FIBRE-REINFORCED METAL MATRIX COMPOSITES

Abstract: A metal matrix composite comprises essentially-aligned, fine-diameter inorganic oxide fibres embedded in a metal matrix material such as a light metal, for example aluminium or magnesium or an alloy thereof. In a particular embodiment the fibres are nominally-continuous and preferably are of mean diameter below 5 microns. The composite can be made by liquid infiltration of a fibre preform comprising the fibres bound together with an inorganic or an organic binder or (in the case of short fibres) by extrusion of a mixture, for example a suspension, of the fibres and powdered metal matrix material.

Description: This invention relates generally to the reinforcement of metals with inorganic fibres and more particularly to fibre-reinforced metal matrix composites comprising inorganic oxide fibres, notably alumina fibres, embedded as reinforcement in a metal matrix. The invention includes preforms made of inorganic oxide fibres and suitable for incorporation as reinforcement in a metal matrix and processes for the preparation of metal matrix composites and preforms. Metal matrix composites (hereinafter abbreviated to MMCs) are known comprising inorganic oxide fibres such as polycrystalline alumina fibres in certain forms embedded as reinforcement in a matrix comprising a metal such as aluminium or magnesium or an alloy containing aluminium or magnesium as the major component. A fibre commonly used in such MMCs is alumina fibre in the form of short (e.g. up to 5 mm), fine-diameter (e.g. mean diameter 3 microns) fibres which are randomly oriented at least in a plane perpendicular to the thickness direction of the composite material. MMCs of this type containing alumina fibres in alloys have begun to be used in industry in a number of applications, notably in pistons for internal combustion engines wherein the ring-land areas and/or crown regions are reinforced with the alumina fibres. MMCs containing aligned, continuous alumina fibres have also been proposed for use in applications where uni-directional strength is required, for example in the reinforcement of connection rods for internal combustion engines. In MMCs of this type, the alumina fibres are of relatively large diameter, for example at least 8 and usually at least 10 microns diameter, and comprise a high proportion, for example from 60 to 100 %, of alpha alumina. Such fibres exhibit high strength but poor flexibility. US-3,218,697 discloses the reinforcement of metals with loose, short fibres having a length of up to ½ inch (about 12.5 mm). GB-2,080,865 also discloses fibre-reinforced metal matrix composites comprising a metal or alloy matrix and an inorganic fibre-reinforcing material. Hitherto, aligned, fine diameter (typically below 10 microns and preferably below 5 microns mean diameter), nominally continuous (typically length greater than 0.5 metre and preferably several metres) fibres, and MMCs containing them have not been produced. The present invention is concerned with MMCs and preforms for MMCs comprising aligned, nominally continuous, fine-diameter fibres. According to the invention there is provided a metal matrix composite comprising a metal matrix material in which is embedded a fibrous product, said fibrous product comprising a plurality of essentially aligned and nominally continuous inorganic oxide fibres of mean diameter below 10 microns and preferably below 5 microns, wherein a degree of non-alignment of some of the fibres provides for fibre intertwining conferring lateral cohesion on said product. Also according to the invention there is provided a preform suitable for incorporation in a metal matrix material to produce a metal matrix composite in accordance with the immediately preceding paragraph and comprising a fibrous product bound together with a binder, said fibrous product comprising a plurality of essentially aligned and nominally continuous inorganic oxide fibres of mean diameter below 10 microns, wherein a degree of non-alignment of some of the fibres provides for fibre intertwining conferring lateral cohesion on said product. The binder preferably is or contains an inorganic binder. The inorganic oxide fibres may if desired be used in admixture with other types of fibres and/or with non-fibrous particulate materials, for example silicon carbide whiskers, aluminosilicate fibres and particulate alumina, zirconia or silicon carbide, the proportion of other material(s) in such mixtures typically being from about 40% to about 80% of the fibres. The volume fraction of the fibres in the MMC (and in the preform) may vary within wide limits depending upon the required duty of the MMC and hence on the reinforcement. As a guide, volume fractions of fibres from about 10% to 60% or even higher can be achieved. The use of essentially-aligned fibres in accordance with the invention has the advantage of enabling high volume fractions of fibres, for example greater than 35%, to be achieved without significant breakage of the fibres. Incorporation of large amounts of fibres in metal matrix composites involves packing the fibres together to obtain high volume fractions of the fibres in the composites. Inorganic oxide fibres are hard and quite brittle and compression of a randomly-oriented mat or blanket of the fibres results in extensive breakage of the fibres. Orientation or alignment of the fibres results in less breakage of the fibres when compression is applied to obtain high volume fractions of fibres. The inorganic oxide fibres may be relatively long fibres of length