USRE37875E1 - Solid imaging process using component homogenization - Google Patents

Images

Classifications

• • C—CHEMISTRY; METALLURGY
  • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
  • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
  • C23C26/00—Coating not provided for in groups C23C2/00 - C23C24/00
  • C23C26/02—Coating not provided for in groups C23C2/00 - C23C24/00 applying molten material to the substrate
• • 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
  • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
  • B22F1/09—Mixtures of metallic powders
• • 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
  • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
  • B22F1/12—Metallic powder containing non-metallic particles
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
  • B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
  • B29C64/00—Additive manufacturing, i.e. manufacturing of three-dimensional [3D] objects by additive deposition, additive agglomeration or additive layering, e.g. by 3D printing, stereolithography or selective laser sintering
  • B29C64/10—Processes of additive manufacturing
  • B29C64/165—Processes of additive manufacturing using a combination of solid and fluid materials, e.g. a powder selectively bound by a liquid binder, catalyst, inhibitor or energy absorber
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B33—ADDITIVE MANUFACTURING TECHNOLOGY
  • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
  • B33Y10/00—Processes of additive manufacturing
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B33—ADDITIVE MANUFACTURING TECHNOLOGY
  • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
  • B33Y70/00—Materials specially adapted for additive manufacturing
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B33—ADDITIVE MANUFACTURING TECHNOLOGY
  • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
  • B33Y70/00—Materials specially adapted for additive manufacturing
  • B33Y70/10—Composites of different types of material, e.g. mixtures of ceramics and polymers or mixtures of metals and biomaterials
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C12/00—Alloys based on antimony or bismuth
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C21/00—Alloys based on aluminium
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C28/00—Alloys based on a metal not provided for in groups C22C5/00 - C22C27/00
• • C—CHEMISTRY; METALLURGY
  • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
  • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
  • C23C26/00—Coating not provided for in groups C23C2/00 - C23C24/00
• • 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
  • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
  • B22F10/20—Direct sintering or melting
  • B22F10/28—Powder bed fusion, e.g. selective laser melting [SLM] or electron beam melting [EBM]
• • 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
  • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
  • B22F10/30—Process control
  • B22F10/32—Process control of the atmosphere, e.g. composition or pressure in a building chamber
• • 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
  • B22F12/00—Apparatus or devices specially adapted for additive manufacturing; Auxiliary means for additive manufacturing; Combinations of additive manufacturing apparatus or devices with other processing apparatus or devices
  • B22F12/40—Radiation means
  • B22F12/41—Radiation means characterised by the type, e.g. laser or electron beam
  • B22F12/43—Radiation means characterised by the type, e.g. laser or electron beam pulsed; frequency modulated
• • 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
  • B22F12/00—Apparatus or devices specially adapted for additive manufacturing; Auxiliary means for additive manufacturing; Combinations of additive manufacturing apparatus or devices with other processing apparatus or devices
  • B22F12/40—Radiation means
  • B22F12/44—Radiation means characterised by the configuration of the radiation means
• • 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
  • B22F12/00—Apparatus or devices specially adapted for additive manufacturing; Auxiliary means for additive manufacturing; Combinations of additive manufacturing apparatus or devices with other processing apparatus or devices
  • B22F12/60—Planarisation devices; Compression devices
  • B22F12/67—Blades
• • 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
  • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
  • B29K—INDEXING SCHEME ASSOCIATED WITH SUBCLASSES B29B, B29C OR B29D, RELATING TO MOULDING MATERIALS OR TO MATERIALS FOR MOULDS, REINFORCEMENTS, FILLERS OR PREFORMED PARTS, e.g. INSERTS
  • B29K2105/00—Condition, form or state of moulded material or of the material to be shaped
  • B29K2105/0058—Liquid or visquous
  • B29K2105/0064—Latex, emulsion or dispersion
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
  • B29K—INDEXING SCHEME ASSOCIATED WITH SUBCLASSES B29B, B29C OR B29D, RELATING TO MOULDING MATERIALS OR TO MATERIALS FOR MOULDS, REINFORCEMENTS, FILLERS OR PREFORMED PARTS, e.g. INSERTS
  • B29K2105/00—Condition, form or state of moulded material or of the material to be shaped
  • B29K2105/0088—Blends of polymers
• • 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
  • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
  • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
  • Y02P10/00—Technologies related to metal processing
  • Y02P10/25—Process efficiency

