WO2010087605A2 - Heat resistant aluminum alloy, and method for manufacturing same - Google Patents

Abstract

The present invention relates to a heat resistant aluminum alloy in which two types of alloy elements are bonded to aluminum while forming a homogeneous solid solution strengthening phase. The heat resistant aluminum alloy according to the present invention has innovative heat resistant properties in that the alloy elements cooperate to form a homogeneous solid solution, and the homogeneous solid solution strengthening phase, which is formed to have no solvus line with respect to the aluminum serving as a matrix metal, is not coarsened or phase-decomposed by the reaction to the aluminum even at the high temperature of 300°C.

Description

Heat-resistant aluminum alloy and its manufacturing method

The present invention relates to a heat-resistant aluminum alloy and a method for manufacturing the same, and more particularly, aluminum and a solid solution having no solid solution or having a solid solution of less than 1% by weight are added to each other. It relates to a manufacturing method.

In general, heat-resistant aluminum alloys developed to date are phase transformations of Al-Si-transition intermetallic compounds or Al-X (Fe, Cu, Cr, Mn, Ti) intermetallic compounds from liquid to solid phase on aluminum and aluminum alloy bases. By controlling the dispersion in the form of a crystallized phase formed during solidification and a precipitated phase formed in a solid phase through heat treatment, heat resistance characteristics are realized.

However, the alloy that has improved the heat resistance characteristics by the crystallization and precipitation of the intermetallic compound on the aluminum and aluminum alloy base as described above has a problem that the heat resistance properties are deteriorated in an environment of 200 ℃ or more.

1 is a conceptual diagram showing the high temperature behavior of elements added to a conventional heat-resistant aluminum alloy, as shown in the conventional heat-resistant aluminum alloy to maintain the thermodynamic equilibrium of the crystallized and precipitated intermetallic compound is maintained for more than 200 ℃ In order to form a new intermediate phase by reacting with a known aluminum, or coarsening of intermetallic compounds, there is a problem that occurs the generation and transition of the crack, this is because the heat-resistant properties are deteriorated is limited to use in the environment above 200 ℃.

Meanwhile, in the case of an aluminum composite material, nitrides, borides, oxides, and carbides are dispersed in a reinforced phase on the base of an aluminum alloy to realize heat resistance characteristics. Such an aluminum matrix composite material has better heat resistance than a heat resistant alloy using an intermetallic compound.

However, these aluminum matrix composites are difficult to control the reinforcement phase uniformly, and there is no price competitiveness in the case of composite materials using powder, and when the interfacial reaction between the base metal aluminum and the aluminum alloy and the reinforcement phase occurs, the characteristics are drastically reduced. There is an underlying problem that is degraded.

That is, the intermetallic compound and the composite material-reinforced phase control heat-resistant alloy as described above reacts to unnecessary reactions of the intermetallic compound or the reinforcement phase exhibiting heat resistance at a high temperature of 200 ° C. or more, and thus the heat resistance of the heat-resistant alloy rapidly decreases. There was a problem.

In addition, most commercial aluminum alloys, including heat-resistant aluminum alloys developed to date, contain more than 10 additional elements. Therefore, when aluminum alloys are recycled, it is difficult to actively select them due to unnecessary reaction between aluminum and the additive elements. Because of this, there are restrictions on recycling.

The present invention is to solve the above problems,

It is an object of the present invention to provide a heat-resistant aluminum alloy and a method of manufacturing the same, which use a alloy element free of aluminum and a solid solution to form a stable reinforcement phase which is not coarsened or phase-decomposed by reaction with aluminum, which is a base metal, at a high temperature.

It is another object of the present invention to provide an alloying element content capable of maintaining a stable reinforcement phase.

The present invention to achieve the above object,

It is to provide a heat-resistant aluminum alloy characterized in that the two kinds of alloying elements that do not have a solid solution with aluminum in aluminum and form a tremor solid solution.

In addition, the alloy element is characterized in that it contains 0.5% to 10% by weight relative to aluminum.

In addition, after the alloy element is added to the molten aluminum molten aluminum, and the alloy element is melted to provide a manufacturing method for producing a heat-resistant aluminum alloy, characterized in that the casting.

1 is a conceptual diagram showing the high temperature behavior of elements added to a conventional heat-resistant aluminum alloy.

Figure 2 is a conceptual diagram showing the stable high temperature behavior of the modulus solid-solid strengthening phase formed in the heat-resistant aluminum alloy according to the present invention.

Figures 3 to 10 are binary state diagrams according to the type of alloying elements, Figure 3 is chromium and tungsten, Figure 4 is copper and nickel, Figure 5 is iron and chromium, Figure 6 is iron and manganese, Figure 7 is manganese and vanadium 8 shows cobalt and nickel, FIG. 9 shows iron and nickel, and FIG. 10 shows copper and manganese.

Figure 11 is an optical microscope histogram of observing the microstructure of the specimen prepared in Preparation Example 1.

12 to 14 are photographs showing the results of mapping the microstructure of the specimens prepared in Preparation Examples 1 to 3 to an Electron Probe Micro-Analyzer (EPMA). FIG. 12 is Preparation Example 1 and FIG. Preparation Example 2, Figure 14 is for Preparation Example 3.

15 is a photograph of the specimen prepared in Preparation Example 1 after the heat treatment at 300 ℃ for 200 hours, the microstructure of the heat-treated specimen with an optical microscope.

Figure 16 is a photograph of the microstructure of the specimens cast after remelting of the specimen prepared in Preparation Example 1 with an optical microscope.

Figure 17 is a graph showing the average size of the electrolytic solid solution according to the content of the alloying elements added to each of the specimens prepared in Preparation Example 4.

18 is a photograph showing an optical microscope histology of observing the microstructure of the specimen prepared in Preparation Example 5.

19 is a photograph showing the results of mapping the microstructure of the specimen prepared in Preparation Example 5 with an Electron Probe Micro-Analyzer (EPMA).

 20 is a photograph showing the results of observing the microstructure of the heat-treated specimen after annealing the specimen prepared in Preparation Example 5 at 300 ℃ for 200 hours.

Figure 21 is a photograph of the microstructure of the specimens cast after remelting of the specimen prepared in Preparation Example 5 with an optical microscope.

22 is a graph showing the average size of the electrification solid solution according to the content of the alloying elements added to each specimen prepared in Preparation Example 6.

Figure 23 is an optical microscope histology of observing the microstructure of the specimen prepared in Preparation Example 7.

24 is a photograph showing the results of mapping the microstructure of the specimen prepared in Preparation Example 7 with an Electron Probe Micro-Analyzer (EPMA).

FIG. 25 is a photograph of the specimen prepared in Preparation Example 7 after heat treatment at 300 ° C. for 200 hours, followed by optical microscopy of the microstructure of the specimen.

Figure 26 is a photograph of the microstructure of the specimens cast after remelting of the specimen prepared in Preparation Example 7 with an optical microscope.

27 is an optical microscope histogram of observing the microstructure of the specimen prepared in Preparation Example 8.

28 is a photograph showing the results of mapping the microstructure of the specimen prepared in Preparation Example 8 with an Electron Probe Micro-Analyzer (EPMA).

29 is a photograph showing the results of observing the microstructure of the heat-treated specimen after annealing the specimen prepared in Preparation Example 8 at 300 ° C. for 200 hours.

30 is a photograph of a microscopic observation of the microstructure of the cast specimen after remelting of the specimen prepared in Preparation Example 8. FIG.

Figure 31 is a graph showing the average size of the electrolytic solid solution according to the content of the alloying elements added to each specimen prepared in Preparation Example 9.

32 is an optical microscope histogram of observing the microstructure of the specimen prepared in Preparation Example 10.

33 is a photograph showing the results of mapping the microstructure of the specimen prepared in Preparation Example 10 with an Electron Probe Micro-Analyzer (EPMA).

