JPH0995750A - Aluminum alloy excellent in heat resistance - Google Patents

Abstract

PROBLEM TO BE SOLVED: To produce an aluminum alloy having heat resistance on an extremely high level by adding Zr and Sc and specifying the size of the dispersed grains of Al-Zr series and Al-Sc series and the distance therebetween. SOLUTION: This aluminum alloy contains either or both of, by weight, 0.05 to 0.50% Zr and 0.05 to 1.0% Sc and has a microstructure satisfying at least either of the following (a) and (b): (a) the size of Al-Zr series dispersed grains is regulated to 35 to 450Å, and the distance therebetween is regulated to 0.005 to 0.6μ and (b) the size of Al-Sc series dispersed grains is regulated to 35 to 450Å, and the distance therebetween is regulated to 0.005 to 0.6μ. Moreover, in addition to the above Zr and Sc, Al may be incorporated with 1 to 8% Cu or, furthermore, with one or more kinds among <=1.5% Fe, 0.8 to 2.4% Ni, 0.05 to 0.15% V, 0.05 to 1.5% Mn and 0.15 to 0.30% Cr or 0.1 to 2.5% Mg as well.

Description

Detailed Description of the Invention

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a heat-resistant aluminum alloy having high strength even at high temperatures, and is used as a plate material for use in transportation equipment such as aircraft, railway vehicles, ships, automobiles, construction materials and general machine parts. It is used as a profile, casting, forging, etc.

[0002]

2. Description of the Related Art 2X18 and 2X19 have been put into practical use as typical heat resistant aluminum alloys. 2X18
Is an Al-Cu-Mg-Ni-based aluminum alloy,
As a typical alloy, 2218 (Al-4.0Cu-1.5Mg-2Ni)
And 2618 (Al-2.3Cu-1.5Mg-1.1Fe-1.2Ni).
In particular, in the case of 2618, since Fe and Ni are added in the same number of atoms, Al ₉ (Fe-Ni) is formed, and therefore, the strength decrease is small even after holding at high temperature for a long time, and the outer plate material of the supersonic Concorde. , Piston, supercharger fan, rubber mold,
Used for general heat resistant parts.

On the other hand, 2X19 is Al-Cu-Mn-Zr.
-V type aluminum alloy. A typical alloy is 2219 (Al-6.1Cu-0.3Mn-0.15Zr-0.1V), which has excellent weldability and is used for tanks of space equipment such as rockets. Further, the applicant of the present invention, as an aluminum alloy having further improved high-temperature characteristics, is a "heat-resistant aluminum alloy" (see JP-A-2-213443) and a "method for producing a heat-resistant aluminum alloy material" (JP-A-3-2).
Japanese Patent Application No. 94439). The "heat resistant aluminum alloy" is to obtain heat resistance by optimizing the addition amounts of Mn, Zr, V, and Ag in the Al-Cu-Mg alloy. On the other hand, in the above-mentioned “method for producing a heat resistant aluminum alloy material”, the room temperature strength is improved while maintaining the heat resistance of the Al—Ni based alloy.
In the i-based alloy, NiAl ₃ is grown by setting the temperature gradient in the liquid phase at the solid-liquid interface at the time of melt casting to 5 ° C./or more, and the Mg ₂ Si content and the Cu content are optimized at room temperature to It has improved strength at high temperatures. Further, in US Pat. No. 3,619,181, improvement of heat resistance is recognized by adding scandium (Sc) to an aluminum alloy.

[0004]

However, even with a typical practical alloy 2618 or 2219, the strength is remarkably lowered at a high temperature exceeding 150 ° C. Therefore, especially when using these aluminum alloys as structural materials,
Often used below 150 ° C. For example, in a supersonic Concorde, the outer plate temperature at a cruise speed of Mach 2.2 is about 120 ° C., and therefore, 2618 can be used as the outer plate material. At present, titanium alloys are often used when lightweight members are required in an environment exceeding 150 ° C. However, the titanium alloy is a difficult-to-process material, and the product becomes expensive. Even in the same aluminum alloy, Al-F
The e-Ce-based rapidly solidified powder metallurgy material (PM material) has been improved in heat resistance. However, casting metallurgy materials (IM
It is much more expensive than the material and its range of use is limited. JP-A-2-213443 or JP-A-3-21343
Also in the 294439 publication, the heat resistance temperature is at most 150.
C. and 200.degree. C., and the strength is remarkably reduced when kept at a high temperature for a long time. Further, also in US Pat. No. 3619181, the effect of improving the heat resistance by adding Sc is small.
This is because the relationship between the microstructure and high temperature characteristics has not been clarified, and the optimum microstructure that greatly improves heat resistance is unknown. Therefore, it is difficult to actually manufacture a product with improved heat resistance.

In recent years, there has been a demand for higher speeds for aircraft and improved fuel economy for engines and the like. Furthermore, conversion from these materials to aluminum alloys is required due to cost reduction requirements for products that have used titanium alloys in high temperature environments and weight reduction requirements for products that have used iron and the like. . Therefore, further improvement in heat resistance of the aluminum alloy is desired. The problem to be solved by the present invention is to use casting metallurgy materials (I
(M material) to provide an aluminum alloy having improved heat resistance.

[0006]

The aluminum alloy excellent in heat resistance of the present invention is Zr: 0.05 to 0.50% and S
c: It has a microstructure containing either or both of 0.05 to 1.0% and satisfying at least one of the following (a) and (b). (A) The Al-Zr-based dispersed particles have a size of 35 to 450 angstroms and an interval of 0.005 to 0.6 μm. (B) The Al-Sc-based dispersed particles have a size of 35 to 450 angstroms and a spacing of 0.005 to 0.6 μm.

