JP2020200513A - Aluminum alloy material - Google Patents
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- JP2020200513A JP2020200513A JP2019109175A JP2019109175A JP2020200513A JP 2020200513 A JP2020200513 A JP 2020200513A JP 2019109175 A JP2019109175 A JP 2019109175A JP 2019109175 A JP2019109175 A JP 2019109175A JP 2020200513 A JP2020200513 A JP 2020200513A
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- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 41
- 239000000956 alloy Substances 0.000 title claims abstract description 30
- 239000000203 mixture Substances 0.000 claims abstract description 10
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 229910052742 iron Inorganic materials 0.000 abstract description 23
- 229910052802 copper Inorganic materials 0.000 abstract description 17
- 229910052749 magnesium Inorganic materials 0.000 abstract description 14
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 50
- 239000000463 material Substances 0.000 description 37
- 229910000765 intermetallic Inorganic materials 0.000 description 26
- 150000001875 compounds Chemical class 0.000 description 23
- 229910052759 nickel Inorganic materials 0.000 description 22
- 230000000694 effects Effects 0.000 description 20
- 229910052710 silicon Inorganic materials 0.000 description 18
- 238000004364 calculation method Methods 0.000 description 16
- 239000013078 crystal Substances 0.000 description 16
- 238000007711 solidification Methods 0.000 description 15
- 230000008023 solidification Effects 0.000 description 15
- 238000002485 combustion reaction Methods 0.000 description 13
- 239000006185 dispersion Substances 0.000 description 11
- 238000002425 crystallisation Methods 0.000 description 10
- 230000008025 crystallization Effects 0.000 description 10
- 239000011159 matrix material Substances 0.000 description 9
- 238000005266 casting Methods 0.000 description 8
- 239000012071 phase Substances 0.000 description 8
- 238000005728 strengthening Methods 0.000 description 8
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 7
- 238000005242 forging Methods 0.000 description 7
- 239000000654 additive Substances 0.000 description 6
- 230000000996 additive effect Effects 0.000 description 6
- 229910052782 aluminium Inorganic materials 0.000 description 6
- 238000009749 continuous casting Methods 0.000 description 6
- 239000000047 product Substances 0.000 description 6
- 230000032683 aging Effects 0.000 description 5
- 230000015572 biosynthetic process Effects 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 5
- 229910052751 metal Inorganic materials 0.000 description 5
- 239000002184 metal Substances 0.000 description 5
- 238000001556 precipitation Methods 0.000 description 5
- 229910002549 Fe–Cu Inorganic materials 0.000 description 4
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 4
- 238000005520 cutting process Methods 0.000 description 4
- 238000004519 manufacturing process Methods 0.000 description 4
- 238000000034 method Methods 0.000 description 4
- 229910052698 phosphorus Inorganic materials 0.000 description 4
- 239000010703 silicon Substances 0.000 description 4
- 229910052726 zirconium Inorganic materials 0.000 description 4
- 238000010438 heat treatment Methods 0.000 description 3
- 238000000265 homogenisation Methods 0.000 description 3
- 239000000843 powder Substances 0.000 description 3
- 238000010791 quenching Methods 0.000 description 3
- 229910052719 titanium Inorganic materials 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 239000012141 concentrate Substances 0.000 description 2
- 238000001125 extrusion Methods 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 230000000171 quenching effect Effects 0.000 description 2
- 239000011856 silicon-based particle Substances 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- 229910021364 Al-Si alloy Inorganic materials 0.000 description 1
- 229910001018 Cast iron Inorganic materials 0.000 description 1
- 229910018054 Ni-Cu Inorganic materials 0.000 description 1
- 229910018481 Ni—Cu Inorganic materials 0.000 description 1
- 229910008458 Si—Cr Inorganic materials 0.000 description 1
- 229910006639 Si—Mn Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 238000000889 atomisation Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 238000004512 die casting Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 229910001651 emery Inorganic materials 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 230000005484 gravity Effects 0.000 description 1
- 238000001192 hot extrusion Methods 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 239000011777 magnesium Substances 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 238000007747 plating Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 239000011347 resin Substances 0.000 description 1
- 229920005989 resin Polymers 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 238000005480 shot peening Methods 0.000 description 1
- 239000007790 solid phase Substances 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 238000004381 surface treatment Methods 0.000 description 1
- 239000013585 weight reducing agent Substances 0.000 description 1
Abstract
Description
この発明は、例えば４輪自動車用、２輪自動車用、汎用などの内燃機関部品に代表されるエンジンピストンやコンプレッサー、シリンダライナ、クランクシャフト、カムシャフト、エンジンブロック等として好適に用いられるアルミニウム合金材に関するものである。 The present invention is an aluminum alloy material suitably used as an engine piston, compressor, cylinder liner, crankshaft, camshaft, engine block, etc. represented by internal combustion engine parts for, for example, four-wheeled automobiles, two-wheeled automobiles, and general-purpose parts. It is about.
近年の自動車業界においては燃費の向上が強く求められており、それに伴って自動車に使用される各種部材例えば、内燃機関のピストンや、コンプレッサー等の軽量化および高機能化の要求が益々高まってきている。 In recent years, there has been a strong demand for improved fuel efficiency in the automobile industry, and along with this, there has been an increasing demand for weight reduction and high functionality of various components used in automobiles, such as pistons of internal combustion engines and compressors. There is.
このような自動車用の各種部材については、従来の鉄鋼材料や鋳鉄材料に代えて、重量に対する強度の比である比強度が高いアルミニウム合金材を使用する傾向が高くなっている。中でも特に高温雰囲気下等の過酷な環境でも耐え得る部材として、高温高強度を有するＡｌ−Ｓｉ系合金等のアルミニウム合金の鍛造材が注目されるようになっている。 For such various members for automobiles, there is a high tendency to use an aluminum alloy material having a high specific strength, which is a ratio of strength to weight, in place of the conventional steel material or cast iron material. Among them, forged aluminum alloys such as Al—Si alloys having high temperature and high strength have been attracting attention as members that can withstand harsh environments such as high temperature atmospheres.
