WO2005118900A1 - Alliage de magnésium résistant au fluage - Google Patents

Alliage de magnésium résistant au fluage Download PDF

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Publication number
WO2005118900A1
WO2005118900A1 PCT/JP2005/006007 JP2005006007W WO2005118900A1 WO 2005118900 A1 WO2005118900 A1 WO 2005118900A1 JP 2005006007 W JP2005006007 W JP 2005006007W WO 2005118900 A1 WO2005118900 A1 WO 2005118900A1
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WO
WIPO (PCT)
Prior art keywords
alloy
sample
creep
mass
present
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Application number
PCT/JP2005/006007
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English (en)
Japanese (ja)
Inventor
Hiroyuki Omura
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Ryobi 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 Ryobi Ltd. filed Critical Ryobi Ltd.
Publication of WO2005118900A1 publication Critical patent/WO2005118900A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C23/00—Alloys based on magnesium
    • C22C23/02—Alloys based on magnesium with aluminium as the next major constituent
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
    • B22D21/002—Castings of light metals
    • B22D21/007—Castings of light metals with low melting point, e.g. Al 659 degrees C, Mg 650 degrees C

Definitions

  • the present invention relates to a creep-resistant magnesium alloy, and particularly to a creep-resistant magnesium alloy having excellent creep resistance and corrosion resistance required for use in a high-temperature environment and free from structural defects such as structural cracks and excellent die-casting properties. About.
  • an Mg-A1-Ca alloy As an alloy used as a material for automobile parts, an Mg-A1-Ca alloy is known. Recently, an Mg-A 1 -Ca-Sr-Mn alloy has been proposed (for example, see Patent Document 1). This alloy has excellent creep resistance and corrosion resistance, with A1 of 2.0 to 6.0% by mass. & Is 0.3 to 2.0%, 3]: is 0.01 to 1.0%, Mn is 0.1 to 1.0%, and the balance is Mg and impurities. In addition, Si was added to the above alloy in an amount of 0.
  • an Mg-Al-Si-Sn-based alloy has been proposed (for example, see Patent Document 2).
  • This alloy contains 0.01 to 4.0% of A1 by mass, 0.2 to 2.0% of 31 and 6.0 to 20.0% of Sn, and the balance consists of Mg and impurities. Alloy.
  • Patent document 1 JP 2001-316675A
  • Patent Document 2 JP-A-7-3374
  • the creep resistance decreases and cracks occur.
  • the corrosion resistance of the Mg-A1-Si-Sn-based alloy is very inferior to that of the Mg-A1-Ca-Sr-Mn-based alloy.
  • an object of the present invention is to provide a creep-resistant magnesium alloy excellent in creep resistance, corrosion resistance and die-casting property.
  • the present invention relates to the following: A1 is 2.5 to 6.5% by mass; Ca is 0.3 to 3.0% by mass; Sn is 0.15 to 3.0% by mass; It provides a creep-resistant magnesium alloy containing 0.1 to 0.5% by mass, with the balance being Mg and unavoidable impurities.
  • A1 is 2.5 to 6.5% by mass
  • Ca is 0.3 to 3.0% by mass
  • Sn is 0.15 to 3.0% by mass
  • It provides a creep-resistant magnesium alloy containing 0.1 to 0.5% by mass, with the balance being Mg and unavoidable impurities.
  • the S r 0. from 01 to 0. It preferably contains 3 mass 0/0.
  • the machinability is further improved, and the effect of preventing machinability cracks and grain boundary cracks is further improved.
  • FIG. 1 (a) is a front view showing the shape of a test piece used for evaluation of cracking performance in experiment 1.
  • FIG. 1 (b) is a side view showing the shape of a test piece used in the evaluation of cracking performance in experiment 1.
  • FIG. 2 is a view showing a measurement result regarding an evaluation of a crack resistance of a creep-resistant magnesium alloy according to an embodiment of the present invention and a comparative material by Experiment 1.
  • FIG. 3 is a view showing the shape of a test piece used in the creep resistance test in Experiment 2.
  • FIG. 4 is a side view showing a state of a creep resistance test in Experiment 2.
  • FIG. 5 is a side view showing a method for measuring the displacement of a test piece in the creep resistance test of Experiment 2.
  • FIG. 6 is a view showing the measurement results of a creep resistance experiment I of the creep-resistant magnesium alloy and the comparative material according to the embodiment of the present invention.
  • FIG. 7 is a view showing the measurement results of a creep resistance experiment II of the creep resistant magnesium alloy and the comparative material according to the embodiment of the present invention.
  • FIG. 8 Experiment 3 of creep-resistant magnesium alloy and comparative material according to the embodiment of the present invention. The figure which shows the measurement result regarding the corrosion resistance experiment of FIG.
  • FIG. 9 is a view showing a result of an E PMA analysis of a creep-resistant magnesium alloy according to an embodiment of the present invention.
