US3178807A - Cermet of aluminum with boron carbide or silicon carbide - Google Patents

Cermet of aluminum with boron carbide or silicon carbide Download PDF

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US3178807A
US3178807A US143125A US14312561A US3178807A US 3178807 A US3178807 A US 3178807A US 143125 A US143125 A US 143125A US 14312561 A US14312561 A US 14312561A US 3178807 A US3178807 A US 3178807A
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carbide
aluminum
metal
titanium
tube
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Oswald R Bergmann
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EIDP Inc
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EI Du Pont de Nemours and Co
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Priority to AT789662A priority patent/AT250686B/de
Priority to DEP30307A priority patent/DE1263576B/de
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/02—Compacting only
    • B22F3/08—Compacting only by explosive forces
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/05—Mixtures of metal powder with non-metallic powder
    • C22C1/051—Making hard metals based on borides, carbides, nitrides, oxides or silicides; Preparation of the powder mixture used as the starting material therefor
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
    • C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
    • C22C29/06—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds
    • C22C29/067—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds comprising a particular metallic binder

Definitions

  • This invention relates to metal cemented ceramic materials, or cermets, and more particularly to cermets in which the ceramic component is a carbide, and to methods for making such cermets.
  • cemented carbides with appropriate physical properties have had large scale industrial application in services requiring high resistance to wear, oxidation, and corrosion, high strength at elevated temperatures, and high thermal shock resistance.
  • One method used for producing cemented carbides involves cold pressing and sintering a tine dispersion of carbide and metal powders produced by grinding the components in a ball mill, usually, wet milling. During the milling the metal component tends to react with the milling medium and/or the milling atmosphere to form oxides. To compensate for the above, the dispersion must be dried and subjected to reduction by hydrogen.
  • the dispersion either dry or in the presence of a lubricant, is pressed in a die and the resulting compact is subjected to a limited sintering cycle and/or heat treatment to remove the lubricant.
  • the compact is then cut or ground to the desired configuration and subjected to a second and more extensive sintering cycle carried out either in vacuum or in a hydrogen atmosphere.
  • An alternative method for the production of cemented carbides is hot pressing which involves simultaneous application of heat and pressure to the carbide-metal mixture and produces ⁇ cermets with superior physical properties, eg., lower porosity, higher hardness, and improved rwear resistance, as compared with the corresponding cermets produced by cold pressing.
  • the mixture of components is pressed, usually by means of hydraulic pressure, into a graphite mold or die and heated either by resistance heating of the die or by induction heating.
  • hot pressing is more expensive than cold pressing followed by sintering since the graphite die can rarely be salvaged for reuse.
  • the expense of producing hotpressed cermets may be reduced by using a graphite mold fabricated in such a manner that two or three articles may be formed during one cycle, but the uniformity of the articles produced is usually inferior to that of singly-produced cermets.
  • a third process for producing cemented carbides is an inltration method.
  • a carbide skeleton i.e., previously pressed or compacted carbide powder which may or may not have been sintered, is exposed to the desired quantity of molten binder metal, e.g., by superpositioning the molten binder saturated with the carbide on the carbide skeleton.
  • the assembly is heated in a reducing atmosphere until the binder has penetrated the carbide skeleton completely and uniformly, i.e., 1-4 hours.
  • cermets of this invention have various advantages. For example, considering first aluminum and magnesium as the cementing metals, they are considerably less expensive than the corresponding cermets cemented by cobalt and nickel which have commonly/been used heretofore. Also because of the dense, adherent oxide layer which forms on aluminum and magnesium surfaces, these metals offer high resistance to destructive oxidation at elevated temperatures. This makes cermets using these metals, particularly the titanium carbide cermets, useful in the construction of components of temperature control instruments, bearings, seals, valve seats, and turbinebuckets and blades for jet engines. The titanium carbide-aluminum cermets of this invention, because of the high electrical conductivity and oxidation resistance of the aluminum, are also useful as electrical contact materials under constant exposure to high current and voltage.
  • Tungsten carbide-cobalt cermets which are widely used in cutting tools have satisfactory oxidation resistance only up toca. 800 C. while the aluminum-cemented titanium carbide compositions of this invention withstand considerably higher operating temperatures.
  • the improved oxidation resistance makes the silicon carbide cermets of the invention particularly useful as heating elements.
  • Ffhe lesser density of a carbide-aluminum or -rnagnesium composition of porosity comparable to available carbide-cobalt or carbide-nickel cermets provides advantages for applications such as missile components where weight is critical.
  • a boron carbide-aluminum cermet, for example, is useful as a light structural material.
