structure produced by the method of claim 145 199 A golf structure comprising the combination of a steel golf club structure and a coating of TiC applied thereon 200 A golf club structure produced by the method of claim 149 201 A golf club structure produced by the method of claim 151 202 A golf club structure produced by the method of claim 152 203 A golf club structure produced by the method of claim 158 204 A golf club structure produced by the method of claim 160 205 The method of enhancing a metal surface of a structure that comprises coating the metal surface with fullerenes and causing the fullerenes to react with the surface metal ofthe structure to form a carbide of said metal, thereby producing a metal carbide surface on said structure 206 The method of claim 205 wherein the metal surface ofthe structure is formed of titamum metal, whereby the metal carbide surface produced thereon is TiC 207 The method of claim 205 wherein the fullerene is caused to react with the metal ofthe structure by a heat treatment 208 The method of claim 206, wherein the fullerene is caused to react with the metal ofthe structure by a heat treatment. 209. The method of claim 207, wherein the heat treatment involving inadiation ofthe metal electrons. 210. The method of claim 208, wherein the heat treatment involving inadiation ofthe metal by inadiation by electrons. 211. The method of claim 205, wherein the structure is a golf club. 212. The method of claim of 206, wherein the structure is a golf club. 213. The method of claim 211, wherein the fullerene is caused to react with the metal ofthe structure by heat treatment. 214. The method of claim 212, wherein the heat treatment involves inadiating the metal with electrons. 215. The method of claim 206, wherein the titanium metal surface of the structure is apphed to the structure as a preliminary step prior to the step of coating it with fullerenes. 216. The method of claim 205 , wherein the metal surface comprises an alloy containing one or more metals that reacts with fullerenes to form carbides. 217. The method of claim 206, wherein the metal surface comprises an alloy containing one or more metals that reacts with fullerenes to form carbides. 218. The method of claim 216, wherein the alloy is comprised of an iron group metal and one or more other elements that react with fullerenes to form a carbide. 219. The method of claim 217, wherein the other elements are selected from among titanium, chromium, molybdenum, silicon, vanadium, yttrium and the rare earths in the 4f and 5f series, and the refractory metals. 220. The method of claim 216, wherein the fullerene is caused to react with the metal ofthe alloy by a heat treatment. 221. The method of claim 1, wherein the ceramic fiber anay is comprised of alumina. 222. The method of making a composite structure that comprises the steps of: forming a fibrous preform of said structure from a naturally occurring starting product or a product derived therefrom that contains one or more of a cellulose, semi cellulose or lignin and which, upon pyrolization, forms a carbonaceous char, subjecting said fibrous preform to heat under non oxidizing pyrolyzing condition to form a porous char of said preform, and infiltrating said porous char with a matrix forming material. 223. The method of claim 222 wherein the starting product is wood. 224. The method of claim 223 wherein the starting product is laminated wood. 225. The method of claim 222 wherein the starting product is paper. 226. The method of claim 225 wherein the paper is disposed in layers alternately with layers of carbon fabric and subjected to heat and pressure in a die to form the preform prior to subjecting it to the pyrolysis step. 227. The method of claim 223 wherein the infiltration step comprises infiltration of the porous char by molten aluminum 228 The method of claim 227 wherein the infiltration is carried out in two steps, first by placing the porous char in a metal die and introducing superheat aluminum into the porous char under pressure, then by removing the aluminum impregnated char from the die and further infiltrating it with molten aluminum 229 The method of claim 223 wherein the infiltration step comprises placing the porous char in a vacuum chamber containing a suspension of isopropyl alcohol and silicon carbide with diamond particles to selectively impregnate a portion of the porous char with said particles, evaporating the isopropyl alcohol, and infiltrating the particle impregnated char with aluminum by squeeze casting in a heated die mold 230 The method of claim 229 wherein the composite structure is a golf club, and the portion of the structure impregnated with particles is the face and sole ofthe club structure 231 The method of claim 223 wherein the infiltration step comprises infiltration ofthe porous char by squeeze casting with molten bronze 232 The method of claim 225 wherein the infiltration step comprises squeeze casting with molten aluminum 233 The method of claim 225 wherein the infiltration step comprises squeeze casting with molten aluminum 234 The method of claim 225 wherein the paper starting product is shredded and soaked with water and water-soluable glue and molded under heat and pressure to form a preform in the shape of an engine piston and wherein the pyrolyzed char preform is infiltrated with magnesium by squeeze casting to produce a composite carbon fiber reinforced magnesium piston 235 The method of claim 223 wherein the porous chaned preform is vacuum impregnated with preceramic polymer ceraset, then heat treated to produce ceramic matrix of silicon carbide, followed by further reimpregnation with said polymers and further pyrolysis to produce a carbon fiber reinforced silicon carbide matrix composite structure 236 The method of claim 234 wherein the porous charred preform is vacuum impregnated with alumina sol-gel to form the matrix, instead of preceramic polymer ceraset 237 The method of claim 234 wherein the porous chaned preform is impregnated by chemical vapor infiltration to deposit silicon carbide matrix using methyltrichlorosilane 238 The method of claim 222 wherein the starting product is comprised of alternate layers of shredded paper and carbon fabric that is cured and die formed under heat and pressure prior to the pyrolysis step and wherein the preformed pyrolyzed char is infiltrated with aluminum by squeeze casting 239 The method of claim 222 wherein the starting product is comprised of a combination of paper and carbon fabric that is cured and formed under heat and pressure prior to the pyrolysis step and wherein the preformed pyrolyzed char is infiltrated by infiltrating with thermoplastic nylon 240. The method of claim 235 wherein the porous chaned preform is subjected to chemical vapor reaction processing to convert the carbon char to silicon carbide prior to the step of infiltrating it with preceramic polymer ceraset and the further pyrolysis step, whereby a silicon carbide/silicon carbide composite structure is produced. 241. The method of claim 222 wherein the starting product is comprised of alternate layers of shredded paper and carbon fabric and wherein the infiltration step involves infiltration with thermoplastic nylon. 242. The method of claim 222 wherein the starting product is comprised of alternate layers of shredded paper and carbon fabric and wherein the infiltration step involves infiltration with thermoset phenolic resin. 243. The method of claim 222 wherein the starting product is comprised of alternate layers of shredded paper and carbon fabric and wherein the infiltration step involves infiltration with a catalyzed cured epoxy resin. 244. The method of claim 222 wherein the starting product is comprised of softened paper and carbon fibers and wherein the infiltration step involves infiltration with molten magnesium by squeeze casting. 245. The method of claim 222 wherein the starting product is comprised of cotton. 246. The method of claim 222 wherein the starting product is comprised of wool. 247. The method of claim 245 wherein the infiltration step involved infiltration with molten aluminum by squeeze casting. 248. The method of claim 247 wherein the porous char is infiltrated with particles of sihcon carbide and diamond prior to the step of infiltrating it with molten aluminum. 249. The method of claim 247 wherein the porous char is converted to silicon carbide by chemical vapor reaction processing prior to the step of infiltrating it with molten aluminum

Inventors: KELLY WILLIAM B, LOUTFY RAOUF O, NEWELL KENNETH J, PICKARD SION M, WITHERS JAMES C, KELLY, WILLIAM, B., LOUTFY, RAOUF, O., NEWELL, KENNETH, J., PICKARD, SION, M., WITHERS, JAMES, C.
Applicants: MAT & ELECTROCHEM RES CORP, MATERIALS AND ELECTROCHEMICAL RESEARCH (MER) CORPORATION
Application year: 2000
Main classification: A63B53
IPC codes: A63B53, C22C1, C22C47