Patent Application
20170107600
The present invention relates to a compressor impeller cast from aluminum alloy for use in turbochargers of the internal combustion engines of automobiles and ships, and to a method for producing same.
BACKGROUND ART
The turbochargers used for the internal combustion engines of automobiles and ships include a compressor impeller that compresses and supplies air into the internal combustion engine by rotating at high speed. The compressor impeller can reach temperatures as high as about 150° C. during its high-speed rotation, and receives high stress, such as the torsional stress from the rotating shaft, and the centrifugal force, near the center of rotation, particularly at the disc section.
Various materials are used for the compressor impeller according to the required performance of the turbocharger. Hot forged materials of an aluminum alloy machined into an impeller shape are typically used in large-scale applications such as ships. Mass production efficiency and costs are more important in relatively smaller applications such as in automobiles (e.g., cars, and trucks), and boats. Such applications commonly use easily castable aluminum alloys of primarily silicon additive such as JIS-AC4CH (Al—7% Si—0.3% Mg alloy), ASTM-354.0 (Al—9% Si—1.8% Cu—0.5% Mg alloy), and ASTM-C355.0 (Al—5% Si—1.3% Cu—0.5% Mg alloy) of desirable castability. These materials are then cast with a plaster mold by using techniques such as low-pressure casting, vacuum casting, and gravity casting, and are strengthened by a solution treatment or an aging treatment before use. A basic method of such procedures is disclosed in detail in Patent Document 1.
Lately, the need for high-speed turbochargers has increased with the increase in the demand for higher compression ratios of air necessitated by smaller engines, higher output, and increased exhaust recirculation. However, faster rotation speeds increase the amount of heat generated by air compression, and at the same time increase the temperature of the exhaust turbine impeller. The temperature of the compressor impeller is increased by a heat transfer due to heat generation. It has been found that conventional compressor impellers made of easily castable aluminum alloys of primarily silicon additive tend to cause problems such as deformation and fatigue failure during use, and fail to keep rotating normally. Specifically, these existing compressor impellers have an operating temperature of at most about 150° C., and there is a strong need for the development of a compressor impeller that can withstand an operating temperature of about 200° C. to meet the demand for high speed rotations.
It may be possible to use an aluminum alloy composition of more desirable high-temperature strength, for example, such as JIS-AC1B (Al—5% Cu—0.3% Mg alloy). However, as described in Patent Document 2, the problem of the alloy such as JIS-AC1B is that the molten metal lacks desirable fluidity, and tends to cause misruns (underfilling) of the molten metal in thin section of vane sections when used to make articles that have complex shapes and thin vane sections such as in compressor impellers.
Patent Document 2 addresses this problem by proposing a method that uses an Al—Si easily castable alloy such as AC4CH for the vane section for which misruns of a molten metal are of concern, and an Al—Cu high-strength alloy such as AC1B for the boss and disk sections that are connected to the rotating shaft and thus require strength. These are coalesced by being poured in two separate sections to form a compressor impeller.
Patent Document 3 proposes a method that uses an alloy of desirable castability for the vane section, and in which a strengthened composite material prepared by impregnating a strengthening material such as a 25%-B (boron) aluminum whisker with aluminum is used for the stressed boss section and the central section of the disk section. These are then joined to each other to form a compressor impeller.
Patent Document 4 proposes a method in which a vane section and a boss section (and a disk section) are joined to each other by friction welding. However, methods such as this that use different materials for different sections are problematic in terms of productivity and cost, and are currently not usable in industrial applications.
Patent Document 5 addresses the problem of using different materials by proposing a compressor impeller that can be cast from a single alloy, specifically an Al—Cu—Mg-base alloy for which the additive elements and the combination range of these elements are optimized. The resulting compressor impeller has a proof stress value of 250 MPa or more at 180° C. Patent Document 6 proposes improving the casting yield by controlling the crystal grain size of an Al—Cu—Mg-base alloy through optimization of the additive elements and the combination range of these elements. The compressor impeller has a proof stress value of 260 MPa or more at 200° C.
However, a problem remains that the products of the single alloy casting using the Al—Cu—Mg-base alloy still need to stably withstand high temperatures in the vicinity of 200° C. over extended time periods if these were to be used for ever faster turbochargers. Another unsolved problem is that the casting yield needs to be improved for stable production.
Patent Document 1: U.S. Pat. No. 4,556,528
Patent Document 2: JP-A-10-58119
Patent Document 3: JP-A-10-212967
Patent Document 4: JP-A-11-343858
Patent Document 5: JP-A-2005-206927
Patent Document 6: JP-A-2012-25986
The present invention has been made in view of the foregoing problems, and it is an object of the present invention to provide a compressor impeller cast from an aluminum alloy (hereinafter, “Al alloy”) that remains stably strong over extended time periods even under operating temperatures of about 200° C., and that excels in productivity. The invention is also intended to provide a method for producing such impellers.
With regard to the foregoing problems, the present inventors focused on the disc section of compressor impellers that receives high stress, and found that the strength of the disc section greatly improves when the intermetallic compounds at the end section of the disc section are finely dispersed. The present inventors also diligently studied a method of production for finely dispersing intermetallic compounds, and found that refining primary phase aluminum crystal grains is important for fine dispersal of intermetallic compounds, and that controlling the cooling rate of Al alloy molten metal, and controlling the distribution of refined particles in a compressor impeller are important to achieve this. The present invention was completed on the basis of these findings.
