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WO2018012326A1 - Matériau de travail de matière plastique et d'alliage d'aluminium et son procédé de production - Google Patents

Matériau de travail de matière plastique et d'alliage d'aluminium et son procédé de production Download PDF

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Publication number
WO2018012326A1
WO2018012326A1 PCT/JP2017/024184 JP2017024184W WO2018012326A1 WO 2018012326 A1 WO2018012326 A1 WO 2018012326A1 JP 2017024184 W JP2017024184 W JP 2017024184W WO 2018012326 A1 WO2018012326 A1 WO 2018012326A1
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Prior art keywords
aluminum alloy
plastic working
phase
working material
alloy plastic
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Legal status (The legal status 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 status listed.)
Ceased
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PCT/JP2017/024184
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English (en)
Japanese (ja)
Inventor
俊 兪
保生 石渡
大輔 下坂
琢年 近藤
喜弘 田口
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Nippon Light Metal Co Ltd
Original Assignee
Nippon Light Metal 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.)
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Publication date
Application filed by Nippon Light Metal Co Ltd filed Critical Nippon Light Metal Co Ltd
Priority to CN201780043200.7A priority Critical patent/CN109477169B/zh
Priority to KR1020197003675A priority patent/KR102444566B1/ko
Priority to EP17827456.9A priority patent/EP3486340B1/fr
Priority to US16/316,974 priority patent/US20190316241A1/en
Priority to JP2017550652A priority patent/JP6341337B1/ja
Publication of WO2018012326A1 publication Critical patent/WO2018012326A1/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
    • 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

