WO2023068166A1 - Procédé de production d'un tuyau à trous multiples extrudé - Google Patents

Procédé de production d'un tuyau à trous multiples extrudé Download PDF

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Publication number
WO2023068166A1
WO2023068166A1 PCT/JP2022/038245 JP2022038245W WO2023068166A1 WO 2023068166 A1 WO2023068166 A1 WO 2023068166A1 JP 2022038245 W JP2022038245 W JP 2022038245W WO 2023068166 A1 WO2023068166 A1 WO 2023068166A1
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mass
less
ingot
extruded multi
content
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PCT/JP2022/038245
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English (en)
Japanese (ja)
Inventor
太一 鈴木
稜 東森
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株式会社Uacj
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Priority to CN202280063203.8A priority Critical patent/CN117957340A/zh
Priority to EP22883470.1A priority patent/EP4393613A1/fr
Publication of WO2023068166A1 publication Critical patent/WO2023068166A1/fr

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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C25/00—Profiling tools for metal extruding
    • B21C25/02—Dies
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F28—HEAT EXCHANGE IN GENERAL
    • F28D—HEAT-EXCHANGE APPARATUS, NOT PROVIDED FOR IN ANOTHER SUBCLASS, IN WHICH THE HEAT-EXCHANGE MEDIA DO NOT COME INTO DIRECT CONTACT
    • F28D1/00—Heat-exchange apparatus having stationary conduit assemblies for one heat-exchange medium only, the media being in contact with different sides of the conduit wall, in which the other heat-exchange medium is a large body of fluid, e.g. domestic or motor car radiators
    • F28D1/02—Heat-exchange apparatus having stationary conduit assemblies for one heat-exchange medium only, the media being in contact with different sides of the conduit wall, in which the other heat-exchange medium is a large body of fluid, e.g. domestic or motor car radiators with heat-exchange conduits immersed in the body of fluid
    • F28D1/04—Heat-exchange apparatus having stationary conduit assemblies for one heat-exchange medium only, the media being in contact with different sides of the conduit wall, in which the other heat-exchange medium is a large body of fluid, e.g. domestic or motor car radiators with heat-exchange conduits immersed in the body of fluid with tubular conduits
    • F28D1/053—Heat-exchange apparatus having stationary conduit assemblies for one heat-exchange medium only, the media being in contact with different sides of the conduit wall, in which the other heat-exchange medium is a large body of fluid, e.g. domestic or motor car radiators with heat-exchange conduits immersed in the body of fluid with tubular conduits the conduits being straight
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F28—HEAT EXCHANGE IN GENERAL
    • F28F—DETAILS OF HEAT-EXCHANGE AND HEAT-TRANSFER APPARATUS, OF GENERAL APPLICATION
    • F28F1/00—Tubular elements; Assemblies of tubular elements
    • F28F1/02—Tubular elements of cross-section which is non-circular
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F28—HEAT EXCHANGE IN GENERAL
    • F28F—DETAILS OF HEAT-EXCHANGE AND HEAT-TRANSFER APPARATUS, OF GENERAL APPLICATION
    • F28F21/00—Constructions of heat-exchange apparatus characterised by the selection of particular materials
    • F28F21/08—Constructions of heat-exchange apparatus characterised by the selection of particular materials of metal

Definitions

  • the present invention relates to a method for manufacturing an extruded multi-hole pipe.
  • the extruded multi-hole pipe has an outer wall portion that constitutes its outer peripheral portion and a partition wall portion that defines a space surrounded by the outer wall portion, and the fluid flows through the passage surrounded by the outer wall portion and the partition wall portion. It is configured so that it can be In order to form a complex cross-sectional shape with such a fine structure by extrusion, the extruded multi-hole tube is made of an aluminum alloy with a relatively low content of alloying elements and excellent extrudability. There are many things.
  • Patent Document 1 in terms of mass%, Si: 0.01 to 0.3%, Fe: 0.01 to 0.3%, Cu: 0.05 to 0.4%, Mn: 0.05 to 0 .3%, Zr: 0.05 to 0.25%, Ti: 0 to 0.15%, the total of Zr and Ti is 0.3% or less, and the balance is Al and inevitable impurities Corrosion resistance, characterized in that the AlFeSi stable phase accounts for an area ratio of 0.1% or more and less than 0.5% among particles made of an aluminum alloy and dispersed in a matrix and having a particle area of 1.0 ⁇ m 2 or more. describes extruded flat multi-hole tubes for heat exchangers which are excellent in
  • aluminum scrap contains various elements other than aluminum.