In claim 1, the present invention is directed to a compressor impeller cast from an Al alloy comprising a boss section, a plurality of vane sections and a disc section,
wherein the boss section, the plurality of vane sections, and the disc section excluding an end section comprise an Al alloy comprising Cu: 1.4 to 3.2 mass %, Mg: 1.0 to 2.0 mass %, Ni: 0.5 to 2.0 mass %, Fe: 0.5 to 2.0 mass %, Ti: 0.01 to 0.35 mass %, and B: 0.002 to 0.070 mass % and a balance of Al and unavoidable impurities,
wherein the end section of the disc section comprises an Al alloy comprising Cu: 1.4 to 3.2 mass %, Mg: 1.0 to 2.0 mass %, Ni: 0.5 to 2.0 mass %, Fe: 0.5 to 2.0 mass %, Ti: 0.005 to 0.175 mass %, and B: 0.001 to 0.035 mass % and a balance of Al and unavoidable impurities, and
wherein at least 10000/mm2 of intermetallic compounds having a circle-equivalent diameter of 1 to 6 μm, and no greater than 500/mm2 of intermetallic compounds having a circle-equivalent diameter exceeding 6 μm exist in the end section of the disc section.
In claim 2 of the present invention according to claim 1, the compressor impeller is for use in large-scale applications including ships, and the boss section has a height of 200 to 80 mm, the disc section has a diameter of 300 to 100 mm and the vane sections have a height of 180 to 60 mm with 30 to 10 vanes measuring 4.0 to 0.4 mm in thickness at a vane tip.
In claim 3 of the present invention according to claim 1, the compressor impeller is for use in small-scale applications including automobiles, and the boss section has a height of 100 to 20 mm, the disc section has a diameter of 120 to 25 mm, and the vane sections have a height of 90 to 5 mm with 20 to 4 vanes measuring 3.0 to 0.1 mm in thickness at a vane tip.
In claim 4, the present invention is directed to a method for producing a compressor impeller cast from an Al alloy, comprising:
a molten metal preparation step of preparing a 720 to 780° C. Al alloy molten metal comprising Cu: 1.4 to 3.2 mass %, Mg: 1.0 to 2.0 mass %, Ni: 0.5 to 2.0 mass %, Fe: 0.5 to 2.0 mass % and a balance of Al and unavoidable impurities, and adding a refining agent to the Al alloy molten metal to incorporate Ti: 0.01 to 0.35 mass % and B: 0.002 to 0.070 mass % in the alloy composition;
a casting step of casting an Al alloy casting by pressure casting whereby the Al alloy molten metal prepared is injected through a molten metal inlet into a space having a product shape configured from a plaster mold having the molten metal inlet at the bottom of the plaster mold, and a 100 to 250° C. chill disposed on a surface that contacts with an impeller disc surface, the space being formed by disposing the plaster mold and the chill so that the chill is at upper position and the plaster mold is at below position, and an inflow rate at the molten metal inlet into the space being 0.12 to 1.00 m/s;
a solution treatment step of solution treating by subjecting the Al alloy casting to a solution treatment; and
an aging treatment step of aging treating by subjecting the Al alloy casting to aging after the solution treatment.
In claim 5 of the present invention according to claim 4, the end section of the disc section has a cooling rate of 0.1 to 200° C./s in the casting step.
In claim 6 of the present invention according to claim 4 or claim 5, the Al alloy casting is heat treated for 2 hours or more at a temperature 5 to 25° C. below the solidus temperature of the Al alloy in the solution treatment step, and the solution-treated Al alloy casting is subjected to a heat treatment at 180 to 230° C. for 3 to 30 hours in the aging treatment step.
The present invention can provide an aluminum alloy cast impeller for compressors that shows stable high-temperature strength even in a high temperature range in the vicinity of 200° C. over extended time periods, and that has excellent productivity such as casting yield.
An embodiment of the present invention is described below in detail.
A. Features of Aluminum Alloy Cast Impeller for Compressors According to the Present Invention
After a series of various experimental studies conducted to solve the foregoing problems, the present inventors found that a compressor impeller that stably maintains excellent high-temperature strength over extended time periods without involving damage to the disc section can be obtained by optimizing the size and the surface density of intermetallic compounds at the end section of the disc section of the compressor impeller, even when the compressor impeller is used under high temperatures of about 200° C. It was also found that the size and the surface density of intermetallic compounds at the end section of the disc section of the compressor impeller can be optimized, and that the casting yield can improve from conventional yields by optimizing the Al alloy composition, controlling the cooling rate of casting through adjustments of molten metal temperature and chill temperature, and controlling the pour rate of molten metal into a compressor impeller mold.
As used herein, “stably maintain desirable high-temperature strength over extended time periods” means that deformation and fatigue failure do not occur over extended time periods even under operating temperatures of about 200° C. Specifically, it means that no damage occurs in a turbo assembly durability test conducted at 200° C. for 150,000 rpm×200 hours.
B. Shape of Al Alloy Cast Impeller for Compressors
C. Al Alloy Composition
The composition of the Al alloy used in the present invention is described below along with the reasons for limiting the Al alloy components.
C-1. Cu, Mg:
Cu and Mg dissolve into the Al matrix and show an effect that a mechanical strength is improved by the solid solution strengthening. By existing together, Cu and Mg also contribute to improving strength through precipitation strengthening such as by Al2Cu, and Al2CuMg. Because these two elements widen the solidification temperature range, excess addition of these elements is detrimental to castability.
When the Cu content is less than 1.4 mass % (hereinafter, simply referred to “%”), and/or Mg content is less than 1.00%, the required mechanical strength at high temperatures of around 200° C. may not be obtained. On the other hand, when the Cu content is above 3.2%, and/or Mg content is in excess of 2.0%, the castability of the compressor impeller is impaired, and may cause an underfill as the molten metal fails to sufficiently run into the vane end section in particular. For these reasons, the Cu content should preferably be 1.4 to 3.2%, and the Mg content should preferably be 1.0 to 2.0%. The Cu content is more preferably 1.7 to 2.8%, and the Mg content is more preferably 1.3 to 1.8% in terms of surely preventing defects such as deformation during use, and practically preventing generation of an underfill during casting and obtaining an industrially preferable yield.
