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WO2021230080A1 - Matériau de forgeage d'alliage d'aluminium et son procédé de fabrication - Google Patents

Matériau de forgeage d'alliage d'aluminium et son procédé de fabrication Download PDF

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Publication number
WO2021230080A1
WO2021230080A1 PCT/JP2021/016908 JP2021016908W WO2021230080A1 WO 2021230080 A1 WO2021230080 A1 WO 2021230080A1 JP 2021016908 W JP2021016908 W JP 2021016908W WO 2021230080 A1 WO2021230080 A1 WO 2021230080A1
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Prior art keywords
aluminum alloy
forged material
alloy forged
content
grain boundaries
Prior art date
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Ceased
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PCT/JP2021/016908
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English (en)
Japanese (ja)
Inventor
劼 ▲けい▼
和宏 塩澤
安志 大和田
和樹 杉原
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Nippon Light Metal Co Ltd
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Nippon Light Metal Co Ltd
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Publication date
Application filed by Nippon Light Metal Co Ltd filed Critical Nippon Light Metal Co Ltd
Priority to JP2022521824A priority Critical patent/JP7799605B2/ja
Priority to US17/922,913 priority patent/US20230167530A1/en
Priority to CN202180034583.8A priority patent/CN115552048A/zh
Priority to EP21804469.1A priority patent/EP4151764A4/fr
Priority to KR1020227042967A priority patent/KR102903319B1/ko
Publication of WO2021230080A1 publication Critical patent/WO2021230080A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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    • 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
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
    • 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
    • C22F1/043—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 of alloys with silicon as the next major constituent
    • 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
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • 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
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
    • C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
    • 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
    • C22F1/047—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 of alloys with magnesium as the next major constituent
    • 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
    • C22F1/05—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 of alloys of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions

Definitions

  • the present invention relates to an aluminum alloy forged material and a method for manufacturing the same, and particularly to an aluminum alloy forged material that can be suitably used for undercarriage parts for automobiles and the like, and a simple and efficient manufacturing method thereof.
  • the 6000 series aluminum alloy is an Al-Mg-Si based aluminum alloy to which Mg and Si are mainly added, and in addition to being excellent in moldability and corrosion resistance, it exhibits moderate age hardening and has good strength.
  • Forged members are widely used as structural members for transportation equipment such as automobiles.
  • Patent Document 1 Japanese Unexamined Patent Publication No. 2017-155251
  • Si 0.7 to 1.5%
  • Mg 0.6 to 1.2%
  • Fe 0 in mass%.
  • Mn 0.05 to 1.0%
  • Cr 0.01 to 0.5%
  • Zr 0.01 to 0.2%.
  • the dislocation density was in the range of 1.0 ⁇ 10 14 to 5.0 ⁇ 10 16 / m 2 on average, and the tilt angle of the crystal grains with an orientation difference of 2 ° or more measured by the SEM-EBSD method was 2 to 2. It is characterized by an average ratio of 15 ° small tilt angle grain boundaries of 50% or more and an average number density of precipitates measurable by TEM at a magnification of 300,000 times of 5.0 ⁇ 10 2 / ⁇ m 3 or more.
  • An aluminum alloy forged material having excellent strength and ductility is disclosed.
  • Patent Document 2 Japanese Unexamined Patent Publication No. 2008-163445
  • Mg 0.5 to 1.25%
  • Si 0.4 to 1.4%
  • Cu 0.01 to 0 in mass%. .7%
  • Fe 0.05 to 0.4%
  • Mn 0.001 to 1.0%
  • Cr 0.01 to 0.35%
  • Ti 0.005 to 0.1%
  • Zr regulated to less than 0.15%
  • the balance is an aluminum alloy forged material composed of Al and unavoidable impurities.
  • the crystallite density observed in the structure of the cross-sectional area where stress is generated is 1.5% or less in average area ratio, and each grain boundary observed in the structure of the cross-sectional area including the parting line generated during forging.
  • Disclosed are automobile undercarriage parts, characterized in that the distance between the precipitates is 0.7 ⁇ m or more in average distance.
  • the cross-sectional structure in the width direction of each specific portion of the rib and the web at the maximum stress generation portion in the rib for example, of the automobile undercarriage component arm portion having a lightweight shape is provided.
  • the components of the arm part of the automobile undercarriage after forging are adjusted and manufactured so that the widthwise cross-sectional structure of each specific part of the rib and the web at the part where the maximum stress is generated such as the rib is a predetermined structure.
