CA1075431A

CA1075431A - Method for fabrication composite shell molds for the production of superalloy castings

Info

Publication number: CA1075431A
Application number: CA248,369A
Authority: CA
Inventors: Bruce E. Terkelsen; James S. Perron; Michael Cybulsky
Original assignee: United Technologies Corp
Current assignee: RTX Corp
Priority date: 1975-03-25
Filing date: 1976-03-16
Publication date: 1980-04-15
Also published as: FR2305255A1; JPS51119616A; GB1546501A; DE2612079C2; DE2612079A1; FR2305255B1

Abstract

ABSTRACT OF THE DISCLOSURE

A method for producing composite ceramic shell molds for investment casting and subsequent directional solidification of nickel and cobalt base superalloys is described. The composite ceramic shell mold is composed of an inner component having an alumina content of at least 80 percent and an average thickness of about ten mills and an outer layer com-posed predominantly of zircon having a thickness of from .1 to .4 inches. The alumina component of the shell mold is wet by the superalloy material and this wetting action is believed to cause the substantial elimination of a surface defect problem know as chain porosity. The zircon component of the shell mold had desirable mechanical properties and my easily be removed from the solidified casting. The alumina and zircon components are bonded together in such a fashion that they will not separate during the casting process.

Description

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Investment casting, also referred to as the lost wax process, is a casting process which is particularly suited for the production o~ small metal parts having a high degree of dimensional accuracy. The investment casting process is widely used for the fabrication of blades and vanes for gas turbine engines. Articles produced by this process h2ve the advantage of requiring only minimal processing following cast-ing. This process is discussed in U.S. Patents to Earl, 1,831,555; Watts, 3,590,905; Horton~ 3,686,006, and Moren, 3,179,523 and 3,196,505.
Turbine efficiency is closely related to operating temp-erature. Demands for improved efficiency have resulted in the development of more heat resistant alloys. Surface condition also affects high temperature life and it is important that the finished casting have a good surface condition, one which is free from defects which may cause subsequent failures.
A technique which has been employed to improve the high temperature properties of superalloys is directional solid-ification. In this technique a molten casting slowly solidi-fied at a controlled rate so that the interface between the molten and solidified portions of the alloy passes slowly along the longitudinal axis of the part. One result of this technique may be to produce a series of columnar grains with the longitudinal axis of the grains being oriented with the longitudinal axis of the casting~ Improved longitudinal : -~ .

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high temperature properties are obtained as a result of the reduction in grain boundary area perpendicular to the longitudinal axis. This technique is described in the VerSnyder Patent 3,260,505 which is assigned to the present assignee.
In the past, a common problem with nickel base super-alloys used at elevated temperatures was a lack o~ ductility at intermediate temperatures such as about 1400F. This lack of ductility was responsible for many failures of turbine parts.
It was discovered that the addition of small amounts of hafnium to nickel base superalloys greatly improved the intermediate temperature of these alloys. Additionally such hafnium additions were found to improve the transverse mechanical properties of the castings. The addition of hafnium to superalloys is discussed in U.S. Patents 3,677,747 and 3,711,337.
A casting defect has been observed in these hafnium containing alloys which has not previously been noted in superalloys. This defect is a surface defect having a resem-blance to a crack or hot tear. The defect has been given the name chain porosity. This defect is found in castings having a change in cross sectional area of at least 1:2 in the vicinity where the change in cross section occurs. When the moving solidification interface passes from a portion of th~ casting having a small cross sectional area ~o a portion of the cast-ing having a larger cross sectional area it is believed that a condition arises which leads to the formation to the surface defect in the partially solidified casting. Careful studies ~7~43~

of the defect reveal that it has a crack-like morphology and that the root portion of the crack contains hafnium/hafnium oxide. Although chain porosity has only been observed in hafnium containing alloys, those skilled in the art will appreciate that the problem may arise in the future in alloys which do not contain hafnium as more advanced alloys are developed.
Accordingly it is the purpose of the present invention - to disclose a mold which may be used for the directional solidification of nickel base superalloys which will substan-tially eliminate the problem known as chain porosity. A
further object of the present invention is the description of the technique useful in producing composite molds useful for the elimination of chain porosity in nickel base superalloy castings.

