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WO1998005450A1 - Procede et dispositif pour solidifier de façon orientee une matiere fondue - Google Patents

Procede et dispositif pour solidifier de façon orientee une matiere fondue Download PDF

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Publication number
WO1998005450A1
WO1998005450A1 PCT/EP1997/004148 EP9704148W WO9805450A1 WO 1998005450 A1 WO1998005450 A1 WO 1998005450A1 EP 9704148 W EP9704148 W EP 9704148W WO 9805450 A1 WO9805450 A1 WO 9805450A1
Authority
WO
WIPO (PCT)
Prior art keywords
melt
plate
germination
casting mold
base plate
Prior art date
Application number
PCT/EP1997/004148
Other languages
German (de)
English (en)
Inventor
Winfried Esser
Robert Singer
Peter Krug
Jürgen PREUHS
Gerhard Grötzschel
Original Assignee
Siemens Aktiengesellschaft
Tfb Feingusswerk Bochum Gmbh
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Siemens Aktiengesellschaft, Tfb Feingusswerk Bochum Gmbh filed Critical Siemens Aktiengesellschaft
Publication of WO1998005450A1 publication Critical patent/WO1998005450A1/fr

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Classifications

    • 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
    • C30B29/10—Inorganic compounds or compositions
    • C30B29/52—Alloys

