KR101197952B1 - Method for producing aluminum alloy thick plate and aluminum alloy thick plate - Google Patents

Abstract

A dissolution process containing a predetermined amount of Mg, and at least one of Si, Fe, Cu, Mn, Cr, Zn, Ti, and Zr, and the balance of which dissolves an aluminum alloy composed of Al and inevitable impurities ( S1), a dehydrogenation gas process (S2) for removing hydrogen gas from the molten aluminum alloy, a filtration process (S3) for removing inclusions from the aluminum alloy from which hydrogen gas has been removed, and an aluminum alloy from which the inclusions have been removed is cast. The casting process (S4) to manufacture, the slice process (S5) which slices the said ingot and manufactures the aluminum alloy thick plate of predetermined thickness, and hold | maintains the aluminum alloy thick plate of predetermined thickness for 1 hour or more at the temperature below 400 degreeC or more melting | fusing point It is a manufacturing method of the aluminum alloy thick plate characterized by sequentially performing the heat processing process (S6) heat-processing.

Description

Manufacturing Method of Aluminum Alloy Plate and Aluminum Alloy Plate {METHOD FOR PRODUCING ALUMINUM ALLOY THICK PLATE AND ALUMINUM ALLOY THICK PLATE}

The present invention relates to a method for producing an aluminum alloy thick plate and to an aluminum alloy thick plate.

Generally, aluminum alloy materials, such as aluminum alloy thick plates, are used for various uses. For example, semiconductor related devices, such as a base substrate, a conveying apparatus, and a chamber for vacuum apparatuses; Electrical and electronic components and their manufacturing apparatus; Household goods; Machine parts and the like.

Such aluminum alloy materials are generally manufactured as follows. That is, an aluminum alloy as a raw material is dissolved and cast to produce an ingot, homogenized and heat treated as necessary, and then the ingot is rolled to a predetermined thickness (see, for example, paragraphs 0037 to 0045 of Patent Document 1). .

In addition, the following material is used as a die material used for a press die. That is, steel, cast steel, etc. are used for mass production production, and zinc alloy casting material, aluminum alloy casting material, etc. are used as a starting use. Moreover, in recent years, since there exists a tendency for small quantity of various products, whole body materials, such as a rolled material of aluminum alloy and a forging material, are spreading | spreading for small and medium quantity production.

Japanese Patent Publication No. 2005-344173

However, there existed a problem shown below in the manufacturing method of the aluminum alloy material by the said rolling.

(1) In the method of rolling after casting, since the control of the surface state and the flatness (especially the flatness in the longitudinal direction) of the rolling plate is made only by the rolling roll, hot rolling also forms a thick oxide film on the surface of the rolling plate. Therefore, control of surface state and flatness was difficult.

(2) Since it is difficult to control plate | board thickness with a rolling roll, it was difficult to aim at the improvement of plate | board thickness precision. Moreover, since the magnitude | size of the intermetallic compound becomes large in the center part of a plate thickness direction, in the case of an armite process, the nonuniformity was easy to generate | occur | produce in the cross section and the surface of a plate thickness direction. In addition, in the case of rolling the ingot, the cost increased because the work process was increased by increasing the number of rolling.

SUMMARY OF THE INVENTION The present invention has been made in view of the above problems, and provides a method for producing an aluminum alloy thick plate that has excellent productivity, can easily control surface state and flatness, and can improve plate thickness precision, and surface state. It is an object to provide an aluminum alloy thick plate excellent in flatness and plate thickness precision.

1st invention of this application WHEREIN: The said aluminum alloy contains Mg: 1.5 mass% or more and 12.0 mass% or less in the method of manufacturing an aluminum alloy thick plate from an aluminum alloy, Si: 0.7 mass% or less, Fe: 0.8 mass It contains at least one of% or less, Cu: 0.6% by mass or less, Mn: 1.0% by mass or less, Cr: 0.5% by mass or less, Zn: 0.4% by mass or less, Ti: 0.1% by mass or less, Zr: 0.3% by mass or less. In addition, the remainder is composed of Al and unavoidable impurities, the melting process for dissolving the aluminum alloy, the dehydrogenation gas process for removing hydrogen gas from the molten aluminum alloy, the removal of inclusions from the aluminum alloy from which hydrogen gas is removed A filtration process, a casting process of casting an aluminum alloy from which the inclusions are removed, to manufacture an ingot, a slicing process of slicing the ingot to produce an aluminum alloy thick plate having a predetermined thickness, and an egg of a predetermined thickness. Minyum the alloy steel plate is characterized by conducting the heat treatment step for heat treatment by keeping at least one hour at a temperature below the melting point above 400 ℃ sequentially.

In the second invention of the present application, in the method for producing an aluminum alloy thick plate from an aluminum alloy, the aluminum alloy contains Mn: 0.3% by mass or more and 1.6% by mass or less, and Si: 0.7% by mass or less and Fe: 0.8% by mass. It contains at least one of% or less, Cu: 0.5% by mass or less, Mg: 1.5% by mass or less, Cr: 0.3% by mass or less, Zn: 0.4% by mass or less, Ti: 0.1% by mass or less, and Zr: 0.3% by mass or less. In addition, the remainder is composed of Al and unavoidable impurities, the melting process for dissolving the aluminum alloy, the dehydrogenation gas process for removing hydrogen gas from the molten aluminum alloy, the removal of inclusions from the aluminum alloy from which hydrogen gas is removed A filtration process, a casting process of casting an aluminum alloy from which the inclusions are removed, to manufacture an ingot, a slicing process of slicing the ingot to produce an aluminum alloy thick plate having a predetermined thickness, and an egg of a predetermined thickness. Minyum the alloy steel plate is characterized by conducting the heat treatment step for heat treatment by keeping at least one hour at a temperature below the melting point above 400 ℃ sequentially.

In the third invention of the present application, in the method for producing an aluminum alloy thick plate from an aluminum alloy, the aluminum alloy contains Si: 0.2% by mass or more and 1.6% by mass or less, Mg: 0.3% by mass or more and 1.5% by mass or less. Fe: 0.8 mass% or less, Cu: 1.0 mass% or less, Mn: 0.6 mass% or less, Cr: 0.5 mass% or less, Zn: 0.4 mass% or less, Ti: 0.1 mass% or less, Zr: 0.3 mass% or less 1 type, and the remainder is composed of Al and unavoidable impurities, the dissolution process of dissolving the aluminum alloy, the dehydrogenation gas process of removing hydrogen gas from the dissolved aluminum alloy, from the aluminum alloy from which hydrogen gas has been removed A filtration process for removing inclusions, a casting process for producing an ingot by casting an aluminum alloy from which the inclusions are removed, a slicing process for slicing the ingot to produce an aluminum alloy thick plate having a predetermined thickness, and a small The aluminum alloy plate having a thickness and characterized by conducting the heat treatment step of heat treatment by keeping at least one hour at a temperature below the melting point above 400 ℃ sequentially.

In the fourth invention of the present application, in the method for producing an aluminum alloy thick plate from an aluminum alloy, the aluminum alloy contains Mg: 0.4% by mass or more and 4.0% by mass or less, Zn: 3.0% by mass or more and 9.0% by mass or less. Si: 0.7 mass% or less, Fe: 0.8 mass% or less, Cu: 3.0 mass% or less, Mn: 0.8 mass% or less, Cr: 0.5 mass% or less, Ti: 0.1 mass% or less, Zr: 0.25 mass% or less 1 type, and the remainder is composed of Al and unavoidable impurities, the dissolution process of dissolving the aluminum alloy, the dehydrogenation gas process of removing hydrogen gas from the dissolved aluminum alloy, from the aluminum alloy from which hydrogen gas has been removed A filtration process for removing inclusions, a casting process for producing an ingot by casting an aluminum alloy from which the inclusions are removed, a slicing process for slicing the ingot to produce an aluminum alloy thick plate having a predetermined thickness, and a small The heat treatment process of heat-treating the aluminum alloy thick plate of a fixed thickness at 350 degreeC or more and less than melting | fusing point for 1 hour or more is performed sequentially, It is characterized by the above-mentioned.

In the said 1st-4th invention, it is preferable to employ | adopt the following structure.

(A) After the heat treatment step, a surface smoothing treatment step of performing a surface smoothing treatment on the surface of the aluminum alloy thick plate is performed. In addition, in such a structure, it is preferable to perform the said surface smoothing process by 1 or more types chosen from the cutting method, the grinding method, and the grinding | polishing method.

(B) In the said slicing process, it has thickness which is equal from the center of thickness direction toward each surface of the thickness direction, and has the thickness of T / 30-T / 5 in the case of making thickness of the said ingot T. The thickness direction center part is removed from the ingot.

In the fifth invention of the present application, in the method for producing an aluminum alloy thick plate from an aluminum alloy, the aluminum alloy contains Mg: 1.5 mass% or more and 12.0 mass% or less, and Si: 0.7 mass% or less and Fe: 0.8 mass. It contains at least one of% or less, Cu: 0.6% by mass or less, Mn: 1.0% by mass or less, Cr: 0.5% by mass or less, Zn: 0.4% by mass or less, Ti: 0.1% by mass or less, Zr: 0.3% by mass or less. In addition, the remainder is composed of Al and unavoidable impurities, the melting process for dissolving the aluminum alloy, the dehydrogenation gas process for removing hydrogen gas from the molten aluminum alloy, the removal of inclusions from the aluminum alloy from which hydrogen gas is removed A filtration step, a casting step of casting an aluminum alloy from which the inclusions are removed to produce an ingot, a heat treatment step of performing heat treatment by maintaining the ingot at a temperature of 200 ° C. or higher and less than 400 ° C. for at least 1 hour, and By slicing the processed ingot slicing process of producing an aluminum alloy plate having a predetermined thickness and characterized in that it carried one by one.

In the sixth invention of the present application, in the method for producing an aluminum alloy thick plate from an aluminum alloy, the aluminum alloy contains Mn: 0.3% by mass or more and 1.6% by mass or less, and Si: 0.7% by mass or less and Fe: 0.8% by mass. It contains at least one of% or less, Cu: 0.5% by mass or less, Mg: 1.5% by mass or less, Cr: 0.3% by mass or less, Zn: 0.4% by mass or less, Ti: 0.1% by mass or less, and Zr: 0.3% by mass or less. In addition, the remainder is composed of Al and unavoidable impurities, the melting process for dissolving the aluminum alloy, the dehydrogenation gas process for removing hydrogen gas from the molten aluminum alloy, the removal of inclusions from the aluminum alloy from which hydrogen gas is removed A filtration step, a casting step of casting an aluminum alloy from which the inclusions are removed to produce an ingot, a heat treatment step of performing heat treatment by maintaining the ingot at a temperature of 200 ° C. or higher and less than 400 ° C. for at least 1 hour, and By slicing the processed ingot slicing process of producing an aluminum alloy plate having a predetermined thickness and characterized in that it carried one by one.

In the seventh invention of the present application, in the method for producing an aluminum alloy thick plate from an aluminum alloy, the aluminum alloy contains Si: 0.2% by mass or more and 1.6% by mass or less, Mg: 0.3% by mass or more and 1.5% by mass or less. Fe: 0.8 mass% or less, Cu: 1.0 mass% or less, Mn: 0.6 mass% or less, Cr: 0.5 mass% or less, Zn: 0.4 mass% or less, Ti: 0.1 mass% or less, Zr: 0.3 mass% or less 1 type, and the remainder is composed of Al and unavoidable impurities, the dissolution process of dissolving the aluminum alloy, the dehydrogenation gas process of removing hydrogen gas from the dissolved aluminum alloy, from the aluminum alloy from which hydrogen gas has been removed Filtration process to remove inclusions, casting process to produce ingot by casting aluminum alloy from which inclusions are removed, heat treatment to heat treatment by holding the ingot at a temperature of 200 ° C or more and less than 400 ° C for at least 1 hour And a slicing step and a slicing step of slicing the heat-treated ingot to produce an aluminum alloy thick plate having a predetermined thickness.

In the 8th invention of this application, in the method of manufacturing an aluminum alloy thick plate from an aluminum alloy, the said aluminum alloy contains Mg: 0.4 mass% or more and 4.0 mass% or less, Zn: 3.0 mass% or more and 9.0 mass% or less Si: 0.7 mass% or less, Fe: 0.8 mass% or less, Cu: 3.0 mass% or less, Mn: 0.8 mass% or less, Cr: 0.5 mass% or less, Ti: 0.1 mass% or less, Zr: 0.25 mass% or less 1 type, and the remainder is composed of Al and unavoidable impurities, the dissolution process of dissolving the aluminum alloy, the dehydrogenation gas process of removing hydrogen gas from the dissolved aluminum alloy, from the aluminum alloy from which hydrogen gas has been removed Filtration process to remove inclusions, casting process to produce ingots by casting aluminum alloy from which inclusions are removed, heat to be heat-treated by maintaining the ingot at a temperature of 200 ° C. to 350 ° C. for at least 1 hour. To slice the re-processing, and the heat-treated ingot and a slicing process for producing the aluminum alloy plate having a predetermined thickness is characterized in that sequentially carried out.

In the fifth to eighth inventions, it is preferable to adopt the following configuration.

(C) After the said slice process, the surface smoothing process process of performing a surface smoothing process to the surface of the aluminum alloy thick plate of predetermined thickness is performed. In addition, in such a structure, it is preferable to perform the said surface smoothing process by 1 or more types chosen from the cutting method, the grinding method, and the grinding | polishing method.

(D) In the slicing step, the thickness has a uniform thickness from the center in the thickness direction toward each surface in the thickness direction, and the thickness has a total thickness of T / 30 to T / 5 when the thickness of the ingot is T. The direction center part is removed from the ingot.

In the ninth invention of the present application, in the method for producing an aluminum alloy thick plate from an aluminum alloy, the aluminum alloy contains Mg: 1.5 mass% or more and 12.0 mass% or less, and Si: 0.7 mass% or less and Fe: 0.8 mass. It contains at least one of% or less, Cu: 0.6% by mass or less, Mn: 1.0% by mass or less, Cr: 0.5% by mass or less, Zn: 0.4% by mass or less, Ti: 0.1% by mass or less, Zr: 0.3% by mass or less. In addition, the remainder is composed of Al and unavoidable impurities, the melting process for dissolving the aluminum alloy, the dehydrogenation gas process for removing hydrogen gas from the molten aluminum alloy, the removal of inclusions from the aluminum alloy from which hydrogen gas is removed A filtration process, a casting process of casting an aluminum alloy from which the inclusions are removed, to manufacture an ingot, a slicing process of slicing the ingot to produce an aluminum alloy thick plate having a predetermined thickness, and an egg of a predetermined thickness. Minyum and an alloy steel plate characterized by conducting the heat treatment step for heat treatment by keeping at least one hour at a temperature of less than 400 ℃ above 200 ℃ sequentially.