The present invention specifically relates to Al--Cu or Al.
-Cu-Mg system (claims 2 to 4), Al-Mg-Si system (claims 5 and 6), Al-Zn-Mg system (claim 7,
8), pure Al-based (claim 9), Al-Mn-Mg-based (claims 10 and 11), Al-Mg-based (claims 12 and 13).
And Al-Si-based (claims 14 and 15) applied to aluminum or an aluminum alloy, and the respective heat resistance levels due to the above-mentioned microstructure in which Al-Zr-based dispersed particles and / or Al-Sc-based dispersed particles are dispersed. Can be improved.

[0008]

BEST MODE FOR CARRYING OUT THE INVENTION When Cu, Mg, Zn or the like is added to Al, the amount of solid solution at high temperature increases, so that heat resistance is improved. However, for example, Al-Cu alloy, Al-M
g-Si system alloy or Al-Zn-Mg system alloy 200-
When left at 300 ℃ for a long time, θ phase (CuAl ₂ ),
β phase (Mg ₂ Si) and η phase (MgZn ₂ ), T phase (Al ₂ Mg ₃ Zn ₃ )
However, it becomes coarse and the strength is significantly reduced. Thus, when left at a high temperature for a long time, the equilibrium state of the point of the component and the temperature shown in the phase diagram is finally reached. Therefore, C
There is a limit to the improvement of heat resistance only by adjusting the components such as u, Mg and Zn.

On the other hand, transition elements such as Mn, Cr, Zr and Sc are subjected to appropriate homogenization heat treatment after melt casting, and Al-Mn type, Al-Cr type, Al-Zr type and Al are respectively applied.
-Sc-based dispersed particles are precipitated in the Al matrix. Since the precipitation temperature of these dispersed particles is in the homogenizing heat treatment temperature range, it is extremely stable in the temperature range of about 200 to 300 ° C., and particularly high strength can be maintained even when left at a high temperature for a long time or used. Can be expected. As a result of intensive studies on the relationship between the stable dispersed particles and the high temperature characteristics, the present inventors have found that the dispersed particles have a size and a spacing of 35 to 450 angstroms (hereinafter, A is used as a substitute) and 0.005 to 0. By controlling the structure to 6 μm, the heat resistance of aluminum or aluminum alloy can be improved, and 80 to 300 A and 0.1 to 0.
It has been found that when it is within the range of 4 μm, it is particularly effective in improving the heat resistance.

However, under normal homogenizing heat treatment conditions, Al
Since the -Mn-based dispersed particles grow to several thousand A and the Al-Cr-based dispersed particles grow to about 1000 A, it has been found that a great effect cannot be expected for these dispersed particles. However, the present inventors have found that Al-Zr-based and Al-Sc-based dispersed particles are
By optimizing the added amounts of Zr and Sc and the homogenization heat treatment conditions, the size and the interval are 35 to 450 A, preferably 80 to 300 A, and 0.005 to 0.6 μm, respectively.
It has been found that it is possible to control the texture to desirably 0.1 to 0.4 μm.

The sizes and intervals of Al-Zr-based and Al-Sc-based dispersed particles are 35 to 450 A and 0.00, respectively.
By controlling the texture to 5 to 0.6 μm, these dispersed particles become resistant to the movement of dislocations during high temperature deformation,
The heat resistance is greatly improved. However, the dispersed particle size is 3
If it is less than 5 A, the strength of the dispersed particles is small, and the dispersed particles are cut by the moving dislocations, so that the strength cannot be expected to be greatly improved, and if the dispersed particles exceed 450 A, the moving dislocations bypass the dispersed particles. After all, the strength cannot be expected to be greatly improved. On the other hand, the dispersed particle size is 35
If the distance between the particles is A or more and the distance between the particles is so coarse as to exceed 0.6 μm, the moving dislocations bypass the dispersed particles, and a significant improvement in strength cannot be expected. Further, if the spacing between particles is less than 0.005 μm, the strength may be too high and processing may be difficult. Therefore, the size and spacing of the dispersed particles should be 35 to 450 A, preferably 8
It is necessary to control the texture to 0 to 300 A, and 0.005 to 0.6 μm, preferably 0.1 to 0.4 μm.

The action of each component Zr and Sc form dispersed particles such as ZrAl ₃ and ScAl ₃ during the homogenizing heat treatment. These dispersed particles become resistant when deformed at high temperature and improve heat resistance. Further, it has an effect of hindering the movement of grain boundaries after recrystallization, which is effective for producing fine crystal grains. In the present invention, the size and spacing of the dispersed particles are 35 to 450 A and 0.005, respectively.
It is necessary to control the texture to ˜0.6 μm, and for this purpose, the addition amount of each is preferably 0.05 wt% or more. However, excessive addition easily forms a coarse insoluble intermetallic compound during melt casting, which is a cause of molding failure. In particular, excessive addition of Zr tends to make the microstructure into a fiber-like shape, which results in fracture toughness in specific directions and fatigue properties as well as formability. Deteriorate. Therefore, the added amount of Zr is 0.5 wt%, Sc
It is desirable that the addition amount of is regulated to 1.0 wt% or less. The heat resistance of the aluminum alloy is improved by adding one or both of Zr and Sc within the above range.
When both r and Sc are added, the effect of improving heat resistance becomes large.