several cms or even several metres (depending of course upon the length of the MMC being produced); in the case of small MMCs most of the fibres may be continuous throughout the length of the MMC. long fibres cannot be aligned during the MMC or preform fabrication technique and should be pre-aligned, for example in the form of a mat or blanket of essentially-aligned fibres. Essentially-aligned fibre products, i.e. product forms such as a mat or blanket in which the fibres as spun are essentially aligned, can be compressed to increase the volume fraction of fibres therein to greater than 25% without undue breakage of the fibres and in particular with only a very low degree of fibre breakage compared with the breakage resulting from compression to the same volume fraction of fibres of a product made of randomly oriented fibres of the same diameter. In a particular embodiment of the invention the product, which comprises essentially aligned, nominally-continuous fibres is compressible to increase the volume fraction of fibres therein to about 50% or greater without significant breakage (i.e. reduction in length) of the fibres. The pressure applied to compress the fibres may be from 5 to 1000 MPa without causing extensive breakage of the fibres. By comparison, compression of a randomly-oriented mat of fibres of the same diameter to a volume fraction of fibres of 12 to 15% results in extensive breakage of the fibres. Breakage of fibres during compression of the product results in a decrease in the tensile strength of the product in the general direction of alignment of the fibres. Excessive breakage of fibres is denoted by an abrupt fall, i.e. a fall to below 50%, in the specific tensile strength (= breaking force/mass of sample) of the product. By compression "without significant breakage" of the fibres we mean compression without causing a fall to below 50% in the specific tensile strength of the product. The degree of compression at which significant breakage of the fibres occurs, as represented by an abrupt fall in specific tensile strength of the product, is roughly determined by compressing strips of the product (each strip of the same length and approximately the same breadth and weight) to different volume fractions of fibres, determining the specific tensile strength of each compressed strip and noting the degrees of compression between which an abrupt fall is observed in the specific strength of the compressed samples. By way of illustration strips of an essentially aligned-fibre product according to the invention wherein the volume fraction of fibres was 10% and of size 50 mm x 3 mm (with the length direction in the general direction of alignment of the fibres) were compressed to thicknesses corresponding to volume fractions of fibres of 20, 30, 35, 40 and 45% in a 50 mm x 3 mm channel with matching plunger. The tensile strength of each compressed strip was determined and the specific tensile strength of the compressed strip was calculated. In this experiment the specific tensile strength of the strips was found to be ± 20% the same for the strips compressed to volume fractions of 20, 30 and 35% whilst the specific tensile strength of the strip compressed to 40% volume fraction had fallen to only about 5% of the strength of the first three compressed strips. The degree of compression at which the fibres suffered significant breakage accordingly was compression to between 35 and 40% volume fraction of fibres. As a rough guide to the compressibility of the fibre product, the abrupt fall in the specific tensile strength of the product indicating excessive breakage of the fibres can be detected by pulling the product sample between the fingers; the undamaged product resists pulling apart whilst a damaged product pulls apart easily. Using this simple test an experienced operator can determine reasonably accurately the point at which excessive damage of the fibres occurs. The fibres in the MMC and the preform are essentially aligned and a high degree of fibre orientation in the MMC and the preform is achieved. If desired, substantially all of the fibres in the MMC or the preform can be oriented in the same direction of alignment so as to impart one-direction strength to the article. Alternatively, a multi-layer fibre reinforcement can be employed in which the fibres in a particular layer are essentially aligned but in which the fibres in different layers are cross-plied, i.e. oriented in different directions, so as to impart multi-direction strength to the article. It is to be understood that MMCs and preforms comprising a multi-layer fibre reinforcement wherein the fibres in each layer are aligned but wherein the direction of orientation of the fibres in different layers is different are nevertheless within the scope of the invention. The present invention resides in modification of the stiffness/modulus and high temperature performance of metals, especially lightweight metals such as aluminium and magnesium and their alloys, by incorporating therein fibres of high strength and modulus. The volume fraction of fibres in the composite material may be for example up to 60% or even higher, typically from 10% to 50%, of the composite. The composite may contain, for example, from 0.1 to 2.5 g/ml of alumina fibres, typically from 0.2 to 2.0 g/ml, or up to 3 g/ml of zirconia fibres. The fibre content of the composite may vary throughout the thickness of the composite being high for example in the outer face (in use) of the composite and lower in the opposite face. Changes in fibre content may