Definitions

  • the present invention relates to an aluminum alloy plastic working material having an excellent proof stress while having a low Young's modulus, and a method for producing the same.
  • Aluminum has many excellent properties such as corrosion resistance, electrical conductivity, thermal conductivity, lightness, radiance, and machinability, so it is used in various applications. Moreover, since the plastic deformation resistance is small, various shapes can be imparted, and it is often used for members subjected to plastic working such as bending.
  • Patent Document 1 JP 2011-105982
  • the Al phase and an aluminum alloy containing Al 4 Ca phase is the Al 4 Ca crystallized substance
  • the Al An aluminum alloy characterized in that the average value of the long side of 4 Ca crystallized substance is 50 ⁇ m or less has been proposed.
  • an object of the present invention is to provide an aluminum alloy plastic work material having a low Young's modulus and excellent in proof stress and an efficient manufacturing method thereof.
  • the present inventors have conducted extensive research on an aluminum alloy plastic work material and a method for producing the same, and as a result, an Al 4 Ca phase is used as a dispersed phase, and the crystal structure of the Al 4 Ca phase is appropriately determined.
  • the present inventors have found that it is extremely effective to control to the present, and reached the present invention.
  • the present invention Containing 5.0-10.0 wt% Ca,
  • the balance consists of aluminum and inevitable impurities
  • the volume ratio of the Al 4 Ca phase that is the dispersed phase is 25% or more
  • the Al 4 Ca phase comprises a tetragonal Al 4 Ca phase and a monoclinic Al 4 Ca phase
  • the intensity ratio (I 1 / I 2 ) between the maximum diffraction peak (I 1 ) attributed to the tetragonal crystal obtained by X-ray diffraction measurement and the maximum diffraction peak (I 2 ) attributed to the monoclinic crystal is 1 That An aluminum alloy plastic working material is provided.
  • an Al 4 Ca compound is formed, and has an effect of lowering the Young's modulus of the aluminum alloy.
  • the effect becomes significant when the Ca content is 5.0% or more, and conversely, if added over 10.0%, the castability deteriorates, and in particular, casting by continuous casting such as DC casting becomes difficult. Therefore, it is necessary to manufacture by a method with high manufacturing cost such as powder metallurgy.
  • the oxide formed on the surface of the alloy powder may be mixed into the product, and the yield strength may be reduced.
  • the crystal structure of the Al 4 Ca phase used as the dispersed phase is basically a tetragonal crystal.
  • the crystal structure of the Al 4 Ca phase is It has been clarified that the presence of a monoclinic crystal does not significantly decrease the yield strength, while the Young's modulus decreases greatly.
  • the volume ratio of the Al 4 Ca phase is 25% or more, and the maximum diffraction peak (I 1 ) attributed to the tetragonal crystal obtained by X-ray diffraction measurement and the maximum diffraction peak (I 1 ) attributed to the monoclinic crystal (I 2 ) and the strength ratio (I 1 / I 2 ) of 1 or less, the Young's modulus can be greatly reduced while maintaining the yield strength.
  • the aluminum alloy plastic working material of the present invention preferably further contains one or more of Fe: 0.05 to 1.0 wt% and Ti: 0.005 to 0.05 wt%. .
  • the solidification temperature range solid-liquid coexistence region
  • the solidification temperature range solid-liquid coexistence region
  • the eutectic structure uniform due to the dispersed crystals of Fe. The effect becomes remarkable when the Fe content is 0.05 wt% or more, and conversely, if the Fe content exceeds 1.0 wt%, the eutectic structure becomes coarse and the proof stress may be reduced.
  • Ti acts as a refined material of the cast structure and exhibits the effect of improving castability, extrudability, and rollability. The effect becomes significant when the Ti content is 0.005 wt% or more, and conversely, even if added in excess of 0.05 wt%, an increase in the effect of refinement of the cast structure cannot be expected.
  • a coarse intermetallic compound may be generated.
  • Ti is preferably added using a rod hardener (Al—Ti—B alloy) during casting. In this case, B added as Ti as a rod hardener is allowed.
  • the average crystal grain size of the Al 4 Ca phase is 1.5 ⁇ m or less.
  • the average particle diameter of the Al 4 Ca phase becomes too large, the proof stress of the aluminum alloy is lowered.
  • the average particle diameter is 1.5 ⁇ m or less, the decrease in the proof stress can be suppressed.