この種のアルミニウム合金製鍛造材の製造方法としては、例えば特許文献１に記載されるように、所定の成分組成のアルミニウム合金溶湯をアトマイズ法等により急冷凝固した粉末に対し、熱間押出加工を行い、得られた押出材を型鍛造して所定の製品形状とすることが一般に行われている。 As a method for producing this kind of aluminum alloy forging material, for example, as described in Patent Document 1, hot extrusion processing is performed on a powder obtained by quenching and solidifying an aluminum alloy molten metal having a predetermined component composition by an atomization method or the like. It is generally practiced to mold-forge the obtained extruded material into a predetermined product shape.
ところで、上記特許文献１に示す従来のアルミニウム合金製鍛造材の製造方法のように、アルミニウム合金製のアトマイズ粉末の押出材を内燃機関用部品として用いる場合、アルミニウム粉末合金特有の、靭性が低いことに起因する脆性破壊が生じる恐れがある。 By the way, when an extruded material of atomized powder made of an aluminum alloy is used as a part for an internal combustion engine as in the conventional method for manufacturing an aluminum alloy forged material shown in Patent Document 1, the toughness peculiar to the aluminum powder alloy is low. There is a risk of brittle fracture due to.
そこで靭性の低下を避けるために、アルミニウム合金製のアトマイズ粉末の押出材を用いずに、従来の一般的な鋳造材を鍛造素材として型鍛造により内燃機関部品を成形する方法を選択する場合がある。しかしながらこの方法を選択した場合に、アルミニウム粉末合金に比べると強度不足が否めず、その強度不足を補うために添加元素を多量に添加すると粗大な金属間化合物を生成して、靭性の低下およびその靭性の低下に伴う引張強さや伸び等の機械的特性の低下が発生するという課題があった。 Therefore, in order to avoid a decrease in toughness, a method of molding an internal combustion engine part by mold forging using a conventional general cast material as a forging material may be selected without using an extruded material of atomized powder made of an aluminum alloy. .. However, when this method is selected, the strength is undeniably insufficient compared to the aluminum powder alloy, and when a large amount of additive elements are added to compensate for the insufficient strength, a coarse intermetallic compound is produced, resulting in a decrease in toughness and its strength. There has been a problem that mechanical properties such as tensile strength and elongation occur due to a decrease in toughness.
この発明は、上記の課題に鑑みてなされたものであり、高強度かつ高靭性のアルミニウム合金材を提供することを目的とする。 The present invention has been made in view of the above problems, and an object of the present invention is to provide an aluminum alloy material having high strength and high toughness.
上記課題を解決するため、本発明は、以下の手段を備えるものである。 In order to solve the above problems, the present invention provides the following means.
［１］Ｓｉ：１３質量％〜１５質量％、Ｃｕ：２．０質量％〜４．０質量％、Ｍｇ：０．２質量％〜０．８質量％、Ｆｅ：０．０５質量％〜０．６２質量％を含み、
Ｎｉを０．０５質量％以上かつ
Ｆｅ含有率が０．０５質量％〜０．４９質量％の場合には、
（Ｎｉ含有率［質量％］）≦６．２８−４．３３×（Ｆｅ含有率［質量％］）
Ｆｅ含有率が０．４９質量％〜０．６２質量％の場合には、
（Ｎｉ含有率［質量％］）≦２０．２９−３２．７２×（Ｆｅ含有率［質量％］）
で表される含有率で含み、残部がＡｌと不可避不純物からなる組成を有することを特徴とするアルミニウム合金材。
[1] Si: 13% by mass to 15% by mass, Cu: 2.0% by mass to 4.0% by mass, Mg: 0.2% by mass to 0.8% by mass, Fe: 0.05% by mass to 0 Contains .62% by weight
When Ni is 0.05% by mass or more and the Fe content is 0.05% by mass to 0.49% by mass,
(Ni content [mass%]) ≤6.28-4.33 × (Fe content [mass%])
When the Fe content is 0.49% by mass to 0.62% by mass,
(Ni content [mass%]) ≦ 20.29-32.72 × (Fe content [mass%])
An aluminum alloy material containing the content represented by (1) and having a composition in which the balance is composed of Al and unavoidable impurities.
［２］Ｐ：０．０００１〜０．０２質量％を含むことを特徴とする前項１に記載のアルミニウム合金材。 [2] The aluminum alloy material according to item 1 above, wherein P: contains 0.0001 to 0.02% by mass.
［３］Ｍｎ：０．０２〜０．３質量％、Ｃｒ：０．０２〜０．３質量％、Ｔｉ：０．０１〜０．１５質量％およびＺｒ：０．０１〜０．１５質量％のうち、少なくとも１種以上を含むことを特徴とする前項１または２に記載のアルミニウム合金材。 [3] Mn: 0.02 to 0.3% by mass, Cr: 0.02 to 0.3% by mass, Ti: 0.01 to 0.15% by mass and Zr: 0.01 to 0.15% by mass. The aluminum alloy material according to item 1 or 2 above, which comprises at least one of them.
上記［１］によれば、Ｓｉ、Ｃｕ、Ｍｇ、Ｆｅ、Ｎｉを所定量含有していることで、Ｓｉ粒子の分散による分散強化、Ａｌ−Ｓｉ−Ｆｅ−Ｎｉ−Ｃｕ系化合物の分散による分散強化およびＣｕ、Ｍｇ系の析出による析出強化等により高い強度を有するとともに、かつ初晶金属間化合物を生じないことによりアルミニウム合金特有の高い靭性を有するアルミニウム合金材が得られる。 According to the above [1], by containing a predetermined amount of Si, Cu, Mg, Fe, and Ni, dispersion strengthening by dispersion of Si particles and dispersion by dispersion of Al-Si-Fe-Ni-Cu based compound are performed. An aluminum alloy material having high strength due to strengthening and precipitation strengthening due to precipitation of Cu and Mg-based materials and having high toughness peculiar to aluminum alloys can be obtained by not producing primary intermetallic compounds.
上記［２］によれば、Ｐを所定量含有しているため、初晶Ｓｉの微細化および均一分散されたアルミニウム合金材が得られる。 According to the above [2], since P is contained in a predetermined amount, an aluminum alloy material in which primary crystal Si is finely dispersed and uniformly dispersed can be obtained.
上記［３］のアルミニウム合金材によれば、Ｍｎ、Ｃｒ、Ｔｉ、およびＺｒのうち少なくとも１種以上を所定量含有しているため、材料の機械的特性に優れた、および／または母相の結晶が微細化されたアルミニウム合金材が得られる。 According to the aluminum alloy material of the above [3], since at least one of Mn, Cr, Ti, and Zr is contained in a predetermined amount, the mechanical properties of the material are excellent and / or the matrix phase. An aluminum alloy material with finer crystals can be obtained.
