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• • C—CHEMISTRY; METALLURGY
  • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
  • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
  • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
  • C04B35/01—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics
  • C04B35/10—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on aluminium oxide
• • C—CHEMISTRY; METALLURGY
  • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
  • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
  • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
  • C04B35/01—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics
  • C04B35/16—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on silicates other than clay
  • C04B35/18—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on silicates other than clay rich in aluminium oxide
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
  • B01J—CHEMICAL OR PHYSICAL PROCESSES, e.g. CATALYSIS OR COLLOID CHEMISTRY; THEIR RELEVANT APPARATUS
  • B01J2/00—Processes or devices for granulating materials, e.g. fertilisers in general; Rendering particulate materials free flowing in general, e.g. making them hydrophobic
  • B01J2/02—Processes or devices for granulating materials, e.g. fertilisers in general; Rendering particulate materials free flowing in general, e.g. making them hydrophobic by dividing the liquid material into drops, e.g. by spraying, and solidifying the drops
  • B01J2/04—Processes or devices for granulating materials, e.g. fertilisers in general; Rendering particulate materials free flowing in general, e.g. making them hydrophobic by dividing the liquid material into drops, e.g. by spraying, and solidifying the drops in a gaseous medium
• • C—CHEMISTRY; METALLURGY
  • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
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  • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
  • C04B35/01—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics
  • C04B35/10—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on aluminium oxide
  • C04B35/111—Fine ceramics
• • C—CHEMISTRY; METALLURGY
  • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
  • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
  • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
  • C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
  • C04B35/64—Burning or sintering processes
• • C—CHEMISTRY; METALLURGY
  • C09—DYES; PAINTS; POLISHES; NATURAL RESINS; ADHESIVES; COMPOSITIONS NOT OTHERWISE PROVIDED FOR; APPLICATIONS OF MATERIALS NOT OTHERWISE PROVIDED FOR
  • C09K—MATERIALS FOR MISCELLANEOUS APPLICATIONS, NOT PROVIDED FOR ELSEWHERE
  • C09K8/00—Compositions for drilling of boreholes or wells; Compositions for treating boreholes or wells, e.g. for completion or for remedial operations
  • C09K8/60—Compositions for stimulating production by acting on the underground formation
  • C09K8/80—Compositions for reinforcing fractures, e.g. compositions of proppants used to keep the fractures open
• • E—FIXED CONSTRUCTIONS
  • E21—EARTH OR ROCK DRILLING; MINING
  • E21B—EARTH OR ROCK DRILLING; OBTAINING OIL, GAS, WATER, SOLUBLE OR MELTABLE MATERIALS OR A SLURRY OF MINERALS FROM WELLS
  • E21B43/00—Methods or apparatus for obtaining oil, gas, water, soluble or meltable materials or a slurry of minerals from wells
  • E21B43/25—Methods for stimulating production
  • E21B43/26—Methods for stimulating production by forming crevices or fractures
  • E21B43/267—Methods for stimulating production by forming crevices or fractures reinforcing fractures by propping
• • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
  • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
  • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
  • Y10T428/00—Stock material or miscellaneous articles
  • Y10T428/12—All metal or with adjacent metals
  • Y10T428/12486—Laterally noncoextensive components [e.g., embedded, etc.]

Definitions

• This invention is concerned with ceramic microspheres produced from bauxite and the use of such microspheres as reinforcing materials and functional fillers.
• United States Patent Numbers 3491492, 4068718, 4427068 and 4713203 all describe processes for manufacture from clay or bauxite materials substantially spherical ceramic particles or pellets in the size range O.25-5.O millimeters, primarily for use as proppants.
• United States Patent Number 4713203 which utilizes naturally occurring bauxite fines as feedstock the other prior art documents describe the use of relatively coarse clay or bauxite particles.
• United States patent Number 4427068 does imply however that expensive grinding of calcined clays or bauxite may be employed to produce particle sizes less than 15 micrometers.
