US3248764A - Method for improving grain structure and soundness in castings - Google Patents

Method for improving grain structure and soundness in castings Download PDF

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US3248764A
US3248764A US336462A US33646264A US3248764A US 3248764 A US3248764 A US 3248764A US 336462 A US336462 A US 336462A US 33646264 A US33646264 A US 33646264A US 3248764 A US3248764 A US 3248764A
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mold
columnar
furnace
metal
casting
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George D Chandley
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Northrop Grumman Space and Mission Systems Corp
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TRW Inc
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D27/00—Treating the metal in the mould while it is molten or ductile ; Pressure or vacuum casting
    • B22D27/04—Influencing the temperature of the metal, e.g. by heating or cooling the mould
    • B22D27/045—Directionally solidified castings
    • C—CHEMISTRY; METALLURGY
    • C30—CRYSTAL GROWTH
    • C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
    • C30B11/00—Single-crystal growth by normal freezing or freezing under temperature gradient, e.g. Bridgman-Stockbarger method
    • C—CHEMISTRY; METALLURGY
    • C30—CRYSTAL GROWTH
    • C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
    • C30B29/00—Single crystals or homogeneous polycrystalline material with defined structure characterised by the material or by their shape
    • C30B29/60—Single crystals or homogeneous polycrystalline material with defined structure characterised by the material or by their shape characterised by shape
    • C30B29/605—Products containing multiple oriented crystallites, e.g. columnar crystallites