  • the mechanical properties of the 6000 series aluminum alloy are affected by the precipitates at the grain boundaries and the crystal precipitates in the crystal grains.
  • the precipitates in the crystal grains are basically used. Focusing only on, the influence of the precipitates at the grain boundaries, which greatly contributes to toughness (dexterity), is not taken into consideration.
  • an object of the present invention is to provide a 6000 series aluminum alloy forged material having high strength and excellent toughness (good ductility) and an efficient manufacturing method thereof. ..
  • the present inventors added sufficient Si to form fine precipitates in the crystal grains. We have found that it is extremely effective to add appropriate amounts of Mn and Cr to refine the precipitates at the grain boundaries in addition to forming them, and have reached the present invention.
  • the present invention Made of 6000 series aluminum alloy
  • the Cu content is 0.2 to 1.0 wt%
  • the composition of the 6000 series aluminum alloy satisfies the following relational formulas (1) and (2). Having precipitates at the grain boundaries of the base metal and Al- (Fe, Mn, Cr) -Si-based crystal precipitates in the grain boundaries of the base metal.
  • an aluminum alloy forged material which is characterized by. Si (at%) ⁇ 2Mg (at%) (1) 0.2 ⁇ Excess Si (wt%) + Mn (wt%) + Cr (wt%) ⁇ 1.7 (2)
  • the aluminum alloy forged member of the present invention by adding sufficient Si for the formation of Mg 2 Si, a fine and large amount of crystal precipitates are formed in the crystal grains.
  • Al- (Fe, Mn, Cr) -Si compounds are crystallized during casting and homogenized heat treatment is performed.
  • the precipitation of excess Si causes precipitates at the crystal grain boundaries.
  • the excess Si amount (wt%) can be calculated by "Si amount (wt%)-(Mg amount (wt%) /1.731".
  • the aluminum alloy forged material of the present invention contains 0.2 to 1.0 wt% of Cu, so that it is an Al, Mg, Si, Cu-based quaternary precipitate (Q phase or Q'phase). Good mechanical strength and fatigue strength are imparted by the formation of.
  • the Si content is 0.5 to 1.4 wt% and the Mg content is 0.6 to 1.7 wt%.
  • the more preferable Si content is 0.9 to 1.2 wt%, and the more preferable Mg content is 0.8 to 1.2 wt%.
  • the Si content is 0.5 wt% or more, solid solution strengthening and aging hardening can be sufficiently exhibited, and when it is 1.4 wt% or less, the corrosion resistance is lowered and the crystallized material and the precipitate are coarse. It is possible to suppress the decrease in ductility caused by the formation. Further, by setting the Si content to 0.9 to 1.2 wt%, these effects can be obtained more reliably.
  • the Mg content can be 0.6 wt% or more, a sufficient amount of Mg-Si-based precipitates can be formed, the strength and fatigue characteristics can be improved, and the Mg content can be 1.7 wt% or less. By doing so, it is possible to suppress the formation of a coarse compound that is the starting point of fracture. By setting the Mg content to 0.8 to 1.2 wt%, these effects can be obtained more reliably.
  • the average particle size of the precipitate at the grain boundaries of the base metal is 50 nm or less.
  • the average particle size of the precipitates at the grain boundaries of the base metal is 50 nm or less, good ductility (toughness) can be imparted to the aluminum alloy forged material.
  • the average particle size of the precipitate may be calculated as a circle-equivalent diameter.
  • the aspect ratio of the precipitate at the grain boundaries of the base material is 5 or less.
  • the width of the non-precipitation zone centered on the grain boundaries of the base metal is 100 nm or less.
  • the 0.2% proof stress is 350 MPa or more and the elongation is 10% or more. Since the aluminum alloy forged material has a 0.2% proof stress of 350 MPa or more and an elongation of 10% or more, it can be suitably used for structural members that require high reliability.
  • the present invention also provides an automobile undercarriage component made of the aluminum alloy forged material of the present invention.
  • the aluminum alloy forged material of the present invention has good strength and ductility, and the undercarriage parts for automobiles of the present invention can be suitably used when high strength and reliability are required.
  • the method for producing an aluminum alloy forged material of the present invention The Cu content of the aluminum alloy forged material is 0.2 to 1.0 wt%.
  • Hot forging preheating process to preheat aluminum alloy material A hot forging step of hot forging the preheated aluminum alloy material obtained in the hot forging preheating step is included.
