EP2337645A2 - Procédé pour produire un moule servant à couler une masse en fusion hautement réactive - Google Patents

Procédé pour produire un moule servant à couler une masse en fusion hautement réactive

Info

Publication number
EP2337645A2
EP2337645A2 EP09783352A EP09783352A EP2337645A2 EP 2337645 A2 EP2337645 A2 EP 2337645A2 EP 09783352 A EP09783352 A EP 09783352A EP 09783352 A EP09783352 A EP 09783352A EP 2337645 A2 EP2337645 A2 EP 2337645A2
Authority
EP
European Patent Office
Prior art keywords
layer
dry mass
hydraulic binder
powder
casting
Prior art date
Legal status (The legal status 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 status listed.)
Granted
Application number
EP09783352A
Other languages
German (de)
English (en)
Other versions
EP2337645B1 (fr
Inventor
Manfred Renkel
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
G4T GmbH
Original Assignee
G4T 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 G4T GmbH filed Critical G4T GmbH
Publication of EP2337645A2 publication Critical patent/EP2337645A2/fr
Application granted granted Critical
Publication of EP2337645B1 publication Critical patent/EP2337645B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22C—FOUNDRY MOULDING
    • B22C9/00—Moulds or cores; Moulding processes
    • B22C9/02—Sand moulds or like moulds for shaped castings
    • B22C9/04—Use of lost patterns
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22C—FOUNDRY MOULDING
    • B22C1/00—Compositions of refractory mould or core materials; Grain structures thereof; Chemical or physical features in the formation or manufacture of moulds
    • B22C1/02—Compositions of refractory mould or core materials; Grain structures thereof; Chemical or physical features in the formation or manufacture of moulds characterised by additives for special purposes, e.g. indicators, breakdown additives
    • B22C1/04—Compositions of refractory mould or core materials; Grain structures thereof; Chemical or physical features in the formation or manufacture of moulds characterised by additives for special purposes, e.g. indicators, breakdown additives for protection of the casting, e.g. against decarbonisation
    • B22C1/06—Compositions of refractory mould or core materials; Grain structures thereof; Chemical or physical features in the formation or manufacture of moulds characterised by additives for special purposes, e.g. indicators, breakdown additives for protection of the casting, e.g. against decarbonisation for casting extremely oxidisable metals
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22C—FOUNDRY MOULDING
    • B22C3/00—Selection of compositions for coating the surfaces of moulds, cores, or patterns