Definitions

  • the present invention relates to improvements in meth- -ods and apparatus Ifor producing sound metal castings, and specifically, to the production of metal castings having columnar grain structures.
  • Columnar structures are formed by the unidirec-tional growth of dendrites during solidication.
  • the rel-ationship between the dendritic structure and the columnar grains is not exact.
  • Each columnar grain is usually composed of more than one dendrite, and the number may vary from a few -to several hundred.
  • the interdendritic spacing is related to the soliication rate only.
  • Columnar grain size may be affected by factors other than the solidification process, such as -ordinary 4grain growth. Despite these differences, ⁇ the most convenient approach for the examination of columnar structure form-ation is through lthe study of the dendrites formed during solidification.
  • the primary requirement Ifor the formation of a parallel dendritic structure is the presence of a unidirectional thermal gradient.
  • the initial solidification occurs at the mold wall due to a chill effect, assuming the mold wall to 'be below the solidiiication temperature of the metal.
  • This chill zone consists of many iine dendrites having a random orientation.
  • the initial freezing releases the heat of fusion, resulting in some temperature rise locally, arresting the chill zone formation.
  • the dendrites begin to grow into the melt at a rate dependent upon the amount and depth of the supercooling.
  • the aligned dendrites formed will display a preferred crystallographic orientation, depending on the crystal system, and, in more complex systems, on the particular metal or alloy. This behavior can be r-ationalized in 4the ICC following rway. Crystals growing into a melt are formed with the planes of maximum atomic density forming the faces. In the face centered cubic metals, for example, the faces of the crystals would form an octohedran bounded by the (lll) planes. The direction of maximum growth lcoincides with the maximum dimension of this octohedran, t-he plane. It would be expected, then, that the (100) would be aligned parallel to the predominating rthermal gradient and this has been observed in numerous cases.
  • the direction of preferred orientation (100) in each case, is generally the same regardless of the metal involved. In systems of non-cubic symmetry the particular metal or alloy will determine the direction. In closed packed hexagonal systems, f-or example, the c/a ratio is an important factor in determining the direction of preferred orientation.
  • the solidiiication -of alloys proceeds along the lines mentioned prev-iously, but in a somewhat more complex mechanism since concentration gradients as well as thermal gradients may exist during solidication.
  • Casting variables affect columnar structure through their influence on the thermal or compositional gradients developed in the molds. These variables include metal superheat, initial mold temperatures, the use of chills or exotherrnie materials, and the alloy composition. Variation of the thermal gradients within the range of columnear formation also inliuences the structure of the casting. lf la steep thermal gradient exists, the rapid rate of heat extraction requires rapid solidication. At the same time the relatively short supercooled layer restricts the lengths of the dendrites extending into the melts. During solidiiication mass transport of solute between the dendrites must take place. Since the overall solidication rate is determined by the rate of heat removal, the diffusion distances must be reduced to permit the proper distribution of solute to take place.
  • Another object of the invention is to provide a method for establishing undirectional thermal gradients in a casting so that the gradients exist parallel tio the direction of major stress which will exist in the casting during use.
  • Still another object of the invention is to provide an apparatus for producing castings having columnar grain structures which permits free expansion of ⁇ the 4shell molds contained therein.
  • Another object of the invention is to provide an apparatus for producing columnar grain type castings which enables one to control the location and intensity of the unidirectional thermal gradients existing therein.
  • a unidirectional thermal gradient is provided in the casting by positioning a ceramic shell mold having uniformly thin Wall thicknesses vwithin the furnace, while permitting free expansion of the shell mold therein.
  • a highly heat conductive material is applied to the mold perpendicular to the direction in which the unidirectional thermal gardient is to exist. Then, radiant heat energy is directed at the mold to preheat the por-tions of the mold above the melting temperature of the metal to be introduced, followed by pouring the moltent metal into the mold and cooling the metal within the mold to produce a casting having an oriented columnar grain structure alonig the line of the thermal gradient.
  • reference numeral indicates generally a furnace assembly for the purposes of the present invention including an outer wall 11 composed of a suitable refractory brick material or the like, and an inner radiating enclosure 12 composed of a material such as graphite. Disposed intermediate the outer wall 11 and the radiating wall 12 is a layer 13 of an insulating refractory material.
  • the radiating Wall 12 is heated to a high temperature by any suitable means, such as induction coils 14, although other heat sources such as electrical resistance heating, gas, or the like, could also be employed.
  • the outer Wall 11 rests upon a support 16 and on this support there is disposed a block 17 of highly thermally conductive material, such as copper. If desired, additional heat transfer means may be included within the copper block, such as a circulating fluid system.
  • a ceramic shell mold 18 of generally uniform thin wall structure rests on the block 17. Generally, the mold 18 will have a thickness of from about /m inch to about 1A inch or so.
  • the mold 18 includes an open ended casting cavity portion 19 and .an open ended riser lcavity portion 21 into which the molten metal is introduced.
  • a top heat shield 22 having a central aperture 23 is disposed over the furnace assembly to prevent heat loss from the top of the mold.
  • a pair of radiation shields 24 and 26 is interposed between the mold 1S and the radiating walls of the heat radiator 112.
  • the shield-s 24- and 26 may take the form of cylindrical bodies which are concentric with the casting cavity 19.
  • the shields may be composed of zirconium silicate or other refractory material which is capable of resisting the high temperatures involved in such furnaces.
  • the purpose of the shields is to control the temperature of various zones Within the casting cavity, as desired, since in some instances it is necessary to provide areas of differing thermal gradients within the same casting.
  • the location and the extent of the shields 24 and 26 determines the amount of heat radiation energy which the casting cavity can assimilate from the radiating walls and thereby determines the temperature in preselected areas or zones of the mold.
  • a relatively loosely packed bed 2S of ceramic particles composed, for example, yof zirconium silicate yor other material which has a sintering temperature in excess of the operating temperature of the furnace.
  • the bed is sufficiently loosely packed, however, so that it permits relatively free expansion of the ceramic shell mold in that area.
  • a first stage jet engine turbine blade was cast in an apparatus of the type shown in the drawing.
  • the graphite radiation source was heated by induction to 2800 F. and held for 20 minutes.
  • a nickel base superalloy havin-g an analysis in the range of l5 to 25% chromium, 5 to 30% cobalt, 0.5 to 5% titanium, 2 to 5% aluminum, 1 to 5% niobium, 5 to 11% tungsten, and the balance essentially nickel was poured into the mold at a pouring temperature of 2700 F. and allowed to cool for 25 minutes.
  • the graphite source was then allowed to cool slowly and reached the melting temperature of ⁇ the alloy about 55 minutes after the orignal pour was made.
  • the insulation around the base was granular magnesia and the conducting heat sink under the insulation was pure copper. This assembly produced an entirely columnar jet engine blade which had its grain parallel to the axis of major stress.
  • the method and apparatus of the present invention provide a carefully controllable means for securing preferred grain orientation in ca-stings, and the production of columnar structures in which the grains are oriented in the direction of maximum stress.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Manufacture And Refinement Of Metals (AREA)
  • Crucibles And Fluidized-Bed Furnaces (AREA)
  • Furnace Housings, Linings, Walls, And Ceilings (AREA)
  • Molds, Cores, And Manufacturing Methods Thereof (AREA)

