US20190316241A1 - Aluminum alloy plastic working material and production method therefor - Google Patents

Aluminum alloy plastic working material and production method therefor Download PDF

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Publication number
US20190316241A1
US20190316241A1 US16/316,974 US201716316974A US2019316241A1 US 20190316241 A1 US20190316241 A1 US 20190316241A1 US 201716316974 A US201716316974 A US 201716316974A US 2019316241 A1 US2019316241 A1 US 2019316241A1
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Prior art keywords
aluminum alloy
plastic working
phase
working material
alloy plastic
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US16/316,974
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English (en)
Inventor
Jun Yu
Yasuo Ishiwata
Dalsuke SHiMOSAKA
Takutoshi KONDO
Yoshihiro Taguchi
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Nippon Light Metal Co Ltd
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Nippon Light Metal Co Ltd
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Assigned to NIPPON LIGHT METAL COMPANY, LTD. reassignment NIPPON LIGHT METAL COMPANY, LTD. ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: KONDO, TAKUTOSHI, SHIMOSAKA, DAISUKE, TAGUCHI, YOSHIHIRO, ISHIWATA, YASUO, YU, JUN
Publication of US20190316241A1 publication Critical patent/US20190316241A1/en
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    • 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
    • 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 an aluminum alloy plastic working material which has a low Young's modulus, but has an excellent proof stress, and relates to a method for producing the working material.
  • aluminum Since aluminum has many excellent characteristics such as corrosion resistance, electric conductivity, thermal conductivity, light weight, brightness and machinability, aluminum is used for various purposes. In addition, since plastic deformation resistance is small, various shapes can be imparted, and aluminum is also widely used for members subjected to plastic working such as bending processing.
  • Patent Literature 1 JP 2011-105982 A proposes an aluminum alloy containing an Al phase and an Al 4 Ca phase, wherein the Al 4 Ca phase contains an Al 4 Ca crystallized product, and an average value of the longer side of the Al 4 Ca crystallized product is 50 ⁇ m or less.
  • Patent Literature 1 JP 2011-105982 A
  • an object of the present invention is to provide an aluminum alloy plastic working material which has a low Young's modulus, but has an excellent proof stress, and relates to a method for efficiently producing the working material.
  • the present invention is to provide an aluminum alloy plastic working material, which comprises:
  • a volume ratio of an Al 4 Ca phase, which is a 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
  • an intensity ratio (I 1 /I 2 ) of the highest diffraction peak (I 1 ) attributed to the tetragonal system to the highest diffraction peak (I 2 ) attributed to the monoclinic system, which are obtained by an X-ray diffraction measurement, is 1 or less.
  • the crystal structure of the Al 4 Ca phase which is used as the dispersed phase is basically a tetragonal crystal
  • the present inventors have intensively studied and found that when the crystal structure of the Al 4 Ca phase contains a monoclinic crystal, the proof stress do not decrease so much, but the Young's modulus is greatly decreased.
  • the intensity ratio (I 1 /I 2 ) of the highest diffraction peak (I 1 ) attributed to the tetragonal system to the highest diffraction peak (I 2 attributed to the monoclinic system, which are obtained by an X-ray diffraction measurement is 1 or less, the Young's modulus can be greatly lowered while maintaining the proof stress.
  • the aluminum alloy plastically working material of the present invention further contains at least one or more of Fe: 0.05 to 1.0 wt % and Ti: 0.005 to 0.05 wt %.
  • the casting property can be improved by broadening the solidification temperature range (solid-liquid coexisting region), and thus the casting surface of the ingot can also be improved. Further there is an effect that the dispersed crystallized product of Fe makes the eutectic structure uniform. The effect becomes remarkable when the Fe content is 0.05 wt % or more. To the contrary, when contained in excess of 1.0 wt %, the eutectic structure becomes coarse and there is a risk to lower the proof stress.
