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WO2000073529A1 - Corps creux en alliage d'aluminium, tuyau en alliage d'aluminium extrude pour canalisations de climatisation, et procede de fabrication de ce corps creux - Google Patents

Corps creux en alliage d'aluminium, tuyau en alliage d'aluminium extrude pour canalisations de climatisation, et procede de fabrication de ce corps creux Download PDF

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Publication number
WO2000073529A1
WO2000073529A1 PCT/JP1999/002843 JP9902843W WO0073529A1 WO 2000073529 A1 WO2000073529 A1 WO 2000073529A1 JP 9902843 W JP9902843 W JP 9902843W WO 0073529 A1 WO0073529 A1 WO 0073529A1
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WO
WIPO (PCT)
Prior art keywords
aluminum alloy
temperature
extruded
porthole
extrusion
Prior art date
Application number
PCT/JP1999/002843
Other languages
English (en)
Japanese (ja)
Inventor
Kazuo Taguchi
Toshio Ohta
Original Assignee
The Furukawa Electric Co., Ltd.
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Priority to JP9354188A priority Critical patent/JPH11172388A/ja
Application filed by The Furukawa Electric Co., Ltd. filed Critical The Furukawa Electric Co., Ltd.
Priority to PCT/JP1999/002843 priority patent/WO2000073529A1/fr
Publication of WO2000073529A1 publication Critical patent/WO2000073529A1/fr
Priority to US09/771,309 priority patent/US6908520B2/en
Priority to US10/772,044 priority patent/US6962632B2/en

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Classifications

    • 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
    • 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
    • B21C23/00—Extruding metal; Impact extrusion
    • B21C23/02—Making uncoated products
    • B21C23/04—Making uncoated products by direct extrusion
    • B21C23/08—Making wire, bars, tubes
    • B21C23/085—Making tubes
    • 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

Definitions

  • the present invention relates to a high corrosion resistant Mn-containing aluminum alloy hollow material useful as a building material and the like, which is manufactured by using a porthole extrusion method, and a method for manufacturing the same.
  • the present invention relates to an aluminum alloy extruded pipe for air conditioner piping suitable for a metal pipe portion such as a refrigerant pipe of an automobile cooler, and a low-cost manufacturing method of the extruded pipe.
  • Aluminum alloy hollow materials such as hollow hollow materials having a square cross section used for building materials and tubes having a circular cross section for refrigerants have been conventionally manufactured by a porthole extrusion method.
  • Port hole extrusion methods include JIS 100 series (pure A 1 series), 3 000 series (A 1-M n series), 600 000 series (A l-M g-Si series), It is used for the production of relatively soft aluminum alloy hollow materials such as 700-based (Al-Zn-Mg-based) that do not contain copper.
  • an extrusion billet is formed from a predetermined aluminum alloy into a gunshot mass by a normal DC manufacturing method (semi-continuous vertical manufacturing method) or a hot-top manufacturing method. Then, the lumps are subjected to a homogenization treatment to reduce segregation, and the lumps are cut into a predetermined length to produce the lumps. Thereafter, the extruded billet is reheated by a low-frequency induction furnace (induction heater) or a gas heating furnace and hot extruded into a hollow material.
  • the reheating temperature is determined in the range of 370 to 530 ° C in consideration of the extrudability and the quality of the extruded material, and is often determined in the temperature range of 400 to 500 ° C.
  • the above-mentioned porthole extruded hollow material may be subjected to drawing processing in order to reduce dimensional accuracy and diameter.
  • drawing processing There are two methods of drawing: a method of pulling out a short extruded hollow material with a drawing bench, and a method of drawing out a long extruded hollow material with a continuous drawing machine using a floating plug.
  • the hollow material after the drawing process is subjected to a solution treatment, an aging treatment, an annealing treatment, etc., depending on the intended use, to thereby impart strength and workability.
  • refrigeration piping for automobile coolers is made of JIS6063 alloy (representative composition A1-0.5 wt% M), which has corrosion resistance to the external environment and strength enough to withstand refrigerant pressure and vibration of engines and compressors.
  • JIS6063 alloy representedative composition A1-0.5 wt% M
  • the JIS 603 alloy is used for piping, particularly so-called flex hose, which is required to withstand vibration fatigue resistance.
  • the JIS 603 alloy is widely used for metal piping such as automobile coolers. Have been.
  • the pipe made of the JIS 003 alloy is a circular pipe having an outer diameter of about 6 to 19 mm and a wall thickness of about 0.8 to 1.2 mm, and is manufactured by, for example, the following process.
  • the JIS 3003 alloy was rounded by a DC semi-continuous vertical manufacturing method. Gun into chunks.
  • the round bar ⁇ is heated at a high temperature and homogenized.
  • the extruded billet is reheated, and the extruded tube is extruded by mandrel extrusion.
  • the extruded pipe is drawn into a pipe having a desired shape by drawing and then annealed to remove processing strain and impart appropriate workability.
  • the conditions are economical factors such as alloy components, ease of extrusion, required characteristics of the product, energy cost required for homogenization treatment, and time. Determined in consideration of factors.
  • the homogenization conditions (holding temperature and holding time) for practical aluminum alloys subjected to hot extrusion are generally as follows.
  • JIS 304 alloy 530 580 ° C
  • 410 hr JJ II SS 66 00 66 33 alloy gold 520580.
  • cooling from the holding temperature to room temperature is performed by air cooling with a fan, cooling down, water sprinkling using a sprinkler, or the like.
  • the pipe manufactured in this manner is further subjected to end processing and bending processing, and is used as an automotive cooler pipe or the like.
  • Various types of beads are formed by a combination of pipe expansion, contraction, and rolling, etc., in the end processing of the piping material.
  • higher reliability is required for beads.
  • a new method called shaft seal bead has been widely adopted. Due to the complicated shape of this shaft seal bead, higher workability is required for the tube material.
  • automotive air conditioner piping must have good brazing properties and maintain high quality even when subjected to brazing heat.
  • corrosion resistance and formability are required for the outer surface of automotive piping.
  • formability dimensional accuracy of fine crystal grains, outer diameter, wall thickness, etc., and brazing properties, etc. are required so that roughening does not occur during processing.
