Patent Application
20120100385
The present invention relates to a production method of a roughly shaped material for an engine piston made of aluminum alloy excellent in wear resistance and high-temperature characteristics, and also relates to the roughly shaped material for an engine piston.
An engine piston for use in an engine to be mounted to a vehicle such as an automobile is required to have lightweight property to reduce the inertia force as much as possible, high-temperature strength at a raised maximum temperature, durability at the raised maximum temperature, low thermal expansibility to reduce clearance fluctuations due to thermal expansion, and wear resistance to reduce abrasion of ring grooves due to sliding of piston rings and/or abrasion of a skirt portion due to contact with a cylinder surface.
For these reasons, in an engine piston produced by forging, as an aluminum alloy constituting the piston, in the case of giving greater importance to wear resistance, an alloy in which an additive amount of Si is equal to or more than the eutectic point has been used (see, e.g., Patent Document 1). On the other hand, in the case of giving greater importance to high temperature strength or high temperature fatigue strength, an alloy in which an additive amount of Si is equal to or less than the eutectic point has been used (see, e.g., Patent Document 2).
In an aluminum alloy engine piston, however, in order to improve the engine efficiency, it is preferable to enhance both the high-temperature strength and the high-temperature fatigue strength while maintaining the wear resistance.
The present invention was made in view of the aforementioned technical background, and aims to provide a production method of a roughly shaped material for an engine piston made of aluminum alloy excellent in wear resistance and high-temperature characteristics, and to provide the roughly shaped material for an engine piston.
Other objects and advantages of the present invention will be apparent from the following preferred embodiments.
The present invention provided the following means.
[1] A production method of a roughly shaped material for an engine piston, comprising:
a continuous casting step for obtaining a cast rod having a diameter of 85 mm or less by continuously casting a molten metal consisting of Si: 11.0 to 13.0 mass %, Fe: 0.6 to 1.0 mass %, Cu: 3.5 to 4.5 mass %, Mn: 0.25 mass % or less; Mg: 0.4 to 0.6 mass %, Cr: 0.15 mass % or less, Zr: 0.07 to 0.15 mass %, P: 0.005 to 0.010 mass %, Ca: 0.002 mass % or less, and the balance being Aluminum and inevitable impurities with a temperature of the molten metal before pouring into a continuous casting mold set to 720° C. or higher; and
a forging step for obtaining a roughly shaped material for an engine piston by forging a forging material obtained by subjecting the cast rod to a homogenization treatment at a temperature of 370 to 500° C.
[2] The production method of a roughly shaped material for an engine piston as recited in the aforementioned Item 1, wherein an additive amount of P in a composition of the molten metal satisfies the following formula:
0.0025×additive amount of Si−0.025≦additive amount of P≦0.0025×additive amount of Si−0.02 (1),
where a unit of the additive amount of P and that of Si are “mass %”, respectively.
[3] A roughly shaped material for an engine piston produced by the production method of a roughly shaped material for an engine piston as recited in the aforementioned Item 1 or 2,
wherein, at least in a skirt portion corresponding portion and a piston ring groove portion corresponding portion in the roughly shaped material, primary Si exists, and
wherein, in an entirety of the roughly shaped material, no primary Si having a maximum grain diameter of 50 μm or larger exists and no Al—Fe—Cr—Mn series giant crystal having a maximum grain diameter of 50 μm or larger exists.
[4] A roughly shaped material for an engine piston produced by forging, wherein a composition of the roughly shaped material consists of Si: 11.0 to 13.0 mass %, Fe: 0.6 to 1.0 mass %, Cu: 3.5 to 4.5 mass %, Mn: 0.25 mass % or less; Mg: 0.4 to 0.6 mass %, Cr: 0.15 mass % or less, Zr: 0.07 to 0.15 mass %, P: 0.005 to 0.010 mass %, Ca: 0.002 mass % or less, and the balance being Aluminum and inevitable impurities.
[5] The roughly shaped material for an engine piston as recited in the aforementioned Item 4, wherein an additive amount of P in the composition of the roughly shaped material satisfies the following formula:
0.0025×additive amount of Si−0.025≦additive amount of P≦0.0025×additive amount of Si−0.02 (1),
where a unit of the additive amount of P and that of Si are “mass %”, respectively.
[6] The roughly shaped material for an engine piston as recited in the aforementioned Item 4 or 5,
wherein, at least in a skirt portion corresponding portion and a piston ring groove portion corresponding portion in the roughly shaped material, primary Si exists, and
wherein, in an entirety of the roughly shaped material, no primary Si having a maximum grain diameter of 50 μm or larger exists, and no Al—Fe—Cr—Mn series giant crystal having a maximum grain diameter of 50 μm or larger exists.
According to the present invention, by adjusting the compositional elements of the molten metal so as to fall within predetermined ranges and producing a roughly shaped material for an engine piston according to the production method of the present invention, a roughly shaped material for an engine piston made by aluminum alloy excellent in wear resistance and high-temperature characteristics can be obtained. Therefore, in the engine piston produced by the aforementioned roughly shaped material, the performance efficiency of the engine can be improved, and the fuel usage in automobiles and motorcycles can be reduced.