Definitions

• the invention relates to a process of making models, molds, near net shape parts, and other integral objects using an imagewise exposure of a dispersion of components to radiation.
• the process is based on homogenizing the components of the dispersion to form an alloy which have properties different from the properties of the dispersion or its individual components.
• Layer-by-layer solid imaging techniques including stereolithography and selective laser sintering, have been used to produce models, mold patterns, and near net shape production parts.
• Stereolithography provides high accuracy and excellent surface finish, but does not normally allow for productions of objects in engineering materials such as nylon or ABS.
• Selective laser sintering can produce objects in nylon or polycarbonate but cannot produce objects of full density, and generally produces objects having low surface quality.
• U.S. Pat. No. 5,354,414 describes imagewise formation of an integral object which can be separated from the non-imaged regions. Processes of brazing, soldering and welding are disclosed for producing the integral object.
• U.S. Pat. No. 4,575,330 describes generation of three-dimensional objects by creating a cross-sectional pattern of the object on the surface of a fluid medium.
• the physical state of the medium is altered to form successive cross-sectional layers and provide a step-wise laminar buildup of the desired object.
• the patent discloses free-radical curing of acrylate.
• U.S. Pat. No. 5,474,719 describes a solid imaging process wherein high viscosity liquids are viscosity-reduced during coating and allowed to increase in viscosity during imaging steps.
• the compositions contain a photohardenable monomer and a photoinitiator, and the photohardening methods suggested involved free-radical polymerization, cationic polymerization, anionic polymerization, condensation polymerization, addition polymerization, and the like.
• U.S. Pat. No. 4,938,816 describes a process for selectively sintering a layer of powder to produce a part comprising a plurality of sintered layers.
• the bulk density of the powder is increased prior to sintering or melting the powder by exposure. Attaining high bulk density of powders for sintering is difficult, however, and requires the use of substantial pressures.
• the invention comprises a process for producing three-dimensional integral objects by imagewise radiation of a dispersion of components A and B, comprising the steps of:
• steps a)-c) repeating steps a)-c) by applying each successive layer of dispersion onto the previous layer, such that each new homogenized region becomes integral with the previous homogenized region to form a homogenized, integral, three-dimensional object.
• Components A and B may be polymers, metals, ceramics, or combinations of these materials.
• the components A and B are capable of alloying, when exposed to imagewise radiation, to form an alloy of the two components A and B which is characterized by physical and/or chemical properties which are distinct from the physical and/or chemical properties of the dispersion of components A and B.
• the components are combined into intimate contact to form the dispersion, preferably with one component being in a liquid state or above solidus state, prior to homogenization.
• the homogenized alloy article may be separated from the unexposed dispersion based on the difference in physical and/or chemical properties.
• the homogenized alloy of components A and B may have a melting point different from the melting point of component A, the melting point of component B, or the melting point of an intimate dispersion of components A and B.
• FIG. 1 is sectional view of equipment suitable for carrying out the process of the invention
• FIG. 2 is a phase digram illustrating homogenization of two components into an alloy.
• FIG. 3 is a sectional view of alternative equipment suitable for carrying out the process of the invention.
• FIG. 4 is a sectional view of still further alternative equipment suitable for carrying out the process of the invention.
• FIG. 5 is a phase diagram illustrating the phase relationship of gallium and aluminum.
• the term “homogenized” or “homogenization”, for the purposes of this disclosure, will refer to the formation of an alloy between the substances which are homogenized. This requires sufficient molecular or elemental mixing between the components to result in properties, either physical or chemical or both, which are different from the properties of the individual components in intimate contact in the form of a dispersion.
• the difference in properties of the alloy is preferably sufficient in itself to permit separation of the alloyed components from non-alloyed, surrounding regions of the dispersed components following imagewise exposure.
• the alloyed (homogenized) material has a different melting point than the dispersion of components A and B, and thus, the alloyed three-dimensional article can be separated from the surrounding dispersion based on the difference in melting point.
• Components which can be alloyed from a dispersion of components in the manner described, and which may be used as component A and component B in the practice of the invention include polymers, metals, and ceramics. In some instances, nonmetal elements may be alloyed with metals.
• Preferred alloys formed by homogenization include polymer/polymer alloys, metal/metal alloys, ceramic/ceramic alloys, polymer/metal alloys, and metal/ceramic alloys. Choice of the particular material combination to be used depends on the nature and intended us of the three-dimensional part or object being produced.
• the components A and B should be selected so as to be: capable of alloying under the exposure of imagewise radiation within a practical range of intensity; the alloy must have physical and/or chemical properties distinct from the properties of an intimate dispersion of A in B or B in A; and the alloy of A and B should preferably be separable from unalloyed dispersion of A and B based on the difference in physical and/or chemical properties.
• the components may consist of polymers, which can be dispersed together and alloyed by the application of radiation.
• a first particulate polymer (A) is dispersed in a second, liquid polymer (B) to form an intimate dispersion.
• Application of imaging radiation causes the particulate polymer to assume a different form in the liquid polymer, which changes the conformation of the particulate to allow for more intimate interaction between the first polymer and the liquid polymer.
• This interaction of the two polymers forms a polymer alloy having properties (for example melting point) different from polymer A, polymer B, and the intimate dispersion of polymer A in polymer B.
• the homogenization to form an alloy between polymers is a non-polymerization interaction, and polymerization techniques (free radical, condensation, and like mechanisms between monomers and/or oligomers and optionally initiators) are excluded from the definition of “homogenization” as used herein.
• the interaction between polymers upon imagewise exposure to radiation is primarily noncovalent, involving hydrogen bonding, n-pi complexing, pi-pi complexing, or dipole interactions, although incidental grafting, cross-linking or the like which may occur between the polymers is not excluded.
• the components may consist of metals or ceramics which, when contacted with appropriate imaging radiation of appropriate intensity, form a metal or ceramic alloy having properties distinguishable from the properties of the components.
• powdered bismuth and powdered magnesium can be combined, in the ratios of about 30 atomic percent bismuth to about 70 atomic percent magnesium, as an intimate powder dispersion.
• the bismuth powder and the magnesium powder retain their characteristic, individual properties. Even if the bismuth powder (melting point 268.5° C.) is melted sufficiently to wet the magnesium powder (melting point 650° C.) and thus increase the intimate contact between the components, each component in the dispersion still retains its essential and unique properties.