Description

May 3, 1966 G. D. CHANDLEY 3,248,764
METHOD FOR IMPROVING GRAIN STRUCTURE AND SOUNDNESS IN CASTINGS med aan. a, 1964 can no!) oooooooooooo o; Vir-waan I NVENTOR.
Tea/ye 0. @hand/sy BY U / AT ORNEYS United States Patent O 3,248,764 METHOD FOR IMPROVING GRAIN STRUCTURE AND SOUNDNESS IN CASTINGS George D. Chandley, Alliance, Ohio, assigner to TRW Inc., a corporation of Ohio Filed Jan. 8, 1964, Ser. No. 336,462 4 Claims. (Cl. 22-211) This application is a continuation-in-part of my application Serial No. 232,763, 'filed October 2A, 1962, and now abandoned.
The present invention relates to improvements in meth- -ods and apparatus Ifor producing sound metal castings, and specifically, to the production of metal castings having columnar grain structures.
The presence of columnar zones in castings h-as been recognized for s-ome time, but until recently, this -type of structure was considered a defect and not nearly so desirable as t-he equiaxed structure. In recent years, however, the properties of columnar structures have undergone reexamination and it has now been determined that in some applications, the columnar structures .are markedly superior to equiaxed structures. F or example, it has been found that the -high temperature properties of clumnar structures are superior particularly in fracture resistance and ductility under creep loading conditions.
Columnar structures are formed by the unidirec-tional growth of dendrites during solidication. The rel-ationship between the dendritic structure and the columnar grains is not exact. Each columnar grain is usually composed of more than one dendrite, and the number may vary from a few -to several hundred. The interdendritic spacing is related to the soliication rate only. Columnar grain size, however, may be affected by factors other than the solidification process, such as -ordinary 4grain growth. Despite these differences, `the most convenient approach for the examination of columnar structure form-ation is through lthe study of the dendrites formed during solidification.
The primary requirement Ifor the formation of a parallel dendritic structure is the presence of a unidirectional thermal gradient. When the metal first enters the mold, the initial solidification occurs at the mold wall due to a chill effect, assuming the mold wall to 'be below the solidiiication temperature of the metal. This chill zone consists of many iine dendrites having a random orientation. The initial freezing releases the heat of fusion, resulting in some temperature rise locally, arresting the chill zone formation. At the interface of the chill zone and `the melt the dendrites begin to grow into the melt at a rate dependent upon the amount and depth of the supercooling.
(Initially, 'all dendrites at the chill zone-melt interface grow at equal rates, since equal supercooling is present. However, those oriented parallel to the thermal gradient are growing into an area of continued supercooling. Those oriented unfavorably cannot advance as rapidly in the direction of the thermal gradient, since only a component of the growth velocity is aligned with this gradient. The dendrites growing parallel to the gradient, since they have already undergone some growth, will give off a latent heat of fusion, due to the freezing process. This heat of fusion increases the tempera-ture at the base of the dendrites and decreases the amount of supercooling available `for growth of the more unfavorably oriented neighbors. `In this manner, the growth of the msoriented dendrites is stilied, and only those aligned with the thermal gradient ywill undergo significant growth.
The aligned dendrites formed will display a preferred crystallographic orientation, depending on the crystal system, and, in more complex systems, on the particular metal or alloy. This behavior can be r-ationalized in 4the ICC following rway. Crystals growing into a melt are formed with the planes of maximum atomic density forming the faces. In the face centered cubic metals, for example, the faces of the crystals would form an octohedran bounded by the (lll) planes. The direction of maximum growth lcoincides with the maximum dimension of this octohedran, t-he plane. It would be expected, then, that the (100) would be aligned parallel to the predominating rthermal gradient and this has been observed in numerous cases. :In 4the more simple crystal systems, the body centered cubic and the face centered cubic, the direction of preferred orientation, (100) in each case, is generally the same regardless of the metal involved. In systems of non-cubic symmetry the particular metal or alloy will determine the direction. In closed packed hexagonal systems, f-or example, the c/a ratio is an important factor in determining the direction of preferred orientation.
The solidiiication -of alloys proceeds along the lines mentioned prev-iously, but in a somewhat more complex mechanism since concentration gradients as well as thermal gradients may exist during solidication.