C-2. Ni, Fe:
Ni and Fe form an intermetallic compound with Al, and disperse into the Al matrix to improve the high-temperature strength of the Al alloy. To this end, the Ni content should be 0.5% or more, and the Fe content should be 0.5% or more. However, when contained in excess, these elements not only coarsen the intermetallic compound, but reduce the amount of the solid solution Cu in the Al matrix, and lower strength by forming Cu2FeAl7 and Cu3NiAl6 at high temperatures. The presence of coarsened intermetallic compounds at the end section of the disc section causes damage to the compressor impeller as the intermetallic compounds become a starting point of damage under the repeatedly applied stress on the end section of the disc section, as will be described later. It is therefore preferable to contain Ni in a content of 2.0% or less, and Fe in a content of 2.0% or less. Taken together, the Ni content should preferably be 0.5 to 2.0%, and the Fe content should preferably be 0.5 to 2.0%. Preferably, the Ni content is 0.5 to 1.4%, and the Fe content is 0.7 to 1.5%. The lower limits of these preferred ranges are provided as indications for stably mass producing products in industrial settings by reducing production variation, whereas the upper limits are indications above which the effects will be saturated, and the elements will be wasted.
C-3. Ti, B:
Ti and B have the effect to inhibit the growth of primary phase aluminum crystal grains during casting, and are added to reduce the size of the solid structure in the casting, and improve the supply and the run of molten metal. These effects may not be sufficiently obtained when the Ti content is less than 0.01%, and/or the B content is less than 0.002% in the boss section, the vane sections, and the disc section other than the end section, or when the Ti content is less than 0.005%, and/or the B content is less than 0.001% in the end section of the disc section. On the other hand, the refining agent particles aggregate, and fatigue cracking occurs from the aggregates when the Ti content exceeds 0.35%, and/or the B content exceeds 0.070% in the boss section, the vane sections, and the disc section other than the end section, or when the Ti content exceeds 0.175%, and/or the B content exceeds 0.035% in the end section of the disc section. When contained in excess of 0.35% in these sections, Ti forms coarse intermetallic compounds of several ten to several hundred micrometers with Al. Such coarse intermetallic compounds become a starting point of fatigue cracking, and lowers the reliability of the compressor impeller. For these reasons, the Ti content should be 0.01 to 0.35%, and the B content should be 0.002 to 0.070%, preferably the Ti content is 0.15 to 0.30%, and the B content is 0.003 to 0.060% in the boss section, the vane sections, and the disc section other than the end section. At the end section of the disc section, the Ti content should be 0.005 to 0.175%, and the B content should be 0.001 to 0.035%, preferably the Ti content is 0.010 to 0.165%, and the B content is 0.002 to 0.033%.
The Al alloy may contain unavoidable impurities, such as about 0.3% or less of Si, and about 0.2% or less of each of Zn, Mn, and Cr. These unavoidable impurities are acceptable because these do not affect the characteristics of the compressor impeller.
D. Intermetallic Compound
The aluminum alloy used in the present invention is cast into a shape of the compressor impeller with a plaster mold by pressure casting (low-pressure casting, vacuum casting, or differential pressure casting) according to a conventional Al—Si aluminum alloy casting producing method.
In the pressure casting using a plaster mold, producing conditions need to be controlled with regard to the distribution of the inter metallic compounds inside each casting in such a manner that the number of intermetallic compounds having a circle-equivalent diameter of 1 to 6 μm is at least 10000/mm2 at the end section of the disc section, and that the number of intermetallic compounds having a circle-equivalent diameter exceeding 6 μm is no greater than 500/mm2 at the end section of the disc section.
After studying the damaging behavior of the compressor impeller, the present inventors found that end section of the disc section receives repeatedly occurring high normal stress due to acceleration and deceleration of compressor impeller rotation, and becomes damaged as the coarse intermetallic compounds having a circle-equivalent diameter exceeding 6 μm at the end section of the disc section become a starting point of cracking and develop cracks. After further studies, it was also found that cracking originating from such intermetallic compounds, and propagation of cracks, when present, can be inhibited when the intermetallic compounds having a circle-equivalent diameter exceeding 6 μm at the end section of the disc section has a surface density of no greater than 500/mm2. It was also found that generation of the coarse intermetallic compounds can be inhibited when the number of intermetallic compounds having a circle-equivalent diameter of 1 to 6 μm at the end section of the disc section is at least 10000/mm2.
The generated amounts of intermetallic compounds depend on the composition under typical casting conditions. Here, “under typical casting conditions” means under the cooling rate of low-pressure casting, specifically 0.1 to 200° C./s. Studies of intermetallic compound changes after a post-casting heat treatment revealed that the heat treatment does not have a large effect on the size of the intermetallic compounds generated during casting. By generating large amounts of fine intermetallic compounds during casting, it then becomes possible to inhibit generation of coarse intermetallic compounds in the subsequent heat treatment.
The reason that the intermetallic compounds having a circle-equivalent diameter of 1 to 6 μm are made to have a surface density of at least 10000/mm2 is as follows. Intermetallic compounds having a circle-equivalent diameter of less than 1 μm do not affect the compressor impeller strength. When the surface density of the intermetallic compounds having a circle-equivalent diameter of 1 to 6 μm is less than 10000/mm2, the generation of intermetallic compounds having a circle-equivalent diameter exceeding 6 μm accelerates, and cracking occurs from the generated intermetallic compounds having a circle-equivalent diameter exceeding 6 μm. The upper limit of the surface density is not particularly limited, and is determined by the composition of the Al alloy, and the producing conditions. In the present invention, the upper limit is 30000/mm2.
The reason that intermetallic compounds having a circle-equivalent diameter exceeding 6 μm is made to have a surface density of no greater than 500/mm2 is as follows. Intermetallic compounds having a circle-equivalent diameter exceeding 6 μm are of interest for the reason described above. When the surface density exceeds 500/mm2, cracking propagates as the distances between the intermetallic compounds become shorter. The lower limit of the surface density is not particularly limited, and depends on the composition of the Al alloy, and the producing conditions. In the present invention, the lower limit is preferably 100/mm2, most preferably 0/mm2.