  • a carbide-titanium cermet is useful at higher temperatures than the corresponding cobalt or nickel detonating explosive, initiating the explosive layer, and thereafter heating the compact thus formed to a temperature above the melting point of the metal.
  • FIGURE 1 represents a longitudinal cross-sectional View of an assembly for use in preparing cermets in solid cylindrical form
  • FIGURE 2 represents a longitudinal cross-sectional View of an assembly for use in preparing cermets in tubular form
  • FIGURE 3 represents a longitudinal cross-sectional view of an assembly for use in preparing cermets in which the metal component is provided in non-particulate form.
  • metal tube I filled with a mixture of the desired carbide and metal powders 2, is sealed with metal plugs 3.
  • the outside wall of metal tube 1 is surrounded with a layer of a detonating explosive 4- and the assembly is immersed in water 5.
  • metal tube 6 is positioned essentially concentrically within metal tube 1.
  • the annulus between the adjacent walls of the two tubes is illed with a mixture of the desired carbide and metal powders 2 and the ends of the annulus are sealed with metal plugs 3.
  • An air-lled metal tube 7 closed at both ends is fastened by taping essentially concentrically within metal tube 6 to absorb the energy of shock waves converging in the center of the assembly.
  • the outside wall of metal tube 1 is surrounded with a layer of a detonating explosive 4 and the assembly, immersed in water which ows into the annulus between metal tube 6 and metal tube 7.
  • metal tube 6 is inserted through the bore of metal tube 8 which metal tube 8 comprises the metal to be incorporated into the novel cermet.
  • Metal tube 9, also comprising the metal to be incorporated into the novel cermet, is inserted within the bore of metal tube 1 and the rst set of tubes 6 and 8 is positioned essentially concentrically within the second set of tubes 9 and 1.
  • the annulus between the adjacent walls of tubes 8 and 9 is filled with the desired carbide powder l@ and sealed with metal plugs 3.
  • An air-filled metal tube 7 closed at both ends is fastened by taping essentially concentrically within metal tube 6 as in FIGURE 2.
  • the outside Wall of metal tube 1 is surrounded with a layer of a detonating explosive 4 and the assembly, immersed in water S which flows into the annulus between tubes 6 and 7 Vnesium, and titanium-cemented cermets are formed, I believe that a brief discussion of the probable mechanism of the preferred method of preparation will elucidate the value of various modications and the reasons for the ineicacy of conventional procedures.
  • the surfaces of carbide powder particles are initially in contact with the surfaces of metal, i.e., aluminum, magnesium, or titanium, powder particles which surfaces are coated, as would be expected, with an oxide film.
  • the pressure of the shock waves generated by the detonation of the layer of explosive surrounding the assembly constricts the metal tube(s) thereby mechanically increasing the density of the powder mixture.
  • this pressure eifectively reduces the particle size of the powders and mechanically ruptures the oxide iilm thus bringing the increased surface area of carbide powder into intimate contact with oxide-free metal within a few microseconds.
  • the surfaces of carbide powder particles are in contact with the oxide-coated, adjacent surfaces ofthe metal, i.e., aluminum, magnesium, or titanium, tubes 8 and 9.
  • the oxide lm is ruptured by the pressure of the shock waves and thc increased surface area of carbide powder is brought into intimate contact with oxide-free metal within microseconds.
  • the carbide-metal system is heated to a temperature at which the metal melts to form a liquid phase which wets the carbide particles and, under the influence of high surface forces, ows into the pores in the carbide skeleton.
  • the type of interaction between the carbide and metal phases is dependent upon the properties of the carbide and the metal, and upon the conditions under which the carbide-metal system is compacted and sintered.
  • Simple mechanical interaction or formation of an interlocking structure between the carbide and the metal in which the metal penetrates and essentially fills the pore volume of the carbide skeleton is essential to the formation of the novel cermets.
  • additional phenomena which may be associated with the formation of the novel compositions are surface reaction between carbide and metal resulting in the formation of a new phase, i.e., an intermetallic compound or alloy, mutual solution and reprecipitation, etc.
  • the metal is provided in nely divided form and the pressure of the shock waves which disrupts the oxide film establishes many more areas of intimate contact between carbide and oxide-free metal than can be Aachieved in the assembly of FIGURE 3 in which the metal is provided in the form of a sheath for a centrally disposed mandrel (metal tube 6) and in the form of a liner for metal tube 1. Furthermore, since the carbide and metal powders are thoroughly blended prior to compaction, during sintering a given quantity of metal has to llow only a relatively short distance before the carbide skeleton is completely penetrated by the metal binder which factor reduces the probability of the reformation of oxides.
