Patent Application
20100144510
The present invention relates to the production of sintered three-dimensional ceramic bodies, and more particularly, to the production of transparent sintered magnesium aluminate spinel domes and the like.
Magnesium aluminate spinel, MgAl2O4, (hereinafter “spinel”) is a very attractive ceramic material for use in various applications requiring a rugged, tough, scratch resistant, transparent material. Spinel articles have a wide transparency range from visible to 5.5 μm wavelength, and mechanical properties several times greater than that of glass while being remarkably lighter than ballistic glass by a factor of 2 for the same degree of armor ballistic protection.
Some of the applications for which spinel is particularly suited require three-dimensional bodies of complex geometry, such as domes for missiles and the like. Since spinel's hardness makes it very difficult to machine, successfully producing such three-dimensional spinel bodies in a cost-effective manner has proven to be no easy task. Illustrative of prior art attempts to do so are the Maguire et al. U.S. Pat. No. 4,347,210, issued Aug. 31, 1982, and the Roy et al. U.S. Pat. No. 4,930,731, issued Jun. 5, 1990.
Maguire et al. employ a hot forging technique in which a combination of tensile and compressive stresses are used to plastically deform a sintered spinel plate between the two portions of a mold defining a cavity of the desired complex shape to produce a spinel body in the shape of the mold cavity. By its very nature, the Maguire et al. technique requires a lot of material rearrangement resulting in nonuniformity in dome dimensions, especially wall thickness, and also introduces undesirable stresses into the spinel body.
The more conventional approach described by Roy et al. uses spinel powder mixed with small amount of a sintering aid, such as lithium fluoride (LiF), which is formed directly into a dome-shaped sintered spinel body in a die mold first using low pressure cold pressing to effect slight compacting of the powder, followed by densification via hot pressing or pressure sintering, followed by further densification via hot isostatic pressing. Since Roy et al. do not specify any unique mode of mixing the spinel powder with the LiF sintering aid, it can be assumed that they contemplated nothing more than traditional mechanical dry mixing, such as mortar and pestle, ball milling or attritor milling. However, as has been well documented by Villalobos et al. in U.S. Patent Application Publication No. 2004/0266605, published Dec. 30, 2004, U.S. Pat. No. 7,211,325, issued May 1, 2007, and U.S. Pat. No. 7,528,086, issued May 5, 2009, inhomogeneity and contamination problems associated with mechanical mixing of the sintering aid with the spinel powder prior to sintering have been found to be the leading cause of high product rejection rates in attempting to produce defect-free transparent sintered spinel articles.
A known technique for producing complexly shaped, three-dimensional bodies of sintered ceramic materials other than spinel, is freeze casting. Representative U.S. patents describing this technique are the Herrmann U.S. Pat. No. 3,330,892, issued Jul. 11, 1967 and the Sundback et al. U.S. Pat. No. 5,047,182, issued Sep. 10, 1991. In freeze casting, a ceramic powder is mixed with a sublimable vehicle to form a slurry which is cast and then frozen in a mold of the desired complex shape. The frozen part or compact is then demolded and the vehicle is removed by sublimation, i.e., freeze-drying, to obtain a green body which is thereafter sintered to the final densified product. More recently, both camphene and eutectic mixtures of camphor and naphthalene were described as suitable for use as nonaqueous sublimable vehicles in the freeze casting of alumina articles at or near room temperature, by Araki et al. in J. Am. Ceram. Soc. 87 (10) 1859-1863 (2004) and J. Am. Ceram. Soc. 87 (11) 2014-2019 (2004).
What appears to be lacking from the prior art is any reference to the successful application of the freeze casting technique or any modification thereof to the production of transparent sintered three-dimensional spinel bodies. One of the reasons for this might very well be the need to first develop a more effective ready-to-sinter spinel powder that overcomes the inhomogeneity and contamination problems associated with the mechanical mixing of the sintering aid with the spinel powder prior to sintering. Such a powder and its method of preparation are described and claimed in the commonly owned U.S. Patent Application of Raouf O. Loutfy et al. entitled “Ready-to-Sinter Spinel Nanomixture and Method for Preparing Same,” filed on even date herewith as Docket No. 7000AB.1, and which is incorporated herein by reference in its entirety.