Examples of the intermetallic compounds generated in the present invention include Al—Fe—Ni—Cu, Al—Fe—Cu—Ni—Mg, Al—Cu—Mg, Al—Cu, Al—Cu—Mg—Si, Al—Cu—Fe, Al—Ni, Al—Mg, and Mg—Si intermetallic compounds. The circle equivalent size of the generated intermetallic compounds has a distribution in a range of from 0.1 to 20.0 μm, though it depends on the composition of the Al alloy, and the producing conditions. As used herein, “circle equivalent size” means “circle equivalent diameter.”
E. Controlling Amounts of Refining Agent Components in End Section of Disc Section
Controlling the size of primary phase aluminum crystal grains is important in controlling the distribution of the intermetallic compounds. This is because the intermetallic compounds are generated at the grain boundary of primary phase aluminum crystal grains. Factors that are important in controlling the size of primary phase aluminum crystal grains are amounts of the refining agent components, and the cooling rate which will be described later.
The appropriate amounts of the Ti and B components in the end section of the disc section are 0.005 to 0.175% for Ti, and 0.001 to 0.035% for B. In order to achieve these refining agent contents, a refining agent comprised of Al, Ti, and B is added in the molten metal preparation step to make the amounts of the Ti and B components 0.01 to 0.35% and 0.002 to 0.070%, respectively, in the aluminum alloy molten metal after the molten metal preparation step. The product-shape space configured from the plaster mold and the chill is formed by vertically disposing these members so that the chill is higher in position than the plaster mold having a molten metal inlet at the bottom. The prepared Al alloy molten metal is poured into the space through the molten metal inlet. The molten metal is poured into the space at a pour rate of 0.12 to 1.00 m/s at the molten metal inlet. The casting step of pressure casting the Al alloy casting by injecting the prepared molten metal into the space is adapted to satisfy the foregoing requirements.
One of the reasons for specifying the foregoing requirements is that only a section of the refining agent amount in the molten metal preparation step reaches end section of the disc section under the effect of the molten metal flow inside the space. The present inventors have confirmed that this is due to the refining agent particles failing to follow the moving molten metal during pressure casting in accordance with the law of inertia. The following describes this in detail.
The refining agent comprised of Al, Ti, and B is added in the molten metal preparation step. When the amount of the Ti component is less than 0.01%, and/or the amount of the B component is less than 0.002% in the aluminum alloy molten metal after the molten metal preparation step, the primary phase aluminum crystal grains coarsen, which, in turn, coarsens the intermetallic compounds at the grain boundary to lower the strength of the Al alloy material. When the amount of the Ti component exceeds 0.35%, and/or the amount of the B component exceeds 0.070% in the aluminum alloy molten metal after the molten metal preparation step, coarse TiB2 aggregates are generated, and become a starting point of fracture. The amounts of the Ti and B components in the aluminum alloy molten metal after adding the refining agent in the molten metal preparation step are therefore 0.01 to 0.35% for Ti, and 0.002 to 0.070% for B.
The product-shape space configured from the plaster mold and the chill is described below. As shown in
Without the space 10 configured as above, balancing during high-speed rotations of the compressor impeller suffers as a result of the nonuniform solidification occurring in the circumferential direction of the compressor impeller, and operation of the device becomes limited as the casting machine becomes complex. For example, as shown
On the other hand, for example, as shown in
When the product-shape space 10 is formed by disposing the plaster mold 7 and the chill 6 as shown in
The pour rate of molten metal at the molten metal inlet is an important factor in controlling the refining agent content at the disc section end. As described above, the content of the refining agent particles comprised of Ti and B reaching the end section of the disc section decreases from the content of refining agent particles in the molten metal preparation step. This is due to the refining agent particles failing to follow the moving molten metal during pressure casting in accordance with the law of inertia. When the pour rate of molten metal at the molten metal inlet exceeds 1.00 m/s, the excessively fast pour rate of the molten metal makes it even more difficult for the inertial movement of the refining agent particles to follow the pour rate of the molten metal, and the refining agent particles cannot reach the end section of the disc section in amounts that are necessary for grain refining. On the other hand, when the pour rate of the molten metal at the molten metal inlet is less than 0.12 m/s, the excessively slow pour rate of the molten metal increases the time it takes for the molten metal to reach the plaster mold through the stalk. This lowers the molten metal temperature, and causes solidification failure. The pour rate of molten metal at the molten metal inlet is preferably 0.20 to 0.85 m/s.
F. Controlling Cooling Rate at End Section of Disc Section
In order to obtain the intermetallic compound distribution above, the cooling rate at the end section of the disc section of the compressor wheel needs to be controlled. Specifically, the molten metal temperature is controlled between 720 and 780° C., and the temperature of the chill (chill plate) disposed on the surface that contacts the compressor disc surface is controlled between 100 and 250° C. The cooling rate at the end section of the disc section is adjusted in a preferred range of 0.1 to 200° C./s by specifying the molten metal temperature and the chill temperature as above. When the cooling rate is less than 0.1° C./s, the primary phase aluminum crystal grain coarsens, which coarsens the intermetallic compounds generated at the grain boundary. Further, shrinkage cavity occurs, and productivity suffers as the cooling rate decreases. On the other hand, when the cooling rate is above 200° C./s, early solidification occurs inside the product-shape space. This causes misruns, and the intended product shape cannot be ensured. The cooling rate at the end section of the disc section is further preferably 3 to 150° C./s.
When the molten metal temperature is below 720° C., the injected molten metal solidifies early inside the product-shape space. This causes misruns, and the intended product shape cannot be ensured. On the other hand, with a molten metal temperature above 780° C., the molten metal progressively undergoes oxidation, and increased porosity numbers due to hydrogen gas absorption, and increased oxides impair the quality of the molten metal. This makes it difficult to ensure product strength.