Definitions

  • the invention relates to a method for the directional solidification of a melt of an alloy containing a base metal in a casting mold, the casting mold filled with the melt being introduced into a cooling bath to solidify the melt.
  • the invention relates to a device for the directional solidification of a melt of an alloy containing a base metal, comprising a casting mold and a cooling bath, into which the casting mold can be inserted to solidify the melt after it has been filled with the melt.
  • This document also provides information on the further design of such a method and such a device, these notes serving in particular to use the method or the device to form a component for a stationary gas turbine, the gas turbine having a power output of 100 MW or has more to be able to pour. It is desirable, by directional solidification
  • this directed structure can be a columnar crystalline structure, i.e. a coherent bundle with a large number of elongated, columnar crystallites, or a single crystalline structure, i.e. a structure consisting essentially of a single crystal.
  • Nickel-based and cobalt-based superalloys are particularly suitable as materials for such a component; Examples include the superalloys known in the technical field with the common designations
  • a superalloy usually has a multi-phase existing, complex structure. This means that the term "single-crystal" in the present context may have to be given a weaker meaning than the meaning familiar from the chemistry of ion crystals. Appropriate knowledge is common in the relevant technical field.
  • the method and the device are suitable for producing parts that do not exceed certain geometric dimensions.
  • a casting mold which was considered as an aid for the directional solidification of a melt, consists of a base plate and a shell, the shell standing on the base plate and the base plate a lower opening of the
  • the shell closes and the shell is ceramic and the base plate is metallic.
  • the base plate in which the directional solidification of the melt is to be accomplished, so that the melt is cooled immediately when it touches the base plate. This creates crystallization nuclei in the melt, from which the melt solidifies.
  • the directional solidification of the melt presupposes that crystallites first form in the region of the base plate, from which the solidification of the melt can continue in one direction against gravity.
  • the mold with the melt is gradually immersed in the cooling bath.
  • the cooling bath quickly dissipates the heat from the mold and the melt, so that a zone with a sharp temperature gradient forms in the melt, which migrates through the melt against gravity as the mold is immersed in the cooling bath.
  • the initial formation of crystallites in the melt on the base plate has so far been statistical.
  • the use of a casting mold of the type described is also common in ordinary investment foundry, in which no special measure for the directional solidification of a melt is used.
  • the base plate consists in particular of copper or a copper alloy and is cooled with water for heat dissipation.
  • the base plate is made of metal, which can be of interest in terms of increased heat dissipation through this base plate, it may be expected that there will be an .alloying of the melt to the base plate. Chemical elements can be exchanged between the melt and the base plate and both the composition of the melt and the composition of the base plate can be changed significantly. This leads on the one hand to undesired wear of the base plate and on the other hand to Necessity to have to cut off a part of the casting made from the melt, which was located near the base plate.
  • DE 29 33 761 C2 describes a process for producing directionally solidified castings.
  • a casting mold is used, consisting of a base plate through which coolant flows, on which a ceramic molded part surrounded by insulation material is placed.
  • An intermediate plate is arranged between the ceramic molded part and the base plate through which coolant flows, and is connected in a heat-conducting manner to the base plate.
  • This intermediate plate consists of a material of the same type as the solidifying melt, the only example being a nickel-based alloy IN738 LC for the production of a directionally solidified gas turbine blade.
  • the intermediate plate serves to protect the melt from contamination by the material of the base plate dissolving. To achieve this protective effect, the material of the intermediate plate must inevitably be of the same type, in order not to cause any other contamination of the melt.
  • DE-AS 21 19 041 also describes a method for casting high-temperature alloys in a heated shell shape.
  • the bowl shape sits on a mold plate (a coolable base plate).
  • Contamination for example from ceramic materials of the shell shape or from binders, can deposit on this mold plate and lead to alloying into the melt of the casting. This allows the alloy of
  • a thin, non-flat metallic cover is inserted into the shell shape at the end resting on the mold plate. This cover melts during the casting process and is dissolved in the alloy of the casting.
  • the cover is made of a metal, which is also a component of the alloy of the Is cast. The cover plate therefore only protects the mold plate from precipitation and condensate. A diffusion of alloy components of the mold plate into the alloy of the casting is still possible.