Definitions

  • the invention relates to a method for producing a casting mold for casting highly reactive melts, in particular for casting titanium, titanium alloys or intermetallic titanium aluminides, according to the preamble of claim 1.
  • a slip for producing a contact layer or face-coat layer contains yttrium oxide, magnesium oxide and calcium oxide.
  • the magnesium oxide causes together with the water of the slurry an exothermic reaction in which water evaporates and the drying time of the contact layer produced from the slip is reduced.
  • About the amount or the proportions of the oxides used from this document is not known.
  • the object of the present invention is to eliminate the disadvantages of the prior art.
  • a method for producing a casting mold for casting highly reactive melts is to be specified, which is as simple as possible, reproducible and quick to carry out.
  • a first dry mass for the preparation of the first slip at least 75 wt.% Y 2 O 3 and contains as further solid component at least 1.0 to 25 wt.% Of a hydraulic binder.
  • a "hydraulic binder” is understood as meaning a substance mixture which hydrates with water. The hydration products formed in this way lead to solidification of the solid constituents contained in the first slip.
  • the proposed composition a particularly rapid solidification of the first slurry can be achieved.
  • the first dry mass contains less than 95% by weight of Y 2 O 3, preferably less than 90% by weight. It has surprisingly been found that the relatively expensive constituent Y 2 O 3 required for stability against corrosive attack by highly reactive melts can be reduced by the addition of a hydraulic binder without the resistance of the contact layer to the corrosive action being highly reactive Melting is reduced.
  • the content of Y 2 O 3 in the first dry mass can be reduced, for example, to 80 or 85% by weight. Part of the Y 2 O 3 , for example 5 to 10 wt.%, Can be replaced by TiO 2 .
  • the content of the hydraulic binder is advantageously between 8 and 16% by weight.
  • the first slip can be applied to the mold core in a spraying process.
  • the grain band of the first powder is between 0 to 50 microns and advantageously has a mean grain size (d 50 ) in the range of 8 to 20 microns. It has been shown that a slurry with the proposed particle size distribution on the one hand can be processed particularly well in the spray process and, on the other hand, that a high surface quality of the contact layer can be achieved.
  • the second Y 2 O 3 powder may have a mean grain size (d 50 ) in the range of 130 to 200 microns.
  • the proposed mean grain size of the second Y 2 O 3 powder contributes to a good flowability and thus facilitates the Besanden the contact layer.
  • the hydraulic binder preferably contains CaO * Al 2 O 3 .
  • Such a calcium aluminate cement expediently contains 60 to 80% by weight of Al 2 O 3 , preferably about 70% by weight of Al 2 O 3 .
  • a contact layer made using the proposed hydraulic binder has excellent strength.
  • the first dry mass expediently contains only unavoidable impurities of MgO. Thus, a particularly good resistance to highly reactive melts, in particular titanium aluminide melts, can be achieved.
  • a cladding layer surrounding the layer sequence of contact and first sanding layer or the plurality of layer sequences is produced.
  • the cladding layer may contain MgO as an essential ingredient.
  • a second dry mass for producing the cladding layer may further contain a hydraulic binder, preferably calcium aluminate cement.
  • a hydraulic binder preferably calcium aluminate cement.
  • a second dry mass contains expediently at least 40 wt.% MgO, preferably 60 to 80 wt.%, And at least 20 wt.% Of the hydraulic binder.
  • the second dry mass may contain one or more of the following oxides: Fe 2 O 3 , SiO 2 , CaO, Al 2 O 3 .
  • the cladding layer essentially serves to mechanically stabilize the contact layer. It can have a considerably greater layer thickness than the contact layer.
  • the intermediate layer can be produced by a second slurry applied by spraying or dipping.
  • the second slip may contain as an essential solid constituent a first MgO powder.
  • the second slurry may be a hydraulic binder, preferably a calcium aluminate cement (CaO * Al 2 O 3 ) containing 60 to 80 weight percent Al 2 O 3 , preferably about 70 weight percent Al 2 O 3 .
  • a third dry mass for producing the second slip may contain at least 50 wt% MgO, preferably 60 to 70 wt%, and at least 20 wt% of the hydraulic binder.
  • the second sanding layer is expediently produced by applying a second MgO powder to the second slip layer.
  • a plurality of such interlayer sequences each of which is formed from the intermediate layer and the second sanding layer, can be applied one after the other to the layer sequence of the contact and first sanding layers.
  • the first MgO powder may have a smaller average grain size than the second MgO powder.
  • the first and / or the third dry mass (s) and / or the coating layer (s) may additionally contain at least one of the following oxides include: CeO 2 , La 2 O 3 , Gd 2 O 3 , Nd 2 O 3 , TiO 2 .
  • the addition of other rare earth oxides is also possible.
  • the interlayer sequence thus produced contributes to improved thermal shock resistance of the mold. Since the intermediate layers also contain a hydraulic binder, they too can be produced quickly and efficiently, in particular by spraying. In this case, a moisture content of the contact and / or the intermediate layer can be reduced to a predetermined value after its application by means of infrared radiation.
  • the predetermined value can be in the range from 10 to 60% residual moisture, preferably less than 20% and more than 5% residual moisture.
  • the proportion of the hydraulic binder in the first dry mass is smaller than in the second or third dry mass.
  • the proportion of the hydraulic binder in the second and / or third dry mass is advantageously at least 2% by weight, preferably at least 5% by weight, higher than in the first dry mass.
  • first and / or second slip have a viscosity of at most 1000 mPas, preferably between 450 and 750 mPas. Slips with such a viscosity can be processed particularly well by spraying.
  • the mandrel is removed by melting or burning out the material forming the mandrel.
  • the material is suitably wise to wax or the like.
  • a formed after removal of the mandrel green body is suitably sintered at a sintering temperature of more than 800 0 C and less than 1200 0 C.
  • the use according to the invention of a hydraulic binder for the production of the casting mold thus also contributes to a considerable reduction of the sintering temperatures.
  • a contact layer 1 contains, for example, 85% by weight of Y 2 O 3 and 15% by weight of hydration products of the calcium aluminate cement. It is expediently free of MgO, apart from unavoidable impurities.
  • the reference numeral 2 designates a first sanding layer, which consists essentially of a further Y 2 O 3 powder having an average particle size of about 150 ⁇ m. The first sanding layer 2 is expediently free of MgO, apart from unavoidable impurities.
  • the contact layer 1 and the first sanding layer 2 form a layer sequence A.
  • an intermediate layer 3 which contains as an essential ingredient MgO, which in turn is bonded to the reaction product of a Calciumaluminatzements.
  • the reference numeral 4 designates a second sanding layer, which is made of a MgO powder.
  • An intermediate layer sequence formed alternately from the intermediate layer 3 and the second sanding layer 4 is designated by the reference B.
  • the interlayer sequence B is backfilled with a cladding layer 5, which as an essential solid component MgO contains, which in turn is bound by means of a hydraulic binder, preferably calcium aluminate cement.
  • the layer sequence A can-like the interlayer sequence B-also be formed from a sequence of several alternately successive contact layers 1 and first sanding layers 2.
  • a first slip is first prepared, the first dry mass of which contains 80 to 90% by weight of a first Y 2 O 3 powder.
  • the average grain size d 50 of the first Y 2 O 3 powder is suitably 10 to 15 microns.
  • the mode is advantageously 15 to 25 microns.
  • the grain band is suitably in the range between 0 to 50 microns.
  • the first dry matter contains 10 to 20 wt.%, Preferably 8 to 17 wt.%, Of a Calciumaluminatze- management.
  • a first slurry having a viscosity in the range from 400 to 700 mPas is produced.
  • the first slip is sprayed onto a, for example made of wax, mold core by spraying.
  • the contact layer 1 produced from the first slurry is sanded with a first boundary layer 2.
  • the first Besandungs Mrs 2 consists of a second Y 2 O 3 powder, which has a mean grain size in the range of 170 to 200 microns and expediently contains only unavoidable impurities.
  • the layer sequence A thus prepared is then dried for a time of about 90 to 180 minutes or a suitable residual moisture content of 10 to 30% is set.
  • the aforesaid process of producing the contact layer 1 and the first sanding layer 2 can be repeated several times, for example three to five times.
  • the Layer sequence A can also be terminated by a contact layer 1 instead of the first sanding layer 2. It may also be the case that a first sanding layer terminating the layer sequence A is essentially produced from a MgO powder.
  • This MgO powder can be designed in terms of its particle size distribution and its average particle size corresponding to the second Y 2 O 3 powder.
  • a second slip is produced.
  • a second dry mass for producing the second slip contains, for example, 65 to 80% by weight, preferably 65 to 70% by weight, MgO and 20 to 35% by weight, preferably 30 to 35% by weight, of a calcium aluminate cement.
  • a second slip is produced whose viscosity is expediently adjusted so that a coating in the conventional dipping process is possible.
  • the layer sequence A applied to the mold core is coated with the second slip in the dipping process.
  • the second sanding layer 4 is applied, which is formed essentially of a MgO powder having a particle size in the range of 0.1 to 2.0 mm.
  • the intermediate layer sequence B thus formed is dried for a period of 15 to 45 minutes or a suitable residual moisture of 10 to 30% is set. Subsequently, further intermediate and second sanding layers 4 can be applied in the same way. The interlayer sequence B can be finally dried for a period of 30 to 100 minutes.
  • the cladding layer 5 is from 60 to 80 wt.%, Preferably 70 to 80 wt.%, MgO, 20 to 40 wt.%, Preferably 20 to 30 wt.%, Calciumaluminatzement and water and Excipients made a still flowable mass.
  • the coated mandrel is then placed in a mold and surrounded with the flowable mass. After drying the flowable mass, the mold is removed. The mandrel is removed by increasing the temperature. Subsequently, the green compact of the casting mold thus produced is sintered at a temperature in the range from 1000 to 1200 ° C., preferably in the range between 1100 and 1200 ° C.
  • a first dry mass for the preparation of the first slurry contains in this case 60 to 70 wt.% Y 2 O 3 and 10 to 20 wt.% CeO 2 , the grain size of the mixture is between 0 to 50 microns. Furthermore, the first dry mass contains 10 to 20 wt.% Of Calciumaluminatzements.
  • the first dry mass is mixed with water to form a first slurry having a viscosity in the range of 300 to 600 mPas.
  • the drying of the layer sequence A and the interlayer sequence B can also be supported by means of infrared radiation.
  • the coated mandrel can be passed through a drying chamber in which an air temperature in the range of 30 to 60 0 C prevails.
  • the first and / or second slip can also contain conventional excipients, in particular the organic auxiliaries, in customary amounts in addition to the abovementioned constituents.