FIG. 34 is a photograph of the specimen prepared in Preparation Example 10 after heat treatment at 300 ° C. for 200 hours, followed by optical microscopy of the microstructure of the specimen.

35 is a photograph of the microstructure of the specimens cast after remelting of the specimen prepared in Preparation Example 10 by optical microscope.

 36 is a graph showing the average size of the electrolytic solid solution according to the content of the alloying elements added to each specimen prepared in Preparation Example 11.

37 is an optical microscope histogram of observing the microstructure of the specimen prepared in Preparation Example 12.

FIG. 38 is a photograph showing the results of mapping the microstructure of the specimen prepared in Preparation Example 12 to an Electron Probe Micro-Analyzer (EPMA). FIG.

FIG. 39 is a photograph of the specimen prepared in Preparation Example 12 after heat treatment at 300 ° C. for 200 hours, followed by optical microscopy of the microstructure of the specimen.

40 is a photograph of a microscopic observation of a microstructure of a cast specimen after remelting of the specimen prepared in Preparation Example 12. FIG.

FIG. 41 is a graph showing the average size of an electrifying solid solution according to the content of alloying elements added to each specimen prepared in Preparation Example 13. FIG.

FIG. 42 is a light microscope histogram of observing microstructure of a specimen prepared in Preparation Example 14. FIG.

43 is a photograph showing the results of mapping the microstructure of the specimen prepared in Preparation Example 14 to an Electron Probe Micro-Analyzer (EPMA).

Figure 44 is a photograph showing the results of observing the microstructure of the heat-treated specimen after the heat treatment of the specimen prepared in Preparation Example 200 at 300 ℃ 200 hours.

45 is a photograph of the microstructure of the specimens cast after remelting of the specimens prepared in Preparation Example 14 with an optical microscope.

46 is a graph showing the average size of the electrolytic solid solution according to the content of the alloying elements added to each specimen prepared in Preparation Example 15.

47 is a photograph showing an optical microscope histogram of observing the microstructure of the specimen prepared in Preparation Example 16.

48 is a photograph showing the results of mapping the microstructure of the specimen prepared in Preparation Example 16 with an Electron Probe Micro-Analyzer (EPMA).

FIG. 49 is a photograph showing the results of observing the microstructure of the heat-treated specimen after optical treatment at 300 ° C. for 200 hours at 300 ° C.

50 is a photograph of the microstructure of the specimens cast after remelting prepared in Preparation Example 16 by optical microscope

51 is a graph showing the average size of the electrification solid solution according to the content of the alloying elements added to each specimen prepared in Preparation Example 17.

Hereinafter, the present invention will be described in more detail.

Figure 2 is a conceptual diagram showing a stable high temperature behavior of the thermal solid solution strengthening phase formed in the heat-resistant aluminum alloy according to the present invention, as shown in Figure 2 is a heat-resistant aluminum alloy of the present invention to form the thermal solid solution with aluminum while It is characterized by the fact that it does not decompose or coarsen even at high temperatures through alloying elements that have no solid solution or a solid solution of less than 1%.

That is, the present invention relates to a heat-resistant aluminum alloy in which two kinds of alloying elements that form a thermally solid solution in aluminum are combined to form a thermally solid solution reinforced phase. These heat-resistant aluminum alloys do not form a solid solution with aluminum or have a solid solution of less than 1%. However, the heat-resistant aluminum alloy does not form a compound between aluminum and metal even when added to form a thermodynamically stable electrolytic solid-reinforced phase present as a single phase. Use what you have.

Accordingly, even at a high temperature of 200 ° C. or higher, the tempering solid-solution reinforcement phase does not react with aluminum, the reinforcing phase is not decomposed or coarsened, and even when the melting point of the aluminum is heated, the tremor solids formed in the aluminum may be stably present. In addition, even if the molten heat-resistant aluminum alloy is remelted, the formed solid-solution solid phase may be present stably. This effect can be confirmed through the experimental results described below.

In the present invention, chromium (Cr) and tungsten (W) may be preferably used as the two kinds of alloying elements. The electrified solidified solid phase formed of an alloy element of chromium and tungsten maintains a stable single phase even at temperatures up to 1800 ° C., and has a size of 1 to 200 μm.

In addition, copper (Cu) and nickel (Ni) may be preferably used as the two kinds of alloying elements. The temporal solid solution strengthening phase formed of an alloying element of copper and nickel is stable even at temperatures up to 873 ° C., and has a grain boundary interface shape of 1 to 50 μm.

In addition, the two kinds of alloying elements may be used iron (Fe) and chromium (Cr). The electrified solid-solid reinforced phase made of iron and chromium maintains a stable single phase even at temperatures up to 1500 ° C., and has a facet shape of 1 to 60 μm in size.

In addition, the two kinds of alloying elements may be iron (Fe) and manganese (Mn). The electrified solidified solid phase composed of iron and manganese has heat resistance even at temperatures up to 1245 ° C., and is formed in a facet shape having a size of 1 to 50 μm.

In addition, the two kinds of alloying elements may be used manganese (Mn) and vanadium (V). The electrified solid-solution strengthening phase formed of manganese and vanadium maintains a stable single phase even at a temperature up to 1245 ° C., and may have a facet shape having a size of 1 to 100 μm.

In addition, the two kinds of alloying elements may be cobalt (Co) and nickel (Ni). Such cobalt and nickel-formed electrified solid-solid reinforcement phase has a heat resistance even at a temperature up to 1490 ℃, can be formed as a needle of 1 ~ 70㎛ size.

In addition, the two kinds of alloying elements may be used iron (Fe) and nickel (Ni). The electrified solid solution phase made of iron and nickel maintains a stable single phase even at a temperature of up to 1245 ° C., and has a granular shape of 1 to 30 μm in size.

In addition, the two types of alloying elements may be copper (Cu) and manganese (Mn). The embrittlement solid solution phase consisting of copper and manganese maintains a stable single phase even at temperatures up to 873 ° C., and has a size of 1 to 10 μm.

As described above, the heat-resistant aluminum alloy of the present invention, which combines an electrifying solid-solution reinforcing phase composed of two kinds of alloying elements that can be used in the present invention, is improved in heat resistance than conventional heat-resistant aluminum alloys that lose heat resistance at 200 ° C. or higher. It exists as a single phase even at a temperature above ℃, it is possible to maintain a stable single phase even during remelting, which can be confirmed through the experiments described later.

On the other hand, the alloying element is preferably contained 0.5% by weight to 10% by weight relative to aluminum. If the alloying element is less than 0.5% by weight with respect to aluminum, the amount of alloying elements contained is not sufficient, so the strengthening effect of the electrified solid solution may be less. On the contrary, when the alloying element is contained in an amount of more than 10% by weight with respect to aluminum, the electrolytic solid solution reinforcing phase is coarse, and may cause problems of castability and segregation due to the specific gravity of the coarse reinforcing phase.

In addition, the two types of alloying elements are not limited to the mixing ratio because they are the elements forming the solid-state solid solution, in the present invention, the two types of alloying elements, one type of element is 10 to 90% by weight, the other type of element It is preferable that 90-10 weight% is contained.

The heat-resistant aluminum alloy of the present invention as described above can be produced by adding an alloying element to the molten aluminum molten aluminum, and then cast when the alloying element is dissolved. At this time, the melting temperature of the aluminum is preferably made at about 700 ℃ 30 ~ 40 ℃ higher than the melting point of aluminum 660 ℃ in consideration of the heat loss.

In addition, in the present invention, chromium and tungsten may be used as the alloying element, and the alloying element may be directly added chromium and tungsten to the molten aluminum, or may be added in the form of a chromium-tungsten mother alloy. Or in the form of an aluminum-chromium master alloy and an aluminum-tungsten master alloy.