  • the aluminum scrap may contain metallic materials other than aluminum, such as iron, in some cases. Therefore, when aluminum waste is reused as a raw material for casting, the content of elements other than aluminum increases, causing various problems such as an increase in deformation resistance during hot extrusion and a decrease in extrusion speed. rice field. Therefore, in the conventional technical level, it was considered difficult to produce an extruded multi-hole pipe having a complicated cross-sectional shape when aluminum waste material was used as a casting raw material.
  • the present invention has been made in view of such a background, and provides a method for manufacturing an extruded multi-hole tube that can be easily hot-extruded even when the content of elements other than aluminum is relatively high. I am trying to.
  • One aspect of the present invention includes Si (silicon): 2.00 mass % or less, Fe (iron): 0.60 mass % or less, Cu (copper): 0.60 mass % or less, Mn (manganese): 2.00 mass % or less.
  • Mg manganesium
  • Cr chromium
  • Zn zinc
  • Ti titanium
  • Ti titanium
  • B boron
  • the ingot is held at a temperature of 550 ° C. or higher and 650 ° C.
  • the ingot is held at a temperature of 450 ° C. or higher and 540 ° C. or lower for 3 hours or more to perform a second homogenization treatment, After that, the ingot is subjected to hot extrusion to produce an extruded multi-hole pipe.
  • the ingot having the chemical composition within the specific range is subjected to the first homogenization treatment and the second homogenization treatment.
  • the homogenization treatment is performed in two stages, and the holding temperature and holding time of the homogenization treatment in each stage are set within the specific ranges described above, so that even when the content of elements other than aluminum is relatively large, Even if there is, an increase in deformation resistance during hot extrusion can be suppressed.
  • FIG. 1 is a perspective view of an extruded multi-hole tube in Example 1.
  • an ingot having the specific chemical composition is produced.
  • the ingot contains one or more elements selected from the group consisting of Si, Fe, Cu, Mn, Mg, Cr, Zn, Ti and B. These elements are contained in casting raw materials such as aluminum ingots, aluminum scraps, and intermediate alloys. When aluminum waste is used as the casting raw material, the elements mentioned above may be mainly derived from the aluminum waste.
  • Si is an element contained in aluminum base metals, aluminum alloys containing Si (for example, 4000 series alloys and 6000 series alloys, etc.) in aluminum scraps, intermediate alloys, and the like.
  • Si has the effect of improving the strength of the extruded multi-hole pipe.
  • the Si content is preferably 0.20% by mass or more, more preferably 0.40% by mass or more, and more preferably 0.60% by mass. It is more preferably 0.70% by mass or more, particularly preferably 0.70% by mass or more, and most preferably 0.80% by mass or more.
  • the Si content is excessively high, the deformation resistance of the ingot during hot extrusion increases, which may lead to a decrease in extrudability.
  • the Si content is 2.00% by mass or less, preferably 1.50% by mass or less, more preferably 1.40% by mass or less, and even more preferably 1.30% by mass or less, during hot extrusion It is possible to improve the strength of the extruded multi-hole pipe while suppressing an increase in the deformation resistance of the ingot.
  • Mn may be contained in an ingot in an amount of more than 0% by mass and 2.00% by mass or less.
  • Mn is an element contained in aluminum base metals, aluminum alloys containing Mn in aluminum scraps (for example, 3000 series alloys, etc.), intermediate alloys, and the like.
  • Mn has the effect of improving the strength of the extruded multi-hole pipe.
  • the Mn content is preferably 0.40% by mass or more, more preferably 0.60% by mass or more, and more preferably 0.80% by mass. It is more preferably 0.90% by mass or more, particularly preferably 0.90% by mass or more, and most preferably 1.00% by mass or more.
  • the Mn content is excessively high, the deformation resistance of the ingot during hot extrusion increases, which may lead to a decrease in extrudability.
  • the Mn content is 2.00% by mass or less, preferably 1.80% by mass or less, and more preferably 1.70% by mass or less, an increase in deformation resistance of the ingot during hot extrusion is suppressed.
  • the strength of the extruded multi-hole tube can be improved.
  • the sum of the Si content and the Mn content in the ingot is 3.20% by mass or less, and the Si content is less than the Mn content.