V, Mn and Cr form dispersed particles of Al ₂₀ Cu ₂ Mn ₃ and Al ₁₂ Mg ₂ Cr, etc., respectively, during the homogeneous heat treatment. These dispersed particles have an effect of hindering the movement of grain boundaries after recrystallization, and are effective for producing fine crystal grains. In order to obtain these effects, the amounts of V, Mn, and Cr added are preferably 0.05%, 0.05%, and 0.15% or more. However, excessive addition easily causes a coarse insoluble intermetallic compound during melt casting, which causes defective molding. Therefore, the addition amounts of V, Mn, and Cr are 0.15%, 1.5%, and 0.30%, respectively. The following restrictions are desirable.

Ni hardly forms a solid solution in Al and is crystallized as hard fibrous NiAl _{3 in the} matrix by a eutectic reaction with Al during solidification. This NiAl ₃ has a small decrease in strength at high temperatures and has an effect of improving heat resistance.
However, if the added amount of Ni is less than 0.8%, the fiber reinforcing effect is not sufficient. Further, excessive addition causes coarse NiAl ₃ to crystallize, which causes defective molding. For this reason, it is desirable to regulate it to 2.4% or less. Fe
Hardly forms a solid solution in Al and forms a crystallized substance or the like. Because they become starting points of fracture, the amount of Fe 0.5% below, preferably when it is desired to be restricted to 0.25% or less, especially Ni simultaneously adding Al ₉ (Fe-N
i) is formed and the heat resistance is significantly improved. However, 1.
If it exceeds 5%, an insoluble intermetallic compound is likely to be formed. For this reason, it is desirable to be regulated to 1.5% or less.

Cu, Mg, Zn and Si are elements that improve the room temperature and high temperature strength of the aluminum alloy by solid solution strengthening and precipitation strengthening. These improve the strength of the aluminum alloy by the effects of both solid solution strengthening and precipitation strengthening.

Now, the alloy according to claim 2 corresponds to 2000 series, and in addition to Zr and Sc, basically Cu: 1 to 8%.
And if necessary, Mg: 0.1-2.5% is included. If necessary, one or more of Fe, Ni, V, Mn, and Cr may be added to improve heat resistance.
In this type of alloy, if the amount of Cu added is less than 1%, the degree of solid solution and precipitation hardening is small, and sufficient strength cannot be obtained. On the other hand, if it exceeds 8%, crystallized substances having a composition of CuAl ₂ are generated, so that extrudability, forgeability, etc., and moldability at room temperature deteriorate. Therefore, the addition amount of Cu is set to 1 to 8%, preferably 1.5 to 6.8%. Mg
If the addition amount of is less than 0.1%, the degree of solid solution and precipitation hardening is small and sufficient strength cannot be obtained. Meanwhile, 2.
If it exceeds 5%, the room temperature strength becomes too high and the formability is lowered. Therefore, the addition amount of Mg is 0.1 to 2.5%, preferably 0.5 to 1.8%.

The alloy of claim 5 corresponds to the 6000 series, and in addition to Zr and Sc, basically Si: 0.1 to 1.5.
% And Mg: 0.2 to 2%. Further C if necessary
The heat resistance can be improved by adding one or more of u, Fe, Ni, V, Mn, and Cr. In this type of alloy, if the amount of Si added is less than 0.1%, the degree of precipitation hardening is small and sufficient strength cannot be obtained.
On the other hand, if it exceeds 1.5%, large crystallized substances having a composition of Mg ₂ Si are likely to occur. Therefore, extrudability, forgeability, etc., and moldability at room temperature are deteriorated. For this reason,
The amount of Si added is 0.1 to 1.5%, preferably 0.2 to
1.2%. If the added amount of Mg is less than 0.2%, the degree of solid solution and precipitation hardening is small and sufficient strength cannot be obtained. On the other hand, if it exceeds 2%, the strength at room temperature becomes too high and the formability deteriorates. Therefore, the added amount of Mg is 0.
2 to 2%, preferably 0.35 to 1.5%. In addition, when Cu is added to this type of alloy, strength is increased because Mg ₂ Si is finely precipitated. However, the addition amount is 0.0
If it is less than 5%, the effect is small, and if it exceeds 1%, the ordinary temperature strength becomes too high and the formability is lowered, and at the same time, the corrosion resistance is also lowered. Therefore, the addition amount of Cu is set to 0.05 to 1.0%.

The alloy of claim 7 corresponds to the 7000 series, and in addition to Zr and Sc, basically Zn: 0.1 to 10%.
And Mg: 0.1-3.5%. If necessary, one or more of Cu, Fe, Ni, V, Mn and Cr may be added to improve heat resistance. In this type of alloy, if the amount of Zn added is less than 0.1%, the degree of solid solution and precipitation hardening is small and sufficient strength cannot be obtained. On the other hand, if it exceeds 10%, the hot workability deteriorates,
Rolling cracks are likely to occur. Therefore, the amount of Zn added is 0.1 to 10%, preferably 0.8 to 6.7%. If the addition amount of Mg is less than 0.1%, the degree of solid solution and precipitation hardening is small and sufficient strength cannot be obtained. On the other hand, if it exceeds 3.5%, the ordinary temperature strength becomes too high and the formability is deteriorated. Therefore, the added amount of Mg is 0.1-3.
5%, preferably 0.1-2.9%. Also, Cu
Addition of improves the age hardenability. However, if it is less than 0.1%, the effect is small, and if it exceeds 3%, the ordinary temperature strength becomes too high and the formability is lowered, and at the same time, the corrosion resistance is also lowered. Therefore, the addition amount of Cu in this system is 0.1 to 3%, preferably 0.1 to 2.6%.