  • FIG. 10 is a view showing the measurement results of the creep resistance test of the creep-resistant magnesium alloy according to the embodiment of the present invention and the comparative material in Experiment 4.
  • FIG. 11 is a microstructure photograph of an Mg—A1-Ca—Mn-based alloy that is a comparative material for a creep-resistant magnesium alloy according to an embodiment of the present invention.
  • FIG. 12 is a microstructure photograph of a creep-resistant magnesium alloy according to an embodiment of the present invention.
  • FIG. 13 is a view showing the shape of a test piece used in the creep resistance test in Experiment 5.
  • FIG. 14 is a view showing a state of a creep resistance test in Experiment 5.
  • FIG. 15 Diagrams showing the results of measurements of the creep resistance test of the creep-resistant magnesium alloy and the comparative material in Experiment 5.
  • a 1 (aluminum) has a mass of 2.5 to 6.5 mass 0 /.
  • the C a (calcium) is 0.3-3.0 mass 0 /.
  • the Sn (tin) is 0.15-3.0 mass 0 /.
  • Mn manganese
  • S r sinrontium
  • Al, Ca, Sn, Mn, and Mg are essential elements, and Sr is an optional element.
  • the amount of A1 added is 6.0 mass. If the ratio exceeds / 0 , a large amount of the Mg 17 Al 12 compound is crystallized, so that high creep resistance cannot be obtained. Therefore, the amount of A1 added was set to 6.0% by mass or less. On the other hand, if the addition amount of A1 is less than 2.5% by mass, the formability such as the fluidity of the molten metal decreases, and the die casting becomes difficult. Therefore, the amount of A1 added was set to 2.5% by mass or more.
  • Addition of Ca improves the flame retardancy of the Mg alloy, and enables forging even at a somewhat high melt temperature. However, if it is added too much, it tends to cause structural cracking and seizure, Goods are not obtained. If the added amount of Ca exceeds 3.0% by mass, it is easy to cause cracking and seizure to a mold, and it is not possible to obtain a sound product. Therefore, the addition amount of Ca was set to 3.0 mass ° / 0 or less. On the other hand, the added amount of Ca was 0.3 mass. If it is less than / 0 , sufficient creep resistance cannot be obtained. Therefore, the addition amount of Ca was set to 0.3% by mass or more.
  • Addition of Mn has an effect on the corrosion resistance, but if the addition amount of Mn exceeds 0.5% by mass, the die-casting becomes difficult due to deterioration of the formability such as seizure to a mold. Therefore, the added amount of Mn is 0.5 mass. / 0 or less. On the other hand, if the added amount of Mn is less than 0.1% by mass, the corrosion resistance decreases. Therefore, the added amount of Mn is 0.1 mass. / 0 or more.
  • a small amount of Sr has little effect on creep resistance, but the addition of Sr improves the morphology of the Mg alloy and prevents grain boundary cracking and the like. If the added amount of Sr exceeds 0.3% by mass, seizure or the like tends to occur. Therefore, the addition amount of Sr was set to 0.3% by mass or less. On the other hand, the amount of Sr added was 0.01 mass. If the ratio is less than / 0 , the effect on shrinkage cracks and grain boundary cracks cannot be obtained. Therefore, the amount of Sr added was set to 0.01% by mass or more.
  • Table 1 shows the composition ratio of the samples used in the experiment.
  • Sample 1 and Sample 2 are alloys described in JP-A-2001-316752
  • Sample 3 is an alloy described in JP-A-7-3374
  • Samples 4 and 5 are Samples 6 and 7 are alloys according to an embodiment of the invention
  • Sample 8 is an ADC12 alloy
  • Sample 9 is an AZ9 ID alloy, in which the weight percent is outside the scope of the embodiments of the present invention.
  • the alloy of the embodiment of the present invention and the comparative material were evaluated for crackability.
  • Sample 1 shown in Table 1 (alloy_1 of JP-A-2001-31 6752), sample 4 (alloy-1 of the present embodiment-1), sample 5 (alloy-1 of the present embodiment 2), sample 6 and Using each of Sample 7 (an alloy in which the added mass% of Sn is out of the range of the present invention) and the four types of manufacturing conditions shown in Table 2, the shapes shown in FIGS. 1 (a) and 1 (b) were used. Specimens were fabricated and the cracking rate was examined.
  • the shape of the specimen 1 in FIGS. 1 (a) and 1 (b) is such that the length of the parallel portion is 105 mm and the corner R of the constrained end has a radius of curvature Omm.
  • Table 2 The shape of the specimen 1 in FIGS. 1 (a) and 1 (b) is such that the length of the parallel portion is 105 mm and the corner R of the constrained end has a
  • a test piece 2 as shown in FIG. 3 was manufactured using (the alloy 1 of the present embodiment 1) and the sample 8 (ADC 12).
  • samples 1 and 2 (alloys 1 and 2 of JP-A-2001-3166752), sample 3 (alloy of JP-A-7-3374), and sample 4 (alloys 1 and 2 of this embodiment) were used.
  • Sample 8 (ADC 12) and Sample 9 (AZ91D) were used to fabricate a test piece 2 as shown in FIG.
  • Test piece 2 was an ASTM B-85 tensile test piece (parallel diameter 6.35 mm, distance between gauges 57.5 mm, length 21 Omm).