The present invention is an adaptation based on the conventional freeze casting technique, and which is referred to herein as “freeze-forging.” It differs from conventional freeze casting by using a free flowing granulated frozen solid mix which is molded into net shape by cold forging, rather than a liquid vehicle-solids slurry which is molded by casting and then freezing.
The freeze-forging method of the present invention produces a net-shape sintered three-dimensional ceramic body of a desired complex geometry, using as starting materials a ready-to-sinter ceramic powder and a nonaqueous liquefied vehicle comprising a sublimable organic binding agent and having a solidification temperature of from about room temperature to below about 200° C. The ceramic powder is mixed with the liquefied vehicle to form a homogeneous pseudoplastic shear thinning ceramic mix comprising from about 30 to about 50 weight percent of the ceramic powder dispersed in the liquefied vehicle. The temperature of the ceramic mix is then reduced to below the solidification temperature of the vehicle to thereby freeze the ceramic mix. The frozen ceramic mix is then crushed into powdered form, and the powdered frozen ceramic mix, which is free flowing and held together by the frozen vehicle and is completely conformable to any given mold cavity, is cold forged in a mold of the desired geometry to form a solidified green body of the desired geometry. The green body is then densified by hot pressing or pressureless sintering into a sintered ceramic body of the desired geometry and substantially free of the vehicle at early stages of the sintering process, and the sintered ceramic body is thereafter subjected to further densification via hot isostatic pressing to thereby substantially eliminate any residual porosity in the sintered body.
While the freeze-forging method of the present invention has been designed primarily for the production of transparent sintered three-dimensional spinel bodies, such as domes and the like, from the ready-to-sinter spinel nanomixture powder described and claimed in the above referenced Loutfy et al. U.S. Patent Application, and to be described more fully hereinafter, the process is equally as applicable to a wide range of other sinterable ceramic materials.
The various ceramic materials, in addition to magnesium aluminate spinel, to which the freeze-forging method of the present invention is applicable, include ceramics such as alumina, zirconia, magnesia, beryllia, silica, cordierita, silimanita, tabular alumina, crystobalita, tridimita, yttria, chromite, lanthanide doped oxide ceramics, yttrium aluminate garnet, vitreous china, porcelain, stoneware, AlON, Si3N4, AlN, SiAlON, SiC and B4C.
The freeze-forging method of the present invention is particularly advantageous for the production of net-shape transparent sintered three-dimensional spinel bodies, in conjunction with the ready-to-sinter spinel nanomixture powder described and claimed in the Loutfy et al. U.S. patent application referred to above. The nanomixture powder consists of a nanomixture of magnesium aluminate spinel nanoparticles and a uniformly distributed controlled concentration of an inorganic sintering aid. The sintering aid will typically be LiF, in a controlled concentration within the range of from about 0.2 to about 2.0 weight percent, preferable from about 0.4 to about 1.25 weight percent, and optimally from about 0.5 to about 0.75 weight percent.
The nanomixture powder is formed by a process comprising mixing the spinel nanoparticles with an aqueous solution of the LiF sintering aid to form a spinel dispersion, decreasing the solubility limit of the LiF in the spinel dispersion to a point sufficiently low so as to induce precipitation of LiF nanoparticles out of solution and into a mixed dispersion with the spinel nanoparticles, separating from the mixed dispersion an in-situ formed nanomixture of the spinel nanoparticles and the LiF nanoparticles, drying the spinel-LiF mixture, and deagglomerating the dried spinel-LiF nanomixture. The resulting ready-to-sinter spinel powder will be composed of LiF nanoparticles 20-100 nm in size, uniformly distributed among spinel nanoparticles 10-2000 nm in size.