be uniform or stepwise. An embodiment of the invention resides in an MMC wherein the fibre content varies stepwise and is provided by a laminate of MMCs of different fibre contents, the individual MMCs being separated if desired in an integral laminate by a layer of the metal e.g. a sheet of aluminium or magnesium. The composite may have a backing sheet of a suitable textile fabric, for example a sheet of Kevlar fabric. The reinforcement in the MMCs is an essentially-aligned fibre product comprising inorganic oxide fibres of average diameter not greater than 10 microns and preferably not greater than 5 microns. By the term "essentially-aligned-fibre product" is meant a product form in which the fibres extend in the same general direction but may not in the case of long fibres be truly parallel over their entire length so that a degree of overlap of fibres is possible and any particular fibre may extend over part of or even its entire length at an angle, e.g. up to 30°, or even higher with respect to the general direction of alignment of the fibres. In such a product the overall impression is of fibres which are parallel but in fact a slight degree of overlap and intertwining of fibres may be desirable in order to confer lateral stability to the product to enable it to be handled without undue separation of the fibres. We prefer that at least 90% of the fibres are essentially parallel. The inorganic oxide fibres are "nominally continuous" by which term is meant that the individual fibres may not be truly continuous in the sense of having infinite length or of extending the entire length of the product but each fibre has appreciable length, e.g. at least 0.5 metre and usually several metres, such that the overall impression in the product is of continuous fibres. Thus free ends of fibres appear in the product, representing an interruption in fibre continuity, but in general the number of free ends in any square cm of the product will be relatively low and the proportion of interrupted fibres in a square cm will be no greater than about 1 in 100. A typical fibre reinforcement for use in making MMCs according to the invention and comprising nominally-continuous fibres is a mat or blanket of thickness a few mms. In a product of this thickness the number of free ends of fibre in a square cm of the product may be up to about 2500; this compares with about 50,000 free ends in a product of similar mass made of short (up to 5 cms) staple fibres of the same diameter. The product made of nominally continuous fibres is thus very different in appearance and properties from a product made of short, staple fibres. The fibres in the fibre reinforcement are polycrystalline metal oxide fibres such as alumina and zirconia fibres and preferably are alumina fibres. In this case the alumina fibres may comprise alpha-alumina or a transition phase of alumina, notably gamma- or delta-alumina, depending largely upon any heat treatment to which the fibres have been subjected. Typically the fibres will comprise wholly a transition alumina or a minor proportion of alpha-alumina embedded in a matrix of a transition alumina such as eta-, gamma- or delta-alumina. We prefer fibres comprising zero or a low alpha-alumina content and in particular an alpha-alumina content of below 20% and especially below 10% by weight. In general the greater the alpha-alumina content of the fibre, the lower is its tensile strength and the lower is its flexibility. The preferred fibres of the invention exhibit acceptable tensile strengths and have a high flexibility. In a particular embodiment of the invention, the fibres have a tensile strength greater than 1750 MPa and a modulus greater than 200 GPa. In the case of alumina fibres, the density of the fibres is largely dependent upon the heat treatment to which the fibres have been subjected. After spinning and at least partial drying, the gel fibres are heated in steam at a temperature of from 200°C to about 600°C to decompose the metal oxide precursor and then are further heated to sinter the resulting metal oxide fibres. Sintering temperatures of 1000°C or higher may be employed. After the steam treatment the fibres are highly porous and high porosity is retained during sintering up to, for example, 900-950°C. However, after sintering at for example, 1100°C or higher the fibres have little porosity. Thus by controlling the sintering temperature, low density fibres of high porosity or high density fibres of low porosity may be obtained. Typical apparent densities for low density and high density fibres are 1.75 g/ml and 3.3 g/ml; fibres of any desired density within this range can be obtained by careful control of the heat treatment to which the fibres are subjected. We have observed that the modulus of alumina fibres does not appear to be greatly affected by the heat treatment programme above 800°C to which the fibres have been subjected and does not vary greatly in accordance with the apparent density of the fibres. For instance, over the range of apparent fibre densities of 2 g/ml to 3.3 g/ml, modulus has typically been observed to change from about 150-200 GPa to about 200-250 Gpa. Thus the ratio of fibre modulus to fibre density (= specific modulus) is generally greatest in respect of low density fibres. Aligned and nominally-continuous fibre products can be produced by a blow-spinning technique or a centrifugal spinning technique, in both cases a spinning formulation being formed into a multiplicity of fibre precursor streams which are dried at least partially in flight to yield gel