  • the preheating temperature in the hot forging preheating step is 300 to 550 ° C., and the preheating time is 1 to 3 hours.
  • the composition of the aluminum alloy satisfies the following relational expressions (1) and (2).
  • a method for manufacturing an aluminum alloy forged material which is characterized by the above. Si (at%) ⁇ 2Mg (at%) (1) 0.2 ⁇ Excess Si (wt%) + Mn (wt%) + Cr (wt%) ⁇ 1.7 (2)
  • an Al- (Fe, Mn, Cr) -Si-based compound is subjected to a hot forging preheating step in which the preheating temperature is 300 to 550 ° C and the preheating time is 1 to 3 hours.
  • the precipitate at the crystal grain boundary is refined by consuming excess Si.
  • a homogenizing heat treatment step for the aluminum alloy material is provided before the hot forging preheating step, and the temperature of the homogenizing heat treatment step is set to 500 to 550 ° C. It is preferable that the holding time is 5 to 10 hours.
  • the Al- (Fe, Mn, Cr) -Si compound is more reliably precipitated, and the strength of the aluminum alloy forged member is increased.
  • the precipitates at the crystal grain boundaries are refined by consuming excess Si.
  • Aluminum alloy forged material (1) Composition
  • the aluminum alloy forged material is made of 6000 series aluminum alloy, and in order to impart high strength and toughness (dexterity) to the aluminum alloy forged material, the content of Si, Mg, Mn and Cr is particularly high. Is optimized.
  • each characteristic element of the aluminum alloy forged material of the present invention will be described.
  • Cu 0.2-1.0 wt%
  • the Cu content is 0.2 to 1.0 wt%.
  • Cu has an action of increasing mechanical strength and fatigue strength by forming Al, Mg, Si, and Cu-based quaternary precipitates (Q phase or Q'phase). If the Cu content is less than 0.2 wt%, these effects cannot be sufficiently obtained, and the proof stress of the aluminum alloy forged material cannot be 350 MPa or more. On the other hand, if the Cu content exceeds 1.0 wt%, the corrosion resistance may be lowered.
  • the Si content is preferably 0.5 to 1.4 wt%.
  • the Si content is preferably 0.5 to 1.4 wt%.
  • the Si content is 0.5 wt% or more, solid solution strengthening and aging hardening can be sufficiently exhibited, and when it is 1.4 wt% or less, the corrosion resistance is lowered and the crystallized material and the precipitate are coarse. It is possible to suppress the decrease in ductility caused by the formation.
  • the more preferable Si content is 0.9 to 1.2 wt%. By setting the Si content to 0.9 to 1.2 wt%, these effects can be obtained more reliably.
  • the Mg content is preferably 0.6 to 1.7 wt%.
  • the Mg content is set to 1.7 wt% or less. This makes it possible to suppress the formation of a coarse compound that is the starting point of fracture.
  • the more preferable Mg content is 0.8 to 1.2 wt%. By setting the Mg content to 0.8 to 1.2 wt%, these effects can be obtained more reliably.
  • Mn 0.1-0.8 wt%
  • the Mn content is preferably 0.1 to 0.8 wt%.
  • the strength of the aluminum alloy forged material can be increased by forming an Al- (Fe, Mn, Cr) -Si-based compound.
  • the Mn content is set to 0.8 wt% or less, it is possible to suppress the formation of coarse Al— (Fe, Mn, Cr) -Si compounds that reduce toughness and ductility.
  • the Cr content is preferably 0.1 to 0.8 wt%.
  • the Cr content is preferably 0.1 to 0.8 wt%.
  • the Fe content is preferably 0.05 to 0.3 wt%.
  • the Fe content is preferably 0.05 to 0.3 wt%.
  • the strength of the aluminum alloy forged material can be increased by forming an Al- (Fe, Mn, Cr) -Si-based compound.
  • the Fe content is set to 0.3 wt% or less, it is possible to suppress the formation of coarse Al— (Fe, Mn, Cr) -Si compounds that reduce toughness and ductility.
  • Cu, Zn, Ti and the like can be contained in the composition range specified as various 6000 series aluminum alloys (Al—Mg—Si based alloys).
  • Si (at%) ⁇ 2Mg (at%) When Si and Mg satisfy Si (at%) ⁇ 2Mg (at%) , sufficient Si is present for the formation of Mg 2 Si, and a large amount of crystal precipitates are formed in the crystal grains. be able to.