In the tenth invention of the present application, in the method for producing an aluminum alloy thick plate from an aluminum alloy, the aluminum alloy contains Mn: 0.3% by mass or more and 1.6% by mass or less, and Si: 0.7% by mass or less and Fe: 0.8% by mass. It contains at least one of% or less, Cu: 0.5% by mass or less, Mg: 1.5% by mass or less, Cr: 0.3% by mass or less, Zn: 0.4% by mass or less, Ti: 0.1% by mass or less, and Zr: 0.3% by mass or less. In addition, the remainder is composed of Al and unavoidable impurities, the melting process for dissolving the aluminum alloy, the dehydrogenation gas process for removing hydrogen gas from the molten aluminum alloy, the removal of inclusions from the aluminum alloy from which hydrogen gas is removed A filtration process, a casting process of casting an aluminum alloy from which the inclusions are removed, to manufacture an ingot, a slicing process of slicing the ingot to produce an aluminum alloy thick plate having a predetermined thickness, and an egg of a predetermined thickness. Minyum and an alloy steel plate characterized by conducting the heat treatment step for heat treatment by keeping at least one hour at a temperature of less than 400 ℃ above 200 ℃ sequentially.

In the 11th invention of this application, in the method of manufacturing an aluminum alloy thick plate from an aluminum alloy, the said aluminum alloy contains Si: 0.2 mass% or more and 1.6 mass% or less, Mg: 0.3 mass% or more and 1.5 mass% or less , Fe: 0.8% by mass or less, Cu: 1.0% by mass or less, Mn: 0.6% by mass or less, Cr: 0.5% by mass or less, Zn: 0.4% by mass or less, Ti: 0.1% by mass or less, Zr: 0.3% by mass or less It contains at least one kind, the remainder is composed of Al and unavoidable impurities, the dissolution process for dissolving the aluminum alloy, the dehydrogenation gas process for removing hydrogen gas from the dissolved aluminum alloy, the aluminum alloy from which hydrogen gas has been removed A filtration step of removing the inclusions from the sintering process, a casting step of casting the aluminum alloy from which the inclusions are removed to produce an ingot, a slicing process of slicing the ingot to produce an aluminum alloy thick plate having a predetermined thickness, and To conduct a heat treatment step of heat-treated by a defined thickness of the aluminum alloy plate to which at least 1 hour at a temperature of less than 400 ℃ above 200 ℃ sequentially and characterized.

In the 12th invention of this application, in the method of manufacturing an aluminum alloy thick plate from an aluminum alloy, the said aluminum alloy contains Mg: 0.4 mass% or more and 4.0 mass% or less, Zn: 3.0 mass% or more and 9.0 mass% or less Si: 0.7 mass% or less, Fe: 0.8 mass% or less, Cu: 3.0 mass% or less, Mn: 0.8 mass% or less, Cr: 0.5 mass% or less, Ti: 0.1 mass% or less, Zr: 0.25 mass% or less 1 type, and the remainder is composed of Al and unavoidable impurities, the dissolution process of dissolving the aluminum alloy, the dehydrogenation gas process of removing hydrogen gas from the dissolved aluminum alloy, from the aluminum alloy from which hydrogen gas has been removed A filtration step of removing the inclusions, a casting step of casting an aluminum alloy from which the inclusions have been removed to produce an ingot, a slice step of slicing the ingot to produce an aluminum alloy thick plate having a predetermined thickness, and To conduct a heat treatment step of heat-treated by a defined thickness of the aluminum alloy plates for keeping more than one hour at a temperature of less than 350 ℃ above 200 ℃ sequentially and characterized.

In the ninth to twelfth inventions, it is preferable to adopt the following configuration.

(E) After the heat treatment step, a surface smoothing treatment step of performing a surface smoothing treatment on the surface of the aluminum alloy thick plate is performed. In addition, in such a structure, it is preferable to perform the said surface smoothing process by 1 or more types chosen from the cutting method, the grinding method, and the grinding | polishing method.

(F) In the said slicing process, it has thickness which is equal from the center of thickness direction toward each surface of the thickness direction, and has thickness of T / 30-T / 5 in the case of making thickness of the said ingot T. The thickness direction center part is removed from the ingot.

13th invention of this application is an aluminum alloy thick plate manufactured by the manufacturing method of the aluminum alloy thick plate which concerns on any one of said 1st-12th invention, It is characterized by having an average grain size of 400 micrometers or less.

In said 1st-4th invention, since content of the predetermined element of an aluminum alloy is limited to the predetermined range, refinement | miniaturization and intensity | strength of the intermetallic compound of an aluminum alloy thick plate improve. In addition, since the hydrogen gas is removed by the dehydrogenation gas process, the hydrogen concentration in the ingot is limited, and even if grains in the ingot are coarsened, hydrogen is not accumulated or concentrated at the grain boundary near the ingot surface. Peeling of the aluminum alloy thick plate resulting from bubbles of the ingot and bubbles is suppressed, and potential defects on the thick plate surface appearing as surface defects of the thick plate are suppressed. In addition, the strength of the aluminum alloy thick plate is improved. Moreover, inclusions, such as an oxide and a nonmetal, are removed from an aluminum alloy by a filtration process. In addition, since the ingot is sliced in the slicing step, the thickness of the oxide film is reduced, and the surface state, flatness and plate thickness precision of the aluminum alloy thick plate are improved, and the productivity is improved. In addition, the aluminum alloy thick plate is heat-treated in the heat treatment process, so that internal stress is removed and internal structure is uniformed.

Therefore, according to the first to fourth inventions, the strength of the aluminum alloy thick plate can be improved. In addition, since the ingot is sliced to produce an aluminum alloy thick plate, it is not necessary to reduce the thickness by hot rolling as in the prior art, so that the work process can be omitted and the productivity can be improved accordingly. Moreover, the nonuniformity (color tone nonuniformity) in the surface and cross section of a thick plate can be eliminated, and the flatness, the appearance property after an alumite process, and plate | board thickness precision can be improved. In addition, after slicing, an aluminum alloy thick plate having a predetermined thickness is subjected to a heat treatment at a temperature of 400 ° C. (or 350 ° C.) to a melting point or less, so that internal stress can be eliminated and internal structure can be homogenized, resulting in good flatness and sheet thickness precision. Can be obtained and the strength can be maintained.

According to the said structure (A), the surface state and flatness of an aluminum alloy thick plate can further be improved. In addition, since gas residues on the surface of the thick plate are eliminated by smoothing the surface, when the aluminum alloy thick plate is used in a chamber for a vacuum apparatus, the vacuum degree of the chamber can be improved.

According to the said structure (B), since the center part of the ingot which is easy to produce a nonuniformity is removed in the surface or cross section of an aluminum alloy thick plate after an alumite treatment, the aluminum alloy thick plate excellent in external appearance can be obtained even after an anodizing process. have. In addition, the variation in the lot can be reduced.

In the fifth to eighth inventions, since the content of a predetermined element of the aluminum alloy is limited to a predetermined range, the refinement and strength of the intermetallic compound of the aluminum alloy thick plate can be improved. In addition, since the hydrogen gas is removed by the dehydrogenation gas process, the hydrogen concentration in the ingot is limited, and even if grains in the ingot are coarsened, hydrogen is not accumulated or concentrated at the grain boundary near the ingot surface, and due to bubbles and bubbles of the ingot. Peeling of the aluminum alloy thick plate is suppressed, and also potential defects on the thick plate surface appearing as surface defects of the thick plate are suppressed. In addition, the strength of the aluminum alloy thick plate is improved. Moreover, inclusions, such as an oxide and a nonmetal, are removed from an aluminum alloy by a filtration process. In addition, since the ingot is heat-treated in the heat treatment step, the internal stress is removed, and the internal structure is uniformed. In addition, since the ingot is sliced in the slicing step, the thickness of the oxide film is reduced, and the surface state, flatness and plate thickness precision of the aluminum alloy thick plate are improved, and the productivity is improved.

Therefore, according to the fifth to eighth inventions, it is possible to improve the balance of flatness, strength and machinability of the aluminum alloy thick plate. That is, since the ingot is subjected to a heat treatment at a temperature of 200 ° C. or more and less than 400 ° C. (or 350 ° C.), ductility can be prevented from being increased, thereby reducing the machinability (cutting property). The internal stress can be eliminated and the internal structure can be made uniform, thus achieving good flatness and plate thickness accuracy and maintaining strength. In addition, since the ingot is sliced to produce an aluminum alloy thick plate, it is not necessary to reduce the thickness by hot rolling as in the prior art, so that work processes can be omitted, and productivity can be improved. Moreover, the nonuniformity (color tone nonuniformity) of the surface in the cross section of a thick plate can be eliminated, and flatness, the appearance property after an alumite process, and plate | board thickness precision can be improved.

According to the said structure (C), the surface state and flatness of an aluminum alloy thick plate can further be improved. In addition, since gas residues on the surface of the thick plate are eliminated by smoothing the surface, when the aluminum alloy thick plate is used in a chamber for a vacuum apparatus, the vacuum degree of the chamber can be improved.

According to the said structure (D), since the center part of the ingot which is easy to produce a nonuniformity in the surface or cross section of an aluminum alloy thick plate after an alumite process is removed, the aluminum alloy thick plate excellent in external appearance can be obtained even after an alumite process. In addition, the variation in the lot can be reduced.

In the ninth to twelfth inventions, since the predetermined element content of the aluminum alloy is limited to a predetermined range, the miniaturization and strength of the intermetallic compound of the aluminum alloy thick plate are improved. In addition, since the hydrogen gas is removed by the dehydrogenation gas process, the hydrogen concentration in the ingot is limited, and even if grains in the ingot are coarsened, hydrogen is not accumulated or concentrated at the grain boundary near the ingot surface, and is caused by bubbles and bubbles in the ingot. Peeling of the aluminum alloy thick plate is suppressed, and potential defects on the thick plate surface appearing as surface defects of the thick plate are suppressed. In addition, the strength of the aluminum alloy thick plate is improved. Moreover, inclusions, such as an oxide and a nonmetal, are removed from an aluminum alloy by a filtration process. In addition, since the ingot is sliced in the slicing step, the thickness of the oxide film is reduced, and the surface state, flatness and plate thickness precision of the aluminum alloy thick plate are improved, and the productivity is improved. In addition, the aluminum alloy thick plate is heat-treated in the heat treatment process, so that the internal stress is eliminated and the internal structure is made uniform.

Therefore, according to the ninth to twelfth inventions, the strength of the aluminum alloy thick plate can be improved. In addition, since the ingot is sliced to produce an aluminum alloy thick plate, it is not necessary to reduce the thickness by hot rolling as in the prior art, so that work processes can be omitted, and productivity can be improved. Moreover, the nonuniformity (color tone nonuniformity) in the surface and cross section of a thick plate can be eliminated, and the flatness, the appearance property after an alumite process, and plate | board thickness precision can be improved. In addition, the balance of the flatness, strength and machinability of the aluminum alloy thick plate can be improved. That is, since the heat treatment is performed on the aluminum alloy thick plate of the predetermined thickness after slicing at a temperature of 200 ° C. or more and less than 400 ° C. (or 350 ° C.), ductility can be prevented from increasing, thereby reducing machinability (cutting property). Without this, internal stress can be eliminated and internal structure can be made uniform, good flatness and plate thickness precision can be realized, and strength can be maintained.

According to the said structure (E), the surface state and flatness of an aluminum alloy thick plate can further be improved. In addition, since gas residues on the surface of the thick plate are eliminated by smoothing the surface, when the aluminum alloy thick plate is used in a chamber for a vacuum apparatus, the vacuum degree of the chamber can be improved.

According to the said structure (F), since the center part of the ingot which tends to produce a nonuniformity is removed in the surface and cross section of an aluminum alloy thick plate after an alumite treatment, the aluminum alloy thick plate excellent in external appearance can be obtained even after an anodizing process. have. In addition, the variation in the lot can be reduced.

According to the thirteenth invention, the surface state, flatness and sheet thickness precision are excellent. In addition, since gas residues are eliminated by the smoothing of the surface, it is of high quality. In addition, since the nonuniformity hardly arises in the surface appearance after an alumite treatment, it can be used for various various uses, and also recycling to other uses is possible.

1 is a view showing the flow of the aluminum alloy thick plate manufacturing method according to the first to fourth invention and the ninth to twelfth invention.
It is a schematic diagram which shows the center part of the thickness direction of the ingot removed in a slicing process.
3 is a view showing a procedure of a method for producing an aluminum alloy thick plate according to the fifth to eighth invention.

With reference to drawings, the manufacturing method and aluminum alloy thick plate of an aluminum alloy thick plate which concern on this invention are demonstrated concretely. In addition, this invention is demonstrated here divided into (A) 1st-4th invention, (B) 5th-8th invention, (C) 9th-12th invention, and (D) 13th invention.

(A) The aluminum alloy according to the first to fourth invention Thick  Manufacturing method

(1) Summary of manufacturing method

As shown in FIG. 1, the manufacturing method of the aluminum alloy thick plate (henceforth "thick plate") concerning 1st-4th invention is a dissolution process (S1), a dehydrogenation gas process (S2), and a filtration process. (S3), casting step (S4), slicing step (S5), and heat treatment step (S6) are performed sequentially. Moreover, the surface smoothing process process S7 is performed after heat processing process S6 as needed.

In this manufacturing method, the aluminum alloy which is a raw material first melt | dissolves in a melting process (S1). Next, hydrogen gas is removed from the dissolved aluminum alloy in the dehydrogenation gas step (S2), and inclusions such as oxides and nonmetals are removed in the filtration step (S3). Next, this aluminum alloy is cast in the casting step S4 to form an ingot. Next, this ingot is sliced in the slicing step (S5) to form a thick aluminum alloy plate. Thereafter, the aluminum alloy thick plate having a predetermined thickness is subjected to a heat treatment in the heat treatment step S6, and then further subjected to a surface smoothing treatment by the surface smoothing treatment step S7 as necessary.

(2) aluminum alloy

In the production methods according to the first to fourth inventions, aluminum alloys, which are raw materials, include 5000 Al-Mg alloys, 3000 Al-Mn alloys, 6000 Al-Mg-Si alloys, and 7000 alloys. Al-Zn-Mg type alloys are used, respectively. Specifically, it is as follows.

(2-1) First invention

5000-based Al-Mg alloy is used. This aluminum alloy contains Mg: 1.5 mass% or more and 12.0 mass% or less, and Si: 0.7 mass% or less, Fe: 0.8 mass% or less, Cu: 0.6 mass% or less, Mn: 1.0 mass% or less, Cr: 0.5 At least 1 sort (s) of mass% or less, Zn: 0.4 mass% or less, Ti: 0.1 mass% or less, Zr: 0.3 mass% or less, and remainder consist of Al and an unavoidable impurity.

Below, the reason which numerically limited content of each component is demonstrated.

[Mg: 1.5 mass% or more and 12.0 mass% or less]

Mg has the effect of improving the strength of the aluminum alloy. The said effect is small when content of Mg is less than 1.5 mass%. On the other hand, when content of Mg exceeds 12.0 mass%, castability will fall remarkably and product manufacture will become impossible. Therefore, content of Mg is limited to 1.5 mass% or more and 12.0 mass% or less.