Furthermore, in the roughly shaped material, since primary Si exists at least in a skirt portion corresponding portion and a piston ring groove portion corresponding portion in the roughly shaped material, at least these portions are excellent in wear resistance. Therefore, an engine piston produced by the roughly shaped material can control abrasion of at least the skirt portion and the piston ring groove.
Next, an embodiment of the present invention will be explained with reference to drawings.
In this embodiment, “excellent in high-temperature characteristics” means “excellent in strength at 250° C.,” in other words, “at 250° C., the tensile strength (i.e., high-temperature tensile strength) is 110 MPa or more and the fatigue strength (i.e., high-temperature fatigue strength) is 60 Mpa or more.”
In
In
In the following explanation, the explanation will be made by defining that on a plane of a paper showing
As shown in
As shown in
In the roughly shaped material 11, there exists a primary Si at least in the skirt portion corresponding portion 14 and the piston ring groove portion corresponding portion 17. Furthermore, in the entire roughly shaped material, there exists no primary Si having a maximum grain diameter of 50 μm or larger and no Al—Fe—Cr—Mn series giant crystal having a maximum grain diameter of 50 μm or larger. Further, in the entire roughly shaped material, there exists no segregation of primary Si.
In this embodiment, “there exists primary Si” specifically means that, for example, when a sample is mirror polished and then the mirror polished surface of the sample is subjected to a microstructure analysis under a metallurgical microscope, there exists a gray-brown block-shaped crystal.
The maximum diameter of the primary Si denotes a diameter measured at a portion where the primary Si has a maximum size. The maximum diameter of the Al—Fe—Cr—Mn series giant crystal denotes a diameter measured at a portion where the giant crystal has a maximum size.
As a specific measuring method of the maximum diameter of primary Si, the following method can be exemplified. For example, when a sample is mirror polished and then the mirror polished surface of the sample is subjected to a microstructure analysis under a metallurgical microscope, a gray-brown block-shaped crystal is considered to be primary Si, and by measuring the maximum length of the crystal using an image analysis device, the maximum diameter of the primary Si can be obtained. As an image analysis device, a device named “LUZEX” manufactured by Nireco Corporation can be used, for example.
As a specific measuring method of the maximum diameter of the Al—Fe—Cr—Mn series giant crystal, the following method can be exemplified. For example, when a sample is mirror polished and then the mirror polished surface of the sample is subjected to a microstructure analysis under a metallurgical microscope, a light gray crystal is considered to be an Al—Fe—Cr—Mn series giant crystal, and by measuring the maximum length of the giant crystal using an image analysis device, the maximum diameter of the Al—Fe—Cr—Mn series giant crystal can be obtained. As an image analysis device, a device named “LUZEX” manufactured by Nireco Corporation can be used, for example.
In this embodiment, among Al—Fe—Cr—Mn series crystals of various sizes, an Al—Fe—Cr—Mn series crystal having a maximum diameter of 50 μm or larger is especially called an Al—Fe—Cr—Mn series giant crystal. The Al—Fe—Cr—Mn series giant crystal is also called an Al—Fe—Cr—Mn series giant intermetallic compound (giant compound).
In the present invention, the criterion for judging whether or not there exists segregation of primary Si is not especially limited. In this embodiment, the criterion of judgment is that when 5 or more primary Si (preferably 3 or more) are gathered to form primary crystal Si aggregation and there exists primary crystal Si aggregation in which at least one of the distances between primary Si is smaller than the grain diameter of the primary Si, it is judged that there exists segregation of primary Si, and when there exists no such primary Si aggregation, it is judged that there exists no segregation of primary Si.
Next, as a production method of a roughly shaped material for an engine piston according to one embodiment of the present invention, a production method of the roughly shaped material 11 will be explained below.
A production method of the roughly shaped material 11 includes a continuous casting step of obtaining a cast bar by continuously casting a molten metal having a predetermined composition, and a forging step of obtaining a roughly shaped material by forging a forging material obtained by subjecting the cast bar to a homogenization treatment.
At the continuous casting step, it is necessary that the molten metal temperature before pouring into a continuous casting mold is set to 720° C. or higher to continuously cast the molten metal. Furthermore, the diameter of the cast bar obtained with the continuous casting step should be 85 mm or less.
The composition of the molten metal includes Si: 11.0 to 13.0 mass %, Fe: 0.6 to 1.0 mass %, Cu: 3.5 to 4.5 mass %, Mn: 0.25 mass % or less; Mg: 0.4 to 0.6 mass %, Cr: 0.15 mass % or less, Zr: 0.07 to 0.15 mass %, P: 0.005 to 0.010 mass %, Ca: 0.002 mass % or less, and the balance being Aluminum and inevitable impurities.
At the forging step, the forging material should be a cast bar homogenized at a temperature of 370 to 500° C.
Hereinafter, the reason for adding compositional elements of the aluminum alloy molten metal, the reason for limiting the additive amount (additive density) thereof, and the reason for limiting the production condition of the roughly shaped material 11 will be explained.