  • FIG. 1 shows a schematic diagram of the fine structure of the forged aluminum alloy material of the present invention.
  • the precipitate 6 is formed at the grain boundaries 4 of the aluminum base material 2.
  • extremely fine Al- (Fe, Mn, Cr) -Si-based crystal precipitates are dispersed in the crystal grains of the aluminum base material 2. It should be noted that what is present in the crystal grains is not limited to Al- (Fe, Mn, Cr) -Si-based crystal precipitates, and is generally known as, for example, an aging precipitation phase of an Al-Mg-Si-based alloy.
  • the ⁇ phase and its precursor phase, the Q phase and its precursor phase and the like may be dispersed.
  • the average particle size of the precipitate 6 at the grain boundaries 4 is preferably 50 nm or less. When the average particle size of the precipitate 6 at the grain boundaries 4 is 50 nm or less, good ductility (toughness) can be imparted to the aluminum alloy forged material.
  • the average particle size of the precipitate 6 is more preferably 40 nm or less, and most preferably 30 nm or less.
  • the aspect ratio of the precipitate 6 at the grain boundaries 4 is preferably 5 or less.
  • the aspect ratio of the precipitate 6 at the crystal grain boundaries 4 is set to 5 or less, the ratio of the precipitates 6 occupying the crystal grain boundaries 4 can be reduced, and the distance between the precipitates 6 can be increased. As a result, it is possible to suppress the propagation of the precipitate 6 and the growth of cracks, and it is possible to impart good ductility (toughness) to the aluminum alloy forged material.
  • the more preferable aspect ratio of the precipitate 6 is 4 or less, and the most preferable aspect ratio is 3 or less.
  • the width of the non-precipitation zone centered on the crystal grain boundaries 4 is preferably 100 nm or less.
  • the width of the non-precipitation zone is 90 nm or less, and the most preferable width is 80 nm or less.
  • the aluminum alloy forged material has the above composition and composition, and thus has excellent tensile properties.
  • the 0.2% proof stress is 350 MPa or more and the elongation is 10% or more.
  • the aluminum alloy forged material 2 has a 0.2% proof stress of 350 MPa or more and an elongation of 10% or more, it can be suitably used for structural members that require high reliability.
  • the more preferable 0.2% proof stress of the aluminum alloy forged material 2 is 360 MPa or more, and the most preferable 0.2% proof stress is 370 MPa or more.
  • the more preferable elongation of the aluminum alloy forged material 2 is 12% or more, and the most preferable elongation is 14% or more.
  • undercarriage parts for automobiles of the present invention are undercarriage parts for automobiles made of the forged aluminum alloy of the present invention.
  • suspension parts for automobiles include upper arms, lower arms, transverse links, etc., which are suspension parts for automobiles.
  • the method for producing an aluminum alloy forged material of the present invention provides an effective method for producing the aluminum alloy forged material of the present invention.
  • the Cu content of the aluminum alloy forged material is 0.2 to 1.0 wt%, and a hot forging preheating step for preheating the aluminum alloy material and a hot forging preheating step. It includes a hot forging step of hot forging the preheated aluminum alloy material obtained in 1.
  • the other steps are not particularly limited as long as the effects of the present invention are not impaired, and various conventionally known steps used for producing a forged material of a 6000 series aluminum alloy may be used, if necessary. Just do it.
  • a process characteristic of the method for producing an aluminum alloy forged material of the present invention will be described.
  • (1) Homogenization heat treatment step As a pretreatment of the hot forging step including the hot forging preheating step, it is preferable to perform the homogenizing heat treatment on the aluminum alloy material to be hot forged. Further, the temperature of the homogenization heat treatment step is preferably 500 to 550 ° C., and the holding time is preferably 5 to 10 hours.
  • the homogenization heat treatment at 500 to 550 ° C. for 5 to 10 hours, Al- (Fe, Mn, Cr) -Si-based compounds are more reliably precipitated in the crystal grains of the aluminum base material 2, and the aluminum alloy is formed.
  • the precipitate 6 at the crystal grain boundary 4 can be made finer by consuming excess Si. As a result, the aspect ratio of the precipitate 6 can be reduced.
  • Hot forging preheating process This is a process performed as a preliminary treatment for the hot forging process.
  • Al- (Fe, Mn, Cr) -Si system is used in the crystal grains of the aluminum base material 2.
  • the precipitate 6 at the crystal grain boundary 4 can be made finer by consuming excess Si. As a result, the aspect ratio of the precipitate 6 can be reduced.
