Patent Application
20210189525
This application claims priority to Korean Patent Application No. 10-2019-0172978, filed on Dec. 23, 2019 which is incorporated herein by reference in its entirety.
Exemplary embodiments of the present disclosure relate to a method of manufacturing aluminum alloy and an aluminum alloy produced thereby; and, particularly, to an aluminum alloy for high-power engine components.
High-performance vehicles may greatly appeal to consumers seeking driving pleasure, and the development and production thereof are also effective in demonstrating the technology of automobile manufacturers to ordinary consumers.
Such a high-performance vehicle inevitably requires a high-power engine. However, as the power of the engine increases, the physical and thermal loads on the material of the engine increase.
An alloy used to cast a conventional cylinder head for high-performance vehicles has the following compositions, shown in Table 1, and the cylinder head is manufactured by heat treatment as illustrated in
The main reinforcing elements of the alloy are Mg and Si. Si is an element that affects the castability and strength of the alloy, and the alloy is improved in strength through the formation of Mg2Si precipitation phase after heat treatment by Mg.
In other words, the alloy is solutionized to evenly dissolve Si and Mg elements in an Al matrix and aged to form an Mg2Si compound, resulting in an increase in strength.
Although the aluminum for the cylinder head of the conventional gasoline engine has an endurance limit temperature of about 200° C., the test of the high-power engine shows that the temperature of the cylinder head increases from 250° C. to 300° C. For this reason, the use of existing materials may cause insurmountable damage to the cylinder head.
That is, the high-power engine is damaged before 1/10 of expected endurance test time due to exposure to high-temperature environment during testing. Hence, it can be seen that the conventional alloy compositions do not withstand the harsh environment of the high-power engine.
The foregoing is intended merely to aid in the understanding of the background of the present disclosure, and is not intended to mean that the present disclosure falls within the purview of the related art that is already known to those skilled in the art.
An embodiment of the present disclosure is directed to an aluminum alloy that can be used in a high-power engine by having excellent high-temperature physical properties and high thermal conductivity in favor of performance and fuel efficiency, and a method of manufacturing the same.
Other objects and advantages of the present disclosure can be understood by the following description, and become apparent with reference to the embodiments of the present disclosure. Also, it is obvious to those skilled in the art to which the present disclosure pertains that the objects and advantages of the present disclosure can be realized by the means as claimed and combinations thereof.
In accordance with an embodiment of the present disclosure, there is provided a method of manufacturing aluminum alloy, which includes solutionizing a cast product made of an aluminum alloy containing 0.1 to 0.3 wt % of Zr, quenching the cast product at a temperature of 30° C. or less after the solutionizing, and aging the cast product after the quenching.
The solutionizing may be performed at a temperature ranging from 520° C. to 560° C. for 4 to 48 hours.
The aging may include primary aging and secondary aging after the primary aging so as to be performed twice.
The primary aging may be performed at a temperature ranging from 165° C. to 195° C. for 4 to 48 hours.
The secondary aging may be performed at a temperature ranging from 200° C. to 225° C. for 3 to 7 hours.
In accordance with another embodiment of the present disclosure, there is provided a method of manufacturing aluminum alloy, which includes solutionizing a cast product made of an aluminum alloy containing 0.1 to 0.3 wt % of Zr, quenching the cast product after the solutionizing, and aging the cast product after the quenching, wherein the aging includes primary aging and secondary aging after the primary aging so as to be performed twice.
The primary aging may be performed at a temperature ranging from 165° C. to 195° C. for 4 to 48 hours.
The secondary aging may be performed at a temperature ranging from 200° C. to 225° C. for 3 to 7 hours.
In accordance with a further embodiment of the present disclosure, there is provided an aluminum alloy that includes Al as a base material, 6.5 to 7.5 wt % of Si, 0.35 to 0.45 wt % of Mg, and 0.1 to 0.3 wt % of Zr.
The aluminum alloy may further include 0.2 wt % or less of Cu.
An Al3Zr precipitation-strengthening phase may be formed in the aluminum alloy.
The accompanying drawings for illustrating exemplary embodiments of the present disclosure should be referred to in order to gain a sufficient understanding of the present disclosure, the merits thereof, and the objectives accomplished by the implementation of the present disclosure.
In the exemplary embodiments of the present disclosure, techniques well known in the art or repeated descriptions may be reduced or omitted to avoid obscuring appreciation of the disclosure by a person of ordinary skill in the art.
A method of manufacturing aluminum alloy and an aluminum alloy produced thereby according to exemplary embodiments of the present disclosure will be described below with reference to
The present disclosure relates to a composition and manufacturing method of an alloy for cylinder heads capable of realizing high-temperature physical properties and high thermal conductivity to withstand the physical and thermal loads of a high-power engine.
