JP2010077475A - Aluminum sintered alloy - Google Patents
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Abstract
【課題】冷間サイジングを行っても高強度であるアルミニウム合金部品の素材に適したアルミニウム焼結合金、及びこの焼結合金の製造に適したアルミニウム焼結合金用粉末を提供する。
【解決手段】Al又はAl合金を母材とするアルミニウム焼結合金であり、遷移金属元素を0.2体積％以上5体積％以下含有する。この焼結合金は、母材を構成する母材粒子の旧粉末粒界gb上に、Alと上記遷移金属元素とを含む金属間化合物imcが点在している。この焼結合金は、Al又はAl合金からなる母材粉末と、遷移金属元素からなり、最大粒径が30μm以下である添加粉末とが混合されてなるアルミニウム焼結合金用粉末を液相焼結することで得られる。
【選択図】図1An aluminum sintered alloy suitable for a material of an aluminum alloy part having high strength even after cold sizing and a powder for an aluminum sintered alloy suitable for production of the sintered alloy are provided.
An aluminum sintered alloy containing Al or an Al alloy as a base material and containing a transition metal element in an amount of 0.2% by volume to 5% by volume. In this sintered alloy, an intermetallic compound imc containing Al and the transition metal element is scattered on the old powder grain boundary gb of the base material particles constituting the base material. This sintered alloy is a liquid phase sintered powder for an aluminum sintered alloy in which a base material powder made of Al or an Al alloy and an additive powder made of a transition metal element and having a maximum particle size of 30 μm or less are mixed. It is obtained by doing.
[Selection] Figure 1
Description
本発明は、機械部品などの素材に利用されるアルミニウム焼結合金、及びこの焼結合金の製造に適したアルミニウム焼結合金用粉末に関するものである。 The present invention relates to an aluminum sintered alloy used as a material for machine parts and the like, and an aluminum sintered alloy powder suitable for producing the sintered alloy.
自動車の内燃機関の構成部品などといった種々の部品の素材に、軽量のアルミニウム合金が利用されている。アルミニウム合金部品の製造方法として、(1)原料粉末の成形体を焼結した後、粉末鍛造を行い、更に熱処理を施す方法(特許文献1)、(2)原料粉末を加熱状態で押し出す方法(特許文献2)などがある。特許文献3には、耐摩耗性の向上を図るために、素地にFe,Ni,Crを分散させた摺動部材用焼結Al合金が開示されている。 Lightweight aluminum alloys are used as materials for various parts such as components of automobile internal combustion engines. As a method for producing an aluminum alloy part, (1) a method of performing powder forging after sintering a compact of a raw material powder, and further performing a heat treatment (Patent Document 1), Patent Document 2) and the like. Patent Document 3 discloses a sintered Al alloy for a sliding member in which Fe, Ni, and Cr are dispersed in a base material in order to improve wear resistance.
昨今、種々の形状のアルミニウム合金部品に対して、(1)高強度であること、(2)耐熱性が高いこと、(3)耐摩耗性が高いこと、(4)寸法精度が高いことが望まれている。しかし、従来のアルミニウム合金では、この要求を十分に満たすことが難しい。 Recently, for aluminum alloy parts of various shapes, (1) high strength, (2) high heat resistance, (3) high wear resistance, (4) high dimensional accuracy. It is desired. However, it is difficult for conventional aluminum alloys to sufficiently satisfy this requirement.
高強度(高密度)が望まれる場合、熱間サイジングが行われ、高精度が望まれる場合、冷間サイジングが行われている。熱間サイジングを行った場合、強度に優れる反面、形状や寸法精度に劣る。一方、冷間サイジングを行った場合、強度が熱間サイジングを行った場合の7割程度と低い。 Hot sizing is performed when high strength (high density) is desired, and cold sizing is performed when high accuracy is desired. When hot sizing is performed, the strength is excellent, but the shape and dimensional accuracy are inferior. On the other hand, when cold sizing is performed, the strength is as low as about 70% of that when hot sizing is performed.