  • the port hole extrusion method is an extrusion method in which an extruded material is divided into a plurality of port holes and these are welded and integrated at an outlet of the port hole. A weld is formed.
  • the aluminum alloy is once divided into four parts, which are welded together in the welding chamber of the extrusion die, and pass through the clearance between the die bearing part and the mandrel. Pressing the desired shape There are a plurality of welds that are continuous in the longitudinal direction to become a material, which remains after drawing.
  • the preferential corrosion of tubing obtained by the porthole extrusion method with four portholes is not only caused by pitting corrosion on the non-welded part, but also by the longitudinal Directionally continuous corrosion occurs preferentially.
  • This preferential corrosion of the welded portion has a very high corrosion rate, and a through hole is formed in a short period of time.
  • the pitting corrosion at the non-welded part does not penetrate after elapse of 400 hr, whereas the pitting corrosion at the welded part is less than 20 Ohr. Penetrate.
  • This preferential corrosion of the welded portion is likely to occur in the A1-Mn alloy, and occurs when the Mn content is 0.3 wt% or more, and rapidly progresses when the Mn content exceeds 0.8 wt%. Since Mn increases deformation resistance and lowers extrudability, the upper limit of the Mn content in porthole extrusion is about 1.5 wt%.
  • A1—Mn-based alloys have excellent strength and corrosion resistance, so JIS 300 (Mn content 1.0 to 1.5 wt%), JIS 3203 (Mn content 1.0 to 1.5 wt%) Alloys such as JIS 7 N 01 (Mn content 0.2 to 0.7 wt) are widely used.
  • JIS 300 Mn content 1.0 to 1.5 wt%)
  • JIS 3203 Mn content 1.0 to 1.5 wt%)
  • Alloys such as JIS 7 N 01 (Mn content 0.2 to 0.7 wt) are widely used.
  • porthole extruded hollow materials have the problem of preferential corrosion described above, so their use has often been refrained from applications where corrosion resistance is important.
  • various defects such as poor hue and gloss appearance occur between the welded portion and the non-welded portion.
  • Fig. 1 is an explanatory diagram of preferential corrosion of the welded part of a pipe manufactured by the porthole extrusion method.
  • FIGS. 2 (A), 2 (B), 2 (C) and 2 (D) are illustrations of end processing types A, B, C and D of extruded tubing for air conditioner piping.
  • FIG. 3 (A) shows the type B shown in FIG. 2 (B)
  • FIG. 3 (B) shows the type B shown in FIG.
  • FIG. 4 (c) is an explanatory view of a process of processing each end of type C shown in FIG.
  • Fig. 4 (A) is an SEM photograph of a current pipe
  • Fig. 4 (B) is an SEM photograph of a type B end portion of each of the pipes of the present invention. Disclosure of the invention
  • the present inventors have investigated the preferential corrosion in detail.
  • the present invention provides the following means.
  • An aluminum alloy hollow material manufactured by porthole extruding an aluminum alloy lump containing at least 0.3 to 1.5 wt% of Mn or by porthole extrusion and drawing.
  • the homogenization treatment is carried out at a predetermined temperature of 500 to 60 ° C for 0 to 24 hours, and then at a cooling rate of 100 ° C / hr or less. Cool to a specified temperature of 0-500 ° C, hold at this temperature for 4 to 48 hr and apply
  • the method for producing a hollow aluminum alloy material according to the above (1) characterized in that:
  • a homogenizing treatment is performed on an aluminum alloy ingot containing at least 0.3 to 1.5 wt% of Mn, and then the ingot is subjected to porthole extrusion or porthole extrusion and drawing.
  • the homogenization treatment of the lump is maintained at a predetermined temperature (T i) of 500 to 60 ° C. for 0 to 16 hours, and then the temperature is reduced from the T i temperature by 10 to 10 hours.
  • the homogenization treatment of the mass is maintained at a predetermined temperature of 400 to 500 ° C. for 0.5 to 4 hours, and then the temperature is maintained at 550 to 63 ° C. After the temperature is raised to the specified temperature and maintained at that temperature for 0.5 to 4 hours, it is cooled to 350 ° C at a cooling rate of 100 ° C / hr or less, and any cooling from 350 ° C
  • Aluminum alloy lump containing one or more of wt%, Zr 0.0-0.3 wt%, Ni 0.0-0.3 wt%, and the balance Al and unavoidable impurities Is an aluminum alloy extruded tube for air conditioner piping manufactured by a porthole type continuous hot extrusion method, wherein the extruded tube has a conductivity of 39.0 IACS% or more (preferably 39.5 IACS). %), And a difference in electrical conductivity in each part in the longitudinal direction of the extruded tubing is 1.0 IACS% or less.
  • a method for producing an aluminum alloy extruded tube for air-con piping in which the aluminum alloy lump described in the above (7) is subjected to homogenization treatment and extruded into a tube by a porthole continuous hot extrusion method.
  • the homogenization treatment of the mass is maintained at a predetermined temperature (T) of 500 to 60 ° C. for 0 to 48 hours, and then cooled from 1 temperature to 100 ° C./hr or less. 3 was cooled to 5 0 ° C (T 2) at a rate, the time up to the arrival after T 2 temperature T i temperature was 1. 2 to 4 8 hr, to room T 2 temperature at any cooling rate
  • T predetermined temperature
  • a method for producing an aluminum alloy extruded tube for air conditioning piping wherein the aluminum alloy lump described in the above (7) is subjected to a homogenization treatment and extruded into a tube by a porthole continuous hot extrusion method.
  • the homogenization treatment of the lump is performed at a predetermined temperature of 400 to 500 ° C. for 12 to 48 hr, and then cooled to room temperature. Manufacturing method of extruded aluminum alloy tube.
  • the aluminum alloy ingot described in (7) above is subjected to homogenization treatment and extruded into a pipe by a porthole continuous hot extrusion method.