  • the aluminum alloy material preheated by using various conventionally known forging methods may be hot forged to obtain a desired shape. Further, by making the final shape an upper arm, a lower arm, a transverse link, etc., which are suspension parts for automobiles, the undercarriage parts for automobiles of the present invention can be obtained.
  • the conditions for the solution treatment and the aging treatment are not particularly limited, and various conventionally known solution treatments and aging treatments can be used as long as the effects of the present invention are not impaired. Since these optimum conditions depend on the type of aluminum alloy, the shape and size of the forged part, etc., it is appropriate to observe the structure and evaluate the mechanical properties of the forged part after solution treatment and aging treatment. It is preferable to select the conditions.
  • the obtained slab was cut and forged to a forging rate of 60% after a hot forging preheating step at 350 ° C. or 500 ° C. for 2 hours to obtain an aluminum alloy forged material.
  • the case where the homogenization heat treatment was performed at 510 ° C. for 6 hours or 550 ° C. for 10 hours before the hot forging preheating step and the case where the homogenization heat treatment was not performed were examined.
  • the obtained aluminum alloy forged material was subjected to a solution treatment at 550 ° C. for 2 hours, then water-cooled, and an aging treatment at 180 ° C. for 8 hours.
  • Table 2 shows the tensile properties and manufacturing conditions of each of the obtained forged aluminum alloy materials.
  • the tensile test piece the No. 14A test piece described in JIS Z2241 is used, and the tensile speed conforms to JIS Z2241. bottom.
  • the aluminum alloy forged material of the present invention has a 0.2% proof stress of 350 MPa and an elongation of 10% or more.
  • the average value and aspect ratio of the equivalent circle diameters of the precipitates present at the grain boundaries of the aluminum base material were obtained.
  • the circle equivalent diameter and the aspect ratio of the precipitate were calculated using image processing software (Image-Pro Premier V9.0 manufactured by Media Cybernetic Inc. in the United States). The results obtained are shown in Table 2. It can be seen that in the aluminum alloy forged material of the present invention, the average value of the equivalent circle diameters of the precipitates present at the crystal grain boundaries is 50 ⁇ m or less, and the aspect ratio is 5 or less.
  • FIG. 2 shows the TEM observation results of the aluminum alloy forged material of Example 1 (homogenization heat treatment: 510 ° C., 6 h, hot forging preheating step: 500 ° C., 2 h) in the vicinity of the grain boundaries of the aluminum base material.
  • a Tecnai series G2-F20 manufactured by FEI was used for TEM observation. Precipitates at the grain boundaries of the aluminum base material can be confirmed, and it can be seen that the precipitates are fine and granular. In addition, the precipitates are not in close contact with each other and are in an ideal state for imparting good toughness and ductility to the forged aluminum alloy.
  • the width of the non-precipitation zone is 100 nm or less.
  • FIG. 3 shows the TEM observation results in the aluminum base metal crystal grains of the aluminum alloy forged material of Example 1 (homogenization heat treatment: 510 ° C., 6 h, hot forging preheating step: 500 ° C., 2 h). It can be confirmed that a large amount of fine crystal precipitates are dispersed in the crystal grains of the aluminum base material.
  • the TEM-EDS spectrum of the crystal precipitate is shown in FIG. 4, and it was confirmed that the crystal precipitate contained an Al- (Fe, Mn, Cr) -Si-based crystal precipitate.
  • Table 3 shows the production conditions, tensile properties, and information on the precipitates present at the grain boundaries of the aluminum base metal, which were obtained as comparative examples. Table 3 also shows the results of obtaining the average value and aspect ratio of the equivalent circle diameters of the precipitates present at the grain boundaries of the aluminum base material for some aluminum alloy forged materials.
  • the aluminum alloy forged material of the comparative example cannot achieve both strength and ductility at a high level.
  • Comparative Examples 1 to 4 having no excess Si the absolute strength is insufficient, and the 0.2% proof stress is less than 350 MPa in each case.
  • Comparative Example 5 which has excess Si but does not contain Mn and / or Cr has poor ductility, and in each case, the elongation is less than 10%.
  • Comparative Example 6 which contains Mn and Cr but does not have excess Si the absolute strength is insufficient, and the 0.2% proof stress is less than 350 MPa in each case. ..
  • the average diameter equivalent to a circle is larger than 50 nm, and the aspect ratio is also larger than 5.