熱間押出による製造方法は、強度に優れるものの、焼結による製造方法と比較して形状の自由度が小さく、種々の形状に対応できない。 Although the manufacturing method by hot extrusion is excellent in strength, the degree of freedom of shape is small as compared with the manufacturing method by sintering, and it cannot cope with various shapes.
特許文献3に記載される焼結Al合金は、抗折力が低いことから、十分な強度が得られていないと考えられる。これは、原料のFe粉が粗大過ぎることが原因の一つであると考えられる。 Since the sintered Al alloy described in Patent Document 3 has low bending strength, it is considered that sufficient strength is not obtained. This is considered to be one of the causes that the raw material Fe powder is too coarse.
本発明は、上記事情を鑑みてなされたものであり、その目的の一つは、高強度で、耐熱性及び耐摩耗性に優れ、形状の自由度が大きいアルミニウム焼結合金を提供することにある。また、本発明の他の目的は、本発明アルミニウム焼結合金の製造に適しており、焼結性が高いアルミニウム焼結合金用粉末を提供することにある。 The present invention has been made in view of the above circumstances, and one of its purposes is to provide an aluminum sintered alloy having high strength, excellent heat resistance and wear resistance, and a large degree of freedom in shape. is there. Another object of the present invention is to provide a powder for an aluminum sintered alloy which is suitable for producing the aluminum sintered alloy of the present invention and has high sinterability.
金属の強度を向上する方法として、固溶強化が考えられる。しかし、アルミニウム(Al)は、固溶元素がZn,Cu,Mg程度と少なく、固溶強化には限界がある。そこで、本発明者らは、固溶強化以外の強度向上の方法を種々検討した結果、Alとの間で金属間化合物を生成する金属元素の粉末を原料に用いて液相焼結することで焼結性を高められ、強度、耐熱性、そして耐摩耗性にも優れる焼結合金が得られるとの知見を得た。特に、上記金属元素の粉末として微細な粉末を用いると、これら微細な粉末の実質的に全てが母材粉末と反応してAlとの間で金属間化合物となって母材の旧粉末粒界上に存在し、微細な粉末が実質的に残存せず、かつ、これら生成された金属間化合物は、旧粉末粒界上に連続的に存在せず、分散して存在するとの知見を得た。即ち、金属間化合物の周囲に母材金属が存在した組織である。このような組織により、金属間化合物の存在による割れなどの進展が生じ難く、金属間化合物の存在による焼結体の強度及び耐熱性の向上効果を十分に得られると考えられる。本発明は、これらの知見に基づくものである。 Solid solution strengthening can be considered as a method for improving the strength of the metal. However, aluminum (Al) has few solid solution elements such as Zn, Cu, and Mg, and there is a limit to solid solution strengthening. Therefore, as a result of various investigations on strength improvement methods other than solid solution strengthening, the present inventors have conducted liquid phase sintering using powders of metal elements that form intermetallic compounds with Al as raw materials. It was found that a sintered alloy having improved sinterability and excellent strength, heat resistance, and wear resistance can be obtained. In particular, when a fine powder is used as the metal element powder, substantially all of the fine powder reacts with the base material powder to form an intermetallic compound with Al, and the old powder grain boundary of the base material. It was found that fine powder was not substantially remained, and that the generated intermetallic compounds were not continuously present on the old powder grain boundaries but were dispersed. . That is, it is a structure in which a base metal is present around an intermetallic compound. With such a structure, it is considered that progress such as cracking due to the presence of the intermetallic compound hardly occurs, and the effect of improving the strength and heat resistance of the sintered body due to the presence of the intermetallic compound can be sufficiently obtained. The present invention is based on these findings.