<Si: 11.0 to 13.0 Mass %>
Si is an element that controls thermal expansion of aluminum alloy to keep small and improves the wear resistance. In other words, the wear resistance can be improved by appropriately controlling the crystallization of primary Si.
The appropriate thermal expansion coefficient is determined by the material of an opposing member of the engine piston 1, i.e., the material of a cylinder block (e.g., steel, aluminum). However, although the cylinder block partially rises in temperature to a high temperature, the cylinder block does not entirely rise in temperature to a high temperature (and it takes a time to rise in temperature to a high temperature). Therefore, it is preferable that the thermal expansion coefficient is as smaller as possible. Generally, in designing the engine piston 1 and selecting the piston ring, they are each designed based on a size when they reached a high temperature. For that reason, if the thermal expansion is too large, the diameter of the skirt portion 4 reduces at low temperatures, which readily causes shakiness of the engine piston 1 at the time of the start-up. Therefore, it is preferable that the additive amount of Si is as large as possible in terms of reducing the thermal expansion. The preferable thermal expansion coefficient is 19 to 21×10−6/K in the range of 25 to 250° C., and the additive amount of the Si that can obtain such thermal expansion coefficient is 11.0 to 13.0 mass %.
On the other hand, with such additive amount of the Si, conventionally, crystallization of primary Si by continuous casting was unstable. That is, since the eutectic point of Al—Si alloy is usually 11.7 mass %, the primary Si will not be crystallized at 11.0 mass % which is lower than 11.7 mass %. Therefore, when an additive amount of Si was around the eutectic point, continuous casting could not be conducted in a manner such that primary Si is stably crystallized. In other words, in cases where the additive amount of Si was, for example, within the range of 11.7±0.5 mass %, the crystallization of primary Si by continuous casting was conventionally unstable.
However, the present inventors could find specific alloy composition and specific production conditions capable of attaining high temperature strength and high temperature fatigue strength while maintaining wear resistance, even in cases where an additive amount of Si was around the eutectic point, and completed the present invention.
In other words, with the composition of the molten metal according to the present invention, by adding Ca and P which will be explained later, even when an additive amount of Si is around the eutectic point, primary Si is crystallized stably by interaction with them, which improves wear resistance. It is more preferable that the additive amount of Si exceeds 12.0 mass %
If the additive amount of Si is less than 11.0 mass %, it is not preferable because the thermal expansion becomes large, and crystallization of primary Si is controlled to decrease wear resistance.
If the additive amount of Si exceeds 13 mass %, such additive amount causes segregation of crystallized primary Si, forming an origin of fatigue fracture, which causes deterioration of high temperature fatigue strength, and therefore it is not preferable.
In particular, when forging the forging material obtained by homogenizing a cast bar at a predetermined temperature into a roughly shaped material for an engine piston, it is preferable that primary Si is in an evenly distributed state and primary Si is minute in size at an outer circumferential portion of the cast bar corresponding to the skirt portion 4 and the piston ring groove portion 7 of the engine piston 1.
<Fe: 0.6 to 1.0 Mass %>
Along with Cr, Mn, etc., Fe is crystallized as an Al—Fe—Cr—Mn series intermetallic compound, and the crystal becomes a dispersion strengthening phase which is stable even at high temperatures, which contributes to improvement of high temperature strength.
If the additive amount of Fe is less than 0.6 mass %, the amount of the dispersion strengthening phase becomes small, resulting in less improved high temperature strength, and therefore it is not preferable.
On the other hand, if the additive amount of Fe exceeds 1.0 mass %, a needle-shaped Al—Fe—Cr—Mn series giant crystal will be crystallized, forming an origin of fatigue fracture, which causes deterioration of high temperature fatigue strength, and therefore it is not preferable.
Generally, if Fe, Cr and Mn are added in large quantity, Al—Fe—Cr—Mn series giant crystals will be crystallized, which causes deterioration of high temperature fatigue strength. In the present invention, however, even if the total additive amount of Fe, Cr and Mn is large, by adding Cr and Mn so that the additive amount becomes 40 mass % or less with respect to the additive amount of Fe, crystallization of giant crystals can be controlled even in cases where the additive amount of Fe is large.
<Cu: 3.5 to 4.5 Mass %>
Cu is precipitated as an Al—Cu (—Mg) series intermetallic compound, and the existence improves the strength and the fatigue strength under 150° C. (hereinafter referred to as “normal temperature strength” and “normal temperature fatigue strength,” respectively).
If the additive amount of Cu is less than 3.5 mass %, the precipitation amount of Al—Cu (—Mg) series intermetallic compound becomes small, which less improves the normal temperature strength and the normal temperature fatigue strength, and therefore it is not preferable.
Since Cu is a heavy element, a larger additive amount of Cu causes hindrance of the inherent lightweight characteristics of aluminum alloy. The solid solubility limit of Cu is 5.65 mass %, but the additive amount of Cu exceeding 4.5 mass % results in less improved effect of the normal temperature strength and normal temperature fatigue strength, and therefore the upper limit of the additive amount of Cu is set to 4.5 mass %.