  • the Si content and the Mn content satisfy the above-described relationship, so that during hot extrusion It is possible to more effectively suppress the increase in deformation resistance of the ingot, and easily produce an extruded multi-hole pipe having a complicated cross-sectional shape.
  • the total content of Si and Mn is preferably 3.00% by mass or less.
  • the extrudability during hot extrusion may deteriorate.
  • the Si content is greater than or equal to the Mn content, it becomes difficult to deposit fine AlMnSi-based intermetallic compounds in the ingot, which may lead to deterioration in extrudability.
  • the extrusion limit speed tends to decrease, which may lead to a decrease in the productivity of the extruded multi-hole tube.
  • the ingot may contain more than 0% by mass and 0.60% by mass or less of Fe.
  • Fe is an element contained in aluminum ingots, aluminum scraps, and the like.
  • aluminum scraps sometimes contain parts made of Fe-based alloys, and when such aluminum scraps are used as casting raw materials, the Fe content in the ingot tends to increase.
  • the Fe content is preferably 0.10% by mass or more, more preferably 0.15% by mass or more, still more preferably 0.20% by mass or more, and particularly preferably 0.25% by mass or more. It is possible to make it easier to increase the ratio of the aluminum waste material in the inside.
  • the Fe content is excessively high, coarse AlFe-based intermetallic compounds tend to be formed in the ingot.
  • a coarse AlFe-based intermetallic compound in the ingot is not preferable because it may lead to deterioration of the surface properties of the extruded multi-hole pipe, such as an increase in surface roughness.
  • ⁇ Cu 0.60% by mass or less
  • the ingot may contain more than 0% by mass and 0.60% by mass or less of Cu.
  • Cu is an element contained in aluminum ingots, aluminum scraps, and the like.
  • aluminum scrap may contain parts made of an aluminum alloy containing a large amount of Cu (for example, a 2000 series alloy), and when such aluminum scrap is used as a casting raw material, The content of Cu tends to increase.
  • Cu has the effect of enhancing the natural potential of the extruded multi-hole pipe and improving the corrosion resistance of the extruded multi-hole pipe.
  • the Cu content is preferably 0.05% by mass or more, more preferably 0.10% by mass or more, and more preferably 0.15% by mass. It is more preferably 0.20 mass % or more, particularly preferably 0.20 mass % or more. Moreover, in this case, it is possible to easily increase the proportion of the aluminum scrap in the raw material for casting.
  • the Cu content is excessively high, the amount of dissolved Cu in the ingot increases, which may lead to an increase in the deformation resistance of the ingot during hot extrusion and a decrease in extrudability.
  • the corrosion resistance of the extruded multi-hole pipe is improved while suppressing an increase in the deformation resistance of the ingot during hot extrusion.
  • the ingot may contain more than 0% by mass and 0.40% by mass or less of Mg.
  • Mg is an element contained in aluminum ingots, aluminum scraps, and the like.
  • aluminum scraps may contain parts made of aluminum alloys containing a large amount of Mg (e.g., 5000 series alloys and 6000 series alloys).
  • Mg content in the ingot tends to increase.
  • Mg has the effect of improving the strength of the extruded multi-hole tube.
  • the Mg content is preferably 0.03% by mass or more, more preferably 0.05% by mass or more, and more preferably 0.07% by mass. It is more preferable that it is above.
  • it is possible to easily increase the proportion of the aluminum scrap in the raw material for casting.
  • the Mg content is excessively high, the amount of Mg solid-dissolved in the ingot increases, which may lead to an increase in the deformation resistance of the ingot during hot extrusion and a decrease in extrudability.
  • the Mg content By setting the Mg content to 0.40% by mass or less, preferably 0.30% by mass or less, an increase in deformation resistance of the ingot during hot extrusion can be suppressed.
  • the ingot may contain more than 0% by mass and 0.10% by mass or less of Cr.
  • Cr is an element contained in aluminum ingots, aluminum scraps, and the like.
  • aluminum scraps sometimes contain parts made of aluminum alloys containing a large amount of Cr (e.g., 5000 series alloys and 7000 series alloys). is likely to increase the Cr content in the ingot.
  • the Cr content By setting the Cr content to preferably 0.01% by mass or more, more preferably 0.02% by mass or more, and even more preferably 0.03% by mass or more, the proportion of aluminum scrap in the raw material for casting can be increased. can be made easier.
