Patent Application
20110014495
The present invention relates to a metal material for parts of a casting machine, a molten aluminum alloy-contact member and a method for producing them, and more particularly to a metal material for parts of a casting machine and a molten aluminum alloy-contact member, which have excellent melting loss resistance to a molten aluminum alloy, and a method for producing them.
A molten aluminum alloy has a property of reacting with a metal, such as iron, to produce an intermetallic compound. Those steel parts of a casting machine which are in direct contact with a molten aluminum alloy can be damaged due to their reaction with aluminum. This phenomenon is called melting loss. In casting of an aluminum alloy, it is essential to take measures against melting loss for chief parts, such as a conduit, a mold, a sleeve and an insert, which are to contact a molten aluminum alloy.
A steel material, such as a tool steel which has undergone a nitriding treatment, is generally used for a mold, etc. for use in aluminum casting. The nitriding treatment, which comprises diffusing nitrogen from a steel surface to form a hard nitride layer, is excellent in enhancing the wear resistance of the material. It has been pointed out, however, that such treatment is not always sufficient for preventing a melting loss.
With respect to members for which high melting loss resistance is required, it is a common practice to form a ceramic coating on the surface of a member by a vapor deposition method, such as PVD (physical vapor deposition) or CVD (chemical vapor deposition). Such a ceramic coating is known to be chemically stable to a molten aluminum alloy and exhibit very high melting loss resistance (see New Mechanical Engineering. Handbook, B2, Processing/Processing Devices, p. 157).
The biggest problem with a ceramic coating, as formed by PVD or CVD, is peeling due to a thermal stress. In particular, because of a large difference in thermal expansion coefficient between a steel base and a ceramic coating, a large thermal stress will be produced at the boundary between the ceramic coating and the steel base by the repetition of heating and cooling during successive casting cycles. The large thermal stress often causes peeling of the ceramic coating from the base, whereby the base comes into direct contact with a molten aluminum alloy. Melting of the steel base thus begins suddenly, resulting in a melting loss of the base.
For the purpose of preventing such peeling of ceramic coating, various improvements have, been made in methods for forming ceramic coatings in order to reduce the thickness of a coating, thereby minimizing a thermal stress generated at the boundary between the coating and a base, or to enhance the bonding strength between a coating and a base.
Despite the various improvements, however, the fundamental difference in thermal expansion between a ceramic coating and a steel base has been an insurmountable bar, and complete prevention of peeling of a ceramic coating has not been achieved as yet.
It is therefore an object of the present invention to solve the above problems in the prior art and provide a metal material for parts of a casting machine and a molten aluminum alloy-contact member, which have materially enhanced melting loss resistance, without resorting to conventional techniques, such as the provision of a ceramic coating by PVD or CVD.
It is another object of the present invention to provide a method for producing a molten aluminum alloy-contact member, which makes it possible to strongly bond TiC particles to a Ni alloy layer of the member so that the member has materially enhanced melting loss resistance.
In order to achieve the above objects, the present invention provides a metal material for machine parts for use in a casting machine for casting an article from a molten aluminum alloy, comprising a steel base, a Ni alloy layer formed on a surface of the base, and titanium carbide (TiC) bonded in a particulate state to the surface of the N alloy layer.
The present invention also provides a machine part for use in a casting machine for casting an article from a molten aluminum alloy, comprising a body, composed of a steel base and a nickel alloy layer formed on a surface of the base on the side to be in direct contact with a molten aluminum alloy, and titanium carbide (TiC) bonded in a particulate state to the surface of the Ni alloy layer.
The present invention also provides a method for producing a molten aluminum alloy-contact member for use in a casting machine for casting an article from a molten aluminum alloy, comprising the steps of: forming a Ni alloy layer on a surface of a steel base, thereby forming a body; burying the body in TiC powder; and placing the body, together with the TiC powder, in a vacuum heating oven and heating them under vacuum to a temperature at which a liquid phase generates from the Ni alloy, thereby bonding the TiC particles to the surface of the Ni alloy layer.
According to the present invention, a molten aluminum alloy-contact member, having materially enhanced melting loss resistance, can be provided without resorting to conventional techniques, such as the provision of a ceramic coating by PVD or CVD. Thus, by applying the present invention to those parts of a casting machine which are to be in direct contact with a molten aluminum alloy, the lives of the parts can be considerably extended.
Preferred embodiments of the present invention will now be described with reference to the drawings.
TiC particles have a property of repelling a molten aluminum alloy. By utilizing this property, direct contact of a molten aluminum alloy with the steel base can be prevented and high melting Toss resistance can be achieved.
Unlike the mechanism of enhancing the melting loss resistance of a metal material by covering the entire surface with a coating to shut off contact of a molten aluminum alloy with the base metal surface, as in the conventional ceramic coating by PVD or CVD, the present metal material can be provided with materially enhanced melting loss resistance simply by densely scattering TiC particles over the base metal surface.
In the structure that the TiC is bonded in a particular state to the Ni alloy layer, a large thermal stress will not act on the TiC particles even when the base thermally expands or contracts. Thus, the TiC particles hardly peel off and, therefore, the melting loss resistance can be maintained for a long period.
The TiC particles may be partly exposed on the surface of the Ni alloy layer. This can increase the contact angle with a molten aluminum alloy, thereby enhancing the property of repelling the molten aluminum alloy.