In addition, copper and nickel may be used as the alloying element. At this time, the alloying element may be added directly to the aluminum molten copper and nickel, or in the form of a copper-nickel mother alloy. Or in the form of an aluminum-copper master alloy and an aluminum-nickel master alloy.

In addition, the alloy element may be used iron and chromium, and the alloy element may be used by adding iron and chromium directly to the molten aluminum, or in the form of an iron-chromium master alloy. Or in the form of an aluminum-iron master alloy and an aluminum-chromium master alloy.

In addition, the alloy element may be used iron and manganese. At this time, the iron and manganese alloy elements can be added directly to the molten aluminum, or in the form of an iron-manganese master alloy. Or in the form of an aluminum-iron master alloy and an aluminum-manganese master alloy.

In addition, manganese and vanadium may be used as the alloying element, and the alloying element may be added directly to the molten aluminum or in the form of a manganese-vanadium master alloy. Or in the form of an aluminum-manganese master alloy and an aluminum-vanadium master alloy.

In addition, cobalt and nickel may be used as the alloying element. This cobalt and nickel can be added directly to the molten aluminum, or in the form of a cobalt-nickel master alloy. Or in the form of an aluminum-cobalt master alloy and an aluminum-nickel master alloy.

In addition, iron and nickel may be used as the alloying element. This iron and nickel can be added directly to the molten aluminum or in the form of an iron-nickel master alloy. Or in the form of an aluminum-iron master alloy and an aluminum-nickel master alloy.

In addition, copper and manganese may be used as the alloying element, and the alloying element may be added directly to the molten aluminum, or copper and manganese in the form of a copper-manganese master alloy. Or in the form of an aluminum-copper master alloy and an aluminum-manganese master alloy.

In addition, the manufacturing of each alloy element in the form of a master alloy can be carried out through a variety of dissolution methods that are commonly used, in the present invention using a plasma arc as a heat source and plasma that can be dissolved over a wide range from low vacuum to atmospheric pressure Metal arc is heated and melted by plasma arc melting (PAM) or Joule heat generated by eddy current flowing in the opposite direction to the current of the coil through the electromagnetic induction action. It is preferable to prepare by Vacuum Induction Melting (VIM), which is easy to control the components and temperature by the strong stirring action.

The alloy element may be added in an amount of 0.5 wt% to 10 wt% based on aluminum. This is because the reinforcement effect is maximized while preventing segregation due to coarsening of the tempered solid-solution reinforcement phase of the heat-resistant aluminum alloy manufactured through the manufacturing method.

In order to prove the effect of the heat-resistant aluminum alloy according to the present invention was carried out the following experiment.

Figures 3 to 10 are binary state diagrams according to the type of alloying elements, Figure 3 is chromium and tungsten, Figure 4 is copper and nickel, Figure 5 is iron and chromium, Figure 6 is iron and manganese, Figure 7 is manganese and vanadium 8 shows cobalt and nickel, FIG. 9 shows iron and nickel, and FIG. 10 shows copper and manganese.

As shown in FIG. 3, chromium and tungsten form a thermal solid solution, and it can be seen that the thermal solid solution stably exists in a solid phase up to 1800 ° C., which is much higher than 660 ° C., which is the melting point of aluminum.

In other words, the heat-resistant aluminum alloy having an electrolytic solid-solution reinforcement phase made of chromium and tungsten can maintain a stable single phase at a temperature about three times higher than the melting point of aluminum, and the electrolytic solid-solution reinforcement phase does not coarsen or decompose even at temperatures up to 1800 ° C. It can be predicted that it may be used as a part of a piston or an aircraft of a diesel engine used at a high temperature such as 1800 ° C.

In addition, it can be seen from FIG. 4 that copper and nickel form tremor solids with each other, and that the tremor solids safely exist as a solid phase up to 870 deg. C, which is higher than 660 deg.

Therefore, the heat-resistant aluminum alloy having a tremor solid-solution reinforcement phase consisting of copper and nickel can be expected that the copper-nickel tremor solid phase is not coarsened or decomposed at a high temperature of about 800 ℃.

In addition, it can be seen through Figure 5 that the iron and chromium forms a thermally solid solution, and the thermally solid solution is safely present in the solid phase up to 1500 ° C higher than the melting point of aluminum 660 ℃.

In other words, the heat-resistant aluminum alloy having an electrified solid solution reinforced phase consisting of iron and chromium may maintain a single phase even at a temperature about two times higher than the melting point of aluminum. Accordingly, coarsening or decomposition of the iron-chromium electrolytic solid-solid reinforcement phase may not occur even at a high temperature of about 1500 ° C., and thus, it may be easily applied to parts such as gasoline turbocharged engine blocks.

In addition, it can be seen from Figure 6 that iron and manganese form a tremor solid solution, and the tremor solid solution is safely present in the solid phase up to 1245 ℃ higher than the melting point of aluminum 660 ℃.

In other words, the heat-resistant aluminum alloy having an electrolytic solid-solution reinforced phase composed of iron and manganese maintains a stable single phase even at a temperature that is twice as high as the melting point of aluminum. It does not occur. Therefore, this heat-resistant aluminum alloy can be easily applied to the diesel engine block.

In addition, it can be seen from FIG. 7 that manganese and vanadium form a tremor solid solution, and the tremor solid solution exists safely at a solid phase up to 1245 ° C. higher than 660 ° C., which is the melting point of aluminum.

That is, it can be seen that the heat-resistant aluminum alloy having the modulus solid-solution strengthening phase composed of manganese and vanadium maintains a stable single phase even at a temperature about two times higher than the melting point of aluminum. It can be predicted that no coarsening or decomposition in solid solution strengthening will occur. Therefore, the heat-resistant aluminum alloy according to the present invention can be easily applied to linerless engine blocks or automobile parts in gasoline engines.

In addition, it can be seen from FIG. 8 that the cobalt and nickel form a tremor solid solution, and the tremor solid solution is stably present in the solid phase up to 1490 ° C., which is 830 ° C. higher than the melting point of aluminum.

In other words, the heat-resistant aluminum alloy forming the thermal solid solution strengthening phase consisting of cobalt and nickel can maintain the single phase up to a temperature of about 830 ℃ higher than the melting point of aluminum. Therefore, coarsening or decomposition of the cobalt-nickel electrified solid phase may not occur at temperatures above 300 ° C. or when remelting. The heat-resistant aluminum alloy having such cobalt-nickel electrified solid phase is applied to the piston of a diesel engine to improve engine efficiency. Can improve.

In addition, it can be seen from FIG. 9 that iron and nickel form a thermally solid solution, and the thermally solid solution stably exists in a solid phase up to 1245 ° C., which is the melting point of aluminum.

In other words, the heat-resistant aluminum alloy having an electrifying solid solution phase composed of iron and nickel maintains a stable single phase even at a temperature about 600 ° C. above the melting point of aluminum. In addition, it can be predicted that the thermodynamic calculation does not cause coarsening or decomposition of the iron-nickel electrified solids strengthening up to 1245 ° C, and can be widely applied not only to the existing automotive engine materials but also components such as aircraft.

In addition, it can be seen from FIG. 10 that copper and manganese form a thermally solid solution, and the thermally solid solution exists in a stable solid phase up to 873 ° C higher than the melting point of aluminum, 660 ° C.

In other words, the heat-resistant aluminum alloy having a thermally solid solution strengthening phase composed of copper and manganese maintains a single phase even at a high temperature of 300 ° C. or higher, and has excellent heat resistance characteristics. It can be predicted that aluminum and the added element copper-manganese can be actively recycled because the phase is not coarsened or decomposition occurs.