  • the effect of the shock waves is to disrupt the metal oxide lm and bring the carbide into intimate contact with the oxide-free metal.
  • the conventional inltration process fails in this respect since no pressure is applied and the oxide lm remains intact.
  • cold pressing Vand hot pressing disrupt the oxide lm, the pressure is applied over a relatively long time, eg., longer than 1/z second, as compared with the pressure of the shock waves which is applied over a short time, eg., up to 10 microseconds.
  • a short time eg., up to 10 microseconds.
  • compositions, means of initiation, loading, velocity of detonation, and confinement of the detonating explosive p layer used in the preferred method of preparation of the novel cermets are not critical. It will be apparent to one skilled in the art that a suliicient quantity of explosive to e'ect the destruction of the oxide iilm without damaging the assembly should be used.
  • a layer of a flexible explosive composition is conveniently wrapped around the outer tubes of the preferred assemblies as illustrated in the attached drawings.
  • the layer of detonating explosive may be initiated by means of a line-Wave generator (as described in U.S. Patent No. 2,943,571 issued July 5, 1960) which in turn may be initiated by means of a conventional electric blasting cap.
  • the containing tubes, i.e., metal tubes 1 and 6 can be removed mechanically before or after sintering, or melted off. Sintering can be effected with any of the several conventional modiiications with respect to temperature, rate of heating and cooling atmosphere, etc.
  • the carbide and metal components used can be provided in a number of forms. Generally powders of particle size less than 200 mesh are desirable; however, cermets have been successfully prepared using 20 mesh metal powder. If the diameter of the tubular container of FIGURE 3 is very small, a sufficient quantity of the metal componentV can be provided in the form of a liner for the container thus obviating the need for the metalsheathed centrally disposed mandrel.
  • the metal can also be in the form of wires or rods extending through a mass of the carbide powder.
  • the composition of the cermets is controlled'by blending the carbide and metal in any desired proportion.
  • the initial pore volume of the carbide skeleton is the initial pore volume of the carbide skeleton.
  • the relative amounts of metal and carbide used can be varied to obtain specic physical properties in the cermets.
  • the -rnetal to carbide ratios used will be in the rangeof about 0.01-1 part by Weight metal to l part by Aweight carbide; for cutting tool applications the preferred range is about 0.01-0.2 -part by Weight metal to 1 part by weight carbide.
  • the cermets produced as described have porosity comparable to commercially available cemented carbides, and have the metallic luster, and thermal and electrical conductivity characteristic of these compositions.
  • composition-s A and B The explosives employed in these examples were in the form of extruded flexible ⁇ sheets of compositions designated as composition-s A and B.
  • Composition A contains 20% very iine pentaerythritol tetranitrate (PETN), 70% red lead, and, as a binder, of a 50/50 mixture of butyl rubber and a thermoplastic terpene resin [mixture of polymers of -pinene of formula (C10H6)n], commercially available as Piccolyte S-lO (manufactured by the Pennsylvania Industrial Chemical Corporation).
  • PETN very iine pentaerythritol tetranitrate
  • red lead a binder
  • thermoplastic terpene resin mixture of polymers of -pinene of formula (C10H6)n]
  • Piccolyte S-lO commercially available as Piccolyte S-lO
  • Composition lB is a modification of'omposition Av (Polybutene No. 24 manufactured by Oronite Chemical Company).
  • Example I A cermet containing titanium carbide and aluminum combined in such a manner that voids in the carbide skeleton were filled with an aluminum-titanium alloy of variable composition was prepared as follows:
  • a solid cylindrical aluminum plug having diameter of 1% inches and a length of 1% inches was inserted 1 inch into the end of a seamless aluminum tube having an outside diameter of 2 inches, a wall thickness of 1/s .inch and a length of 7 inches and Welded inV place thus sealing one end of the tube.
  • the bore of the 'tube was lined With paper and vibrator-packed to within 1 inch of the open end of the tube with a mixture of 88 parts of less than 325 mesh titanium carbide powder and 12 parts of less than 325 mesh aluminum powder prepared by mixing the constituent powders in a twincone blender for one hour.
  • the titanium carbidealuminum powder mixture thus packed had a bulk density of about 2.15 grams per cubic centimeter.
  • a second aluminum plug 1% inches in length was inserted 1 inch into the open end of the tube assembly and welded in place to form an assembly substantially as illustrated in FIGURE 1 of the attached drawings.
  • a rectangular sheet of the above-described explosive composition B having a Weight distribution of 16 grams per square inch was glued around the outside Wall of the aluminum tube, encircling the tube for its entire length.