  • the present invention also provides: An aluminum alloy ingot containing 5.0 to 10.0 wt% Ca, the balance being aluminum and inevitable impurities, and the volume ratio of the Al 4 Ca phase being a dispersed phase being 25% or more is subjected to plastic working.
  • One process A second step of performing a heat treatment in a temperature range of 100 to 300 ° C., The manufacturing method of the aluminum alloy plastic working material characterized by these is also provided.
  • An aluminum alloy ingot containing 5.0 to 10.0 wt% Ca, the balance being aluminum and inevitable impurities, and the volume ratio of the Al 4 Ca phase being a dispersed phase being 25% or more is subjected to plastic working.
  • heat treatment (second step) in a temperature range of 100 to 300 ° C. after one step, a part of the Al 4 Ca phase having a tetragonal crystal structure can be changed to a monoclinic crystal.
  • the holding temperature in the second step is less than 100 ° C., the change from tetragonal to monoclinic crystal is difficult to occur, and when the holding temperature is 300 ° C. or more, recrystallization of the aluminum base material occurs and the proof stress may be reduced.
  • a more preferable temperature range for the heat treatment is 160 to 240 ° C.
  • an appropriate heat treatment time varies depending on the size and shape of the aluminum alloy material, it is preferable that at least the temperature of the aluminum alloy material itself is held at the holding temperature for 1 hour or more.
  • the aluminum alloy ingot is one of Fe: 0.05 to 1.0 wt% and Ti: 0.005 to 0.05 wt%. It is preferable to include more than one type.
  • the solidification temperature range solid-liquid coexistence region
  • the solidification temperature range solid-liquid coexistence region
  • the eutectic structure uniform due to the dispersed crystals of Fe. The effect becomes remarkable when the Fe content is 0.05 wt% or more, and conversely, if the Fe content exceeds 1.0 wt%, the eutectic structure becomes coarse and the proof stress may be reduced.
  • Ti acts as a refined material of the cast structure and exhibits the effect of improving castability, extrudability, and rollability. The effect becomes significant when the Ti content is 0.005 wt% or more, and conversely, even if added in excess of 0.05 wt%, an increase in the effect of refinement of the cast structure cannot be expected.
  • a coarse intermetallic compound may be generated.
  • Ti is preferably added using a rod hardener (Al—Ti—B alloy) during casting. In this case, B added as Ti as a rod hardener is allowed.
  • a homogenization treatment is performed in which the ingot is held at 400 to 600 ° C. before plastic working.
  • Al 4 Ca contained in the aluminum alloy is performed.
  • the phase tends to be large, and the average particle size becomes larger than 1.5 ⁇ m. Since the yield strength decreases due to the increase in the average particle size, it is preferable not to perform a homogenization treatment in which the holding temperature is 400 ° C. or higher.
  • FIG. 3 is a structural photograph of a comparative aluminum alloy plastic working material 8.
  • Aluminum Alloy Plastic Work Material (1) Composition
  • the aluminum alloy plastic work material of the present invention contains 5.0 to 10.0 wt% Ca, with the balance being aluminum and inevitable impurities. Further, it is preferable to include at least one of Fe: 0.05 to 1.0 wt% and Ti: 0.005 to 0.05 wt%.
  • Fe iron
  • Ti titanium
  • Ca 5.0 to 10.0 wt% (preferably 6.0 to 8.0 wt%) Ca forms a compound of Al 4 Ca and has an action of reducing the Young's modulus of the aluminum alloy. The effect becomes remarkable at 5.0% or more, and conversely, if added over 10.0%, the castability deteriorates, and in particular, casting by continuous casting such as DC casting becomes difficult. Therefore, it is necessary to use a method having a high production cost.
  • the oxide formed on the surface of the alloy powder may be mixed into the product and the proof stress may be reduced.
  • Fe 0.05 to 1.0 wt%
  • the solidification temperature range solid-liquid coexistence region
  • the castability is improved
  • the casting surface of the ingot is improved.
  • It also has the effect of making the eutectic structure uniform due to the dispersed crystals of Fe. The effect becomes remarkable at 0.05 wt% or more, and conversely, if the content exceeds 1.0 wt%, the eutectic structure becomes coarse and the proof stress may be reduced.
  • Ti acts as a refining material for the cast structure and exhibits the effect of improving castability, extrudability, and rollability. The effect becomes significant at 0.005 wt% or more, and conversely, even if added in excess of 0.05 wt%, an increase in the refinement effect of the cast structure cannot be expected. There is a risk that intermetallic compounds are produced.