DESCRIPTION OF THE PREFERRED EMBODIMENTS
The mold of the present invention is a composite mold having an inner component comprised predominantly of alumina and an outer component comprised predominantly of zircon.
The inner alumina component interacts with the molten and partially solidified metal in such a way as to reduce and eliminate chain porosity. The outer zircon component has desirable mechanical properties both before and after casting and easily removed fromthe finished part. The mold of the present invention may easily be produced using conventional equipment. Since the mold is predominantly zircon which is the material presently used to produce investment casting molds, i43~

the thermal expansion characteristics will be similar to those of the molds presently used. Accordingly, the patterns used to produce present molds will produce dimensionally satis-factory molds using the process of the present invention.
The mold of the present invention has an inner component comprised o~ at least 80 percent alumina having a thickness of from 2 to 20 mils. The inner component also contains silica which serves as a binder. The sum of the alumina and silica components must excede 90%. The outer component is comprised predominantly of zircon and has a thickness of from .1 to .4 inches. Because alumina and zircon have different coefficients of thermal expansion the thickness of the inner component must be carefully maintained within the previously described limits. If the thickness of the inner component varies ou-tside of these limits satisfactory performance will not be obtained and it is quite probable that the inner alumina component will crack or will spall away from the outer zircon component.
The exact cause of chain porosity is not known and therefore the way in which the alumina component eliminates chain porosity is not known, however, it has been observed that the alloys in question, nickel base superalloys which contain hafnium, wet alumina to a much greater extent than they wet zircon. It is believed that this difference in wetting significantly changes the heat transfer coefficient from the mold to the molten metal and this change in heat transfer coefficient quite likely changes the shape of the interface ~543~

between the solid and molten metal. It is believed that this change in interface shape is responsible for the elimination of the chain porosity problem. A minor drawback which has been encountered in the use of an alumina mold surface is that some slight reaction occurs between the molten metal and the alumina. This reactivity is somewhat implicit since the fact that the alumina is wet by the molten material implies some chemical affinity between the mold material and the molten metal. This slight reaction between the mold and the metal has not been found to be deleterious and can be completely removed by a sandblasting treatment and/or etching treatment.
Such reaction is entirely confined to the outer most layer of a casting and the maximum depth of reaction has been found to be not greater than 0~5~ mil. Although it might seem that the problem to which the present invention is addressed might be solved through the use of a shell comprised completely of alumina this is not the case. An all alumina shell becomes extremely strong and hard after it is heated to elevated temperatures by the molten metal. This strength is retained at room temperature and as a result it is difficult if not impossible to remove such a shell from the solidified casting.
In addition, since alumina has a different coefficient of thermal expansion, use of alumina molds would require an expensive redesign of existing patterns. The dimensional equivalence of the mold of the present invention with the prior art molds is of great commercial significance. Through the use of the composite mold of the present invention a ~7~;~3~
desirable combination of the attributes of both the zircon shell and alumina shell may readiLy be obtained. The resultan~
shell has adequate mechanical properties for the loads and stresses applied during the casting process but is weak enough to be readily removed from the solidified casting.
The thickness and composition of the alumina component are critical to the proper functioning of the mold. In its final dried form, the alumina component of the mold must contain at least 80% alumina if satisfactory results are to be obtained.
Silica is the preferred binder, and the sum of the alumina and silica should excede 90%. The average thickness of the inner component must be restricted to the range of

2 to 20 mils and this restriction can be satisfied through the selection of the slurry components from which the alumina component is fabricated. The thickness of the alumina component or prime coat is largely determined by the viscosity and density of the slurry. For proper results the viscosity , of the slurry must be from 13 to 19 seconds as measured in a ~4 Zahn cup at 75F. Two further restrictions are that the specific gravity of the slurry must lie in the range of 2.~5 to 2.60 and the pH must be between 9 and ~0. This is in conjunction with forced drying, as those skilled in the art know that with air dried shells these parameters can vary.
As an alternate embodiment, a plurality of prime coats using a lower viscosity slurry may be employed to achieve an inner layer of a satisfactory thickness.
Within the restrictions set forth above we have obtained particularly satisfactory results with an alumina containing slurry described below: In the following description all .: '.

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parts are by weight and include the water necessary to obtain the desired viscosity. From 20 to 30 parts of a 30 percent aqueous solution of colloidal silica, from 50 to 70 parts of alumina having a particle size of -325 mesh, from 10 to lS
parts of aLumina having a particle size -400 mesh, from 4 to 8 parts of alumina having a particle size of -100 mesh and from 0 to 5 parts of kyanite having a -100 mesh particle size. We have found that the addition of from 1 to 5 parts of cobalt al~lminate to the slurry mixture produces a signifi-cant improvement in surface finish. The cobalt aluminateaddition is preferred, but not required. In the preceding description the colloidal silica component is a binder which insures strength and adherence of the alumina component. At high temperatures the silica reacts with the alumina to form complex aluminates which bond the alumina particles together.
The particular selection of mesh sizes given above has produced extremely satisfactory results in that an alumina component produced with this slurry has an e~ceptional com-bination of mechanical properties and good surface finish.
It will be appreciated by those skilled in the art that the exact combination of particle size and distribution of par-ticle sizes in a slurry has a significant effect on viscosity and density. A slurry made according to the previous descrip-tion has a density and viscosity falling withln the l;mits previously described.
Alumina occurs in a wide variety of crystal structures and particle sizes. Examples of different types of alumina include tabular alumina, fused alumina and calcined alumina.