Example 1 Cr-W Electrification Reinforced Heat-resistant Aluminum Alloy

Preparation Example 1

The aluminum molten aluminum melted at 700 ° C. was added with chromium (Cr) and tungsten (W) 1.5% by weight, respectively, as an alloying element while maintaining the temperature at 700 ° C., followed by addition of chromium (Cr) and tungsten. (W) is maintained for about 30 minutes to 60 minutes to dissolve, then cast and heat-resistant aluminum alloy having a Cr-W tremor solid solution reinforced phase (hereinafter referred to as 'Cr-W tremor employment reinforced heat-resistant aluminum alloy') Specimen was prepared.

Preparation Example 2

An aluminum molten aluminum melted at 700 ° C. was maintained at 700 ° C., and an Al-Cr master alloy containing 50 wt% chromium (Cr) and an Al-W master alloy containing 50 wt% tungsten (W) were used. After adding 1.5% by weight, the Al-Cr mother alloy and the Al-W mother alloy were kept for about 30 minutes to 60 minutes to dissolve, followed by casting to test the specimen of Cr-W electrified tempered reinforced heat-resistant aluminum alloy. Was prepared.

Preparation Example 3

Cr-W wool manufactured by melting the aluminum at 700 ° C and having a chromium (Cr): tungsten (W) ratio of 50% by weight to 50% by weight using a plasma arc melting method at 700 ° C. After adding 3% by weight of the alloy to the molten metal in the molten metal, it is maintained for about 30 minutes to 60 minutes until the added Cr-W master alloy is completely dissolved, and then cast and cast Cr-W thermally strengthened heat-resistant aluminum alloy A specimen of was prepared.

FIG. 11 shows an optical microscope tissue photograph of the microstructure of the specimen prepared in Preparation Example 1. After polishing the specimen with SiC Emery paper # 200, 400, 600, 800, 1000, 1500, 2400, After micropolishing using Al ₂ O ₃ 1㎛ powder, the structure was observed with an optical microscope, heat-resistant aluminum alloy according to the manufacturing method of the present invention through Figure 11 has a facet-shaped reinforcement phase of about 1 ~ 200㎛ size It could be confirmed that it exists.

12 to 14 show the results of mapping the microstructure of the specimens prepared in Preparation Examples 1 to 3 to the Electron Probe Micro-Analyzer (EPMA).

As shown in FIG. 12, the specimen prepared in Preparation Example 1 was confirmed that the facet-shaped reinforcement phase identified in FIG. 11 was a Cr-W modulus solid solution. In addition, it can be seen from FIGS. 13 and 14 that chromium (Cr) and tungsten (W) of each of the specimens prepared in Preparation Example 2 and Preparation Example 3 form an electroluminescent solid.

In addition, through the results of FIGS. 12 to 14 as described above, the path of adding chromium (Cr) and tungsten (W) used as alloying elements in the heat-resistant aluminum alloy according to the present invention is irrelevant to the formation tube of the electrolytic solid solution. Able to know.

The following is to confirm the high temperature stability of Cr-W electrification-employment reinforced heat-resistant aluminum alloy according to the present invention, after the specimen prepared in Preparation Example 1 was heat-treated at 300 ℃ for 200 hours, the microstructure of the heat-treated specimen The results observed with an optical microscope are shown in FIG. 15.

As shown in FIG. 15, the reinforcing phase made of Cr-W electrolytic solid solution has the same facet shape as the microstructure shown in FIG. 11, unlike the existing intermetallic compound in which coarsening or phase decomposition occurs in an aluminum matrix at high temperature. In addition, no coarsening or phase decomposition of the reinforcing phase was observed, and the Cr-W tremor solid solution strengthening phase of the Cr-W tremor employment tempered aluminum alloy according to the present invention was confirmed to be stable at 300 ° C.

FIG. 16 is a photograph of a microstructure of a specimen prepared after remelting of the specimen prepared in Preparation Example 1, using an optical microscope, wherein the specimen prepared after remelting is a melting point of aluminum for the specimen prepared in Preparation Example 1. After remelting until casting.

 As shown in FIG. 16, the electrified solid formed in the Cr-W electrified tempered reinforced heat-resistant aluminum alloy according to the present invention is not coarsened or decomposed at all during remelting, as expected in the binary system diagram shown in FIG. 3. It was confirmed that the reinforcement phase was maintained. Through this, the heat-resistant aluminum alloy according to the present invention is expected to be utilized to actively recycle the base metal aluminum and the alloying elements chromium and tungsten at the environmentally friendly virgin level when recycling.

Preparation Example 4

Cr-W manufactured by melting the aluminum at 700 ° C. in a chromium (Cr): tungsten (W) ratio of 50% by weight to 50% by weight using a plasma arc melting method while maintaining the temperature at 700 ° C. The master alloy was added to the molten metal by 0.5 wt%, 1 wt%, 3 wt%, 5 wt%, 7 wt%, 9 wt%, 10 wt%, and 11 wt% with respect to aluminum, and then added Cr- After the W master alloy was completely dissolved for about 30 to 60 minutes, casting was performed to prepare specimens of Cr-W modulus-employment reinforced heat-resistant aluminum alloy.

FIG. 17 is a graph showing the average size of the electrolytic solid solution according to the content of alloying elements added to each specimen prepared in Preparation Example 4, an image of the microstructure of each specimen prepared in Preparation Example 4 measured by an optical microscope The average size of the tremor solid solution according to each content was measured by using an analyzer.

As a result, when the 0.5 wt% Cr-W mother alloy was added, the amount of the tremor solid formed was small, and the size of the tremor solid was found to be small as 10 μm. You can see the conversation.

Therefore, in the Cr-W electrification-employment reinforced heat-resistant aluminum alloy according to the present invention, when the content of the alloying element added with respect to aluminum is 0.5% by weight to 10% by weight, a sufficient amount of the electrolytic solution is formed to exert the effect as an alloy. It can be predicted that problems such as segregation due to the coarsening of the size can be prevented from occurring.

Example 2 Reinforced Heat-resistant Aluminum Alloy for Cu-Ni Electrification

Preparation Example 5

A heat-resistant aluminum alloy having a Cu-Ni electrolytic solid-solution strengthening phase in the same manner as in Preparation Example 1, except that 1.5 wt% of copper (Cu) and nickel (Ni) were used as the alloying elements (hereinafter, referred to as' Cu-Ni conductivity A specimen of solid solution strengthening heat-resistant aluminum alloy).

FIG. 18 is an optical microscope photograph showing the microstructure of the specimen prepared in Preparation Example 5. After polishing the specimen with SiC Emery paper # 200, 400, 600, 800, 1000, 1500, 2400, After micropolishing using Al ₂ O ₃ 1 μm powder, the tissue was observed under an optical microscope. As a result, it was confirmed that the Cu-Ni electrification-employment-reinforced heat-resistant aluminum alloy specimen of Preparation Example 5 had a reinforcement phase of grain boundary interface having a size of about 1 to 50 μm.

FIG. 19 illustrates a result of mapping the microstructure of the specimen prepared in Preparation Example 5 to an Electron Probe Micro-Analyzer (EPMA), and the enhanced phase of the grain boundary interface identified in FIG. 18 is Cu-Ni conductivity. It was confirmed that it is an employment structure.

The following is to confirm the high temperature stability of the Cu-Ni electrified employment-enhanced heat-resistant aluminum alloy according to the present invention, after the specimen prepared in Preparation Example 5 was heat-treated at 300 ℃ for 200 hours, the microstructure of the heat-treated specimen The result observed with the optical microscope is shown in FIG.

As shown in FIG. 20, the reinforcing phase made of Cu-Ni electrolytic solid solution has the same grain boundary interface shape as that of the microstructure shown in FIG. 18, unlike the existing intermetallic compound, which is coarsened or phase decomposition occurs in the aluminum matrix at high temperature. The enhanced phase of was confirmed, and no coarsening or phase decomposition of the enhanced phase was observed. Therefore, it could be confirmed that the Cu-Ni electrified solid-solution reinforcement phase of the Cu-Ni electrification-employed reinforced heat-resistant aluminum alloy according to the present invention is stable even at 300 ° C.