• Each of United States Patents 34914 2, 4068718, 4427068 and 4713203 is concerned with the manufacture of proppants for hydraulic fracturing of subterranean formations and each requires the physical formation of pellets by agglomeration in a rotary pelletizer or the like, with or without a binder. Subsequently calcining of the green pellets is usually carried out in a rotary calcining kiln.
• MMCs Metal-matrix composites
• the enhancement in properties over those of the matrix material which can be achieved include: improvement in strength at ambient and high temperatures, improvement in stiffness, improvement in fatigue strength, improvement in wear resistance, reduction in coefficient of thermal expansion.
• MMCs attractive for structural applications at room temperature and at elevated temperatures.
• the magnitude of the enhancements in properties depend on many factors, such as, the: matrix metal or alloy, content of the reinforcing phases, chemistry, geometry, distribution and orientation of the reinforcing phases, nature of the interface between the reinforcing phases and the matrix material, manufacturing method, thermo-mechanical history.
• Aluminium, magnesium, titanium, copper and their alloys can be used as matrix materials.
• a variety of compounds such as carbides, oxides, nitrides, borides, etc. and elements such as carbon and boron, in various forms such as fibres, whiskers, platelets and particulates, have proven to be effective.
• High performance fibres and whiskers are manufactured by costly, energy-intensive processes which make them expensive, resulting in high cost to the finished MMC product.
• the present invention relates to a reinforcement for low-cost MMCs incorporating an in inexpensive naturally occurring raw material.
• the geometries of reinforcing materials employed by MMC producers are typically fibre, platelet and particulate.
• the fibre geometry has a long dimension in one direction which is the preferred direction of reinforcement. Little or no reinforcing effect, sometimes even deleterious effects, are observed in the directions perpendicular to the longitudinal direction.
• the platelet geometry imparts reinforcing effects only in the plane of the platelet which, again, is the preferred plane for reinf rcement. Consequently, MMCs reinforced by fibres and platelets exhibit anisotropic properties. Randomly oriented fibres and platelets can restore isotropy but this is difficult to achieve in practice and unlikely to be maintained during forming operations.
• Particle reinforced composites do not exhibit the anisotropic characteristics of fibre or platelet composites. Hence they are the most efficient for the production of isotropic MMCs, in addition to being low in cost.
• the use of the ceramic microspheres defined above as a reinforcing material offers, by virtue of its geometry, a high degree of isotropy to the MMCs.
• the particulate materials presently used for reinforcing purposes have angular or irregular shapes. When reinforcements of such shapes are incorporated in a metallic matrix, the particles can act as stress raisers under the action of an applied stress. This can lead to premature nucleation of cracks with associated reduction in plasticity of the MMC. Reduced plasticity is reflected in lower elongation, toughness, formability and perhaps strength.
• the geometry and fine microstrueture of the particulate material embodied in this invention is free of any stress raising features such that MMCs reinforced with the material have improved ability for plastic deformation.
• Microspheres of the above type have now been determined to be suited for use as a reinforcement material in metals to form metal matrix composites as well as in other materials such as plastics, to provide improved strength and wearing properties.
• bauxite microspheres having improved sphericity, density, such as chemistry and crystal structures and to provide a simple and economic method for the production of such microspheres from bauxite and bauxitic clays.
• a calcined microsphere of fine bauxite particles said microsphere having a particle size less than 100 micrometers and being characterised by a substantially solid form having a pycnometric density substantially falling in the range 3-2 to 3-9 g/cm 3 , a BET surface area substantially falling in the range 0.05 to 0.5 m 2 /g and a crystal grain size less than 4 micrometres, said microsphere having a surface chemistry selected to enhance the wettability of the microsphere and improve its ability to bond strongly with the matrix materials in use.
• the microspheres are formed from bauxite particles having a mean particle size substantially falling within the range 0.01 to 0.3 micrometers and the microspheres have a particle size substantially falling in the range 1 to 0 micrometers and most preferably less than
• the microspheres are better adapted to perform well in the selected end composite. All of the defined features influence wetting. Wetting in turn influences ease of preparation of the MMC and also determines how well the interface transfers the strengthening effect of the ceramic.