この発明のアルミニウム合金材を実施するための形態について詳細に説明する。 A form for carrying out the aluminum alloy material of the present invention will be described in detail.
本発明のアルミニウム合金材は、Ｓｉ、Ｃｕ、Ｍｇ、Ｆｅ、Ｎｉを所定量含有し、残部がＡｌと不可避不純物からなる。 The aluminum alloy material of the present invention contains a predetermined amount of Si, Cu, Mg, Fe, and Ni, and the balance is Al and unavoidable impurities.
また本発明のアルミニウム合金材は、Ｐをさらに所定量含有することが好ましい。 Further, the aluminum alloy material of the present invention preferably further contains a predetermined amount of P.
また本発明のアルミニウム合金材は、Ｍｎ、Ｃｒ、ＴｉおよびＺｒのうち少なくとも１種以上をさらに所定量含有することが好ましい。 Further, the aluminum alloy material of the present invention preferably further contains at least one of Mn, Cr, Ti and Zr in a predetermined amount.
本発明のアルミニウム合金材を構成する各元素について、以下に説明する。 Each element constituting the aluminum alloy material of the present invention will be described below.
Ｓｉの添加量は１３％〜１５％である。Ｓｉは高温強度を向上させる効果を有している。この効果はＳｉが１３％未満では表れ難く、１３％以上で特に顕著に表れる。Ｓｉが１５％を超えると初晶Ｓｉの晶出が多く室温での伸びが低下して、またアルミよりも固い初晶Ｓｉの存在によって切削加工の切削刃が欠けるおそれがある。よってＳｉは１３％〜１５％とする必要があり、好ましくは１３．５％〜１４．５％とするのが望ましい。 The amount of Si added is 13% to 15%. Si has the effect of improving high temperature strength. This effect is less likely to appear when Si is less than 13%, and is particularly remarkable when Si is 13% or more. If Si exceeds 15%, primary crystal Si is often crystallized and the elongation at room temperature is reduced, and the presence of primary crystal Si, which is harder than aluminum, may cause the cutting blade to be chipped. Therefore, Si needs to be 13% to 15%, preferably 13.5% to 14.5%.
Ｃｕの添加量は２．０％〜４．０％である。Ｃｕは高温強度、とりわけ内燃機関の実用温度域である１５０℃〜２５０℃における強度を向上させる効果を有している。この効果はＣｕの析出によるもので、人工時効を施すことで上記効果を得ることができる。またＮｉおよびＦｅと同時添加することで、Ａｌ−Ｓｉ−Ｎｉ−Ｆｅ−Ｃｕ系化合物として晶出し分散強化を得て高温強度が一層向上する効果がある。この双方の効果は、Ｃｕが２％未満では表れ難く、２．０％以上で顕著に表れる。また４．０％を超えると、上記効果が顕著に表れ難くなり、また比重が増すことによって比強度が向上しなくなるおそれがある。よってＣｕは２．０％〜４．０％とする必要があり、より好ましくは２．５％〜３．５％とするのが望ましい。 The amount of Cu added is 2.0% to 4.0%. Cu has the effect of improving high-temperature strength, particularly strength in the practical temperature range of an internal combustion engine of 150 ° C. to 250 ° C. This effect is due to the precipitation of Cu, and the above effect can be obtained by applying artificial aging. Further, by adding Ni and Fe at the same time, there is an effect that the crystallization dispersion is strengthened as an Al-Si-Ni-Fe-Cu-based compound and the high temperature strength is further improved. Both of these effects are less likely to appear when Cu is less than 2%, and are remarkable when Cu is 2.0% or more. On the other hand, if it exceeds 4.0%, the above effect is less likely to appear remarkably, and the specific strength may not be improved due to the increase in specific gravity. Therefore, Cu needs to be 2.0% to 4.0%, more preferably 2.5% to 3.5%.
Ｍｇの添加量は０．２％〜０．８％である。Ｍｇは高温強度を向上させる効果がある。Ｍｇは連続鋳造時に固溶し、人工時効時にＳｉやＣｕと化合物を形成し析出することで、内燃機関の実用温度域である１５０℃〜２５０℃での強度を向上させる効果がある。この効果はＭｇが０．２％未満では表れ難く、０．２％以上で顕著に表れる。また０．８％を超えると上記効果が顕著に表れなくなる。よってＭｇは０．２％〜０．８％とする必要があり、より好ましくは０．４％〜０．６％にするのが望ましい。 The amount of Mg added is 0.2% to 0.8%. Mg has the effect of improving high temperature strength. Mg dissolves solidly during continuous casting and forms a compound with Si and Cu during artificial aging and precipitates, which has the effect of improving the strength of the internal combustion engine in the practical temperature range of 150 ° C to 250 ° C. This effect is hard to appear when Mg is less than 0.2%, and is remarkable when Mg is 0.2% or more. If it exceeds 0.8%, the above effect will not be noticeable. Therefore, Mg needs to be 0.2% to 0.8%, more preferably 0.4% to 0.6%.
Ｆｅの添加量は０．０５％〜０．６２％である。ＦｅはＳｉおよびＮｉ、Ｃｕと同時添加することでＡｌ−Ｓｉ−Ｎｉ−Ｆｅ−Ｃｕ系化合物を晶出して分散強化に寄与し、コンプレッサーの実用温度域での強度を向上させる効果がある。この効果はＦｅが０．０５％未満では表れ難く、０．０５％以上で顕著に表れる。また０．６２％を超えると粗大化した化合物が晶出し、靱性の低下をもたらす。よってＦｅは０．０５％〜０．６２％とする必要があり、より好ましくは０．２％〜０．４％とするのが望ましい。 The amount of Fe added is 0.05% to 0.62%. When Fe is added at the same time as Si, Ni, and Cu, it crystallizes an Al-Si-Ni-Fe-Cu compound, contributes to strengthening the dispersion, and has the effect of improving the strength of the compressor in the practical temperature range. This effect is unlikely to appear when Fe is less than 0.05%, and is remarkable when Fe is 0.05% or more. If it exceeds 0.62%, the coarsened compound crystallizes, resulting in a decrease in toughness. Therefore, Fe needs to be 0.05% to 0.62%, more preferably 0.2% to 0.4%.