FIG. 21 is a photograph of a microstructure of a specimen prepared after remelting in Preparation Example 5 using an optical microscope, wherein the specimen prepared after remelting is a melting point of aluminum for the specimen prepared in Preparation Example 5. After remelting until casting.

 As shown in FIG. 21, the electrified solid formed in the Cu-Ni electrified tempered reinforced heat-resistant aluminum alloy according to the present invention is not coarsened or decomposed at all upon remelting, as expected in the binary state diagram shown in FIG. 4. It was confirmed that the reinforcement phase was maintained. In addition, using the above-mentioned characteristics and the Cu-Ni electrolytic solid-solution reinforcement phase is 3.3 times the specific gravity of aluminum, the environmentally friendly virgin of copper (Cu) and nickel (Ni), which are base metals and alloying elements, is recycled during the heat-resistant aluminum alloy recycling It is expected to be used to actively sort and recycle at the level of.

Preparation Example 6

Except for using Cu-Ni master alloy prepared by using the plasma arc melting method in a copper (Cu): nickel (Ni) ratio of 50% by weight to 50% by weight, Cu- A specimen of Ni-elective tempered reinforced heat-resistant aluminum alloy was prepared.

 FIG. 22 is a graph showing the average size of the electrolytic solid solution according to the content of alloying elements added to each specimen prepared in Preparation Example 6, an image of the microstructure of each specimen prepared in Preparation Example 6 measured by an optical microscope The average size of the tremor solid solution according to each content was measured by using an analyzer.

As a result, when the 0.5 wt% Cu-Ni master alloy was added, the amount of the electrified solid formed was small, and it was not possible to confirm the measurement with a size of 1 μm or less, and at 10 wt% or more, the size of the electrified solid was more than 300 μm. You can see that it is too coarse. Therefore, when the content of the alloying element added to the aluminum Cu-Ni electrification employment-enhanced heat-resistant aluminum alloy is 0.5% by weight to 10% by weight, a sufficient amount of the electric conductivity solid to exhibit the effect as an alloy is formed It can be predicted that problems such as segregation due to the coarsening of the size can be prevented from occurring.

Example 3 Fe-Cr Electrification-Enhanced Heat-Resistant Aluminum Alloy

Preparation Example 7

A heat-resistant aluminum alloy having a Fe-Cr electrified solid-reinforced phase in the same manner as in Preparation Example 1, except that 1.5 wt% of iron (Fe) and chromium (Cr) were used as alloy elements. Specimens of solid-solution-reinforced heat-resistant aluminum alloys.

FIG. 23 is an optical microscope photograph showing the microstructure of the specimen prepared in Preparation Example 7. After polishing the specimen with SiC Emery paper # 200, 400, 600, 800, 1000, 1500, 2400, After micro-polishing using Al ₂ O ₃ 1㎛ powder, the structure was observed with an optical microscope, the heat-resistant aluminum alloy prepared in Preparation Example 7 through FIG. 23 has a facet-shaped reinforcement phase of about 1 ~ 60㎛ size I could confirm that.

FIG. 24 illustrates a result of mapping the microstructure of the specimen prepared in Preparation Example 7 to an Electron Probe Micro-Analyzer (EPMA), whereby the reinforcement phase of the facet shape confirmed in FIG. 23 is Fe-Cr. It was confirmed that it is a tremor employment.

The following is to confirm the high temperature stability of the Fe-Cr electrification employment-enhanced heat-resistant aluminum alloy according to the present invention, after the specimen prepared in Preparation Example 7 is heat-treated at 300 ℃ for 200 hours, the microstructure of the heat-treated specimen The results observed with an optical microscope are shown in FIG. 25.

As shown in FIG. 25, the reinforcing phase made of the Fe-Cr electrolytic solid solution has the same facet shape as that of the microstructure shown in FIG. 23, unlike the existing intermetallic compound in which coarsening or phase decomposition occurs in an aluminum matrix at a high temperature. The coarsening or phase decomposition of the reinforcing phase was not observed, and thus the Fe-Cr tremor solid solution strengthening phase of the Fe-Cr tremor employment tempered aluminum alloy according to the present invention was confirmed to be stable at 300 ° C.

FIG. 26 is an optical microscope photograph of a microstructure of a specimen cast after remelting in Preparation Example 7, wherein the specimen prepared after remelting is a melting point of aluminum for the specimen prepared in Preparation Example 7. After remelting until casting.

 As shown in FIG. 26, the electrified solid formed in the Fe-Cr electrified employment-enhanced heat-resistant aluminum alloy according to the present invention is not coarsened or decomposed at all during remelting, as expected in the binary system diagram shown in FIG. 5. It was confirmed that the reinforcement phase was maintained, and this characteristic and the specific gravity of the Fe-Cr electrifying solids were 2.78 times that of aluminum, and the base metals aluminum and alloy elements iron (Fe) and chromium were recycled when the heat-resistant aluminum alloy was recycled. It is expected that (Cr) can be used to actively sort and recycle to the level of eco-friendly virgin.

Example 4 Fe-Mm Electrification-Enhanced Heat-Resistant Aluminum Alloy

Preparation Example 8

A heat-resistant aluminum alloy having a Fe-Mn electrified solid-reinforced phase in the same manner as in Preparation Example 1, except that 1.5 wt% of iron (Fe) and manganese (Mn) were used as alloying elements, respectively (hereinafter, 'Fe-Mn conductivity Specimens of solid-solution-reinforced heat-resistant aluminum alloys.

FIG. 27 is an optical microscope photograph showing the microstructure of the specimen prepared in Preparation Example 8. After polishing the specimen with SiC Emery paper # 200, 400, 600, 800, 1000, 1500, 2400, After micropolishing using Al ₂ O ₃ 1㎛ powder, the structure was observed with an optical microscope. The heat-resistant aluminum alloy according to the present invention prepared in Preparation Example 8 through FIG. 27 has a facet shape having a size of about 1 to 50 μm. It could be confirmed that the reinforcement phase of existed.

FIG. 28 shows the results of mapping the microstructure of the specimen prepared in Preparation Example 8 to an Electron Probe Micro-Analyzer (EPMA). The facet-reinforced phase identified in FIG. 27 is a Fe-Mn electrolytic solid solution. I could confirm that.

The following is to confirm the high temperature stability of the Fe-Mn electroluminescent employment-enhanced heat-resistant aluminum alloy according to the present invention, after the specimen prepared in Preparation Example 8 was heat-treated at 300 ℃ for 200 hours, the microstructure of the heat-treated specimen The results observed with an optical microscope are shown in FIG. 29.

As shown in FIG. 28, the reinforcing phase made of Fe-Mn electrolytic solid solution has the same facet shape as that of the microstructure shown in FIG. 27, unlike the existing intermetallic compound in which coarsening or phase decomposition occurs in an aluminum matrix at high temperature. The coarsening and phase decomposition of the reinforcement phase were not observed, and thus the Fe-Mn tremor solid-solution solidified phase of the Fe-Mn tremor employment tempered aluminum alloy according to the present invention was found to be stable at 300 ° C.

30 is an optical microscope photograph of the microstructure of the specimen cast after remelting prepared in Preparation Example 8, wherein the specimen prepared after remelting is the melting point of aluminum to the specimen prepared in Preparation Example 8 After remelting until casting.

As shown in FIG. 30, the electrified solid formed in the Fe-Mn electrified employment-enhanced heat-resistant aluminum alloy according to the present invention is not coarsened or decomposed at all during remelting, as expected in the binary system diagram shown in FIG. 6. It was confirmed that the reinforcement phase was maintained, and the characteristics and the specific gravity of the Fe-Mn electrolytic solids were more than 2.8 times higher than that of aluminum, and the base metals aluminum and the alloying elements iron (Fe) Manganese (Mn) is expected to be used to actively sort and recycle to the level of eco-friendly virgin.