• the mechanical properties (stiffness and strength) of the microsphere depend on the phases and structure which in turn influence properties of the composite product.
• the combination of spherical shape and microcrystalline structure provide isotropic properties in the composite.
• the shape on its own influences certain properties since notch effects are eliminated and formability and castability are also improved.
• microsphere size 0-lOOum which is a consequence of the spray-drying method is an important advantage since other reinforcing materials are available in only limited size ranges.
• other reinforcing materials are available in only limited size ranges.
• commonly available SiC commonly available SiC
• A1 2 0 3 have a narrow size range 1-5» 5-15. 10-25, etc.
• Typical property data for a preferred calcined microsphere embodying the invention are :
• a method for the manufacture of bauxite microspheres comprising the steps of:- preparing a dispersion of bauxite or bauxitic clay; classifying the dispersed bauxite particles to recover the ultrafine fraction; adding small quantities of water soluble salts, mineral compositions or organometallic complexes to control the microsphere surface chemistry so as to enhance the wetting and dispersion of the microphere and improve its ability to bonding strongly with the matrix materials in use; spray drying the dispersion to produce green microspheres of a predetermined mean particle diameter, and subjecting said green microspheres to calcination and sintering to produce microspheres having a size within the range 0-100 micrometers, preferably from 1 to 50 micrometers and most preferably less than 30 micrometers, said microsphere being characterised by a substantially solid form having a pycnometric density substantially falling in the range. 3.2 to 3 * 9 g/cm 3 ,
• the water soluble salt, mineral composition or organometalllc complex is required to achieve the necessary modification of the surface chemistry of the resultant microsphere.
• the additions may contain elements selected from Group 1, 2 or 3 of the Periodic Table.
• said dispersion of bauxite or bauxitic clay comprises an aqueous slurry having a solids content in the range 10-70 w/w solids.
• spray drying is carried out by directing a fine spray of said slurry into a heated region under conditions adapted to produce green microspheres of predetermined mean particle size.
• calcination and sintering is effected in a stationary or gas suspension calciner, in a temperature range between 1100°C and l600°C, and most preferably between 1300°C and 1450°C.
• a composite, material comprising as a functional filler bauxite microsphere product in accordance with the invention.
• Suitable composites include metalmatrix composites (MMCs) and plastics composites.
• the present invention preferably uses ultrafine bauxite or bauxitic clay as the starting material.
• ultrafine bauxite or bauxitic clay as the starting material.
• the relative ease of manufacture and the superior material properties of the product formed from the preferred material arise primarily from the choice of starting material, an ultrafine fraction of a naturally occurring bauxite.
• This ultrafine fraction has a particle size typically less than 1 micrometer and more typically from about 0.02 to 0.3 micrometers with an associated surface area of about 34 square metres per gram.
• the very fine particle size of the bauxite or bauxitic clay feedstock allows an exceptionally high degree of uniformity of blend in the manufacture of the green microsphere.
• the green microsphere comprising a multitude of ultrafine particles has numerous points of contact between the particles, and it is at these points that sintering will be initiated.
• the ultrafine particle size of the constituted minerals permits the use of the simple spray drying process to form particles of substantially spherical shape.
• Previous experience with the same material in spray drying to form larger particle diameters resulted in rounded but not spherical particles which were characterised by a shape of mushroom cap appearance. This shape has been ascribed to the aerodynamic deformation of the slurry droplet before it dried in the hot gas stream of the spray dryer. It has now been found that when the droplet size is restricted to a particle size less than about 100 micrometers, these deformities in shape substantially disappear.
• the spray drying process allows relatively simple control over the particle size of the green microspheres.
• Choice of such appropriate spray drying parameters such as slurry solids concentration, slurry viscosity rate of introduction of inlet and outlet temperature and spray head type and configuration permit this control to be achieved.