When the chill temperature is below 100° C., solidification proceeds at an excessive rate, and misruns occur. On the other hand, when the chill temperature is above 250° C., solidification from the chill slows down, and the slow cooling rate coarsens the primary phase aluminum crystal grains, which coarsens the intermetallic compounds generated at the grain boundary. Further, a chill temperature above 250° C. causes burr defects, which occur when the molten metal enters between the plaster mold and the chill.
In the present invention, it is preferable to control the preheating temperature of the plaster mold between 200 and 350° C., though the temperature is not particularly limited. When the preheating temperature of the plaster mold is less than 200° C., solidification takes place before the charged molten metal fills the mold end. This causes misruns, and the intended product shape cannot be ensured. On the other hand, when the preheating temperature of the plaster mold exceeds 350° C., the solidification slows down inside the plaster mold, and a shrinkage cavity failure occurs.
The chill material is preferably copper or a copper alloy, which has high thermal conductivity. However, materials such as steel, and stainless steel also may be used. Preferably, the chill temperature is adjusted by using a mechanism by which superheating in the casting is reduced with a coolant such as water passed inside the chill.
G. Producing Method
A method for producing the Al alloy cast impeller for compressors according to the present invention is described below. The producing method includes a molten metal adjusting step, a casting step, and a heat treatment step.
Molten Metal Preparation Step:
Each component element is melted under heat to make the Al alloy composition above by using an ordinary method, and molten metal processes such as processing of dehydrogenated gas, and removal of inclusions are performed. The temperature is adjusted to make the final molten metal temperature 720 to 780° C. The hydrogen gas amount in the molten metal is also adjusted. A rotary gas blower is used to adjust the hydrogen gas amount in the molten metal. However, the method is not limited to this.
Casting Step:
In the casting step, the molten metal adjusted to 720 to 780° C. is cast into a shape of the compressor impeller by pressure casting using a plaster mold. As described above, the temperature of the chill disposed on the surface that contacts the disc surface is adjusted to 100° C. to 250° C. As for the product-shape space configured from the plaster mold and the chill, the product-shape space configured from the plaster mold and the chill is formed by vertically disposing these members so that the chill is higher in position than the plaster mold, as shown in
Heat Treatment Step:
The Al alloy casting is subjected to a heat treatment step. The heat treatment step includes a solution treatment step and an aging treatment step. The heat treatment step can effectively take advantage of the solid solution strengthening by Cu; the precipitation strengthening by Cu and Mg; and the dispersion strengthening by the intermetallic compounds formed by Al and Fe and by Al and Ni.
Solution Treatment Step:
The solution treatment is performed preferably in a temperature range that is 5 to 25° C. lower than the solidus temperature. In the preferred Al alloys for use in the present invention, a temperature range of 510 to 530° C. represents such a temperature range that is 5 to 25° C. lower than the solidus temperature. The risk of melting the second phase of crystal grain boundaries increases, and it becomes difficult to ensure strength at temperatures above the temperature range that is 5 to 25° C. lower than the solidus temperature. On the other hand, the elements do not diffuse sufficiently, and the solution treatment becomes insufficient at temperatures below the temperature range that is 5 to 25° C. lower than the solidus temperature. Preferably, the solution treatment is performed for at least 2 hours. The elements do not diffuse sufficiently, and the solution treatment becomes insufficient when the solution treatment is less than 2 hours. Considering mass production, the solution treatment by element diffusion is performed for preferably 30 hours or less, though the treatment time is not particularly limited as long as the solution treatment is performed for at least 2 hours.
Aging Treatment:
The aging treatment involves a heat treatment performed preferably at 180 to 230° C. for 3 to 30 hours, more preferably 190 to 210° C. for 5 to 20 hours. The precipitation strengthening for improving strength may become insufficient when the process temperature is below 180° C., or when the process time is less than 3 hours. On the other hand, the precipitated phase formed may coarsen (overaging), and may fail to provide a sufficient strengthening effect, and the solid solution strengthening capability of Cu weakens when the process temperature exceeds 230° C., or when the process time exceeds 30 hours.
H. Shape of Compressor Wheel
The shape and the dimensions of the compressor impeller according to the present invention, and the number of vanes of the compressor impeller are not particularly limited, and the compressor impeller is applicable to many different applications, ranging from large-scale applications such as ships to small-scale applications such as automobiles. Taking a large scale application such as ships as an example, the boss section has a height of 200 to 80 mm, preferably 180 to 100 mm, the disc section has a diameter of 300 to 100 mm, preferably 260 to 120 mm, and the vane sections have a height of 180 to 60 mm, preferably 160 to 90 mm. The thickness at the tip of the vane is 4.0 to 0.4 mm, preferably 3.0 to 0.6 mm. The number of vanes is 30 to 10, preferably 26 to 12. In the case of smaller applications such as automobiles, the boss section has a height of 100 to 20 mm, preferably 90 to 25 mm, the disc section has a diameter of 120 to 25 mm, preferably 100 to 30 mm, and the vane sections have a height of 90 to 5 mm, preferably 80 to 8 mm. The thickness at the tip of the vane is 3.0 to 0.1 mm, preferably 2.0 to 0.2 mm. The number of vanes is 20 to 4, preferably 18 to 6.
The present invention is described below in greater detail using Examples.
Each Al alloy of the composition shown under the column “Components” in Table 1 was melted by using a common molten metal process, and the molten metal was adjusted to the temperature shown in Table 1 by a molten metal preparation step. In the molten metal preparation step, 150 kg of the Al alloy of the composition shown under the column “Components” in Table 1 was melted to obtain a molten metal. Thereafter, a blow degassing process was performed by blowing argon gas into the molten metal for 30 minutes with a rotary gas blower operated at a rotation speed of 400 rpm, and a gas flow rate of 2.5 Nm3/h. The whole molten metal was held still for 1 hour to remove the slag. After the slag removal, a refining agent was added to the molten metal in the metal preparation step to make the amounts of Ti and B components as shown under the column “Amounts of refining agent components after molten metal preparation” in Table 1.
