Patent Application
20170327929
The present disclosure relates to metal casting and more specifically to aluminum alloy compositions and methods of aluminum alloy metal casting.
The statements in this section merely provide background information related to the present disclosure and may or may not constitute prior art.
Al—Si based cast aluminum alloys have widespread applications for structural components in the automotive, aerospace, and general engineering industries because of good castability, corrosion resistance, machinability, and high strength-to-weight ratio. Regarding castability, alloy compositions having lower silicon content have been thought to inherently produce poor castings due to a wider freezing range and the reduced latent heat. Alternatively, alloy compositions having higher Silicon content are increasingly difficult to machine and have lower ductility and fracture toughness due to coarser primary silicon particles. In general, aluminum alloy casting performance is based on several factors including alloy composition, casting and solidification conditions, and post-casting process or heat treating.
In attempting to expand or improve the use of aluminum alloys in additional applications that can reap the benefits that aluminum alloys offer, existing aluminum alloy casting composition and processes have fallen short of success in high temperature applications. The overwhelming problem with using aluminum alloy castings in high temperature applications is the tendency for the material to change properties in service. In designing cast parts for such applications, one of the most important aspects of material properties is exactly that the material properties stay unchanged in service. However, to this end currently available commercial aluminum alloys fail to provide such material property stability.
Accordingly, there is a need in the art for an aluminum alloy composition and manufacturing method that has improved initial material properties while maintaining or stabilizing the material properties throughout the service life of the casting in a high temperature application.
The present invention provides an Aluminum-Silicon based casting alloy and manufacturing process. The casting alloy has a composition including, by weight percentage, from about 5.00% to about 17.00% Silicon (Si), from about 0.00% to about 0.90% Iron (Fe), from about 0.00% to about 1.00% Manganese (Mn); from about 0.000% to about 0.018% Strontium (Sr), from about 0.00% to about 2.00% Copper (Cu), from about 0.00% to about 0.50% Magnesium (Mg), from about 0.00% to about 0.05% Zinc (Zn), from about 0.01% to about 0.10% Boron (B); and a balance of Aluminum (Al).
In another example of the present invention, the composition includes, by weight percentage, from about 7.85% to about 7.90% Silicon and about 0.20% to about 0.30% Iron.
In yet another example of the present invention, the composition includes, by weight percentage, about 0.00% Strontium.
In yet another example of the present invention, the composition includes, by weight percentage, about 0.009% Strontium.
In yet another example of the present invention, the composition includes, by weight percentage, from about 0.40% to about 0.41% Iron and about 0.00% Strontium.
In yet another example of the present invention, the composition includes, by weight percentage, more than about 0.25% Magnesium.
In yet another example of the present invention, the composition includes, by weight percentage, more than about 1.50% Copper.
In yet another example of the present invention, the manufacturing process includes producing a casting by means of one of a sand casting process, a permanent mold casting process, a semi-permanent mold casting process, a high-pressure die casting process, a squeeze casting process, and lost foam casting process.
In yet another example of the present invention, the casting is analyzed to determine an as-cast silicon particle volume fraction, an average silicon particle size, an insoluble intermetallic particle volume fraction, and an insoluble intermetallic average particle size.
In yet another example of the present invention, the casting is solution treated to above an incipient melting temperature by heating the casting to a first temperature for a first period of time, heating the casting to a second temperature for a second period of time, and heating the casting to a third temperature for a third period do time.
In yet another example of the present invention, casting is aged at a temperature between about 150° C. and 190° C. and a time of about 6 to 10 hours.
In yet another example of the present invention, the first temperature is about 495° C. and the first period of time is three hours, the second temperature is about 515° C. and the second period of time is three hours, and the third temperature is about 530° C. and the third period of time is two hours.
The above features and advantages and other features and advantages of the present invention are readily apparent from the following detailed description of the best modes for carrying out the invention when taken in connection with the accompanying drawings.
The drawings described herein are for illustration purposes only and are not intended to limit the scope of the present disclosure in any way.
The following description is merely exemplary in nature and is not intended to limit the present disclosure, application, or uses.
As with most metal casting practices and applications, the metal alloy's microstructure has a great effect on the mechanical properties of the material. Specifically addressing Al—Si alloys, the primary casting practices that affect microstructure are solidification rate, chemical impurity modification, and thermal modification during heat treatment. For nearly all compositions, the minimum attained elevated temperature strength, specifically after long term elevated temperature exposure, is higher for parts cast in Al—Si alloys that have not undergone a solution heat treatment. Additionally, higher volume fractions of eutectic Si is another way to retain higher elevated temperature strength. However, both absence of a solution heat treatment and high eutectic Si contribute to lower heat treated and room temperature strength.
Referring now to
With reference to
Next,
As can be concluded from the above results, solution treatment of unmodified and Strontium modified 319 Al tends towards a similar microstructure of coarse, rounded eutectic Silicon. However, 48 hours is too long for commercial production of castings. A path to the microstructure achieved at 48 hours of solution treatment must be created.