Preferably, the gaps in the TiC particles are filled in with fine ceramic particles comprising at least one of boron nitride (BN), alumina (Al2O3) and zirconia (ZrO2), as shown in
The Ni alloy preferably has the composition of 2.6 to 3.2% of B, 18 to 28% of Mo, 3.6 to 5.2% of Si and 0.05 to 0.22% of C, with the remainder being Ni and unavoidable impurities.
The TiC particles can be bonded to the Ni alloy, having the above composition, with high strength through generation of a liquid phase from the Ni alloy. Further, because of good wetting between the liquid phase and TiC particles, a large number of TiC particles can be densely bonded to the Ni alloy layer.
A conduit, a mold, a molten metal sleeve, an insert, etc. for use in a casting machine, can be typically exemplified for molten aluminum alloy-contact members or machine parts of a casting machine to which the above-described metal material is applicable.
The member to be produced comprises a steel base. First, a alloy layer is formed on the base by thermal spraying.
Next, as shown in
The vessel, containing the TiC powder and the member buried in it, is placed in a vacuum heating oven, and heated under vacuum to a temperature at which a liquid phase is generated from the Ni alloy, thereby bonding the TiC particles to the surface of the Ni alloy layer.
By the heating, the TiC particles are bonded to the Ni alloy layer in such a state that they protrude from the surface of the Ni alloy layer, as shown in
When the particle diameter of the TiC particles is smaller than 10 μm, it is difficult to control the temperature during the vacuum-heating so that the TiC particles may not be entirely covered with the liquid phase of the Ni alloy. The intended melting loss resistance will not be obtained if the TiC particles are entirely covered with the liquid phase of the Ni alloy.
When the particle diameter of the TiC particles is larger than 500 μm, on the other hand, the liquid phase of the Ni alloy will cover only lower portions of the particles with small contact area and weak bonding strength. Accordingly, the particles will easily fall off.
After the bonding of TiC particles to the member, the member may optionally be subjected to a process comprising applying a slurry of a mixture of a binder and a fine ceramic powder comprising at least one of boron nitride (BN), alumina (Al2O3) and zirconia (ZrO2) to the TiC particles, and burning the ceramic powder into the surface of the member. The melting loss resistance of the member increases after this process.
The Ni alloy layer, to which the TiC particles are bonded, itself has a poor melting loss resistance to a molten Al alloy. The melting loss resistance can be improved by attaching the fine ceramic powder to the Ni alloy layer. Furthermore, the attached fine powder is present such that it fills in the gaps in the TiC particles. Accordingly, the fine ceramic powder hardly falls off upon contact with a molten aluminum alloy.
The present invention will now be further described with reference to experimental examples.
In the examples, test specimens for melting loss test were prepared using a steel material (JIS S45C) as a base. A Ni alloy having the above-described composition was thermally sprayed onto the steel base to line the base with the Ni alloy. The Ni alloy-lined base was then buried in TiC powder in a vacuum heating oven, and heated under vacuum until the TiC particles came to be bonded to a liquid phase generated from the Ni alloy.
Two types of test specimens were prepared for Example 1 and Example 2. The specimen of Example 1 is the above specimen with the TiC particles bonded thereto but no ceramic powder attached, while the specimen of Example 2, was prepared by burning fine powder of boron nitride (BN) into the surface of the above specimen with the TiC particles bonded thereto.
For comparison with the melting loss resistances of the specimens of Examples 1 and 2, a comparative specimen was prepared by coating the same steel base as in Examples 1 and 2 with titanium nitride (TiN) by CVD.
A melting loss test was carried out in the following manner: Each test specimen was immersed in a molten aluminum alloy (JIS AC4C) which was kept at 720° C., and was rotated at a peripheral speed of 0.8 m/s while keeping it immersed in the molten metal for 24 hours. Thereafter, the test specimen was taken out of the molten metal, and a change in the weight of the specimen was measured.
As is apparent from comparison of the data for the specimen of Example 1 with the data for the comparative specimen, the amount of melting loss for the specimen of Example 1, having the TiC particles bonded to the Ni alloy layer, can be reduced to approximately half of the amount of melting loss for the comparative specimen having the TiN coating formed by CVD. The data in
A description will now be given of Example 3 in which a conduit, a flow passage for a molten aluminum alloy, was produced as a molten aluminum alloy-contact member.
In Example 3 was used the same material as in Example 2 except for using fine alumina powder having an average particle diameter of about 1 μm instead of the fine boron nitride (BN) powder.
For comparison with the melting loss resistance of the conduit of Example 3, a comparative conduit was produced using a material composed of the same steel base and a coating of TiN formed by CVD. A molten aluminum alloy at about 700° C. was allowed to flow in the conduit of Example 3 and in the comparative conduit, and the time elapsed before detection of a melting loss was measured.
A melting loss was detected after about 19 hours in the comparative conduit, whereas no melting loss was detected in the conduit of Example 3 even after an elapse of 100 hours.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2004-082990 | Mar 2004 | JP | national |
This application is a divisional of U.S. application Ser. No. 10/599,118 filed Sep. 20, 2006. U.S. application Ser. No. 10/599,118 claims priority to Japanese Patent Application No. 2004-082990 filed Mar. 22, 2004. Japanese Patent Application No. 2004-082990 claims priority to International Application No. PCT/JP2005/005100 filed Mar. 22, 2005. The entire contents of all of the applications mentioned above are incorporated herein by reference.
| Number | Date | Country | |
|---|---|---|---|
| Parent | 10599118 | Sep 2006 | US |
| Child | 12891477 | US |