  • FIG. 5 shows the TEM observation results of the aluminum alloy forged material of Comparative Example 5 (homogenization heat treatment: 510 ° C., 6 h, hot forging preheating step: 500 ° C., 2 h) in the vicinity of the grain boundaries of the aluminum base material. Precipitates at the grain boundaries of the aluminum base material can be confirmed, and it can be seen that the precipitates are coarse and needle-shaped. In addition, the width of the non-precipitation zone is larger than that of the aluminum alloy forged material obtained in the examples.
  • FIG. 6 shows the TEM observation results of the aluminum alloy forged material of Comparative Example 1 (homogenization heat treatment: 510 ° C., 6 h, hot forging preheating step: 500 ° C., 2 h) in the vicinity of the grain boundaries of the aluminum base material. Precipitates at the grain boundaries of the aluminum base material can be confirmed, and it can be seen that the amount of the precipitates is smaller than that of the aluminum alloy forged material obtained in the examples.
  • FIG. 7 shows the TEM observation results of the aluminum alloy forged material of Comparative Example 4 (homogenization heat treatment: 510 ° C., 6 h, hot forging preheating step: 500 ° C., 2 h) in the vicinity of the grain boundaries of the aluminum base material. Precipitates at the grain boundaries of the aluminum base material can be confirmed, and it can be seen that the precipitates are finer than in the case of Comparative Example 1.
  • FIG. 8 shows the TEM observation results in the aluminum base metal crystal grains of the aluminum alloy forged material of Comparative Example 5 (homogenization heat treatment: 510 ° C., 6 h, hot forging preheating step: 500 ° C., 2 h). Dispersion of crystal precipitates is not clearly confirmed in the crystal grains of the aluminum base material.
  • the aluminum alloy forged material of Comparative Example 7 has sufficient Si and satisfies the relationship of 0.2 ⁇ excess Si (wt%) + Mn (wt%) + Cr (wt%) ⁇ 1.7.
  • the Cu content is less than 0.2 wt%, and the tensile strength and 0.2% proof stress are low values.
  • the aluminum alloy forged material of the present invention a large amount of fine Al- (Fe, Mn, Cr) -Si-based crystal precipitates are dispersed in the crystal grains of the aluminum base material, and the precipitates in the crystal grains. It can be seen that the material has a fine and nearly granular shape, and as a result, it has high strength and excellent toughness (good ductility).

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Abstract

La présente invention concerne un matériau de forgeage d'alliage d'aluminium de série 6000 présentant une résistance élevée et une ténacité exceptionnelle (excellente ductilité), et un procédé efficace pour le fabriquer. Ce matériau de forgeage d'alliage d'aluminium est caractérisé en ce qu'il est formé à partir d'un alliage d'aluminium de série 6000, présentant une teneur en Cu de 0,2 à 1,0 % en poids, la composition de l'alliage d'aluminium de série 6000 satisfaisant les expressions relationnelles (1) et (2), et ayant des dépôts au niveau du joint des grains cristallins de métal de base, plus précisément des dépôts cristallins de type Al-(Fe,Mn,Cr)-Si au niveau du joint des grains cristallins de métal de base. (1) Si (% at) ≥ 2 Mg (% at) (2) 0,2 ≤ surplus de Si (% en poids) + Mn (% en poids) + Cr (% en poids) ≤ 1,7
PCT/JP2021/016908 2020-05-13 2021-04-28 Matériau de forgeage d'alliage d'aluminium et son procédé de fabrication Ceased WO2021230080A1 (fr)

Priority Applications (5)

Application Number Priority Date Filing Date Title
JP2022521824A JP7799605B2 (ja) 2020-05-13 2021-04-28 アルミニウム合金鍛造材及びその製造方法
US17/922,913 US20230167530A1 (en) 2020-05-13 2021-04-28 Aluminum alloy forging material and method for manufacturing same
CN202180034583.8A CN115552048A (zh) 2020-05-13 2021-04-28 铝合金锻造材料及其制造方法
EP21804469.1A EP4151764A4 (fr) 2020-05-13 2021-04-28 Matériau de forgeage d'alliage d'aluminium et son procédé de fabrication
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JP7727053B1 (ja) 2024-05-29 2025-08-20 株式会社神戸製鋼所 アルミニウム合金鍛造材
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JP2025180061A (ja) * 2024-05-29 2025-12-11 株式会社神戸製鋼所 アルミニウム合金鍛造材

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JP7799605B2 (ja) 2026-01-15
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