  • a method of manufacturing wherein the homogenization treatment of the mass is maintained at a predetermined temperature of 400 to 500 ° C. for 0.5 to 4 hours, and then is performed at a predetermined temperature of 550 to 63 ° C. After the temperature is raised to the temperature and maintained at that temperature for 0.5 to 4 hours, it is cooled to 350 at a cooling rate of 100 ° (/) 1> or less, and any cooling rate from 350 ° C
  • a method for producing an aluminum alloy extruded tube for air-con pipes wherein the tube is cooled to room temperature. (Hereinafter, the extruded tube material described in the above item (6) and the production method described in the above items (7) to (10) are collectively referred to as a second invention of the present invention.)
  • the present invention means the first and second inventions.
  • the aluminum alloy ingot containing a predetermined amount of Mn is subjected to a specific homogenization treatment, whereby the aluminum alloy ingot is formed by port hole extrusion.
  • the hollow member according to the above (1) which does not cause preferential corrosion of the welded portion, can be manufactured.
  • This hollow material is suitable as a building material or the like.
  • alloy components other than Mn are also specified in place of the aluminum alloy lumps used in the method described in the above (2) to (5).
  • the above-mentioned (6) which does not cause preferential corrosion in the welded portion by subjecting the aluminum alloy ingot to homogenization treatment similar to the method described in the above (2) to (5).
  • the extruded tubing described can be manufactured. This pipe is suitable for air conditioner piping.
  • Mn is an element that contributes to strength improvement without deteriorating corrosion resistance.
  • the content if the content is less than 0.3 wt%, the effect cannot be sufficiently obtained, and if the content exceeds 1.5 wt%, the effect is saturated, and the deformation resistance during hot working increases. As a result, port hole extrudability decreases. Therefore, its content should be 0.3-1.5 wt% (preferably 0.5-: L.3 w t%).
  • the content of Mn is less than 0.8 wt%, the effect is small, and if it exceeds 1.5 wt%, the effect is saturated, and the deformation resistance during hot working increases. As a result, port hole extrudability decreases. Therefore, its content is set to 0.8 to 1.5 wt% (preferably 0.9 to 1.2 wt%).
  • each of the alloy components including Mn is determined in consideration of the strength, corrosion resistance, workability, and the like required for the material for automotive air conditioner piping, and that porthole extrusion is easy. .
  • Fe and Si are forces s contained in general aluminum alloys in a small amount, and these elements reduce the amount of solid solution of Mn and simultaneously form A 1 and an intermetallic compound during fabrication, This has the effect of refining the recrystallized structure, and it is desirable that Fe and Si be appropriately contained.
  • the contents of Fe and Si are respectively 0.1 to 0.7 wt% (preferably 0.2 to 0.6 wt%) and 0.3 to 0.6 wt% (preferably 0.3 to 0.3 wt%)
  • Cu contributes to improvement in strength.
  • Cu dissolved in the substrate enhances the spontaneous potential and slightly improves the corrosion resistance.
  • the content of Cu is set to 0.0 to 0.45 t% (preferably 0.0 to 0.25 wt%).
  • Mg contributes to solid solution and contributes to strength improvement, it significantly reduces hot deformation resistance. If the Mg content exceeds 0.3 wt% in addition to the Mn content, the porthole extrudability decreases. Therefore, the content of Mg should be 0.0 to 0.3 wt% (preferably 0.0 to 0.3 wt%).
  • Cr is a force that is effective in refining the crystal structure. If its content exceeds 0.3 wt%, a coarse A1-Cr compound is formed and the formability is impaired. Therefore, the Cr content is 0.0. To 0.3 wt% (preferably 0.0 to 0.05 wt%).
  • Ti refines the crystal structure with a small amount of Ti. If its content exceeds 0.1 wt%, extrudability will be reduced and a giant intermetallic compound harmful to moldability will be produced. Therefore, the content of Ti is set to 0.0 to 0.1 wt% (preferably 0.0 to 0.05 wt%).
  • the content of Zn is set to 0.0 to 0.5 wt% (preferably 0 to 0. lwt%).
  • Zr is effective in refining the crystal structure, but a large amount of it decreases extrudability and formability. Therefore, the content of Zr is set to 0.0 to 0.3 wt% (preferably 0.0 to 0.05 wt%).
  • Ni has a slight strength-improving effect, but the addition of a large amount reduces extrudability and formability. Therefore, the content of Ni is set to 0.0 to 0.3 wt% (preferably 0.0 to 0.05 wt%).
  • the content of the alloy component is 0 wt% means that the alloy component is not contained at all.
  • the aluminum alloy used for the extruded tube material of the second invention contains Cu, Mg, Cr, ⁇ i, ⁇ , in addition to containing the aforementioned predetermined amounts of Mn, Fe, and Si. Selected from the group consisting of ⁇ r and ⁇ i One or two or more, and the balance consists of A1 and unavoidable impurities.
  • the aluminum alloy composed of the above components can be sufficiently extruded into an air-conditioner piping material having a predetermined shape by a port hole extrusion method.
  • the aluminum alloy has a uniform fine recrystallized structure, strength and ductility similar to those obtained by annealing a drawn tube in the extrusion process (immediately after leaving the die).
  • the electrical conductivity of the extruded tubing is defined as the electrical conductivity of each part along the entire length in the longitudinal direction of the extruded tubing, and the electrical conductivity difference in the longitudinal direction of each extruded tubing (the maximum value of the electrical conductivity) in the second invention
  • the difference between the minimum value and the minimum value is specified in order to avoid preferential corrosion of the weld.
  • the present inventors have obtained the following knowledge about the cause of preferential corrosion at a welded portion.
  • Mn In the DC or hot-top construction, most of Mn is in solid solution in the aluminum solid phase because it is immediately cooled with water and solidified immediately after solidification. ⁇ In the homogenization treatment applied to the lump, Mn does not precipitate much because it is maintained at a high temperature close to the solidus temperature for the purpose of eliminating micro-segregation, separating crystallized matter, spheroidizing, etc. . Also, in the cooling step after holding at a high temperature, Mn hardly precipitates here because the cooling rate is relatively high. Here, regardless of the presence or absence of homogenization, the lump is subjected to the next reheating and extrusion process.
  • Mn-containing compound Al—Mn-based compounds, Al— (Fe, Mn) -based compounds, A1- (Fe, Mn) -Si-based compounds, etc. are known. Put out.