本発明アルミニウム焼結合金は、Al又はAl合金を母材とし、母材とは別に遷移金属元素を0.2体積％以上5体積％以下含有する。この焼結合金は、母材を構成する母材粒子の旧粉末粒界上に、Alと上記遷移元素とを含む金属間化合物が点在した組織を有する。この組織は、上記旧粉末粒界上に存在する金属間化合物が旧粉末粒界を切断する長さを切断長とするとき、上記旧粉末粒界の粒界長に対する上記切断長の割合(以下、切断長割合と呼ぶ)が3％以上50％以下を満たす。 The aluminum sintered alloy of the present invention uses Al or an Al alloy as a base material, and contains a transition metal element in an amount of 0.2% by volume to 5% by volume separately from the base material. This sintered alloy has a structure in which intermetallic compounds containing Al and the above transition elements are scattered on the old powder grain boundaries of the base material particles constituting the base material. This structure is the ratio of the cutting length to the grain boundary length of the old powder grain boundary (hereinafter referred to as the cutting length) when the length of the intermetallic compound existing on the old powder grain boundary cuts the old powder grain boundary. (Referred to as cutting length ratio) satisfies 3% to 50%.
上記特有の組織を有する本発明アルミニウム焼結合金は、本発明アルミニウム焼結合金用粉末により製造することができる。本発明焼結合金用粉末は、Al又はAl合金を母材とするアルミニウム焼結合金の製造に利用されるものであり、Al又はAl合金からなる母材粉末と、遷移金属元素からなる添加粉末とが混合されてなり、添加粉末を0.2体積％以上5体積％以下含有する。この添加粉末の最大粒径は、30μm以下である。 The aluminum sintered alloy of the present invention having the above specific structure can be produced from the powder for an aluminum sintered alloy of the present invention. The sintered alloy powder of the present invention is used for the production of an aluminum sintered alloy whose base material is Al or Al alloy, and is a base material powder made of Al or Al alloy and an additive powder made of a transition metal element. And the additive powder is contained in an amount of 0.2% by volume to 5% by volume. The maximum particle size of the additive powder is 30 μm or less.
上述のように微細な添加粉末を母材粉末に混合することで、母材粒子の外周に細かい添加粒子が満遍なく付着された状態となる。この状態で液相焼結を行うと、母材と添加した遷移金属元素(以下、添加金属元素と呼ぶ)とが反応して、添加金属元素のほぼ全てがAlとの金属間化合物として焼結合金中に存在する。 By mixing the fine additive powder with the base material powder as described above, the fine additive particles are uniformly attached to the outer periphery of the base material particles. When liquid phase sintering is performed in this state, the base metal and the added transition metal element (hereinafter referred to as an additive metal element) react, and almost all of the additive metal element is burned and bonded as an intermetallic compound with Al. Exists in gold.
また、上記母材と添加金属元素との反応は、概ね旧粉末粒界上で行われ、生成されたAlとの金属間化合物は、焼結合金中の母材粒子の旧粉末粒界上に点在する。即ち、本発明焼結合金は、Alよりも高強度である金属間化合物が母材粒子や添加粒子の全周を覆うように連続して存在するのではなく、旧粉末粒界上に不連続に存在し、母材粒子などの全周面が金属間化合物で覆われることが実質的に無いため、金属間化合物や旧粉末粒界に沿った割れの進展が実質的に起こり難く、結果として強度を向上できる。 In addition, the reaction between the base material and the additive metal element is generally performed on the old powder grain boundary, and the generated intermetallic compound with Al is formed on the old powder grain boundary of the base material particle in the sintered alloy. Dotted. That is, the sintered alloy of the present invention does not exist continuously so that the intermetallic compound having higher strength than Al covers the entire circumference of the base material particles and additive particles, but discontinuous on the old powder grain boundary. As a result, cracks along the intermetallic compound and the old powder grain boundary are substantially unlikely to occur because the entire peripheral surface of the base material particles is not covered with the intermetallic compound. Strength can be improved.