Preparation Example 9

Heat-resistant aluminum in the same manner as in Preparation Example 4, except that the Fe-Mn mother alloy prepared by using the plasma arc melting method was made to have an iron (Fe): manganese (Mn) ratio of 50% by weight to 50% by weight. Specimen of the alloy was prepared.

FIG. 31 is a graph showing the average size of the electrolytic solid solution according to the content of the alloying elements added to each specimen prepared in Preparation Example 9, an image of the microstructure of each specimen prepared in Preparation Example 9 measured by an optical microscope The average size of the tremor solid solution according to each content was measured by using an analyzer.

As a result, when the 0.5 wt% Fe-Mn mother alloy was added, the amount of the emulsified solid formed was small, and the size of the emulsified solid was found to be less than 5 μm. You can see that it is too coarse. Therefore, in the Fe-Mn electrified employment-enhanced heat-resistant aluminum alloy according to the present invention, when the content of the alloying element added to the aluminum is 0.5% by weight to 10% by weight, a sufficient amount of the electrolytic solution is formed to exert the effect as an alloy. It can be predicted that problems such as segregation due to the coarsening of the size can be prevented from occurring.

Example 5 Mn-V Electrification-Enhanced Heat-Resistant Aluminum Alloy

Preparation Example 10

A heat-resistant aluminum alloy having a Mn-V conductivity solid-solution strengthening phase in the same manner as in Preparation Example 1, except that 1.5 wt% of manganese (Mn) and vanadium (V) were used as alloying elements, respectively (hereinafter referred to as 'Mn-V conductivity' Specimens of solid-solution-reinforced heat-resistant aluminum alloys.

FIG. 32 shows an optical microscope tissue photograph of the microstructure of the specimen prepared in Preparation Example 10. After polishing the specimen with SiC Emery paper # 200, 400, 600, 800, 1000, 1500, 2400, After micropolishing using Al ₂ O ₃ 1㎛ powder, the structure was observed with an optical microscope. The Mn-V modulus employment-enhanced heat-resistant aluminum alloy prepared in Preparation Example 10 according to the present invention through FIG. It could be confirmed that there is a facet-shaped reinforcement phase having a size of about 100 μm.

FIG. 33 shows the results of mapping the microstructure of the specimen prepared in Preparation Example 10 to an Electron Probe Micro-Analyzer (EPMA). The facet-shaped reinforcement phase identified in FIG. 32 is a Mn-V electrolytic solid solution. I could confirm that.

The following is to confirm the high temperature stability of the Mn-V conductivity-enhanced reinforced heat-resistant aluminum alloy according to the present invention, after the specimen prepared in Preparation Example 10 was heat-treated at 300 ℃ for 200 hours, the microstructure of the heat-treated specimen The results observed with an optical microscope are shown in FIG. 27.

As shown in FIG. 34, the reinforcing phase made of the Mn-V electrolytic solid solution has the same facet shape as the microstructure shown in FIG. 32, unlike the existing intermetallic compound in which coarsening or phase decomposition occurs in an aluminum matrix at a high temperature. The coarsening and phase decomposition of the reinforcing phase was not observed, and thus the Mn-V tremor solid-solution solidified phase of the Mn-V tremor employment tempered aluminum alloy according to the present invention was found to be stable at 300 ° C.

FIG. 35 is a photograph of a microstructure of a specimen prepared after remelting in Preparation Example 10 using an optical microscope, wherein the specimen prepared after remelting is a melting point of aluminum for the specimen prepared in Preparation Example 10. After remelting until casting.

 As shown in FIG. 35, the electrified solid formed in the Mn-V electrified tempered reinforced heat-resistant aluminum alloy according to the present invention is not coarsened or decomposed at all during remelting, as expected in the binary system diagram shown in FIG. 7. It was confirmed that the reinforcement phase was maintained, and that the characteristics and the specific gravity of the electrolytic solids were more than 2.4 times of aluminum, the base metal aluminum and the alloying elements of manganese (Mn) and vanadium ( It is expected to be used to actively recycle V) to the level of eco-friendly virgin.

Preparation Example 11

The Mn-V mother alloy was prepared in the same manner as in Preparation Example 4, except that a Mn-V mother alloy prepared by using the plasma arc melting method to have a manganese (Mn): vanadium (V) ratio of 50% by weight to 50% by weight. A specimen of the V shim employment reinforced heat-resistant aluminum alloy was prepared.

FIG. 36 is a graph showing the average size of the electrolytic solid solution according to the content of the alloying elements added to each specimen prepared in Preparation Example 11, an image of measuring the microstructure of each specimen prepared in Preparation Example 11 by optical microscope The average size of the tremor solid solution according to each content was measured by using an analyzer.

As a result, when the 0.5 wt% Mn-V mother alloy was added, the amount of the emulsified solid formed was small, and the size of the emulsified solid was found to be less than 4 μm. You can see that it is coarse. Therefore, when the content of the alloying element added to the Mn-V electrification-employment reinforced heat-resistant aluminum alloy according to the present invention is 0.5% by weight to 10% by weight, a sufficient amount of the electrolytic solution is formed to exert the effect as an alloy. It can be predicted that problems such as segregation due to the coarsening of the size can be prevented from occurring.

Example 6 Co-Ni Elective Reinforced Heat-resistant Aluminum Alloy

Preparation Example 12

A heat-resistant aluminum alloy having a Co-Ni conductivity solid phase strengthening phase in the same manner as in Preparation Example 1, except that 1.5 wt% of cobalt (Co) and nickel (Ni) were used as the alloying elements (hereinafter, referred to as' Co-Ni conductivity Specimens of solid-solution-reinforced heat-resistant aluminum alloys.

FIG. 37 is an optical microscope photograph showing the microstructure of the specimen prepared in Preparation Example 12. After polishing the specimen with SiC Emery paper # 200, 400, 600, 800, 1000, 1500, 2400, After micropolishing using Al ₂ O ₃ 1㎛ powder, the structure was observed with an optical microscope, the heat-resistant aluminum alloy of the present invention prepared in Preparation Example 12 through Figure 37 has a needle shape of about 1 ~ 70㎛ size It was confirmed that the reinforcement phase exists.

FIG. 38 shows the results of mapping the microstructure of the specimen prepared in Preparation Example 12 to an Electron Probe Micro-Analyzer (EPMA), wherein the needle-shaped reinforcement phase identified in FIG. I could confirm that.

The following is to confirm the high-temperature stability of the Co-Ni electrification-employment reinforced heat-resistant aluminum alloy according to the present invention, after the specimen prepared in Preparation 12 was heat-treated at 300 ℃ for 200 hours, the microstructure of the heat-treated specimen The result observed with the optical microscope is shown in FIG.

As shown in FIG. 39, the reinforcing phase made of Co-Ni electrolytic solid solution has the same acicular shape as that of the microstructure shown in FIG. 37, unlike the existing intermetallic compound in which coarsening or phase decomposition occurs in an aluminum matrix at high temperature. No coarsening or phase decomposition of the reinforcing phase was observed, and the Co-Ni electrifying solidified phase of the Co-Ni electrification-employed tempered aluminum alloy according to the present invention was confirmed to be stable at 300 ° C.

40 is a photograph of the microstructure of the specimens cast after remelting prepared in Preparation Example 12 using an optical microscope, wherein the specimens cast after remelting are the melting point of aluminum in the specimen prepared in Preparation Example 12 After remelting until casting.