  • Ti acts as a refining material of the casted structure and exhibits an action to improve casting property, extrudability, and rolling property. The effect is remarkable when the Ti content is 0.005 wt % or more. To the contrary, even when added in excess of 0.05 wt %, it cannot be expected to increase the effect of refining the casted structure, and on the contrary, there is a risk that a coarse intermetallic compound which is to be the starting point of fracture may be generated. It is preferable that Ti is added by a rod hardener (Al—Ti—B alloy) during the casting. B added at this time together with Ti as the rod hardener is acceptable.
  • a rod hardener Al—Ti—B alloy
  • an average crystal grain size of the Al 4 Ca phase is 1.5 ⁇ m or less.
  • the average grain size of the Al 4 Ca phase becomes too large, the proof stress of the aluminum alloy decreases, but when the average grain size is 1.5 ⁇ m or less, it is possible to suppress the decrease of the proof stress.
  • the present invention provides a method for producing an aluminum alloy plastic working material, comprising:
  • a first step for obtaining a plastic workpiece of an aluminum alloy by subjecting an aluminum alloy ingot which contains 5.0 to 10.0 wt % of Ca with the remainder aluminum and inevitable impurities, and has a volume ratio of an Al 4 Ca phase which is a dispersed phase of 25% or more to a plastic processing, and
  • the first step for obtaining a plastic workpiece of an aluminum alloy by subjecting an aluminum alloy ingot which contains 5.0 to 10.0 wt % of Ca with the remainder aluminum and inevitable impurities, and has a volume ratio of an Al 4 Ca phase which is a dispersed phase of 25% or more to a plastic processing by conducting the step for subjecting to a heat treatment in a temperature range of 100 to 300° C. (Second step), a part of the tetragonal Al 4 Ca phase can be changed into monoclinic crystal.
  • the holding temperature in the second step is less than 100° C., a change from a tetragonal to a monoclinic crystal is difficult to occur, and when the holding temperature is 300° C. or more, recrystallization of the aluminum base material occurs and there is a risk that the proof stress will be lowered.
  • the more preferable temperature range of the heat treatment is 160 to 240° C. Though the appropriate time for the heat treatment varies depending on the size and shape of the aluminum alloy material, it is preferable that the temperature of the aluminum alloy material itself is kept at least at the holding temperature for 1 hour or more.
  • the aluminum alloy ingot contains at least one or more of Fe: 0.05 to 1.0 wt % and Ti: 0.005 to 0.05 wt %.
  • the casting property can be improved by broadening the solidification temperature range (solid-liquid coexisting region), and thus the casting surface of the ingot can also be improved. Further there is an effect that the dispersed crystallized product of Fe makes the eutectic structure uniform. The effect becomes remarkable when the Fe content is 0.05 wt % or more. To the contrary, when contained in excess of 1.0 wt %, the eutectic structure becomes coarse and there is a risk to lower the proof stress.
  • Ti acts as a refining material of the casted structure and exhibits an action to improve casting property, extrudability, and rolling property. The effect is remarkable when the Ti content is 0.005 wt % or more. To the contrary, even when added in excess of 0.05 wt %, it cannot be expected to increase the effect of refining the casted structure, and on the contrary, there is a risk that a coarse intermetallic compound which is to be the starting point of fracture may be generated. It is preferable that Ti is added by a rod hardener (Al—Ti—B alloy) during the casting. B added at this time together with Ti as the rod hardener is acceptable.
  • a rod hardener Al—Ti—B alloy
  • the aluminum alloy ingot is not subjected to a heat treatment where the ingot is maintained at a temperature of 400° C. or more.
  • a homogenization treatment is carried out where the ingot is held at a temperature of 400 to 600° C., but when this homogenization treatment is performed, the Al 4 Ca phase contained in the aluminum alloy tends to be large, and the average grain size becomes larger than 1.5 ⁇ m. Since the proof stress reduces due to the increase in the average grain size, it is preferable that the homogenization treatment at a holding temperature of 400° C. or higher would not be performed.
  • an aluminum alloy plastic working material which has both an excellent proof stress and a low Young's modulus, and a method for efficiently producing the working material.