Ｎｉの添加量は０．０５質量％以上かつＦｅ含有率が０．０５質量％〜０．４９質量％の場合には、（Ｎｉ含有率［質量％］）≦６．２８−４．３３×（Ｆｅ含有率［質量％］）Ｆｅ含有率が０．４９質量％〜０．６２質量％の場合には、（Ｎｉ含有率［質量％］）≦２０．２９−３２．７２×（Ｆｅ含有率［質量％］）である。Ｎｉは高温強度を向上させる効果および熱伝導率を低下させる効果を有している。ＮｉはＣｕおよびＦｅ、Ｓｉと同時添加することで、Ａｌ−Ｓｉ−Ｎｉ−Ｆｅ−Ｃｕ系化合物を晶出させ、分散強化にて目的温度域での強度を向上させる効果がある。この効果はＮｉが上記範囲下限値未満では表れ難く、上記範囲下限値以上で顕著に表れる。また上記範囲上限値を超えると粗大晶出物が晶出し、靱性が著しく低下する。よってＮｉは上記範囲とする必要がある。 When the amount of Ni added is 0.05% by mass or more and the Fe content is 0.05% by mass to 0.49% by mass, (Ni content [mass%]) ≤ 6.28-4.33 × (Fe content [mass%]) When the Fe content is 0.49% by mass to 0.62% by mass, (Ni content [mass%]) ≦ 20.29-32.72 × (Fe content) Rate [mass%]). Ni has the effect of improving high temperature strength and the effect of lowering thermal conductivity. When Ni is added at the same time as Cu, Fe, and Si, it has the effect of crystallizing Al-Si-Ni-Fe-Cu compounds and improving the strength in the target temperature range by strengthening the dispersion. This effect is unlikely to appear when Ni is less than the above range lower limit value, and is remarkable when Ni is above the above range lower limit value. If the upper limit of the above range is exceeded, coarse crystallized products will crystallize and the toughness will be significantly reduced. Therefore, Ni needs to be in the above range.
Ｐは任意添加元素であり、その添加量は０．０００１％〜０．０２％である。ＰはＡｌＰ化合物を形成して初晶Ｓｉの核となり、初晶Ｓｉの微細化および均一分散に寄与する効果がある。この効果はＰが０．０００１％未満では表れ難く、０．０００１％以上で顕著に表れる。また０．０２％を超えると湯流れ性が低下し鋳造が難しくなるおそれがある。よってＰは０．０００１％〜０．０２％とする必要があり、より好ましくは、０．０１０％〜０．０１５％とするのが望ましい。また上記Ｓｉ、Ｃｕ、Ｍｇ、Ｆｅ、Ｎｉの成分範囲であれば、Ｐの添加によるＦｅ、Ｎｉ系金属間化合物の晶出形態に変化は生じないため、Ｐ添加によるＦｅ、Ｎｉ系初晶金属間化合物の生成は生じない。 P is an optional additive element, and the addition amount thereof is 0.0001% to 0.02%. P forms an AlP compound and becomes a nucleus of primary crystal Si, which has the effect of contributing to the miniaturization and uniform dispersion of primary crystal Si. This effect is hard to appear when P is less than 0.0001%, and is remarkable when P is 0.0001% or more. If it exceeds 0.02%, the flowability of the molten metal may decrease and casting may become difficult. Therefore, P needs to be 0.0001% to 0.02%, more preferably 0.010% to 0.015%. Further, within the above-mentioned Si, Cu, Mg, Fe, and Ni component ranges, the crystallization form of the Fe and Ni intermetallic compounds does not change due to the addition of P, so that the Fe and Ni primary crystal metals due to the addition of P do not change. No intermetallic formation occurs.
Ｍｎは任意添加元素であり、その添加量は０．０２％〜０．３％である。ＭｎはＡｌ−Ｓｉ−Ｍｎ系化合物をして晶出し、材料の機械的特性を向上させる。これは０．０２％未満では表れ難く、０．０２％以上で顕著に表れる。また０．３％を超えるとＭｎ系化合物が粗大化し、機械的特性が低下する。よってＭｎは０．０２％〜０．３％とする。より好ましくは、０．１％〜０．２％とするのが望ましい。また上記Ｓｉ、Ｃｕ、Ｍｇ、Ｆｅ、ＮｉおよびＰの成分範囲内であれば、Ｍｎの添加によるＦｅ、Ｎｉ系金属間化合物の晶出形態に変化は生じないため、Ｍｎ添加によるＦｅ、Ｎｉ系初晶金属間化合物の生成は生じない。 Mn is an optional additive element, and the amount of Mn added is 0.02% to 0.3%. Mn forms an Al—Si—Mn-based compound and crystallizes to improve the mechanical properties of the material. This is unlikely to appear below 0.02% and is prominent at 0.02% or higher. If it exceeds 0.3%, the Mn-based compound becomes coarse and the mechanical properties deteriorate. Therefore, Mn is set to 0.02% to 0.3%. More preferably, it is 0.1% to 0.2%. Further, as long as it is within the component range of Si, Cu, Mg, Fe, Ni and P, the crystallization form of the Fe and Ni intermetallic compounds does not change due to the addition of Mn. No formation of primary intermetallic compounds occurs.
Ｃｒは任意添加元素であり、その添加量は０．０２％〜０．３％である。ＣｒはＡｌ−Ｓｉ−Ｃｒ系化合物またはＡｌ−Ｓｉ−Ｍｎ−Ｃｒ系化合物として晶出し、材料の機械的特性を向上させる。これは０．０２％未満では表れ難く、０．０２％以上で顕著に表れる。また０．３％を超えるとＣｒ系化合物が粗大化し、機械的特性が低下する。よってＣｒは０．０２％〜０．３％とする。より好ましくは、０．１％〜０．２％とするのが望ましい。また上記Ｓｉ、Ｃｕ、Ｍｇ、Ｆｅ、ＮｉおよびＰの成分範囲内であれば、Ｃｒの添加によるＦｅ、Ｎｉ系金属間化合物の晶出形態に変化は生じないため、Ｃｒ添加によるＦｅ、Ｎｉ系初晶金属間化合物の生成は生じない。 Cr is an optional additive element, and the amount of Cr added is 0.02% to 0.3%. Cr crystallizes as an Al—Si—Cr based compound or an Al—Si—Mn—Cr based compound to improve the mechanical properties of the material. This is unlikely to appear below 0.02% and is prominent at 0.02% or higher. If it exceeds 0.3%, the Cr-based compound becomes coarse and the mechanical properties deteriorate. Therefore, Cr is set to 0.02% to 0.3%. More preferably, it is 0.1% to 0.2%. Further, as long as it is within the component range of Si, Cu, Mg, Fe, Ni and P, the crystallization form of the Fe and Ni intermetallic compounds does not change due to the addition of Cr. No formation of primary intermetallic compounds occurs.