[Si: 0.7 mass% or less]

Si has the effect of improving the strength of the aluminum alloy. Si is usually incorporated into aluminum alloys as earth impurities and causes Al- (Fe)-(Mn) -Si-based intermetallic compounds such as Mn and Fe in the ingot in the casting step (S4). When the content of Si exceeds 0.7% by mass, coarse intermetallic compounds are formed in the ingot, whereby nonuniformity tends to occur in the surface appearance after the alumite treatment. Therefore, content of Si is limited to 0.7 mass% or less.

[Fe: 0.8% by mass or less]

Fe has the effect of making the crystal grains of the aluminum alloy finer, stabilized, and improving the strength. Fe is now commonly incorporated into aluminum alloys as impurities and causes Al-Fe- (Mn)-(Si) -based intermetallic compounds, such as Mn and Si, in the ingot in the casting process (S4) or the like. When the content of Fe exceeds 0.8% by mass, coarse intermetallic compounds are formed in the ingot, whereby nonuniformity tends to occur in the surface appearance after the alumite treatment. Therefore, content of Fe is limited to 0.8 mass% or less.

[Cu: 0.6 mass% or less]

Cu has the effect of improving the strength of the aluminum alloy. However, in order to ensure the strength which can endure use as a thick plate, content of Cu is enough in 0.6 mass%. Therefore, content of Cu is limited to 0.6 mass% or less.

[Mn: 1.0 mass% or less]

Mn has an effect of improving strength by being dissolved in an aluminum alloy. When content of Mn exceeds 1.0 mass%, a coarse intermetallic compound will generate | occur | produce, and it will become easy to produce a nonuniformity in the surface appearance after an alumite treatment. Therefore, Mn content is limited to 1.0 mass% or less.

[Cr: 0.5 mass% or less]

Cr precipitates as a fine compound in the casting step (S4) and the heat treatment step (S6) and has an effect of suppressing grain growth. When Cr content exceeds 0.5 mass%, a coarse Al-Cr type intermetallic compound will generate | occur | produce as a primary tablet, and it will become easy to produce a nonuniformity in the surface appearance after an alumite treatment. Therefore, content of Cr is limited to 0.5 mass% or less.

[Zn: 0.4 mass% or less]

Zn has the effect of improving the strength of the aluminum alloy. However, in order to ensure the strength which can endure use as a thick plate, content of Zn is 0.4 mass% is enough. Therefore, content of Zn is limited to 0.4 mass% or less.

[Ti: 0.1 mass% or less]

Ti has an effect which refines the grain of an ingot. When the content of Ti exceeds 0.1% by mass, the above effect is saturated. Therefore, content of Ti is limited to 0.1 mass% or less.

[Zr: 0.3 mass% or less]

Zr has the effect of refining the grains of the ingot. When the content of Zr exceeds 0.3 mass%, the above effect is saturated. Therefore, content of Zr is limited to 0.3 mass% or less.

[Al and unavoidable impurities: balance]

In addition to the above components, the aluminum alloy is composed of Al and inevitable impurities. As unavoidable impurities, for example, V, B and the like can be considered, but these impurities do not affect the properties of the aluminum alloy thick plate of the present invention if the respective contents are 0.01% by mass or less.

(2-2) 2nd invention

Al-Mn alloy of 3000 type is used. This aluminum alloy contains Mn: 0.3 mass% or more and 1.6 mass% or less, Si: 0.7 mass% or less, Fe: 0.8 mass% or less, Cu: 0.5 mass% or less, Mg: 1.5 mass% or less, Cr: 0.3 At least 1 sort (s) of mass% or less, Zn: 0.4 mass% or less, Ti: 0.1 mass% or less, Zr: 0.3 mass% or less, and remainder consist of Al and an unavoidable impurity.

Below, the reason which numerically limited content of each component is demonstrated.

On the other hand, the reason for limitation of Si, Fe, Cu, Cr, Zn, Ti, and Zr and the unavoidable impurities are the same as those of the Al-Mg-based alloy, and thus description thereof is omitted here.

[Mn: 0.3 mass% or more and 1.6 mass% or less]

Mn has the effect of improving strength by solid solution in aluminum alloy. The said effect is small when content of Mn is less than 0.3 mass%. On the other hand, when content of Mn exceeds 1.6 mass%, a coarse intermetallic compound will generate | occur | produce, and it will become easy to produce a nonuniformity in the surface appearance after an alumite treatment. Therefore, Mn content is limited to 0.3 mass% or more and 1.6 mass% or less.

[Mg: 1.5 mass% or less]

Mg has the effect of improving the strength of the aluminum alloy. However, in order to ensure the strength which can endure use as a thick plate, content of Mg is 1.5 mass% is enough. Therefore, content of Mg is limited to 1.5 mass% or less.

(2-3) Third invention

Al-Mg-Si type alloy of 6000 type | system | group is used. This aluminum alloy contains Si: 0.2 mass% or more and 1.6 mass% or less, Mg: 0.3 mass% or more and 1.5 mass% or less, Fe: 0.8 mass% or less, Cu: 1.0 mass% or less, Mn: 0.6 mass% or less At least one of Cr: 0.5% by mass or less, Zn: 0.4% by mass or less, Ti: 0.1% by mass or less, and Zr: 0.3% by mass or less, and the balance is made of Al and unavoidable impurities.

Below, the reason which numerically limited content of each component is demonstrated.

On the other hand, the reason for limitation of Fe, Mn, Cr, Ti, and Zr and the unavoidable impurities are the same as those of the Al-Mg-based alloy, and thus description thereof is omitted here.

[Si: 0.2 mass% or more and 1.6 mass% or less]

Si has the effect of improving the strength of the aluminum alloy. Si is now commonly incorporated into aluminum alloys as impurities, resulting in Al- (Fe) -Si based intermetallic compounds and Si based intermetallic compounds in the ingot in the casting process (S4) and the like. The said effect is small when content of Si is less than 0.2 mass%. On the other hand, when content of Si exceeds 1.6 mass%, a coarse Si type intermetallic compound will arise in an ingot, and it will become easy to produce a nonuniformity in the surface appearance after an alumite treatment. Therefore, content of Si is limited to 0.2 mass% or more and 1.6 mass% or less.

[Mg: 0.3 mass% or more and 1.5 mass% or less]

Mg has the effect of improving the strength of the aluminum alloy by coexisting with Si to form Mg ₂ Si. The said effect is small when content of Mg is less than 0.3 mass%. On the other hand, when content of Mg exceeds 1.5 mass%, the said effect is saturated. Therefore, content of Mg is limited to 0.3 mass% or more and 1.5 mass% or less.

[Cu: 1.0 mass% or less]

Cu has the effect of improving the strength of the aluminum alloy. If content of Cu exceeds 1.0 mass%, corrosion resistance will fall. Therefore, content of Cu is limited to 1.0 mass% or less.

[Zn: 0.4 mass% or less]

Zn has the effect of improving the strength of the aluminum alloy. If content of Zn exceeds 0.4 mass%, corrosion resistance will fall. Therefore, content of Zn is limited to 0.4 mass% or less.

(2-4) Fourth invention

7000 type Al-Zn-Mg type alloy is used. Mg: 0.4 mass% or more and 4.0 mass% or less, Zn: 3.0 mass% or more and 9.0 mass% or less, Si: 0.7 mass% or less, Fe: 0.8 mass% or less, Cu: 3.0 mass% or less At least one of Mn: 0.8% by mass or less, Cr: 0.5% by mass or less, Ti: 0.1% by mass or less, and Zr: 0.25% by mass or less, and the balance consists of Al and unavoidable impurities.

Below, the reason which numerically limited content of each component is demonstrated.

On the other hand, the reason for limitation of Cr, Ti and Zr and the unavoidable impurities are the same as those of the Al-Mg-based alloy, and thus description thereof is omitted here.

[Mg: 0.4 mass% or more and 4.0 mass% or less]

Mg has the effect of improving the strength of the aluminum alloy. The said effect is small when content of Mg is less than 0.4 mass%. On the other hand, when content of Mg exceeds 4.0 mass%, a nonuniformity will generate | occur | produce easily in the surface appearance after an alumite treatment. Therefore, content of Mg is limited to 0.4 mass% or more and 4.0 mass% or less.

[Zn: 3.0 mass% or more and 9.0 mass% or less]

Zn has the effect of improving the strength of the aluminum alloy. If the content of Zn is less than 3.0 mass%, the above effect is small. On the other hand, when content of Zn exceeds 9.0 mass%, nonuniformity will generate | occur | produce easily in the surface appearance after an alumite treatment. Therefore, content of Zn is limited to 3.0 mass% or more and 9.0 mass% or less.

[Si: 0.7 mass% or less]

Si is now usually incorporated into aluminum alloys as impurities and causes Al- (Fe) -Si-based intermetallic compounds in the ingot in the casting step (S4) or the like. When the content of Si exceeds 0.7% by mass, coarse Al- (Fe) -Si-based intermetallic compounds are generated in the ingot, whereby unevenness tends to occur in the surface appearance after the alumite treatment. Therefore, content of Si is limited to 0.7 mass% or less.

[Fe: 0.8% by mass or less]

Fe is usually incorporated into aluminum alloy as an impurity now, and causes Al-Fe-based intermetallic compound in the ingot in the casting step (S4) or the like. When the content of Fe exceeds 0.8% by mass, coarse Al-Fe-based intermetallic compounds are generated in the ingot, whereby nonuniformity tends to occur in the surface appearance after the alumite treatment. Therefore, content of Fe is limited to 0.8 mass% or less.

[Cu: 3.0 mass% or less]

Cu has the effect of improving the strength of the aluminum alloy. If content of Cu exceeds 3.0 mass%, corrosion resistance will fall. Therefore, content of Cu is limited to 3.0 mass% or less.

[Mn: 0.8 mass% or less]

Mn has the effect of refining the crystal structure. When content of Mn exceeds 0.8 mass%, a coarse intermetallic compound will generate | occur | produce, and it will become easy to produce a nonuniformity in the surface appearance after an alumite treatment. Therefore, Mn content is limited to 0.8 mass% or less.

(3) Details of the manufacturing method

Next, each process in the manufacturing method which concerns on 1st-4th invention is demonstrated.

(3-1) melting process

Melting process (S1) is a process of melt | dissolving the aluminum alloy which is a raw material.

(3-2) Dehydrogenation Gas Process

The dehydrogenation gas step (S2) is a step of removing hydrogen gas from the aluminum alloy dissolved in the dissolution step (S1).

Hydrogen gas is generated from hydrogen in fuel, moisture, organic matter, etc. adhering to the present. If a large amount of hydrogen gas is included, the following defects are present.

[a] Pinholes are generated.

[b] The strength of the product is weakened.

[c] Hydrogen accumulates and is concentrated at grain boundaries near the ingot surface. Thereby, peeling of the thick plate resulting from the bubble and bubble of an ingot generate | occur | produces. In addition, potential defects of the thick plate surface appear as surface defects of the thick plate.

Therefore, it is preferable to make hydrogen gas 0.2 ml or less in 100 g of aluminum alloys, and it is more preferable to set it as 0.1 ml or less. The removal of hydrogen gas can be suitably carried out by performing fluxing, chlorine refining, or inline refining of the molten metal. In addition, in a dehydrogenation gas apparatus, a SNIFF or a porous plug is used. (See Japanese Patent Laid-Open No. 2002-146447) can be more suitably executed.

The concentration of hydrogen gas in the ingot can be obtained, for example, as follows. That is, a sample is cut out from the ingot after a casting process. Next, the sample is ultrasonically cleaned with alcohol and acetone. The sample is then treated, for example, by an inert gas airflow fusion thermal conductivity method (LISAO6-1993).

The concentration of hydrogen gas in the aluminum alloy thick plate can be obtained, for example, as follows. That is, a sample is cut out from an aluminum alloy thick plate. Next, the sample is immersed in an aqueous NaOH solution. Next, the oxide film on the surface of the sample is removed by treating the sample with nitric acid. Next, the sample is ultrasonically cleaned with alcohol and acetone. The sample is then treated, for example, by vacuum heated extraction capacity method (LISAO6-1993).

(3-3) Filtration Process

Filtration process (S3) is a process of removing an oxide and nonmetallic inclusion mainly from an aluminum alloy with a filtration apparatus. The filtration apparatus is provided with a ceramic tube using, for example, alumina having a particle size of about 1 mm. The inclusions are removed by passing a molten metal through the ceramic tube.

By passing through the dehydrogenation gas step and the filtration step, the ingot can be obtained from an aluminum alloy having a high quality in the next casting step (S4). In addition, since the formation of oxide deposits (dross) can be suppressed, the labor of dross removal can be reduced.

(3-4) casting process

Casting process S4 is a process of manufacturing an ingot by forming molten aluminum alloy into a predetermined shape, such as a rectangular parallelepiped shape, and solidifying. For example, a casting apparatus with a water cooling mold is used. As the casting method, a semicontinuous casting method can be adopted. In the semi-continuous casting method, a molten aluminum alloy is injected from above into a metal water-cooled mold having an open bottom, and the aluminum alloy solidified at the bottom of the water-cooled mold is continuously taken out, whereby an ingot having a predetermined thickness is obtained. In addition, you may perform the semicontinuous casting method in the longitudinal direction and the lateral direction.

(3-5) Slicing Process

The slicing step S5 is a step of slicing the ingot manufactured in the casting step S4 to produce an aluminum alloy thick plate having a predetermined thickness. As the slicing method, the slab slicing method can be adopted. In the slab slicing method, the ingot produced by the semi-continuous casting method is taken out in the casting direction by being sliced by a band saw cutter or the like, whereby an aluminum alloy thick plate having a predetermined thickness is obtained. Although the thickness of an aluminum alloy thick plate is preferable 15-200 mm, it is not specifically limited, It can change suitably according to the use of a thick plate.

It is preferable to use a band saw as the slicing method, but it is not particularly limited, but a round saw cutter may be used, or a laser, a hydraulic pressure, or the like may be used.

By slicing the ingot, it is possible to obtain an aluminum alloy thick plate having excellent surface conditions, flatness, plate thickness accuracy, and the like compared with the rolled material. For example, an aluminum alloy thick plate having a flatness (warpage amount) per meter of casting direction of 0.4 mm or less / 1 m in length and a plate thickness precision of ± 100 μm or less can be obtained.

In addition, as shown in FIG. 2, in slice process S5, it is preferable to remove center part B shown with the oblique line. The center portion B has a uniform thickness from the center in the thickness direction A toward the respective surfaces in the thickness direction, and when the thickness of the ingot 1 is T, the total T / 30 to T / 5 thickness is obtained. Have. In addition, in FIG. 2, the center part B has about T / 5 thickness. Here, although the upper and lower thicknesses b1 and (b2) in the center portion B of the ingot 1 are preferably the same, a difference of about 30% is allowed. In addition, the said thickness direction center A is the center of the thickness direction of the ingot 1, and is the place which is about 1/2 of the thickness T of the ingot 1, ie, about T / 2.