Landscapes

  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Chemical & Material Sciences (AREA)
  • Materials Engineering (AREA)
  • Molds, Cores, And Manufacturing Methods Thereof (AREA)
  • Mold Materials And Core Materials (AREA)
  • Continuous Casting (AREA)

Abstract

L'invention concerne un procédé pour produire un moule servant à couler des masses en fusion hautement réactives, en particulier à couler du titane, des alliages de titane ou des aluminides de titane intermétalliques. Ce procédé comprend les étapes qui consistent : à produire une feuille de contact (1) par application d'une première barbotine contenant une première poudre de Y2O3 en tant que premier composant sensiblement solide sur un noyau; à sabler la couche de contact (1) formée à partir de ladite première barbotine au moyen d'une deuxième poudre Y2O3 contenant du Y2O3 en tant que composant essentiel. L'objectif de cette invention est de rendre ce procédé particulièrement efficace. A cet effet, une première masse sèche destinée à produire la première barbotine contient au moins 75 % en poids de Y2O3, et au moins entre 1,0 et 25 % en poids d'un liant hydraulique en tant que composant solide supplémentaire.
EP09783352.9A 2008-09-25 2009-09-24 Procédé pour produire un moule servant à couler une masse en fusion hautement réactive Active EP2337645B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102008042376A DE102008042376A1 (de) 2008-09-25 2008-09-25 Verfahren zur Herstellung einer Gussform zum Vergießen hochreaktiver Schmelzen
PCT/EP2009/062355 WO2010034762A2 (fr) 2008-09-25 2009-09-24 Procédé pour produire un moule servant à couler une masse en fusion hautement réactive