Ｔｉは任意添加元素であり、その添加量は０．０１％〜０．１５％である。Ｔｉは母相に固溶・濃化することで母相の結晶の微細化を促進する。これは０．０１％未満では表れ難く、０．０１％以上で顕著に表れる。また０．１５％を超えるとＴｉ系化合物が粗大晶出し、機械的特性が低下する。よってＴｉは０．０１％〜０．１５％とする。より好ましくは０．０１５％〜０．０５％とするのが望ましい。また上記Ｓｉ、Ｃｕ、Ｍｇ、Ｆｅ、ＮｉおよびＰの成分範囲内であれば、Ｔｉの添加によるＦｅ、Ｎｉ系金属間化合物の晶出形態に変化は生じないため、Ｔｉ添加によるＦｅ、Ｎｉ系初晶金属間化合物の生成は生じない。 Ti is an optional additive element, and the amount of Ti added is 0.01% to 0.15%. Ti dissolves and concentrates in the matrix phase to promote the miniaturization of crystals in the matrix phase. This is unlikely to appear below 0.01% and is prominent above 0.01%. On the other hand, if it exceeds 0.15%, the Ti-based compound crystallizes coarsely and the mechanical properties deteriorate. Therefore, Ti is set to 0.01% to 0.15%. More preferably, it is 0.015% to 0.05%. Further, as long as it is within the component range of Si, Cu, Mg, Fe, Ni and P, the crystallization form of the Fe and Ni intermetallic compounds does not change due to the addition of Ti. No formation of primary intermetallic compounds occurs.
Ｚｒは任意添加元素であり、その添加量は０．０１％〜０．１５％である。ＺｒはＴｉと同様に母相に固溶・濃化することで母相の結晶の微細化を促進する。これは０．０１％未満では表れ難く、０．０１％以上で顕著に表れる。また０．１５％を超えるとＺｒ系化合物が粗大晶出し、機械的特性が低下する。よってＺｒは０．０１％〜０．１５％とする。より好ましくは０．０１５％〜０．０５％とするのが望ましい。また上記Ｓｉ、Ｃｕ、Ｍｇ、Ｆｅ、ＮｉおよびＰの成分範囲内であれば、Ｚｒの添加によるＦｅ、Ｎｉ系金属間化合物の晶出形態に変化は生じないため、Ｚｒ添加によるＦｅ、Ｎｉ系初晶金属間化合物の生成は生じない。 Zr is an optional additive element, and the amount of Zr added is 0.01% to 0.15%. Like Ti, Zr dissolves and concentrates in the matrix phase to promote the miniaturization of crystals in the matrix phase. This is unlikely to appear below 0.01% and is prominent above 0.01%. If it exceeds 0.15%, Zr-based compounds are coarsely crystallized and the mechanical properties are deteriorated. Therefore, Zr is set to 0.01% to 0.15%. More preferably, it is 0.015% to 0.05%. Further, as long as it is within the component range of Si, Cu, Mg, Fe, Ni and P, the crystallization form of the Fe and Ni intermetallic compounds does not change due to the addition of Zr. No formation of primary intermetallic compounds occurs.
次に本実施形態における内燃機関部品用アルミニウム合金材を製造するプロセスの一例について、図１を参照しながら詳細に説明する。 Next, an example of the process of manufacturing the aluminum alloy material for internal combustion engine parts in the present embodiment will be described in detail with reference to FIG.
まず溶製することによって前述のように成分調整されたアルミニウム合金溶湯を作製する。この溶湯を用いて図１に示すように連続鋳造を行って連続鋳造材を製作する。本実施形態において、この連続鋳造材は、鍛造素材用または総切削素材用のビレットとして構成されるものであり、例えば直径φ３０ｍｍ〜４０ｍｍの寸法で丸棒状に形成される。 First, the molten aluminum alloy having the components adjusted as described above is produced by melting. As shown in FIG. 1, continuous casting is performed using this molten metal to produce a continuous cast material. In the present embodiment, the continuous cast material is configured as a billet for a forging material or a total cutting material, and is formed in a round bar shape having a diameter of, for example, φ30 mm to 40 mm.
なお連続鋳造によって押出用のビレットを作製し、その押出用ビレットを押出加工して押出材を成形し、その押出材を鍛造素材または総切削素材として用いることも可能である。また連続鋳造以外にも、鋳物やダイキャストといった鋳造材全般を、切削素材として用いることも可能である。 It is also possible to produce a billet for extrusion by continuous casting, extrude the billet for extrusion to form an extruded material, and use the extruded material as a forging material or a total cutting material. In addition to continuous casting, general casting materials such as castings and die castings can also be used as cutting materials.
得られた連続鋳造材は、鋳造時に晶出物の偏析等が起きる場合が有るため、その不均一な組織を除去するために、均質化処理を施す。均質化処理においては加熱温度を４８０〜５０５℃とし、処理時間を０．５時間（ｈｒ）〜６ｈｒとするのが良い。 Since the obtained continuous cast material may undergo segregation of crystallized material during casting, a homogenization treatment is performed in order to remove the non-uniform structure. In the homogenization treatment, the heating temperature is preferably 480 to 505 ° C., and the treatment time is preferably 0.5 hours (hr) to 6 hr.
均質化処理した後、連続鋳造材を所定の長さに切断し、鍛造素材とする。 After the homogenization treatment, the continuous cast material is cut to a predetermined length to obtain a forged material.
こうして得られた鍛造素材に対し鍛造加工を行って、鍛造材を成形する。この鍛造工程においては、金型温度を１００℃〜２５０℃とし、素材温度を３７０℃〜４５０℃とするのが良い。 The forged material thus obtained is subjected to forging processing to form the forged material. In this forging step, the mold temperature is preferably 100 ° C. to 250 ° C., and the material temperature is preferably 370 ° C. to 450 ° C.