かつ、本発明焼結合金は、母材粒子同士が金属間化合物を介して強固に結合されるため、焼結後、冷間サイジングを行っても強度に優れる上に、冷間サイジングを行うことで、寸法精度にも優れる部品が得られる。また、本発明焼結合金は、組織中に、耐熱性が高く高硬度なAl-遷移金属系金属間化合物が多く分散しているため、耐熱性及び耐摩耗性の双方に優れている。更に、本発明焼結合金は、押出の場合に比べて、形状の自由度が大きく、種々の形状に対応可能である。なお、押出材では、母材を構成する母材粒子のアスペクト比が非常に大きく細長い形状であり、焼結合金の場合、上記アスペクト比が小さい。 In addition, since the sintered particles of the present invention are firmly bonded to each other through intermetallic compounds, the base particles are excellent in strength even after performing cold sizing after sintering, and performing cold sizing. Thus, a part having excellent dimensional accuracy can be obtained. In addition, the sintered alloy of the present invention is excellent in both heat resistance and wear resistance because a large amount of Al-transition metal intermetallic compound having high heat resistance and high hardness is dispersed in the structure. Furthermore, the sintered alloy of the present invention has a greater degree of freedom of shape than the case of extrusion, and can accommodate various shapes. In addition, in the extruded material, the aspect ratio of the base material particles constituting the base material is a very long and elongated shape, and in the case of a sintered alloy, the aspect ratio is small.
以下、本発明をより詳細に説明する。
＜焼結合金＞
[母材]
本発明焼結合金の母材は、Al及び不可避的不純物からなる純アルミニウム(以下、Alと呼ぶ)、又は合金添加元素と残部がAl及び不可避的不純物からなるアルミニウム合金(以下、Al合金と呼ぶ)で構成される。Al合金は、例えば、Al-Zn-Mg-Cu合金、Al-Si-Cu-Mg合金などが挙げられる。合金添加元素は、焼結合金の母材に固溶又は析出して存在する。その他、特許文献3に記載されるような潤滑成分を含んでいてもよい。
Hereinafter, the present invention will be described in more detail.
<Sintered alloy>
[Base material]
The base material of the sintered alloy of the present invention is pure aluminum (hereinafter referred to as Al) made of Al and unavoidable impurities, or an aluminum alloy (hereinafter referred to as Al alloy) consisting of Al and unavoidable impurities with the alloy additive element and the balance. ). Examples of the Al alloy include an Al—Zn—Mg—Cu alloy and an Al—Si—Cu—Mg alloy. The alloy additive element exists as a solid solution or precipitate in the base material of the sintered alloy. In addition, a lubricating component as described in Patent Document 3 may be included.
[金属間化合物]
本発明焼結合金は、上記合金添加元素とは別に、遷移金属元素を0.2体積％以上5体積％以下含有しており、この遷移金属元素は、その大部分(焼結合金中の含有量を100体積％とするとき、大よそ70体積％以上)がAlとの金属間化合物を形成して合金中に存在すると考えられる。0.2体積％未満では、十分な量の金属間化合物が合金中に存在せず、焼結性の低下による強度の低下を招き、5体積％超では、金属間化合物が合金中に過剰に存在して、割れの発生や割れの進展が生じ易くなり強度の低下を招く。より好ましい遷移金属元素の含有量は、1体積％以上1.5体積％以下である。
[Intermetallic compounds]
The sintered alloy of the present invention contains a transition metal element in an amount of 0.2% by volume or more and 5% by volume or less, in addition to the above-mentioned alloy additive element, and most of the transition metal element (the content in the sintered alloy is reduced). When the volume is 100% by volume, approximately 70% by volume or more) is considered to be present in the alloy by forming an intermetallic compound with Al. If it is less than 0.2% by volume, a sufficient amount of intermetallic compounds are not present in the alloy, resulting in a decrease in strength due to a decrease in sinterability, and if it exceeds 5% by volume, intermetallic compounds are excessively present in the alloy. Therefore, the occurrence of cracks and the progress of cracks are likely to occur, leading to a decrease in strength. The transition metal element content is more preferably 1% by volume or more and 1.5% by volume or less.