The comparison between the composition of the aluminum alloy according to the present disclosure and the composition of the alloy according to the related art is indicated in the following table, and the aluminum alloy is prepared by T6 heat treatment illustrated in
The aluminum alloy according to the present disclosure contains 0.1 to 0.3 wt % of Zr.
When the Zr content of the aluminum alloy exceeds 0.3 wt %, a coarse acicular Zr-related crystallization phase begins to appear, which is adversely affects the physical properties of the alloy. Therefore, the Zr content is limited to 0.1 to 0.3 wt %.
The aluminum alloy may further include Sr, Mn, Ti, and the like.
The aluminum alloy of the present disclosure has the above compositions shown in Table 2, and a cylinder head cast from the alloy is heat-treated to secure physical properties. In particular, examples of the product cast from the alloy may include not only a cylinder head that requires high-temperature physical properties, but also a component that requires similar properties.
The heat treatment includes solutionizing, quenching, primary aging, and secondary aging.
The solutionizing is performed at a temperature ranging from 520° C. to 560° C. for 4 to 48 hours. As a preferable example, the drawing illustrates that the solutionizing is performed at a temperature of 535° C. for 6 hours.
Unlike the related art, the quenching is performed at a temperature of 30° C. or less.
The primary aging is performed at a temperature ranging from 165° C. to 195° C. for 4 to 48 hours. As a preferable example, the drawing illustrates that the primary aging is performed at a temperature of 180° C. for 6 hours.
Unlike the related art, the present disclosure further includes the secondary aging. That is, the secondary aging is performed at a temperature ranging from 200° C. to 225° C. for 3 to 7 hours. As a preferable example, the drawing illustrates that the secondary aging is performed at a temperature of 215° C. for 6 hours.
In the AC4CH—Zr alloy of the present disclosure, an Al3Zr precipitation-strengthening phase is formed during the aging. Since the precipitation phase is effectively formed at a temperature of 200° C. or more that is higher than the existing Mg2Si precipitation-strengthening phase, additional aging is performed on the AC4CH—Zr alloy.
Meanwhile, a fine acicular Al3Zr crystallization phase is formed even in the composition of Zr in an amount of 0.3 wt % or less, which causes deterioration in physical properties. In order to prevent this physical property deterioration, the quenching is performed at a temperature of 30° C. or less after the solutionizing in the present disclosure.
Tables 3 and 4 summarize a test result for physical properties according to the amount of Zr in the alloy composition of the present disclosure.
As indicated in Table 3, when 0.1 wt % or more of Zr is added to the alloy, the elongation of the alloy significantly increases. However, it can be seen that the alloy is decreased in hardness, yield strength, and tensile strength at room temperature, in inverse proportion to elongation.
In addition, when the aging condition is changed to prevent the deterioration of physical properties at room temperature, the alloy shows that an increment in elongation is decreased but strength properties are increased.
However, when the Zr content of the alloy exceeds 0.3 wt %, a coarse acicular Zr-related crystallization phase begins to appear as illustrated in
In the heat treatment application of
A quenching temperature will be described below in more detail.
In the heat treatment process of the conventional alloy for cylinder heads, the quenching temperature is essential to be maintained at 80° C. or more. Since the cylinder head has a complicated internal structure, residual stress is apt to occur according to the cooling rate for each part in the cylinder head. In fact, the cylinder head may be damaged by the residual stress at the time of development. Therefore, as can be seen in
However, when the alloy of the present disclosure is quenched at a temperature of 80° C. or more, a fine acicular Zr phase is crystallized as illustrated in
However, when the quenching is performed at a temperature of 30° C. or less as in the heat treatment method of the present disclosure, the Zr-related crystallization phase becomes fine and is changed in shape from acicular to spherical as illustrated in
A change in physical properties according to the change of Zr crystallization phase may be referred to in the following Table 6.
The term “crystallization phase” refers to a phase in which particles, which have not dissolved beyond the solid solution limit when molten Al is cooled, remain in the Al matrix. Generally, the crystallization phase may be observed when a material structure is analyzed using an optical microscope and an SEM. As a result of the Jmatpro thermodynamic simulation of
The term “precipitation phase” refers to a phase in which particles dissolved in molten Al exist in a supersaturated solid solution state due to quenching and are later precipitated into a solid by heat treatment. The crystallization phase is formed during solidification whereas the precipitation phase is formed during heat treatment (solutionizing+aging). Since the precipitation phase is fine enough not to be seen in general structure observation, it can be seen through TEM observation as illustrated in
Furthermore, in the present disclosure, the secondary aging is performed after the quenching is performed at 30° C. or less and the primary aging is then performed.
If only the primary aging is conventionally performed in spite of the optimal composition of Zr, it can be seen that the treatment may not satisfy desired physical properties, namely all of high elongation, high thermal conductivity, and high-temperature durability.