次にこの鍛造材に対し溶体化処理を行う。この溶体化処理においては加熱温度を４８５℃〜５１０℃とし、処理時間を１．０ｈｒ〜５．０ｈｒとするのが良い。 Next, the forged material is subjected to a solution treatment. In this solution treatment, the heating temperature is preferably 485 ° C to 510 ° C, and the treatment time is preferably 1.0 hr to 5.0 hr.
溶体化処理を行った鍛造材に対し水焼き入れ処理を行って急冷する。この水焼き入れ処理において水温は１０℃〜８０℃に設定するのが良い。 The solution-treated forged material is subjected to water-quenching treatment and rapidly cooled. In this water quenching treatment, the water temperature is preferably set to 10 ° C. to 80 ° C.
水焼き入れ処理を行った鍛造材に対し人工時効処理を行う。この人工時効処理においては加熱処理温度を１６０℃〜２２０℃とし、処理時間を１ｈｒ〜１８ｈｒとするのが良い。 Artificial aging treatment is performed on the forged material that has been water-quenched. In this artificial aging treatment, the heat treatment temperature is preferably 160 ° C. to 220 ° C., and the treatment time is preferably 1 hr to 18 hr.
人工時効処理を行った後、人工時効処理済みの鍛造材（鍛造Ｔ６処理品）に対し機械加工により表面を切削し所定の製品形状を得る。その後必要に応じて表面処理、すなわちショットスピーニング処理、アルマイト処理、メッキ処理などを行い、製品を得る。 After the artificial aging treatment is performed, the surface of the forged material (forged T6 treated product) that has been artificially aged is cut by machining to obtain a predetermined product shape. After that, if necessary, surface treatment, that is, shot peening treatment, alumite treatment, plating treatment, etc. are performed to obtain a product.
こうして本実施形態の内燃機関部品用アルミニウム合金材（鍛造材）が製造される。こうして得られたアルミニウム合金材は、Ｓｉ、Ｃｕ、Ｍｇ、ＦｅおよびＮｉを所定量含有していることで、Ｓｉ粒子の分散による分散強化、Ａｌ−Ｓｉ−Ｎｉ−Ｆｅ−Ｃｕ系化合物の分散による分散強化およびＣｕ、Ｍｇ系の析出による析出強化等により高い強度を得ながら、且つアルミニウム合金特有の高靭性を失うことがないため、内燃機関部品として高い性能を得ることができる。 In this way, the aluminum alloy material (forged material) for internal combustion engine parts of the present embodiment is manufactured. The aluminum alloy material thus obtained contains Si, Cu, Mg, Fe and Ni in a predetermined amount, so that the dispersion is strengthened by dispersing Si particles and the Al-Si-Ni-Fe-Cu based compound is dispersed. High performance can be obtained as an internal combustion engine component because high strength is obtained by dispersion strengthening and precipitation strengthening by precipitation of Cu and Mg, and the high toughness peculiar to aluminum alloy is not lost.
以下、本発明について実施例および比較例により詳細に説明する。 Hereinafter, the present invention will be described in detail with reference to Examples and Comparative Examples.
まず、本発明において規定する組成によれば、初晶金属間化合物が生成しないことをシミュレーションソフトを用いた凝固計算によって確認する。 First, according to the composition defined in the present invention, it is confirmed by solidification calculation using simulation software that a primary intermetallic compound is not formed.
凝固計算はＳｃｈｅｉｌ−Ｇｕｌｌｉｖｅｒモデルに基づく凝固計算法が実装されているＪＭａｔＰｒｏ１０．１（Ｓｅｎｔｅ Ｓｏｆｔｗａｒｅ社製）を用い、初期温度８００℃、温度間隔１℃に設定し、ｂａｃｋ ｄｉｆｆｕｓｉｏｎを考慮せず、モデル化されている全固相を考慮して実施した。 The solidification calculation uses JMatPro 10.1 (manufactured by Center Software), which implements the solidification calculation method based on the Scheil-Gulliver model, and is set to an initial temperature of 800 ° C. and a temperature interval of 1 ° C., without considering the back diffusion. It was carried out in consideration of the whole solid phase.
凝固計算により、鋳造工程中に晶出してくる各化合物に対して、鋳造工程中の各温度における相分率が図２のように得られる。各化合物について、図２中に示すように相分率が０より大きい値をもつ最高の温度がその化合物の晶出開始温度である。 By the solidification calculation, the phase fraction at each temperature during the casting process can be obtained as shown in FIG. 2 for each compound crystallized during the casting process. For each compound, as shown in FIG. 2, the highest temperature at which the phase fraction has a value greater than 0 is the crystallization start temperature of the compound.
上記の通り算出した晶出開始温度を用い、アルミニウム母相より高温の晶出開始温度をもつ化合物（シリコンを除く）を初晶金属間化合物と判断できる。アルミニウム母相より高温の晶出開始温度をもつ化合物（シリコンを除く）が存在しない場合は、初晶金属間化合物が生成しないと判断できる。 Using the crystallization start temperature calculated as described above, a compound having a crystallization start temperature higher than that of the aluminum matrix (excluding silicon) can be determined as a primary intermetallic compound. When there is no compound (excluding silicon) having a crystallization start temperature higher than that of the aluminum matrix, it can be determined that the primary intermetallic compound is not formed.
次に、上記の判定方法を用いた初晶金属間化合物の生成しない元素含有率の範囲探索について説明する。 Next, a range search for the element content in which the primary intermetallic compound is not formed using the above determination method will be described.
Ｓｉ、ＣｕおよびＭｇの含有率を表１に記載の値で固定し、ＦｅおよびＮｉ含有率を変化させながら凝固計算を実施することで、初晶金属間化合物の生成しないＦｅおよびＮｉ含有率の範囲を探索した。 By fixing the contents of Si, Cu and Mg at the values shown in Table 1 and performing the solidification calculation while changing the contents of Fe and Ni, the contents of Fe and Ni that do not form primary intermetallic compounds I searched the range.
具体的には、種々に固定したＦｅ含有率に対して、Ｎｉ含有率を変化させながら凝固計算を実施し、初晶金属間化合物の生成しない最大のＮｉ含有率を算出した。 Specifically, the solidification calculation was carried out with respect to the various fixed Fe contents while changing the Ni content, and the maximum Ni content in which the primary intermetallic compound was not formed was calculated.