• Figure 1 is a scanning electron micrograph of microspheres embodying the invention of size range 1 - 40 um;
• Figure 2 shows the microstructure of squeeze cast alloy
• Figure 3 is a graph showing sliding wear resistance of unreinforced 6061 and 6061 reinforced with ceramic microspheres or SiC;
• Figure 4 shows the improved elevated temperature tensile strength of COMRAL-85 compared with unreinforced 6061
• Figure 5 shows the improved fatigue strength of COMRAL-85 compared with unreinforced 6061
• Figure 6 shows increased elevated temperature elastic modulus of COMRAL-85 compared with unreinforced 6 ⁇ 6l
• Figure 7 shows the stiffness of COMRAL composites as a function of volume fraction of ceramic microsphere reinforcemen ;
• Figure 8 shows the density of COMRAL composites as a function of volume fraction of ceramic microshpere reinforcement
• Figure 9 is an improved modulus-density combination of composites reinforced with ceramic microspheres compared with pure A1 2 0 3 reinforcement
• Figure 10 is a microstructure section of an extruded COMRAL-85 composite sample (unetched) showing the uniform distribution of particulate
• Figure 11 is a further enlarged microstructure section of an extruded COMRAL-85 composite sample (unetched) showing the uniform distribution of particulate;
• Figure 12 is a microstructure section of a gravity cast Al-Si alloy reinforced with 15 vol of ceramic microspheres (etched) ;
• Figure 13 is a further enlarged microstructure section of a gravity case Al-Si alloy reinforced with 15 vol% of ceramic microspheres (etched);
• Figure 14 is a Bachscattered electron image of a ceramic microsphere in an aluminium matrix (polished section of an extrusion) ;
• Figure 15 is an image analysis of the shape of ceramic particulate in SiC reinforced composite compared with ceramic microsphere reinforced composite
• Figure 16 is a low magnification scanning electron microscope (SEM) image of the calcined microspheres embodying the invention.
• Figure 17 is a high magnification scanning electron microscope (SEM) image of the calcined microspheres embodying the invention.
• Figure 18 shows the pin-on-disk sliding wear resistance of COMRAL-85 compared with unreinforced 6061
• Figure 19 compares the fatigue of COMRAL-85 and a commercial A1 2 0 3 reinforced composite and unreinforced 6061.
• Finely divided materials suitable for the production of ceramic microspheres according to the invention are readily obtained from bauxite deposits such as for example those of the type occurring at Weipa in Northern Queensland.
• bauxite deposits such as for example those of the type occurring at Weipa in Northern Queensland.
• a fine fraction exists which is easily separated, for example, by slurrying the bauxite in water in the presence of a dispersant.
• dispersants may be used, such as compounds based on phosphates or polyacrylates.
• a simple separation step results in recovery of the fine fraction as a dilute slurry from coarse particulate matter. Satisfactory separation may be effected for instance using gravity settlers or hydrocyclones.
• the solids content of the settled slurry may still be too low for economical operation of the process, and it may be necessary to introduce a further dewatering step, such as centrifuga ion or filtration.
• the thickened solids now have the consistency of a paste, and it is necessary to redisperse them to a suitably low viscosity before the next step.
• More efficient dispersion may be facilitated by the addition of dispersants such as polyacrylates e.g. ammonium polyacrylate, sodium hexametaphosphate or sodium polyphosphate.
• dispersants such as polyacrylates e.g. ammonium polyacrylate, sodium hexametaphosphate or sodium polyphosphate.
• the use of a high intensity mixer aids in the destruction of agglomerates and the dispersion of most of the particles in their liberated form.
• a spray dryer such as manufactured by the Niro company, or as manufactured by the Bowen-Stork company, is used to form the green microspheres. It is possible to exercise control over particle size distribution by controlling the preparation of the dispersed slurry and the conditions of operation of the spray dryer.
• the particular fraction of bauxite proposed as a source of microspheres has in the Weipa deposits an alumina content of about 59% with a typical range from 55- 63%- Similarly, the silica content will average about 10%, with a range typically 7-13%. Substantially, all of this silica will be present as the mineral kaolinite, although small amounts of quartz may be present. Typically, the mineralogy will comprise 30-50% gibbsite with 15-45% boehmite, 16-27% kaolinite with less than 0.2% quartz. Oxides of iron 6-10% and titanium 3-5% will total about 8-14%. This relatively high level of iron oxide reduces the calcination temperature and results in the formation of the pseudobrookite phase in the calcined microspheres.