  • the object of the invention is therefore to provide a method of the type mentioned and a device of the type mentioned, with which method or with which device the problems described during solidification of the melt can be avoided and preferably achieves an increased quality of the casting made from the melt - is cash.
  • Melt is inserted into the mold before it is filled with the melt so that a surface can be wetted by the melt, and then the mold is filled with the melt over the sheet and the melt is solidified.
  • the solidification of the melt is based on a specially provided sheet which provides protection against alloying of the melt against a metallic part, in particular a base plate, the casting mold and also provides crystallization nuclei for initiating the directional solidification of the melt.
  • Crystallization nuclei in the melt compared to the density that occurs without using the sheet would.
  • the density of crystallization nuclei can be increased ten to one hundred times by using the sheet, which is very beneficial to the quality of the casting to be produced.
  • the germination plate brings about a targeted structural change in the starting area of the casting and avoids the problems of oxidation that occur when using the same type of material.
  • the alloys which usually have aluminum, titanium, zirconium or hafnium with a high affinity for oxygen, undergo oxidation to avoid expensive process or design Versions must be chosen.
  • a germination plate made of a material that is not of the same type often makes it possible to use an inexpensive material for the germination plate, which avoids the problem of the formation of an oxide skin through the absence of oxygen-affine elements.
  • the germination plate preferably has a high grain density of over 250 grains per mm.
  • the grain density is preferably over 1500 to the order of 2000 grains per mm. This also results in a very high grain density in the starting zone of the directional or single-crystal solidification of the melt, which is particularly favorable for a functioning growth selection and thus a directional solidification.
  • a base plate for example made of a molybdenum alloy or copper, a grain density of clearly becomes apparent in the melt in the starter zone
  • the germination plate has a recrystallization texture with a cube layer.
  • This recrystallization texture can be achieved with materials such as nickel or an iron-nickel alloy with 36% by weight of nickel, but also with a large number of other materials.
  • a germination plate is subjected to a heat treatment with preferably a high degree of deformation of up to over 99%.
  • the heat treatment is carried out at a temperature and time period adapted to the material, which results in a fine grain structure. As a result, very high grain densities can be achieved in the starting area when the melt solidifies.
  • the germination plate Before the melt is poured into the casting mold, the germination plate is preferably subjected to a surface treatment, in particular a chemical surface treatment, as a result of which any scale layers or thin oxide layers are removed. This is done, for example, by electrolytic polishing with a mixture of hydrochloric acid and 10% methanol or with perchloric acid. Degreasing the surface of the germination plate can be carried out with an organic liquid.
  • the sheet preferably consists entirely of the base metal or an alloy which contains the base metal as an essential component. It is quite possible that the sheet is made of a more or less arbitrary material and is only provided with a corresponding layer containing the base metal on the surface to be wetted by the melt.
  • the casting mold used for the method preferably consists of a base plate and a shell, the shell standing on the base plate and the base plate closing a lower opening of the shell, and the base plate of which Cooling bath is cooled while the sheet is being inserted and while the melt is being filled. This ensures that the sheet is cooled in the casting mold and premature melting of the sheet and mixing of the material of the sheet with the melt is avoided.
  • Nickel and cobalt, in particular nickel, are preferred as the base metal for forming the alloy which is to be produced from the melt and as the material for the sheet. Iron is also conceivable as the base metal, although iron is rather uncommon in the current practice of superalloys.
  • the germination plate is an alloy with nickel and iron, e.g. 36% nickel and the rest iron.
  • the melt initially has a temperature between 1250 ° C. and 1600 ° C. For cooling, this melt is preferably cooled to a temperature below 300 ° C. in the cooling bath; this can be achieved by choosing liquid tin as the cooling bath.
  • the melt is preferably solidified before the sheet is completely melted. This ensures that the sheet can fully perform its function of providing nuclei and also provides protection.
  • the melt solidifies in particular to form a directional structure, that is to say a stem-crystalline or single-crystal structure of the type explained above.
  • the melt, mold and sheet be kept under a vacuum with a residual pressure which residual pressure is less than a decomposition pressure of an oxide of the base metal.
  • This configuration is particularly important when the base metal is nickel.
  • Nickel oxide has a decomposition pressure in a temperature range between 1250 ° C and 1600 ° C, which is of particular interest, depending on the temperature between 10 ⁇ 2 Pa and 10 Pa, i.e. in a pressure range in which there is a technical suitable for carrying out the process Vacuum would move.