このように算出した各Ｆｅ含有率に対する最大のＮｉ含有率を、図３のように横軸にＦｅ含有率、縦軸にＮｉ含有率をとったグラフへプロットした。なお、Ｆｅ含有率によってＮｉ含有率が算出した最大値を超えた場合に生成する初晶金属間化合物が異なり、図３中の四角印は初晶Ａｌ９（Ｆｅ，Ｎｉ）２、丸印は初晶β―ＡｌＦｅＳｉがそれぞれ生成することを表している。 The maximum Ni content for each Fe content calculated in this way is plotted on a graph in which the horizontal axis represents the Fe content and the vertical axis represents the Ni content, as shown in FIG. The compounds between primary crystals produced when the Ni content exceeds the calculated maximum value differ depending on the Fe content. The squares in FIG. 3 are primary crystals Al 9 (Fe, Ni) 2 , and the circles are. It shows that primary crystal β-AlFeSi is produced respectively.
図３中の四角印、丸印ごとに直線での回帰を実施した。回帰式は以下の通りである。 A straight line regression was performed for each of the square and circle marks in FIG. The regression equation is as follows.
四角印：（Ｎｉ含有率［質量％］）＝６．２８−４．３３×（Ｆｅ含有率［質量％］）
丸印：（Ｎｉ含有率［質量％］）＝２０．２９−３２．７２×（Ｆｅ含有率［質量％］）
また、回帰直線の交点のＦｅ含有率は下記の通りである。
Square mark: (Ni content [mass%]) = 6.28-4.33 × (Fe content [mass%])
Circle: (Ni content [mass%]) = 20.29-32.72 x (Fe content [mass%])
The Fe content at the intersection of the regression lines is as follows.
四角印の回帰直線と丸印の回帰直線との交点：０．４９質量％
丸印の回帰直線とＮｉ：０．０５質量％線との交点：０．６２質量％
上記２本の回帰直線とＦｅ：０．０５質量％線およびＮｉ：０．０５質量％線とに囲まれた領域（図３中の網掛け領域）では添加したＦｅおよびＮｉが化合物として晶出し分散強化に寄与し、かつ初晶金属間化合物としては生成しない。
Intersection of the regression line marked with a square and the regression line marked with a circle: 0.49% by mass
Intersection of the regression line marked with a circle and the Ni: 0.05 mass% line: 0.62 mass%
In the region surrounded by the above two regression lines and the Fe: 0.05 mass% line and the Ni: 0.05 mass% line (shaded region in FIG. 3), the added Fe and Ni crystallize as a compound. It contributes to dispersion strengthening and is not produced as a primary intermetallic compound.
一般的に添加元素量が多いほど初晶金属間化合物が生成されやすいため、表１に記載のＳｉ、Ｃｕ、Ｍｇ含有率以下であるＳｉ：１３質量％〜１５質量％、Ｃｕ：２質量％〜４質量％、Ｍｇ：０．２質量％〜０．８質量％の範囲では、図３中の網掛け領域として示したＦｅおよびＮｉ含有率の範囲において初晶金属間化合物は生成しない。 Generally, the larger the amount of added elements, the easier it is to generate primary crystal metal-to-metal compounds. Therefore, Si: 13% by mass to 15% by mass and Cu: 2% by mass, which are equal to or less than the Si, Cu, and Mg contents shown in Table 1. In the range of ~ 4% by mass and Mg: 0.2% by mass to 0.8% by mass, the primary crystal metal-to-metal compound is not formed in the range of Fe and Ni contents shown as the shaded region in FIG.
したがって、本発明において規定する、Ｓｉ：１３質量％〜１５質量％、Ｃｕ：２．０質量％〜４．０質量％、Ｍｇ：０．２質量％〜０．８質量％、Ｆｅ：０．０５質量％〜０．６２質量％を含み、Ｎｉを０．０５質量％以上かつＦｅ含有率が０．０５質量％〜０．４９質量％の場合には、（Ｎｉ含有率［質量％］）≦６．２８−４．３３×（Ｆｅ含有率［質量％］）Ｆｅ含有率が０．４９質量％〜０．６２質量％の場合には、（Ｎｉ含有率［質量％］）≦２０．２９−３２．７２×（Ｆｅ含有率［質量％］）で表される含有率で含み、残部がＡｌと不可避不純物からなる組成のアルミニウム合金材によれば、初晶金属間化合物は生成されず、内燃機関用部品での使用に好適である。 Therefore, Si: 13% by mass to 15% by mass, Cu: 2.0% by mass to 4.0% by mass, Mg: 0.2% by mass to 0.8% by mass, Fe: 0. When it contains 05% by mass to 0.62% by mass, contains 0.05% by mass or more of Ni, and has an Fe content of 0.05% by mass to 0.49% by mass (Ni content [mass%]). ≤6.28-4.33 x (Fe content [mass%]) When the Fe content is 0.49% by mass to 0.62% by mass, (Ni content [mass%]) ≤20. According to the aluminum alloy material having a content of 29-32.72 × (Fe content [mass%]) and the balance consisting of Al and unavoidable impurities, no primary crystal metal-to-metal compound is produced. , Suitable for use in internal combustion engine parts.
次に、上記計算結果の妥当性の検証を行う為に実際にサンプルを作製し、評価を実施した。下記にその詳細を示す。 Next, in order to verify the validity of the above calculation results, a sample was actually prepared and evaluated. The details are shown below.
表２に示す実施例１および比較例１の組成を有するアルミニウム合金溶湯をそれぞれ溶製し、各アルミニウム合金溶湯を用いて、鋳造径３８ｍｍで連続鋳造を行ってφ３８ｍｍの連続鋳造材を得た。得られた連続鋳造材を４７０℃×７ｈｒにて均質化処理を施し、空冷した。 The molten aluminum alloys having the compositions of Example 1 and Comparative Example 1 shown in Table 2 were respectively melted, and continuous casting was performed using each of the molten aluminum alloys with a casting diameter of 38 mm to obtain a continuous cast material having a diameter of 38 mm. The obtained continuous cast material was homogenized at 470 ° C. × 7 hr and air-cooled.