  • Ti is preferably added using a rod hardener (Al—Ti—B alloy) during casting. In this case, B added as Ti as a rod hardener is allowed.
  • the volume fraction of the Al 4 Ca phase that is a dispersed phase is 25% or more, and the Al 4 Ca phase is composed of tetragonal Al 4 Ca phase and monoclinic Al.
  • 4 Intensity ratio (I 1 / I) of the maximum diffraction peak (I 1 ) due to tetragonal crystal and the maximum diffraction peak (I 2 ) due to monoclinic crystal, which is made of 4 Ca phase and obtained by X-ray diffraction measurement. 2 ) is 1 or less.
  • the Al 4 Ca phase which is a dispersed phase, includes a tetragonal Al 4 Ca phase and a monoclinic Al 4 Ca phase, but the volume ratio of the Al 4 Ca phase that combines these is 25% or more. .
  • the volume ratio of the Al 4 Ca phase By setting the volume ratio of the Al 4 Ca phase to 25% or more, excellent proof stress can be imparted to the aluminum alloy plastic working material.
  • the average crystal grain size of the Al 4 Ca phase is preferably 1.5 ⁇ m or less. If the average particle size exceeds 1.5 ⁇ m, the proof stress of the aluminum alloy plastic working material may be reduced.
  • the crystal structure of the Al 4 Ca phase is normally tetragonal, but where the present inventors have conducted extensive studies, if there is one crystal structure in the Al 4 Ca phase is monoclinic, yield strength almost It has been found that the Young's modulus is greatly reduced, although not reduced. Note that the crystal structure of all Al 4 Ca phases does not have to be monoclinic, and may be mixed with tetragonal crystals.
  • the presence of an Al 4 Ca phase having a monoclinic crystal structure can be identified by measuring a diffraction peak using, for example, an X-ray diffraction method.
  • FIG. 1 shows a process diagram of the aluminum alloy plastic work material of the present invention.
  • the method for producing an aluminum alloy plastic working material of the present invention includes a first step (S01) for performing plastic working on an aluminum alloy ingot and a second step (S02) for performing heat treatment.
  • S01 first step
  • S02 second step
  • the casting method is not particularly limited, and various conventionally known casting methods can be used. For example, using a continuous casting method such as DC casting, plastic processing (extrusion, rolling, forging) in the first step (S01). Etc.) is preferably cast into a shape that is easy to perform. Note that a rod hardener (Al—Ti—B) may be added during casting to improve castability.
  • a homogenization treatment is performed by maintaining the ingot at 400 to 600 ° C. before plastic processing.
  • the homogenization treatment is performed, the Al 4 Ca phase becomes large (average particle size 1. It is preferable that the homogenization treatment is not performed in the method for producing an aluminum alloy plastic working material of the present invention.
  • the first step (S01) is a step in which the aluminum alloy ingot obtained in (1) is subjected to plastic working to obtain a desired shape.
  • Plastic processing such as extrusion, rolling, and forging may use either hot processing or cold processing, or a plurality of them may be combined.
  • the aluminum alloy becomes a work structure and the proof stress is improved.
  • most of the Al 4 Ca phase contained in the aluminum alloy has a tetragonal crystal structure.
  • Second step (S02) is a step of performing a heat treatment on the aluminum alloy plastic working material obtained in the first step (S01).
  • a part of the Al 4 Ca phase whose crystal structure is tetragonal is monoclinic by performing a heat treatment for holding the aluminum alloy plastic working material after the plastic working in the first step (S01) at 100 to 300 ° C. Crystal.
  • the change from tetragonal to monoclinic is unlikely to occur when the holding temperature is less than 100 ° C.
  • the holding temperature is 300 ° C. or higher, the aluminum base material may be recrystallized and the proof stress may be reduced. Therefore, the heat treatment holding temperature is preferably 100 to 300 ° C., and 160 to 240 ° C. More preferably.
  • the optimum heat treatment time varies depending on the size and shape of the aluminum alloy plastic work material to be treated, but it is preferable that at least the temperature of the aluminum alloy plastic work material is held at the holding temperature for 1 hour or more.
  • Example> An aluminum alloy having the composition shown in Table 1 was cast into a ⁇ 8 inch ingot (billet) by a DC casting method and then formed into a flat plate having a width of 180 mm and a thickness of 8 mm at an extrusion temperature of 500 ° C. without being homogenized. Plastic working. Then, after cold-rolling to thickness 5mm, the heat processing hold