By the way, in the center part B of the ingot 1, nonuniformity tends to arise in the thick plate surface or cross section after an armite treatment. However, in the slicing step S5, the center portion B is removed, so that a thick plate having excellent appearance after the alumite treatment can be obtained, and the variation in the lot can be reduced. If the thickness to remove is less than T / 30, the thick plate which has a nonuniformity in the surface appearance after an alumite process will generate | occur | produce easily, and the deviation in a lot will generate | occur | produce easily. On the other hand, when the thickness to remove exceeds T / 5, the removal amount increases, and there exists a possibility that productivity may fall by this. Therefore, the removal amount of the center part B of the ingot 1 is the thickness equal to each surface of the thickness direction from the thickness direction center A, and when the thickness of the ingot 1 is set to T, total T / It is preferable to limit to 30-T / 5 thickness.

After slicing the ingot in the slicing step (S5), in the next heat treatment step (S6), a heat treatment for the purpose of removing the internal stress and homogenizing the internal structure is performed. By carrying out the heat treatment, flatness, plate thickness accuracy, and appearance after an alumite treatment are improved.

(3-6) heat treatment process

The heat treatment step S6 is a step of heat treatment (homogenization heat treatment) of the aluminum alloy thick plate of a predetermined thickness obtained in the slicing step S5. Heat treatment is performed according to a conventional method. That is, when the aluminum alloy is a 5000-based Al-Mg alloy (first invention), a 3000-based Al-Mn alloy (second invention) and a 6000-based Al-Mg-Si alloy (third invention) The heat treatment should be maintained for at least 1 hour at a temperature of 400 ° C. or higher and below the melting point. In the case where the aluminum alloy is a 7000 Al-Zn-Mg-based alloy (fourth invention), the heat treatment should be maintained for at least 1 hour at a temperature of 350 ° C or more and a melting point or less.

By the way, when the ingot obtained by the casting process S4 is slice-processed, internal residual stress is released, and bending becomes easy to occur. However, in this invention, since the aluminum alloy thick plate of predetermined thickness after slice processing is heat-processed, for example on a surface plate, etc., flatness improves.

In the first to third inventions, when the treatment temperature is less than 400 ° C, the amount of removal of the internal stress is small, and the homogenization of the solute elements segregated during casting is also insufficient, so that the effect of performing heat treatment is small. Therefore, processing temperature is limited to 400 degreeC or more. In addition, when the processing temperature is equal to or higher than the melting point, partial melting occurs in the interior, and internal defects occur, and the strength and ductility decrease. Therefore, the treatment temperature is limited to below the melting point.

In the fourth aspect of the invention, when the treatment temperature is less than 350 ° C, the amount of removal of internal stress is small, and the homogenization of the solute elements segregated during casting is insufficient, so that the effect of performing heat treatment is small. Therefore, processing temperature is limited to 350 degreeC or more. In addition, when the processing temperature is equal to or higher than the melting point, partial melting occurs in the interior, and internal defects occur, and the strength and ductility decrease. Therefore, the treatment temperature is limited to below the melting point.

If the treatment time is less than 1 hour, the solid solution of the intermetallic compound is insufficient, and the intermetallic compound is easily precipitated. Therefore, the processing time is limited to 1 hour or more. In addition, when the treatment time exceeds about 8 hours, the effect of heat treatment is saturated, resulting in energy loss. Therefore, the treatment time is preferably limited to 8 hours or less.

The aluminum alloy thick plate heat-treated in the heat treatment step (S6) may be surface smoothed as necessary to remove crystals and oxides formed on the thick plate surface or to remove gas residues on the thick plate surface. .

(3-7) Surface Smoothing Process

Surface smoothing process S7 is a process of performing surface smoothing process on the surface of the aluminum alloy thick plate obtained by heat processing process S6. Examples of the surface smoothing treatment include cutting methods such as end mill cutting and diamond bite cutting; Grinding method of cutting the surface with a grindstone or the like; Although polishing methods, such as buffing, etc. can be employ | adopted, it is not limited to these.

In the case where the aluminum alloy thick plate is used in a chamber for a vacuum apparatus, it is particularly effective to perform a surface smoothing treatment. The reason for this is as follows. That is, when the vacuum chamber is depressurized to high vacuum, the degree of vacuum decreases due to the release of adsorption gas from the inner surface of the chamber or due to the release to the surface of the gas atom dissolved in the thick plate. Thereby, the time to reach the target vacuum degree becomes long, and production efficiency falls. Therefore, the aluminum alloy thick plate used for the chamber is required to have less gas adsorbed to the thick plate surface located inside the chamber, and that gas atoms dissolved in the thick plate are not released even at high vacuum. Surface smoothing treatments satisfy this requirement.

(B) the aluminum alloy according to the fifth to eighth inventions Thick  Manufacturing method

(1) Summary of manufacturing method

The manufacturing method of the aluminum alloy thick plate which concerns on 5th-8th invention is a dissolution process (S1), a dehydrogenation gas process (S2), a filtration process (S3), a casting process (S4), as shown in FIG. The heat treatment step (S5) and the slice step (S6) are performed sequentially. If necessary, the surface smoothing treatment step S7 is performed after the slicing step S6.

In the said manufacturing method, the aluminum alloy which is a raw material first melt | dissolves in a melting process (S1). Next, hydrogen gas is removed from the dissolved aluminum alloy in the dehydrogenation gas step (S2), and inclusions such as oxides and nonmetals are removed in the filtration step (S3). Next, this aluminum alloy is cast in the casting step S4 to form an ingot. Next, the ingot is heat-treated in the heat treatment step S5 and then sliced in the slicing step S6 to form an aluminum alloy thick plate having a predetermined thickness. Thereafter, the aluminum alloy thick plate having a predetermined thickness is further subjected to surface smoothing by a surface smoothing treatment step (S7) as necessary.

(2) aluminum alloy

In the manufacturing method according to the fifth to eighth inventions, the aluminum alloy as the raw material is made of 5000 Al-Mg alloy, 3000 Al-Mn alloy, 6000 Al-Mg-Si alloy and 7000 series. Al-Zn-Mg type alloys are used, respectively. Specifically, it is as follows.

(2-1) Fifth invention

The Al-Mg type alloy of 5000 type | system | group like 1st invention is used. The reason for numerical limitation of the composition, component content, and content of this aluminum alloy is the same as that of 1st invention.

(2-2) Sixth invention

The Al-Mn type alloy of 3000 type like 2nd invention is used. The reason for numerical limitation of the composition, component content, and content of this aluminum alloy is the same as that of 2nd invention.

(2-3) Seventh invention

The Al-Mg-Si type alloy of 6000 type like 3rd invention is used. The reason for numerical limitation of the composition, component content, and content of this aluminum alloy is the same as that of 3rd invention.

(2-4) 8th invention

A 7000 Al-Zn-Mg-based alloy similar to the fourth invention is used. The reason for numerical limitation of the composition, component content, and content of this aluminum alloy is the same as that of 4th invention.

(3) Details of the manufacturing method

Next, each process in the manufacturing method which concerns on 5th-8th invention is demonstrated.

(3-1) melting process

It is the same as the dissolution process (S1) of 1st-4th invention.

(3-2) Dehydrogenation Gas Process

It is similar to the dehydrogenation gas process (S2) of 1st-4th invention.

(3-3) Filtration Process

It is the same as the filtration process (S3) of 1st-4th invention.

(3-4) casting process

It is the same as the casting process (S4) of 1st-4th invention.

Before slicing the ingot obtained in the casting step (S4), a heat treatment for the purpose of removing the internal stress and homogenizing the internal structure is performed in the next heat treatment step (S5). By performing heat treatment on the ingot, flatness, plate thickness accuracy, and appearance after an alumite treatment are improved.

(3-5) heat treatment process

The heat treatment step S5 is a step of heat treatment (homogenization heat treatment) of the ingot obtained in the casting step S4. Heat treatment is performed according to a conventional method. That is, when the aluminum alloy is a 5000-based Al-Mg-based alloy (fifth invention), a 3000-based Al-Mn-based alloy (sixth invention) and a 6000-based Al-Mg-Si-based alloy (seventh invention) The heat treatment is carried out at a temperature of 200 ° C. or more and less than 400 ° C. for 1 hour or more. In the case where the aluminum alloy is a 7000 Al-Zn-Mg-based alloy (eighth invention), the heat treatment is performed at a temperature of 200 ° C to 350 ° C for at least 1 hour.

In the fifth to seventh inventions, the removal amount of the internal stress is small when the treatment temperature is less than 200 ° C, and thus the effect of performing the heat treatment is small. Therefore, processing temperature is limited to 200 degreeC or more. Moreover, when a processing temperature is 400 degreeC or more, ductility becomes high and strength and cutting property fall. In addition, cutting property means cut-off segmentation property. It is preferable that the cutting-off is finely divided. This is because, if the cutout is long, the cutout is entangled in the processing tool (knife) and rotates together, thereby damaging the thick plate surface and also breaking the tool. Therefore, the processing temperature is limited to less than 400 ° C. By heat treatment at such a temperature condition, flatness and sheet thickness precision can be improved, without degrading strength or machinability.

In the eighth invention, when the treatment temperature is less than 200 ° C, the amount of removal of internal stress is small, whereby the effect of performing heat treatment is small. Therefore, processing temperature is limited to 200 degreeC or more. Moreover, when a processing temperature is 350 degreeC or more, ductility becomes high and strength and cutting property fall. In addition, cutting property means cut-off segmentation property. It is preferable that the cutting-off is finely divided. This is because, if the cutout is long, the cutout is entangled in the machining tool (knife) and rotates together, thereby damaging the thick plate surface and also breaking the tool. Therefore, the treatment temperature is limited to less than 350 ° C. By heat treatment at such a temperature condition, flatness and sheet thickness precision can be improved, without degrading strength or machinability.

If the treatment time is less than 1 hour, the solid solution of the intermetallic compound is insufficient, and the intermetallic compound is easily precipitated. Therefore, the processing time is limited to 1 hour or more. In addition, when the treatment time exceeds about 8 hours, the effect of heat treatment is saturated, resulting in energy loss. Therefore, the treatment time is preferably limited to 8 hours or less.

(3-6) Slicing Process

The slicing step (S6) is a step of slicing the ingot obtained in the heat treatment step (S5) to produce an aluminum alloy thick plate having a predetermined thickness. The details are the same as in the slicing step (S5) of the first to fourth inventions.

The aluminum alloy thick plate obtained in the slicing step (S6) may be surface smoothed as necessary to remove crystals and oxides formed on the thick plate surface, or to eliminate gas residues on the thick plate surface.

(3-7) Surface Smoothing Process

Surface smoothing process S7 is a process of performing a surface smoothing process to the surface of the aluminum alloy thick plate obtained by the slicing process S6. The detail is the same as the surface smoothing process S7 of 1st-4th invention.

(C) the aluminum alloy according to the ninth to twelfth inventions Thick  Manufacturing method

(1) Summary of manufacturing method

The manufacturing method of the aluminum alloy thick plate which concerns on 9th-12th invention is a dissolution process (S1), a dehydrogenation gas process (S2), a filtration process (S3), a casting process (S4), as shown in FIG. The slice step (S5) and the heat treatment step (S6) are performed sequentially. Moreover, the surface smoothing process process S7 is performed after heat processing process S6 as needed.

In such a manufacturing method, the aluminum alloy which is a raw material first melt | dissolves in a melting process (S1). Next, hydrogen gas is removed from the dissolved aluminum alloy in the dehydrogenation gas step (S2), and inclusions such as oxides and nonmetals are removed in the filtration step (S3). Next, this aluminum alloy is cast in the casting step S4 to form an ingot. Next, this ingot is sliced in the slicing step (S5) to form a thick aluminum alloy plate. Thereafter, the aluminum alloy thick plate having a predetermined thickness is subjected to a heat treatment in the heat treatment step S6, and then further subjected to a surface smoothing treatment by the surface smoothing treatment step S7 as necessary.

(2) aluminum alloy

In the manufacturing method according to the ninth to twelfth inventions, the aluminum alloy as a raw material is made of 5000 Al-Mg alloy, 3000 Al-Mn alloy, 6000 Al-Mg-Si alloy and 7000 series. Al-Zn-Mg type alloys are used, respectively. Specifically, it is as follows.

(2-1) 9th invention

The Al-Mg type alloy of 5000 type | system | group like 1st invention is used. The reason for numerical limitation of the composition, component content, and content of this aluminum alloy is the same as that of 1st invention.

(2-2) Tenth invention

The Al-Mn type alloy of 3000 type like 2nd invention is used. The reason for numerical limitation of the composition, component content, and content of this aluminum alloy is the same as that of 2nd invention.

(2-3) 11th invention

The Al-Mg-Si type alloy of 6000 type like 3rd invention is used. The reason for numerical limitation of the composition, component content, and content of this aluminum alloy is the same as that of 3rd invention.

(2-4) 12th invention

A 7000 Al-Zn-Mg-based alloy similar to the fourth invention is used. The reason for numerical limitation of the composition, component content, and content of this aluminum alloy is the same as that of 4th invention.

(3) Details of the manufacturing method

Next, each process in the manufacturing method which concerns on 9th-12th invention is demonstrated.

(3-1) melting process

It is the same as the dissolution process (S1) of 1st-4th invention.

(3-2) Dehydrogenation Gas Process

It is similar to the dehydrogenation gas process (S2) of 1st-4th invention.

(3-3) Filtration Process

It is the same as the filtration process (S3) of 1st-4th invention.

(3-4) casting process

It is the same as the casting process (S4) of 1st-4th invention.

(3-5) Slicing Process

It is the same as the slice process (S5) of 1st-4th invention.

(3-6) heat treatment process

The heat treatment step S6 is a step of heat treatment (homogenization heat treatment) of the aluminum alloy thick plate of a predetermined thickness obtained in the slicing step S5. Heat treatment is performed according to a conventional method. That is, when the aluminum alloy is a 5000-based Al-Mg-based alloy (ninth invention), a 3000-based Al-Mn-based alloy (tenth invention) and a 6000-based Al-Mg-Si-based alloy (eleventh invention) The heat treatment is carried out at a temperature of 200 ° C. or more and less than 400 ° C. for 1 hour or more. In the case where the aluminum alloy is a 7000 Al-Zn-Mg-based alloy (twelfth invention), the heat treatment is performed at a temperature of 200 ° C to 350 ° C for at least 1 hour. Other details are the same as those of the heat treatment step S6 of the first to fourth inventions.

In the ninth to eleventh inventions, when the treatment temperature is less than 200 ° C, the amount of removal of internal stress is small, and accordingly, the effect of performing heat treatment is small. Therefore, processing temperature is limited to 200 degreeC or more. Moreover, when a processing temperature is 400 degreeC or more, ductility becomes high and strength and cutting property fall. In addition, cutting property means cut-off segmentation property. It is preferable that the cutting-off is finely divided. This is because, if the cutout is long, the cutout is entangled in the processing tool (knife) and rotates together, thereby damaging the thick plate surface and also breaking the tool. Therefore, the processing temperature is limited to less than 400 ° C. By heat treatment at such temperature conditions, flatness and sheet thickness precision can be improved without degrading the strength or the machinability.