• the mineral particles are typically from about 0.02 to 0.3 micrometers in diameter and the minerals gibbsite, boehmite,kaolinite, hematite and anatase are commonly present as liberated crystallites.
• the particles are frequently mono-minerallic in nature, and because of the large surface area and the presence of relatively high levels of non-oxide in the bauxite chemistry, rapid reaction between particles is facilitated at elevated temperatures, producing mainly corundum and mullite.
• the alumina minerals which are present namely, gibbsite, boehmite and kaolinite progressively lose their combined water as the temperature is increased to about 600°C.
• the crystal lattices become disordered and as the temperature is further increased the aluminium oxides undergo a series of phase changes. It is to be expected that the sequence of phase changes may include as transition states gamma, delta, theta, chi and kappa forms of alumina. As a temperature of approximately 950°C the formation of mullite commences and at about 1050°C the alumina begins to convert to the alpha-phase mineral which is known as corundum. Further increase in temperature causes sintering of the mullite and corundum and the production of a pseudobrookite phase to form a polycrystalline ceramic body with high strength. The phases corundum, mullite and pseudobrookite are the final major phases in the end product. As the temperature is increased the particles gain in compressive strength due to the development of an extremely fine interlocking network of crystals. Excessively high temperatures result in a coarsening of the crystal size which then reduces the strength of the ceramic.
• the pellets may shrink in diameter by up to 30% so the spray drying process is controlled to produce green microspheres which will produce the required calcined microsphere falling in the preferred ranges 1-100 micrometers, and preferably less than 30 micrometers.
• the high reactivity of the uncalcined bauxite and its very fine particle size facilitates the formation of the required phases.
• the green microspheres are subjected to calcination and sintering to form the final product.
• calcination is performed by placing the green microspheres in a suitable crucible and heating the crucible in a muffle furnace to about 900°C.
• the heating rate should be slow enough to allow diffusion of the chemically bonded water to occur. This rate is suitable of the order of about 100°C/hour.
• heating is continued with a temperature increase rate of about 10°C/minute until the crucible and its contents reach about 1300°C. The process is then interrupted to prevent the sintering of the particles to each other.
• the material is cooled, lightly crushed to break up any agglomerates and screened through a 106 um screen to ensure individual particles.
• the microspheres are then returned to the crucible and rapidly fired up to the final sintering temperature of between 1300°C-l6 ⁇ O°C at a rate of about 20°C/minute.
• the temperatures and times chosen for the sintering of the microspheres are dependent on the chemical composition of the raw material, as well as the desired properties of the product. For instance, density and porosity of the product may be varied by altering the sintering temperature and time. Generally, a sintering temperature between 1300°C and l600°C is used.
• such devices are manufactured by the Deutsche-Babcock and Lurgi companies of the Federal Republic of Germany, the F.L. Smidth company of Denmark, or the Fuller company of the United States of America.
• improvements to the quality of the product are noted. This is particularly in respect to the microcrystallinity of the particles which is expressed in the surface and strength, of the sintered particles.
• Gas suspension calciners feature a particularly short residence time of particles in the sintering zone of the furnace.
• the High Temperature Mixer manufactured by the Beutsche Babcock company features a residence time in the calcination zone estimated at about one quarter to one half of a second.
• crystal grain growth is inhibited, and a fine crystal microstructure Is evident.
• the average crystal grain size has been estimated to be about one micrometer.
• a fine microstructure is conducive to obtaining strength in a ceramic object.
• the fine microstructure is also important in conveying a smooth surface to the microspheres. When used in composites which are to be subject to such processes as injection moulding, wear of the surfaces of the forming equipment is reduced.
• the sodium levels in the samples described in Examples 1 and 2 were carefully controlled by the addition of 0.15 wt/wt% sodium hydroxide during the slurry preparation step.