  • the obtained aluminum alloy plastic working material 3 was subjected to X-ray diffraction, and the peak position of the Al 4 Ca phase was measured.
  • X-ray diffraction method a 20 mm ⁇ 20 mm sample was cut out from a plate-shaped aluminum alloy plastic working material, and after cutting a surface layer portion of about 500 ⁇ m, ⁇ -2 ⁇ was measured with a Cu—K ⁇ ray source. The obtained results are shown in FIG.
  • the intensity ratio (I 1 / I 2 ) between the maximum diffraction peak (I 1 ) attributed to tetragonal crystal and the maximum diffraction peak (I 2 ) attributed to monoclinic crystal was 0.956. there were.
  • Table 2 shows the volume ratio of the dispersed phase (Al 4 Ca phase) calculated from the results of the structure observation with an optical microscope.
  • the aluminum alloy plastic working materials 6 to 9 were obtained in the same manner as in the case of the aluminum alloy plastic working material 3 except that the temperature of the heat treatment was any of 100 ° C., 160 ° C., 240 ° C. and 300 ° C. Further, the Young's modulus and the proof stress were measured by a tensile test in the same manner as in the case of working aluminum alloy plastic working materials 1 to 5. The obtained results are shown in Table 3.
  • the obtained comparative aluminum alloy plastic working material 3 was subjected to X-ray diffraction, and the peak position of the Al 4 Ca phase was measured.
  • X-ray diffraction method a 20 mm ⁇ 20 mm sample was cut out from a plate-shaped aluminum alloy plastic working material, and after cutting a surface layer portion of about 500 ⁇ m, ⁇ -2 ⁇ was measured with a Cu—K ⁇ ray source. The obtained results are shown in FIG.
  • the intensity ratio (I 1 / I 2 ) between the maximum diffraction peak (I 1 ) attributed to the tetragonal crystal and the maximum diffraction peak (I 2 ) attributed to the monoclinic crystal was determined to be 1.375. there were.
  • JIS-14B test pieces were cut out from the comparative aluminum alloy plastic working materials 1 to 5, and Young's modulus and proof stress were measured by a tensile test. The obtained results are shown in Table 2.
  • Comparative aluminum alloy plastic working materials 6 and 7 were obtained in the same manner as in the case of the aluminum alloy plastic working material 3 except that the temperature of the heat treatment was either 90 ° C. or 310 ° C. Further, as in the case of comparative aluminum alloy plastic working materials 1 to 5, Young's modulus and proof stress were measured by a tensile test. The obtained results are shown in Table 3.
  • a comparative aluminum alloy plastic working material 8 was obtained in the same manner as in the aluminum alloy plastic working material 3 except that it was cast into an ingot (billet) and then homogenized at 550 ° C. Further, a JIS-14B test piece was cut out from the comparative aluminum alloy plastic working material 8, and Young's modulus and proof stress were measured by a tensile test. Table 4 shows the obtained results. In addition, as comparative data, Table 4 also shows the Young's modulus and proof stress of the aluminum alloy plastic working material 3 that differs only in the presence or absence of the homogenization treatment.
  • the Young's modulus of the aluminum alloy plastic working material of the present invention (implementing aluminum alloy plastic working materials 1 to 5) is compared between the aluminum alloy plastic working material having the same composition and the comparative aluminum alloy plastic working material. Is significantly lower than the Young's modulus of the comparative aluminum alloy plastic working materials 1 to 5 not subjected to heat treatment. On the other hand, the proof stress and tensile strength of the working aluminum alloy plastic working materials 1 to 5 are not significantly reduced as compared with the comparative aluminum alloy plastic working materials 1 to 5.
  • the volume fraction of the dispersed phase in the aluminum alloy plastic working material of the present invention (Al 4 Ca phase) is found to be 25% or more.
  • FIGS. 3 and 4 Structure photographs of the working aluminum alloy plastic working material 3 and the comparative aluminum alloy plastic working material 8 by an optical microscope are shown in FIGS. 3 and 4, respectively.
  • the black region was the Al 4 Ca phase
  • the average crystal grain size of the Al 4 Ca phase was measured by image analysis. Table 4 shows the obtained results.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Forging (AREA)
  • Powder Metallurgy (AREA)
  • Manufacture Of Alloys Or Alloy Compounds (AREA)