  • a triangular line-wave generator (as described in U.S. Patent No. 2,943,571 issued July 5, 1960) was glued to the edge of the sheet explosive which conformed to the upper periphery of the aluminum tube.
  • a N0. 8 electric blasting cap was fastened to the apex of the line-wave generator and the assembly was immersed in Water. The blasting cap was actuated by application of an electric current thus initiating the line-Wave generator which, in turn, initiated the sheet of explosive.
  • the cemented carbide thus produced had a density of 4.20 grams per cubic centimeter, or approximately 90% of the theoretical density, a transverse rupture strength of 27,850 ypounds yper square inch, and diamond pyramid hardness number under a 1000-gram load of 1030.
  • the oxidation resistance of the novel composition was very good; e.g., a sample cut from the cermet gained less than 3.1 milli-grams per square centimeter of surface area per hour at 1100 C. in air.
  • Example 2 A composition comprising titanium carbide and aluminum combined as in Example 1 was prepared by mixing parts of less than 32S mesh titanium carbide powder and 5 parts of less than-325 mesh aluminum powder. The assembly was arranged and ,detonation and sintering carried out as in Example 1. Prior to detonatiou the'bulk density of the titanium carbide-aluminum titanium alloys AlTi and Al3Ti in the A.S.T.M. card file.
  • Example 3 A composition comprising titanium carbide and aluminum combined as in Example 1 was prepared accordling to the following procedure:
  • a seamless aluminum tube having an outside diameter of 1 inch, a wall thickness of 1A inch, and a length of 8 inches was positioned concentrically within a second seamless aluminum tube having an outside diameter of 2 inches, a wall thickness of 1/s inch, and a length of 7 inches.
  • An aluminum plug 1% inches in length was inserted 1 inch into one end of the annulus between the adjacent walls of the two tubes and welded in place thus sealing one end of the annulus.
  • the adjacent walls of the aluminum tubes were lined with paper and the annulus between the walls, vibrator-packed to within 1 inch of the open end of the annulus with a mixture of 88 parts of less than 325 mesh titanium carbide powder and 12 parts of less than 325 mesh aluminum powder prepared as in Example l.
  • the titanium carbide-alumi11um powder mixture thus packed had a bulk density of about 2.1 grams per cubic centimeter.
  • a second aluminum plug 11A inches in length was inserted l inch into the open end of the annulus and welded in place.
  • An airlled copper tube sealed at both ends having an outside diameter of 1/1 inch, a wall thickness of 1/32 inch, and a length of about 7% inches was positioned concentrically within the inner aluminum tube in such a manner that a portion of the copper tube about 1/8 inch in length extended beyond each end of the compaction assembly and taped in place to form an assembly substantially as illustrated in FIGURE 2 of the attached drawings.
  • a sheet of explosive composition B having a weight distribution of 22 grams per square inch was glued to the outside wall of the outer aluminum tube.
  • a linewave generator and a No. 8 electric blasting cap were attached as in Example l and the assembly was immersed 'in water which owed into the annulus between the outside wall of the copper tube and the inside wall of the inner aluminum tube.
  • the explosive was initiated, and after the detonation the end plugs v/ere cut otf and the Copper tube was removed.
  • the remaining assembly was subjected to heat treatment as in Example 1 during which process the constricted aluminum tubes were melted off.
  • the density of the cemented carbide thus produced was 4.23 grams per cubic centimeter, or approximately 91% of the theoretical density, and the transverse rupture strength, 33,250 pounds per square inch.
  • the hard ness of the composition as indicated by a diamond pyramid hardness number of 1050 under a G-gram load, was in the range of that of commercial cutting tools, and a drill bit ground from the new material was effectively used to cut steel, brass, and aluminum.
  • the oxidation resistance of the titanium carbide-aluminum composition at high temperatures was very good; eg., a specimen gained less than 8 milligrams per square centimeter of surface area after 12 hours in air at 1025 C.
  • Example 4 A composition comprising titanium carbide and aluminum combined as in Example 1 was prepared by mixing 51.1 parts of less than 325 mesh titanium carbide powder and 48.9 parts of less than 325 mesh aluminum powder. The assembly was arranged and detonation and sintering carried out as in Example 3. X-ray diifraction of a sample of the cemented carbide product gave the following pattern of lattice spacings, d, A, and relative intensities, I/Il:
  • Example 3 A composition comprising titanium carbide and aluminum combined as in Example l was prepared by mixing 88 parts of less than 325 mesh titanium' carbide and l2 parts of approximately 20 mesh aluminum. The assembly was arranged and detonation and sintering carried out as 1n Example 3.