The alloy of claim 9 corresponds to 1000 series, and Z
In addition to r and Sc, one or more of Fe, Ni, V, Mn, Cr and Cu are added to improve heat resistance.

The alloy according to claim 10 corresponds to the 3000 series, and in addition to Zr and Sc, basically Mn: 0.05-.
Includes 1.5% and Mg: 0.05 to 1.5%. If necessary, one or more of Cu, Fe, Ni, V and Cr can be added to improve heat resistance. In this type of alloy, if the amount of addition of Mg is less than 0.05%, the degree of solution hardening is small and sufficient strength cannot be obtained. On the other hand, if it exceeds 1.5%, the normal temperature strength becomes too high and the moldability deteriorates. Therefore, the addition amount of Mg is 0.0
5 to 1.5%, preferably 0.2 to 1.3%. The amount of Mn added is as described above, but it is preferably 0.3 to 1.3% in this type of alloy. Also, C
Addition of u causes age hardening. However, if less than 0.05%, the effect is small. Further, if it exceeds 0.4%, the corrosion resistance decreases. Therefore, the amount of Cu added in this system is 0.05 to 0.4%, preferably 0.05 to 0.25.
%.

The alloy according to claim 12 corresponds to 5000 series, and basically Mg: 0.05 to 7 in addition to Zr and Sc.
%including. If necessary, Cu, Fe, Ni, V, Mn,
Heat resistance can be improved by adding one or more of Cr. In this type of alloy, if the addition amount of Mg is less than 0.05%, the degree of solution hardening is small and sufficient strength cannot be obtained. On the other hand, if it exceeds 7%,
The normal temperature strength becomes too high, the formability is lowered, the hot workability is lowered, and rolling cracks are likely to occur. Furthermore, stress corrosion cracking is likely to occur regardless of the type of tempering. Therefore, the addition amount of Mg is 0.05 to 7%, preferably 0.5 to 5.6%.

The alloy according to claim 14 corresponds to the 4000 series, and in addition to Zr and Sc, basically Si: 0.2 to 22.
%including. If necessary, Mg, Cu, Fe, Ni, V,
The heat resistance can be improved by adding one or more of Mn and Cr. In this type of alloy, Si
If the addition amount of is less than 0.2%, the degree of solid solution and precipitation hardening is small and sufficient strength cannot be obtained. On the other hand, 22%
If it exceeds, casting cracks are likely to occur. For this reason, Si
Addition amount of 0.2 to 22%, desirably 0.2 to 18%
And If the addition amount of Mg is less than 0.05%, the degree of solid solution and precipitation hardening is small and sufficient strength cannot be obtained. If it exceeds 1.5%, the increase in strength due to age hardening becomes small. Therefore, the addition amount of Mg is 0.05 to
It is set to 1.5%, preferably 0.05 to 1.3%. In addition, addition of Cu causes age hardening. But 0.0
If it is less than 5%, the effect is small, and if it exceeds 1.5%, the corrosion resistance decreases. Therefore, in this system, the added amount of Cu is 0.
05 to 1.5%, preferably 0.05 to 1.3%.

The product of the alloy of the present invention may be in the form of a plate, a profile, a forged material, or a cast material. In the case of the plate, for example, after ingoting by melting casting, homogenization heat treatment, hot working It can be provided by rolling, and if necessary, cold rolling, solution heat treatment water quenching, tension straightening, aging treatment, and the like. Further details will be given below.

In melt casting, it is desirable to regulate the hydrogen concentration in the molten metal by degassing before casting. Hydrogen contained in the molten metal has extremely low solid solubility in the aluminum alloy, so that it forms microporosity during casting and remains as small voids in the final product. These cavities tend to be the starting points of fracture and cause the fracture toughness and fatigue properties of the product to deteriorate. In particular, in products with low workability such as rolling ratio and wrought degree after melting and casting, microporosity is not destroyed and tends to remain as cavities. For this reason, it is desirable that the hydrogen gas concentration in the molten metal be regulated to 0.05 cc / 100 ml Al or less, preferably 0.02 cc / 100 ml Al.

The homogenizing heat treatment is for re-dissolving crystallized substances harmful to fracture toughness and fatigue properties, and in particular, the size of Al-Zr-based and Al-Sc-based dispersed particles is 35 to 450 A,
Desirably 80 to 300 A, the interval is 0.005
˜0.6 μm, preferably 0.1 to 0.4 μm in order to control the texture. Optimum homogenization heat treatment condition is 350 ℃
As described above, it is preferably 2 hours or more at 380 ° C. or more. Three
If the temperature is lower than 50 ° C., the temperature is too low to re-dissolve the crystallized substance, and if the temperature exceeds 470 ° C., the dispersed particles become coarse and it becomes difficult to obtain the dispersed particle size necessary for improving the heat resistance. For this reason, the homogenization heat treatment is performed at 350 to 470 ° C. for 2 hours.
The above is desirable, and more desirably, it is 2 hours or more at 380 to 470 ° C.