fibres which are then collected on a suitable device such as a wind-up drum rotating at high speed. The speed of rotation of the wind-up drum will depend upon the diameter of the drum and is matched to the speed of spinning of the fibres so that undue tension is not applied to the weak gel fibres. As a guide only, a wind-up drum speed of 1500 rpm is fairly typical for a drum of diameter 15 cms. In practice it may be desirable to wind the wind-up drum slightly faster than the speed of extrusion of the fibres so that the fibres are subjected to slight tension which serves to draw down the fibres to the desired diameter and to keep the fibres straight. Of course, the applied tension should not be sufficient to break the majority of the fibres. As stated hereinbefore, the fibres may not be truly continuous and generally are of length a few metres. The minimum fibre length in the case of collection on a wind-up drum is approximately equal to the circumference of the wind-up drum since fibres which are shorter than this tend to be flung off the rotating drum. Because the fibres are not of infinite length it is important that a multiplicity of fibres be spun simultaneously so that the resulting collection of fibres pass through the apparatus in a bundle or sheet whereby free ends of fibres are carried along by the bundle or sheet of fibres which gives an overall impression of fibre-continuity. The spinning formulation may be any of those known in the art for producing polycrystalline metal oxide fibres and preferably is a spinning solution free or essentially free from suspended solid particles of size greater than 10, preferably of size greater than 5, microns. The rheology characteristics of the spinning formulation can be readily adjusted to result in long fibres rather than short fibres, for example by use of spinning aids such as organic polymers or by varying the concentration of fibre-forming components in the formulation. The fibre reinforcement can be a sheet or mat comprising essentially-aligned and nominally-continuous fibres exhibiting lateral cohesion as a result of entanglement of some of the fibres. A small degree of non-alignment of the fibres in the product has the advantage of conferring lateral stability on the product to enable it to be handled satisfactorily. A preferred product possesses a degree of lateral cohesion such that significant separation of the fibres is resisted under normal product handling conditions. Preferably the lateral cohesion in the product is such that the product exhibits a tensile strength of at least 25,000 Pa in a direction perpendicular to the general direction of alignment of the fibres. The lateral strength of the product will depend to some extent upon the diameter of the fibres since given the same degree of entanglement, fatter fibres will produce a greater lateral strength than will thinner fibres; in fact fatter fibres tend to be less entangled than thinner fibres so that in practice fatter fibres result in lower lateral strengths in the product. A typical product of this type is a sheet or mat of thickness a few, say 2-5 mms, width several cms and length a metre or more, obtained by collecting the fibres on a wind-up drum and cutting the collected fibres parallel to the axis of the wind-up drum (the length and width of the sheet or mat thus being determined by the dimensions of the wind-up drum). Other product forms such as yarns, rovings, tapes and ribbons can be obtained either from the product collected on a wind-up drum or directly by using a suitable fibre-collection technique. In the case of a product collected on a wind-up drum, the product can be cut in the general direction of alignment of the fibres to provide tapes or ribbons which can be drawn off from the drum and converted if desired into yarns or rovings. A fibre product in the form of yarns,rovings, tapes or ribbons can be converted into woven products using suitable weaving techniques. Any metal may be employed as the matrix material which melts at a temperature below about 1200°C. However a particular advantage of the invention is improvement in the performance of light metals so that they may be used instead of heavy metals and it is with reinforcement of light metals that the invention is particularly concerned. Examples of suitable light metals are aluminium, magnesium and titanium and alloys of these metals containing the named metal as the major component, for example representing greater than 80% or 90% by weight of the alloy. As is described hereinbefore, the fibres may be porous, low density materials or high density materials of low or zero porosity depending upon the heat treatment to which the fibres have been subjected. Since the fibres can constitute 50% or more by volume of the MMC the density of the fibres can significantly affect the density of the MMC. Thus, for example, a magnesium alloy of density about 1.9 g/ml reinforced with 50% volume fraction of fibres of density 3.3 g/ml will provide an MMC of density about 2.6 g/ml, i.e. denser than the alloy itself; conversely an aluminium alloy of density 2.8 g/ml reinforced with 50% volume fraction of fibres of density 2.1 g/ml will provide an MMC of density 2.45 g/ml, i.e. less dense than the alloy itself. The present invention thus enables MMCs to be produced having a predetermined density within a wide range. Aluminium and magnesium and their alloys typically have a density in the range 1.7 to 2.8 g/ml and since the density of the fibres can vary from about 1.75 to 3.3 g/ml, MMCs of density 1.9 to about 3.0 