In the preferred embodiment of the freeze-forging method of the present invention, the above-described spinel nanomixture powder will be one of the two starting materials. The other precursor is a nonaqueous liquefied vehicle comprising a sublimable organic binding agent and having a solidification temperature from about room temperature to below about 200° C., ideally within the range of from about 30° C. to about 60° C. Suitable binding agents include, for example, camphor, naphthalene, camphor-napthalene mixtures and camphene, with camphor-napththlene mixtures of from about 55 to about 80 weight percent camphor and from about 45 to about 20 weight percent naphthalene being preferred. The most preferred binder is a close to eutectic mixture of about 60 weight percent camphor and about 40 weight percent naphthalene, since it has a solidification temperature very close to room temperature, i.e., 31-32° C.
The vehicle may consist of the binder alone or, if desired, may also include very small amounts of an organic solvent, such as alcohol, acetone or benzene, to increase its fluidity. In either case, the vehicle is liquefied by being heated to a temperature above its solidification temperature, preferably to from about 10° C. to about 40° C. above the solidification temperature, prior to its being mixed with the spinel nanomixture powder. The powder, likewise, may be preheated to the same temperature prior to being mixed.
Referring now to the flow sheet diagram of
The temperature of the spinel mix is then reduced to below the solidification temperature of the vehicle, preferably to below 0° C., to thereby freeze the spinel mix.
Thereafter, the frozen spinel mix is crushed into granulated powdered form, e.g., mortar and pestle, to a size finer than about 30 mesh. The crushed material is classified on a 30 mesh plastic sieve, with the coarser fraction being recrushed until all solids pass through the 30 mesh screen. The powdered frozen spinel mix is a free flowing powder which is held together by the frozen vehicle and which is completely conformable to any given mold cavity under compression given its pseudoplastic shear thinning properties.
The next step in the process is the cold forging step. The powdered frozen spinel mix is loaded into a die mold having upper and bottom rams both conformed to the desired three-dimensional shape. The die may be made of graphite, common metallic alloys or steel, preferably graphite. The powder may be protected by using a thin film of polymer plastic liner on both faces of the die. Forging is carried out at or near room temperature at a pressure of from about 15 to about 25 Ksi in two stages of from about 2 to about 5 minutes each stage, using a uniaxial Carver type press whose capacity will vary, for example, from 30 to 100 ton, depending upon the size of the body being formed. The cold forging step produces a solidified green body of the desired three-dimensional shape, with green density as high as 38-46% of theoretical density (Th.D.), and net shaped to fit exactly the final graphite dies to be used for densifying the body.
The solidified green body resulting from the cold forging step is then densified, either by hot pressing or by pressureless sintering, into a sintered spinel body of the desired three-dimensional shape and substantially free of both the vehicle and the LiF sintering aid, both of which sublime out of the green body during the sintering step. When hot pressing is used, the green body loaded in a graphite die, which may be the same graphite die that was employed in the cold forging step, is transferred to the hot press, for example, a 60 ton Centorr vacuum hot press, and hot pressed. A suitable hot pressing profile comprises LiF liquefaction at 950° C., followed by LiF sublimation at 1300° C. to 1450° C., followed by sintering at 1600° C. to 1800° C. under a ram pressure of from 500 to 5000 psi. A suitable pressureless sintering profile would be similar, differing only in the final sintering stage of the profile, which would be 1650° C. to 1900° C. for 2 to 3 hours, with no applied pressure.
The sintered spinel body is thereafter subjected to further densification via hot isostatic pressing at 1600° C. to 1750° C. at a pressure of 27 to 30 Ksi for 2 to 5 hours, to thereby substantially eliminate any residual porosity in the sintered body and improve its flexural strength.
By following the freeze-forging procedure described above, spinel domelets with apertures in the range of from 50° to 170°, as well as full hemispherical spinel domes with apertures as large as 180°, have been produced in sizes ranging up to 7 inches in diameter. These transparent sintered spinel domes and domelets, densified to 99.95+% theoretical density, and after being rendered and mechanically polished, were found to be free of any ceramic defects and, as illustrated by the transmission properties graph of
The invention is further illustrated by way of the following examples.