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As a general rule these types of alumina are broadly inter-changeable in the production of the present invention.
~lowever, a particularly preferred embodiment is set forth below in Example III.
The present invention will be made more clear through consideration of the following illustrative examples which deal with the production of experimental nickel base superalloy castings in a variety of types of shell molds. The alloy used has a nominal composition of 9% chromium, 10% cobalt, 12.5% tungsten, 1% columbium, 2% titanium, 5% aluminum, 2%
hafnium, .015% boron, .1% carbon, balance essentially nickel.
This alloy was cast from a temperature of about 2800F into a variety of molds described below having an internal shape corresponding to that of a turbine blade. In the molds the blade section which had a smaller cross sectional area than the root section as located beneath the root section so that -during directional solidification the solidification front passed from the small cross sectional area of the blade to the larger cross sectional area of the root. When chain porosity was encountered it was located in the near area of change in cross section. The castings were solidified at a rate of approximately 8 inches per hour using a withdrawal technique in which the mold was withdrawn from the furnace at a rate of about 8 inches per hour. All molds were produced using a conventional shell mold preparation technique which basically involves dipping a wa~ pattern into a ceramic slurry and applying a relatively coarse dry ceramic material (called stucco) to the wet slurry surface. This procedure is followed _~_ ~7~i~3~
a number of times with intermediate drying steps until a desired mold thickness is built up.
Example I
Conventionally all zircon molds were produced using the technique described above. The details of the compositions of the different slurries and dry ceramic mi~tures are given in Table I. Several molds were produced and test castings were made using these molds. A very high incidence of chain porosity was observed and a representative photomicrograph showing this chain porosity is shown in Fig. 1. Fig. 1 sho~7s a chain pososity having a depth of approgimately 10 mils into the body of the blade. Such a defect is obviously detrimental to the strength and useful life of an article such as the tur-bine blade which is subject to high stresses at elevated temperatures.
Example II
Several composite molds were produced according to the present invention using the sLurry and stucco sequence shown in Table II. Identical castings were made in these molds. These castings were found to be characterized by a complete absence of chain porosity. The molds were easily removed from the castings following solidification and the surface of the castings was easily cleaned using conventional abrasive techniques. The alumina slurry composition described in Table II has given excellent results and is a preferred embodiment.

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Example III
An all alumina shell was produced using the stucco and slurry sequence shown in Table III. Castings were successfully made in these molds and showed no evidence of chain porosity, however, the molds were extremely difficult to remove from the solidiEied casting and the dimensional accuracy of the final castings was not as good as those produced by the mold of the present example in Table II.
Although the invention has been shown and described with respect to a preferred embodiment thereof, it should be understood by those skilled in the art that various changes and omissions in the form and detail thereof may be made therein without depar~ing from the spirit and the scope of the invention.

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Claims

The embodiments of the invention in which an exclu-sive property or privilege is claimed are defined as follows:

1. A composite ceramic shell mold having an internal cavity for producing castings of superalloys, which are susceptible to chain porosity, which comprises a) an inner component composed predominantly of alumina and silica, with the alumina composing at least 80%
by weight of the component, and the sum of the alumina and silica composing at least 90% by weight of the component, said inner component having an average thickness of about 2 to 20 mills, and b) an outer component, composed predominantly of zircon, having a thickness of from .1 to .4 inch.

2. A shell mold as in claim 1 wherein the internal cavity contains a region where the cross-sectional area changes by a factor of at least 1:2.

3. A method of making a composite ceramic shell mold for the production of superalloy castings which includes the steps of a) providing a wax pattern b) providing a slurry composed predominantly of alumina with a colloidal silica binder, having a viscosity of 14 to 19 seconds as measured with a number 4 Zahn cup at 75°F, and a specific gravity of from 2.45 to 2.60, said slurry composition being such that the resultant ceramic, in its final form will contain at least 80% alumina, with the sum of the alumina and silica contents being at least 90%
c) dipping the pattern into the alumina containing slurry and removing the pattern d) applying a dry ceramic material to the slurry coated pattern and allowing the slurry to dry e) dipping the pattern into a slurry which is pre-dominantly composed of zircon and removing the pattern f) applying a dry ceramic material to the slurry coated pattern and allowing the slurry to dry, and g) repeating steps e and f a plurality of times, until the desired thickness is obtained.