<Mn: 0.25 Mass % or Less>
Mn is an element which will be crystallized as an intermetallic compound together with Fe and/or Cr to become a dispersion strengthening phase, which contributes to improvement of high temperature strength. However, as compared with Fe, Mn more likely forms Al—Fe—Cr—Mn series giant crystals. Therefore, the additive amount of Mn is set to 0.25 mass % or less. The additive amount of Mn is preferred to be as small as possible, especially preferable to be below the detection limit. The most preferable additive amount of Mn is 0 mass %.
<Mg: 0.4 to 0.6 Mass %>
Mg is an element which improves the normal temperature strength and the normal temperature fatigue strength by coexisting with Si and/or Cu. If the additive amount of Mg is less than 0.4 mass %, the aforementioned effects can be less expected, which is not preferable. However, even if Mg is added so as to exceed 0.6 mass %, the aforementioned effects will be saturated. Therefore, the additive amount of Mg is set to 0.4 to 0.6 mass %.
<Cr: 0.15 Mass % or Less>
Cr is an element which will be crystallized as an intermetallic compound together with Fe and Mn to become a dispersion strengthening phase, which contributes to improvement of high temperature strength. However, as compared with Fe, Cr more likely forms Al—Fe—Cr—Mn series giant crystals. Therefore, the additive amount of Cr is set to 0.15 mass % or less. The additive amount of Cr is preferred to be as small as possible, especially preferable to be below the detection limit. The most preferable additive amount of Cr is 0 mass %.
<Zr: 0.07 to 0.15 Mass %>
Zr is an element which that precipitates Al—Zr series intermetallic compound at 350° C. or above to improve the high temperature strength of the alloy material. If the additive amount of Zr is below 0.07 mass %, the aforementioned effects can be less expected, and therefore it is not preferable. Even if the additive amount of Zr exceeds 0.15 mass %, the aforementioned effects will be saturated. Therefore, the additive amount of Zr is set to 0.07 to 0.15 mass %.
<P: 0.005 to 0.010 Mass %>
P is an element which shifts the lower limit of the additive amount of Si at which primary Si is crystallized toward a lower Si amount side, and refines the grain diameter of the primary Si crystal. In cases where the additive amount of Si is relatively large, no addition of P causes coarse primary Si. In cases where the additive amount of P is below 0.005 mass %, the aforementioned defects can be less expected, and therefore it is not preferable. On the other hand, the additive amount of P exceeding 0.010 mass % causes saturation of the aforementioned effects, and also accelerates formation of needle-shaped eutectic Si to deteriorate toughness, and therefore it is not preferable. Therefore, the additive amount of P is set to 0.005 to 0.010 mass %. This additive amount can result in the maximum diameter of primary Si of 50 μm or less.
In particular, it is preferable that the additive amount of P satisfies the following formula (I). Satisfying the formula makes it possible to assuredly stabilize crystallization of primary Si by continuous casting. This assuredly results in existence of primary Si in the entire roughly shaped material, assuredly prevents segregation of primary Si, and further assuredly causes spheroidized eutectic Si. As a result, a roughly shaped material for an engine piston excellent in wear resistance and high temperature characteristics can be assuredly obtained.
0.0025×additive amount of Si−0.025 additive amount of P 0.0025×additive amount of Si−b 0.02 (1),
wherein a unit of the additive amount of P and that of Si are “mass %”, respectively.
With respect to P, in the case of P alone, the melting amount of P (i.e., the additive amount of P) into a molten metal is small, and it is troublesome to handle P alone. Therefore, in order to increase the additive amount of P and attain easier handling, it is preferable to add P to a molten metal in the form of P—Cu (8 mass % of P and 92 mass % of mother alloy of Cu).
<Ca: 0.002 Mass % or Less>
Ca is an element which hinders refinement and hardening of primary Si due to P. Therefore, flux including magnesium chloride (MgCl2) is added to the molten metal and agitated to thereby control so that the amount of Ca in the molten metal decreases and the additive amount of Ca becomes 0.002 mass % or less. More preferably, the additive amount of Ca and P (unit:mass %) is set to P>6×Ca, so that even in cases where an additive amount of Si is around the eutectic point, P is not depleted by Ca. As a result, AlP is created, and the AlP effectively works as a nucleus for forming heterogeneous nucleus of primary Si, which causes minute and even crystallization of primary Si. In this way, the wear resistance can be improved. The additive amount of Ca is preferably as small as possible, especially below the detection limit. The most preferable additive amount of Ca is 0 mass %.
In the continuous casting step, the reason for setting the temperature of the molten metal to 720° C. or above is as follows.
Casting while maintaining molten metal before starting solidification in a high temperature state controls formation of Al—Fe—Cr—Mn series giant crystals during the solidification process and also contributes to refinement and even distribution of primary Si crystallized in a cast bar. Therefore, the casting temperature is set to 720° C. or higher. This can be realized by setting the molten metal temperature before pouring into a continuous casting mold to 720° C. or higher. The preferable molten metal temperature is 740° C. or higher. By setting the molten metal temperature to 720° C. or higher, when forging a forging material obtained by homogenizing the cast bar into a roughly shaped material for an engine piston, the crystallization state of primary Si on an outer circumferential portion of the cast bar corresponding to the skirt portion 4 and the piston ring grove portion 7 of the engine piston 1 can be refined and evenly. The upper limit of the molten metal temperature is not especially limited, and can be, for example, 850° C. (preferably 750° C.).