  • the ingot may contain more than 0% by mass and 1.50% by mass or less of Zn.
  • Zn is an element contained in aluminum ingots, aluminum scraps, and the like.
  • aluminum scrap may contain parts made of aluminum alloys containing a large amount of Zn (for example, 7000 series alloys, etc.).
  • the content of Zn in the inside tends to increase.
  • Zn weakens the surface oxide film of the extruded multi-hole pipe and disperses the occurrence of pitting corrosion, thereby improving corrosion resistance.
  • the Zn content is preferably 0.05% by mass or more, more preferably 0.10% by mass or more, and 0.15% by mass or more. is more preferred.
  • the Zn content is excessively high, the solidus temperature of the aluminum alloy will decrease, which may cause partial melting of the ingot or extruded multi-hole tube during homogenization or hot extrusion. be.
  • the Zn content is 1.50% by mass or less, preferably 1.00% by mass or less, the effects of Zn can be obtained while avoiding partial melting of the ingot or extruded multi-hole pipe.
  • the ingot may contain more than 0% by mass and 0.10% by mass or less of Ti.
  • Ti has the effect of refining the crystal grains in the metal structure of the ingot. From the viewpoint of further enhancing such effects, the Ti content is preferably 0.005% by mass or more, more preferably 0.007% by mass or more, and more preferably 0.010% by mass or more. More preferred.
  • the ingot may contain more than 0% by mass and 0.10% by mass or less of B.
  • the content of B in the extruded multi-hole tube is preferably 0.005% by mass or more and 0.10% by mass or less.
  • the ingot may contain elements other than the elements described above as unavoidable impurities.
  • examples of such elements include Zr (zirconium) and V (vanadium).
  • the content of elements as unavoidable impurities may be, for example, 0.05% by mass or less for each element. Also, the total content of elements as unavoidable impurities should be 0.50% by mass or less.
  • the ingot contains Si: 0.60% by mass or more and 1.40% by mass or less and Mn: 0.80% by mass or more and 1.80% by mass or less.
  • the balance consists of Al and unavoidable impurities, the total of the Si content and the Mn content is 3.20% by mass or less, and the Si content is less than the Mn content Chemical component
  • the ingot further has Fe: 0.10% by mass or more and 0.50% by mass or less, Cu: 0.05% by mass or more and 0.40% by mass or less, Mg: 0.05% by mass or more and 0.30% by mass.
  • % by mass or less Cr: 0.01% by mass or more and 0.10% by mass or less, Zn: 0.10% by mass or more and 1.00% by mass or less, Ti: 0.005% by mass or more and 0.10% by mass or less and B : 1 or 2 or more elements selected from the group consisting of 0.005% by mass or more and 0.10% by mass or less may be included as optional components.
  • the ingot has Si: 0.70% by mass or more and 1.30% by mass or less, Fe: 0.10% by mass or more and 0.50% by mass or less, Cu: 0.05% by mass or more and 0.40% by mass. % by mass or less, Mn: 0.90% by mass or more and 1.70% by mass or less, Mg: 0.05% by mass or more and 0.30% by mass or less, Cr: 0.01% by mass or more and 0.10% by mass or less, Zn : 0.10% by mass or more and 1.00% by mass or less, Ti: 0.005% by mass or more and 0.10% by mass or less, and B: 0.005% by mass or more and 0.10% by mass or less, and the balance is composed of Al and unavoidable impurities, the total of the Si content and the Mn content is 3.00% by mass or less, and the Si content is less than the Mn content. is preferred.
  • a known casting method such as DC casting or CC casting can be used to produce the ingot.
  • a raw material for casting when producing an ingot for example, virgin aluminum metal or scrap aluminum can be used.
  • the aluminum waste material includes offcuts and chips generated in the manufacturing process of aluminum products, used aluminum products, aluminum parts separated from used products, and the like.
  • the chemical composition of the ingot is set within the specific range, and then the two-stage homogenization treatment described later is performed to remove elements other than aluminum. Even when the content is relatively large, it is possible to suppress an increase in deformation resistance during hot extrusion. Therefore, according to the manufacturing method of the above aspect, even if aluminum waste material is used as at least a part of the casting raw material and the content of elements other than aluminum is relatively large, the casting material has a complicated cross-sectional shape. An extruded multi-hole tube can be easily produced.