 As shown in FIG. 40, the electrified solid formed in the Co-Ni electrified tempered reinforced heat-resistant aluminum alloy according to the present invention is not coarsened or decomposed at all during remelting, as expected in the binary system diagram shown in FIG. 8. It was confirmed that the reinforcement phase was maintained, and this characteristic could be utilized to actively recycle base metal aluminum and alloy elements cobalt (Co) and nickel (Ni) to the level of eco-friendly virgin when recycling the heat-resistant aluminum alloy. It is expected to be able.

Preparation Example 13

Heat-resistant aluminum in the same manner as in Preparation Example 4, except that a Co-Ni mother alloy prepared by using a plasma arc melting method to have a cobalt (Co): nickel (Ni) ratio of 50% by weight to 50% by weight. Specimen of the alloy was prepared.

FIG. 41 is a graph showing the average size of the electrolytic solid solution according to the content of the alloying elements added to each specimen prepared in Preparation Example 13, an image of measuring the microstructure of each specimen prepared in Preparation Example 13 by an optical microscope The average size of the tremor solid solution according to each content was measured by using an analyzer.

As a result, it was found that when 0.5 wt% of Co-Ni master alloy was added, the amount of the tremor solid formed was small, and the size of the tremor solid was smaller than 5 μm. You can see that it is coarse. Therefore, when the content of the alloying element added to the aluminum Co-Ni electrification-employment reinforced heat-resistant aluminum according to the present invention is 0.5% by weight to 10% by weight, a sufficient amount of the electric conductivity solid to exhibit the effect as an alloy is formed It can be predicted that problems such as segregation due to the coarsening of the size can be prevented from occurring.

Example 7 Fe-Ni Elective Reinforced Heat-resistant Aluminum Alloy

Preparation Example 14

A heat-resistant aluminum alloy having a Fe-Ni conductivity solid phase strengthening phase in the same manner as in Preparation Example 1, except that 1.5 wt% of iron (Fe) and nickel (Ni) were used as alloying elements (hereinafter, 'Fe-Ni conductivity Specimens of solid-solution-reinforced heat-resistant aluminum alloys.

FIG. 42 is an optical microscope photograph showing the microstructure of the specimen prepared in Preparation Example 14. After polishing the specimen with SiC Emery paper # 200, 400, 600, 800, 1000, 1500, 2400, After micropolishing using Al ₂ O ₃ 1㎛ powder, the structure was observed with an optical microscope, the heat-resistant aluminum alloy according to the manufacturing method of the present invention through Figure 42 is a granular shape of the granular shape of about 1 ~ 30㎛ size It could be confirmed that it exists.

FIG. 43 shows the results of mapping the microstructure of the specimen prepared in Preparation Example 14 to an Electron Probe Micro-Analyzer (EPMA). The granular reinforcement phase identified in FIG. I could confirm that.

The following is to confirm the high temperature stability of the Fe-Ni electrification-employment enhanced heat-resistant aluminum alloy according to the present invention, after the specimen prepared in Preparation Example 14 was heat-treated at 300 ℃ for 200 hours, the microstructure of the heat-treated specimen The results observed with an optical microscope are shown in FIG. 44.

As shown in FIG. 44, the reinforcing phase made of a Fe-Ni electrolytic solid solution has a granular shape of the same granular shape as the microstructure shown in FIG. 42, unlike the existing intermetallic compound in which coarsening or phase decomposition occurs in an aluminum matrix at a high temperature. The coarsening or phase decomposition of the reinforcing phase was not observed, and thus the Fe-Ni tremor solid-solution strengthening phase of the Fe-Ni tremor employment-type tempered aluminum alloy according to the present invention was confirmed to be stable at 300 ° C.

45 is a photograph of the microstructure of the specimens cast after remelting prepared in Preparation Example 14 using an optical microscope, wherein the specimens cast after remelting are the melting point of aluminum in the specimen prepared in Preparation Example 14 After remelting until casting.

 As shown in FIG. 45, the electrified solid formed in the Fe-Ni electrification-employment-reinforced heat-resistant aluminum alloy according to the present invention is not coarsened or decomposed at all during remelting, as expected in the binary state diagram shown in FIG. 9. It was confirmed that the reinforcement phase was maintained, and this property could be utilized to actively recycle base metal aluminum and alloy elements iron (Fe) and nickel (Ni) to the level of eco-friendly virgin when recycling the heat-resistant aluminum alloy. It is expected to be able.

Preparation Example 15

Heat-resistant aluminum in the same manner as in Preparation Example 4, except that the Fe-Ni master alloy prepared by using the plasma arc melting method was made to have an iron (Fe): nickel (Ni) ratio of 50% by weight to 50% by weight. Specimen of the alloy was prepared.

FIG. 46 is a graph showing the average size of the electrolytic solid solution according to the content of the alloying elements added to each specimen prepared in Preparation Example 15, an image of the microstructure of each specimen prepared in Preparation Example 15 measured by an optical microscope The average size of the tremor solid solution according to each content was measured by using an analyzer.

As a result, when the 0.5 wt% Fe-Ni master alloy was added, the amount of the emulsified solid formed was small, and the size of the emulsified solid was found to be less than 3 μm. At 10 wt% or more, the size of the emulsified solid was greater than about 280 μm. You can see that it is too coarse. Therefore, when the content of the alloying element added to the Fe-Ni electrification-employment reinforced heat-resistant aluminum alloy according to the present invention is 0.5% by weight to 10% by weight, a sufficient amount of a high-temperature solid solution that can exert the effect as an alloy is formed. It can be predicted that problems such as segregation due to the coarsening of the size can be prevented from occurring.

Example 8 Cu-Mn Electrification-Enhanced Heat-Resistant Aluminum Alloy

Preparation Example 16

A heat-resistant aluminum alloy having a Cu-Mn electrolytic solid-solution strengthening phase in the same manner as in Preparation Example 1, except that 1.5 wt% of copper (Cu) and manganese (Mn) were used as alloying elements, respectively. Specimens of solid-solution-reinforced heat-resistant aluminum alloys.

FIG. 47 is a light microscopic photograph showing the microstructure of the specimen prepared in Preparation Example 16. After polishing the specimen with SiC Emery paper # 200, 400, 600, 800, 1000, 1500, 2400, After micropolishing using Al ₂ O ₃ 1㎛ powder, the structure was observed with an optical microscope. The heat-resistant aluminum alloy according to the manufacturing method of the present invention through FIG. It could be confirmed that it exists.

FIG. 48 shows the results of mapping the microstructure of the specimen prepared in Preparation Example 16 to an Electron Probe Micro-Analyzer (EPMA), which is present at the grain boundary interface of 5-10 μm in FIG. 47. Reinforcing phase was confirmed to be Cu-Mn tremor solid solution.

The following is to confirm the high temperature stability of the Cu-Mn electrification employment-enhanced heat-resistant aluminum alloy according to the present invention, after the specimen prepared in Preparation Example 16 was heat-treated at 300 ℃ for 200 hours, the microstructure of the heat-treated specimen The results observed with an optical microscope are shown in FIG. 49.

As shown in FIG. 49, the reinforcing phase made of Cu-Mn electrolytic solid solution has a size of 5-10 μm, which is the same as that of the microstructure shown in FIG. The reinforcing phase present at the grain boundary interface of was confirmed, and the coarsening or phase decomposition of the reinforcing phase was not observed. Could confirm. Therefore, the Cu-Mn electrification employment-enhanced heat-resistant aluminum alloy according to the present invention can increase fuel efficiency by increasing the heat resistance limit of the automotive engine.

FIG. 50 is a photograph of a microstructure of a specimen prepared after remelting in Preparation Example 16 using an optical microscope, wherein the specimen prepared after remelting is a melting point of aluminum as the specimen prepared in Preparation Example 16. FIG. After remelting until casting.