  • the titanium carbide-aluminum powder mixture Prior to detonation the titanium carbide-aluminum powder mixture, as packed between the adjacent walls of the aluminum tubes, had a bulk density of 2.02 grams per cubic centimeter.
  • the explosive employed in this example was an extruded sheet of the above-described explosive composition A having a weight distribution of 14 grams per square inch.
  • Example 6 A composition comprising titanium carbide and aluminum combined as in Example 1 was prepared as follows:
  • a seamless mild steel tube having an outside diameter of 11/2 inches, a wall thickness of 1A inch, and a length of 7 inches was inserted through the bore of a seamless aluminum tube having an outside diameter of 1% inches, a wall thickness of 1/32 inch, and a length of 5 inches in such a manner that a portion of the mild steel tube 1 inch in length extended beyond each end of the aluminum tube.
  • a second seamless aluminum tube having an outside diameter of 2.95 inches, a Wall thickness of 1A inch, and a length of 5 inches was inserted within the bore of a second seamless mild steel tube having an inside diameter of 3 inches, a wall thickness of l inch, and a length of 7 inches in such a manner that a portion of the mild steel tube 1 inch in length extended beyond each end of the aluminum tube.
  • the first set of tubes was positioned concentrically within the second set of tubes and a steel plug 1% inches in length, inserted 1 inch into one end of the annulus between the adjacent walls of the aluminum tubes sealing one end of the annulus.
  • the annulus Vbetween the adjacent walls of the aluminum tubes was Yvibrator-packed to wi-thin 1 inch of the open end of the tube assembly with less than 325 mesh titanium carbide powder.
  • the powder thus packed had a bulk density of approximately
  • a second steel plug 1% inches in length was inserted 1 inch into lthe open 'end of the tube assembly and welded in place.
  • the compaction assembly was evacuated to 2.5 104 mm. of mercury by conventional means through a piece of copper tubing inserted into a hole drilled in one plug. An air-filled copper tube sealed at both ends having an voutside diameter of 1/z inch, a wall thickness of 1/32 vinch,
  • Example 3 a length of about 7% inches was positioned concentrically within the inner mild steel tube and taped in place as in Example 3.
  • the explosive employed in this example was an extruded sheet of explosive composition A having a weight distribution of 22 grams per square inch.
  • the sheet of explosive was glued around the outside Wall of the outer mild steel tube and a line-wave generator and a No. 8 electric blasting cap were attached as in Example 1.
  • the assembly was immersed in water which flowed into the annulus between the adjacent walls ot the copper tube and the inner mild steel tube, and the explosive, initiated as in Example 1.
  • the copper tube was removed.
  • the remaining assembly was heated unopened for two hours at 800 C. in a muumble furnace and furnace cooled.
  • the end plugs were cut olf and the inner mild steel tube, slit and mechanically removed. It was found that the titanium carbide compact had been penetrated by aluminum from the aluminum tubes.
  • the remnants of the aluminum tubes were melted oit by heating the assembly atSOt)D C. in a carbon dioxide atmosphere and the outer mild steel tube was mechanically removed.
  • Metallographic examination and photomicrographs of the cermet thus produced revealed a microstructure similar to that of the cemented carbide described in Example 1.
  • X-ray dilraction of a sample of the cemented carbide gave the following pattern of lattice spacings, d, A and relative intensities, I/Il:
  • the density of the cemented carbide thus produced was 4.44 grams per cubic centimeter, or approximately 95.3% of the theoretical density, and the transverse rupture strength, 52,600 pounds per square inch.
  • the hardness of the composition as indicated by a diamond pyramid hardness number of 1160 under a 1000-gram load, was in the range of commercial cutting tools, and a bit ground from the new material was effectively used to cut steel, brass, and aluminum.
  • the oxidation resistance at high temperatures of the composition was very good; e.g., a specimen gained less than 7 milligrams per square centimeter of surface area after 12 hours at 1025 C. g
  • alloys of the approximate composition AlTi have melting points above 1200 C., good oxidation resistance, and a higher hardness than other titanium alloys.
  • the novel titanium carbide-aluminum cerments exhibited high strength at elevated temperatures and superior thermal shock resistance which enabled them to withstand repeated cycles of heating to 900 C. and quenching without cracking.
  • the cermets generally had a transverse-rupture strength of above 45,000 pounds per square inch under which stress a uniform, metallic fracture, rather than a chalky crumbling, developed.
  • Example 7 A composition comprising tungsten carbide and valuminum was prepared by mixing 95 parts of less than 325 mesh tungsten carbide powder and 5 partsV of less than 325 mesh aluminum powder prepared -by blending the constituent powders in a twin-cone blender for one hour. The assembly described in Example 3 was used. The bulk density of the powder -mixture as packed between the adjacentwalls of the aluminum t-ubes Aprior to detonation was approximately 3.0 grams per cubic centimeter.