• homogenization for purposes of the invention requires intimate mixing of at least two components with resultant formation of an alloy between the components, which cannot be achieved using conventional sintering techniques.
• the sintered object in the case of sintering, the sintered object cannot be separated from a surrounding powder bed based on melting temperature, whereas convenience of separation is an advantage associated with certain embodiments of the present invention.
• Brazing is a metal joining process wherein a nonferrous filler metal wets a base metal when molten in a manner similar to a solder and its base metal. There is a slight diffusion of the filler metal into the hot, solid base metal, or a surface alloying of the base and filler metals. A surface bond is formed between materials that does not cause changes in physical properties in the individual components except at the surface. Brazing, welding and soldering are also different from homogenization as described herein.
• homogenization does not require complete mixing. It is recognized, for example, that solidified alloys may contain crystals or phases of varying composition. In the context of the present invention, homogenization progresses to the extent that the homogenized regions forming the three-dimensional integral object have different properties, and normally can be separated from the non-homogenized surround regions based on those different properties.
• Suitable polymer materials for components A and B are disclosed generally in the following disclosures, which are incorporated herein by reference. Polymer alloys are disclosed in Battelle, “Report on Major Developments in Polymer Blends”, Vols. 1-3, Columbus Division, Columbus, Ohio, (1986); and Barlow et al., Polymer Blends and Alloys, A Review of Selected Considerations, Polymer Engineering and Science, 21: 985 (1981). Polymers used as component A or B may comprise pure polymer or may comprise polymers and related monomers and solvents.
• the repeating functional units of one polymer interact with the repeating units of the other polymer(s) in a manner which renders the polymers miscible and makes the alloy thermodynamically stable upon imaging. As noted, such interactions are primarily noncovalent.
• the polymer alloys have different properties than the individual polymers or the polymers in dispersion, such properties including, for example, melting temperature, glass transition temperature, heat distortion temperature, and the like.
• Exemplary of polymer pairs suitable for components A and B of the invention are the following: polycaprolacetone/poly(vinylchloride); polycaprolactone/Saran; polycaprolactone/bisphenol A polycarbonate; poly(vinyl methyl ether)/phenoxy; poly (ethylene oxide)/phenoxy; poly(ethylene oxide)/poly (acrylic acid); BPA polycarbonate/PHFA; polystyrene/polyphenylene oxide.
• Preferred ceramic/ceramic and ceramic/metal alloys are disclosed in “Phase Diagrams for Ceramicists”, Vols. 1-8, The American Ceramic Society, Columbus, Ohio.
• Material pairs selected from within the materials disclosed in these references should be selected to achieve the criteria described above, primarily, alloy formation upon imagewise exposure to radiation.
• the components A and B exhibit properties in accordance with the phase diagram shown in FIG. 2 .
• FIG. 2 illustrates certain preferred principles to be considered, but should not be understood as limiting the possible phase relationships between components.
• FIG. 2 shows, by means of a phase diagram the characteristics of a binary alloy of component A and component B having properties particularly contemplated for use in this invention.
• the X-axis starts with 100% of component A at the left and increasing amounts of component B moving toward the right.
• the Y-axis shows increasing temperatures.
• Component A tends to crystallize in crystalline structure ⁇ especially when in pure form.
• Component B tends to crystallize in crystalline structure ⁇ especially when in pure form.
• Components A and B preferably form an intercomponent compound AB at a certain relative percentage of component A and component B.
• Intercomponent compounds AB may have different component ratios than the stochiometric ratios which are required with other chemical reactions and with other chemical compounds.
• the type of bonding for chemical compounds may be different from that of alloy crystals and intercomponent compounds.
• the intercomponent compound AB provides a thermodynamic barrier which allows a distinct separation based on melting point.
• Intercomponent compounds AB are not necessarily line compounds, as shown, but may exist over a broader composition range of component A and component B.
• the melting point of component A is shown as MpA
• the melting point of component B is shown as MpB
• the melting point of intercomponent compound AB is shown as MpAB.
• L liquid
• components A and B form a crystalline alloy comprised of ⁇ and intercomponent crystal AB.
• components A and B form a crystalline alloy comprised of ⁇ and intercomponent crystal AB.
• the mixture of components forms either a liquid L or a dispersion of one of the solid crystalline components ⁇ , ⁇ , or AB and liquid L.
• melting begins to occur.
• the melting point of intercomponent compound AB, MpAB is the highest, followed by MpA, then EuA, then MpB, with the melting point of EuB being the lowest.
• Phase diagrams such as FIG. 2 represent the state of component mixtures under equilibrium conditions where the components are mixed on a molecular or atomic level in the liquid state and are allowed to cool slowly such that the crystalline structure and composition occur as depicted (or where solid state diffusion exists and sufficient time is allowed such that an equilibrium is reached). If cooling is fast, different crystalline structures or compositions may exist. If solid powders of component A are introduced into a liquid bath of component B at a temperature above MpB but below MpA, a dispersion of powdered A in liquid B may result rather than a molecular or atomic mix of components A and B. This is more likely when the solubility of liquid component B is low in solid component A since, under such temperature conditions, homogenization may not occur or may occur slowly. Homogenization may also be somewhat inhibited if liquid component B does not easily wet solid component A. However, it is preferred that good wetting exist between components A and B.
• aluminum and gallium form a eutectic EuB with a melting point of roughly 26.6° C. for weight percent compositions of approximately 20 to 92.2% gallium.
• a dispersion comprising an alloy A 1 B 1 of slightly more than 20 weight % gallium with aluminum as the liquid phase component B and a powdered component A of aluminum is provided and coated into a layer, then a homogenized alloy region A 2 B 2 of the dispersion would have a significantly higher melting point.
• dispersion A 1 B 1 +(S)A For example, consider the following dispersion A 1 B 1 +(S)A:
• component B Alloy A 1 B 1 containing 30% gallium and 70% aluminum
• the dispersion A 1 B 1 +(S)A would begin to form a liquid phase if heated to above 26.2° C.
• the amount of liquid can be calculated based upon tie-line calculations well known in the art.
• the dispersion (L)A 1 B 1 +(S)A could be coated into a layer.
• the layer could be imagewise homogenized forming an alloy region A 2 B 2 having a composition of 85% aluminum and 15% gallium. This region A 2 B 2 (assuming complete homogenization of the aluminum and gallium) would have a melting point of over 300° C.
• the difference between the homogenized alloy A 2 B 2 melting point and the melting point EuB of the dispersion (L)A 1 B 1 +(S)A would allow separation of the homogenized region A 2 B 2 from surrounding dispersion(L) A 1 B 1 +(S)A.
• liquidus curve extends up to 99.2% by weight of gallium. This reduces the amount of liquid formed (based upon tie-line estimates) in the liquid component (L)A 1 B 1 +(S)A so that higher temperatures T 1 should be used during coating.
• coating pressures such as the use of a heated roller, could be used to aid the formation of the dispersion (L)A 1 B 1 +(S)A into a layer.
• the system illustrated in FIG. 1 utilizes focused radiation adapted to be scanned imagewise by means of, for example, an X-Y mirror scanning apparatus.