Casting variables affect columnar structure through their influence on the thermal or compositional gradients developed in the molds. These variables include metal superheat, initial mold temperatures, the use of chills or exotherrnie materials, and the alloy composition. Variation of the thermal gradients within the range of columnear formation also inliuences the structure of the casting. lf la steep thermal gradient exists, the rapid rate of heat extraction requires rapid solidication. At the same time the relatively short supercooled layer restricts the lengths of the dendrites extending into the melts. During solidiiication mass transport of solute between the dendrites must take place. Since the overall solidication rate is determined by the rate of heat removal, the diffusion distances must be reduced to permit the proper distribution of solute to take place. This is accomplished by increasing the number of dendrites, thus reducing the interdendritic distances. It has been experimentally veried that as the solidication rate increases, the interdendritic spacing -decreases at a rate proportion-al to the square root of the solidiiication rates.
The consequences of this behavior are evident in eX- tended columnar structures. As the distance from the mold wall increases, the dendritic spacing also increases. This can probably be attributed partially to the elimination of unfavorably oriented dendrites, but the major iniuence responsible is the decrease in thermal gradients as the dendrite-melt interface moves through the mold.
Comparative tests between equiaxed and columnar castings indicate that the columnar casting has marked advantages for certain applications. The high 'temperature strength and ductility of the columnar structures is generally superior to the equiaxed structure, and may be attributed to the preferential occurrence of gas porosity at grain boundary locations. In the equiaxed structures the gas porosity is distributed randomly, following a grain boundary pattern. As a result, intengranular fractures occurred wi-th very low ductility. In the columnar structure the grain boundaries are oriented parallel to the growth direction. Accordingly, the porosity has little or no influence on ductility. The improvement in d-uctility can be attributed 4to several factors. The segregation normally associated with equ'iaxed grains is reduced by the columnar solidifi'cation process. The conditions necessary to lform columnar structures are identical to those required for proper feeding. Thus, microshrinkage is almost completely eliminated. The primary reason for improved ductility, however, appears -to be the elimination of grain boundaries perpendicular to the stress axis. This prevents the normally brittle intergranular type of ifracture, permitting a greater amount of deformation to occur prior to failure,
While the desirability of producing columnar structures for certain applications has been recognized by workers in the art, the problems of achieving such structures have always been substantial. One technique which has been used to produce columnar structures involves the use of a tapered, relatively thick mold with a heat abstracting means positioned at the bottom of the mold. The high temperature differentials existing in the mold structure, however, have caused severe cracking problems to exist. In some instances where relatively thin walled ceramic shell molds were employed, the molds were constrained against movement, inhibiting their free expansion, and presentingA the problems of cracked molds and the introduction iof inclusions. The need still remains, therefore, for a method and apparatus for conveniently producing columnar structures in castings. The satisfaction of that need is the principal object of the present invention.
Another object of the invention is to provide a method for establishing undirectional thermal gradients in a casting so that the gradients exist parallel tio the direction of major stress which will exist in the casting during use.
Still another object of the invention is to provide an apparatus for producing castings having columnar grain structures which permits free expansion of `the 4shell molds contained therein.
Another object of the invention is to provide an apparatus for producing columnar grain type castings which enables one to control the location and intensity of the unidirectional thermal gradients existing therein.
In accordance with the present invention, a unidirectional thermal gradient is provided in the casting by positioning a ceramic shell mold having uniformly thin Wall thicknesses vwithin the furnace, while permitting free expansion of the shell mold therein. A highly heat conductive material is applied to the mold perpendicular to the direction in which the unidirectional thermal gardient is to exist. Then, radiant heat energy is directed at the mold to preheat the por-tions of the mold above the melting temperature of the metal to be introduced, followed by pouring the moltent metal into the mold and cooling the metal within the mold to produce a casting having an oriented columnar grain structure alonig the line of the thermal gradient.
A further description of the present invention will be made in conjunction with the attached sheet of drawings in which the single ligure illustrates an apparatus which can be employed for the lpurposes of this invention.
In the figure, reference numeral indicates generally a furnace assembly for the purposes of the present invention including an outer wall 11 composed of a suitable refractory brick material or the like, and an inner radiating enclosure 12 composed of a material such as graphite. Disposed intermediate the outer wall 11 and the radiating wall 12 is a layer 13 of an insulating refractory material. The radiating Wall 12 is heated to a high temperature by any suitable means, such as induction coils 14, although other heat sources such as electrical resistance heating, gas, or the like, could also be employed.