If re-dissolution of the crystallized product is insufficient under the homogenizing heat treatment conditions, hot rolling may be started immediately after reheating rapidly to the required temperature. At this time, it is better if it can be rapidly heated with an induction heater, etc.
The temperature may be raised stepwise within the range of 350 ° C to the reheating temperature. On the other hand, the main components of the crystallized substances are Fe and S
When the added amount of i or the like is small and crystallized substances are less likely to be generated componentally, the homogenizing heat treatment temperature can be performed at a low temperature of less than 350 ° C. In addition, deterioration of toughness due to crystallized substances,
Even when the alloy of the present invention is used for applications where the increase in fatigue crack propagation rate does not matter, the homogenizing heat treatment temperature is set to 3
It may be performed at a low temperature of less than 50 ° C. The optimum soaking conditions (temperature, time) naturally change depending on the solidification rate during melting and casting, the heating rate during soaking, etc. In short, the microstructure defined in the present invention is the final product stage. It is only necessary to obtain the above, and the above-mentioned conditions of 350 ° C. to 470 ° C., preferably 380 ° C. to 470 ° C. for 2 hours or more are typical homogenizing heat treatment conditions. Further, since the heat resistance is improved if the microstructure defined in the present invention is obtained, it is natural that the effect can be expected in the aluminum alloys other than the alloy system defined in claims 2 to 15.

When the alloy of the present invention is used as the core material and a laminated material having the pure aluminum alloy or the 7072 alloy as the skin material is manufactured, the diffusion of the core material components such as Cu, Mg, and Zn into the skin material is reduced and corrosion resistance is improved. In order to prevent the deterioration, it is desirable that the core material and the skin material are separately homogenized and heat-treated, then both sides or one side of the core material are covered with the skin material, and the core material and the skin material are pressure-bonded by the following hot rolling to form a combined material.

Hot rolling and cold rolling are carried out in accordance with ordinary methods. However, when it is necessary to refine the crystal grains in the final product, the hot rolling inlet and outlet temperatures are both lowered. It is desirable to increase the amount of work hardening introduced at the time of rolling, and it is particularly necessary for products in which cold rolling after hot rolling is omitted. The refinement of crystal grains improves fracture toughness and fatigue characteristics, and further improves moldability. Hot rolling is preferably started at 410 ° C. or lower after taking out the ingot from the furnace after the homogenization heat treatment is completed. When hot rolling is started from a temperature exceeding 410 ° C, the recovery amount during rolling is large and the work hardening amount is drastically reduced. Further, when the hot rolling outlet temperature exceeds 250 ° C., recrystallization is completed and grain growth is likely to occur during cooling, and in particular, cold rolling is omitted and heat treatment such as solution treatment is performed in the next manufacturing process. In products, grain growth easily occurs during heat treatment. Further, if the hot rolling outlet temperature is less than 210 ° C., remarkable rolling scratches are likely to occur on the rolled surface. Therefore, the hot rolling outlet temperature is preferably 210 ° C. or higher and 250 ° C. or lower.

The rolled sheet after the hot rolling is subjected to cold rolling if necessary, and further subjected to solution treatment and quenching as necessary. The heat treatment furnace may be a batch furnace, a continuous baking furnace, or a molten salt bath furnace.
Either water injection or air injection may be used. Solution treatment and quenching re-dissolve the soluble intermetallic compound and sufficiently suppress reprecipitation during cooling. Therefore, JIS-W-110 is used.
3. It is desirable to carry out under the conditions specified in MIL-H-6088F. The temperature rising rate is preferably kept at 5 ° C./min or more in order to prevent the coarsening of crystal grains which occurs during the temperature rise to the solution treatment temperature and to obtain fine recrystallization excellent in fracture toughness and fatigue properties.

In order to prevent coarsening of Al-Zr-based and Al-Si-based dispersed particles, all heat treatments (including solution treatment) after the homogenization treatment are completed at the lowest possible temperature and in the shortest time. Of course, it is desirable.
Hardened materials may be subjected to cold working up to 10% in terms of elongation as necessary using a cold rolling mill or stretcher for the purpose of straightening strain during hardening and increasing the proof stress value of the final product. Do it. Further, the product strength may be increased by room temperature aging or artificial aging.

In the present invention, the size of dispersed particles was determined by a TEM photograph (× 100,000 times) using the sample after the final heat treatment. The size of the dispersed particles is obtained by averaging the maximum length of each particle (200 or more). Further, the interval is calculated by the line intercept method (line length 20 μm or more). In the case of a laminated material,
Observe the 1/4 thick plate of the heartwood.

[0032]

The present invention will be described in more detail with reference to the following examples. (Example 1 ... Al-Cu system) The aluminum alloys having the chemical components (1) and (2) shown in the footnotes of Table 1 below were each melt-cast to form a 30 mm thick ingot, and both sides of the ingot were chamfered. (2.5 mm on one side and 5 mm on both sides). Next, after homogenizing heat treatment under the conditions shown in Table 1, immediately hot rolling was performed to a thickness of 3 mm, followed by cold rolling to obtain a plate having a thickness of 2.5 mm.
The cold-rolled material was solution quenched at 530 ° C for 35 minutes and then immediately water-quenched, and then heat-treated at 188 ° C for 36 hours.
6 materials were used. The T6 material was observed by TEM for microstructure and subjected to a tensile test.

[0033]

[Table 1]

The microstructure (dispersed particle size, spacing) was measured by the method described above, and the tensile properties (proof stress, elongation) were measured using JIS No. 13B test pieces taken in the direction perpendicular to the rolling direction, and the tensile speed was 0. It was determined by conducting a tensile test at 3 mm / min. In addition, at each temperature of 150 ° C. or higher, tensile was started after holding the temperature for 30 minutes. The results are shown in Table 1. As shown here, Examples 1 to 3 of the present invention have high strength even in a high temperature range (up to 250 ° C) as compared with Comparative Example 1 not containing Sc. On the other hand, Comparative Example 2 in which the dispersed particle size and the spacing between particles exceed the specifications of the present invention is almost the same as Comparative Example 1, and the elongation is also inferior to the inventive example. Further, in Comparative Example 3 in which the dispersed particle size does not meet the requirements of the present invention, the increase in strength in the high temperature region peaks, and the homogenization treatment temperature is low, and the crystallized substance remains, so that the elongation is high. It is inferior to the inventive examples.