  • the term "decomposition pressure" is to be understood in such a way that nickel oxide decomposes into the elements, that is to say elemental nickel and elemental oxygen, at an ambient pressure which is less than the decomposition pressure depending on the prevailing temperature.
  • the method is particularly suitable for solidifying a melt of a superalloy.
  • the method is also particularly preferred for producing a component for a gas turbine, in particular a blade or a heat shield element, through the solidification of the melt.
  • a device for the directional solidification of a melt of an alloy containing a base metal comprising a casting mold and a cooling bath, into which the casting mold can be introduced after filling with the melt to solidify the melt, in which
  • a sheet is inserted into the casting mold and has a surface that can be wetted by the melt, which serves for the targeted germination of the melt.
  • the mold in the device preferably consists of a base plate and a shell, the shell being on the base plate and the base plate being a lower opening in the
  • the base plate also preferably consists of a material with high thermal conductivity, in particular a molybdenum alloy, and the shell consists of a ceramic.
  • a molybdenum alloy commonly known as TZM, which contains titanium, zirconium and carbon in addition to molybdenum, is particularly suitable for the base plate.
  • the sheet in the device preferably has a thickness of between 0.3 mm and 2 mm, the thickness of the sheet to be selected based on the circumstances of the individual case.
  • the thickness of the sheet is to be selected in accordance with the temperatures prevailing in the casting mold and in the melt and in consideration of the length of a holding time which may be provided during which the melt is held in the casting mold without solidification. Melting or even completely dissolving the sheet is generally not desirable and should be avoided.
  • the base metal preferably has a structure of many crystallites oriented identically to one another in the sheet and the sheet is inserted into the casting mold in such a way that a crystal axis of the structure is aligned parallel to a longitudinal axis of the casting mold.
  • the sheet has an essentially single-crystal one Structure and is inserted into the mold in such a way that a crystal axis of the structure is aligned parallel to a longitudinal axis of the mold.
  • the base metal is nickel or iron. It is in fact possible to give a sheet made of Nikkei or iron a macroscopically oriented structure by means of a suitable sequence of treatments from hot and / or cold forming steps with possibly subsequent heat treatment (recrystallization annealing). In particular, all the crystallites in the sheet are oriented in a certain crystallographic direction with respect to a normal axis of the sheet. The ⁇ 001) direction can in particular be selected as the crystallographic axis. Other crystallographic directions, for example directions (100) and (110), are also suitable for practical use.
  • a sheet with an essentially single-crystalline structure can be considered.
  • An "essentially single-crystalline" structure should be considered to exist when the sheet comes into contact with a single, correspondingly large crystallite of the melt.
  • the structure that forms when the melt solidifies grows epitaxially on the sheet and thus forms a casting with a macroscopic orientation. If there is only one sheet made of a material that does not sufficiently contain the base metal, the sheet can first be given the desired macroscopically oriented structure, if not already present, and then a layer of the base metal or a suitable alloy can be epitaxially grown on it Sheet are generated.
  • the sheet must then be placed in the mold in such a way that the layer comes into contact with the melt to be poured in. In this way, the crystals required to solidify the melt are Installation germs provided over the layer on the sheet.
  • molten tin is preferred as the cooling bath.
  • Melted tin enables the melt to be cooled very quickly to a temperature below 300 ° C, since tin melts at 232 ° C under normal conditions. This enables a particularly high temperature gradient to be achieved in the melt.
  • the cooling bath is covered by a flowable, ceramic cover layer, through which the casting mold with the melt can be introduced into the cooling bath.
  • a cover layer can effectively isolate the cooling bath from a temperature prevailing on and in the casting mold and / or an oven in which the casting mold is initially held, in order to prevent the cooling bath and / or heating from undesirable
  • 2 shows a turbine blade that can be obtained by directional solidification of a melt
  • 3 shows a heat shield element that can be obtained by directional solidification of a melt
  • FIG. 1 shows a device with which a melt 1 is to be solidified in a casting mold 2, 3.
  • the casting mold 2, 3 consists of a base plate 2 and a shell 3.
  • the base plate 2 is metallic and consists of a molybdenum alloy commonly known as TZM, which, apart from molybdenum, contains parts of tantalum and zirconium. This alloy is suitable to withstand all relevant thermal and mechanical loads.
  • the shell 3 is made of ceramic material and is open at its lower end; an opening 6 at the lower end of the shell 3 is closed by the base plate 2.
  • the mold 2, 3 with the melt 1 is immersed in a cooling bath 4 made of liquid tin.