  • Sample 4 (Alloy-1 of this embodiment) is superior to that of Sample 1 (Alloy-1 of JP-A-2001-3166752), and Sample 3 (Alloy-1 of JP-A-7-3374) You can see that it is much better than).
  • Sample 4 (alloy 1 of this embodiment) is considered to have improved creep resistance due to the addition of Ca and Sn, and the same creep resistance as sample 8 (ADC 12), which is an aluminum die-cast alloy was gotten.
  • Sample 2 (alloy No. 1 in JP-A-2001-316752) is considered to have reduced creep resistance due to the addition of Si.
  • the addition of Ca and Si improves the creep resistance.However, when both are used together, the effect is not obtained, and conversely, the creep resistance is considered to decrease.
  • the solid solution range for Mg is extremely narrow, so that it does not form a solid solution, but Sn dissolves well in Mg and forms a solid solution with Mg,
  • FIG. 8 shows the results.
  • the corrosion resistance of Sample 4 (alloy-1 of the present embodiment) and Sample 5 (alloy-1 of the present embodiment) was as shown in Sample 2 (Japanese Unexamined Patent Publication No. 2001-31).
  • sample 7 (adding 0.35% by mass of Sn) was inferior to that of sample 5 (alloy No. 2 of the present embodiment), and the amount of Sn added exceeded 3.0%.
  • the corrosion resistance is expected to decrease. This is thought to be due to the crystallization of intermetallic compounds that adversely affect corrosion resistance.
  • E PMA analysis was performed on the alloy according to the embodiment of the present invention.
  • the composition of the sample analyzed was Mg-4.5% A1-1.7% Ca-0.15% Mn-0.7% Sn, and the results are shown in FIG.
  • Sn partially dissolved in the Mg matrix, and Sn was crystallized at the grain boundaries.
  • S n at the grain boundaries, not put out Mg Ha Mari crystal, A 1 2 C a and S n compounds gave the grain boundary crystallized.
  • it is a force S Mg Ca-based compound in which crystallization of Mg is partially observed.
  • Al 2 Ca was crystallized in the form of links in the matrix, and a structure effective for creep resistance was obtained.
  • Samples 10 and 11 are Mg-A1-Ca-Mn-based alloys as comparative materials
  • Sample 12 is an alloy having the same composition as the sample subjected to EPMA analysis
  • Sample 13 Is an alloy according to an embodiment of the present invention
  • Sample 14 is an ADC 12 alloy.
  • Three specimens were prepared for one sample, and all the specimens were tested.
  • Figure 10 shows the displacement of each test piece and the average value of each sample. From Fig. 10, creep resistance of Samples 12 and 13 is better than Samples 10 and 11. You can see that.
  • FIGS. 11 and 12 show microstructure photographs of Samples 11 and 12, respectively.
  • sample 11 has many cracks at the grain boundaries.
  • the Mg_Al-Ca-Mn alloy is considered to have cracked because the grain boundaries are extremely unstable.
  • FIG. 12 no grain boundary crack was observed in Sample 12, which is the alloy of the present embodiment.
  • the S n added Caro the modification effect of the grain boundary, such as A 1 2 C a crystallizes in the grain boundary was observed.
  • Table 4 shows the samples used in the experiment.
  • Sample 15 is an alloy according to an embodiment of the present invention
  • Sample 16 is an alloy outside the scope of the present invention
  • Sample 17 is an ADC12 alloy
  • Sample 18 is an AZ91D alloy.
  • the test piece 10 used in the experiment had a parallel part diameter of 6.0 mm, 0.1 mm, a distance between gauge points of 52 mm, and a length of 15 Omm.
  • Specimen 10 was produced by producing under the production conditions shown in Condition 4 of Table 2. Then, as shown in Fig. 14, the test piece was placed in the preheating furnace 11 set at 150 ° C, the strain gauge 12 was fixed to the test piece 10, a load of 35 MPa was applied, and the strain was measured at each elapsed time. did.
  • Table 4 shows the samples used in the experiment.
  • Sample 15 is an alloy according to an embodiment of the present invention
  • Sample 16 is an alloy outside the scope of the present invention
  • Sample 17 is an ADC12 alloy
  • Sample 18 is an AZ
  • Figure 15 shows the results of the creep test of Experiment 5. As can be seen from the results of Samples 15 and 16, it was recognized that the addition of Sn improved the creep resistance. In addition, it can be seen that the creep resistance of the sample 15 which is the alloy according to the present embodiment is superior to the sample 17 which is the ADC12 alloy. This is believed to thermally From Jona A 1 2 C a compound S n addition as described above is because you put the grain boundary crystallized.
  • the creep-resistant magnesium alloy according to the present invention is not limited to the above embodiment, and various modifications and improvements can be made within the scope described in the claims. '
  • the creep-resistant magnesium alloy of the present invention can be used as an alloy used as a material for automobile parts.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Prevention Of Electric Corrosion (AREA)
  • Continuous Casting (AREA)