• a cylinder 101 and coating platform surface 101 ′ are positioned such that the platform surface 101 ′ is generally normal to and in the focal region of beam 107 .
• piston 102 Within the cylinder 101 is piston 102 , which is adapted to move up and down relative to the platform surface 101 ′.
• the piston 102 is driven by a motorized screw drive 103 .
• a doctor blade 104 is adapted such that the doctor blade edge 104 ′ is slidably in close proximity with the platform surface 101 ′ and traverses the platform surface 101 ′ and the piston surface 102 ′ or above the piston surface 102 ′, should the piston 102 be lower than the platform surface 101 ′.
• the doctor blade 104 is driven by a motor drive/linear bearing mechanism not shown.
• a portion of dispersion of components A and B 105 is placed on the platform surface 101 in advance of the motion of the doctor blade 104 such that the blade edge 104 ′ can spread the dispersion 105 across the platform surface 101 ′ and across the piston surface 102 ′.
• Enough dispersion 105 is placed forward of the motion of the doctor blade 104 to fill in a cavity made within the cylinder 101 between the platform surface 101 ′ and the surface of the piston 102 ′.
• the piston 102 is positioned within the cylinder 101 such that the piston surface 102 ′ is approximately one layer thickness below the surface of the platform 101 ′.
• Doctor blade 104 traverses across the platform surface 101 ′ and spreads the dispersion 105 into the cavity made by the piston 102 and the cylinder 101 .
• the coated dispersion 106 within the cavity is exposed imagewise by beam 107 in part regions 108 and 108 ′, the part regions being shown as having different shapes.
• the coated dispersion 106 is heated by the focused beam 107 such that the components A and B are homogenized and form alloy regions 108 and 108 ′ which are hardened and can be separated from the surrounding liquid dispersion 106 .
• the first formed regions 108 and 108 ′ are adhered to the piston surface 102 ′.
• piston 102 is moved down another one layer thickness forming a cavity between the dispersion surface 106 ′, the part surface 108 and 108 ′, and the platform surface 101 ′.
• More dispersion 105 is placed in advance of the motion of the doctor blade 104 . The dispersion 105 is spread into the cavity forming a new coated dispersion surface 106 ′.
• this dispersion surface 106 ′ is exposed imagewise with beam 107 forming new homogenized part surfaces 108 and 108 ′.
• Adequate exposure is provided by beam 107 to ensure adhesion between the new part surfaces 108 and 108 ′ and the previously homogenized part surfaces exposed after the first coating step. This adhesion is assured by providing enough energy through beam 107 to make the new layers 108 and 108 ′ thicker than the coated layer 106 ′.
• the adhered layers form integral parts 109 and 109 ′.
• multilayer homogenized integral parts 109 and 109 ′ are formed.
• heat Q is provided simply by ambient air surrounding the apparatus of FIG. 1, it may be necessary in some cases to pre-heat the surface of piston 102 ′ prior to coating the first layer to assure adhesion between the first image region 108 and 108 ′ and the piston surface 102 ′.
• This preheating Q can be accomplished with a hot air gun, or can be applied to any portion of the apparatus of FIG. 1 by any heating method, for example resistance wires, ambient air, or exposure beam 107 .
• the parts 109 and 109 ′ as shown are cantilevered sections and other unsupported sections as depicted in FIG. 1 .
• the parts formed may be solid parts, or may be partially hollow. There are no size limitations on the parts which can be formed other than the capacity of the equipment and the fineness of the dispersion 106 .
• a further preferred means of carrying out the invention is described with reference to both FIG. 1 and FIG. 2.
• a dispersion 105 is supplied before doctor blade 104 .
• the dispersion 105 comprises a dispersion of liquid alloy A 1 B 1 which has a composition coincident with eutectic isothermal EuB at the eutectic point and also comprises a solid component of pure A (see FIG. 2 ).
• the composition of the dispersion 105 is such that, if completely homogenized by beam 107 , the dispersion 105 would form an alloy region 108 having a composition A 2 B 2 , which is shown in FIG. 2 as a composition coincident with the eutectic point on the eutectic isothermal line EuA.
• Heat Q is supplied to the apparatus such that the temperature of the apparatus in FIG. 1 is at T 1 in FIG. 2 .
• the dispersion 105 is also at temperature T 1 as shown in FIG. 2 during spreading by doctor blade 104 over the platform surface 101 ′ and piston surface 102 ′, or over the previous coated dispersion 106 or homogenized objects 109 and 109 ′. Therefore dispersion 105 has a liquid phase component (L)A 1 B 1 and a solid phase component (S)A at temperature T 1 as shown in FIG. 2 .
• the piston 102 Prior to coating the dispersion 105 , the piston 102 is moved down in the cylinder 101 a distance such that a cavity exists above the piston surface 102 ′ and below the platform surface 101 ′.
• the distance is the depth of one layer of the object 109 and 109 ′ to be formed.
• a layer of coated dispersion 106 fills this cavity.
• a focused beam 107 is then scanned imagewise over the surface of coated dispersion 106 ′ such that homogenized regions 108 and 108 ′ are formed.
• the focused beam 107 supplies enough heat to raise the temperature of the dispersion 106 from temperature T 1 to temperature T 2 , as shown on FIG. 2 .
• the piston 102 is moved down the distance of one layer creating a cavity between the surface of dispersion 106 ′ or the layer 108 and 108 ′ and the platform surface 101 ′.
• New dispersion 105 is spread into this cavity creating an additional layer of coated dispersion 106 .
• This layer of dispersion 106 is scanned imagewise with beam 107 such that all the components in the dispersion 106 are heated to temperature T 2 causing melting and homogenization in the image regions 108 and 108 ′.
• the new image regions 108 and 108 ′ are allowed to cool until new solid homogenized alloy regions (S)A 2 B 2 108 and 108 ′ are formed.
• Dispersion 106 Upon completion of fabrication of integral objects 109 and 109 ′, the piston 102 is raised. Dispersion 106 , maintained at temperature T 1 , is allowed to flow away thereby separating the dispersion 106 from the integral objects 109 and 109 ′. If necessary, dispersion is removed from the object by washing, solvent, heating, or the like.
• the doctor blade 104 and the dispersion 105 are heated to a temperature T 1 while the remainder of the equipment shown in FIG. 1 is maintained at a temperature less than EuB. All the fabrication steps would be the same as described above, with the exception of the last step.
• the piston 102 would be raised.
• the solidified block consisting of solidified coated dispersion 106 and integral objects 109 and 109 ′ would be removed from the piston surface 102 ′.
• the solidified block would then be placed in an oven at temperature T 1 where the dispersion 106 would be melted away from the integral objects 109 and 109 ′.
• the piston 102 would be placed in the oven with the solidified block attached. The dispersion would then melt and flow away leaving the integral objects 109 and 109 ′ which could be removed from the piston 102 .
• the lower melting component(L)A 1 B 1 be comprised of a significant amount of component A. This has two advantages, there is less of a density difference and less of component A need be present in order to enrich the alloy to a higher melting composition.
• Such a lower melting component (L)A 1 B 1 would have a composition comprising component B in a % slightly more than intercomponent compound AB as shown in FIG. 2 .
• FIG. 3 Another method to carry out the process of the instant invention is shown in FIG. 3 .
• the apparatus of FIG. 3 is very similar to that of FIG. 1 . However, the operation is somewhat different.
• a solid powdered component 306 has a lower density than that of a liquid phase 310 .
• Piston 302 is positioned within cylinder 301 such that a cavity is formed between piston surface 302 ′ and coating platform surface 301 ′. The thickness of the cavity is less than the thickness of one layer.