  • the cooling bath 4 extracts the heat from the melt 1, a strong temperature gradient being formed in the melt 1 when immersed in the cooling bath 4, which temperature gradient along a longitudinal axis 13 of the casting mold 2, 3 migrates upward through the melt 1 while the Mold 2, 3 with the melt 1 increasingly immersed in the cooling bath 4.
  • the melt solidifies in the area of this migratory temperature gradient and thus also moves along the longitudinal axis 13 from bottom to top; therefore the solidification is called "directional" solidification.
  • This sheet 5 fulfills several important functions.
  • the sheet metal 5 ready for crystallization nuclei on its surface to be wetted by the melt 1, from which the solidification of the melt 1 can proceed, possibly with the formation of a structure directed along the longitudinal axis 13.
  • the melt 1 does not come into direct contact with the base plate 2, since, unlike the ceramic shell 3, this could be attacked by the melt 1. In particular, this could result in the melt 1 being alloyed with the base plate 2 and thus in contamination of the melt 1 and wear in the base plate 2.
  • Aluminum may be considered as an alternative for the tin in the cooling bath 4; then the temperature in the cooling bath 4 cannot drop below the melting point of the aluminum at 658 ° C.
  • Other metals or mixtures, each with a sufficiently low melting point, are also possible instead of tin.
  • the cooling bath 4 is covered by a covering layer 9 made of ceramic bulk material, in particular hollow balls or solid balls made of mullite or the like.
  • This ceramic bulk material completely encloses the casting mold immersed in the cooling bath 4 and thus prevents the cooling bath 4 from being exposed directly to an elevated temperature from the surroundings of the casting mold 2, 3.
  • the device according to FIG. 1 is completed by supports 14 for the casting mold 2, 3, which are connected to the base plate 2 in a suitable manner, an oven 15 in which the casting mold 2, 3 is held before it is immersed in the cooling bath 4 and a crucible 16 in which the cooling bath 4 is located.
  • the cover layer 9 In the furnace 15 a temperature is to be expected which is sufficient to keep the melt 1 liquid. This means that there is intense heat radiation in the furnace 15. If you want to keep the cooling bath 4 at a sufficiently low temperature, you have to ensure a very good thermal insulation between the cooling bath 4 and the oven 15. For this, the cover layer 9 has proven to be particularly advantageous, which also emerges from the already mentioned WO 96/05006 AI.
  • FIG. 2 shows a component for a gas turbine that can be produced with the device according to FIG. 1, namely a blade 10.
  • FIG. 2 can be seen as a schematic representation and does not represent a specific product.
  • the blade 10 can be both a moving blade and a guide blade. .
  • the sheet 5, from which the melt from which the blade 10 was formed, has solidified on the blade 10.
  • the sheet 5 consists of crystallites 8, which are all oriented identically, so that certain crystal axes 12 of all crystallites 8 are arranged parallel to one another.
  • a structure 7 directed along a longitudinal axis 13 has formed in the blade 10, the longitudinal axis 13 being approximately parallel to the crystal axes 12.
  • the directed structure 7 can be a columnar crystalline structure; it is also possible to achieve a single-crystal structure by using a single-crystal sheet 5.
  • Figure 3 shows another component for a gas turbine, namely a heat shield element 11, which is also basically pourable with the method and / or in the device presented.
  • Figure 3 is again only to be seen as a symbolic representation; it is not claimed that the heat shield element 11 shown would be a particularly preferred design in any respect.
  • Figures 4 and 5 each show an orientation of the structure with respect to the longitudinal axis of the casting, represented by an angle ⁇ .
  • a frequency of the respective orientations of the crystallites is specified for an angular range between 0 ° and 45 °.
  • This frequency distribution of the alignment is shown in the border area of the solidified melt to the germ plate (FIG. 5) and to a copper base plate without germ plate (FIG. 4). It can be clearly seen that if the melt solidifies directly on the copper base plate, there is essentially an even distribution of the direction of the grains in the angular range between 0 ° and 50 °. On the other hand, when using a germination plate according to the invention, there is a clear alignment of the grains in the direction of the longitudinal axis of the mold.
  • the germination plate therefore has an increased proportion of (001) oro-oriented grains. A significantly improved orientation selection is thus achieved by the germination plate with a corresponding epitaxial growth of the melt.
  • the invention relates to a method and a device for directional solidification of a melt, which are particularly distinguished for the production of a component of a stationary gas turbine or an aircraft engine gas turbine from a nickel-based or cobalt-based superalloy.
  • a large number of crystallization nuclei are provided for the solidification of the melt.
  • the measure required is simple and cheap, and it enables a significant Continuous increase in the quality of the manufactured product In addition, contamination of the melt to be solidified is reliably avoided.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Inorganic Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Turbine Rotor Nozzle Sealing (AREA)