At the continuous casting step, the reason for setting the diameter of the cast bar to 85 mm or less is as follows.
When the diameter of the cast bar (casting diameter) becomes larger, the cooling rate of the center portion of the ingot becomes low, which readily causes Al—Fe—Cr—Mn series giant crystals, and furthermore disturbs refinement and even distribution of primary Si in the center portion of the cast bar. When the diameter of the cast bar is 85 mm or smaller, the difference between the cooling rate of the center portion of the cast bar and that of the outer circumferential portion of the cast bar can be kept small. This preferably makes the cooling rate difference to be 200° C./s or less, which in turn can control formation of Al—Fe—Cr—Mn series giant crystals. Therefore, the diameter of the cast bar is set to 85 mm or less. By setting so, when forging a forging material obtained by homogenizing the cast bar into a roughly shaped material for an engine piston, there will be no existence of Al—Fe—Cr—Mn series giant crystals at the center portion of the cast bar corresponding to the crown surface portion 2 of the engine piston 1, and the crystallization state of primary Si can be refined such as less than 50 μm in maximum diameter and evenly distributed. The lower limit of the diameter of the cast bar is not especially limited, and can be, for example, 20 mm.
The reason for homogenizing the cast bar at 370 to 500° C. is as follows.
As the area of the boundary surface between Al—Si series crystals or Al—Fe—Cr—Mn series crystals and aluminum base increases, the Al—Fe—Cr—Mn series crystals resist plastic deformation at a high temperature, which results in hard plastic deformation at a high temperature. As a result, the high temperature strength and the high temperature fatigue strength are improved.
However, a homogenization treatment generally performed at immediately below the solidus temperature to improve forging performance is high in processing temperature, which causes decoupling and spheroidizing of Al—Si series crystals and/or Al—Fe—Cr—Mn series crystals to reduce the area of the boundary surface. In the present invention, the upper limit of the processing temperature is set to a temperature at which no decoupling and spheroidizing of Al—Si series crystals and/or Al—Fe—Cr—Mn series crystals occur. However, if the homogenization treatment temperature is too low, deformability becomes insufficient, causing cracks during forging. Therefore, the homogenization treatment temperature is set between 370 to 500° C., more preferably set to be as low as possible within a range in which no cracks are generated in the material at the time of forging the material into the engine piston shape. The retention time of the homogenization treatment is preferably 4 hours or longer. By subjecting the cast bar to a homogenization treatment under the aforementioned treatment conditions, it becomes possible to retain a state in which no decoupling or spheroidizing of Al—Si series crystals and/or Al—Fe—Cr—Mn series crystals occurs. The upper limit of the retention time of the homogenization treatment is not specifically limited, and can be within 24 hours, for example.
Next, the continuous casting device used for continuously casting a molten metal will be explained.
As a continuous casting device, as long as a cast bar having a diameter of 85 mm or less can be obtained in a state in which the molten metal temperature is maintained at 720° C. or above, the continuous casting device is not limited in type, and can be, for example, a vertical semi-continuous casting device, a hot top continuous casting device, a horizontal continuous casting device, and a gas pressurizing type continuous casting device.
According to the present invention, in each of the aforementioned continuous casting devices 20A and 20B, it is preferable that the temperature at the position C immediately before pouring the molten metal 30 into the mold 22 is defined as a molten metal temperature, and the temperature is preferably set to 720° C. or higher. In the following columns of [Example], the temperature of the molten metal 30 at the position C is defined as a molten metal temperature.
Next, a homogenization treatment furnace used for homogenizing the forged bar will be explained.
As the homogenization heat treatment furnace, it is sufficient as long as the furnace can accommodate the cast bar and conduct a homogenization treatment thereof at a temperature of 370 to 500° C., and can be any conventional widely used furnace. For example, in the case of a circulating hot air furnace, the furnace can be either a direct heating furnace or a radiant tube furnace, and in the case of a carrier system furnace, the furnace can be either a continuous furnace or a batch furnace.
Next, a forging device used for forging a forging material is explained.
As a forging device, it is sufficient as long as the device is equipped with a forging mold for forging a forging material into an engine piston shaped roughly shaped material. It is particularly desirable that the device is further equipped with a preliminary heating device and a lubricant applying device. Furthermore, it is preferred that the forging mold is a closed forging mold. More specifically, as the forging device, a knuckle joint press, a crank press, a friction press, a hydraulic press, and a servo press, can be used.
The production method of a roughly shaped material of this embodiment is performed as follows.
Using a continuous casting device, at a molten metal temperature of 720° C. or higher, a molten metal having a predetermined composition is continuously cast into a cast bar having a diameter of 85 mm or less [Continuous casting step]. It is preferable that the cross-sectional shape of the cast bar is a circle shape. In other words, it is preferable that the cast bar is in a cylindrical bar shape.