• Solid powdered component 305 [(S)A in FIG. 2 ] is spread by doctor blade 304 with tip 304 ′ slidably in contact with coating platform surface 301 ′ such that the cavity is filled with spread solid powder component 306 [(S)A in FIG. 2 ].
• the piston 302 is translated down by drive mechanism 303 the remaining thickness of the layer (i.e. the distance between the piston surface 302 ′ and the platform surface 301 ′ is one layer thickness).
• Pumping device 312 pumps liquid phase component 311 [(L)A 1 B 1 in FIG. 2 ] through connector hose 313 and platform nozzle 314 into the cavity until the solid powder component 306 is substantially even with the top of the platform surface 301 ′.
• Heat Q is supplied to the apparatus and the pump 312 to maintain a temperature of T 1 (as in FIG. 2 ). Since the solid powder component 306 has a lower density than the liquid phase component 310 , the powder 306 floats at the surface but is preferably wetted by the liquid phase component 310 .
• Focused beam 307 is scanned imagewise over the surface of the solid powder component 306 causing it to melt (the temperature is raised to T 2 as in FIG. 2 ).
• the melted powder component 306 then rapidly homogenizes with the liquid phase component 310 in the image region and forms an alloy region 308 and 308 ′ [(L)A 2 B 2 in FIG. 2 ].
• This alloy region 308 and 308 ′ is allowed to cool to below temperature EuA in FIG. 2 and becomes solidified alloy region 308 and 308 ′.
• Pump mechanism 312 pumps liquid phase composition 311 into the cavity such that any remaining solid powder component 306 is raised above coating platform surface 301 ′.
• Doctor blade 304 is translated across the coating platform surface 301 ′ and the solid powdered component 306 and some of the liquid phase component 310 are combined into a dispersion 315 which is pushed into container 316 .
• Piston 302 is moved down less than the thickness of one layer.
• New solid powder component 305 is placed in front of doctor blade 304 where it is spread into the cavity made by the solidified alloy regions 308 and 308 ′ and the surface of liquid phase component 310 .
• the piston 302 is translated down the remaining distance of one layer.
• Pump mechanism 312 pumps more liquid phase component 311 into the cavity adding to liquid phase component 310 in the cavity.
• Enough liquid phase component 310 is pumped until the surface of the solid powder component 306 is substantially level with the surface of the coating platform 301 ′.
• Focused beam 307 is then scanned imagewise forming new homogenized alloy regions 308 and 308 ′ which adhere to the previously formed image regions 308 and 308 ′, where they overlap, thereby forming integral objects 309 and 309 ′.
• the steps of scraping off remaining dispersions 315 , creating a cavity for coating new powder 306 , creating a cavity for pumping in new liquid phase component 310 , imagewise exposing with beam 307 to homogenize new regions 308 and 308 ′ which adhere to integral object 309 and 309 ′ are repeated until the integral objects 309 and 309 ′ are completed.
• the integral objects 309 and 309 ′ are separated from the powder 306 due to lack of inter-particle bonding, and from the liquid phase component 310 due to the difference in melting temperature.
• the solid phase component 306 could be supplied in the form of a thin sheet which is melted imagewise by focused beam 307 to form homogenized alloy regions 308 and 308 ′.
• a new sheet 306 could be supplied for each layer. Such a method could be used independent of the density of the material components.
• Still another embodiment involves the addition of a material component A in either solid or liquid form, in an imagewise fashion, to the surface of a liquid phase component (L)A 1 B 1 contained in a vat or a piston/cylinder cavity.
• a material component A in either solid or liquid form, in an imagewise fashion, to the surface of a liquid phase component (L)A 1 B 1 contained in a vat or a piston/cylinder cavity.
• homogenization would result forming an alloy (S)A 2 B 2 having a higher melting temperature than the temperature of surrounding liquid component (L)A 1 B 1 .
• the homogenized regions would harden into layers which would be built into integral objects.
• the integral objects could then be separated from the surrounding liquid phase component (L)A 1 B 1 since the objects would be solid at that temperature.
• the imagewise addition of material component could be accomplished using ink jet technology or powder jet technology.
• the preferred property change for separation of imaged objects from non-imaged dispersion is a melting point change.
• the melting point change assuming it is sufficiently large, allows a separation of the homogenized region from the unhomogenized region (unexposed to radiation) though the application of heat which causes the lower melting point region to melt away from the higher melting point region.
• the layer-by-layer process as described herein allows the production of objects with property changes that exist deep within the object and with property changes of specific shape within the object.
• the dispersion of bismuth and magnesium it is possible to produce shaped object regions, which are homogenized such that the intermetallic compound Mg 2 Bi 2 (melting point 823° C.) and dispersed Mg is the primary alloy, within an object which has greater homogenization such that an alloy having a temperature of 551° C. is formed.
• the homogenization time or temperature could be lower for the intermetallic compound region, such that some magnesium powder is surrounded by the intermetallic compound.
• liquid phase sintering In the practice of liquid phase sintering it is known that approximately 35% volume liquid is preferred, since this volume percent allows optimum rearrangement of the solid particles in the dispersion and therefore the greatest amount of densification. However, greater or lesser amounts of liquid may be present depending on the wetting characteristics of the particles with the liquid and the solubility characteristics of the components.
• the process of the present invention involves a layer-by-layer processing of the dispersion or a surface liquid phase sintering process, rather than, for example, an impregnation of liquid into a compacted powder as in a bulk liquid phase sintering process, problems related to pore growth and such can be easily relieved through the surface during processing.
• the optimum liquid to solid ratios for surface liquid phase sintering are much broader than those ratios recommended for bulk liquid phase sintering. It is also important to note that a liquid phase need not be present just prior to the homogenization step when practicing the instant invention. Indeed it may be preferable to have the liquid phase present only during the coating steps, during the homogenization steps, and during the object separation steps when components A and B have a degree of solubility such that over a short period of time, premature homogenization occurs, since homogenization is usually greatly enhanced when at least one component is in the liquid state. Another method to prevent premature homogenization would be to use coated particles. The coating could be such that homogenization is only possible at elevated temperatures. An example coating would be an oxidized coated solid particle A. This oxide coating would be lost at the higher homogenization temperatures and could be reduced in an atmosphere of, for example, hydrogen. Or, the oxide coating could be incorporated as a third component into the homogenized alloy article.
• the liquid phase need not be comprised of a pure component B or a pure component A.
• the liquid phase may be comprised of, for example, an alloy of component A and component B at a eutectic point such that upon heating above the eutectic isothermal line EuB temperature the liquid phase does not have crystalline components AB or ⁇ .
• Such a condition ensures a greater amount of liquid to solid particle ratio and also reduces the amount of homogenization required to change the composition to a higher melting alloy.
• the solid particles are comprised of an alloy of components A and B at the eutectic point on the isothermal eutectic line EuA.