 As shown in FIG. 50, the electrified solid formed in the Cu-Mn electrified employment-enhanced heat-resistant aluminum alloy according to the present invention is not coarsened or decomposed at all during remelting, as expected in the binary system diagram shown in FIG. 10. It was confirmed that the reinforcement phase was maintained, and this characteristic could be used to actively recycle base metal aluminum and alloy elements copper (Cu) and manganese (Mn) to the level of eco-friendly virgin when recycling the heat-resistant aluminum alloy. It is expected to be able.

Preparation Example 17

Cu-Mn mother alloy prepared by using a plasma arc melting method in a copper-to-manganese (Mn) ratio of 50% by weight to 50% by weight, except that Cu-Mn mother alloy was used. A specimen of Mn electrification-employment reinforced heat-resistant aluminum alloy was prepared.

FIG. 51 is a graph showing the average size of the electrolytic solid solution according to the content of alloying elements added to each specimen prepared in Preparation Example 17. An image of the microstructure of each specimen prepared in Preparation Example 17 measured by an optical microscope. The average size of the tremor solid solution according to each content was measured by using an analyzer.

As a result, when 0.5 wt% Cu-Mn mother alloy was added, it was found that the amount of the electrified solid formed was small, and the size thereof was less than 2 μm, and at 10 wt% or more, the size of the electrified solid was greater than about 250 μm. You can see that it is too coarse. Therefore, in the Cu-Mn electrified employment-enhanced heat-resistant aluminum alloy according to the present invention, when the content of the alloying element added to the aluminum is 0.5% by weight to 10% by weight, a sufficient amount of the electrolytic solution is formed to exert the effect as an alloy. It can be predicted that problems such as segregation due to the coarsening of the size can be prevented from occurring.

As described above, the heat-resistant aluminum alloy according to the present invention forms a thermally solid solution with each other, and a strengthening solid-state solidified phase formed of two kinds of alloying elements that do not have a solid solution with aluminum, which is a base metal, reacts with aluminum even at a high temperature of 300 ° C. or higher. It does not occur or phase decomposition has an innovative heat resistance, and after re-melting them when recycling the alloying elements and aluminum, can be selected by using the difference in melting point or specific gravity can be applied environmentally friendly in various fields. In addition, it is applicable to automobiles, diesel engines, aircraft parts, etc., which could not be applied at a high temperature of 200 ° C. or higher due to the limitation of heat-resistant aluminum, and it is possible to pursue fuel efficiency improvement by increasing the heat resistance limit of the currently used automobile engine.

In addition, it is possible to prevent coarsening, segregation, and the like of the modulus of strengthening the solid solution formed by using an appropriate amount of alloying elements.

Claims (29)

Heat-resistant aluminum alloy, characterized in that the two kinds of alloying elements to form a thermally solid solution in aluminum combined to form a thermally solid solution reinforced phase. The method according to claim 1, The alloy element is a heat-resistant aluminum alloy, characterized in that containing 0.5% by weight to 10% by weight relative to aluminum. The method according to claim 2, The two types of alloying elements are heat-resistant aluminum alloy, characterized in that one element contains 10 to 90% by weight, the other element contains 90 to 10% by weight. The method according to claim 3, The two kinds of alloying elements are heat-resistant aluminum alloy, characterized in that chromium and tungsten. The method according to claim 4, Heat-resistant aluminum alloy, characterized in that the thermal solid solution is made of chromium and tungsten to maintain a stable single phase even at a temperature up to 1800 ℃. The method according to claim 3, Heat-resistant aluminum alloy, characterized in that the two kinds of alloying elements are copper and nickel. The method according to claim 6, The thermally solid solution strengthening phase is stable even at a temperature of up to 873 ℃, heat-resistant aluminum alloy, characterized in that it has a grain boundary interface shape of 1 ~ 50㎛ size. The method according to claim 3, The two kinds of alloying elements are heat-resistant aluminum alloy, characterized in that iron and chromium. The method according to claim 8, The thermally solid solution strengthening phase maintains a stable single phase even at a temperature up to 1500 ℃, heat-resistant aluminum alloy, characterized in that it has a Facet shape of 1 ~ 60㎛ size. The method according to claim 3, The two kinds of alloying elements are heat-resistant aluminum alloy, characterized in that iron and manganese. The method according to claim 10, The thermally solid solution strengthening phase has heat resistance even at a temperature up to 1245 ℃, heat-resistant aluminum alloy, characterized in that formed in the facet shape of 1 ~ 50㎛ size. The method according to claim 3, Heat-resistant aluminum alloy, characterized in that the two kinds of alloying elements are manganese and vanadium. The method according to claim 12, The thermally solid solution reinforced phase maintains a stable single phase even at temperatures up to 1245 ° C., and has a Facet shape of 1 to 100 μm in size. The method according to claim 3, The two kinds of alloying elements are heat-resistant aluminum alloy, characterized in that the cobalt and nickel. The method according to claim 14, The thermally solid solution strengthening phase has a heat resistance even at a temperature up to 1490 ℃, heat-resistant aluminum alloy, characterized in that formed in the needle bed of 1 ~ 70㎛ size. The method according to claim 3, The two kinds of alloying elements are heat-resistant aluminum alloy, characterized in that iron and nickel. The method according to claim 16, The thermally solid solution strengthening phase maintains a stable single phase even at a temperature up to 1245 ℃, heat-resistant aluminum alloy, characterized in that it has a granular shape of 1 ~ 30㎛ size. The method according to claim 3, The two kinds of alloying elements are heat-resistant aluminum alloy, characterized in that copper and manganese. The method according to claim 18, The thermal solid solution strengthening phase maintains a stable single phase even at a temperature up to 873 ℃, heat-resistant aluminum alloy, characterized in that it has a size of 1 ~ 10㎛. The method of producing a heat-resistant aluminum alloy, characterized in that the alloy element is added to the molten aluminum molten aluminum, and then cast when the alloy element is dissolved. The method of claim 20, The alloying element is a method for producing a heat-resistant aluminum alloy, characterized in that the addition of chromium and tungsten directly, or in the form of chromium-tungsten master alloy or in the form of aluminum-chromium master alloy and aluminum-tungsten master alloy. The method of claim 20, The alloying element is a method for producing a heat-resistant aluminum alloy, characterized in that the copper and nickel directly added, or added in the form of copper-nickel master alloy or in the form of aluminum-copper master alloy and aluminum-nickel master alloy. The method of claim 20, The alloying element is a method for producing a heat-resistant aluminum alloy, characterized in that the iron and chromium is added directly, or in the form of iron-chromium master alloy or in the form of aluminum-iron master alloy and aluminum-chromium master alloy. The method of claim 20, The alloying element is a method for producing a heat-resistant aluminum alloy, characterized in that directly added iron and manganese, or in the form of iron-manganese master alloy or aluminum-iron master alloy and aluminum-manganese master alloy. The method of claim 20, The alloying element is a method for producing a heat-resistant aluminum alloy, characterized in that directly added to the manganese and vanadium, or in the form of a manganese-vanadium master alloy or aluminum-manganese master alloy and aluminum-vanadium master alloy. The method of claim 20, The alloying element is a method for producing a heat-resistant aluminum alloy, characterized in that directly added cobalt and nickel, or in the form of cobalt-nickel master alloy or in the form of aluminum-cobalt master alloy and aluminum-nickel master alloy. The method of claim 20, The alloying element is a method for producing a heat-resistant aluminum alloy, characterized in that the iron and nickel is added directly, or in the form of iron-nickel master alloy or in the form of aluminum-iron master alloy and aluminum-nickel master alloy. The method of claim 20, The alloying element is a method for producing a heat-resistant aluminum alloy, characterized in that the copper and manganese directly added, or added in the form of copper-manganese master alloy or in the form of aluminum-copper master alloy and aluminum-manganese master alloy. The method according to any one of claims 20 to 28, wherein The alloying element is a method for producing a heat-resistant aluminum alloy, characterized in that added 0.5% by weight to 10% by weight relative to aluminum.

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