The outer Wall 11 rests upon a support 16 and on this support there is disposed a block 17 of highly thermally conductive material, such as copper. If desired, additional heat transfer means may be included within the copper block, such as a circulating fluid system.
A ceramic shell mold 18 of generally uniform thin wall structure rests on the block 17. Generally, the mold 18 will have a thickness of from about /m inch to about 1A inch or so. The mold 18 includes an open ended casting cavity portion 19 and .an open ended riser lcavity portion 21 into which the molten metal is introduced. A top heat shield 22 having a central aperture 23 is disposed over the furnace assembly to prevent heat loss from the top of the mold.
A pair of radiation shields 24 and 26 is interposed between the mold 1S and the radiating walls of the heat radiator 112. In the form of the invention illustrated, the shield-s 24- and 26 may take the form of cylindrical bodies which are concentric with the casting cavity 19. The shields may be composed of zirconium silicate or other refractory material which is capable of resisting the high temperatures involved in such furnaces. The purpose of the shields is to control the temperature of various zones Within the casting cavity, as desired, since in some instances it is necessary to provide areas of differing thermal gradients within the same casting. The location and the extent of the shields 24 and 26 determines the amount of heat radiation energy which the casting cavity can assimilate from the radiating walls and thereby determines the temperature in preselected areas or zones of the mold.
Also includ-ed within the furnace is a relatively loosely packed bed 2S of ceramic particles composed, for example, yof zirconium silicate yor other material which has a sintering temperature in excess of the operating temperature of the furnace. The bed is sufficiently loosely packed, however, so that it permits relatively free expansion of the ceramic shell mold in that area.
As an example of the technique involved in the present invention, a first stage jet engine turbine blade was cast in an apparatus of the type shown in the drawing. The graphite radiation source was heated by induction to 2800 F. and held for 20 minutes. A nickel base superalloy havin-g an analysis in the range of l5 to 25% chromium, 5 to 30% cobalt, 0.5 to 5% titanium, 2 to 5% aluminum, 1 to 5% niobium, 5 to 11% tungsten, and the balance essentially nickel was poured into the mold at a pouring temperature of 2700 F. and allowed to cool for 25 minutes. The graphite source was then allowed to cool slowly and reached the melting temperature of `the alloy about 55 minutes after the orignal pour was made. The insulation around the base was granular magnesia and the conducting heat sink under the insulation was pure copper. This assembly produced an entirely columnar jet engine blade which had its grain parallel to the axis of major stress.
From the foregoing, it will be seen that the method and apparatus of the present invention provide a carefully controllable means for securing preferred grain orientation in ca-stings, and the production of columnar structures in which the grains are oriented in the direction of maximum stress.
I claim as my invention:
1. The method of providing a casting of controlled directional orientation of grain structure which comprises positioning a thin walled ceramic mold in a furnace in spaced relation to the radiating walls thereof, closing off a portion of said mold with a metal chill, radiantly heating said furnace to a pouring temperature appropriate to the molten metal to be cast into said mold, shielding iother portions of said mold selectively against radiated heat in said furnace to thereby cooperate with and augment the chilling effect of said chill to provide a desired thermal gradient between said other portions and the por-tion in which said chill is located, said thermal gradient being capable of influencing solidification of said molten =metal to produce a desired controlled directional orientation of grain structure in the solidifying metal, casting molten metal in-to said mold while such thermal gradient exists therein, solidifying the cast metal in the mold under the influence of said temperature gradient, and recovering la casting of said structure.
2. The method of claim 1 in which the metal chill is positioned to provi-de a thermal gradient parallel to the direction of major stress which will exist in the casting during use.
3. The method of claim 1 in which the thermal gradient and cooling conditions are such as to produce -a columnar grain structure in the casting.
4. The method of claim 1 in which t-he radiant heating is 'provided by induction heating.
References Cited by the Examiner UNITED STATES PATENTS 5 Loomis et al. 22-74 Mackenzie 22-74 Roth 22-74 Snoek et a1 22-213 XR 10 Kroll 22-200 9/1955 Georgen 22-193 XR 1/1957 Andrews 22-193 11/ 1960 Operhall et a1 22-196 1/1964 Linstedt 22-58 10/1964 Holmes 22-192 FOREIGN PATENTS 4/ 1951 Great Britain.
I. SPENCER OVERHOLSER, Primary Examiner.
V. K. RISING, Assistant Examiner.