• an eutectic point alloy With such an eutectic point alloy, the temperatures needed during the homogenization step or the amount of heat given during imagewise exposure can be lower since the alloy transitions directly to a liquid without containing some crystalline content of ⁇ or AB.
• use of an eutectic point alloy as the solid particle may require that more of the solid component be provided in the dispersion prior to homogenization since a certain amount of component A must be present in the imagewise homogenized region for a higher melting point alloy to be formed.
• the atmosphere surrounding the process is critical. For example, some components may easily oxidize and require the use of vacuum conditions, inert gases, or reducing atmospheres in order to form the integral objects. Atmosphere can be controlled in the process or used in the alloy reaction. For example, oxygen can be used to form a ceramic alloy on the surface of a layer of liquid phase metal. Such a ceramic alloy or cermet (metal ceramic) typically has a much higher melting point than the surrounding pool of metal, allowing easy separation of an integral object.
• the metal component in this case could be supplied in sheet form and the oxygen could be supplied with, for example, an acetylene torch (with excess oxygen for some materials which are easily reduced with heat or with insufficient oxygen for materials which oxidize in the presence of carbon oxides) which is translated imagewise over the surface of each sheet stacked one on another.
• the heat from the torch would create a localized liquid phase component which would react with oxygen forming a higher melting alloy region.
• a new sheet would then be applied to the previous sheet and higher melting alloy region.
• the torch would then be translated imagewise over the surface of the new sheet forming a higher melting alloy region which would preferentially adhere to the previous alloy regions forming part of an integral object. This process would continue until all the layers of the integral object are formed.
• the sheets and the integral object would be placed in an oven (with a vacuum, inert or reducing atmosphere) such that the non-oxidized portions of the sheets are melted and allowed to flow away from the higher melting alloy integral object.
• regions of lower melting point by enriching a higher melting point layer with a component which, when homogenized with the higher melting point component, forms a lower melting point alloy.
• a sheet of a higher melting point component A could be supplied.
• a second component B could be deposited imagewise on the surface of the sheet.
• the imagewise deposition of the second component could be a perimeter of the integral object to be formed or a region of greater area.
• the second component would be chosen such that, when the higher melting component and the second component are homogenized, a lower melting point alloy results.
• the second component would also be chosen such that the melting point of the sheet component would be depressed when in contact with the melted second component.
• the stacking of the sheets and the imagewise deposition of the second component would continue until all layers of the potential object have been applied.
• the stacked sheets (with the imagewise deposited second component) would then be placed in an oven at a temperature (above the depressed melting point temperature of the sheet but below the melting point of the sheet component) where the second component would melt and cause the stacked sheets to melt imagewise forming imagewise regions of relatively low melting alloy which would be drained away from the non-imaged stacked sheet regions.
• the non-imaged stacked sheet regions would then be heated to a temperature such the sheet layers sinter together and create an integral object.
• the imagewise deposition step could be accompanied by an imagewise heat step such that a lower melting alloy results at each layer. If the temperature of the stacked sheets are above the melting point of the alloy, the alloy could be drained or removed by other means, such as by vacuum, at each layer.
• Separation of the dispersion from the homogenized object can also be enhanced by using a suitable solvent.
• the melting point of the dispersion could be lowered after the homogenized object has been formed by homogenizing the dispersion with additional low melting component or by the addition of another component capable of lowering the dispersion melting point.
• homogenized regions and integral objects may be significantly soluble in the liquid phase component or even a solid phase component over a period of time. This condition would cause a loss of resolution in the object during manufacture since the object might dissolve in the liquid phase or the solid dispersion.
• components are chosen such that the homogenized object is not significantly soluble in the dispersion of A and B. Problems in this regard can be avoided if the annealing temperature of the homogenized object is above the temperature required for separation of the homogenized object from the dispersion.
• homogenized objects could be formed using nickel and copper as the components. Copper has a melting point of 1085° C. and nickel has a melting point of 1455° C.
• the melting point of homogenized alloys of copper and nickel would increase roughly linearly as a function of increasing nickel.
• typical annealing temperatures for copper-nickel alloys are below 870° C. indicating substantial solid solubility of copper with nickel. Therefore it is unlikely that a dispersion could be maintained or that the dispersion could be separated from the homogenized object, since the solubility of these components and alloys is high and the homogenized object would begin to lose resolution below the melting temperature of the low melting copper component.
• FIG. 4 illustrates a process embodiment designed to minimize the length of time that the integral object is in contact with a liquid phase component.
• a platform 402 having a surface 402 ′, is translated using a motorized drive 403 and positioned above and coplanar to a plate 417 .
• the plate 417 may be made of, for example, fused silica glass such that focused beam 407 can be transmitted through it, or for example a high melting but conductive material, such as tungsten, which would absorb the energy from focused beam 407 and conduct the energy in the form of heat through a plate surface 417 ′ to dispersion 405 .
• platform 402 would be positioned in the liquid pool of dispersion 405 such that the platform surface 402 ′ would be one layer thickness from the surface of plate 417 ′.
• the temperature of dispersion 405 (and preferably substantial portions of the apparatus of FIG. 4 as provided by heat Q) is T 1 and the composition is (L)A 1 B 1 +(S)A.
• focused beam 407 is then scanned imagewise on regions 408 of the dispersion 405 in this layer raising the temperature [to T 2 of FIG. 2 ] of these regions 408 and causing homogenization [and a new composition (L)A 2 B 2 of FIG.
• the melting point of the regions 408 is raised [to above the solidus lines of either a or EuA in FIG. 2 ] and upon cooling below the solidus, form solid regions 408 [having a composition (S)A 2 B 2 in FIG. 2 ].
• the solid regions 408 adhere to platform surface 402 ′ but do not substantially adhere to plate surface 417 ′.
• platform 402 is raised at least the distance of one layer such that dispersion 405 forms a layer between solid region 408 and the surface of the plate 417 ′.
• Focused beam 407 is then scanned imagewise such that a new region 408 is homogenized and upon cooling preferentially adheres to the homogenized region 408 of the previous layer thereby forming a part of integral objects 409 and 409 ′.
• the steps of positioning the platform 402 such that a new layer of dispersion 405 is formed between homogenized solid region 408 and exposing with focused beam 407 imagewise such that new homogenized regions 408 are adhered to integral object 409 and 409 ′ is continued until the objects 409 and 409 ′ are complete.
• the level of dispersion 405 can be such that adequate dispersion 405 is supplied to form the object 409 and 409 ′ but not enough to keep the object 409 and 409 ′ submerged for long periods of time.