The Al alloy molten metal prepared in the molten metal preparation step was then subjected to low-pressure casting to produce an Al alloy casting, whereby the molten metal was pressure injected into a predetermined space configured from a plaster mold that had been adjusted to 250° C., and a copper chill that had been adjusted to the temperature shown in Table 1 and disposed on the surface that contacts the impeller disc surface. Here, the molten metal was injected through the molten metal inlet provided at the bottom of the lower plaster mold (
The Al alloy casting was removed from the plaster mold, and subjected to a solution treatment at 530° C. for 8 hours, and thereafter to an aging treatment at 200° C. for 20 hours. In this way, a sample Al alloy cast impeller for compressors was prepared.
The samples produced in the manner described above were each evaluated with respect to the surface density of intermetallic compounds having a circle equivalent size of 1 to 6 μm at the end section of the disc section, the surface density of intermetallic compounds having a circle equivalent size of more than 6 μm at the end section of the disc section, amounts of the refining agent components (Ti, B) at the end section of the disc section, amounts of the refining agent components (Ti, B) in sections other than the end section of the disc section, high-temperature characteristics (durability test evaluation), and productivity (casting yield evaluation), as follows.
1. Surface Density Measurement of Intermetallic Compounds
The samples were cut along the central axis to determine the size and the surface density of intermetallic compounds at the end section of the disc section.
2. Measurement of Refining Agent Component Amounts
The refining agent content was measured at the end section of the disc section, and in sections other than the end section of the disc section. 5 g of sample was collected for analysis from the end section 31 of the disc section, the boss section 2, the vane section 4, and the disc section 32 other than the end section shown in
3. High Temperature Characteristics
High-temperature fatigue strength was evaluated in a high-temperature durability test (turbo assembly; 150,000 rpm×200 h, outlet temperature 200° C.). The results are presented in Table 2. The durability test evaluation results in Table 2 followed the following notation.
Poor: Fractured
Acceptable: No fracture, but cracking is occurred
Good: No fracture or cracking, and the sample remained intact
The parentheses following Acceptable and Poor indicate the location of the occurred cracks and fractures.
4. Casting Yield Evaluation
Casting yield was evaluated for 1,000 samples produced in each Example. Each sample was tested for external appearance failure due to misruns and shrinkage cavity failure, and internal failure based on the detected internal blow holes in an X-ray examination. The proportions (%) of samples with misruns, shrinkage cavity failure, and internal failure in all samples were determined. The proportion (%) of non-defective products was then determined by subtracting the sum of the proportions of these defective products from the total 100%. The results are presented in Table 2.
Poor: The proportion of non-defective products is less than 90% (worse than in existing products)
Acceptable: The proportion of non-defective products is 90% or more and less than 95% (same as in existing products)
Good: The proportion of non-defective products is 95% to 100% (great improvement over existing products)
In Present Examples 1 to 7, the surface density of intermetallic compounds having a circle equivalent size of 1 to 6 μm at the end section of the disc section, the surface density of intermetallic compounds having a circle equivalent size of more than 6 μm at the end section of the disc section, and the refining agent contents in the end section of the disc section and in sections other than the end section fell in the specified ranges, and because of this, the high-temperature characteristics, and the casting yield were both desirable.
In Comparative Example 1, with a high chill temperature, the surface density was low in the intermetallic compounds having a circle equivalent size of 1 to 6 μm at the end section of the disc section, and was high in the intermetallic compounds having a circle equivalent size of more than 6 μm at the end section of the disc section. Because of this, fracture occurred at the end section of the disc section, and the sample was inferior in terms of high-temperature characteristics. Further, multiple shrinkage cavity failures occurred at the boss section, and the casting yield was considerably poor.
In Comparative Example 2, with a low chill temperature, multiple defects occurred in the appearance of the disc section due to misruns, and the casting yield was poor.
In Comparative Example 3, there was a decrease in the molten metal temperature. As a result, multiple defects occurred in the appearance of the vane sections due to misruns and shrinkage cavity, and the casting yield was considerably poor. Further, cracking occurred in the vane sections, and the high-temperature characteristics were poor.
In Comparative Example 4, the molten metal temperature was high, and the cooling rate was low. The surface density was therefore low in the intermetallic compounds having a circle equivalent size of 1 to 6 μm at the end section of the disc section. As a result, multiple defects occurred in the appearance of the boss section due to shrinkage cavity, and the casting yield was considerably poor. Further, cracking occurred in the end section of the disc section, and the high-temperature characteristics were poor.
In Comparative Example 5, with the low Cu content, the high-temperature characteristics were desirable. However, there was a high incidence of misruns in the vane sections, and the casting yield was poor.
In Comparative Example 6, with the low Mg content, cracking occurred in the boss section, and the high-temperature characteristics were poor.
In Comparative Example 7, with the low Fe content, cracking occurred in the vane sections, and the high-temperature characteristics were poor.
In Comparative Example 8, with the low Ni content, fracture occurred in the disc section, and the high-temperature characteristics were poor.
In Comparative Example 9, with the small amount of refining agent component (B) in the molten metal preparation, the amounts of the Ti and B components became small in the end section of the disc section, and in sections other than the end section of the disc section. The grain refining effect was therefore insufficient, and the surface density was low in the intermetallic compounds having a circle equivalent size of 1 to 6 μm in the end section of the disc section, and was high in the intermetallic compounds having a circle equivalent size of more than 6 μm. As a result, multiple defects occurred in the appearance of the vane sections due to misruns, and the casting yield was considerably poor. Further, fracture occurred in the disc section, and the high-temperature characteristics were poor.
In Comparative Example 10, with the high Cu content, fracture occurred in the disc section, and high-temperature characteristics were poor.
In Comparative Example 11, with the high Mg content, multiple misruns occurred in the vane sections, and the casting yield was poor, though the high-temperature characteristics were desirable.
In Comparative Example 12, with the high Fe content, the intermetallic compounds having a circle equivalent size of more than 6 μm had a high surface density. Because of this, cracking occurred in the disc section, and the high-temperature characteristics were poor.