Abstract

L'invention concerne un procédé pour solidifier de façon orientée une matière fondue (1) d'un alliage contenant un métal de base, dans un moule (2, 3), ce dernier, rempli de matière fondue (1), étant introduit dans un bain de refroidissement pour assurer la solidification de la matière fondue (1). Une tôle de germination (5) est introduite dans le moule (2, 3) afin de permettre une germination orientée, avant le remplissage du moule (2, 3), de sorte qu'une surface puisse être imprégnée par la matière fondue (1), puis cette dernière (1) est versée au-dessus de la tôle (5) dans le moule (2, 3) où elle est solidifiée. L'invention concerne également un dispositif adapté à ce procédé.
PCT/EP1997/004148 1996-08-06 1997-07-30 Procede et dispositif pour solidifier de façon orientee une matiere fondue WO1998005450A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE19631767 1996-08-06
DE19631767.3 1996-08-06

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Publication Number Publication Date
WO1998005450A1 true WO1998005450A1 (fr) 1998-02-12

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Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1070561A1 (fr) * 1999-07-19 2001-01-24 General Electric Company Ecran isolateur flottant pour la coulée à solidification directionelle
DE102007014744A1 (de) * 2007-03-28 2008-10-02 Rwth Aachen Form und Verfahren zur gießtechnischen Herstellung eines Gusstücks
US8141769B2 (en) 2005-07-22 2012-03-27 Siemens Aktiengesellschaft Process for repairing a component comprising a directional microstructure by setting a temperature gradient during the laser heat action, and a component produced by such a process
DE102015218408A1 (de) 2015-09-24 2017-03-30 Siemens Aktiengesellschaft Bauteil und/oder Oberfläche aus einem Refraktärmetall oder einer Refraktärmetalllegierung für thermozyklische Belastungen und Herstellungsverfahren dazu
CN112157245A (zh) * 2020-09-03 2021-01-01 中国科学院金属研究所 利用lmc定向凝固技术制备大尺寸定向叶片过程中定向柱晶晶粒控制方法
CN115213361A (zh) * 2022-07-26 2022-10-21 王小川 浇注定向凝固工艺

Citations (7)

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Publication number Priority date Publication date Assignee Title
DE2324376A1 (de) * 1972-05-17 1973-12-06 United Aircraft Corp Gerichtet erstarrte legierungsartikel
US4190094A (en) * 1978-10-25 1980-02-26 United Technologies Corporation Rate controlled directional solidification method
EP0038660A2 (fr) * 1980-04-18 1981-10-28 Trw Inc. Procédé de coulée
EP0059549A2 (fr) * 1981-03-02 1982-09-08 PCC Airfoils, Inc. Procédé de coulée d'un objet
US4412577A (en) * 1982-01-27 1983-11-01 United Technologies Corporation Control of seed melt-back during directional solidification of metals
DE4321640A1 (de) * 1993-06-30 1995-01-12 Leybold Durferrit Gmbh Verfahren zum gerichteten Erstarren einer Metallschmelze und Gießvorrichtung zu seiner Durchführung
WO1996005006A1 (fr) * 1994-08-08 1996-02-22 Siemens Aktiengesellschaft Procede et dispositif permettant une solidification dirigee d'une matiere fondue

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE2324376A1 (de) * 1972-05-17 1973-12-06 United Aircraft Corp Gerichtet erstarrte legierungsartikel
US4190094A (en) * 1978-10-25 1980-02-26 United Technologies Corporation Rate controlled directional solidification method
EP0038660A2 (fr) * 1980-04-18 1981-10-28 Trw Inc. Procédé de coulée
EP0059549A2 (fr) * 1981-03-02 1982-09-08 PCC Airfoils, Inc. Procédé de coulée d'un objet
US4412577A (en) * 1982-01-27 1983-11-01 United Technologies Corporation Control of seed melt-back during directional solidification of metals
DE4321640A1 (de) * 1993-06-30 1995-01-12 Leybold Durferrit Gmbh Verfahren zum gerichteten Erstarren einer Metallschmelze und Gießvorrichtung zu seiner Durchführung
WO1996005006A1 (fr) * 1994-08-08 1996-02-22 Siemens Aktiengesellschaft Procede et dispositif permettant une solidification dirigee d'une matiere fondue

Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1070561A1 (fr) * 1999-07-19 2001-01-24 General Electric Company Ecran isolateur flottant pour la coulée à solidification directionelle
US8141769B2 (en) 2005-07-22 2012-03-27 Siemens Aktiengesellschaft Process for repairing a component comprising a directional microstructure by setting a temperature gradient during the laser heat action, and a component produced by such a process
DE102007014744A1 (de) * 2007-03-28 2008-10-02 Rwth Aachen Form und Verfahren zur gießtechnischen Herstellung eines Gusstücks
DE102015218408A1 (de) 2015-09-24 2017-03-30 Siemens Aktiengesellschaft Bauteil und/oder Oberfläche aus einem Refraktärmetall oder einer Refraktärmetalllegierung für thermozyklische Belastungen und Herstellungsverfahren dazu
CN112157245A (zh) * 2020-09-03 2021-01-01 中国科学院金属研究所 利用lmc定向凝固技术制备大尺寸定向叶片过程中定向柱晶晶粒控制方法
CN112157245B (zh) * 2020-09-03 2022-03-29 中国科学院金属研究所 利用lmc定向凝固技术制备大尺寸定向叶片过程中定向柱晶晶粒控制方法
CN115213361A (zh) * 2022-07-26 2022-10-21 王小川 浇注定向凝固工艺

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