Publications (2)

Publication Number Publication Date
EP2337645A2 true EP2337645A2 (fr) 2011-06-29
EP2337645B1 EP2337645B1 (fr) 2020-04-22

Family

ID=41794726

Family Applications (1)

Application Number Title Priority Date Filing Date
EP09783352.9A Active EP2337645B1 (fr) 2008-09-25 2009-09-24 Procédé pour produire un moule servant à couler une masse en fusion hautement réactive

Country Status (5)

Country Link
US (1) US20110203760A1 (fr)
EP (1) EP2337645B1 (fr)
JP (1) JP2012503552A (fr)
DE (1) DE102008042376A1 (fr)
WO (1) WO2010034762A2 (fr)

Families Citing this family (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US8579013B2 (en) * 2011-09-30 2013-11-12 General Electric Company Casting mold composition with improved detectability for inclusions and method of casting
US9192983B2 (en) * 2013-11-26 2015-11-24 General Electric Company Silicon carbide-containing mold and facecoat compositions and methods for casting titanium and titanium aluminide alloys
DE102016124322A1 (de) 2016-12-14 2018-06-14 Manfred Renkel Verfahren zur Herstellung einer Gussform zum Vergießen einer hochreaktiven Schmelze
DE102016124321A1 (de) 2016-12-14 2018-03-01 Manfred Renkel Verfahren zur Herstellung einer Gussform zum Vergießen einer hochreaktiven Schmelze
EP3560627B1 (fr) * 2018-04-24 2022-06-08 Ceranovis GmbH Procédé de travail d'aluminium fondu ou d'alliage d'aluminium fondu
CN109063322B (zh) * 2018-07-27 2022-08-02 哈尔滨理工大学 一种铸件缩松缺陷数值预测的方法
DE102020108196B4 (de) 2020-03-25 2024-05-16 Technische Universität Bergakademie Freiberg Verfahren zur Herstellung einer keramischen, silikatfreien Feingussform für die Herstellung von Feingussteilen aus höherschmelzenden Metallen und Verwendung einer keramischen, silikatfreien Feingussform für die Herstellung von Feingussteilen aus höherschmelzenden Metallen

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Publication number Priority date Publication date Assignee Title
US3994346A (en) * 1972-11-24 1976-11-30 Rem Metals Corporation Investment shell mold, for use in casting of reacting and refractory metals
US4057433A (en) 1974-03-05 1977-11-08 Rem Metals Corporation Oxyfluoride-type mold for casting molten reactive and refractory metals
DE3272840D1 (en) 1982-05-04 1986-10-02 Remet Corp Refractory material
JPS6012246A (ja) * 1983-07-01 1985-01-22 Agency Of Ind Science & Technol 超合金の一方向性凝固鋳造用インベストメントシエル鋳型の製造法
US4703806A (en) * 1986-07-11 1987-11-03 Howmet Turbine Components Corporation Ceramic shell mold facecoat and core coating systems for investment casting of reactive metals
US5535811A (en) * 1987-01-28 1996-07-16 Remet Corporation Ceramic shell compositions for casting of reactive metals
GB9601910D0 (en) * 1996-01-31 1996-04-03 Rolls Royce Plc A method of investment casting and a method of making an investment casting mould
DE10346953A1 (de) 2003-10-09 2005-05-04 Mtu Aero Engines Gmbh Werkzeug zum Herstellen von Gussbauteilen, Verfahren zum Herstellen des Werkzeugs und Verfahren zum Herstellen von Gussbauteilen
US7128129B2 (en) * 2003-10-30 2006-10-31 Wisys Technology Foundation, Inc. Investment casting slurry composition and method of use
DE102004048451A1 (de) * 2004-10-05 2006-04-06 Mk Technology Gmbh Verfahren und System zum Herstellen einer Schalenform insbesondere für das Feingießen

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Also Published As

Publication number Publication date
WO2010034762A2 (fr) 2010-04-01
WO2010034762A3 (fr) 2010-08-19
DE102008042376A1 (de) 2010-04-08
JP2012503552A (ja) 2012-02-09
US20110203760A1 (en) 2011-08-25
EP2337645B1 (fr) 2020-04-22

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