• the sodium was added to modify the surface composition of the microsphere for certain applications such as the reinforcement of aluminium alloys.
• the presence of sodium on the particle surface enhances wetting and dispersion.
• the surface enrichment of sodium occurs during the spray drying process from the crystallization of dissolved sodium hydroxide at the microsphere particle surface.
• X-ray photoelectron spectroscopy (XPS) studies confirmed this and results are given for sodium enrichment on the surface of the sample described in Example 2.
• the desired surface chemistry can be achieved with the addition of water soluble inorganic compounds such as boron oxide or boric acid prior to spray drying.
• Water soluble inorganic compounds such as boron oxide or boric acid
• Small additions (0.1-5 wt%) during slurry preparation will result in a boron enriched surface layer during spray drying. This will assist with microsphere wettability and dispersion in a plastic or polymer matrix.
• Bauxite microspheres produced in accordance with the invention may be used for a variety of purposes and in particular may be used as functional fillers in a variety of media.
• the ceramic composition of the particles lend such properties as toughness, hardness, wear and abrasion resistance, chemical resistance, resistance to weathering and the like in a composite material.
• the surface characteristics of the microspheres may also be modified, due to crystal structure (Figs. 14 and 17), by controlling the calcination conditions.
• microspheres embodying the invention are particularly adapted for use for reinforcement of metals and polymers and plastics.
• aluminium, magnesium, copper, nickel or titanium, or their alloys could be used as the matrix material, but aluminium and its alloys are preferred.
• New aluminium alloys such as Al-Li alloys also can be used besides the conventional casting and wrought alloys.
• Processes presently employed to produce MMCs can be used to produce the novel MMC disclosed above.
• a foundry-based method of assimilating the reinforcing material in molten metal Is the most desirable for the production of low cost MMCs.
• a foundry-based method is therefore proposed as the preferred production method, although other methods such as those based on powder metalurgy techniques and preform infiltration also can be used.
• a foundry-based method is particularly suitable, because the ceramic microspheres are easily wetted by molten aluminium compared with other types of reinforcement.
• the sphericity of the reinforcing material results in increased fluidity and castability of the composite melt when compressed with other MMC melts. Consequently, production and casting of this novel composite is easier via a foundry-based method than for other MMCs.
• Porous preforms could be also made with microsphere particles. These could be infiltrated by a molten alloy by use of pressure or vacuum to produce MMC billets or near net shape castings.
• the wettability between microspheres and aluminium alloys is promoted by the chemical and phase composition of the ceramic microspheres as well as by the surface chemistr described above.
• the natural balanc between the various chemical components in the microspheres thus provides the dual characteristics of good wettability an chemical inertness with respect to the matrix - a feature which is not achieved by any other reinforcing material known to us.
• the spherical shape is geometrically the most isotropic shape. Furthermore, unlike other reinforcing materials, the calcined bauxite microspheres are polycrystalline which eliminates even crystallographic anisotropy which is inherent in single crystal whiskers, platelet, and particulates. Therefore, the novel spherical bauxite particulates described above have the highest degree of isotropy among all available reinforcing materials. This fact, combined with uniform distribution in the matrix, will endow MMCs with maximum isotropy.
• the content of the microsphere reinforcing material in an MMC can be varied from 1 vol% to as high as 50 vol% but, when a foundry-based production method is used, practical difficulties inmixing and casting generally limit the reinforcement content to levels below 30 vol%. When a powder metallurgy production method is employed, however, this upper limit could be as high as 50 vol%.
• the lower limit for reinforcement content is determined by the resulting properties. To achieve noticeable enahancements in properties, a reinforcement content of at least 5 vol% must be present.
• This example describes a metal matrix composite where the commercial aluminium alloy 6 ⁇ 6l was reinforced by ceramic microspheres.
• a foundry-based method of preparation was used. Approximately 3 «5kg of aluminium alloy 6 ⁇ 6l was melted in a crucible. A quantity of ceramic microspheres was weighed out so as to produce an MMC with reinforcement content of 15 vol%. this measured quantity was preheated to 200°C in an oven. The size of the microspheres of bauxite varied between about 1 um and 40 um. A scanning electron micrograph of these particles is shown in Figure 1, which demonstrates their sphericity and polycrystallinity.