g/ml can readily be produced. An especially light metal or alloy reinforced with an especially light fibre is a preferred feature of the invention, in particular magnesium or a magnesium alloy of density less than 2.0 g/ml reinforced with a fibre (notably an alumina fibre) of density less than or about 2.0 g/ml to provide an MMC of density less than 2.0 g/ml. If desired the surface of the fibres may be modified in order to improve wettability of the fibres by the metal matrix material and other fibre characteristics. For example the fibre surface may be modified by coating the fibres or incorporating a modifying agent in the fibres to improve their chemical resistance or control interfacial bonding and hence properties such as fracture toughness . Alternatively, the metal matrix material may be modified by incorporating therein elements which enhance the wettability of the inorganic oxide fibres by the matrix material, for example tin, cadmium, antimony, barium, bismuth, calcium, strontium or indium. For making the MMCs according to the invention we prefer a preform/liquid metal infiltration technique in which the fibres are first assembled into a preform wherein the fibres are bound together by a binder, usually one consisting of or containing an inorganic binder such as silica. This binder may be fugitive, i.e. displaced by the molten metal with which the preform is infiltrated. It is possible to incorporate elements in the binder which enhance the wettability of the fibres by the matrix material during infiltration of the preform. Whilst we prefer to employ a preform in which the fibres are bound together with a binder, especially an inorganic binder, so as to constrain the fibres against movement during infiltration of the preform with liquid metal, it is possible to employ an assembly of fibres in which the fibres are constrained against movement by means other than an inorganic binder. One way of doing this is to pack the fibres into a tube or mould. Aligned long, continuous or nominally-continuous fibres can be packed directly into a mould having moving parts and compressed to the required volume fraction fibres on closure of the mould. In the preferred preform/infiltration technique, the molten metal may be squeezed into the preform under pressure or it may be sucked into the preform under vacuum. We have observed that application of pressure or vacuum to facilitate infiltration of the preform with a liquid metal matrix material obviates any problems of wetting of the fibres by the matrix material. Infiltration of the metal into the preform may be effected in the thickness direction of the preform or at an angle, preferably at 90°, to the thickness direction of the preform and along the fibres. In the preform the aligned fibres will usually be orientated in a plane perpendicular to the thickness direction of the preform. Infiltration of the metal into the preform in the thickness direction, i.e. across the fibres, may cause separation of the fibres and/or compression of the preform and loss of reinforcement properties in the MMC; infiltration of the metal into the preform along the fibre length in the direction of alignment/orientation of the fibres reduces the tendency of the fibres to separate and/or the tendency to compress the preform and may lead to enhanced reinforcement of the metal by the fibres. Infiltration of the molten metal into the preform may in the case of aluminium or aluminium alloys be carried out under an atmosphere containing oxygen, e.g. ambient air, but when using certain metal matrix materials such as, for example, magnesium and magnesium alloys, oxygen is preferably excluded from the atmosphere above the molten metal. Molten magnesium or an alloy thereof is typically handled under an inert atmosphere during infiltration thereof into the preform, for example an atmosphere comprising a small amount (e.g. 2%) of sulphur hexafluoride in carbon dioxide in order to avoid oxidation of the (molten) metal. Preparation of preforms for infiltration by molten metal matrix materials can be effected by a wide variety of techniques, including for example pultrusion, filament-winding, injection moulding, compression moulding, spraying or dipping. Such techniques are well known in the production of fibre-reinforced resin composites and it will be appreciated that use of mobile binder(s) or a suspension of binder(s) instead of a resin in the known techniques will yield a preform. Other techniques for producing preforms include hand lay-up techniques and powder-compaction techniques. In hand lay-up techniques thin samples of fibrous materials, e.g. woven materials, are impregnated with a suspension of binder(s) and multiple layers of the wet, impregnated samples are assembled by hand and the assembly is then compressed in a die or mould to yield an integral preform. In powder-compaction techniques, layers of fibrous materials and binder(s) in powder form are assembled, e.g. by hand lay-up, and the assembly is then compressed in a die or mould at a temperature sufficient to melt the powdered binder(s) to form an integral preform. The binder used to form the preform may be an inorganic binder or an organic binder or a mixture thereof. Any inorganic or organic binder may be used which (when dried) binds the fibres together to an extent such that the preform can be handled without damage. Examples of suitable inorganic binders are silica, alumina, zirconia and magnesia and mixtures thereof. Examples of suitable organic binders are carbohydrates, proteins, gums, latex materials and