• an object 409 ′ shown in cross section
• an enclosed volume 409 ′′ a hollow region surrounded by part surfaces
• a region of an object formed in a layer-by-layer process as described herein may be enriched, with greater amounts of the same or another component, such that is has different magnetic properties than the remainder of the object.
• a gear could be formed with a region of different magnetic susceptibility which when rotated past a magnetic sensor would create an electrical pulse like an encoder.
• a turbine could be formed with an internal region of a lower melting alloy or density which would provide an automatic balancing mechanism for the turbine at its operating temperature.
• regions could be included in integral objects which have different hardness, ductility, electrical/thermal conductivity, elasticity, color, etc., than the remainder of the object.
• the dispersion was mixed at room temperature to uniform consistency and moderate viscosity.
• Trimethylolpropane triacrylate is a liquid at room temperature and formed a liquid phase of the dispersion. Below approximately 43° C., the polyethylene oxide is essentially insoluble in the trimethylolpropane triacrylate. Above this temperature, sudden homogenization ensues with the homogenized region forming a rubbery solid having a higher melting point.
• the graphite was added to increase the surface absorption of the laser beam energy used (Argon Ion laser operating in the visible with all visible lines predominantly 488 and 514 nm). The graphite would not be necessary if laser wavelengths having greater surface absorbance were used or if other imagewise heating methods were employed.
• the surface of the dispersion was scanned with the laser beam in a series of parallel lines spaced approximately 0.002 inches apart.
• the diameter of the beam spot was approximately 167 ⁇ m 1/e 2 and the power was 2.89 watts.
• the photospeed of the dispersion was obtained by pouring a portion of the dispersion in a petri-dish and exposing the surface of the dispersion in one inch square regions. Shortly after exposure, and after the region was allowed to cool, the exposed surface was removed. The bottom surface of the layer was scraped off with a spatula and the layer thickness was then measured with calipers.
• other acrylates or diluents and other solid polymers are useful in the practice of the instant invention so long as the diluent and the solid polymer form an alloy having a higher melting temperature than at least the melting point of the diluent allowing easy separation of the alloy object from the diluent dispersion.
• the parts 109 and 109 ′ had cantilevered sections and other unsupported sections as depicted in FIG. 1 .
• the size of the parts were as large as 2 inches (50 mm) square and 0.64 inches (16.3 mm) high. However, there was no identifiable limitation of size other than that of the capacity of the equipment used and the fineness of the dispersion 106 .
• the dispersion 106 was capable of producing unsupported, cantilevered and bridging, regions in parts 109 and 109 ′ as large as 0.4 inches (10 mm).
• the parts 109 and 109 ′ were cleaned in isopropyl alcohol.
• the parts produced in this example can be used in an investment casting process where the parts are used as a pattern and dipped in a ceramic slurry.
• the pattern with the ceramic slurry shell can then be fired, burning off the pattern and hardening the ceramic shell.
• the pattern could first be dipped in a free radical initiator bath, for example a peroxide, which would tend to cross-link the trimethylolpropane triacrylate at the surface of the part.
• the pattern could be dipped in a free-radical photoinitiator liquid such as Irgacure (1173, 2-Hydroxy-2-methyl-2-phenyl-propan-1-one; Ciba Corporation, Hawthorne N.Y.), or any liquefied free-radical photoinitiator, and then exposed to UV light in order to cross-link the outer portions of the pattern.
• a free-radical photoinitiator liquid such as Irgacure (1173, 2-Hydroxy-2-methyl-2-phenyl-propan-1-one; Ciba Corporation, Hawthorne N.Y.)
• any liquefied free-radical photoinitiator liquefied free-radical photoinitiator
• the pattern could be coated with, for example, a wax or a paint.
• the pattern may expand to such a degree that it cracks the shell before the pattern burns-off during firing.
• the trimethylolpropane triacrylate will polymerize during the firing step and therefore the pattern will shrink.
• homogenized objects, made from the dispersion were exposed to hot air from a hot air gun. The objects heated in this manner did not melt but became very stiff and then eventually charred.
• incorporation of a free-radical photoinitiator which is also thermally degradable, or a thermally degradable free-radical initiator, such as for example a Vazoo® (Cyclohexanecarbonitrile, 1,1′-azobis, available from DuPont, Wilmington, Del.) in the formulation would further ensure shrinkage, due to acrylate free-radical polymerization of the pattern during firing.
• a thermally degradable free-radical initiator such as for example a Vazoo® (Cyclohexanecarbonitrile, 1,1′-azobis, available from DuPont, Wilmington, Del.) in the formulation would further ensure shrinkage, due to acrylate free-radical polymerization of the pattern during firing.
• the photoinitiator not form significant quantities of free-radicals due to exposure by beam 107 , such as would occur when a dispersion containing a UV photoinitiator is exposed by visible or infra-red light, or that the temperature reached during the fabrication of the object 109 not be high enough to cause the thermally degradable free-radical initiator to form significant quantities of free-radicals such that the acrylate is polymerized during object formation.
• some polymerization of the acrylate as well of homogenization of the dispersion may be advantageous and preferred.
• Example I The exposures necessary to produce a layer for the dispersion in Example I were somewhat higher than normally required.
• Light absorbers such as graphite are often not as efficient as certain thermal dyes which can be mixed on a molecular level, which have a greater yield for conversion of photon energy to phonon energy, and which may not have a large emittance.
• graphite and some other dyes have a fairly high and somewhat uniform absorption over the UV to near infrared spectrum, it should be appreciated that often other dyes have significantly greater absorption over a narrower wavelength region and are therefore optimally associated with lasers having an emission wavelength within the absorption wavelength of the dye. Examples of other thermal dyes are listed in U.S. Pat. No.
• SQS squalarium dye
• Kawamura U.S. Pat. No. 4,283,475
• Gravestejin U.S. Pat. No. 4,508,811
• SQS is best used with a diode laser emitting at a wavelength of approximately 830 nm. It should also be appreciated that in some cases the dispersion itself may have a significant absorption at the emission wavelength of some lasers. In such a case, it may not be necessary to add any other absorber in order to induce localized heat and subsequent homogenization of the dispersion in an imagewise manner.
• imagewise heat can be provided form other sources, such as for example an acetylene torch which, if fitted with a small tip, can produce a flame of resolution in the range of mils, for example “The Little Torch”, manufactured by Smith Equipment, Waterton, S.D.
• a flame tip can be translated over the surface of the dispersion in an imagewise fashion by, for example, the adaptation of an X-Y pen plotter such that the flame tip replaces the pen.
• the dispersion and the homogenized region are electrically conductive and are adapted to form a ground plane
• localized heat could be provided through the use of a translated carbon electrode, of opposite polarity to the ground plane, adapted to replace the pen in an X-Y pen plotter.
• the degree of homogenization may be controlled by, for example, homogenization temperature or homogenization time.
• the imagewise homogenization may also be aided through the use of localized ultrasonic energy, for example a modulated laser beam as taught in U.S. Pat. No. 4,330,699 by Farrow.