  • FIG. 1 is a process chart relating to the method of producing the aluminum alloy plastic working material of the present invention.
  • FIG. 2 is an X-ray diffraction pattern of the aluminum alloy plastic working material.
  • FIG. 3 is a photograph of the structure of the present aluminum alloy plastic working material 3.
  • FIG. 4 is a photograph of the structure of the comparative aluminum alloy plastic working material 3.
  • the aluminum alloy plastic working material includes 5.0 to 10.0 wt % of Ca, and the remainder aluminum and unavoidable impurities.
  • Ca forms a compound of Al 4 Ca and has the activity to lower the Young's modulus of the aluminum alloy.
  • the effect becomes remarkable when the content of Ca is 5.0% or more.
  • the casting property decreases, and since particularly casting by continuous casting such as DC casting becomes difficult, it is necessary to produce by a method with a high production cost such as powder metallurgy method.
  • powder metallurgy method there is a risk that oxides formed on the surface of the alloy powder may get mixed in the product, which may lower the proof stress.
  • the casting property can be improved by broadening the solidification temperature range (solid-liquid coexisting region), and thus the casting surface of the ingot can also be improved. Further there is an effect that the dispersed crystallized product of Fe makes the eutectic structure uniform. The effect becomes remarkable when being 0.05 wt % or more, and to the contrary, when contained in excess of 1.0 wt %, the eutectic structure becomes coarse and there is a risk to lower the proof stress.
  • Ti acts as a refining material of the casted structure and exhibits an action to improve casting property, extrudability, and rolling property.
  • the effect is remarkable when being 0.005 wt % or more, and to the contrary, even when added in excess of 0.05 wt %, it cannot be expected to increase the effect of refining the casted structure, and on the contrary, there is a risk that a coarse intermetallic compound which is to be the starting point of fracture may be generated.
  • Ti is added by a rod hardener (Al—Ti—B alloy) during the casting. B added at this time together with Ti as the rod hardener is acceptable.
  • the aluminum alloy plastic working material has a volume ratio of an Al 4 Ca phase, which is a 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, and an intensity ratio (I 1 /I 2 ) of the highest diffraction peak (I 1 ) attributed to the tetragonal system to the highest diffraction peak (I 2 ) attributed to the monoclinic system, which are obtained by an X-ray diffraction measurement, is 1 or less.
  • the tetragonal Al 4 Ca phase and the monoclinic Al 4 Ca phase exist in the Al 4 Ca phase, which is a dispersed phase, and the volume ratio of the combined Al 4 Ca phase is 25% or more.
  • the volume ratio of the Al 4 Ca phase is 25% or more, it is possible to impart an excellent proof stress to the aluminum alloy plastic working material.
  • an average crystal grain size of the Al 4 Ca phase is 1.5 ⁇ m or less.
  • the average grain size of the Al 4 Ca phase exceeds 1.5 ⁇ m, there is a risk that the proof stress of the aluminum alloy plastic working material decreases.
  • the crystal structure of the Al 4 Ca phase is generally a tetragonal crystal
  • the present inventors have intensively studied and found that when the monoclinic crystal structure exists in the Al 4 Ca phase, the proof stress do not almost decrease, but the Young's modulus is greatly decreased. It is not necessary that all crystal structure of the Al 4 Ca phases is monoclinic, and it may be in the state of being mixed with the tetragonal crystal.
  • the existence of the Al 4 Ca phase which has the monoclinic crystal structure can be identified, for example, by measuring the diffraction peak with X ray diffraction method.
  • the intensity ratio (I 1 /I 2 ) of the highest diffraction peak (I 1 ) attributed to the tetragonal system to the highest diffraction peak (I 2 ) attributed to the monoclinic system can generally be obtained by a X-ray diffraction measurement.
  • FIG. 1 shows a process chart of the aluminum alloy plastic working material of the present invention.