solutions or suspensions of polymers. The amount of binder(s) may vary within a wide range of up to about 50% by weight of the fibres in the preform but typically will be within the range of 10% to 30% by weight of the fibres. By way of a guide, a suitable mixed binder comprises from 1 to 20%, say about 5%, by weight of an inorganic binder such as silica and from 1 to 10%, say about 5%, by weight of an organic binder such as starch. In the case where the binder is applied in the form of a suspension in a carrier liquid, an aqueous carrier liquid is preferred. As is discussed hereinbefore, the MMCs of the invention can be made by infiltration of a preform. Alternatively, any of the other techniques described for making preforms may be adapted for making MMCs directly by employing a metal matrix material instead of a binder or mixture of binders. Additional techniques for making MMCs include chemical coating, vapour deposition, plasma spraying, electro-chemical plating, diffusion bonding, hot rolling, isostatic pressing, explosive welding and centrifugal casting. In making MMCs, care needs to be exercised to prevent the production of voids in the MMC. In general, the voidage in the MMC should be below 10% and preferably is below 5%; ideally the MMC is totally free of voids. The application of heat and high pressure to the MMC during its production will usually be sufficient to ensure the absence of voids in the structure of the MMC. The MMCs according to the invention may be used in any of the applications where fibre-reinforced metals are employed, for example in the motor industry and for impact resistance applications. The MMC may, if desired, be laminated with other MMCs or other substrates such as sheets of metal. The invention is illustrated by the following Examples in which the fibre reinforcement was produced as follows: Preparation of a gel spinning solution 0.1 gm of thiourea was dissolved in 600 gms of commercial aluminium chlorhydrate solution (Locron L available from Hoechst AG). The solution was stirred with a propeller stirrer and 6.5 gms of polyethylene oxide (Union Carbide Polyox WSR-N-750) were added; the polymer dissolved over a period of 2 hours. At this stage the solution viscosity was approximately 1 poise. 160 gms of aluminium chlorhydrate powder (Hoechst Locron P) were then added to the solution; the powder dissolved after a further 2 hours stirring. 35 gms of a siloxane surfactant, Dow DC 193, were then added. The solution was filtered through a glass fibre filter (Whatman 6FB) rated nominally between 1 and 1.5 microns. The solution viscosity, measured on a low shear Ubbelhode capillary viscometer was 18 poise. Formation of Fibres The solution was extruded through a row of holes on either side of which were slits through which air was directed to converge on the emerging extrudate. The air flowed at 60 m/sec and was humidified to 85% relative humidity at 25°C. Further streams of heated dry air at 60°C flowed outside the humidified air streams. Long, (nominally continuous) gel fibres were formed and these were fed with the co-flowing air streams into a converging duct at the base of which the mixture impinged at a gas velocity of 14 m/sec on a rotor coated with fine Carborundum paper and rotating at 12 m/sec peripheral velocity. A blanket of essentially aligned fibres accumulated on the rotor. After 30 minutes, the rotor was withdrawn from the base of the converging duct, stopped and the aligned-fibre blanket was cut parallel to the axis of the rotor and removed from the rotor. At this stage the gel fibres contained 43% by weight of refractory material with silica constituting 4.1% by weight of the refractory material. The median gel fibre diameter was 5 microns. The "as spun", gel fibre blanket was dried for 30 minutes in an oven at 150°C and then was immediately transferred to a second oven purged with steam at 300°C and 1 atmosphere pressure. The purge steam temperature was raised to 600°C over a period of 45 minutes, whereupon the oven was purged with air and the temperature was then increased gradually to 900°C over a period of 45 minutes. At this stage, the fibres were white and porous. The main crystalline phase was eta-alumina, the porosity 40% by volume and the surface area 140 m²/g. The median diameter of the fibres was 3.6 microns. The fibre product, where indicated, was then heated in air for 15 minutes at 1300°C. A refractory fibre of median diameter 3 microns was obtained. The principle alumina phase in the fibre was delta-alumina in the form of small crystallites together with 3% by weight of alpha-alumina. The fibre porosity was 10%. Example 1 A circular preform of size 100 mm diameter and 15 mm thickness was prepared from polycrystalline alumina fibres by a hand lay-up technique. Circular samples (100 mm diameter) were cut from a sheet or mat of essentially-aligned, nominally-continuous, polycrystalline alumina fibres fired at 1300°C. The density, tensile strength and modulus of the fibres were 3.3 g/ml, 2,000 MPa and 300 GPa. The mat had a lateral strength of 42,500N/m². The samples of fibre mat were sprayed with an aqueous silica sol in an amount providing a pick-up of silica (dry weight) of about 5% by weight of the fibres. Immediately following the silica application, the sample were sprayed with an aqueous solution of starch and a retention aid available under the trade name "Percol" in an amount to provide a pick-up (dry weight) of 5% starch and 2% "Percol" by weight of the fibres. The starch/"Percol" solution serves to flocculate the silica