  • the ratio of the aluminum waste material to the casting raw material is preferably 35% by mass or more, more preferably 45% by mass or more, and particularly preferably 60% by mass or more.
  • the ingot is held at a temperature of 550°C or higher and 650°C or lower for 2 hours or longer to perform a first homogenization treatment.
  • a first homogenization treatment By setting the holding temperature and holding time in the first homogenization treatment to the specific ranges, coarse crystallized substances in the ingot are decomposed, granulated, or redissolved in the Al matrix. can do.
  • the holding temperature in the first homogenization treatment is preferably 580°C or higher and 620°C or lower. From the same point of view, the holding time in the first homogenization treatment is preferably 10 hours or longer. Moreover, the retention time in the first homogenization treatment is preferably 24 hours or less from the viewpoint of productivity.
  • the holding temperature in the first homogenization treatment is less than 550°C, or if the holding time is less than 2 hours, there is a risk that the decomposition of crystallized substances will be insufficient. If the holding temperature in the first homogenization treatment exceeds 650°C, the ingot may partially melt.
  • the ingot after the first homogenization treatment is subjected to the second homogenization treatment.
  • the holding temperature in the second homogenization treatment is 450° C. or higher and 540° C. or lower, and the holding time is 3 hours or longer.
  • the primary purpose of the first homogenization treatment is to decompose, granulate, and redissolve coarse crystallized substances crystallized in the ingot during casting.
  • the holding temperature and holding time in the first homogenization treatment are within the above-mentioned specific ranges, the decomposition, granulation, and re-dissolution of crystallized substances, as well as the solute elements Mn and Si into the Al matrix phase. Solid solution is also promoted. If the amount of the solute element dissolved in the Al matrix is excessively large, the movement speed of dislocations in the matrix during hot extrusion decreases, and the deformation resistance tends to increase.
  • the Si and Mn dissolved in the Al matrix phase in the first homogenization treatment are finely precipitated as AlMnSi-based intermetallic compounds. can be done.
  • the solid solution amount of the solute element in the Al matrix can be reduced, and the deformation resistance during hot extrusion can be reduced. Therefore, the extrudability during hot extrusion can be improved by heating the ingot after the first homogenization treatment under the specific conditions and performing the second homogenization treatment.
  • the holding temperature in the second homogenization treatment is preferably 480°C or higher and 520°C or lower.
  • the holding time in the second homogenization treatment is preferably 5 hours or more.
  • the holding time in the second homogenization treatment is preferably 24 hours or less, more preferably 15 hours or less, from the viewpoint of productivity.
  • the holding temperature in the second homogenization treatment is less than 450 ° C., or if the holding time is less than 3 hours, the amount of precipitation of the AlMnSi-based intermetallic compound tends to decrease, and the extrudability during hot extrusion deteriorates. may lead to When the holding temperature in the second homogenization treatment exceeds 540 ° C., it becomes difficult for Si and Mn dissolved in the Al matrix to form an intermetallic compound, which may lead to deterioration of extrudability during hot extrusion.
  • the first homogenization treatment and the second homogenization treatment can be performed continuously.
  • performing the first homogenization treatment and the second homogenization treatment continuously means that after the first homogenization treatment is completed, the temperature of the ingot is lowered to the holding temperature in the second homogenization treatment, It refers to starting the second homogenization treatment when the temperature of the ingot reaches the holding temperature in the second homogenization treatment.
  • the second homogenization is performed at an average cooling rate of 20 ° C./hour or more and 60 ° C./hour or less. It is preferable to cool the ingot to the holding temperature in the hardening treatment.
  • the ingot after the first homogenization treatment is completed, the ingot can be once cooled to a temperature lower than the holding temperature in the second homogenization treatment, and then the second homogenization treatment can be performed.
  • the temperature of the ingot at the completion of cooling can be, for example, 200° C. or less.
  • the ingot is heated to the holding temperature in the second homogenization treatment at an average temperature increase rate of 20 ° C./hour or more and 60 ° C./hour or less. preferably.
  • the extruded multi-hole pipe can be obtained by subjecting the ingot after the second homogenization treatment to hot extrusion.
  • the temperature of the ingot at the start of extrusion and the temperature of the extruded multi-hole tube at the end of extrusion may be appropriately set according to the chemical composition of the extruded multi-hole tube.
  • the temperature of the ingot at the start of extrusion can be appropriately set within the range of 450°C or higher and 550°C or lower.