  • the explosive used in this example was an extruded vsheet of above-described kexplosive composition B having a Weight distribution of 14 .grams per square inch, initiated as in Example l.
  • the density of the neat-treated tungstencarbide-aluminum cermet. was 7.61 grams per cubic centimeter, or approximately 51% of the theoretical density, .andv the diamond pyramid ,hardness Vnumber was 517.V
  • Metallographic examination and microphotographs of polished and etched ⁇ samples ofthis composition showed a cemented structure similar to that of the compositions described in the previous examples. However, X-ray diiraction indicated that no substantial reaction had taken place between the components.
  • Example 8 A composition comprising silicon .carbide fand Yaluminum was prepared frorna mixture of parts of less than325 mesh silicon carbide powderand 20 parts of less than 325 mesh aluminum powder prepared as in Example 1. The assembly, explosive, and compaction technique described in Example 3 were used. The bulk density ot the powder mixture as packed between the adenr/aso? jacent Walls of the aluminum tubes prior to detonation was approximately 1.38 grams per cubic centimeter.
  • Example 9 A composition comprising boron carbide and aluminum was prepared from a mixture 8O parts of less than 20a particle size boron carbide powder and 20 parts of less than 325 mesh aluminum powder using the assembly and technique of Example 8. The bulk density of the powder mixture prior to ⁇ detonation was approximately .85 gram per cubic centimeter.
  • the cermet thus produced had a density of 2.42 grams per cubic centimeter, or approximately 95.3% of the theoretical density, and a microstructure similar to that of the novel compositions of the previous examples.
  • X-ray diffraction gave the following observed pattern of lattice spacings, d, A, and relative intensities, I/I1, the majority of which correspond to those for boron carbide and aluminum in the A.S.T.M. card le:
  • composition comprising titanium carbide and magnesium was prepared from a mixture of 95 parts of less than 325 mesh titanium carbide powder and 5 pants of less than 325 mesh magnesium powder using the assembly,
  • the density of the cemented carbide was 3.94 grams per l cubic centimeter or approximately 82.6% of the theoretical density and the diamond pyramid hardness number was 970,
  • the microstructure of the cermet was similar to that of the cermets described in the previous examples and the following observed pattern of lattice spacings, d, A, and relative intensities, I/Il, indicate formation of a new phase, i.e., magnesium carbide, between the components:
  • Example 11 A composition comprising titanium carbide and titanium was prepared from a mixture of 45.4 parts of less than 325 mesh titanium carbide powder and 54.6 parts of less than 325 mesh titanium powder using the assembly, explosive, and compaction technique described in Example 8. The bulk density of the powder mixture as packed prior to detonation was approximately 1.56 grams per cubic centimeter.
  • This cermet had a density of 4.4 grams per cubic centimeter, or approximately 93.5% of the theoretical density, hardness on the Rockwell A scale of 79, and a transverse rupture strength of 21,050 pounds per square inch.
  • X-ray diffraction revealed no new phase formation; however, the titanium lines shifted toward higher lattice spacing values than for the pure metal indicating mutual solubility of the components and the formation of a solid solution. The following is the observed pattern of lattice spacings, d, A, and relative intensities, I/ll:
  • a cermet consisting essentially of a iinely-divided ceramic component selected from the group consisting of boron carbide, silicon carbide and mixtures thereof cemented by metallurgical bonding by elemental aluminum.
  • a cermet of claim 1 containing from 0.01 to 1 part by weight of elemental aluminum for each part by weight of ceramic component.
  • a cermet consisting essentially of a finely-divided .ceramic component selected from the group consisting of boron carbide, silicon carbide and mixtures thereof cemented by metallurgical bonding by elemental aluminum, the aluminum coating the particles of said nelydivided ceramic component and filling the spaces between said particles.
  • a cermet of claim 3 containing from 0.01 to 1 part by weight of elemental aluminum for each part by weight of ceramic component.