上記で得られた連続鋳造品を１０ｍｍ×１０ｍｍ×１０ｍｍの角材に加工し、樹脂埋めを行い組織観察用サンプルを作製した。観察方向は、連続鋳造の軸方向に垂直な断面を観察面とし観察した。観察面をエメリー紙＃２４０〜＃２０００で研磨をし、仕上げをバフ研磨０．１μｍで実施した。組織観察には光学顕微鏡（Ｎｉｋｏｎ ＥＰＩＰＨＯＴ ３００）を用いて、倍率３４０倍にて組織観察を実施した。組織観察より、初晶金属間化合物の有無を判断した。結果を表２に示す。 The continuous cast product obtained above was processed into a square lumber of 10 mm × 10 mm × 10 mm and embedded with resin to prepare a sample for structure observation. As for the observation direction, the cross section perpendicular to the axial direction of continuous casting was used as the observation surface. The observation surface was polished with emery paper # 240 to # 2000, and the finish was buffed with 0.1 μm. The tissue was observed using an optical microscope (Nikon EPIPHOT 300) at a magnification of 340 times. The presence or absence of the primary intermetallic compound was determined from the microstructure observation. The results are shown in Table 2.
表２より、実施例１のアルミニウム合金の場合、初晶金属間化合物が晶出していることは確認されず、比較例１のアルミニウム合金の場合、針状に粗大な金属間化合物が晶出していることが確認された。 From Table 2, in the case of the aluminum alloy of Example 1, it was not confirmed that the primary intermetallic compound was crystallized, and in the case of the aluminum alloy of Comparative Example 1, needle-like coarse intermetallic compounds were crystallized. It was confirmed that there was.
また、表２に記載の実施例１および比較例１にて上記の凝固計算を実施した。 In addition, the above solidification calculation was carried out in Example 1 and Comparative Example 1 shown in Table 2.
実施例１の化学組成について凝固計算を行うと、高温側から順にシリコンが６１１℃、アルミニウム母相が５６４℃、β―ＡｌＦｅＳｉが５６２℃で晶出を開始し、初晶金属間化合物は生成しない。実際にサンプルを作製した表２に示す結果は、上記凝固計算に整合しており凝固計算が正しいことが裏付けられる。 When the solidification calculation was performed for the chemical composition of Example 1, silicon started to crystallize at 611 ° C., the aluminum matrix at 564 ° C., and β-AlFeSi at 562 ° C. in order from the high temperature side, and no primary intermetallic compound was formed. .. The results shown in Table 2 in which the sample was actually prepared are consistent with the above solidification calculation, confirming that the solidification calculation is correct.
また比較例１の化学組成について凝固計算を行うと、高温側から順にシリコンが６０６℃、β―ＡｌＦｅＳｉが６０４℃、アルミニウム母相が５６１℃で晶出を開始し、β―ＡｌＦｅＳｉが初晶金属間化合物として生成した。実際にサンプルを作製した表２に示す結果は、上記凝固計算に整合しており凝固計算が正しいことが裏付けられる。 Further, when the solidification calculation was performed on the chemical composition of Comparative Example 1, silicon started to crystallize at 606 ° C., β-AlFeSi at 604 ° C., and the aluminum matrix at 561 ° C. in order from the high temperature side, and β-AlFeSi was a primary crystal metal. It was produced as an intermetallic compound. The results shown in Table 2 in which the sample was actually prepared are consistent with the above solidification calculation, confirming that the solidification calculation is correct.
以上のとおり本発明において規定する組成によれば、初晶金属間化合物が生成しないため、粗大金属間化合物による靱性の低下を回避することができる。 As described above, according to the composition defined in the present invention, since the primary intermetallic compound is not formed, it is possible to avoid a decrease in toughness due to the coarse intermetallic compound.
したがって、本発明において規定する組成によれば、Ｓｉ、Ｃｕ、Ｍｇ、ＦｅおよびＮｉを所定量含有していることで高い強度を得ながら、高い靱性を備えたアルミニウム合金材を得ることができ、内燃機関用部品での使用に好適である。 Therefore, according to the composition specified in the present invention, it is possible to obtain an aluminum alloy material having high toughness while obtaining high strength by containing a predetermined amount of Si, Cu, Mg, Fe and Ni. Suitable for use in internal combustion engine parts.
この発明のアルミニウム合金材は、例えば４輪自動車用、２輪自動車用、汎用の内燃機関におけるエンジンピストンやコンプレッサー、シリンダライナ、クランクシャフト、カムシャフト、エンジンブロック等として好適に用いることができる。 The aluminum alloy material of the present invention can be suitably used, for example, as an engine piston or compressor, a cylinder liner, a crankshaft, a camshaft, an engine block, or the like in a general-purpose internal combustion engine for a four-wheeled vehicle or a two-wheeled vehicle.
Claims (3)
Ｎｉを０．０５質量％以上かつ
Ｆｅ含有率が０．０５質量％〜０．４９質量％の場合には、
（Ｎｉ含有率［質量％］）≦６．２８−４．３３×（Ｆｅ含有率［質量％］）
Ｆｅ含有率が０．４９質量％〜０．６２質量％の場合には、
（Ｎｉ含有率［質量％］）≦２０．２９−３２．７２×（Ｆｅ含有率［質量％］）
で表される含有率で含み、残部がＡｌと不可避不純物からなる組成を有することを特徴とするアルミニウム合金材。 Si: 13% by mass to 15% by mass, Cu: 2.0% by mass to 4.0% by mass, Mg: 0.2% by mass to 0.8% by mass, Fe: 0.05% by mass to 0.62% by mass Including%
When Ni is 0.05% by mass or more and the Fe content is 0.05% by mass to 0.49% by mass,
(Ni content [mass%]) ≤6.28-4.33 × (Fe content [mass%])
When the Fe content is 0.49% by mass to 0.62% by mass,
(Ni content [mass%]) ≦ 20.29-32.72 × (Fe content [mass%])
An aluminum alloy material containing the content represented by (1) and having a composition in which the balance is composed of Al and unavoidable impurities.
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| JPH0790459A (en) * | 1993-09-17 | 1995-04-04 | Mitsubishi Alum Co Ltd | Production of wear resistant aluminum alloy for extrusion and wear resistant aluminum alloy material |
| JP2004076110A (en) * | 2002-08-20 | 2004-03-11 | Toyota Central Res & Dev Lab Inc | Aluminum cast alloy for piston, piston and method for producing the same |
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