Next, the cast bar is subjected to a homogenization treatment at a temperature of 370 to 500° C. to thereby obtain a forging material. After the homogenization treatment, as needed, the outer circumferential surface of the material is subjected to a peeling treatment (i.e., the outer circumferential surface cutting treatment). Thereafter, this material is cut in the longitudinal direction to have a predetermined length (thickness) into a disk or cylinder shape. At this stage, the cross-sectional surface of the cast bar becomes an upper or lower surface of the material, and the outer circumferential surface or the inner side vicinity of the cast bar becomes an outer circumferential surface of the material. Furthermore, as needed, the material is subjected to upset processing, lubrication processing, and preheating processing.
Next, the material is forged into a roughly shaped material of an engine piston shape with a forging device [Forging step].
The molds 41 of the forging devices 40 shown in
In
In
As shown in
The processing temperature for the preheating process to be performed immediately before forging and the material temperature during the forging are preferably 470° C. or lower in as a short time period as possible. It is more preferred to be a temperature lower than the homogenization treatment temperature. The heating time can be the shortest amount of time during which the material temperature can be raised to the processing temperature (i.e., 470° C. or below). By processing at a low temperature for a short time, the state of Al—Si series crystals and Al—Fe—Cr—Mn series crystals after the homogenization treatment can be maintained even after forging.
As needed, the roughly shaped material 11 obtained in this manner is subjected to a solution treatment or an aging treatment.
The solution treatment temperature is preferably set to be the same as or lower than the solidus temperature because the state of Al—Si series crystals or Al—Fe—Cr—Mn series crystals after the homogenization treatment can be maintained.
As to the aging treatment temperature and the aging treatment time, it is preferable that slight over aging is performed by adjusting the temperature and the time. Such adjustment enables controlling of the dimensional growth due to the aging during the use of the product.
The roughly shaped material 11 is subjected to a final finish processing, such as, e.g., machining processing. Thereafter, other members, such as, e.g., piston rings, are attached to the roughly shaped material to obtain an engine piston.
In the roughly shaped material 11 produced in accordance with the production method of a roughly shaped material according to this embodiment explained above, there exists no cracks in the crown surface portion corresponding portion 12 during the forging processing, adequate amount of primary Si at least in the skirt portion corresponding portion 14 and the piston ring groove portion corresponding portion 17, no primary Si having a maximum diameter of 50 μm or larger. Further, there exists no segregation of primary Si, and no Al—Fe—Cr—Mn series giant crystals having a maximum diameter of 50 μm or larger. Therefore, an engine piston 1 produced using the roughly shaped material 11 is excellent in wear resistance, and also excellent in normal temperature tensile characteristics, high temperature characteristics (i.e., high temperature tensile characteristics and high temperature fatigue characteristics).
Although the embodiment of the present invention has been explained above, it should be noted that the present invention is not limited to the aforementioned embodiment, and can be changed variously within a range not deviating from the gist of the present invention.
Next, concrete Examples of the present invention and Comparative Examples will be described. It should be noted, however, that the present invention is not limited the following Examples.
The unit of the Aluminum alloy composition in Table 1 is “mass %.”
A round bar-shaped cast bar was obtained by continuously casting the aluminum alloy molten metal having the composition shown in Table 1 using a hot top continuous casting device (see
In casting, the molten metal was casted in a mold according to JIS Z 2611 to obtain an analysis sample 50 of an approximately disk-shape as shown in
Next, the cast bar was cut into a length of 6,000 mm. Then, the cut cast bar was subjected to a homogenization treatment. In the homogenization treatment, the treatment temperature was set as shown in the “Homogenization treatment temperature” column of Table 2. The treatment time was 7 hours for each case.
Thereafter, the outer circumference of the cast bar was cut out to have a diameter of 50 mm, and further, the cast bar was cut into a length of 60 mm to thereby obtain a cylindrical forging material.
Next, after preheating the material at 420° C., the material was upset forged into a thickness of 10 mm by pressing the material from its end surface in the axial direction. The upset forging corresponds to the forging in the forging step of the present invention, and the forging was conducted at the forging processing rate corresponding to the forging processing rate of actually forging the material into the roughly shaped material for an engine piston.
Thereafter, the upset forged product was subjected to a T6 heat treatment. In other words, the upset forged product was subjected to a solution treatment at a temperature of 495° C., and thereafter an artificial aging treatment was conducted under the conditions of aging temperature of 200° C. and aging time of 6 hours.
The upset forged product to which the T6 heat treatment was executed was subjected to a visual inspection to check whether or not there exists cracks and hole defects on the surface of the upset forged product by a solvent removable penetrant testing method (color check). Thereafter, the upset forged product was cut, and the cut surface was mirror-polished. The mirror polished surface was subjected to a microscopic inspection to inspect the structure from the center portion to the outer circumferential portion of the upset forged product using a metallurgical microscope to check whether or not there exists primary Si, primary Si having a maximum diameter of 50 μm or larger, Al—Fe—Cr—Mn series giant crystals, and segregation of primary Si. These results are shown in the column of “Presence or absence of primary Si,” “Presence or absence of primary Si of 50 μm or larger,” “Presence or absence of giant crystals,” and “Presence or absence of segregation of primary Si” in Table 2, respectively. Primary Si was present in the entirety of the upset forged product of all of Examples 1 to 7. For the upset forged product to which T6 heat treatment was executed, the normal temperature tensile characteristics, the high temperature tensile characteristics and the high-temperature fatigue characteristics were evaluated.