Abstract

La présente invention concerne un matériau de travail de matière plastique et d'alliage d'aluminium présentant un faible module de Young, mais présentant une limite d'élasticité supérieure, et un procédé permettant la production efficace d'un matériau de travail de matière plastique et d'alliage d'aluminium. Le matériau de travail de matière plastique et d'alliage d'aluminium, selon la présente invention, contient de 5,0 à 10,0% en poids de Ca, le reste étant composé d'aluminium et d'impuretés inévitables, et présente 25% ou plus en volume de phase Al4Ca qui est une phase dispersée. La phase Al4Ca comprend une phase Al4Ca tétragonale et une pahe Al4Ca monoclinique, et le rapport d'intensité (I1/I2) entre le pic de diffraction le plus élevé (I1) attribué au système tétragonal et le pic de diffraction le plus élevé (I2) attribué au système monocyclique, qui sont obtenus par mesure de diffraction aux rayons X, est inférieur ou égal à un.
PCT/JP2017/024184 2016-07-12 2017-06-30 Matériau de travail de matière plastique et d'alliage d'aluminium et son procédé de production Ceased WO2018012326A1 (fr)

Priority Applications (5)

Application Number Priority Date Filing Date Title
CN201780043200.7A CN109477169B (zh) 2016-07-12 2017-06-30 铝合金塑性加工材料及其制造方法
KR1020197003675A KR102444566B1 (ko) 2016-07-12 2017-06-30 알루미늄 합금 소성 가공재 및 그 제조 방법
EP17827456.9A EP3486340B1 (fr) 2016-07-12 2017-06-30 Matériau de travail de matière plastique et d'alliage d'aluminium et son procédé de production
US16/316,974 US20190316241A1 (en) 2016-07-12 2017-06-30 Aluminum alloy plastic working material and production method therefor
JP2017550652A JP6341337B1 (ja) 2016-07-12 2017-06-30 アルミニウム合金塑性加工材及びその製造方法

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JP2016137522 2016-07-12
JP2016-137522 2016-07-12

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US (1) US20190316241A1 (fr)
EP (1) EP3486340B1 (fr)
JP (1) JP6341337B1 (fr)
KR (1) KR102444566B1 (fr)
CN (1) CN109477169B (fr)
TW (1) TWI718319B (fr)
WO (1) WO2018012326A1 (fr)

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WO2022240023A1 (fr) * 2021-05-14 2022-11-17 엘지전자 주식회사 Alliage d'aluminium, son procédé de fabrication et pièces l'utilisant
CN115522102B (zh) * 2022-10-12 2023-07-18 苏州大学 一种铝合金导电材料及其制备方法

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KR101199912B1 (ko) * 2009-11-20 2012-11-09 한국생산기술연구원 알루미늄 합금의 제조 방법
KR101273383B1 (ko) * 2011-05-20 2013-06-11 한국생산기술연구원 알루미늄 용접용 용가재 및 그 제조방법

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WO2009035029A1 (fr) * 2007-09-14 2009-03-19 Nissan Motor Co., Ltd. Matériau amortissant les contraintes
JP2010126740A (ja) * 2008-11-25 2010-06-10 Nissan Motor Co Ltd アルミニウム合金及びその製造方法
JP2011105982A (ja) * 2009-11-16 2011-06-02 Nissan Motor Co Ltd アルミニウム合金およびその製造方法

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PELLEGRINI, G ET AL.: "Growth and Crystallography of the Unidirectionally Solidified Al-Al4Ca Eutectic", MATERIALS SCIENCE AND ENGINEERING, vol. 34, February 1978 (1978-02-01), pages 171 - 181, XP024084573 *
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CN109477169A (zh) 2019-03-15
EP3486340B1 (fr) 2021-01-27
TWI718319B (zh) 2021-02-11
KR102444566B1 (ko) 2022-09-20
KR20190028472A (ko) 2019-03-18
CN109477169B (zh) 2021-03-26
JP6341337B1 (ja) 2018-06-13
US20190316241A1 (en) 2019-10-17
EP3486340A1 (fr) 2019-05-22
JPWO2018012326A1 (ja) 2018-07-12
EP3486340A4 (fr) 2019-11-20
TW201816140A (zh) 2018-05-01

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