(Example 2 ... Al-Cu-Mg system) The aluminum alloys of chemical components (1) to (4) shown in the footnotes of Table 2 below were each melt-cast and made into a 30 mm thick ingot. Both surfaces were chamfered (one side 2.5 mm, both sides 5 mm).
Then, after homogenizing heat treatment for 8 hours at 400 ° C, immediately after 3 m
hot rolling to m thickness, followed by cold rolling to 2.5
A plate having a thickness of mm was used. The cold rolled material was solution quenched at 520 ° C for 35 minutes immediately followed by water quenching, then at 200 ° C for 20 hours.
Heat treatment of r was performed to obtain T6 material. As in Example 1, the T6 material was observed for microstructure by TEM and subjected to a tensile test.

[0036]

[Table 2]

Table 2 shows the measurement results of the microstructure and the tensile test results. The measuring method is the same as that of the example, and the tensile test method is 30 minutes or 100 at each temperature of 150 ° C. or higher.
hr The same as Example 1 except that tension was started after the temperature was maintained. As shown in Table 2, Examples 4 and 5 of the present invention containing Sc and Zr have high strength even in a high temperature range (up to 250 ° C) as compared with Comparative Example 4 not containing these. Inventive Example 6 containing both Zr and Sc has higher strength.

(Example 3 ... Al-Mg-Si system) Aluminum alloys having chemical components (1) to (3) shown in the footnotes of Table 2 below were each melt-cast to form a 30 mm thick ingot, and the ingot was formed. Both surfaces were chamfered (one side 2.5 mm, both sides 5 mm).
Next, after homogenizing heat treatment for 6 hours at 450 ° C, immediately after 3m
hot rolling to m thickness, followed by cold rolling to 2.5
A plate having a thickness of mm was used. The cold rolled material was solution quenched at 520 ° C. for 30 minutes and immediately water quenched, then at 160 ° C. for 18 h.
Heat treatment of r was performed to obtain T6 material. As in Example 1, the T6 material was observed for microstructure by TEM and subjected to a tensile test.

[0039]

[Table 3]

Table 3 shows the measurement results of the microstructure and the tensile test results. The measuring method and the test method are the same as in Example 1. As shown in Table 3, Example 7 of the present invention containing Sc
Is higher than the high temperature range (~
It has high strength even at 250 ° C. Inventive Example 8 containing both Zr and Sc has higher strength.

(Example 4 ... Al-Zn-Mg system) Aluminum alloys having chemical components (1) to (3) shown in the footnotes of Table 4 below were each melt-cast to form a 30 mm thick ingot, and the ingot was formed. Both surfaces were chamfered (one side 2.5 mm, both sides 5 mm).
Then, after homogenizing heat treatment at 430 ° C. for 12 hours, immediately perform 3
1. Hot rolling is performed to a thickness of mm, and then cold rolling is performed.
The plate was 5 mm thick. The cold rolled material was solution quenched at 480 ° C for 35 minutes immediately after water quenching and then at 120 ° C for 24 hours.
Heat treatment was performed for hr to obtain T6 material. As in Example 1,
The T6 material was observed by TEM for microstructure and subjected to a tensile test.

[0042]

[Table 4]

Table 4 shows the measurement results of the microstructure and the tensile test results. The measuring method and the test method are the same as in Example 1. As shown in Table 4, Example 9 of the present invention containing Sc
Compared with Comparative Example 6 that does not contain Sc, is a high temperature range (~
It has high strength even at 250 ° C. Inventive Example 10 containing both Zr and Sc has higher strength.

Example 5: Al-Mg system Table 5 below
Each of the aluminum alloys having the chemical components (1) to (3) shown in the footnote of 1. was melt-cast to form a 30 mm thick ingot, and both surfaces of the ingot were chamfered (one side 2.5 mm, both sides 5 mm). next,
After the homogenizing heat treatment at 460 ° C. for 4 hours, hot rolling was immediately performed to a thickness of 3 mm, and then cold rolling was performed to obtain a plate having a thickness of 2.5 mm. The cold rolled material was annealed at 345 ° C. for 2 hours to obtain an O material. As in Example 1, the O material was observed for a microstructure by TEM and subjected to a tensile test.

[0045]

[Table 5]

Table 5 shows the measurement results of the microstructure and the tensile test results. The measuring method and the test method are the same as in Example 1. As shown in Table 5, Example 1 of the present invention containing Sc
1 has high strength even in a high temperature range (up to 250 ° C.) as compared with Comparative Example 7 that does not contain Sc. Zr and S
Inventive Example 12 containing both of c has higher strength.

Example 6 Pure Al System Aluminum alloys of chemical components (1) to (3) shown in the footnotes of Table 6 below were each melt-cast to form a 30 mm thick ingot, and both surfaces of the ingot were The surface was ground (2.5 mm on one side and 5 mm on both sides). Then 46
After the homogenizing heat treatment at 0 ° C. for 8 hours, it was immediately hot-rolled to a thickness of 3 mm and then cold-rolled to obtain a plate having a thickness of 2.5 mm. The cold rolled material was annealed at 345 ° C. for 2 hours to obtain an O material. As in Example 1, the O material was observed for a microstructure by TEM and subjected to a tensile test.