In the twelfth invention, when the treatment temperature is less than 200 ° C, the amount of removal of internal stress is small, and accordingly, the effect of performing heat treatment is small. Therefore, processing temperature is limited to 200 degreeC or more. Moreover, when a processing temperature is 350 degreeC or more, ductility becomes high and strength and cutting property fall. In addition, cutting property means cut-off segmentation property. It is preferable that the cutting-off is finely divided. This is because, if the cutout is long, the cutout is entangled in the processing tool (knife) and rotates together, thereby damaging the thick plate surface and also breaking the tool. Therefore, the treatment temperature is limited to less than 350 ° C. By heat treatment under such temperature conditions, flatness and sheet thickness precision can be improved without degrading the strength or the machinability.

If the treatment time is less than 1 hour, the solid solution of the intermetallic compound is insufficient, and the intermetallic compound is easily precipitated. Therefore, the processing time is limited to 1 hour or more. In addition, when the treatment time exceeds about 8 hours, the effect of heat treatment is saturated, resulting in energy loss. Therefore, the treatment time is preferably limited to 8 hours or less.

(3-7) Surface Smoothing Process

It is the same as the surface smoothing treatment process (S7) of 1st-4th invention.

(D) thirteenth invention

Next, the aluminum alloy thick plate which concerns on this invention is demonstrated.

This aluminum alloy thick plate is manufactured by the manufacturing method in any one of 1st-12th invention mentioned above, and has an average grain size of 400 micrometers or less.

According to the aluminum alloy thick plate of this invention, since the average grain size is 400 micrometers or less, the external appearance after an alumite process can be improved and the variation in a lot can be reduced.

In addition, when the size of the intermetallic compound in the thick plate becomes large, nonuniformity (color tone nonuniformity) occurs in the end face and the surface of the thick plate when the alumite treatment is performed. However, according to the aluminum alloy thick plate of the present invention, nonuniformity is unlikely to occur because of the small size of the intermetallic compound.

The crystal grain size is measured, for example, as follows. That is, when the thickness of the ingot is set to T, the measured value is obtained from four thickness sections of T / 5, 2T / 5, 3T / 5, and 4T / 5 from one surface of the ingot to the other surface. Find the average. As a method of obtaining such a measurement, the cutting method can be adopted, for example. In the cutting method, the cross section of the aluminum alloy thick plate is etched by the Barker method and then observed by optical microscope observation.

As a method of controlling an average grain size to 400 micrometers or less, the following method can be employ | adopted, for example. That is, the cooling rate (average cooling rate from liquidus temperature to solidus temperature) at the time of casting is made into 0.2 degreeC / sec or more. In addition, when implementing the manufacturing method of 1st-3rd invention, 5th-7th invention, and 9th-11th invention, aluminum alloy contains 0.1 mass% or less of Ti or 0.3 mass% or less of Zr. In the case where the crystal grain size can be further refined and the production methods of the fourth, eighth and twelfth inventions are carried out, the aluminum alloy contains 0.1 mass% or less of Ti or 0.25 mass% or less of Zr to determine the crystal size. The particle diameter can be further refined.

Since the aluminum alloy thick plate obtained by the manufacturing method according to the first to twelfth invention described above has good surface state, flatness and plate thickness precision as described above, semiconductors such as a base substrate, a conveying apparatus, a chamber for a vacuum apparatus, etc. Related devices; Electrical and electronic components or apparatuses for manufacturing the same; Household goods; It can be used for various uses, such as mechanical parts, and can also be recycled for other uses.

On the other hand, the corrosion resistance of the aluminum alloy thick plate need not be a problem. Because the thick plate for the base substrate and the thick plate for the conveying device are used in a clean room, they do not require general corrosion resistance. In addition, the thick plate used in the chamber for the vacuum apparatus is used in an environment in which the corrosive gas is less exposed and does not require strict corrosion resistance.

As mentioned above, although preferred embodiment of this invention was described, this invention is not limited to the said embodiment.

[Example]

Hereinafter, the Example of this invention is described.

(1) First embodiment

This embodiment relates to the first invention. The aluminum alloy used in this embodiment is a 5000-based Al-Mg based alloy.

Alloys 1A to 12A shown in Table 1 were used as example alloys, and alloys 13A to 22A were used as comparative alloys.

(process)

First, alloys 1A to 22A were sequentially processed in a dissolution step, a dehydrogenation gas step, a filtration step, and a casting step to produce an ingot having a sheet thickness of 500 mm.

Next, a slice material and a hot rolled material were produced from the ingot. Sliced material was obtained by treating the ingot in a slicing process. The hot rolled material was obtained by hot rolling after heat treatment of the ingot. The slice material and the hot rolled material are aluminum alloy thick plates each having a thickness of 20 mm, a width of 1,000 mm, and a length of 2,000 mm.

And the said slice material was processed in the heat processing process. That is, the said slice material was hold | maintained at 500 degreeC for 4 hours.

Therefore, the slice material after the treatment is an aluminum alloy thick plate obtained by the production method of the first invention, but the hot rolled material after the treatment is not. And only the slice material using alloy 1A-22A corresponds to the Example of 1st invention.

Next, the following tests were done about the slice material and the hot rolling material after the said process.

<Flatness evaluation test>

Flatness evaluation was performed by measuring the curvature amount (flatness) per 1m of casting direction about a slice material, and measuring the curvature amount (flatness) per 1m of rolling direction about a hot rolled material. The case where flatness was 0.4 mm / 1 m or less was made into pass ((circle)), and the case exceeding 0.4 mm / 1m length was made into reject (x).

<Plate thickness precision evaluation test>

Plate thickness precision evaluation measured the thickness of 6 site | parts using the micrometer and performed it. The six sites are sites that are 20 mm inward in the width direction from the sites in which the four corners of the thick plate and the long side of the thick plate are divided in half. The case where all 6 sites were 19.94 mm or more and 20.06 mm or less was made good ((◎)), and the case where it was 19.90 mm or more and 20.10 mm or less was made pass ((circle)).

<Strength Test>

The strength test was performed as follows. That is, the JIS No. 5 test piece was produced from the aluminum alloy thick plate, the tensile test was performed on the test piece, and the tensile strength and 0.2% yield strength were measured. When the tensile strength is 180 N / mm ² or more, pass (○) is set, and the tensile strength is 180 N / mm ^2. The case below was set as reject (x).

<Armite evaluation test>

The armite evaluation was performed as follows. An armite film having a thickness of 10 µm was formed on the surface and the cross section of the aluminum alloy thick plate by an armite sulfate treatment. Treatment conditions are 15% sulfuric acid, 20 ° C, and current density 2A / dm ² . And the external appearance of the surface and the cross section of the thick plate was observed. The case where there was no nonuniformity (color tone nonuniformity) in external appearance was made into pass ((circle)), and the case where there was nonuniformity was made into rejection (x).

On the other hand, the average grain size of the thick plate was determined because the grain size of the thick plate affects the alumite properties. The average crystal grain size was measured as follows. That is, in the case where the thickness of the aluminum alloy thick plate is T, the measured values are measured at four thickness sections of T / 5, 2T / 5, 3T / 5 and 4T / 5 from one surface to the other surface of the thick plate. I got the average. In addition, the cutting method was employ | adopted as a method of obtaining such a measured value. That is, after the cross section of the aluminum alloy thick plate was etched by the Barker method, it observed by optical microscope observation.

The test results are shown in Tables 2 and 3.

Table 2 shows the test results for the slice material. In Table 2, alloys 1A to 12A correspond to Examples, and alloys 13A to 22A correspond to Comparative Examples. Table 3 shows the test results for the hot rolled material. In Table 3, all of alloys 1A to 22A correspond to comparative examples.

(About slice materials)

As shown in Table 2, in the case of alloys 1A to 13A and 15A to 22A, there was little work deformation and warpage was small. That is, flatness was favorable. Moreover, the plate | board thickness precision was also excellent.

In the case of alloy 14A, since the content of Mg exceeded the upper limit, casting cracking occurred and manufacturing was impossible. In the case of alloy 13A, since the content of Mg was less than the lower limit, the strength was insufficient.

In the case of alloys 1A to 13A, 17A and 20A to 22A, there was no nonuniformity in the appearance of the surface after the alumite treatment. In the case of alloys 15A, 16A, 18A, and 19A, since the content of Si, Fe, Mn, and Cr exceeded the upper limit, respectively, coarse intermetallic compounds occurred, and unevenness occurred in the appearance of the surface after the alumite treatment. . In the case of alloys 1A to 13A and 15A to 22A, there was no nonuniformity in the appearance of the cross section after the alumite treatment.

On the other hand, in the case of alloys 17A, 20A, 21A, and 22A, since the contents of Cu, Zn, Ti, and Zr exceeded the upper limit, respectively, the effects based on them were saturated, and the economy was inferior.

(About hot rolled material)

As shown in Table 3, in the case of alloys 1A to 13A and 15A to 22A, work strain was accumulated and warping in the rolling direction was large. That is, flatness was poor. In addition, the plate | board thickness precision was inferior to the slice material in many cases.

In the case of alloy 14A, since the content of Mg exceeded the upper limit, casting cracking occurred and manufacturing was impossible. In the case of alloy 13A, since the content of Mg was less than the lower limit, the strength was insufficient.

In the case of alloys 15A, 16A, 18A, and 19A, since the contents of Si, Fe, Mn, and Cr exceeded the upper limit, respectively, coarse intermetallic compounds were formed, resulting in unevenness in the appearance of the surface after the alumite treatment. In the case of alloys 1A-13A and 15A-22A, the nonuniformity generate | occur | produced in the external appearance of the cross section after an armite treatment.

(2) Second Embodiment

This embodiment relates to the first invention. In this example, alloy 3A shown in Table 1 was used.

(process)

First, alloy 3A was sequentially processed in a dissolution step, a dehydrogenation gas step, a filtration step, and a casting step to produce an ingot having a plate thickness of 500 mm.

Next, the ingot was treated in a slicing step to obtain a slice material. The slice material is an aluminum alloy thick plate having a thickness of 20 mm × width 1,000 mm × length 2,000 mm.

And the said slice material was processed in the heat processing process. That is, the said slice material was heat-processed on the conditions shown in Table 4.

Therefore, A1 and A2 in which the heat treatment conditions satisfy the first invention correspond to the examples of the first invention, and A3 to A5 in which the heat treatment conditions do not satisfy the first invention correspond to the comparative examples.

The flatness evaluation test and the plate | board thickness precision evaluation test were done about the slice material after the said process.

<Flatness evaluation test>

Flatness evaluation was performed by measuring the curvature amount (flatness) per 1m of casting directions. The case where flatness was 0.4 mm / 1 m or less was made into pass ((circle)), and the case where it was 0.25 mm / 1 m or less was made into good (◎).

<Plate thickness precision evaluation test>

The sheet thickness precision evaluation test is the same as that in the first embodiment.

The test results are shown in Table 4.

As shown in Table 4, in Examples A1 and A2, the heat treatment conditions satisfied the first invention, so that the flatness and the plate thickness precision were good. In Comparative Example A3, heat treatment was not performed, so that the flatness and the plate thickness precision were slightly inferior to those of Examples A1 and A2. In Comparative Example A4, since the treatment temperature was lower than the range of the first invention (less than 400 ° C), the flatness was slightly inferior to Examples A1 and A2. In Comparative Example A5, since the treatment temperature is higher than the range of the first invention (it is exceeding the melting point), partial melting occurs inside, which may result in an internal defect, and thus cannot be a product.

(3) Third embodiment

This embodiment relates to the second invention. The aluminum alloy used in the present embodiment is a 3000-based Al-Mn alloy.

Alloys 23A and 24A shown in Table 5 were used as example alloys, and alloys 25A and 26A were used as comparative alloys.

(process)

First, alloys 23A to 26A were sequentially processed in a dissolution step, a dehydrogenation gas step, a filtration step, and a casting step to produce an ingot having a sheet thickness of 500 mm.

Next, a slice material and a hot rolled material were produced from the ingot. Sliced material was obtained by treating the ingot in a slicing process. The hot rolled material was obtained by hot rolling after heat treatment of the ingot. The slice material and the hot rolled material are aluminum alloy thick plates each having a thickness of 20 mm, a width of 1,000 mm, and a length of 2,000 mm.

And the said slice material was processed in the heat processing process. That is, the said slice material was hold | maintained at 500 degreeC for 4 hours.

Therefore, the slice material after the treatment is an aluminum alloy thick plate obtained by the production method of the second invention, but the hot rolled material after the treatment is not. And only the slice material using alloy 23A, 24A corresponds to the Example of 2nd invention.

Next, the flatness evaluation test, the plate | board thickness precision evaluation test, the strength test, and the armite property evaluation test were performed about the slice material and the hot rolling material after the said process.

The method and evaluation criteria of each test are the same as those of the first embodiment.

However, since the characteristics of the thick plate differed depending on the alloy type, the evaluation criteria for the strength were as follows. That is, the intensity | strength makes pass ((circle)) the case where tensile strength is 90 N / mm <^2> or more, and tensile strength is 90 N / mm <^2>. The case below was set as reject (x).

The test results are shown in Table 6.

(About slice materials)

As shown in Table 6, in the case of alloys 23A to 26A, there was little work deformation and warpage was small. That is, flatness was favorable. Moreover, the plate | board thickness precision was also excellent.

In the case of alloy 25A, since the content of Mn was less than the lower limit, the strength was insufficient. In the case of alloy 26A, since the content of Mn exceeds the upper limit, coarse intermetallic compounds are generated, causing unevenness in the appearance of the surface after the alumite treatment. In the case of alloys 23A to 26A, unevenness occurred in the appearance of the cross section after the alumite treatment.

(About hot rolled material)

As shown in Table 6, in the case of alloys 23A to 26A, work strain was accumulated, and warpage in the rolling direction was large. That is, flatness was poor. In addition, the plate | board thickness precision was inferior to the slice material in many cases.

In the case of alloy 25A, since the content of Mn was less than the lower limit, the strength was slightly inferior to that of other hot rolled materials. In the case of alloy 26A, since content of Mn exceeded the upper limit, the coarse intermetallic compound generate | occur | produced and the nonuniformity generate | occur | produced in the external appearance of the surface after an alumite process. In the case of alloys 23A to 26A, nonuniformity occurred in the appearance of the cross section after the alumite treatment.

(4) Fourth Embodiment

This embodiment relates to the third invention. The aluminum alloy used in this embodiment is a 6000-based Al-Mg-Si alloy.

Alloys 27A and 28A shown in Table 7 were used as example alloys, and alloys 29A to 32A were used as comparative alloys.

(process)

First, alloys 27A to 32A were sequentially processed in a dissolution step, a dehydrogenation gas step, a filtration step, and a casting step to produce an ingot having a sheet thickness of 500 mm.