  • the extrusion temperature is about 400 to 500 ° C. This temperature range is the temperature at which the supersaturated solid solution of Mn tends to precipitate. And during extrusion The study by the present inventors has revealed that the precipitation rate of the steel is remarkably large because the precipitation is promoted by the processing.
  • the extrusion time of a billet having a length of about several tens of cm is several minutes at most, and precipitation progresses remarkably in these few minutes.
  • the amount of precipitation is larger than that of the front end of the extrusion. If the same heating is performed for several minutes without processing, the Mn-containing compound hardly precipitates.
  • the precipitation of the Mn-containing compound proceeds more at the rear end side of the extruded tubing material.
  • the welding mechanism is formed by the following mechanism. Difference between the non-welded portion and the non-welded portion.
  • the first billet remaining in the space created by the die hole and the welding chamber (chamber) is formed.
  • the precipitation of Mn progressed most at the end of extrusion, and the Mn solid solution A second billet with a high degree is placed adjacent by extrusion.
  • the welded portion is formed of the aluminum alloy at the rear end of the preceding billet, and the non-welded portion is formed of the aluminum alloy of the succeeding billet. You. This configuration continues until the end of extrusion of the subsequent billet while the width of the welded portion is narrowed.
  • the deposition proceeds in the non-welded portion in the latter half of extrusion, and the difference in the deposition state between the welded portion and the non-welded portion becomes smaller. This configuration is the same even if the number of extrusions increases.
  • the welded part where the precipitation of the Mn-containing compound has progressed has a lower potential, and the welded part is sandwiched between non-welded parts with a noble potential.
  • the welded part is preferentially corroded in a corrosive environment, causing corrosion problems.
  • the present inventors have made it effective to reduce the difference in solid solution amount of Mn between the front end side and the rear end side of the extruded billet before extrusion.
  • the present invention has been completed.
  • the present inventors have found that it is effective to precipitate a Mn-containing compound during the homogenization treatment in order to reduce the difference in the amount of solid solution of Mn. That is, in the lump in which the precipitation of the Mn-containing compound has already progressed, excessive precipitation does not progress in the extrusion process. And adjust the homogenization conditions If the Mn-containing compound is precipitated appropriately, there is no large difference in conductivity between the front and rear ends of the extruded tubing, and between other parts, and corrosion of the welded portion is not caused. Dramatically suppressed.
  • the electrical conductivity of each part of the extruded material is 39.0 IACS% or more, preferably 39.5 IACS% or more. .
  • preferential corrosion of the weld cannot be sufficiently suppressed unless all the longitudinal parts of the extruded material achieve 39.0 IACS% or more.
  • the precipitation state of the Mn-containing compound in the extruded tubing material is exactly the same from the extruded tip to the extruded end.
  • the difference in conductivity is 1.0 IACS% or less, preferably 0.6 IACS% or less, higher reliability for corrosion resistance is obtained. Property is obtained.
  • the difference in the electrical conductivity of each part of the hollow material or the extruded tubular material is a difference between the maximum value and the minimum value of the electrical conductivity of all samples obtained by cutting the hollow material or the tubular material in the longitudinal direction.
  • a relatively high predetermined temperature of 500 to 63 ° C. is maintained for 0 to 24 hours, and then 100 ° C./hr Cool at the following cooling rate.
  • Temperature rise process in this heat treatment The Mn-containing compound that precipitates during the holding process grows relatively coarsely during the cooling process.
  • the cooling rate is set to be higher than 100 ° C./hr, a large amount of new precipitates are deposited. However, the precipitates are so fine that they are easily dissolved again as described above. Also, higher cooling rates are difficult in furnace cooling and are not practical from an industrial point of view.
  • a cooling rate of 50 ° C / hr or less is particularly preferred.
  • the temperature is maintained in the temperature range of 400 to 500 ° C.
  • the Mn-containing compound is most easily precipitated in the A 1 -Mn-based alloy, and the amount of precipitation is further increased during this holding process.
  • the holding time at the above temperature is required to be 4 hours or more for the purpose of increasing the amount of precipitation, and if it exceeds 48 hours, the precipitation effect is saturated and uneconomical, so the upper limit is 48 hours.
  • the method described in the above (2) or (7) is a method in which an appropriate precipitation state is revealed by gradually cooling after maintaining at a high temperature, and thereafter, the precipitation amount is further increased by maintaining the temperature in the range where precipitation is most easily performed.
  • the method described in the above (3) is a method in which an appropriate precipitation state is revealed by gradually cooling after maintaining at a high temperature, and thereafter, the precipitation amount is further increased by maintaining the temperature in the range where precipitation is most easily performed.
  • (8) is a method in which precipitation proceeds only in a slow cooling process from a high temperature.
  • the reason for setting the cooling rate to 100 ° C./hr or less by this method is the same as the reason in the above (2) and (7).
  • ⁇ reason for defining the T 2 at slow cooling process from (5 0 0 ⁇ 6 3 0 ° C) to T 2 to 3 5 0 ° C is 3 5 0 °
  • Do precipitated M n containing compound mostly less than C This is because there is no point in specifying the cooling rate.
  • to influence the deposition amount and deposition state mainly from 5 0 0 ⁇ 6 3 ⁇ ° C when us ( ⁇ ) down to 3 5 0 ° C (T 2 ) This is a process.
  • the time from reaching the T i temperature to reaching the T 2 temperature is defined as 12 to 48 hr.
  • the retention time is defined as 12 to 48 hr.
  • the holding time is set to a short time of 0.5 to 4 hr. Holding at a predetermined temperature of 550 to 63 ° C, if held for a long time, will cause the fine precipitates, which are nuclei, to disappear, so the holding time is also specified as a short time of 0.5 to 4 hr. I do.
  • the cooling rate after maintaining at a predetermined temperature of 550 to 63 ° C shall be 100 ° C / hr or less, which is effective for expanding the size of existing precipitates.
  • the reason for limiting the cooling rate to cooling to 350 ° C is that precipitation hardly occurs below 350 ° C.
  • an aluminum alloy hollow material in which there is no difference in the structure (such as the amount of precipitated Mn) between a welded portion and a non-welded portion in porthole extrusion and preferential corrosion of the welded portion is prevented.
  • the hollow material can be easily manufactured by subjecting a lump to a predetermined homogenization treatment to precipitate Mn in a coarse compound.