sol onto the fibres and retain the silica on the fibres. Impregnated circular samples of the fibres were laid-up by hand in a cylindrical mould such that the fibres in the several layers were aligned in the same direction and the assembly was compressed to a predetermined density corresponding to a predetermined volume fraction of fibre. The assembly was dried in air at approximately 110°C for about 4 hours and then was fired at 1200°C for 20 minutes to consolidate the assembly and burn out any organic materials. Using this technique, preforms were produced of fibre volume fractions 0.2 and 0.5 which were designated "Preform A" and "Preform B" respectively. Two further preforms, designated "Preform C" and "Preform D" of fibre volume fraction 0.2 and 0.5 respectively were produced by the above technique from a mat of essentially-aligned, nominally-continuous polycrystalline alumina fibres fired at 900°C. The density, strength and modulus of the fibres were 2.1 g/ml, 2100 MPa and 210 GPa. The mat had a lateral strength of 35,000N/m². In making Preforms C and D the temperature at which the assembly of fibres was fired was 900°C instead of 1200°C. MMCs were made from the preforms as follows. Each of the preforms A and B was placed in a die preheated to 500°C and molten metal at a temperature of 840°C was poured onto the preform. Each of preforms C and D was preheated at 840°C in a die and molten metal at 840°C was poured onto the preform.. The metal was an aluminium alloy available as A1 6061 and of approximate percentage composition 97.95 A1, 1.0 Mg, 0.6 Si, 0.25 Cu, 0.25 Cr. The molten metal was forced into the preforms under a pressure of 30 MPa applied by a hydraulic ram for a period of 1 minute. The resulting billet (MMC) was demoulded and given a T6 treatment (520°C for 8 hours solution treatment and 220°C for 24 hours precipitation treatment). The resulting tempered billet was cooled to room temperature and its properties were measured. The results are shown in Table 1 below. Preform Density (g/ml) Ultimate Tensile Strength (MPa) Modulus (GPa) Relative Specific Strength *Relative Specific Modulus A 2.92 480 116 1.48 1.58 B 3.0 780 185 2.26 2.31 C 2.58 434 97 1.26 1.42 D 2.40 665 138 2.48 2.20 Fibres (A/B) 3.3 2000 300 Fibres (C/D) 2.1 2100 206 Alloy 2.7 310 70 Example 2 Four preforms, designated "Preforms A-D", were prepared as described in Example 1. MMCs were made from the preforms by the squeeze infiltration technique described in Example 1 but using a magnesium alloy, Mg-ZE63 of approximate %age composition 90 Mg, 5.8 Zn, 2.5 rare earth metals and 0.7 Zr, instead of an aluminium alloy. The molten magnesium alloy under a blanket of 2% SF₆ in carbon dioxide and at a temperature of 800°C was poured onto the preform (preheated at 500°C in the case of preforms A and B and 800°C in the case of preforms C and D) and squeezed into the preform under a pressure of 30 MPa applied for 1 minute. The resulting MMC was demoulded and cooled and its properties were determined and are shown in Table 2. Preform Density (g/ml) Ultimate Tensile Strength (MPa) Modulus (GPa) Relative Specific Strength Relative Specific Modulus A 2.16 395 96 1.18 1.84 B 2.60 727 173 1.81 2.76 C 1.92 278 77 1.08 1.66 D 1.99 568 126 1.79 2.63 Fibres (A/B) 3.3 2000 300 Fibres (C/D) 2.1 2100 206 Alloy 1.87 289 45 EXAMPLES 3 AND 4 Fibre tows of length approximately 5-7 cm produced from a blanket of essentially-aligned alumina fibres of mean diameter 3 microns which had been heat-treated in steam and then heated at 950°C were weighed and laid in layers in the lower half of a mould comprising two half-round members which form a cylinder of diameter 1-1.5 cm when the mould is closed. The mould was closed to compress the fibres, both halves of the mould moving to reduce uneven pressures and dead zones. The mould is open-ended, thereby providing access to the ends of the compressed bundle of fibres. The volume fraction of fibres in the compressed bundle was 0.57 (Example 3). The mould was turned through 90° so that the fibre bundle was vertical and its lower end was closed and connected to an Edwards 5 single stage vacuum pump. Using a funnel, a liquid methyl methacrylate resin (Modar 835) was poured into the top of the mould whilst vacuum was applied to the bottom of the mould to suck the resin into the mould to impregnate the bundle of fibres. The connection to vacuum was removed and the resin was left to cure for 2 hours at room temperature. The mould was then opened and the resin-bonded fibre preform was removed and finished on a lathe. The finished preform was fitted into a mild steel tube which was then heated to about 700°C to burn out the resin and allow the aligned fibres to relax within the tube. The tube was then placed in a squeeze-infiltration machine and infiltrated at 600°C with a molten aluminium alloy (6061) of approximate composition A1 97.95%:Mg 1%:Si 0.6%:Cr 0.25%:Cu 0.25%. The tube was then allowed to cool; the composite was not aged. In a further experiment (Example 4), a rod-like metal matrix composite was prepared as described above except that the volume fraction of alumina fibres was 0.56 instead of 0.57. The modulus of the metal matrix composites were:- Ex.3 Modulus - 160 GPa Ex.4 Modulus - 154 GPa. EXAMPLE 5 A rod-like metal matrix composite was prepared as described in Example 3 except that the volume fraction of alumina fibres was 0.45 and the fibres were taken from a blanket which had been heated in air at 1300°C instead of 950°C. The modulus of the composite was 151 GPa. EXAMPLES 6-15 Rod-like metal