The metallographic structure photograph of Example 1 is shown in
In the metallographic structure photograph, the Al—Fe—Cr—Mn series crystal is shown as a light gray colored crystal, the primary Si is shown as a gray-brown colored block-shaped crystal, and the eutectic Si is shown as a gray-brown colored crystal smaller than the primary Si and having an average grain diameter of about 5 μm.
In
In
The evaluation method of the normal temperature tensile characteristics was as follows.
From the upset forged product to which a T6 heat treatment was executed, a JIS 14A proportional test piece was obtained. The tensile strength of the test piece was measured at 25° C. It was evaluated as “Good” when the tensile strength was 350 MPa or above, and evaluated as “Poor” when the tensile strength was less than 350 MPa. The results are shown in the column of “Normal temp. tensile property” in Table 2.
The evaluation method of the high temperature tensile property was as follows.
After holding the upset forged product to which a T6 heat treatment was executed at 250° C. for 100 hours, a JIS 14A proportional test piece with a flange was obtained from the upset forged product. At the time of a strength test, after holding the test piece again at 250° C. for 15 minutes, the tensile strength of the test piece was measured at 250° C. It was evaluated as “Good” when the tensile strength was 110 MPa or above, and evaluated as “Poor” when the tensile strength was less than 110 MPa. The results are shown in the column of “High temp. tensile property” in Table 2.
The evaluation method of the high temperature fatigue property was as follows.
After holding the upset forged product to which a T6 heat treatment was executed at 250° C. for 100 hours, a fatigue test piece was obtained from the upset forged product. A fatigue test of the test piece was performed at 250° C. using a Ono-type rotary bending fatigue testing machine. A stress value at which no breakage occurs at 10,000,000 cycles was defined as fatigue strength, and it was evaluated as “Good” when the stress value was 60 MPa or above and evaluated as “Poor” when the stress value was less than 60 MPa. The results are shown in the column of “High temp. fatigue property” in Table 2.
Examples 1-7 satisfy all of requirements of the present invention, and therefore it was confirmed that no cracks were generated, there existed primary Si along the entire upset forged product, there existed no primary Si having a maximum diameter of 50 μm or more, there existed no Al—Fe—Cr—Mn series giant crystals having a maximum diameter of 50 μm or more, and there existed no segregation of primary Si. Further, it was confirmed that they were excellent in normal temperature tensile property, high temperature tensile property and high temperature fatigue property.
In Comparative Example 1, since the additive amount of Si was small, there existed no primary Si.
In Comparative Example 2, the additive amount of Si was too large, there existed segregation of primary Si and the grain diameter of the primary Si was large, which caused cracks starting from the primary Si at the time of the upset forging.
In Comparative Example 3, since the additive amount of Fe was too large, Al—Fe—Cr—Mn series giant crystals were generated, which caused cracks starting from the giant crystals at the time of the upset forging.
In Comparative Example 4, since the additive amount of Mn and Cr was too large, Al—Fe—Cr—Mn series giant crystals were generated, which caused cracks starting from the giant crystals at the time of the upset forging.
In Comparative Example 5, since the additive amount of Cu and Mg was too small, the normal temperature tensile strength was deteriorated.
In Comparative Example 6, since the additive amount of Zr was too small, the high temperature tensile strength property and the high temperature fatigue property were deteriorated.
In Comparative Example 7, since the additive amount of Fe was too small, the high temperature tensile strength property and the high temperature fatigue property were deteriorated.
In Comparative Example 8, since the additive amount of Si was relatively small and no P was added, there existed no primary Si.
In Comparative Example 9, since the additive amount of Si was relatively large and no P was added, primary Si was coarsened.
In Comparative Example 10, since the additive amount of Ca was not reduced by flux, primary Si was roughened.
In Comparative Example 11, since the molten alloy temperature was too low, segregation of primary Si occurred.
In Comparative Example 12, since the diameter of the cast bar was too large, the primary Si in the middle portion of the upset forged product was roughened.
In Comparative Example 13, since the temperature for the homogenization treatment was too low, spheronization of eutectic Si, etc., was insufficient, which caused cracks at the time of upset forging.
In Comparative Example 14, since the temperature for the homogenization treatment was too high, eutectic melting occurred by preheating before the upset forging, which caused cracks starting from the molten portion at the time of the upset forging.
In Table 3, the unit of Al alloy composition is “mass %.”
By continuously casting the molten Al alloy having the composition shown in Table 3 using a hot top continuous casting device (see
In casting, molten alloy was casted into a mold in accordance with JIS Z 2611 to obtain an analysis sample 50 having a roughly disk-shape as shown in
Next, the cast bar was cut into a length of 6,000 mm. Then, the cut cast bar was homogenized under the conditions of the temperature of 470° C. and the holding time of 7 hours.
Thereafter, the outer periphery of the cast bar was cut to have a diameter of 50 mm and then cut into a length of 60 mm to thereby obtain a columnar forging material.