Landscapes

• Chemical & Material Sciences (AREA)
• Engineering & Computer Science (AREA)
• Materials Engineering (AREA)
• Mechanical Engineering (AREA)
• Organic Chemistry (AREA)
• Metallurgy (AREA)
• Manufacturing & Machinery (AREA)
• Chemical Kinetics & Catalysis (AREA)
• Ceramic Engineering (AREA)
• Structural Engineering (AREA)
• Composite Materials (AREA)
• Civil Engineering (AREA)
• Physics & Mathematics (AREA)
• Optics & Photonics (AREA)
• Powder Metallurgy (AREA)
• Sampling And Sample Adjustment (AREA)
• Detergent Compositions (AREA)
• Solid State Image Pick-Up Elements (AREA)

Abstract

Description

Claims (51)

Priority Applications (1)

Applications Claiming Priority (2)

Related Parent Applications (1)

Publications (1)

Family

ID=25297407

Family Applications (2)

Family Applications Before (1)

Country Status (9)

Cited By (4)

Families Citing this family (37)

Citations (44)

Family Cites Families (6)

• 1997
  • 1997-04-30 US US08/846,271 patent/US5980812A/en not_active Ceased
• 1998
  • 1998-04-28 DE DE69840812T patent/DE69840812D1/en not_active Expired - Lifetime
  • 1998-04-28 EP EP98919933A patent/EP1015213B1/en not_active Expired - Lifetime
  • 1998-04-28 AU AU72612/98A patent/AU7261298A/en not_active Abandoned
  • 1998-04-28 AT AT98919933T patent/ATE430648T1/en active
  • 1998-04-28 WO PCT/US1998/008490 patent/WO1998048993A1/en active Application Filing
  • 1998-04-28 JP JP54726498A patent/JP4766723B2/en not_active Expired - Fee Related
  • 1998-04-28 DE DE98919933T patent/DE98919933T1/en active Pending
  • 1998-04-28 ES ES98919933T patent/ES2325696T3/en not_active Expired - Lifetime
  • 1998-04-28 CA CA002288153A patent/CA2288153C/en not_active Expired - Fee Related
• 2000
  • 2000-11-13 US US09/711,128 patent/USRE37875E1/en not_active Expired - Lifetime

Patent Citations (47)

Non-Patent Citations (18)

Also Published As

Similar Documents

Legal Events