Next, a slice material and a hot rolled material were produced from the ingot. Sliced material was obtained by treating the ingot in a slicing process. The hot rolled material was obtained by hot rolling after heat treatment of the ingot. The slice material and the hot rolled material are aluminum alloy thick plates each having a thickness of 20 mm, a width of 1,000 mm, and a length of 2,000 mm.

And the said slice material was processed in the heat processing process. That is, the said slice material was hold | maintained at 500 degreeC for 4 hours.

In addition, the obtained sliced material and hot rolled material were melt-processed at 520 degreeC, and also aged at 175 degreeC for 8 hours.

Therefore, the slice material after the treatment is an aluminum alloy thick plate obtained by the production method of the third invention, but the hot rolled material after the treatment is not. And only the slice material using alloy 27A and 28A corresponds to the Example of 3rd invention.

Next, the strength test and the alumite evaluation test were performed about the slice material and the hot rolling material after the said process.

The method and evaluation criteria of each test are the same as those of the first embodiment.

However, since the characteristics of the thick plate differed depending on the alloy type, the evaluation criteria for the strength were as follows. That is, the intensity | strength makes pass ((circle)) the case where tensile strength is 200N / mm <^2> or more, and tensile strength is 200N / mm <^2>. The case below was set as reject (x).

The test results are shown in Table 8.

(About slice materials)

As shown in Table 8, in the case of alloys 29A and 31A, the contents were insufficient because the contents of Si and Mg were less than the lower limit, respectively. In the case of alloy 30A, since the content of Si exceeded the upper limit, a coarse intermetallic compound was generated, and a nonuniformity occurred in the appearance of the surface after the alumite treatment. In the case of alloy 32A, since content of Mg exceeded the upper limit, the effect based on Mg was saturated, and it was inferior to economic efficiency. In the case of alloys 27A to 32A, unevenness occurred in the appearance of the cross section after the alumite treatment.

(About hot rolled material)

As shown in Table 8, in the case of alloys 29A and 31A, the contents were insufficient because the contents of Si and Mg were less than the lower limit, respectively. In the case of alloy 30A, since the content of Si exceeded the upper limit, a coarse intermetallic compound was generated, and a nonuniformity occurred in the appearance of the surface after the alumite treatment. In the case of alloy 32A, since content of Mg exceeded the upper limit, the effect based on Mg was saturated, and it was inferior to economic efficiency. In the case of alloys 27A to 32A, nonuniformity occurred in the appearance of the cross section after the alumite treatment.

(5) Fifth Embodiment

This embodiment relates to the fourth invention. The aluminum alloy used in this embodiment is a 7000 Al-Zn-Mg based alloy.

Alloys 33A and 34A shown in Table 9 were used as example alloys, and alloys 35A to 38A were used as comparative alloys.

(process)

First, alloys 33A to 38A were sequentially processed in a dissolution step, a dehydrogenation gas step, a filtration step, and a casting step to produce an ingot having a sheet thickness of 500 mm.

Next, a slice material and a hot rolled material were produced from the ingot. Sliced material was obtained by treating the ingot by a slicing process. The hot rolled material was obtained by hot rolling after heat treatment of the ingot. The slice material and the hot rolled material are aluminum alloy thick plates each having a thickness of 20 mm, a width of 1,000 mm, and a length of 2,000 mm.

And the said slice material was processed in the heat processing process. That is, the said slice material was hold | maintained at 500 degreeC for 4 hours.

In addition, the obtained sliced material and hot rolled material were melt-processed at 470 degreeC, and also aged at 120 degreeC for 48 hours.

Therefore, the slice material after the treatment is an aluminum alloy thick plate obtained by the production method of the fourth invention, but the hot rolled material after the treatment is not. And only the slice material using alloy 33A and 34A corresponds to the Example of 4th invention.

Next, the strength test and the alumite evaluation test were performed about the slice material and the hot rolling material after the said process.

The method and evaluation criteria of each test are the same as those of the first embodiment.

However, since the characteristics of the thick plate differed depending on the alloy type, the evaluation criteria for the strength were as follows. That is, the intensity | strength makes pass ((circle)) the case where tensile strength is 250 N / mm <^2> or more, and tensile strength is 250 N / mm <^2>. The case below was set as reject (x).

The test results are shown in Table 10.

(About slice materials)

As shown in Table 10, in the case of alloys 35A and 37A, the strengths were insufficient because the contents of Mg and Zn were less than the lower limit, respectively. In the case of alloys 36A and 38A, since the contents of Mg and Zn exceeded the upper limit, respectively, nonuniformity occurred in the appearance of the surface after the alumite treatment. In the case of alloys 33A to 38A, nonuniformity did not occur in the appearance of the cross section after the alumite treatment.

(About hot rolled material)

As shown in Table 10, in the case of alloys 35A and 37A, the strengths were insufficient because the contents of Mg and Zn were less than the lower limit, respectively. In the case of alloys 36A and 38A, since the contents of Mg and Zn exceeded the upper limit, respectively, nonuniformity occurred in the appearance of the surface after the alumite treatment. In the case of alloys 33A to 38A, unevenness occurred in the appearance of the cross section after the alumite treatment.

(6) Sixth Embodiment

This embodiment relates to the fifth invention. The aluminum alloy used in this embodiment is a 5000-based Al-Mg based alloy.

Alloys 1B to 12B shown in Table 11 were used as example alloys, and alloys 13B to 22B were used as comparative alloys.

(process)

First, alloys 1B to 22B were sequentially processed in a dissolution step, a dehydrogenation gas step, a filtration step, and a casting step to produce an ingot having a sheet thickness of 500 mm.

Next, the ingot was treated in a heat treatment step. That is, the ingot was kept at 350 ° C. for 4 hours.

And the slice material and the hot rolling material were produced from the ingot after heat processing. The slice material was obtained by processing the ingot by the slicing process. The hot rolled material was obtained by hot rolling the ingot. The slice material and the hot rolled material are aluminum alloy thick plates each having a thickness of 20 mm, a width of 1,000 mm, and a length of 2,000 mm.

Therefore, the slice material after the treatment is an aluminum alloy thick plate obtained by the manufacturing method of the fifth invention, but the hot rolled material after the treatment is not. And only the slice material using alloy 1B-22B corresponds to the Example of 5th invention.

Next, the flatness evaluation test, the plate | board thickness precision evaluation test, the strength test, and the armite property evaluation test were performed about the slice material and the hot rolling material after the said process. The method and evaluation criteria of each test are the same as those of the first embodiment.

The test results are shown in Table 12 and Table 13.

Table 12 shows the test results for the slice material. In Table 12, Alloys 1B to 12B correspond to Examples of the fifth invention, and Alloys 13B to 22B correspond to Comparative Examples. Table 13 shows the test results for the hot rolled material. In Table 13, all of alloys 1B to 22B correspond to comparative examples.

(About slice materials)

As shown in Table 12, in the case of alloys 1B to 13B and 15B to 22B, the processing deformation was small and the warpage was small. That is, flatness was favorable. Moreover, the plate | board thickness precision was also excellent.

In the case of alloy 14B, since the content of Mg exceeded the upper limit, casting cracking occurred and manufacturing was impossible. In the case of alloy 13B, since the content of Mg was less than the lower limit, the strength was insufficient.

In the case of alloys 1B to 13B, 17B and 20B to 22B, there was no nonuniformity in the appearance of the surface after the alumite treatment. In the case of alloys 15B, 16B, 18B, and 19B, since the contents of Si, Fe, Mn, and Cr exceeded the upper limit, respectively, coarse intermetallic compounds were generated, and nonuniformity occurred in the appearance of the surface after the alumite treatment. . In the case of alloys 1B to 13B and 15B to 22B, there was no nonuniformity in the appearance of the cross section after the alumite treatment.

On the other hand, in the case of alloys 17B, 20B, 21B, and 22B, since the contents of Cu, Zn, Ti, and Zr exceeded the upper limit, respectively, the effects based on them were saturated, and the economy was inferior.

(About hot rolled material)

As shown in Table 13, in the case of alloys 1B to 13B and 15B to 22B, the work strain was accumulated and the warping in the rolling direction was large. That is, flatness was poor. In addition, the plate | board thickness precision was inferior to the slice material in many cases.

In the case of alloy 14B, since the content of Mg exceeded the upper limit, casting cracks occurred and manufacturing was impossible. In the case of alloy 13B, since the content of Mg was less than the lower limit, the strength was insufficient.

In the case of alloys 15B, 16B, 18B, and 19B, since the contents of Si, Fe, Mn, and Cr exceeded the upper limit, respectively, coarse intermetallic compounds were generated, and nonuniformity occurred in the appearance of the surface after the alumite treatment. . In the case of alloys 1B to 13B and 15B to 22B, nonuniformity occurred in the appearance of the cross section after the alumite treatment.

(7) Seventh Embodiment

This embodiment relates to the fifth invention. In this embodiment, Alloy 3B shown in Table 11 is used.

(process)

First, alloy 3B was sequentially processed in a dissolution step, a dehydrogenation gas step, a filtration step, and a casting step to produce an ingot having a plate thickness of 500 mm.

Next, the ingot was treated in a heat treatment step. That is, the ingot was heat-treated under the conditions shown in Table 14.

And the ingot after heat processing was processed in the slice process, and the slice material was obtained. The slice material is an aluminum alloy thick plate having a thickness of 20 mm, a width of 1,000 mm, and a length of 2,000 mm.

Therefore, B1 and B2 whose heat treatment conditions satisfy the fifth invention correspond to the examples of the fifth invention, and B3 to B5 whose heat treatment conditions do not satisfy the fifth invention correspond to the comparative examples.

The flatness evaluation test, the plate thickness precision evaluation test, and the cutting property evaluation test were performed about the slice material after the said process.

<Flatness evaluation test>

Flatness evaluation was performed by measuring the curvature amount (flatness) per 1m of casting directions. The case where flatness was 0.4 mm / 1 m or less was made into pass ((circle)), and the case exceeding 0.4 mm / 1m length was made into reject (x).

<Plate thickness precision evaluation test>

The sheet thickness precision evaluation test is the same as that in the first embodiment.

<Cutting Test Evaluation>

Evaluation of machinability, ie, cut-off segmentation, was performed by measuring the number per unit mass of cutting when performing punching with a drill. Specifically, drilling was performed at a rotational speed of 7,000 rpm and a feed rate of 300 mm / min using a drill having a diameter of 5 mmφ, and the number per 10 g of cut outs generated was measured. The case of 1,000 pieces / 10 g or more was made into pass ((circle)), and the case of less than 1,000 pieces / 10 g was made into reject (x).

The test results are shown in Table 14.

As shown in Table 14, in Examples B1 and B2, since the heat treatment conditions satisfied the fifth invention, the flatness, the plate thickness precision and the machinability were good. In Comparative Example B3, since the heat treatment was not performed, flatness was poor, and the plate thickness precision was slightly inferior to that of Examples B1 and B2. In the comparative example B4, since process temperature was higher than the range of 5th invention, cutting property was inferior. In the comparative example B5, since process temperature was lower than the range of 5th invention, flatness was bad, and plate | board thickness precision was inferior to Example B1, B2 slightly.

(8) Eighth Embodiment

This embodiment relates to the sixth invention. The aluminum alloy used in the present embodiment is a 3000-based Al-Mn alloy.

Alloys 23B and 24B shown in Table 15 were used as example alloys, and alloys 25B and 26B were used as comparative alloys.

(process)

First, alloys 23B to 26B were sequentially processed in a dissolution step, a dehydrogenation gas step, a filtration step, and a casting step to produce an ingot having a sheet thickness of 500 mm.

Next, the ingot was treated in a heat treatment step. That is, the ingot was kept at 350 ° C. for 4 hours.

And the slice material and the hot rolling material were produced from the ingot after heat processing. The slice material was obtained by processing an ingot in a slice process. The hot rolled material was obtained by hot rolling the ingot. The slice material and the hot rolled material are aluminum alloy thick plates each having a thickness of 20 mm, a width of 1,000 mm, and a length of 2,000 mm.

Therefore, the slice material after the treatment is an aluminum alloy thick plate obtained by the manufacturing method of the sixth invention, but the hot rolled material after the treatment is not. And only the slice material using alloy 23B and 24B corresponds to the Example of 6th invention.

Next, the flatness evaluation test, the plate | board thickness precision evaluation test, the strength test, and the armite property evaluation test were performed about the slice material and the hot rolling material after the said process.

The method and evaluation criteria of each test are the same as those of the first embodiment.

However, since the characteristics of the thick plate differed depending on the alloy type, the evaluation criteria for the strength were as follows. That is, the intensity | strength made pass ((circle)) the case where tensile strength was 90 N / mm <^2> or more, and made the case where tensile strength less than 90 N / mm <^2> fail (x).

The test results are shown in Table 16.

(About slice materials)

As shown in Table 16, in the case of alloys 23B to 26B, there was little work deformation and warpage was small. That is, flatness was favorable. Moreover, the plate | board thickness precision was also excellent.

In the case of alloy 25B, since the content of Mn was less than the lower limit, the strength was insufficient. In the case of alloy 26B, since the content of Mn exceeded the upper limit, a coarse intermetallic compound was produced, causing nonuniformity in the appearance of the surface after the alumite treatment. In the case of alloys 23B to 26B, unevenness occurred in the external appearance of the cross section after the alumite treatment.

(About hot rolled material)

As shown in Table 16, in the case of alloys 23B to 26B, work strain was accumulated and warping in the rolling direction was large. That is, flatness was poor. In addition, the plate | board thickness precision was inferior to the slice material in many cases.

In the case of alloy 25B, since the content of Mn was less than the lower limit, the strength was slightly inferior to that of other hot rolled materials. In the case of alloy 26B, since the content of Mn exceeded the upper limit, a coarse intermetallic compound was produced, causing nonuniformity in the appearance of the surface after the alumite treatment. In the case of alloys 23B to 26B, nonuniformity occurred in the appearance of the cross section after the alumite treatment.

(9) Ninth Embodiment

This embodiment relates to the seventh invention. The aluminum alloy used in this embodiment is a 6000-based Al-Mg-Si alloy.

Alloys 27B and 28B shown in Table 17 were used as example alloys, and alloys 29B to 32B were used as comparative alloys.

(process)

First, alloys 27B to 32B were sequentially processed in a dissolution step, a dehydrogenation gas step, a filtration step, and a casting step to produce an ingot having a sheet thickness of 500 mm.

Next, the ingot was treated in a heat treatment step. That is, the ingot was kept at 350 ° C. for 4 hours.

And the slice material and the hot rolling material were produced from the ingot after heat processing. The slice material was obtained by processing the ingot by the slicing process. The hot rolled material was obtained by hot rolling the ingot. The slice material and the hot rolled material are aluminum alloy thick plates each having a thickness of 20 mm, a width of 1,000 mm, and a length of 2,000 mm.