  • the extruded multi-hole pipe obtained in this way may be used as it is, or may be straightened or cut to adjust the size and shape, heat treated to adjust strength, zinc sprayed to improve corrosion resistance, or painted. You may use it after performing post-processing, such as. These post-treatments can be appropriately combined according to the use of the extruded multi-hole pipe.
  • the extruded multi-hole tube obtained by the manufacturing method has an outer wall section that separates an outer space from the inside of the extruded multi-hole tube, and a plurality of partition walls that separate the inner space of the outer wall section.
  • the extruded multi-hole tube has a plurality of passages surrounded by the outer wall portion and the partition wall portion, and is configured such that liquid, gas, etc. can be circulated through these passages.
  • the cross-sectional shape of the extruded multi-hole tube is not particularly limited, and can have various cross-sectional shapes such as an oval shape and a rectangular shape.
  • the cross-sectional shape of the passage of the extruded multi-hole tube is not particularly limited, and can have various cross-sectional shapes such as circular, triangular, and quadrangular.
  • the extruded multi-hole tube may have a flat cross-sectional shape.
  • the ratio of the width to the thickness of the extruded multi-hole tube can be 2 or more and 50 or less, preferably 3 or more and 30 or less.
  • the higher the ratio of the width to the thickness the more difficult it is to extrude, and there is a tendency that high extrudability is required.
  • the aluminum alloy ingot having the specific chemical composition is subjected to two-stage homogenization treatment to suppress the increase in deformation resistance during hot extrusion and improve the extrudability. can be enhanced. Therefore, it is possible to easily obtain an extruded multi-hole tube having a cross-sectional shape that requires such high extrudability.
  • the extruded multi-hole pipe has an outer wall portion that separates an outer space from the inside of the extruded multi-hole pipe, and a plurality of partition walls that separate the inner space of the outer wall portion.
  • the partition wall may have a thickness of 0.10 mm or more and 2.0 mm or less, preferably 0.15 mm or more and 1.5 mm or less.
  • the aluminum alloy ingot having the specific chemical composition is subjected to two-stage homogenization treatment to suppress the increase in deformation resistance during hot extrusion and improve the extrudability. can be enhanced. Therefore, it is possible to easily obtain an extruded multi-hole tube having a cross-sectional shape that requires such high extrudability.
  • an extruded multi-hole pipe can be produced by subjecting the ingot after the completion of the second homogenization treatment to hot extrusion.
  • the extruded multi-hole tube 1 of this example has a flat cross-sectional shape, as shown in FIG. More specifically, the extruded multi-hole tube 1 has an oval cross-sectional shape.
  • the width of the extruded multi-hole tube 1 is, for example, 14.0 mm, and the thickness is, for example, 2.5 mm.
  • the extruded multi-hole tube 1 has an outer wall portion 11 that separates the outer space from the inside, and a partition wall portion 13 that separates the space surrounded by the outer wall portion 11 into 19 passages 12 .
  • the passage 12 of the extruded multi-hole tube 1 in this example has a circular cross-sectional shape.
  • the thickness of the thinnest portion of the outer wall portion 11 and the partition wall portion 13 is, for example, 0.4 mm.
  • the ingot After producing the ingot, the ingot is held at a temperature of 600°C for 10 hours to perform a first homogenization treatment. After completing the first homogenization treatment, the ingot is held at a temperature of 500° C. for 10 hours to perform a second homogenization treatment.
  • the first homogenization treatment and the second homogenization treatment may be performed continuously, or after the first homogenization treatment is completed and before the second homogenization treatment is performed, the temperature of the ingot is the second It may be below the holding temperature in the homogenization treatment.
  • the extruded multi-hole tube 1 is produced by subjecting the ingot to hot extrusion while the temperature of the ingot is 500°C.
  • the test materials S1 to S3 shown in Table 2 can be obtained.
  • the test materials R1 to R4 shown in Table 2 are test materials for comparison with the test materials S1 to S3.
  • the method for producing test materials R1 to R3 was the same as that for test materials S1 to S3, except that the chemical composition of the ingot was changed to alloy symbols A4 to A6 shown in Table 1.
  • the method for producing test material R4 was the same as that for test materials S1 to S3, except that the chemical composition of the ingot was changed to alloy symbol A7 shown in Table 1 and the second homogenization treatment was omitted.