  • an aluminum alloy porthole extruded pipe material for air conditioner piping in which preferential corrosion of a welded portion is improved, and the extruded pipe material is subjected to a predetermined homogenization treatment for a lump to reduce the alloy element. It can be easily manufactured by precipitating the compound containing Mn coarsely.
  • Alloy Nos. 1 to 8 having the compositions shown in Table 1 were formed into a 6-inch outer diameter extruded round bar by the DC forming method, of which alloys Nos. After heating at ° C for 4 hr, the furnace was cooled to 350 ° C at a cooling rate of 30 C / hr, then taken out of the furnace and sprinkled with a sprinkler. The alloy ingots of Nos. 6 and 7 were heated at 585 ° C for 4 hours, cooled to 350 ° C at a cooling rate of 30 ° C / hr, then taken out of the furnace and sprinkled with a sprinkler.
  • Alloy Nos. 1 to 8 having the compositions shown in Table 1 were formed into a 6-inch outer diameter round rod for extrusion by DC fabrication, and the resulting alloy was obtained at 530 ° C. Heating was performed for 6 hours, and then the furnace was cooled to 350 ° C at a cooling rate of 30 ° C / hr, then taken out of the furnace, and cooled with a sprinkler.
  • Alloy Nos. 1 to 8 having the compositions shown in Table 1 were made into a 6-inch outer diameter extruded round bar by using the DC method, and alloy Nos. 1 to 5 and 8 were After heating at 600 ° C for 16 hours, it was quickly transferred out of the furnace, sprinkled with a sprinkler, and cooled at a rate exceeding 100 ° C / hr.
  • the alloy ingots of Nos. 6 and 7 were heated at 585 ° C for 8 hours, quickly transferred out of the furnace, sprinkled with a sprinkler, and cooled at a rate exceeding 100 ° C / hr.
  • the lump produced in the steps of Examples 1 and 2 and Comparative Example 1 was cut into a predetermined length to obtain an extruded billet, which was obtained by a porthole extrusion method with a side of 12.0111111 and a wall thickness of 1.4. It was extruded into a hollow rectangular section with a square cross section of 0 mm. The number of extruded hollow sections was one, the port holes were two, and the welds were at the centers of the opposite sides.
  • the extruded billet was reheated to 44 ° C using an induction heater, and the extruded material was forcibly air-cooled with a fan. Three extruded billets were prepared for each alloy and extruded continuously.
  • a hollow section corresponding to the third extrusion billet was provided.
  • the section up to 5 m from the head of this hollow section was excluded because many subsequent billets were mixed in, and the remaining sections were excluded.
  • Sampled from the part. The conductivity of each sample was measured by the four-terminal method, and the conductivity difference ⁇ E C between the front end side and the rear end side of the hollow profile was obtained.
  • Table 2 shows the results of the evaluation of the tip part where the degree of corrosion is severe in the CASS test.
  • Alloy No. 2 having the composition shown in Table 1 was formed into a 6-inch outer diameter extruded round bar by DC fabrication, and the alloy was heated at 610 ° C for 8 hours. The furnace was cooled to 350 ° C at a cooling rate of 25 ° C / hr, then transferred outside the furnace and sprinkled with a sprinkler.
  • Alloy No. 2 having the composition shown in Table 1 was formed into a 6-inch outer diameter extruded round bar by DC fabrication, and this alloy was heated at 450 ° C for 36 hr. Then, it was transferred outside the furnace and allowed to cool.
  • Alloy No. 2 having the composition shown in Table 1 was prepared by a DC The extruded round bar was made into a lump, heated at 580 ° C for 6 hours, cooled in a furnace at a cooling rate of 40 ° C / hr to 420 ° C, and cooled to 420 ° C. After heating at ° C for 18 hr, it was transferred outside the furnace and allowed to cool.
  • No. 2 alloy was formed into a 6-inch outer diameter round bar for extrusion by DC forming, and the obtained block was homogenized at 6100 ° C for 16 hours.
  • Each lump obtained in Examples 3 to 5 and Comparative Example 2 was cut into a predetermined length to obtain an extruded billet, which was heated to 450 ° C. by an induction heater. Hot-extruded into a tube with an outer diameter of 18.6 mm and a wall thickness of 2.3 mm (hereinafter referred to as 18.6 ⁇ 0 ⁇ 2.3 ⁇ ), and the extruded product was fan-shaped. More air cooled.
  • Extrusion was performed using a 4-port die with two extruded products and welds formed at four locations in the circumferential direction. Five extrusion billets were prepared for each alloy, and these were continuously extruded.
  • the third extruded billet part is extruded tubing, and the fourth and fifth extruded billets are each subjected to one-pass and two-pass drawing after extrusion, followed by one-pass drawn tubing and two-pass.
  • the drawn tube material was collected and subjected to various evaluations.
  • the one-pass drawn tube material 1 8. 6 mm ⁇ zi X 2. 3 a Paiiotaiotaita iota extruded tube material 1 6. O mm x 2. Drawing process to O mm (processing rate 2 5.3%), and the The two-pass drawing tubing was produced by further drawing the above-mentioned one-pass drawing tubing to 13.8 mm ⁇ 1.75 mmt (processing rate 25.0%). The total drawing rate of 2-pass drawn tubing is 44.0%. Said A draw bench was used for the drawing process.
  • extruded tubing and the extraction tubing obtained in this way were the same as in Examples 1 and 2, except for 5 m from the front end, and the remaining front end, rear end, and the middle part Samples were taken from locations.
  • the corrosion resistance of the sample at the front end, middle, and rear end was examined by a 200 hr CASS test. The appearance after the test was visually observed and evaluated according to the same criteria as in Example 1.
  • the lower row shows the CASS test results for the front end / middle / rear end.
  • the examples of the present invention (Examples 3, 4.5) had an EC of less than 1.0 IACS% for both the extruded tube and both drawn tubes, and the CASS test results were all ranked A. No preferential corrosion of the weld was observed. There was no particular difference between the one-pass drawn material and the two-pass drawn material.