  • the method for producing the aluminum alloy plastic working material of the present invention includes a first step (S 01 ) of subjecting an aluminum alloy ingot to plastic working, and a second step (S 02 ) of applying a heat treatment. Each step and the like will be explained herein below.
  • the molten metal After subjecting the aluminum alloy molten metal having the composition of the above-mentioned aluminum alloy plastic working material of the present invention to conventionally known molten metal cleaning treatments such as desulfurization treatment, degassing treatment, and filtration treatment, the molten metal is casted into an ingot having a desired shape.
  • the casting method there is no particular restriction on the casting method, and various conventionally known casting methods can be used. For example, it is preferable, by using a continuous casting method such as DC casting, to cast into a shape that the plastic working (extrusion, rolling, forging, etc.) in the first step (S 01 ) is easy to be performed.
  • a rod hardener Al—Ti—B
  • Al—Ti—B a rod hardener
  • a homogenization treatment is carried out where the ingot is held at a temperature of 400 to 600° C., but when this homogenization treatment is performed, the Al 4 Ca phase tends to be large (average grain size of 1.5 ⁇ m or larger), and since the proof stress of the aluminum alloy reduces, it is preferable that the homogenization treatment would not be performed in the method for producing aluminum alloy plastic working material according to the present invention.
  • the first step (S 01 ) is a step of subjecting the aluminum alloy ingot obtained in (1) to the plastic working to obtain a desired shape.
  • either hot working or cold working may be used, or a plurality of them may be combined.
  • the aluminum alloy becomes a processed structure, and the proof stress is improved.
  • most Al 4 Ca phases contained in the aluminum alloy have the tetragonal crystal structure.
  • the second step (S 02 ) is a step for applying the heat treatment to the aluminum alloy plastic working material obtained in the first step (S 01 ).
  • the holding temperature of the heat treatment is preferably 100 to 300° C., more preferably 160 to 240° C.
  • the temperature of at least the aluminum alloy plastic working material is kept at the above holding temperature for 1 hour or more.
  • An aluminum alloy having the composition shown Table 1 was cast into an ingot (billet) of ⁇ 8 inches by a DC casting method without any homogenization treatment, and then, plastic-working at an extrusion temperature of 500° C. to obtain a plate having a width of 180 mm ⁇ a thickness of 8 mm. Then, after cold rolling to a thickness of 5 mm, a heat treatment was carried out to hold at 200° C. for 4 hours to obtain the present aluminum alloy working plastic material.
  • the obtained present aluminum alloy plastic working material 3 was subjected to the X-ray diffraction measurement to measure the position pf the peak of the Al 4 Ca phase.
  • a specimen of 20 mm ⁇ 20 mm was cut out from the plate-like aluminum alloy plastic working material, the surface layer portion was removed by about 500 ⁇ m, and then a ⁇ -2 ⁇ measurement was carried out with respect to the region from a Cu—K ⁇ beam source. The results are shown in FIG. 2 .
  • the intensity ratio (I 1 /I 2 ) of the highest diffraction peak (I 1 ) attributed to the tetragonal system to the highest diffraction peak (I 2 ) attributed to the monoclinic system was 0.956.
  • the present aluminum alloy plastic working materials 6 to 9 were obtained in the same manner as in the case of the present aluminum alloy plastic working material 3 except that the heat treatment temperature was any one of 100° C., 160° C., 240° C. and 300° C.
  • the Young's modulus and proof stress were measured by a tensile test. The obtained results are shown in Table 3.
  • An aluminum alloy having the composition shown Table 1 was cast into an ingot (billet) of ⁇ 8 inches by a DC casting method without any homogenization treatment, and then, plastic-working at an extrusion temperature of 500° C. to obtain a plate having a width of 180 mm ⁇ a thickness of 8 mm. Thereafter, the cold rolling to a thickness of 5 mm was carried out to obtain the comparative aluminum alloy plastic working materials 1 to 5.
  • the obtained comparative aluminum alloy plastic working material 3 was subjected to the X-ray diffraction measurement to measure the position pf the peak of the Al 4 Ca phase.