  • Extrudability can be evaluated based on the appearance of the test material. More specifically, the appearance of the test material is visually observed to evaluate the presence or absence of cracks and streaky patterns along the extrusion direction. Table 2 shows the presence or absence of cracks and streaky patterns at the ends of each test material.
  • the ingot having the specific chemical composition is subjected to the first homogenization treatment and the second homogenization treatment under the specific conditions. Therefore, the deformation resistance of the ingot during hot extrusion can be reduced. Therefore, the test materials S1-S3 have a good appearance.
  • the extrudability of the test material R1 is inferior to the test materials S1 to S3, and streaky patterns are generated on the surface of the test material. Since the total of the Si content and the Mn content of the test material R2 is excessively large, the extrudability is inferior to the test materials S1 to S3, and cracks occur at the ends in the width direction of the test material. , a streaky pattern occurs on the surface of the test material.
  • the extrudability is inferior to the test materials S1 to S3, and streaky patterns are generated on the surface of the test material.
  • the test material R4 was not subjected to the second homogenization treatment in the manufacturing process, it was inferior to the test materials S1 to S3 in extrudability, and streaky patterns were generated on the surface of the test material.

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  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • General Engineering & Computer Science (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Geometry (AREA)
  • Extrusion Of Metal (AREA)
  • Heat-Exchange Devices With Radiators And Conduit Assemblies (AREA)

Abstract

Dans ce procédé de production d'un tuyau à trous multiples extrudé (1), un lingot est produit, qui présente une composition chimique contenant un ou plusieurs éléments parmi Si : 2,0 % en masse ou moins, Fe : 0,6 % en masse ou moins, Cu : 0,6 % en masse ou moins, Mn : 2,0 % en masse ou moins, Mg : 0,4 % en masse ou moins, Cr : 0,1 % en masse ou moins, Zn : 1,5 % en masse ou moins, Ti : 0,1 % en masse ou moins et B : 0,1 % en masse ou moins, le reste comprenant de l'Al et des impuretés inévitables, la teneur totale en Si et Mn étant de 3,2 % en masse ou moins, la teneur en Si étant inférieure à la teneur en Mn. Après un premier traitement d'homogénéisation dans lequel le lingot est maintenu à une température de 550 à 650 °C pendant 2 heures ou plus, un second traitement d'homogénéisation est effectué dans lequel le lingot est maintenu à une température de 450-540 °C pendant 3 heures ou plus. Le lingot est ensuite extrudé à chaud.
PCT/JP2022/038245 2021-10-20 2022-10-13 Procédé de production d'un tuyau à trous multiples extrudé WO2023068166A1 (fr)

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Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH1161312A (ja) * 1997-08-28 1999-03-05 Nippon Steel Corp 押出用アルミニウム合金およびその製造方法
JP2007031730A (ja) * 2005-07-22 2007-02-08 Denso Corp 表面性状に優れたアルミニウム合金押出材とその製造方法、および熱交換器用多孔管ならびに該多孔管を組み込んだ熱交換器の製造方法
JP2009046702A (ja) 2007-08-14 2009-03-05 Mitsubishi Alum Co Ltd 耐食性に優れた熱交換器用押出扁平多穴管
JP2011247459A (ja) * 2010-05-25 2011-12-08 Sumitomo Light Metal Ind Ltd アルミニウム合金製熱交換器の製造方法
JP2013204070A (ja) * 2012-03-27 2013-10-07 Mitsubishi Alum Co Ltd 熱交換器用押出伝熱管とその製造方法

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH1161312A (ja) * 1997-08-28 1999-03-05 Nippon Steel Corp 押出用アルミニウム合金およびその製造方法
JP2007031730A (ja) * 2005-07-22 2007-02-08 Denso Corp 表面性状に優れたアルミニウム合金押出材とその製造方法、および熱交換器用多孔管ならびに該多孔管を組み込んだ熱交換器の製造方法
JP2009046702A (ja) 2007-08-14 2009-03-05 Mitsubishi Alum Co Ltd 耐食性に優れた熱交換器用押出扁平多穴管
JP2011247459A (ja) * 2010-05-25 2011-12-08 Sumitomo Light Metal Ind Ltd アルミニウム合金製熱交換器の製造方法
JP2013204070A (ja) * 2012-03-27 2013-10-07 Mitsubishi Alum Co Ltd 熱交換器用押出伝熱管とその製造方法

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