Abstract

Il est prévu un alliage de magnésium résistant au fluage, de la composition chimique suivante, en % de masse, Al: 2,5 à 6,5 %, Ca: 0,3 à 3,0%, Sn: 0,15 à 3,0 %, Mn: 0,1 à 0,5 % et le reste : Mg et les inévitables impuretés. Autre possibilité, l’alliage de magnésium comprend en outre 0,01 à 0,3 % en masse de Sr. L’échantillon 4, qui est un mode de réalisation de l’alliage de magnésium ci-dessus résistant au fluage, présente une résistance au fluage supérieure à celles de l’échantillon 1 et de l’échantillon 2 (l’alliage-1,2 dans JP 2001-316752 A), l’échantillon 3 (l’alliage dans JP 07-3374 A) et l’échantillon 9 (AZ91D).
PCT/JP2005/006007 2004-06-03 2005-03-23 Alliage de magnésium résistant au fluage WO2005118900A1 (fr)

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JP2004166323A JP2007270159A (ja) 2004-06-03 2004-06-03 耐クリープマグネシウム合金
JP2004-166323 2004-06-03

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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPWO2016136781A1 (ja) * 2015-02-26 2017-12-21 株式会社栗本鐵工所 耐熱マグネシウム合金
CN113981286A (zh) * 2021-11-01 2022-01-28 吉林大学 一种耐蚀高强塑性镁合金及其制备方法

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP4852082B2 (ja) * 2008-09-29 2012-01-11 株式会社豊田中央研究所 マグネシウム合金
JP5894079B2 (ja) * 2009-12-07 2016-03-23 ユー アンド アイ コーポレーション マグネシウム合金
CN103290290A (zh) * 2013-06-26 2013-09-11 重庆大学 一种低成本变形镁合金及其制备方法
JP7315941B2 (ja) * 2018-10-03 2023-07-27 地方独立行政法人東京都立産業技術研究センター 粉末材料、及びマグネシウム合金部材の製造方法

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS613863A (ja) * 1984-06-15 1986-01-09 Ube Ind Ltd ダイカスト用マグネシウム基合金
US20030084968A1 (en) * 2001-11-05 2003-05-08 Boris Bronfin High strength creep resistant magnesium alloys
JP2004084066A (ja) * 2002-06-24 2004-03-18 Toyota Central Res & Dev Lab Inc マグネシウム合金多孔質体およびその製造方法

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS613863A (ja) * 1984-06-15 1986-01-09 Ube Ind Ltd ダイカスト用マグネシウム基合金
US20030084968A1 (en) * 2001-11-05 2003-05-08 Boris Bronfin High strength creep resistant magnesium alloys
JP2004084066A (ja) * 2002-06-24 2004-03-18 Toyota Central Res & Dev Lab Inc マグネシウム合金多孔質体およびその製造方法

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPWO2016136781A1 (ja) * 2015-02-26 2017-12-21 株式会社栗本鐵工所 耐熱マグネシウム合金
EP3263725A4 (fr) * 2015-02-26 2018-01-03 Kurimoto, Ltd. Alliage de magnésium résistant à la chaleur
US10550453B2 (en) 2015-02-26 2020-02-04 Kurimoto, Ltd. Heat-resistant magnesium alloy
CN113981286A (zh) * 2021-11-01 2022-01-28 吉林大学 一种耐蚀高强塑性镁合金及其制备方法
CN113981286B (zh) * 2021-11-01 2022-06-21 吉林大学 一种耐蚀高强塑性镁合金及其制备方法

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