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US143125A 1961-10-05 1961-10-05 Cermet of aluminum with boron carbide or silicon carbide Expired - Lifetime US3178807A (en)

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US143125A US3178807A (en) 1961-10-05 1961-10-05 Cermet of aluminum with boron carbide or silicon carbide
GB32231/62A GB967136A (en) 1961-10-05 1962-08-22 Cermet materials
AT789662A AT250686B (de) 1961-10-05 1962-10-05 Cermet und Verfahren zu seiner Herstellung
DEP30307A DE1263576B (de) 1961-10-05 1962-10-05 Verfahren zur Herstellung von Cermets

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Cited By (23)

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US3364152A (en) * 1964-01-23 1968-01-16 Kempten Elektroschmelz Gmbh Process for the manufacture of a boron, aluminum or alkaline earth metal, and carbon composition and product
US3386812A (en) * 1965-12-23 1968-06-04 Atomic Energy Commission Usa Castable machine tool bit composition of boron carbide and nickel
US3459515A (en) * 1964-03-31 1969-08-05 Du Pont Cermets of aluminum with titanium carbide and titanium and zirconium borides
US3718441A (en) * 1970-11-18 1973-02-27 Us Army Method for forming metal-filled ceramics of near theoretical density
US3765300A (en) * 1967-05-22 1973-10-16 Carborundum Co Dense carbide composite for armor and abrasives
US4104062A (en) * 1969-08-13 1978-08-01 Norton Company Process for making aluminum modified boron carbide and products resulting therefrom
US4212621A (en) * 1979-06-21 1980-07-15 Michelotti Paul E Bladder molding
US4301387A (en) * 1972-03-22 1981-11-17 Foseco International Limited Protection of carbon articles
US4514268A (en) * 1982-12-30 1985-04-30 Corning Glass Works Electrolytic Al production with reaction sintered cermet component
US4605440A (en) * 1985-05-06 1986-08-12 The United States Of America As Represented By The United States Department Of Energy Boron-carbide-aluminum and boron-carbide-reactive metal cermets
US4655830A (en) * 1985-06-21 1987-04-07 Tomotsu Akashi High density compacts
US4661155A (en) * 1985-06-01 1987-04-28 Kernforschungszentrum Karlsruhe Gmbh Molded, boron carbide-containing, sintered articles and manufacturing method
US5271726A (en) * 1992-05-26 1993-12-21 E. I. Du Pont De Nemours And Company Apparatus for explosive shocking of materials
US5298051A (en) * 1987-12-23 1994-03-29 Lanxide Technology Company, Lp Method of modifying ceramic composite bodies by a post-treatment process and articles produced thereby
US5669059A (en) * 1994-01-19 1997-09-16 Alyn Corporation Metal matrix compositions and method of manufacturing thereof
US5722033A (en) * 1994-01-19 1998-02-24 Alyn Corporation Fabrication methods for metal matrix composites
US5980602A (en) * 1994-01-19 1999-11-09 Alyn Corporation Metal matrix composite
US6123895A (en) * 1998-02-24 2000-09-26 Sumitomo Electric Industries, Ltd. Aluminum base member for semiconductor device containing a nitrogen rich surface and method for producing the same
NL1016112C2 (nl) * 2000-09-06 2002-03-07 Tno Lichaam van gradueel hardmetaal zoals stansgereedschap en werkwijze voor het produceren daarvan.
US20030042647A1 (en) * 2001-08-29 2003-03-06 Pyzik Aleksander J. Boron containing ceramic-aluminum metal composite and method to form the composite
US20060286883A1 (en) * 2005-01-24 2006-12-21 The Brown Idea Group, Llc Ballistics panel, structure, and associated methods
CN103572087A (zh) * 2013-11-25 2014-02-12 武汉理工大学 碳化硼颗粒增强铝基复合材料的制备方法
CN111575522A (zh) * 2012-11-19 2020-08-25 力拓加铝国际有限公司 用于改善铝-碳化硼复合材料的可铸性的添加剂

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US2391752A (en) * 1942-05-30 1945-12-25 Stern Max Method for treating aluminum or aluminum alloy scrap
US2746133A (en) * 1951-10-16 1956-05-22 Norton Co Process of making boron carbide containing aluminum, and products thereof
US2791025A (en) * 1951-09-14 1957-05-07 Deutsche Edelstahlwerke Ag Sintered hard metals
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US2124509A (en) * 1935-07-15 1938-07-19 Philip M Mckenna Carbides of tantalum and like metals and method of producing the same
US2391752A (en) * 1942-05-30 1945-12-25 Stern Max Method for treating aluminum or aluminum alloy scrap
US2791025A (en) * 1951-09-14 1957-05-07 Deutsche Edelstahlwerke Ag Sintered hard metals
US2746133A (en) * 1951-10-16 1956-05-22 Norton Co Process of making boron carbide containing aluminum, and products thereof