  • Comparative Example (2) which was homogenized by the conventional method, ⁇ EC exceeded 1.0 IACS% for both the extruded tubing and both drawn tubing. In the middle part, severe preferential corrosion was observed at the weld.
  • Alloy A having the composition shown in Table 4 was formed into a 6-inch outer diameter round bar for extrusion by DC forming, and the obtained block was subjected to the homogenization treatment shown in Table 5 and homogenized. The electrical conductivity of the lumps after the chemical treatment was measured. Table 5 shows the results.
  • the temperature was maintained at 600 ° C. for 8 hours, and then cooled in a furnace at a cooling rate of 50 ° C./hr to 450 ° C., followed by 450 ° C.
  • Wood invention example (600-450: Cooling rate 50 ° C / hr) 39.3S1ACS 5
  • the lump treated in the present invention has higher conductivity than the lump treated in Comparative Examples 3 and 4, and the precipitation of the Mn-containing compound is progressing. Compared with the conductivity (36.5 IACS%) before the homogenization treatment, in Comparative Examples 3 and 4, precipitation hardly progressed from the solid state.
  • the lump cut into a predetermined length was homogenized under each condition, and then hot-extruded continuously into 5 mm each of 8 mm 0 x 1.0 mm tube using a 4-port hole die. . There were four welds in the extruded tube in the circumferential direction and continuous in the longitudinal direction.
  • the billet was heated to 420-460 ° C using an induction heater.
  • the extrusion speed of the tubing was 60 m / min.
  • the tube immediately after extrusion was water-cooled, the adhering water droplets were removed by blowing, and the tube was wound up with an in-line coiler.
  • the coiled extruded material was cut to a fixed length of about 6 m, stretched (remanufactured), and the required parts were sampled.
  • sampling was performed at seven locations every 30 m from the tip end to the rear end of the extrusion, and the conductivity, mechanical performance, and corrosion resistance were investigated. did.
  • the conductivity was measured by a four-terminal method.
  • the non-welded portion (the portion other than the welded portion) exhibited pitting corrosion that did not lead to penetration. No particular difference was observed between the example and the comparative example. This pitting condition was at a level comparable to that of the current tubing (3003 alloy manufactured through the extrusion, drawing and annealing processes) that was separately tested. The preferential corrosion of the weld was evaluated by classifying the degree into five levels.
  • the materials marked with ⁇ or X often have through holes in the preferentially corroded part of the welded part. From this point, when the pipe material of the comparative example is applied to automobile air-con pipes, it is not desirable because corrosion may cause early leakage due to corrosion. On the other hand, the tube material of the present invention example can be sufficiently used except for a very small part on the side of the extrusion tip.
  • the bending workability was tested using an NC bending machine at two levels of bending angles of 45 degrees and 90 degrees and a bending radius of 25 mm.
  • Samples of the extruded tubing of the present invention and comparative examples 3 and 4 were 30 cm in length from the seven places at three equal intervals in the longitudinal direction. A sample was taken. Table 8 shows the results.
  • the conventional 0.3-alloy annealed tubing of Eve and the tubing of the present invention have the same characteristics, but the elongation value of the tubing of the present invention exceeds 30% and the crystal structure further increases. Is uniform and fine.
  • Table 9 shows the samples of the extruded tubing material of the present invention, each of which had a length of 2 cm and a length of 20 cm, respectively. The result of performing a processing test is shown. The terminal addition was indicated by the presence or absence of abnormalities in the sample after the test.
  • the dimensions of the extruded tubing are as follows: the maximum outer diameter is 8.05 mm, the minimum is 7.92 mm, the maximum wall thickness is 1.04 mm, and the minimum is 0.97 mm. It is almost the same as.
  • the extruded tube material of the present invention can be sufficiently used as an air conditioner pipe for an automobile.
  • the processing end (1) of the current pipe has a longitudinal line due to minute streaks (groove-like defects) formed on the surface of the pipe during drawing. A significant number of streaks were inevitably present.
  • the processing end portion (1) of the tube material of the present invention exhibited an extremely smooth surface state without such fine streaks.
  • the end portion (3) of the pipe material of the present invention is not It had a beautiful and beautiful processed surface.
  • the extruded tubing material of the present invention has the strength performance, corrosion resistance, bending / end workability, extrudability, etc. to be provided as automotive air-con piping, and is a material suitable for automotive air-conditioning piping. It is.
  • the pipe material of the present invention does not require drawing and annealing, simplifies the process and reduces manufacturing costs, and has good surface quality, and is suitable for automotive air conditioner piping materials.
  • Alloy B having the composition shown in Table 4 was formed into a 6-inch OD extruded round bar by DC sintering, kept at 600 ° C for 4 hours, and then cooled at 50 ° C / The mixture was cooled in a furnace at 450 ° C. for hr, kept at 450 ° C. for 24 hr, and air-cooled to room temperature after keeping at 450 ° C. for homogenization. ⁇ After cutting the lump to a predetermined length, heat it by induction heating to 44 to 460 ° C, and use a 4-port or 3-port port hole die, each with 8 mm ⁇ X 1 mm ' thin tubing or 1 2. 7 mm ⁇ 1. 2 ⁇ ⁇ the ⁇ the large diameter tube material which it by five extrusion rate of tube material was continuously extruded in 4 0 m / min.
  • the extruded material was fan-cooled immediately after extrusion, cut and stretched as it was straight. Conducted on the obtained round bar and lump and extruded tube material.Similar to row 6. ⁇ The conductivity of the lump, the difference in conductivity between the extruded tube material and the rear end of the extruded part, tensile properties, corrosion resistance, Various properties of the preferential corrosion property and workability of the welded part were examined. As a result, a result similar to that of Example 6 was obtained.
  • Alloys having the compositions shown in Table 4 (:, D were made into a 9-inch outer diameter extruded round bar by the DC manufacturing method, and alloys E and F were manufactured by the DC manufacturing method.
  • Extrusion rods with a diameter of 6 inches were extruded into a lump and kept at 600 ° C for 4 hours, then cooled in a furnace at a cooling rate of 50 ° C / hr to 450 ° C, and then cooled. The temperature was maintained at 450 ° C for 10 hours, and after the temperature was maintained at 450 ° C, air-cooling was performed to room temperature to perform a homogenization process.