matrix composites were prepared as described in Example 3 containing the fibre volume fractions shown below together with the properties of the composite. The density of the composites in Examples 14 and 15 (Mg matrix) was less than 2.0 g/ml. In all Examples the strength and modulus of the composites were as predicted from the corresponding properties of the fibres and the matrix metal. EXAMPLE 16 Circular samples of diameter 100 mm were cut from a mat of aligned alumina fibres and assembled in a circular vacuum-infiltration mould (diameter 100 mm) with the fibres in all the layers being aligned in the same general direction. The thickness of the fibre assembly was built up to a level at which compression to 15 mm thickness would yield a preform of density 1.2 g/ml. The assembly was then infiltrated with a dilute solution of silica sol (1030W silica sol) containing 30% by weight silica to achieve a pick-up of 5% by weight of silica based on the weight of the fibres. The silica was precipitated onto the fibres by passing through the assembly firstly a 2.5% starch solution and secondly a 0.5% solution of a floculating agent (Percol 292). The assembly was then compressed to a thickness of 15 mm in a press and allowed to dry overnight at about 110°C to yield a silica-bound preform. A rectangular sample cut from the preform was boxed in an open-ended rectangular box and heated to 750°C to burn out any organic material. The boxed preform (at 750°C) was placed in a casting die preheated to 300°C and squeeze-infiltrated with an aluminium alloy (LM10 containing 10% magnesium) at 820°C using a pressure of 30 MPa applied by a ram assembly preheated to 350°C. The resulting MMC was demoulded and surplus aluminium was removed by machining. The (boxed) MMC was cut into rectangular bars and its tensile strength and modulus were determined. For purposes of comparison an MMC was made by the above procedure from a mat of randomly-orientated, short (up to 5 cm) alumina fibres of mean diameter 3 microns. In order to avoid damaging the fibres on compression, the volume fraction of fibres was limited to 20%. Results Ultimate Tensile Strength (MPa) Modulus (GPa) Unreinforced LM10 190 70 MMC of invention 442 128 MMC of comparison 270 94

Claims: A metal matrix composite comprising a metal matrix material in which is embedded a fibrous product said fibrous product comprising a plurality of essentially aligned and nominally continuous inorganic oxide fibres of mean diameter below 10 microns wherein a degree of non-alignment of some of the fibres provides for fibre intertwining conferring lateral cohesion on said product. A composite as claimed in claim 1 wherein the lateral cohesion in the fibrous product is such that the product exhibits a tensile strength of at least 25,000 Pa in a direction perpendicular to the general direction of fibre alignment. A composite as claimed in claim 1 or claim 2 wherein at least 90 % of the inorganic oxide fibres are essentially parallel in the general direction of alignment of the fibres. A composite as claimed in any one of claims 1 to 3 wherein the mean diameter of the inorganic oxide fibres is below 5 microns. A composite as claimed in any one of the preceding claims wherein the volume fraction of fibres is from 10 % to 60 %. A composite as claimed in any one of the preceding claims wherein the inorganic oxide fibres are alumina fibres. A composite as claimed in claim 6 wherein the apparent density of the fibres is from 1.75 to 3.3 g/ml. A composite as claimed in claim 6 or claim 7 wherein the fibres have a tensile strength greater than 1500 MPa and a modulus greater than 150 GPa. A composite as claimed in any one of the preceding claims wherein the matrix metal is aluminium or an alloy of aluminium. A composite as claimed in any one of claims 1 to 8 wherein the matrix metal is magnesium or an alloy of magnesium. A composite as claimed in claim 10 comprising a matrix metal of density less than 2 g/ml having embedded therein alumina fibres of apparent density 2 g/ml or less, the composite having an apparent density of less than 2 g/ml. A preform comprising a fibrous product bound together with a binder said fibrous product comprising a plurality of essentially aligned and nominally continuous inorganic oxide fibres of mean diameter below 10 microns wherein a degree of non-alignment of some of the fibres provides for fibre intertwining conferring lateral cohesion on said product. A preform as claimed in claim 12 wherein the lateral cohesion in the fibrous product is such that the product exhibits a tensile strength of at least 25,000 Pa in a direction perpendicular to the general direction of fibre alignment. A preform as claimed in claim 12 or claim 13 wherein the binder is an inorganic binder. A preform as claimed in any one of claims 12 to 14 wherein the volume fraction of fibres is from 10 % to 60 %. A preform as claimed in any one of claims 12 to 15 wherein the mean diameter of the fibres is below 5 microns. A method for the manufacture of a metal matrix composite as claimed in claim 1 which comprises forming a preform of the inorganic oxide fibres bound together with a binder and infiltrating the preform with a liquid metal matrix material. A method as claimed in claim 17 wherein the metal matrix composite is produced by squeeze-infiltration of the preform.

Inventors: DINWOODIE, JOHN, STACEY, MARTYN HUGH, TAYLOR, MICHAEL DAVID
Applicants: IMPERIAL CHEMICAL INDUSTRIES PLC
Application year: 1986
Main classification: C22C1
IPC codes: B22F3, C22C14, C22C21, C22C49, C22C23, C22C47