The freeze-forging forming of 3.5″ radius, 66° aperture, 0.15″ thick, 4″ base diameter spinel domelet blank was pursued in this example. Through computer 3D modeling a 99.95% of Th.D. sintered domelet blank volume was calculated to be 35.2 cc. This corresponded to a total sintered spinel weight of 126 g. Accordingly, 126 g of nanomixed spinel powder containing 0.75% LiF was mixed with 54 g of camphor/naphthalene sublimable eutectic vehicle. The vehicle was heated up to 70° C. until fluid and homogeneous prior to mixing with the prepared spinel powder. The vehicle was added by slowly adding it onto the solids while dispersing at the same time. The solids were dispersed under mechanical agitation for approximately 10 minutes. Large agglomerates were broken at the end of this period. A homogeneous pseudoplastic, shear thinning powder mix was produced. The powder mix was then frozen by lowering the temperature to −10° C. by placing it into a freezer. The frozen mix was then crushed (mortar and pestle) to a size finer than 30 mesh. The crushed composite material was classified on a 30 mesh plastic sieve. The coarser fraction was re-crushed until all solids passed through the 30 mesh plastic screen.
The deagglomerated −30 mesh composite mix was transferred to a graphite die for cold forging forming with upper and bottom rams conformed to the desired sintered domelet blank shape. The powder was protected by using a thin film of polymer plastic liner on both faces. The part was forged at 20 Ksi, two stage pressing, 3 min each stage, using a uniaxial 30 Ton capacity Carver type press. A 4″ domelet blank body with a green density 40% of ThD was obtained.
The 4″ spinel domelet green blank preform was left loaded into the same graphite die and transferred to a 60 ton Centorr vacuum hot press. The domelet blank was hot pressed at 4000 psi, 1600° C., for 210 minutes, at 5×10−5 torr pressure. A weight reduction of 4.7% was observed. A high quality hot pressed domelet blank was obtained exhibiting high transmission, with no discolorations or inclusions. The domelet blank was further sintered via hot isostatic pressing (HIP) at 29750 psi, 1750° C. for 5 hours, in Argon, to eliminate any residual porosity and to improve its flexural strength to 300 MPa.
The final domelet was rendered and polished at Nu-Tek, Aberdeen, Md., to produce the final intended polished domelet 0.11″ thick, weighing 75.6 grams. No ceramic defects were obtained. A very high quality polished domelet was produced.
The freeze-forging forming of 4″ diameter, 180° aperture hemispherical spinel dome blank was pursued in this example. Through computer 3D modeling a total sintered spinel weight of 457 g. Accordingly, 457 g of nanomixed spinel powder containing 0.75% LiF was mixed with 192 g of camphor/naphthalene sublimable eutectic vehicle. The vehicle was heated up to 70° C. until fluid and homogeneous prior to mixing with the prepared spinel powder. The vehicle was added by slowly adding it onto the solids while dispersing at the same time. The solids were dispersed under mechanical agitation for approximately 10 minutes to obtain a homogeneous shear thinning mix. Large agglomerates were broken at the end of this period. The powder mix was then frozen by lowering the temperature to −10° C. by placing it into a freezer. The frozen mix was then crushed (mortar and pestle) to approximately a size finer than 30 mesh. The crushed composite material was classified on a 30 mesh plastic sieve. The deagglomerated −30 mesh composite mix was transferred to a graphite die for cold forging forming with upper and bottom rams conformed to the desired sintered 4″ in diameter hemispherical dome blank. The powder was protected by using a thin film of polymer plastic liner on both faces. The part was forged at 20 Ksi, two stage pressing, 5 min each stage, using a uniaxial 30 Ton capacity Carver type press. A 4″, 180° aperture, dome body with a green density 39% of Th.D. was obtained.
The 4″ diameter, 180° aperture, hemispherical spinel dome blank green preform was momentarily removed from the green forming die and loaded into the hot pressing graphite die protected by upper and lower 3D contoured grafoil liners. The loaded graphite die was transferred to a 60 ton Centorr vacuum hot press. The domelet was hot pressed at 3200 psi, 1600-1625° C., for 400 minutes, at 5×10−5 torr pressure. A very high quality hot pressed dome blank was obtained exhibiting high transmission, with no discolorations or inclusions. The dome was further sintered via hot isostatic pressing (HIP) at 29750 psi, 1700° C. for 3 hours, in Argon, to eliminate any residual porosity and to improve its flexural strength.