  • a specimen of 20 mm ⁇ 20 mm was cut out from the plate-like aluminum alloy plastic working material, the surface layer portion was removed by about 500 ⁇ m, and then a ⁇ -2 ⁇ measurement was carried out with respect to the region from a Cu—K ⁇ beam source.
  • the results are shown in FIG. 2 .
  • the intensity ratio (I 1 /I 2 ) of the highest diffraction peak (I 1 ) attributed to the tetragonal system to the highest diffraction peak (I 2 ) attributed to the monoclinic system was 1.375.
  • the comparative aluminum alloy plastic working materials 6 and 7 were obtained in the same manner as in the case of the present aluminum alloy plastic working material 3 except that the heat treatment temperature was 90° C. and 310° C.
  • the Young's modulus and proof stress were measured by a tensile test. The obtained results are shown in Table 3.
  • the comparative aluminum alloy plastic working material 8 was obtained in the same manner as in the case of the present aluminum alloy plastic working material 3 except that, after casting in an ingot (billet), the homogenization treatment was carried out while holding at 550° C.
  • JIS-14B specimen was cut out from the comparative aluminum alloy plastic working material 8, and the Young's modulus and proof stress were measured by a tensile test. The obtained results are shown in Table 4.
  • the Young's modulus and the proof stress of the present aluminum alloy plastic working material 3 which is different only in the presence or absence of homogenization treatment are also shown as comparison data.
  • the Young's modulus of the aluminum alloy plastic working materials of the present invention (the present aluminum alloy plastic working materials 1 to 5) are greatly lower than the Young's modulus of the comparative aluminum alloy plastic working materials 1 to 5 which were not subjected to the heat treatment.
  • the proof stress and tensile strength of the present aluminum alloy plastic working materials 1 to 5 are not greatly reduced as compared with the comparative aluminum alloy plastic working materials 1 to 5. It is clear that the volume ratios of the dispersed phase (Al 4 Ca phase) in the aluminum alloy plastic working materials of the present invention are 25% or more.
  • FIG. 3 and FIG. 4 The structural photographs of the present aluminum alloy plastic working material 3 and the comparative aluminum alloy plastic working material 8 by an optical microscope are shown in FIG. 3 and FIG. 4 , respectively.
  • the black region is the Al 4 Ca phase
  • the average crystal grain size of the Al 4 Ca phase is measured by image analysis. The obtained results are shown in Table 4.

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PCT/JP2017/024184 WO2018012326A1 (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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EP4339316A1 (en) * 2021-05-14 2024-03-20 LG Electronics Inc. Aluminum alloy, method for manufacturing same, and parts using same
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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GB1452646A (en) * 1974-11-13 1976-10-13 Euratom Aluminium based alloy
JPS60194039A (ja) * 1984-03-14 1985-10-02 Toyota Central Res & Dev Lab Inc 繊維強化アルミニウム合金複合材料および製造方法
AU5148596A (en) * 1995-03-31 1996-10-16 Merck Patent Gmbh Tib2 particulate ceramic reinforced al-alloy metal-matrix co mposites
JP5305067B2 (ja) * 2007-09-14 2013-10-02 日産自動車株式会社 アルミニウム合金からなる応力緩衝材料
JP5287171B2 (ja) * 2008-11-25 2013-09-11 日産自動車株式会社 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
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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ASM Handbook Annealing of Aluminum and Its Alloys, Volume 4E (Year: 2016) *

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TWI718319B (zh) 2021-02-11
EP3486340B1 (en) 2021-01-27
JP6341337B1 (ja) 2018-06-13
KR102444566B1 (ko) 2022-09-20
WO2018012326A1 (ja) 2018-01-18
TW201816140A (zh) 2018-05-01
CN109477169B (zh) 2021-03-26
KR20190028472A (ko) 2019-03-18
EP3486340A4 (en) 2019-11-20
CN109477169A (zh) 2019-03-15
EP3486340A1 (en) 2019-05-22

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