Next, after preheating this material at 420° C., the material was upset forged into a thickness of 10 mm by pressing the material from the end face in the axial direction. This upset forging corresponds to the forging of the forging step of the present invention, and was performed at the forging processing rate corresponding to the forging processing rate for actually forging the material into a roughly shaped material for an engine piston.
Thereafter, the upset forging product was subjected to a T6 heat treatment. That is, the upset forged product was subjected to a solution treatment at 495° C., and then artificial aging was performed under the conditions of the aging temperature of 200° C. and the aging time of 6 hours.
The upset forged product to which T6 heat treatment was performed was cut, and the cut surface was mirror polished. The polished surface was subjected to a microscopic inspection from the center portion to the outer peripheral portion of the upset forged product using a metallurgical microscope to investigate whether there exists primary Si at the center portion and the peripheral portion of the upset forged product, whether there exists segregation of primary Si, and to investigate the shape of eutectic Si.
As to the existence or non-existence of primary Si, it was judged based on whether or not there existed a gray-brown colored block-shaped crystal under microstructure observation.
As to the existence or non-existence of segregation of primary Si, it was judged that there existed segregation of primary Si when there existed primary Si aggregation formed by three or more primary Si and having at least one of distances between primary Silicones smaller than the grain diameter of primary Si, and judged that there existed no segregation of primary Si when there existed no such primary Si.
Eutectic Si is a gray-brown colored block-shaped crystal smaller than primary Si. By measuring the size of the crystal, it was judged that the eutectic Si was formed into a needle-shape when the “maximum length/minimum length” was 3 or more, and it was judged that the eutectic Si was formed into a spherical shape when the “maximum length/minimum length” was less than 3.
In the evaluation column in
As shown in Table 4 and
In Comparative Examples 15, 21, and 22, since the content of Si was too small, primary Si partially existed in the upset forged product, or primary Si did not exist along the entire upset forged product.
In Comparative Examples 16, although the content of Si was within the range of the present invention, since the additive amount of P was too small, primary Si existed only at the center portion of the upset forged product, and no primary Si existed at the periphery thereof.
In Comparative Examples 17, 18, and 19, since the additive amount of Si was too large, segregation of primary Si occurred.
In Comparative Examples 20, although the content of Si was within the present invention, since the additive amount of P was too large, eutectic Si was formed into a needle-shape. Therefore, the toughness of the upset forged product was poor.
This application claims priority to Japanese Patent Application No. 2009-158954 filed on Jul. 3, 2009, and the entire disclosure of which is incorporated herein by reference in its entirety.
It should be understood that the terms and expressions used herein are used for explanation and have no intention to be used to construe in a limited manner, do not eliminate any equivalents of features shown and mentioned herein, and allow various modifications falling within the claimed scope of the present invention.
While the present invention may be embodied in many different forms, a number of illustrative embodiments are described herein with the understanding that the present disclosure is to be considered as providing examples of the principles of the invention and such examples are not intended to limit the invention to preferred embodiments described herein and/or illustrated herein.
While illustrative embodiments of the invention have been described herein, the present invention is not limited to the various preferred embodiments described herein, but includes any and all embodiments having equivalent elements, modifications, omissions, combinations (e.g., of aspects across various embodiments), adaptations and/or alterations as would be appreciated by those in the art based on the present disclosure. The limitations in the claims are to be interpreted broadly based on the language employed in the claims and not limited to examples described in the present specification or during the prosecution of the application, which examples are to be construed as non-exclusive. For example, in the present disclosure, the term “preferably” is non-exclusive and means “preferably, but not limited to.” In this disclosure and during the prosecution of this application, means-plus-function or step-plus-function limitations will only be employed where for a specific claim limitation all of the following conditions are present in that limitation: a) “means for” or “step for” is expressly recited; b) a corresponding function is expressly recited; and c) structure, material or acts that support that structure are not recited. In this disclosure and during the prosecution of this application, the terminology “present invention” or “invention” may be used as a reference to one or more aspect within the present disclosure. The language present invention or invention should not be improperly interpreted as an identification of criticality, should not be improperly interpreted as applying across all aspects or embodiments (i.e., it should be understood that the present invention has a number of aspects and embodiments), and should not be improperly interpreted as limiting the scope of the application or claims. In this disclosure and during the prosecution of this application, the terminology “embodiment” can be used to describe any aspect, feature, process or step, any combination thereof, and/or any portion thereof, etc. In some examples, various embodiments may include overlapping features. In this disclosure and during the prosecution of this case, the following abbreviated terminology may be employed: “e.g.” which means “for example;” and “NB” which means “note well.”
The present invention can be applicable to a production method of a roughly shaped material for producing an engine piston for an engine to be mounted on a vehicle such as an automobile or a motorcycle, and also can be applicable to a roughly shaped material for an engine piston.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2009-158954 | Jul 2009 | JP | national |
| Filing Document | Filing Date | Country | Kind | 371c Date |
|---|---|---|---|---|
| PCT/JP2010/061329 | 7/2/2010 | WO | 00 | 12/29/2011 |