  • each piece was cut into a predetermined length to form an extruded billet, and each piece was extruded continuously by a porthole extruder five by five.
  • the 9 inch pellets were extruded into 16 mm ⁇ xl. 2 mm 'thick tubing or 8 mm x 1 mm' thin tubing. In this extrusion, four products were simultaneously extruded at three welded parts.
  • the 6-inch billet was extruded into a large-diameter tube of 12.7 mm x 1.2 mm 'or a small-diameter tube of 8 mm 0 x lmm' different in size from the 9-inch bottle.
  • This extrusion is a two-piece extrusion and has three welds.
  • the billet was heated during extrusion using a gas burner type reheating furnace for 9-inch materials and induction heating for 6-inch materials.
  • the billet heating temperature was set at 44 to 48 ° C.
  • the extrusion speed was 25 m / min for a tube material of 8 mm outside S in the case of 9 inches, and 40 m / min for the others.
  • the material immediately after extrusion was cooled with a fan, cut straight, without coiling, and stretched.
  • tubing of the present invention has sufficient corrosion resistance against preferential corrosion of the welded portion, which is the most problematic when applying the porthole extruded tubing to automotive air conditioner piping.
  • Alloy G having the composition shown in Table 4 was formed into a 6-inch outer diameter round bar for extrusion by the DC casting method, and the electrical conductivity of the gunshot after the homogenization treatment was measured. The results are shown in Table 10.
  • the furnace was cooled to 450 ° C. to 420 ° C. to a temperature at which the most Mn-containing compound was precipitated. Then, the mixture was kept at the same temperature, and then air-cooled to room temperature.
  • Example 5 to 9 of the present invention after maintaining at a relatively high temperature, the furnace was cooled to 350 ° C at a cooling rate of 30 ° C / hr, and furnace cooling or air cooling was performed at 350 ° C or less.
  • Example 10 of the present invention at the initial stage, the temperature was maintained at 450 ° C. where precipitation is likely to proceed for 2 hours to precipitate fine precipitates, and then the temperature was raised to 600 ° C. It was carried out with the intention of increasing the diameter of the precipitate by holding the temperature and holding for a short time and then cooling the furnace at 30 ° C / hr.
  • Example 11 of the present invention the progress of the precipitation was aimed at by maintaining the temperature at around 450 ° C. where the precipitation is most easily performed for a relatively long time.
  • Comparative Examples 5 and 6 were held at a high temperature under the same or similar conditions as the homogenization treatment often used for A1_Mn-based alloys, and 560 in Comparative Example 7. After holding at 3 ° C for 3 hours, both were cooled by water cooling or air cooling at a high cooling rate (> 100 ° C / hr).
  • IACSX Item Rate of homogenization condition after homogenization process
  • Ratio 5 Water-cooling: ⁇ Take the lump out of the furnace and water by the stiffener) 36.8 ⁇ 60 O X 12hr air cooling
  • Table 11 shows the measurement results of the front end (No. 1), which has the lowest conductivity, and the rear end (No. 6), which has the highest conductivity, and the difference ( ⁇ ⁇ ⁇ ) between the two.
  • No. 1 which has the lowest conductivity
  • No. 6 which has the highest conductivity
  • Ratio 5 38. 6 40. 2 1.6 Comparison 600t: x I2hr air cooling
  • the conductivity was included in the conductivity of about 41 to 43 IACS%, and the conductivity difference AEC at the front and rear ends was 1 IACS% or less in all cases. This is because precipitation was already progressing in the homogenization stage, and precipitation in the extrusion stage was suppressed.
  • Table 12 shows the results of a corrosion resistance test after a CASS test (test time: 200 hr).
  • the corrosion state of the welded portion was ⁇ (no corrosion at the welded portion) or ⁇ (slightly pitted pits), indicating extremely excellent corrosion resistance.
  • ⁇ the welded part has a tendency to corrode, but the corrosion progresses slower than the non-welded part, and there is no practical problem.
  • each of the pipes of Example 1 of the present invention 1 and the pipe of Comparative Example 3 had a tensile strength of 99-: L 08 N / mm 2 , 0.2% yield strength 38--4 In the range of 5 mm / ⁇ and elongation of 38 to 43%, the same tensile properties as the current material were shown.
  • Alloys H to P having the compositions shown in Table 4 were formed into a 6-inch outer diameter extruded round bar by DC forming, and the obtained block was homogenized in the same manner as in Example 8. (600 ° C x 4 hr + 450 ° C x 0 hr air cooling: 600 ° C ⁇ 450 ° C cooling rate 50 ° (: // ] 1]?) Then, the lump is cut into extruded billets, and a 12.7 mm ⁇ 1.2 mm t tube (three welded portions) is formed by a porthole extrusion method of two co-extrusions. Extruded. The extruder was heated to a heating temperature of 450 to 480 ° C by induction heating. The extrusion speed was set at 50 m / min as the target speed, or it was impossible to extrude at that speed depending on the material. Table 13
  • alloys H to M could be extruded at a predetermined extrusion speed, but alloys N and P had extremely low extrusion speeds of about 5 m / min. At the stage, it was not extrudable, and alloy 0 was not extrudable at all. This is M n or Cu for alloys N and P respectively. Is excessively added, and hot deformation resistance is high. In alloy 0, Mg, which increases deformation resistance most, is added excessively.
  • the porthole extruded tubing after subjecting the alloys H to K and M of the present invention to the homogenization treatment of the present invention has the characteristics and workability required for automotive air conditioner piping, and is suitable for automotive air conditioning piping. It is fully applicable.
  • the alloys L, N, 0, and P of the comparative examples are not practical because porthole extrusion is impossible or only low-speed extrusion is possible. Industrial applicability
  • the hollow material of the present invention has no difference in the structure (such as the amount of precipitated Mn) between the welded portion and the non-welded portion in porthole extrusion, preferential corrosion of the welded portion is prevented, and is used as a building material. It is suitable.
  • Hollow of the present invention The method for producing the material is suitable as a method for easily producing the hollow material by subjecting the ingot to a predetermined homogenization treatment to precipitate Mn in a coarse compound. Things.
  • the extruded tubing of the present invention is suitable as an aluminum alloy porthole extruded tubing for air conditioning piping in which preferential corrosion of a welded portion is improved.