In addition, the obtained sliced material and hot rolled material were melt-processed at 520 degreeC, and also aged at 175 degreeC for 8 hours.

Therefore, the slice material after the treatment is an aluminum alloy thick plate obtained by the manufacturing method of the seventh invention, but the hot rolled material after the treatment is not. And only the slice material using alloy 27B and 28B corresponds to the Example of 7th invention.

Next, the strength test and the alumite evaluation test were performed about the slice material and the hot rolling material after the said process.

The method and evaluation criteria of each test are the same as those of the first embodiment.

However, since the characteristics of the thick plate differed depending on the alloy type, the evaluation criteria for the strength were as follows. That is, the intensity | strength makes pass ((circle)) the case where tensile strength is 200N / mm <^2> or more, and tensile strength is 200N / mm <^2>. The case below was set as reject (x).

The test results are shown in Table 18.

(About slice materials)

As shown in Table 18, in the case of alloys 29B and 31B, the strengths were insufficient because the contents of Si and Mg were less than the lower limit, respectively. In the case of alloy 30B, since content of Si exceeded the upper limit, the coarse intermetallic compound generate | occur | produced and the nonuniformity generate | occur | produced in the external appearance of the surface after an alumite process. In the case of alloy 32B, since content of Mg exceeds the upper limit, the effect based on Mg was saturated, and it was inferior to economic efficiency. In the case of alloys 27B to 32B, there was no nonuniformity in the appearance of the cross section after the alumite treatment.

(About hot rolled material)

As shown in Table 18, in the case of alloys 29B and 31B, the strengths were insufficient because the contents of Si and Mg were less than the lower limit, respectively. In the case of alloy 30B, since the content of Si exceeded the upper limit, a coarse intermetallic compound was generated, and a nonuniformity occurred in the appearance of the surface after the alumite treatment. In the case of alloy 32B, since Mg content exceeded the upper limit, the effect based on Mg was saturated, and it was inferior to economic efficiency. In the case of alloys 27B to 32B, unevenness occurred in the external appearance of the cross section after the alumite treatment.

(10) Tenth Embodiment

This embodiment relates to the eighth invention. The aluminum alloy used in this embodiment is a 7000 Al-Zn-Mg based alloy.

Alloys 33B and 34B shown in Table 19 were used as the example alloys, and alloys 35B to 38B were used as the comparative alloys.

First, alloys 33B to 38B were sequentially processed in a dissolution step, a dehydrogenation gas step, a filtration step, and a casting step to produce an ingot having a sheet thickness of 500 mm.

Next, the ingot was treated in a heat treatment step. That is, the ingot was kept at 300 ° C. for 4 hours.

And the slice material and the hot rolling material were produced from the ingot after heat processing. The slice material was obtained by processing the ingot by the slicing process. The hot rolled material was obtained by hot rolling the ingot. The slice material and the hot rolled material are aluminum alloy thick plates each having a thickness of 20 mm, a width of 1,000 mm, and a length of 2,000 mm.

In addition, the obtained sliced material and hot rolled material were melt-processed at 470 degreeC, and also aged at 120 degreeC for 48 hours.

Therefore, the slice material after the treatment is an aluminum alloy thick plate obtained by the manufacturing method of the eighth invention, but the hot rolled material after the treatment is not. And only the slice material using alloy 33B and 34B corresponds to the Example of 8th invention.

Next, the strength test and the alumite evaluation test were performed about the slice material and the hot rolling material after the said process.

The method and evaluation criteria of each test are the same as those of the first embodiment.

However, since the characteristics of the thick plate differed depending on the alloy type, the evaluation criteria for the strength were as follows. That is, the intensity | strength made pass ((circle)) the case where tensile strength was 250 N / mm <^2> or more, and made the case where tensile strength less than 250 N / mm <^2> fail (x).

The test results are shown in Table 20.

(About slice materials)

As shown in Table 20, in the case of alloys 35B and 37B, the strengths were insufficient because the contents of Mg and Zn were less than the lower limit, respectively. In the case of alloys 36B and 38B, since the contents of Mg and Zn exceeded the upper limit, respectively, nonuniformity occurred in the appearance of the surface after the alumite treatment. In the case of alloys 33B to 38B, nonuniformity did not occur in the external appearance of the cross section after the alumite treatment.

(About hot rolled material)

As shown in Table 20, in the case of alloys 35B and 37B, the strengths were insufficient because the contents of Mg and Zn were less than the lower limit, respectively. In the case of alloys 36B and 38B, since the contents of Mg and Zn exceeded the upper limit, respectively, nonuniformity occurred in the appearance of the surface after the alumite treatment. In the case of alloys 33B to 38B, nonuniformity occurred in the appearance of the cross section after the alumite treatment.

(11) Eleventh embodiment

This embodiment relates to the ninth invention. The aluminum alloy used in this embodiment is a 5000-based Al-Mg based alloy.

Alloys 1C to 12C shown in Table 21 were used as example alloys, and alloys 13C to 22C were used as comparative alloys.

(process)

First, alloys 1C to 22C were sequentially processed in a dissolution step, a dehydrogenation gas step, a filtration step, and a casting step to produce an ingot having a sheet thickness of 500 mm.

Next, a slice material and a hot rolled material were produced from the ingot. Sliced material was obtained by treating the ingot by a slicing process. The hot rolled material was obtained by hot rolling after heat treatment of the ingot. The slice material and the hot rolled material are aluminum alloy thick plates each having a thickness of 20 mm, a width of 1,000 mm, and a length of 2,000 mm.

And the said slice material was processed in the heat processing process. That is, the said slice material was hold | maintained at 350 degreeC for 4 hours.

Therefore, the slice material after the treatment is an aluminum alloy thick plate obtained by the manufacturing method of the ninth invention, but the hot rolled material after the treatment is not. And only the slice material using alloy 1C-22C corresponds to the Example of 9th invention.

Next, the flatness evaluation test, the plate | board thickness precision evaluation test, the strength test, and the armite property evaluation test were performed about the slice material and the hot rolling material after the said process. The method and evaluation criteria of each test are the same as those of the first embodiment.

On the other hand, since the crystal grain size of the thick plate affects the armite property, the average grain size of the thick plate was obtained as in the case of the first example.

The test results are shown in Table 22 and Table 23.

Table 22 shows the test results for the slice material. In Table 22, Alloys 1C to 12C correspond to Examples of the ninth invention, and Alloys 13C to 22C correspond to Comparative Examples. Table 23 shows the test results for the hot rolled material. In Table 23, all of alloys 1C to 22C correspond to comparative examples.

(About slice materials)

As shown in Table 22, in the case of alloys 1C to 13C and 15C to 22C, the processing deformation was small and the warpage was small. That is, flatness was favorable. Moreover, the plate | board thickness precision was also excellent.

In the case of Alloy 14C, since the content of Mg exceeded the upper limit, casting cracking occurred and manufacturing was impossible. In the case of Alloy 13C, the strength was insufficient because the Mg content was less than the lower limit.

In the case of alloys 1C to 13C, 17C and 20C to 22C, there was no nonuniformity in the appearance of the surface after the alumite treatment. In the case of alloys 15C, 16C, 18C, and 19C, since the contents of Si, Fe, Mn, and Cr exceeded the upper limit, respectively, coarse intermetallic compounds were generated, and nonuniformity was generated in the appearance of the surface after the alumite treatment. . In the case of alloys 1C to 13C and 15C to 22C, there was no nonuniformity in the appearance of the cross section after the alumite treatment.

On the other hand, in the case of alloys 17C, 20C, 21C, and 22C, since the contents of Cu, Zn, Ti, and Zr exceeded the upper limit, respectively, the effects based on them were saturated and the economy was inferior.

(About hot rolled material)

As shown in Table 23, in the case of alloys 1C to 13C and 15C to 22C, work strain was accumulated and warping in the rolling direction was large. That is, flatness was poor. In addition, the plate | board thickness precision was inferior to the slice material in many cases.

In the case of Alloy 14C, since the content of Mg exceeded the upper limit, casting cracks occurred, and production was impossible. In the case of Alloy 13C, the strength was insufficient because the Mg content was less than the lower limit.

In the case of alloys 15C, 16C, 18C, and 19C, since the contents of Si, Fe, Mn, and Cr exceeded the upper limit, respectively, coarse intermetallic compounds were generated, and unevenness occurred in the appearance of the surface after the alumite treatment. . In the case of alloys 1C to 13C and 15C to 22C, nonuniformity occurred in the appearance of the cross section after the alumite treatment.

(12) Twelfth Embodiment

This embodiment relates to the ninth invention. In this example, alloy 3C shown in Table 21 is used.

(process)

First, alloy 3C was sequentially processed in a dissolution step, a dehydrogenation gas step, a filtration step, and a casting step to produce an ingot having a plate thickness of 500 mm.

Next, the ingot was treated in a slicing step to obtain a slice material. The slice material is an aluminum alloy thick plate having a thickness of 20 mm, a width of 1,000 mm, and a length of 2,000 mm.

And the said slice material was processed in the heat processing process. That is, the slice material was heat-treated under the conditions shown in Table 24.

Therefore, C1 and C2 whose heat treatment conditions satisfy the ninth invention correspond to the ninth embodiment, and C3 to C5 whose heat treatment conditions do not satisfy the ninth invention correspond to the comparative example.

The flatness evaluation test and the plate | board thickness precision evaluation test were done about the slice material after the said process.

<Flatness evaluation test>

Flatness evaluation was performed by measuring the amount of warpage (flatness) per casting direction 1m. The case where flatness was 0.4 mm / 1 m or less was made into pass ((circle)), and the case exceeding 0.4 mm / 1m length was made into reject (x).

<Plate thickness precision evaluation test>

The sheet thickness precision evaluation test is the same as that in the first embodiment.

<Cutting Test Evaluation>

The machinability evaluation test was the same as that in the seventh example.

The test results are shown in Table 24.

As shown in Table 24, in Examples C1 and C2, since the heat treatment conditions satisfy the ninth invention, the flatness, the plate thickness precision, and the machinability were good. In Comparative Example C3, since the heat treatment was not performed, the flatness was poor, and the plate thickness precision was slightly inferior to that of Examples C1 and C2. In the comparative example C4, since process temperature was higher than the range of 9th invention, cutting property was inferior. In Comparative Example C5, since the treatment temperature was lower than the range of the ninth invention, flatness was poor, and the plate thickness precision was slightly inferior to Examples C1 and C2.

(13) thirteenth embodiment

This embodiment relates to the tenth invention. The aluminum alloy used in the present embodiment is a 3000-based Al-Mn alloy.

Alloys 23C and 24C shown in Table 25 were used as example alloys, and alloys 25C and 26C were used as comparative alloys.

(process)

First, alloys 23C to 26C were sequentially processed in a dissolution step, a dehydrogenation gas step, a filtration step, and a casting step to produce an ingot having a sheet thickness of 500 mm.

Next, a slice material and a hot rolled material were produced from the ingot. Sliced material was obtained by treating the ingot by a slicing process. The hot rolled material was obtained by hot rolling after heat treatment of the ingot. The slice material and the hot rolled material are aluminum alloy thick plates each having a thickness of 20 mm, a width of 1,000 mm, and a length of 2,000 mm.

And the said slice material was processed in the heat processing process. That is, the said slice material was hold | maintained at 350 degreeC for 4 hours.

Therefore, the slice material after the treatment is an aluminum alloy thick plate obtained by the manufacturing method of the tenth invention, but the hot rolled material after the treatment is not. And only the slice material using alloy 23C and 24C corresponds to the Example of 10th invention.

Next, the flatness evaluation test, the plate | board thickness precision evaluation test, the strength test, and the armite property evaluation test were performed about the slice material and the hot rolling material after the said process.

The method and evaluation criteria of each test are the same as those of the first embodiment.

However, since the characteristics of the thick plate differed depending on the alloy type, the evaluation criteria for the strength were as follows. That is, the intensity | strength makes pass ((circle)) the case where tensile strength is 90 N / mm <^2> or more, and tensile strength is 90 N / mm <^2>. The case below was set as reject (x).

The test results are shown in Table 26.

(About slice materials)

As shown in Table 26, in the case of alloys 23C to 26C, there was little work deformation and warpage was small. That is, flatness was favorable. Moreover, the plate | board thickness precision was also excellent.

In the case of alloy 25C, since the content of Mn was less than the lower limit, the strength was insufficient. In the case of alloy 26C, since the content of Mn exceeded the upper limit, a coarse intermetallic compound was produced, causing nonuniformity in the appearance of the surface after the alumite treatment. In the case of alloys 23C to 26C, nonuniformity did not occur in the appearance of the cross section after the alumite treatment.

(About hot rolled material)

As shown in Table 26, in the case of alloys 23C to 26C, work strain was accumulated and warping in the rolling direction was large. That is, flatness was poor. In addition, the plate | board thickness precision was inferior to the slice material in many cases.

In the case of alloy 25C, since the content of Mn was less than the lower limit, the strength was slightly inferior to that of other hot rolled materials. In the case of alloy 26C, since the content of Mn exceeded the upper limit, a coarse intermetallic compound was produced, causing nonuniformity in the appearance of the surface after the alumite treatment. In the case of alloys 23C to 26C, nonuniformity occurred in the appearance of the cross section after the alumite treatment.

(14) Fourteenth Embodiment

This embodiment relates to the eleventh invention. The aluminum alloy used in this embodiment is a 6000-based Al-Mg-Si alloy.

Alloys 27C and 28C shown in Table 27 were used as example alloys, and alloys 29C to 32C were used as comparative alloys.

(process)

First, alloys 27C to 32C were sequentially processed in a dissolution step, a dehydrogenation gas step, a filtration step, and a casting step to produce an ingot having a sheet thickness of 500 mm.

Next, a slice material and a hot rolled material were produced from the ingot. Sliced material was obtained by treating the ingot by a slicing process. The hot rolled material was obtained by hot rolling after heat treatment of the ingot. The slice material and the hot rolled material are aluminum alloy thick plates each having a thickness of 20 mm, a width of 1,000 mm, and a length of 2,000 mm.

And the said slice material was processed in the heat processing process. That is, the said slice material was hold | maintained at 350 degreeC for 4 hours.

In addition, the obtained sliced material and hot rolled material were melt-processed at 520 degreeC, and also aged at 175 degreeC for 8 hours.

Therefore, the slice material after the treatment is an aluminum alloy thick plate obtained by the manufacturing method of the eleventh invention, but the hot rolled material after the treatment is not. And only the slice material using alloy 27C and 28C corresponds to the Example of 11th invention.

Next, the strength test and the alumite evaluation test were performed about the slice material and the hot rolling material after the said process.

The method and evaluation criteria of each test are the same as those of the first embodiment.

However, since the characteristics of the thick plate differed depending on the alloy type, the evaluation criteria for the strength were as follows. That is, the intensity | strength made pass ((circle)) the case where tensile strength was 200 N / mm <^2> or more, and made the case where tensile strength less than 200N / mm <^2> fail (x).

The test results are shown in Table 28.