In the continued search for stable aluminum castings in high temperature service environment, the effects of both composition modification and solution temperature on microstructure is examined. Table 1 below provides the compositions of a 319 Al with Manganese (Mn), 319 Al with Mn modified with Strontium (Sr), and 319 Al with Mn modified with higher levels of Iron (Fe).
With reference to
Tensile strengths from the samples of
Tensile strength of samples from Tables 1 and 2 that were subsequently stabilized for 200 hours at 250° C. are charted in
The larger quantity of hard particles in the microstructure, the aggregate hardness and strength increases; especially at elevated temperature where the hardness and strength of the aluminum matrix drop rapidly. Soluble phases such as soluble intermetallics and strengthening precipitates add very little to the hardness and strength after long-term elevated temperature exposure. However, soluble intermetallics and strengthening precipitates are very helpful during fabrication. For example, machining forces and tool wear are generally lower for higher hardness aluminum castings. Thus, retaining a minimum degree of hardening is necessary to aid in manufacturing the machined casting. Regarding long-term durability in an elevated temperature or cycling temperature environment, an optimum volume fraction of hard particles is required that balance hardness and strength against ductility and fatigue resistance. The optimum volume fraction is not fixed for every casting design application in that loading, design geometry, in-service temperature, and heating rates all contribute to determining the optimum volume fraction. In addition, the type of hard particle, including the hardness, size, shape, spacing and interfacial bonding to the matrix also contribute to the information required to specify the optimum volume fraction of hard particles.
As a result, a minimum level of precipitation hardening is required. In aluminum-silicon casting alloys adequate hardness can be developed with magnesium above 0.25% or copper above 1.5% or some combination of the two. Keeping Mg and Cu as low as practical is important since higher levels lead to the formation of soluble intermetallics that will reduce casting quality and impair the heat treatment process proposed below via the threat of incipient melting.
Additionally, the volume fraction, size, and distribution of insoluble hard phases, both eutectic silicon and intermetallic, must be controlled to a close tolerance. This is accomplished by chemistry modification to suit the local solidification conditions during the primary casting process. The volume fraction of these phases are not changed by subsequent thermal processing; only the shape and size and so it is favorable to produce the right amount in the initial microstructure. For high temperature applications, the alloy includes Silicon in the amount between 5.0% and 17.0% by weight, Iron in the amount between 0.0% and 0.9% by weight, Manganese in the amount between 0.0% and 1.0% by weight, Chromium in the amount between 0.0% and 0.3% by weight, and Nickle in the amount between 0.0% and 2.0% by weight.
Next, optimization of the heat treatment process produces the size, shape and volume fraction of insoluble hard particles specified to the application. Commercial alloys can show improved elevated-temperature strength when they have not been solution treated due to a significant fraction of the hard phases being soluble and thus disappear during solutionizing. In addition, current solution treatment processes have been optimized to minimize the eutectic silicon size in order to maximize ductility. However, for elevated temperature strength, slightly larger particle sizes are required. Thus under-solution treating an alloy with a fairly good morphological control of the insoluble intermetallics at an optimum volume fraction is one possible process to use. Alternatively, a super-critical solution treatment by stepping the temperature to levels that allow the eutectic silicon to grow past the minimum while simultaneously refining and speriodizing the insoluble intermetallic phases is another possible process. Once the shape and size of the hard particles is defined by the solution treatment process, subsequent thermal exposure during aging and in service will have little effect on the properties. Therefore, maintaining a stable structure and properties that will define the minimum hardness and strength attained is the target of the process once the hardening precipitates have become incoherent.
Alloy composition, casting process and heat treatment method are controlled to form an aluminum casting with insoluble intermetallic phases that are refined and spheroidized. Whereas the intermetallic phases are primarily iron-based, they can contain Mn, Cr, Ni, etc. as minor impurities. The intermetallic phases are included at less than 2 to 3 volume percent for applications requiring room-temperature toughness, or 6 to 10 volume percent for high stiffness applications. The eutectic silicon phase is stabilized beyond the minimum particle size and spheroidized via fragmentation of unmodified structures or agglomeration of modified structures. Particle size of hard particles is ideally between 50 and 110 microns (equivalent circle diameter (μm)=√{square root over (4A/π)}, with A as the measured area of the particle) with particle shape approaching spheroidal. The eutectic silicon phase is included as about 6 to 12 volume percent for high toughness applications and from 6 to 15 volume percent for higher stiffness applications.
Thus, Table 3 details alloy compositions for different applications; including moderate or high temperature and high or low toughness.
In addition to the composition guidelines of Table 3, Table 4 includes guidelines for optimal microstructure features for each of the applications.
While the best modes for carrying out the invention have been described in detail, those familiar with the art to which this invention relates will recognize various alternative designs and examples for practicing the invention within the scope of the appended claims.