The freeze-forging forming of 6″ in diameter, 140° aperture spinel domelet blank was pursued in this example. Through computer 3D modeling a total sintered spinel weight of 1530 g. Accordingly, 1530 g of nanomixed spinel powder containing 0.75% LiF was mixed with 640 g of camphor/naphthalene sublimable eutectic vehicle. The vehicle was heated up to 70° C. until fluid and homogeneous prior to mixing with the prepared spinel powder. The vehicle was added by slowly adding it onto the solids while dispersing at the same time. The solids were dispersed under mechanical agitation to obtain a homogeneous mix for approximately 10 minutes. The powder was then prepared following the same procedure of Example 1 and Example 2.
The deagglomerated −30 mesh composite mix was transferred to a graphite die for cold forging forming with upper and bottom rams conformed to the desired sintered 6″ in diameter hemispherical domelet blank. The powder was protected by using a thin film of polymer plastic liner on both faces. The domelet was forged at 20 Ksi, two stage pressing, 5 min each stage, using a uniaxial 30 Ton capacity Carver type press. A 6″, 140° aperture, domelet body with a green density 41% of Th.D. was obtained. The hemispherical spinel domelet blank green preform was momentarily removed from the green forming die and loaded into the hot pressing graphite die protected by upper and lower 3D contoured grafoil liners. The loaded graphite die was transferred to a 60 ton Centorr vacuum hot press. The domelet was hot pressed at 3600 psi, 1600-1625° C., for 660 minutes, at 5×10−5 ton pressure. A very high quality hot pressed domelet blank was obtained exhibiting high transmission, with no discolorations or inclusions. The dome was further sintered via hot isostatic pressing (HIP) at 29750 psi, 1700° C. for 3 hours, in Argon, to eliminate any residual porosity and to improve its flexural strength.
The freeze-forging forming of 7″ diameter, 180° aperture spinel dome blank was pursued in this example. Through computer 3D modeling a total sintered spinel weight of 2002 g. Accordingly, 2002 g of nanomixed spinel powder containing 0.75% LiF was mixed with 850 g of camphor/naphthalene sublimable eutectic vehicle. The vehicle was heated up to 70° C. until fluid and homogeneous prior to mixing with the prepared spinel powder. The vehicle was added by slowly adding it onto the solids while dispersing at the same time. The solids were dispersed under mechanical agitation to obtain a homogeneous mix for approximately 10 minutes. The powder was then prepared following the same procedure used in the previous examples.
The deagglomerated −30 mesh composite mix was transferred to a graphite die for cold forging forming with upper and bottom rams conformed to the desired sintered 7″ in diameter hemispherical dome blank. The powder was protected by using a thin film of polymer plastic liner on both faces. The domelet was forged at 22 Ksi, two stage pressing, 5 min each stage, using a uniaxial 100 ton capacity Carver type press. A 7″ diameter, 180° aperture, dome body with a green density 39% of Th.D. was obtained. The hemispherical spinel dome blank green preform was removed from the green forming die and loaded into the hot pressing graphite die protected by upper and lower 3D contoured grafoil liners. The loaded graphite die was transferred to a 60 ton Centorr vacuum hot press. The domelet was hot pressed at 3200 psi, 1600-1650° C., for 1290 minutes, at 5×10−5 ton pressure. A very high quality hot pressed dome blank was obtained exhibiting high transmission, with no discolorations or inclusions. The dome was further sintered via hot isostatic pressing (HIP) at 29750 psi, 1700° C. for 3 hours, in Argon, to eliminate any residual porosity and to improve its flexural strength.
This application claims the benefit of U.S. Provisional Application No. 61/135,035, filed Jul. 16, 2008.
This invention was made with Government support under Government Contract No. W31P4Q-07-C-0080, awarded by the U.S. Army. The Government has certain rights in the invention.
| Number | Date | Country | |
|---|---|---|---|
| 61135035 | Jul 2008 | US |