In Comparative Example 13, with the high Ni content, the intermetallic compounds having a circle equivalent size of more than 6 μm had a high surface density. Because of this, cracking occurred in the disc section, and the high-temperature characteristics were poor.
In Comparative Example 14, the amounts of the Ti and B components were high in sections other than the end section of the disc section because of the large amounts of the Ti and B components in the molten metal preparation, and the high pour rate of molten metal into the space mold (here and below, “space mold” refers to the product-shape space configured from the plaster mold and the chill). Because of this, fracture occurred in the boss section, and the high-temperature characteristics were poor. There was also a disturbed molten metal flow in the space mold, and the casting yield was considerably poor because of multiple internal failures.
In Comparative Example 15, the amounts of the Ti and B components in the end section of the disc section were small (0%) because of the high pour rate of molten metal into the space mold, though the amounts of the Ti and B components in the molten metal preparation were in the specified ranges. Because of this, the grain refining effect was insufficient, and the surface density was low in the intermetallic compounds having a circle equivalent size of 1 to 6 μm in the end section of the disc section, and was high in the intermetallic compounds having a circle equivalent size of more than 6 μm. As a result, fracture occurred in the disc section, and the high-temperature characteristics were poor. There was also a disturbed molten metal flow in the space mold, and the casting yield was considerably poor because of multiple internal failures.
In Comparative Example 16, because of the large amounts of the Ti and B components in the molten metal preparation, the amounts of the Ti and B components were large in the end section of the disc section, and in sections other than the end section of the disc section. This caused aggregation of refining agent particles. Further, fracture occurred in the disc section, and the high-temperature characteristics were poor.
In Comparative Example 17, because of the slow pour rate of molten metal into the plaster mold, the molten metal temperature decreased in the process of delivering the molten metal to the plaster mold. This caused multiple failures in the appearance of the vane sections due to misruns, and the casting yield was considerably poor. Further, cracking occurred in the vane sections, and the high-temperature characteristics were poor.
In Comparative Example 18, because of the high pour rate of molten metal into the plaster mold, the inertial movement of the refining agent particles had difficulties following the pour rate of the molten metal. Because of this, the Ti content was low in the end section of the disc section, and the refining agent particles failed to reach the end section of the disc section in sufficient amounts. Refining of crystal grains therefore did not take place, and coarse intermetallic compounds were created. This caused cracking in the end section of the disc section, and the high-temperature characteristics were poor. There was also a disturbed molten metal flow in the space mold, and the casting yield was considerably poor because of multiple internal failures.
In Comparative Example 19, because of the lateral pour direction of molten metal into the space mold, nonuniform solidification occurred in the circumferential direction of the compressor impeller. This caused cracking in the boss section due to an axial runout, and the high-temperature characteristics were poor. Further, because the molten metal was nonuniformly charged into the space mold, multiple internal failures occurred, and the casting yield was considerably poor.
In Comparative Example 20, because of the downward pour direction of molten metal into the space mold, the molten metal temperature decreased in the process of delivering the molten metal to the plaster mold. This caused multiple failures in the appearance of the disc section due to misruns, and the casting yield was considerably poor. Further, cracking occurred in the disc section, and the high-temperature characteristics were poor.
Each Al alloy of the composition shown under the column “Components” in Table 3 was melted by using a common molten metal process, and the molten metal was adjusted to the temperature shown in Table 3 by a molten metal preparation step. In the molten metal preparation step, 150 kg of the Al alloy of the composition shown under the column “Components” in Table 3 was melted to obtain a molten metal. Thereafter, a blow degassing process was performed by blowing argon gas into the molten metal for 20 minutes with a rotary gas blower operated at a rotation speed of 400 rpm, and a gas flow rate of 2.5 Nm3/h. The whole molten metal was held still for 1 hour to remove the slag. After the slag removal, a refining agent was added to the molten metal in the metal preparation step to make the amounts of the Ti and B components as shown under the column “Amounts of refining agent components after molten metal preparation” in Table 3.
The Al alloy molten metal prepared in the molten metal preparation step was then subjected to low-pressure casting to produce an Al alloy casting, whereby the molten metal was pressure injected into a predetermined space configured from a plaster mold that had been adjusted to 220° C., and a copper chill that had been adjusted to the temperature shown in Table 3 and disposed on the surface that contacts the impeller disc surface. The Al alloy casting was intended as a turbocharger compressor impeller for trucks, and had a shape with a disc section measuring 80 mm in diameter, a boss section measuring 70 mm in height, vane sections measuring 60 mm in height and having 14 vanes that were 0.4 mm in thickness at the vane tip. As shown in
The Al alloy casting was removed from the plaster mold, and subjected to a solution treatment under the conditions shown in Table 3, and thereafter an aging treatment under the conditions of Table 3. In this way, a sample Al alloy cast impeller for compressors was prepared.
The samples produced in the manner described above were each evaluated in the same manner as in First Example with respect to the surface density of intermetallic compounds having a circle equivalent size of 1 to 6 μm at the end section of the disc section, the surface density of intermetallic compounds having a circle equivalent size of more than 6 μm at the end section of the disc section, amounts of the refining agent components (Ti, B) at the end section of the disc section, amounts of the refining agent components (Ti, B) in sections other than the end section of the disc section, high-temperature characteristics (durability test evaluation), and productivity (casting yield evaluation). The results are presented in Table 4. For high-temperature characteristics, samples that scored “Good” in the evaluation of First Example were further tested for 100 hours for a total of 300 hours under the same conditions (turbo assembly, 150000 rpm, output temperature 200° C.). Samples that produced desirable results after the 300-hour test were evaluated as “Excellent.”
In Present Examples 8 to 18, the surface density of intermetallic compounds having a circle equivalent size of 1 to 6 μm at the end section of the disc section, the surface density of intermetallic compounds having a circle equivalent size of more than 6 μm at the end section of the disc section, and the amounts of the refining agent components in the end section of the disc section and in sections other than the end section fell in the specified ranges, and because of this, the high-temperature characteristics, and the casting yield were both desirable.