Claims (1)

1. THE METHOD OF PROVIDING A CASTING OF CONTROLLED DIRECTIONAL ORIENTATION OF GRAIN STRUCTURE WHICH COMPRISES POSITIONING A THIN WALLED CERAMIC MOLD IN A FURNACE IN SPACED RELATION TO THE RADIATING WALLS THEREOF, CLOSING OFF A PORTION OF SAID MOLD WITH A METAL CHILL, RADIANTLY HEATING SAID FURNACE TO A POURING TEMPERATURE APPROPRIATE TO THE MOLTEN METAL TO BE CAST INTO SAID MOLD, SHIELDING OTHER PORTIONS OF SAID MOLD SELECTIVELY AGAINST RADIATED HEAT IN SAID FURNACE TO THEREBY COOPERATE WITH AND AUGMENT THE CHILLING EFFECT OF SAID CHILL TO PROVIDE A DESIRED THERMAL GRADIENT BETWEEN SAID OTHR PORTIONS AND THE
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Cited By (16)

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US3376915A (en) * 1964-10-21 1968-04-09 Trw Inc Method for casting high temperature alloys to achieve controlled grain structure and orientation
US3381742A (en) * 1967-06-23 1968-05-07 North American Rockwell Metal casting and solidification
US3485291A (en) * 1968-06-07 1969-12-23 United Aircraft Corp Method of casting by directional solidification
US3494709A (en) * 1965-05-27 1970-02-10 United Aircraft Corp Single crystal metallic part
US3519063A (en) * 1968-07-18 1970-07-07 United Aircraft Corp Shell mold construction with chill plate having uniform roughness
US3620288A (en) * 1969-06-27 1971-11-16 United Aircraft Corp Directionally solidified castings
US3680625A (en) * 1970-11-12 1972-08-01 Trw Inc Heat reflector
US3915761A (en) * 1971-09-15 1975-10-28 United Technologies Corp Unidirectionally solidified alloy articles
US3942581A (en) * 1974-11-29 1976-03-09 General Electric Company Method and apparatus for casting directionally solidified articles
US4168182A (en) * 1975-11-11 1979-09-18 Motoren- Und Turbinen-Union Munchen Gmbh Method of producing shaped metallic parts
DE3327934A1 (en) * 1982-08-05 1984-02-09 Howmet Turbine Components Corp., 06830 Greenwich, Conn. METHOD AND DEVICE FOR PRODUCING AN OBJECT WITH A SPECIFIED CRYSTALLINE ORIENTATION
EP0127552A1 (en) * 1983-04-27 1984-12-05 Howmet Turbine Components Corporation Casting of articles with predetermined crystalline orientation
US4813470A (en) * 1987-11-05 1989-03-21 Allied-Signal Inc. Casting turbine components with integral airfoils
US6568456B1 (en) 1999-08-11 2003-05-27 Alstom Method for manufacture of a directionally solidified columnar grained article
US20170136535A1 (en) * 2014-06-25 2017-05-18 Halliburton Energy Services, Inc. Insulation enclosure incorporating rigid insulation materials
WO2020106372A3 (en) * 2018-10-05 2020-07-23 General Electric Company Controlled grain microstructures in cast alloys

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US4168182A (en) * 1975-11-11 1979-09-18 Motoren- Und Turbinen-Union Munchen Gmbh Method of producing shaped metallic parts
US4580613A (en) * 1982-08-05 1986-04-08 Howmet Turbine Components Corporation Method and mold for casting articles having a predetermined crystalline orientation
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US7225857B2 (en) 1999-08-11 2007-06-05 Alstom Apparatus for manufacture of directionally solidified columnar grained article thereof
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US20050028959A1 (en) * 1999-08-11 2005-02-10 Asea Brown Boveri Ag Apparatus for manufacture of directionally solidified columnar grained article thereof
US6568456B1 (en) 1999-08-11 2003-05-27 Alstom Method for manufacture of a directionally solidified columnar grained article
US7250088B2 (en) 1999-08-11 2007-07-31 Alstom Directionally solidified columnar grained article and apparatus for manufacture thereof
US20170136535A1 (en) * 2014-06-25 2017-05-18 Halliburton Energy Services, Inc. Insulation enclosure incorporating rigid insulation materials
US10195662B2 (en) * 2014-06-25 2019-02-05 Halliburton Energy Services, Inc. Insulation enclosure incorporating rigid insulation materials
WO2020106372A3 (en) * 2018-10-05 2020-07-23 General Electric Company Controlled grain microstructures in cast alloys
CN113165054A (en) * 2018-10-05 2021-07-23 通用电气公司 Controlled grain microstructure in cast alloys
US11597005B2 (en) 2018-10-05 2023-03-07 General Electric Company Controlled grain microstructures in cast alloys
CN113165054B (en) * 2018-10-05 2024-05-28 通用电气公司 Controlled grain microstructure in casting alloys

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DE1483656B1 (en) 1970-07-30

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