[0048]

[Table 6]

Table 6 shows the measurement results of the microstructure and the tensile test results. The measuring method and the test method are the same as in Example 1. As shown in Table 6, Example 1 of the present invention containing Sc
3 has high strength even in a high temperature range (up to 250 ° C.) as compared with Comparative Example 8 that does not contain Sc. Zr and S
Inventive Example 14 containing both c has higher strength.

(Example 7 ... Al-Mn-Mg system) Aluminum alloys having chemical components (1) to (3) shown in the footnotes of Table 7 below were each melt-cast to form a 30 mm thick ingot, and the ingot was formed. Both surfaces were chamfered (one side 2.5 mm, both sides 5 mm).
Next, after homogenizing heat treatment for 4 hours at 440 ° C, immediately after 3 m
hot rolling to m thickness, followed by cold rolling to 2.5
A plate having a thickness of mm was used. The cold rolled material was annealed at 345 ° C. for 2 hours to obtain an O material. As with Example 1, this O material had T
Observation of the microstructure by EM and a tensile test were performed.

[0051]

[Table 7]

Table 7 shows the measurement results of the microstructure and the tensile test results. The measuring method and the test method are the same as in Example 1. As shown in Table 7, Example 1 of the present invention containing Sc
5 has high strength even in a high temperature range (up to 250 ° C.) as compared with Comparative Example 9 containing no Sc. Zr and S
Inventive Example 16 containing both c is even stronger.

(Example 8 ... Al-Si system) Table 8 below
Each of the aluminum alloys of chemical components (1) to (3) shown in the footnote of 1. was melt-cast and made into a φ150 mm ingot, and the surface of the ingot was chamfered (2.5 mm). Next, at 470 ° C for 6 hours
Immediately after the homogenization heat treatment of (2), it was extruded into a 20 mm thick x 120 mm wide. The extruded material was water-quenched immediately after the solution treatment at 505 ° C. for 45 minutes, and then heat-treated at 170 ° C. for 10 hours to obtain a T6 material.

[0054]

[Table 8]

Table 8 shows the measurement results of the microstructure and the tensile test results. The method for measuring the microstructure is the same as in Example 1, and the tensile test method is 1 at each temperature of 150 ° C. or higher.
Same as Example 1 except that pulling was started after holding for 0000 hours. As shown in Table 8, Inventive Example 17 containing Sc has higher strength in a high temperature range (up to 250 ° C) as compared with Comparative Example 10 containing no Sc. Inventive Example 18 containing both Zr and Sc has higher strength.

[0056]

According to the present invention, by controlling the structure such that one or both of Al-Zr-based or Al-Sc-based dispersed particles are dispersed in aluminum or an aluminum alloy at a predetermined size and a predetermined interval, The heat resistance level of each of the aluminum alloys can be improved. 200 which has been used for heat resistance
By applying the present invention to a 0 series aluminum alloy,
It is possible to obtain an aluminum alloy having an extremely high level of heat resistance, and it is possible to apply the aluminum alloy even in the fields where titanium alloys, Fe and the like have been conventionally used.

Claims (16)