This is due to the crystallization of acicular Zr structures and the absence of Zr-related precipitation-strengthening phases. The Mg2Si precipitation phase, which is a strengthening phase of the existing AC4CH alloy, shows an optimum precipitation-strengthening effect when aging is performed at 180° C. for 6 hours, whereas Al3Zr, which is a Zr-related precipitation phase, is precipitated into a matrix at a higher temperature to exhibit a strengthening effect. Accordingly, after the Mg2Si precipitation phase is distributed in the matrix by performing aging at 160 to 195° C. for 4 to 24 hours, the secondary aging is further performed. Since the Mg2Si precipitation phase begins to lose a strengthening phase effect when exposed to a high temperature of 200° C. or more, additional aging temperature and time are required to obtain the Al3Zr precipitation phase, which is a high-temperature strengthening phase, while minimizing the effect degradation of the Mg2Si precipitation phase.
The effects of strengthening phases are tested through physical property measurement, and the following Table 7 summarizes a result of the test. Table 7 indicates results when the secondary aging is performed at 200 to 225° C. for 3 to 7 hours under the conditions that the solutionizing is performed at 535° C. for 6 hours, the quenching is performed at 30° C., the primary aging is performed at 180° C. for 6 hours. In particular, as the result of additional aging at 215° C. for 6 hours, it can be seen that the strength properties at room temperature are slightly decreased due to the loss of Mg2Si strengthening effect, but the strength properties at high temperature are improved due to the effect of Al3Zr acting as a high-temperature strengthening phase.
In addition, performing the secondary aging can resolve the residual stress caused by the quenching at room temperature and obtain high elongation and high thermal conductivity by strength decreased at room temperature.
As described above, it can be seen that the alloy of the present disclosure including Zr in the range has a tensile strength of about 272 MPa at room temperature and a tensile strength of about 146 MPa at high temperature as illustrated in Table 7. However, it can be seen that the alloy does not have desired physical properties when each heat treatment condition is not satisfied as illustrated in the following Table 8. Therefore, it is possible to derive optimum heat treatment conditions as illustrated in Table 9.
As described above, the alloy according to the present disclosure can exhibit the following effects as illustrated in the following Table 10.
The alloy is increased by 50% in elongation and 10% in thermal conductivity at room temperature, compared to existing materials. Although the alloy is somewhat decreased in strength properties (hardness: HB93→HB 78) at room temperature, it is increased in strength properties at the high temperature at which the engine is driven, for example, by 11% in yield strength and 17% in tensile strength, compared to existing materials. Overall, the alloy is increased by 30% or more in fatigue strength at a high temperature due to the increase in elongation, yield strength, and tensile strength. In addition, when the thermal conductivity of the cylinder head is increased by 10%, the torque of the engine is increased to result in an improvement in performance, which also helps to reduce knocking and thus improve fuel efficiency.
Furthermore, the current process in which quenching is performed at a temperature of 80° C. or more to reduce residual stress incurs the cost of maintaining water at a high temperature and the cost of excessive evaporation of water, whereas the present disclosure is expected to achieve a reduction in cost since quenching is performed at a temperature of 30° C. or less, compared to the related art.
In accordance with exemplary embodiments of the present disclosure, the aluminum alloy can be applied to the cylinder head of the high-power engine by having excellent high-temperature physical properties and high thermal conductivity in favor of performance and fuel efficiency.
More specifically, the aluminum alloy is increased by 50% in elongation and 10% in thermal conductivity at room temperature, compared to existing materials. Although the aluminum alloy is somewhat decreased in strength properties (hardness: HB93→HB 78) at room temperature, it is increased in strength properties at the high temperature at which the engine is driven, for example, by 11% in yield strength and 17% in tensile strength, compared to existing materials. Overall, the aluminum alloy is increased by 30% or more in fatigue strength at a high temperature due to the increase in elongation, yield strength, and tensile strength. In addition, when the thermal conductivity of the cylinder head is increased by 10%, the torque of the engine is increased to result in an improvement in performance, which also helps to reduce knocking and thus improve fuel efficiency.
Furthermore, the current process in which quenching is performed at a temperature of 80° C. or more to reduce residual stress incurs the cost of maintaining water at a high temperature and the cost of excessive evaporation of water, whereas the present disclosure is expected to achieve a reduction in cost since quenching is performed at a temperature of 30° C. or less, compared to the related art.
While the specific embodiments have been described with reference to the drawings, the present disclosure is not limited thereto. It will be apparent to those skilled in the art that various changes and modifications may be made without departing from the spirit and scope of the disclosure as defined in the following claims. Therefore, these changes and modifications will fall within the scope of the disclosure as long as they are apparent to those skilled in the art, and the scope of the present disclosure should be defined based on the entire content set forth in the appended claims.
| Number | Date | Country | Kind |
|---|---|---|---|
| 10-2019-0172978 | Dec 2019 | KR | national |