• the molten alloy was then stirred by a rotor at 700°C in order to produce a vortex on the melt surface. Hot ceramic microsphere particulates were then added into the vortex. After adding the particulates, stirring was stopped and the molten composite was squeeze cast into blocks of 110mm x 6 ⁇ mm x 20mm. Specimens were machined from these blocks for testing.
• a typical microstructure of the composite is shown in Figure 2. It demonstrates that the particles are individually wetted.
• the room temperature tensile test results after a T6 heat treatment are given in Table 1. Results are given for a A1 2 0 3 reinforced 6 ⁇ 6l, produced via a foundry process by a commercial manufacturer, for comparison. The data show that the microsphere reinforced MMC exhibits higher yield strength than the corresponding commercial MMC while being comparable in other properties.
• the melt was cooled to the two-phase region while stirring to a thixotropic slurry.
• a temperature of 645°C was reached, the preheated ceramic microspheres were added at a slow and steady rate.
• the uppermost blades assimilated the bauxite into the slurry while sweeping its surface.
• stirring was continued in the temperature range 605°C - 645°C until all the bauxite was wetted and distributed in the liquid phase of the slurry.
• Powders of Al (-325 mesh), Mg (-325 mesh) and Si (-20 um) were weighed out in a ratio to comply with the specification for alloy 6 ⁇ 6l and to make a total weight of approximately 7kg.
• the powders were mixed with 10 vol% ceramic microspheres and were milled in an inert atmosphere for about 15 minutes.
• the blended powder was filled and vibrated into an elastomer mould of diameter 89mm (3.5 inch) and length 430mm (17 inch).
• the mould was vacuum sealed and cold-isostatically pressed.
• the elastomer mould was then stripped and the cold pressed billet was sintered to produce a 95% dense billet.
• the sintered billet was extruded into 12.5mm (0.5 inch) diameter bar and room temperature mechanical properties were determined (Table 1) after the heat treatment as in Examples 1 and 2.
• Example 6 Description : Comral-85 is an aluminum matrix, up to 20 v/o, ceramic microsphere reinforced composite.
• Matrix Standard alloy 6 ⁇ 6l Reinforcement Alumina containing microspheres: type CMS-20 with an average particle size of 20 microns. Designation : 606l/A1203/20p (proposed Aluminum Association)
• Composites, such as the above example, embodying the invention can be heat treated to achieve strengths higher than those quoted in Example 6.
• Example 7

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• 1990
  • 1990-12-21 ES ES90314167T patent/ES2056394T3/es not_active Expired - Lifetime
  • 1990-12-21 EP EP90314167A patent/EP0434461B1/en not_active Expired - Lifetime
  • 1990-12-21 US US07/630,968 patent/US5175133A/en not_active Expired - Fee Related
  • 1990-12-21 NZ NZ236638A patent/NZ236638A/xx unknown
  • 1990-12-21 IE IE465090A patent/IE904650A1/en unknown
  • 1990-12-21 AT AT90314167T patent/ATE108425T1/de not_active IP Right Cessation
  • 1990-12-21 DE DE69010646T patent/DE69010646T2/de not_active Expired - Fee Related
  • 1990-12-22 CN CN91100740A patent/CN1056674A/zh active Pending
  • 1990-12-22 KR KR1019900021532A patent/KR0154119B1/ko not_active Expired - Fee Related
  • 1990-12-24 CA CA002033131A patent/CA2033131A1/en not_active Abandoned
  • 1990-12-24 WO PCT/AU1990/000609 patent/WO1991009815A1/en not_active Ceased
  • 1990-12-25 JP JP2413795A patent/JPH04263002A/ja active Pending
  • 1990-12-26 BR BR909006590A patent/BR9006590A/pt not_active Application Discontinuation
• 1991
  • 1991-02-09 TW TW080101056A patent/TW235290B/zh active

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