On the other hand, in Comparative Example 21, the molten metal temperature was low, and the casting yield was poor with multiple failures occurring in the appearance of the vane sections due to misruns. Further, cracking occurred in the vane sections, and the high-temperature characteristics were poor.
In Comparative Example 22, the molten metal temperature was high, and the cooling rate was low. The surface density was therefore low in the intermetallic compounds having a circle equivalent size of 1 to 6 μm at the end section of the disc section, and was high in the intermetallic compounds having a circle equivalent size of more than 6 μm at the end section of the disc section. This caused multiple failures in the appearance of the boss section due to shrinkage cavity, and the casting yield was considerably poor. Further, fracture occurred in the disc section, and the high-temperature characteristics were poor.
In Comparative Example 23, with a low chill temperature, multiple misruns occurred in the disc section, and the casting yield was poor. Further, cracking due to misruns occurred in the disc, and the high-temperature characteristics were poor.
In Comparative Example 24, the chill temperature was high, and the surface density was low in the intermetallic compounds having a circle equivalent size of 1 to 6 μm at the end section of the disc section, and was high in the intermetallic compounds having a circle equivalent size of more than 6 μm at the end section of the disc section. This caused fractures in the disc section, and the high-temperature characteristics were poor.
The solution treatment step was not performed in Comparative Example 25. The aging treatment step was not performed in Comparative Example 26. As a result, fracture occurred in the disc section, and the high-temperature characteristics were poor.
Each Al alloy of the composition shown under the column “Components” in Table 5 was melted by using a common molten metal process, and the molten metal was adjusted to the temperature shown in Table 5 by a molten metal preparation step. In the molten metal preparation step, 200 kg of the Al alloy of the composition shown under the column “Components” in Table 5 was melted to obtain a molten metal. Thereafter, a blow degassing process was performed by blowing argon gas into the molten metal for 40 minutes with a rotary gas blower operated at a rotation speed of 400 rpm, and a gas flow rate of 2.5 Nm3/h. The whole molten metal was held still for 1.5 hours to remove the slag. After the slag removal, a refining agent was added to the molten metal in the metal preparation step to make the amounts of the Ti and B components as shown under the column “Amounts of refining agent components after molten metal preparation” in Table 5.
The Al alloy molten metal prepared in the molten metal preparation step was then subjected to low-pressure casting to produce an Al alloy casting, whereby the molten metal was pressure injected into a predetermined space configured from a plaster mold that had been adjusted to 220° C., and a copper chill that had been adjusted to the temperature shown in Table 5 and disposed on the surface that contacts the impeller disc surface. The Al alloy casting was intended as a turbocharger compressor impeller for ships, and had a shape with a disc section measuring 150 mm in diameter, a boss section measuring 160 mm in height, vane sections measuring 120 mm in height and having 16 vanes that were 0.6 mm in thickness at the vane tip. As shown in
The Al alloy casting was removed from the plaster mold, and subjected to a solution treatment under the conditions shown in Table 5, and thereafter to an aging treatment under the conditions of Table 5. In this way, a sample Al alloy cast impeller for compressors was prepared.
The samples produced in the manner described above were each evaluated in the same manner as in First Example with respect to the surface density of intermetallic compounds having a circle equivalent size of 1 to 6 μm at the end section of the disc section, the surface density of intermetallic compounds having a circle equivalent size of more than 6 μm at the end section of the disc section, amounts of the refining agent components (Ti, B) at the end section of the disc section, amounts of the refining agent components (Ti, B) in sections other than the end section of the disc section, high-temperature characteristics (durability test evaluation), and productivity (casting yield evaluation). The results are presented in Table 6.
In Present Examples 19 to 28, the surface density of intermetallic compounds having a circle equivalent size of 1 to 6 μm at the end section of the disc section, the surface density of intermetallic compounds having a circle equivalent size of more than 6 at the end section of the disc section, and the amounts of the refining agent components in the end section of the disc section and in sections other than the end section fell in the specified ranges, and the high-temperature characteristics, and the casting yield were both desirable.
On the other hand, in Comparative Example 27, the molten metal temperature was high, and the cooling rate was low. The surface density was therefore low in the intermetallic compounds having a circle equivalent size of 1 to 6 μm at the end section of the disc section, and was high in the intermetallic compounds having a circle equivalent size of more than 6 μm at the end section of the disc section. This caused multiple failures in the appearance of the boss section due to shrinkage cavity, and the casting yield was considerably poor. Further, fracture occurred in the disc section, and the high-temperature characteristics were poor.
In Comparative Example 28, the molten metal temperature was low, and the casting yield was poor with multiple failures occurring in the appearance of the vane sections due to misruns. Further, cracking occurred in the vane sections, and the high-temperature characteristics were poor.
In Comparative Example 29, with the low chill temperature, multiple misruns occurred in the disc section, and the casting yield was poor. Further, cracking due to misruns occurred in the disc, and the high-temperature characteristics were poor.
In Comparative Example 30, the chill temperature was high, and the surface density was low in the intermetallic compounds having a circle equivalent size of 1 to 6 μm at the end section of the disc section, and was high in the intermetallic compounds having a circle equivalent size of more than 6 μm at the end section of the disc section. This caused fractures in the disc section, and the high-temperature characteristics were poor.
The solution treatment step was not performed in Comparative Example 31, and the aging treatment step was not performed in Comparative Example 32. As a result, the disc section was damaged, and high-temperature characteristics was poor.
The present invention enables inexpensively providing an Al alloy impeller for compressors that has excellent high-temperature strength, and that can stably withstand an increasing of temperatures due to an increasing of number of rotations over extended time periods. The present invention is also industrially very effective in that the output power of an internal combustion engine can be improved by increasing the supercharge ability of a turbocharger.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2014-052840 | Mar 2014 | JP | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/JP2015/001340 | 3/11/2015 | WO | 00 |