US2943933A (en) * 1959-05-21 1960-07-05 Beryllium Corp Method and apparatus for making isotropic propertied beryllium sheet

Cited By (31)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3364152A (en) * 1964-01-23 1968-01-16 Kempten Elektroschmelz Gmbh Process for the manufacture of a boron, aluminum or alkaline earth metal, and carbon composition and product
US3459515A (en) * 1964-03-31 1969-08-05 Du Pont Cermets of aluminum with titanium carbide and titanium and zirconium borides
US3386812A (en) * 1965-12-23 1968-06-04 Atomic Energy Commission Usa Castable machine tool bit composition of boron carbide and nickel
US3765300A (en) * 1967-05-22 1973-10-16 Carborundum Co Dense carbide composite for armor and abrasives
US4104062A (en) * 1969-08-13 1978-08-01 Norton Company Process for making aluminum modified boron carbide and products resulting therefrom
US3718441A (en) * 1970-11-18 1973-02-27 Us Army Method for forming metal-filled ceramics of near theoretical density
US4301387A (en) * 1972-03-22 1981-11-17 Foseco International Limited Protection of carbon articles
US4212621A (en) * 1979-06-21 1980-07-15 Michelotti Paul E Bladder molding
US4514268A (en) * 1982-12-30 1985-04-30 Corning Glass Works Electrolytic Al production with reaction sintered cermet component
US4605440A (en) * 1985-05-06 1986-08-12 The United States Of America As Represented By The United States Department Of Energy Boron-carbide-aluminum and boron-carbide-reactive metal cermets
AU577760B2 (en) * 1985-05-06 1988-09-29 Regents Of The University Of California, The Boron-carbide-metal (aluminium) cermets
US4661155A (en) * 1985-06-01 1987-04-28 Kernforschungszentrum Karlsruhe Gmbh Molded, boron carbide-containing, sintered articles and manufacturing method
US4655830A (en) * 1985-06-21 1987-04-07 Tomotsu Akashi High density compacts
US5298051A (en) * 1987-12-23 1994-03-29 Lanxide Technology Company, Lp Method of modifying ceramic composite bodies by a post-treatment process and articles produced thereby
US5437833A (en) * 1987-12-23 1995-08-01 Lanxide Technology Company, Lp Method of modifying ceramic composite bodies by a post-treatment process and articles produced thereby
US5271726A (en) * 1992-05-26 1993-12-21 E. I. Du Pont De Nemours And Company Apparatus for explosive shocking of materials
US5669059A (en) * 1994-01-19 1997-09-16 Alyn Corporation Metal matrix compositions and method of manufacturing thereof
US5722033A (en) * 1994-01-19 1998-02-24 Alyn Corporation Fabrication methods for metal matrix composites
US5980602A (en) * 1994-01-19 1999-11-09 Alyn Corporation Metal matrix composite
US6507105B1 (en) 1998-02-24 2003-01-14 Sumitomo Electric Industries, Ltd. Member for semiconductor device and method for producing the same
US6123895A (en) * 1998-02-24 2000-09-26 Sumitomo Electric Industries, Ltd. Aluminum base member for semiconductor device containing a nitrogen rich surface and method for producing the same
NL1016112C2 (nl) * 2000-09-06 2002-03-07 Tno Lichaam van gradueel hardmetaal zoals stansgereedschap en werkwijze voor het produceren daarvan.
WO2002020863A1 (en) * 2000-09-06 2002-03-14 Nederlandse Organisatie Voor Toegepast-Natuur-Wetenschappelijk Onderzoek Tno Hard metal body with hardness gradient, such as punching tools
US20040093985A1 (en) * 2000-09-06 2004-05-20 Carton Eric Peter Hard metal body with hardness gradient, such as punching tools
US20030042647A1 (en) * 2001-08-29 2003-03-06 Pyzik Aleksander J. Boron containing ceramic-aluminum metal composite and method to form the composite
US6835349B2 (en) 2001-08-29 2004-12-28 The Dow Chemical Company Boron containing ceramic-aluminum metal composite and method to form the composite
US20050081963A1 (en) * 2001-08-29 2005-04-21 Pyzik Aleksander J. Boron containing ceramic-aluminum metal composite and method to form the composite
US7160627B2 (en) 2001-08-29 2007-01-09 The Dow Chemical Company Boron containing ceramic-aluminum metal composite and method to form the composite
US20060286883A1 (en) * 2005-01-24 2006-12-21 The Brown Idea Group, Llc Ballistics panel, structure, and associated methods
CN111575522A (zh) * 2012-11-19 2020-08-25 力拓加铝国际有限公司 用于改善铝-碳化硼复合材料的可铸性的添加剂
CN103572087A (zh) * 2013-11-25 2014-02-12 武汉理工大学 碳化硼颗粒增强铝基复合材料的制备方法

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DE1263576B (de) 1968-03-14
GB967136A (en) 1964-08-19
AT250686B (de) 1966-11-25

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