[Claims] 1. Zr: 0.05 to 0.50% (% by weight,
The same shall apply hereinafter) and Sc: 0.05 to 1.0%, or both, and has a microstructure satisfying at least one of the following (a) and (b). Excellent aluminum alloy. (A) The Al-Zr-based dispersed particles have a size of 35 to 450 angstroms and an interval of 0.005 to 0.6 μm. (B) The Al-Sc-based dispersed particles have a size of 35 to 450 angstroms and a spacing of 0.005 to 0.6 μm. 2. Zr: 0.005 to 0.50% and Sc:
An Al-Cu alloy containing 0.005 to 1.0% of one or both of them and further containing Cu: 1 to 8%, which satisfies at least one of the following (a) and (b): An aluminum alloy having excellent heat resistance characterized by having a structure. (A) The Al-Zr-based dispersed particles have a size of 35 to 450 angstroms and an interval of 0.005 to 0.6 μm. (B) The Al-Sc-based dispersed particles have a size of 35 to 450 angstroms and a spacing of 0.005 to 0.6 μm. 3. The Al—Cu based alloy is Zr: 0.0.
5 to 0.50% and Sc: 0.05 to 1.0%, one or both of them, Cu: 1 to 8%, further Fe: ≤ 1.5%, Ni: 0. 8-2.4%, V:
0.05-0.15%, Mn: 0.05-1.5%, C
The aluminum alloy having excellent heat resistance according to claim 2, characterized in that r: 0.15 to 0.30% of one type or two or more types, and the balance is Al and impurities. 4. The aluminum alloy having excellent heat resistance according to claim 2 or 3, further containing Mg: 0.1 to 2.5%. 5. Zr: 0.05 to 0.50% and Sc:
One or both of 0.05 to 1.0% is included, and further, Mg: 0.2 to 2%, Si: 0.1 to 1.5.
% Al-Mg-Si alloy, which has a microstructure satisfying at least one of the following (a) and (b): (A) The Al-Zr-based dispersed particles have a size of 35 to 450 angstroms and an interval of 0.005 to 0.6 μm. (B) The Al-Sc-based dispersed particles have a size of 35 to 450 angstroms and a spacing of 0.005 to 0.6 μm. 6. The Al—Mg—Si alloy is Zr:
One or both of 0.05 to 0.50% and Sc: 0.05 to 1.0%, and Mg: 0.2 to 2%,
Si: 0.1 to 1.5% included, and further Cu: 0.0
5 to 1.0%, Fe: ≤1.5%, Ni: 0.8 to 2.
4%, V: 0.05 to 0.15%, Mn: 0.05 to
Aluminum having excellent heat resistance according to claim 5, characterized in that it contains one or more of 1.5% and Cr: 0.15 to 0.30%, and the balance is Al and impurities. alloy. 7. Zr: 0.05 to 0.50% and Sc:
One or both of 0.05 to 1.0% is contained, and Zn: 0.1 to 10%, Mg: 0.1 to 3%.
An Al-Zn-Mg-based alloy containing 5%, which has a microstructure satisfying at least one of the following (a) and (b), and is an aluminum alloy excellent in heat resistance. (A) The Al-Zr-based dispersed particles have a size of 35 to 450 angstroms and an interval of 0.005 to 0.6 μm. (B) The Al-Sc-based dispersed particles have a size of 35 to 450 angstroms and a spacing of 0.005 to 0.6 μm. 8. The Al—Zn—Mg-based alloy is Zr:
One or both of 0.05 to 0.50% and Sc: 0.05 to 1.0%, and Zn: 0.1 to 10
%, Mg: 0.1 to 3.5%, and further Cu:
0.1-3.0%, Fe: ≤1.5%, Ni: 0.8-
2.4%, V: 0.05 to 0.15%, Mn: 0.05
To 1.5%, Cr: 0.15 to 0.30%, and one or more of them are contained, and the balance is Al and impurities, and the heat resistance is excellent according to claim 7. Aluminum alloy. 9. Zr: 0.05 to 0.50% and Sc:
It contains either or both of 0.05 to 1.0%, and Fe: ≤1.5%, Ni: 0.8 to 2.4.
%, V: 0.05 to 0.15%, Mn: 0.05 to 1.
5%, Cr: 0.15 to 0.30%, Cu: ≤0.15
%, And the balance comprises Al and impurities, and the aluminum alloy with excellent heat resistance according to claim 1. 10. Zr: 0.05 to 0.50% and Sc:
Either or both of 0.05 to 1.0% are included, and Mn: 0.05 to 1.5% and Mg: 0.05.
In an Al-Mn-Mg-based alloy containing 0.5 to 1.5%, an aluminum alloy having excellent heat resistance, which has a microstructure satisfying at least one of the following (a) and (b). (A) The Al-Zr-based dispersed particles have a size of 35 to 450 angstroms and an interval of 0.005 to 0.6 μm. (B) The Al-Sc-based dispersed particles have a size of 35 to 450 angstroms and a spacing of 0.005 to 0.6 μm. 11. The Al-Mn-Mg-based alloy is Z
r: 0.05 to 0.50% and Sc: 0.05 to 1.0%
One or both of them are included, and Mn: 0.05 to
1.5%, including Mg: 0.05 to 1.5%, and
Cu: 0.05-0.4%, Fe: ≤1.5%, Ni:
0.8-2.4%, V: 0.05-0.15%, Cr:
0.15 to 0.30% out of one or more,
The balance comprises Al and impurities.
Al alloy with excellent heat resistance described in No. 0. 12. Zr: 0.05 to 0.50% and Sc:
An Al-Mg-based alloy containing either or both of 0.05 to 1.0% and further containing Mg: 0.05 to 7% satisfies at least one of the following (a) and (b): An aluminum alloy having excellent heat resistance, which has a microstructure that (A) The Al-Zr-based dispersed particles have a size of 35 to 450 angstroms and an interval of 0.005 to 0.6 μm. (B) The Al-Sc-based dispersed particles have a size of 35 to 450 angstroms and a spacing of 0.005 to 0.6 μm. 13. The Al—Mg alloy is Zr: 0.
One or both of 05: 0.50% and Sc: 0.05-1.0%, Mg: 0.05-7%, and Cu: 0.05-0.3% , Fe: ≤1.
5%, Ni: 0.8 to 2.4%, V: 0.05 to 0.1
5%, Mn: 0.05 to 1.5%, Cr: 0.15
The Al alloy having excellent heat resistance according to claim 12, wherein one or more of 0.30% is contained and the balance is Al and impurities. 14. Zr: 0.05 to 0.50% and Sc:
At least one of the following (a) and (b) is satisfied in an Al-Si-based alloy containing one or both of 0.05 to 1.0% and further containing Si: 0.2 to 22%. An aluminum alloy having excellent heat resistance, which has a microstructure that (A) The Al-Zr-based dispersed particles have a size of 35 to 450 angstroms and an interval of 0.005 to 0.6 μm. (B) The Al-Sc-based dispersed particles have a size of 35 to 450 angstroms and a spacing of 0.005 to 0.6 μm. 15. The Al—Si alloy has a Zr: 0.05.
˜0.50% and Sc: 0.05 to 1.0%, either or both, and Si: 0.2 to 22%,
Furthermore, Mg: 0.05-1.5%, Cu: 0.05-
1.5%, Fe: ≤1.5%, Ni: 0.8 to 2.4
%, V: 0.05 to 0.15%, Mn: 0.05 to 1.
The Al alloy having excellent heat resistance according to claim 14, characterized in that it contains one or two or more of 5% and Cr: 0.15 to 0.30%, and the balance is Al and impurities. 16. The aluminum alloy having excellent heat resistance according to claim 1, which has a microstructure satisfying at least one of the following (a) and (b). (A) The Al-Zr-based dispersed particles have a size of 80 to 300 angstroms and an interval of 0.1 to 0.4 μm. (B) The Al-Sc-based dispersed particles have a size of 80 to 300 angstroms and an interval of 0.1 to 0.4 μm.