  • the extruded tube material is easily produced by subjecting a lump to a predetermined homogenization treatment to coarsely precipitate a compound containing the alloy element Mn. This is a suitable method for performing the above.

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Abstract

L'invention concerne un corps creux en alliage d'aluminium, fabriqué par extrusion d'un orifice, ou par extrusion d'un orifice et extraction-étirage d'un lingot en alliage d'aluminium qui contient au moins 0,3 à 1,5 % en poids de Mn. On obtient ainsi une différence de conductivité électrique entre différentes sections dans le sens de la longueur du corps creux inférieure à 1,0 % IACS, la corrosion préférentielle sur des parties déposées pendant le processus d'extrusion d'un orifice étant par ailleurs prévenue. Cette invention concerne également le procédé de fabrication dudit corps creux.
PCT/JP1999/002843 1997-12-08 1999-05-28 Corps creux en alliage d'aluminium, tuyau en alliage d'aluminium extrude pour canalisations de climatisation, et procede de fabrication de ce corps creux WO2000073529A1 (fr)

Priority Applications (4)

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JP9354188A JPH11172388A (ja) 1997-12-08 1997-12-08 エアコン配管用アルミニウム合金押出管材およびその製造方法
PCT/JP1999/002843 WO2000073529A1 (fr) 1997-12-08 1999-05-28 Corps creux en alliage d'aluminium, tuyau en alliage d'aluminium extrude pour canalisations de climatisation, et procede de fabrication de ce corps creux
US09/771,309 US6908520B2 (en) 1999-05-28 2001-01-26 Aluminum alloy hollow material, aluminum alloy extruded pipe material for air conditioner piping and process for producing the same
US10/772,044 US6962632B2 (en) 1999-05-28 2004-02-04 Aluminum alloy hollow material, aluminum alloy extruded pipe material for air conditioner piping and process for producing the same

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JP9354188A JPH11172388A (ja) 1997-12-08 1997-12-08 エアコン配管用アルミニウム合金押出管材およびその製造方法
PCT/JP1999/002843 WO2000073529A1 (fr) 1997-12-08 1999-05-28 Corps creux en alliage d'aluminium, tuyau en alliage d'aluminium extrude pour canalisations de climatisation, et procede de fabrication de ce corps creux

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US09/771,309 Continuation US6908520B2 (en) 1999-05-28 2001-01-26 Aluminum alloy hollow material, aluminum alloy extruded pipe material for air conditioner piping and process for producing the same

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JPH11172388A (ja) * 1997-12-08 1999-06-29 Furukawa Electric Co Ltd:The エアコン配管用アルミニウム合金押出管材およびその製造方法
US6908520B2 (en) 1999-05-28 2005-06-21 The Furukawa Electric Co., Ltd. Aluminum alloy hollow material, aluminum alloy extruded pipe material for air conditioner piping and process for producing the same
JP2002038232A (ja) * 2000-07-21 2002-02-06 Furukawa Electric Co Ltd:The 熱交換器用アルミニウム合金配管材
JP4846124B2 (ja) * 2001-05-22 2011-12-28 住友軽金属工業株式会社 耐食性と加工性に優れた自動車の配管用アルミニウム合金管材の製造方法
WO2004061147A1 (fr) * 2002-12-27 2004-07-22 Showa Denko K.K. Tuyau d'aluminium et son procede de production
CN100469926C (zh) * 2004-02-13 2009-03-18 株式会社电装 换热器用铝合金挤压材料及其制造方法
JP2008121108A (ja) * 2006-10-16 2008-05-29 Showa Denko Kk 熱交換器用チューブおよびその製造方法
JP2009138983A (ja) * 2007-12-05 2009-06-25 Toyo Densen Kk 冷媒配管
JP5789355B2 (ja) * 2007-12-26 2015-10-07 アイシン軽金属株式会社 熱交換器用アルミニウム合金
JP5822562B2 (ja) * 2011-07-01 2015-11-24 昭和電工株式会社 感光ドラム基体用アルミニウム合金及び感光ドラム基体用アルミニウム合金押出管の製造方法
CA2776003C (fr) * 2012-04-27 2019-03-12 Rio Tinto Alcan International Limited Alliage d'aluminium offrant une excellente combinaison de resistance, d'extrudabilite et de resistance a la corrosion
KR20140000406A (ko) * 2012-06-22 2014-01-03 현대자동차주식회사 알루미늄 합금 조성물, 이를 포함하는 내식성이 향상된 인터쿨러용 알루미늄 압출 튜브 및 이의 제조방법
US10669616B2 (en) 2012-09-21 2020-06-02 Rio Tinto Alcan International Limited Aluminum alloy composition and method
CN102994812A (zh) * 2012-11-19 2013-03-27 宁波福士汽车部件有限公司 一种铝合金空调管材料及制备方法
CN102978482A (zh) * 2012-11-27 2013-03-20 温州天迪铝业有限公司 一种铝管成型用铝合金材料
CN103191946B (zh) * 2013-03-27 2015-11-18 江苏格林威尔金属材料科技有限公司 铝合金内圆型多孔平行流管制造工艺
US10508325B2 (en) * 2015-06-18 2019-12-17 Brazeway, Inc. Corrosion-resistant aluminum alloy for heat exchanger
CN105605958A (zh) * 2015-12-21 2016-05-25 江苏格林威尔金属材料科技有限公司 一种镀银铝合金散热器用圆管
CN107159729A (zh) * 2017-05-12 2017-09-15 辽宁忠旺集团有限公司 军用装甲车用7a52铝合金管材挤压工艺
CN109022939A (zh) * 2018-10-10 2018-12-18 江苏亚太安信达铝业有限公司 一种用于家用空调微通道铝扁管的铝合金及其应用
CN110257671B (zh) * 2019-07-03 2021-05-28 张家港市宏基精密铝材科技有限公司 一种铝合金、铝扁管和铝扁管生产工艺
KR102457118B1 (ko) * 2019-09-27 2022-10-20 씨앤지하이테크 주식회사 내식성이 향상된 전열관용 알루미늄 합금 튜브 및 이의 제조방법

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