(About slice materials)

As shown in Table 28, in the case of alloys 29C and 31C, the strength was insufficient because the contents of Si and Mg were less than the lower limit, respectively. In the case of alloy 30C, since the content of Si exceeded the upper limit, a coarse intermetallic compound was generated, and a nonuniformity occurred in the appearance of the surface after the alumite treatment. In the case of alloy 32C, since the content of Mg exceeded the upper limit, the effect based on Mg was saturated, and the economic efficiency was inferior. In the case of alloys 27C to 32C, nonuniformity did not occur in the appearance of the cross section after the alumite treatment.

(About hot rolled material)

As shown in Table 28, in the case of alloys 29C and 31C, the strength was insufficient because the contents of Si and Mg were less than the lower limit, respectively. In the case of alloy 30C, since the content of Si exceeded the upper limit, a coarse intermetallic compound was generated, and a nonuniformity occurred in the appearance of the surface after the alumite treatment. In the case of alloy 32C, since the content of Mg exceeded the upper limit, the effect based on Mg was saturated, and the economic efficiency was inferior. In the case of alloys 27C to 32C, nonuniformity occurred in the appearance of the cross section after the alumite treatment.

(15) Fifteenth Embodiment

This embodiment relates to the twelfth invention. The aluminum alloy used in this embodiment is a 7000 Al-Zn-Mg based alloy.

Alloys 33C and 34C shown in Table 29 were used as example alloys, and alloys 35C to 38C were used as comparative alloys.

(process)

First, alloys 33C to 38C were sequentially processed in a dissolution step, a dehydrogenation gas step, a filtration step, and a casting step to produce an ingot having a plate thickness of 500 mm.

Next, a slice material and a hot rolled material were produced from the ingot. Sliced material was obtained by treating the ingot in a slicing process. The hot rolled material was obtained by hot rolling after heat treatment of the ingot. The slice material and the hot rolled material are aluminum alloy thick plates each having a thickness of 20 mm, a width of 1,000 mm, and a length of 2,000 mm.

And the said slice material was processed in the heat processing process. That is, the said slice material was hold | maintained at 300 degreeC for 4 hours.

In addition, the obtained sliced material and hot rolled material were melt-processed at 470 degreeC, and also aged at 120 degreeC for 48 hours.

Therefore, the slice material after the treatment is an aluminum alloy thick plate obtained by the manufacturing method of the twelfth invention, but the hot rolled material after the treatment is not. And only the slice material using alloy 33C and 34C corresponds to the Example of 12th invention.

Next, the strength test and the alumite evaluation test were performed about the slice material and the hot rolling material after the said process.

The method and evaluation criteria of each test are the same as those of the first embodiment.

However, since the characteristics of the thick plate differed depending on the alloy type, the evaluation criteria for the strength were as follows. That is, the intensity | strength makes pass ((circle)) the case where tensile strength is 250 N / mm <^2> or more, and tensile strength is 250 N / mm <^2>. The case below was set as reject (x).

The test results are shown in Table 30.

(About slice materials)

As shown in Table 30, in the case of alloys 35C and 37C, the contents were insufficient because the contents of Mg and Zn were less than the lower limit, respectively. In the case of alloys 36C and 38C, since the contents of Mg and Zn exceeded the upper limit, respectively, nonuniformity occurred in the appearance of the surface after the alumite treatment. In the case of alloys 33C to 38C, nonuniformity did not occur in the appearance of the cross section after the alumite treatment.

(About hot rolled material)

As shown in Table 30, in the case of alloys 35C and 37C, the contents were insufficient because the contents of Mg and Zn were less than the lower limit, respectively. In the case of alloys 36C and 38C, since the contents of Mg and Zn exceeded the upper limit, respectively, nonuniformity occurred in the appearance of the surface after the alumite treatment. In the case of alloys 33C to 38C, nonuniformity occurred in the appearance of the cross section after the alumite treatment.

The manufacturing method of the aluminum alloy thick plate of this invention has the outstanding productivity, since it can control a surface state and flatness easily, and can improve plate thickness precision, and it is of great industrial use value.

S1 melting process
S2 Dehydrogenation Process
S3 filtration process
S4 casting process
S5 slice process or heat treatment process
S6 heat treatment process or slice process
S7 Surface Smoothing Process
A thickness direction center
B thickness direction center part
T thickness
1 ingot

Claims (15)

As a method for producing an aluminum alloy thick plate from an aluminum alloy without performing hot rolling,
The aluminum alloy contains Mg: 1.5% by mass or more and 12.0% by mass or less, and Si: 0.7% by mass or less, Fe: 0.8% by mass or less, Cu: 0.6% by mass or less, Mn: 1.0% by mass or less, Cr: 0.5 At least one of mass% or less, Zn: 0.4 mass% or less, Ti: 0.1 mass% or less, Zr: 0.3 mass% or less, and the remainder are made of Al and unavoidable impurities,
A dissolution step of dissolving the aluminum alloy,
Dehydrogenation process for removing hydrogen gas from the molten aluminum alloy,
A filtration process for removing inclusions from an aluminum alloy from which hydrogen gas has been removed,
A casting process of manufacturing an ingot by casting an aluminum alloy from which inclusions are removed;
A heat treatment step of performing heat treatment by maintaining the ingot at a temperature of 200 ° C. or more and less than 400 ° C. for at least 1 hour, and
Slicing process to slice the heat-treated ingot to produce a thick aluminum alloy plate
The manufacturing method of the aluminum alloy thick plate characterized by performing sequentially. As a method for producing an aluminum alloy thick plate from an aluminum alloy without performing hot rolling,
The said aluminum alloy contains Mn: 0.3 mass% or more and 1.6 mass% or less, Si: 0.7 mass% or less, Fe: 0.8 mass% or less, Cu: 0.5 mass% or less, Mg: 1.5 mass% or less, Cr: 0.3 At least one of mass% or less, Zn: 0.4 mass% or less, Ti: 0.1 mass% or less, Zr: 0.3 mass% or less, and the remainder are made of Al and unavoidable impurities,
A dissolution step of dissolving the aluminum alloy,
Dehydrogenation process for removing hydrogen gas from the molten aluminum alloy,
A filtration process for removing inclusions from an aluminum alloy from which hydrogen gas has been removed,
A casting process of manufacturing an ingot by casting an aluminum alloy from which inclusions are removed;
A heat treatment step of performing heat treatment by maintaining the ingot at a temperature of 200 ° C. or more and less than 400 ° C. for at least 1 hour, and
Slicing process to slice the heat-treated ingot to produce a thick aluminum alloy plate
The manufacturing method of the aluminum alloy thick plate characterized by performing sequentially. As a method for producing an aluminum alloy thick plate from an aluminum alloy without performing hot rolling,
The said aluminum alloy contains Si: 0.2 mass% or more and 1.6 mass% or less, Mg: 0.3 mass% or more and 1.5 mass% or less, and also Fe: 0.8 mass% or less, Cu: 1.0 mass% or less, Mn: 0.6 mass% Hereafter, at least one of Cr: 0.5% by mass or less, Zn: 0.4% by mass or less, Ti: 0.1% by mass or less, Zr: 0.3% by mass or less, and the remainder are made of Al and unavoidable impurities,
A dissolution step of dissolving the aluminum alloy,
Dehydrogenation process for removing hydrogen gas from the molten aluminum alloy,
A filtration process for removing inclusions from an aluminum alloy from which hydrogen gas has been removed,
A casting process of manufacturing an ingot by casting an aluminum alloy from which inclusions are removed;
A heat treatment step of performing heat treatment by maintaining the ingot at a temperature of 200 ° C. or more and less than 400 ° C. for at least 1 hour, and
Slicing process to slice the heat-treated ingot to produce a thick aluminum alloy plate
The manufacturing method of the aluminum alloy thick plate characterized by performing sequentially. As a method for producing an aluminum alloy thick plate from an aluminum alloy without performing hot rolling,
The aluminum alloy contains Mg: 0.4% by mass or more and 4.0% by mass or less, Zn: 3.0% by mass or more and 9.0% by mass or less, and Si: 0.7% by mass or less, Fe: 0.8% by mass or less, and Cu: 3.0% by mass or less. At least one of Mn: 0.8% by mass or less, Cr: 0.5% by mass or less, Ti: 0.1% by mass or less, and Zr: 0.25% by mass or less, and the balance is made of Al and unavoidable impurities.
A dissolution step of dissolving the aluminum alloy,
Dehydrogenation process for removing hydrogen gas from the molten aluminum alloy,
A filtration process for removing inclusions from an aluminum alloy from which hydrogen gas has been removed,
A casting process of manufacturing an ingot by casting an aluminum alloy from which inclusions are removed;
A heat treatment step of performing heat treatment by maintaining the ingot at a temperature of 200 ° C. or higher and less than 350 ° C. for at least 1 hour, and
Slicing process to slice the heat-treated ingot to produce a thick aluminum alloy plate
The manufacturing method of the aluminum alloy thick plate characterized by performing sequentially. The method according to any one of claims 1 to 4,
A surface smoothing treatment step of subjecting the surface of the aluminum alloy thick plate of a predetermined thickness to a surface smoothing treatment is performed after the slicing step. The method of claim 5, wherein
The surface smoothing treatment is performed by at least one method selected from a cutting method, a grinding method and a polishing method. The method according to any one of claims 1 to 4,
In the slicing step, the thickness direction center portion has a thickness equal to the respective surfaces in the thickness direction from the thickness direction center and has a total thickness of T / 30 to T / 5 when the thickness of the ingot is T. And removing the ingot from the ingot. As a method for producing an aluminum alloy thick plate from an aluminum alloy without performing hot rolling,
The aluminum alloy contains Mg: 1.5% by mass or more and 12.0% by mass or less, and Si: 0.7% by mass or less, Fe: 0.8% by mass or less, Cu: 0.6% by mass or less, Mn: 1.0% by mass or less, Cr: 0.5 At least one of mass% or less, Zn: 0.4 mass% or less, Ti: 0.1 mass% or less, Zr: 0.3 mass% or less, and the remainder are made of Al and unavoidable impurities,
A dissolution step of dissolving the aluminum alloy,
Dehydrogenation process for removing hydrogen gas from the molten aluminum alloy,
A filtration process for removing inclusions from an aluminum alloy from which hydrogen gas has been removed,
A casting process of manufacturing an ingot by casting an aluminum alloy from which inclusions are removed;
A slice process of slicing the ingot to produce an aluminum alloy thick plate having a predetermined thickness; and
The heat treatment process of heat-treating the aluminum alloy thick plate of predetermined thickness at 200 degreeC or more and less than 400 degreeC for 1 hour or more is performed.
The manufacturing method of the aluminum alloy thick plate characterized by performing sequentially. As a method for producing an aluminum alloy thick plate from an aluminum alloy without performing hot rolling,
The said aluminum alloy contains Mn: 0.3 mass% or more and 1.6 mass% or less, Si: 0.7 mass% or less, Fe: 0.8 mass% or less, Cu: 0.5 mass% or less, Mg: 1.5 mass% or less, Cr: 0.3 At least one of mass% or less, Zn: 0.4 mass% or less, Ti: 0.1 mass% or less, Zr: 0.3 mass% or less, and the remainder are made of Al and unavoidable impurities,
A dissolution step of dissolving the aluminum alloy,
Dehydrogenation process for removing hydrogen gas from the molten aluminum alloy,
A filtration process for removing inclusions from an aluminum alloy from which hydrogen gas has been removed,
A casting process of manufacturing an ingot by casting an aluminum alloy from which inclusions are removed;
A slice process of slicing the ingot to produce an aluminum alloy thick plate having a predetermined thickness; and
The heat treatment process of heat-treating the aluminum alloy thick plate of predetermined thickness at 200 degreeC or more and less than 400 degreeC for 1 hour or more is performed.
The manufacturing method of the aluminum alloy thick plate characterized by performing sequentially. As a method for producing an aluminum alloy thick plate from an aluminum alloy without performing hot rolling,
The said aluminum alloy contains Si: 0.2 mass% or more and 1.6 mass% or less, Mg: 0.3 mass% or more and 1.5 mass% or less, and also Fe: 0.8 mass% or less, Cu: 1.0 mass% or less, Mn: 0.6 mass% Hereafter, at least one of Cr: 0.5% by mass or less, Zn: 0.4% by mass or less, Ti: 0.1% by mass or less, Zr: 0.3% by mass or less, and the remainder are made of Al and unavoidable impurities,
A dissolution step of dissolving the aluminum alloy,
Dehydrogenation process for removing hydrogen gas from the molten aluminum alloy,
A filtration process for removing inclusions from an aluminum alloy from which hydrogen gas has been removed,
A casting process of manufacturing an ingot by casting an aluminum alloy from which inclusions are removed;
A slice process of slicing the ingot to produce an aluminum alloy thick plate having a predetermined thickness; and
The heat treatment process of heat-treating the aluminum alloy thick plate of predetermined thickness at 200 degreeC or more and less than 400 degreeC for 1 hour or more is performed.
The manufacturing method of the aluminum alloy thick plate characterized by performing sequentially. As a method for producing an aluminum alloy thick plate from an aluminum alloy without performing hot rolling,
The aluminum alloy contains Mg: 0.4% by mass or more and 4.0% by mass or less, Zn: 3.0% by mass or more and 9.0% by mass or less, and Si: 0.7% by mass or less, Fe: 0.8% by mass or less, and Cu: 3.0% by mass or less. At least one of Mn: 0.8% by mass or less, Cr: 0.5% by mass or less, Ti: 0.1% by mass or less, and Zr: 0.25% by mass or less, and the balance is made of Al and unavoidable impurities.
A dissolution step of dissolving the aluminum alloy,
Dehydrogenation process for removing hydrogen gas from the molten aluminum alloy,
A filtration process for removing inclusions from an aluminum alloy from which hydrogen gas has been removed,
A casting process of manufacturing an ingot by casting an aluminum alloy from which inclusions are removed;
A slice process of slicing the ingot to produce an aluminum alloy thick plate having a predetermined thickness; and
The heat treatment step of heat treatment by maintaining the aluminum alloy thick plate of a predetermined thickness at a temperature of 200 ℃ to less than 350 ℃ for 1 hour or more
The manufacturing method of the aluminum alloy thick plate characterized by performing sequentially. The method according to any one of claims 8 to 11,
And a surface smoothing treatment step of subjecting the surface of the aluminum alloy thick plate to a surface smoothing treatment after the heat treatment step. 13. The method of claim 12,
The surface smoothing treatment is performed by at least one method selected from a cutting method, a grinding method and a polishing method. The method according to any one of claims 8 to 11,
In the slicing step, the thickness direction center portion has a thickness equal to the respective surfaces in the thickness direction from the thickness direction center and has a total thickness of T / 30 to T / 5 when the thickness of the ingot is T. And removing the ingot from the ingot. An aluminum alloy thick plate manufactured by the method for producing an aluminum alloy thick plate according to any one of claims 1 to 4 and 8 to 11, wherein the aluminum alloy has an average grain size of 400 μm or less. Thick plates.

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