上記遷移金属元素は、Alとの間で金属間化合物を形成し易い元素が好ましく、Fe,Ni,Ti,Cr,Mnなどが挙げられる。特に、Feは、安価で経済的である。遷移金属元素は、1種でも2種以上の複数種でもよい。複数種の遷移金属元素を含む場合、合計含有量が上記範囲を満たすことが好ましい。これらの複数種の元素は、個々の元素とAlとの金属間化合物や、複数の元素の複合金属間化合物を形成して存在する。 The transition metal element is preferably an element that easily forms an intermetallic compound with Al, and examples thereof include Fe, Ni, Ti, Cr, and Mn. In particular, Fe is inexpensive and economical. The transition metal element may be one type or two or more types. When multiple types of transition metal elements are included, the total content preferably satisfies the above range. These plural kinds of elements exist by forming intermetallic compounds of individual elements and Al, or composite intermetallic compounds of a plurality of elements.
上記遷移金属元素とAlとの金属間化合物は、母材を構成する母材粒子の旧粉末粒界上に点在している(切断長割合が3％以上50％以下を満たす)ことが本発明焼結合金の最も特徴とする構成である。即ち、図10に示すように旧粉末粒界100の長さL100よりも、旧粉末粒界100上に存在する金属間化合物imcが旧粉末粒界100と重なり合う部分の長さ(切断長)ln(n=1,2,3,…)の合計の方が短い。この合計切断長は、旧粉末粒界上に存在する金属間化合物が旧粉末粒界と重複しない部分の長さの合計と同等(切断長割合が50％の場合)、又は当該長さの合計よりも短い(切断長割合が50％未満の場合)。切断長割合が3％未満では、旧粉末粒界上に金属間化合物が十分に存在せず、金属間化合物による母材粒子同士の結合が十分に行えず、強度の低下を招く。切断長割合が50％超では、旧粉末粒界上に金属間化合物が隣接して連続的に存在する部分が生じるようなり、金属間化合物に沿って割れが伝播するなどして、強度の低下を招く。より好ましい切断長割合は、15％以上20％以下である。切断長割合の算出方法の詳細は、後述する。 The intermetallic compound of the transition metal element and Al is scattered on the old powder grain boundary of the base material particles constituting the base material (the cutting length ratio satisfies 3% to 50%). It is the most characteristic structure of the invention sintered alloy. That is, the length (cutting length) of the portion where the intermetallic compound imc existing on the old powder grain boundary 100 overlaps the old powder grain boundary 100 rather than the length L 100 of the old powder grain boundary 100 as shown in FIG. The sum of l n (n = 1,2,3, ...) is shorter. This total cut length is equivalent to the total length of the parts where the intermetallic compound existing on the old powder grain boundary does not overlap with the old powder grain boundary (when the cutting length ratio is 50%), or the total of the lengths Shorter (when the cutting length ratio is less than 50%). When the cutting length ratio is less than 3%, there are not enough intermetallic compounds on the old powder grain boundaries, and the base metal particles cannot be sufficiently bonded to each other by the intermetallic compounds, leading to a decrease in strength. If the cutting length ratio exceeds 50%, there will be a part where intermetallic compounds exist continuously on the old powder grain boundary, and cracks propagate along the intermetallic compound, resulting in a decrease in strength. Invite. A more preferable cutting length ratio is 15% or more and 20% or less. Details of the method for calculating the cutting length ratio will be described later.
焼結合金中の金属間化合物の含有量は、上記遷移金属元素の含有量に概ね依存し、金属間化合物の大きさは、遷移金属元素からなる添加粒子の大きさや焼結条件に概ね依存する。金属間化合物が大き過ぎると破壊の起点となるため、金属間化合物の最大粒径が30μm以下、好ましくは10μm以下となるように添加粒子の大きさや焼結条件を制御することが好ましい。 The content of the intermetallic compound in the sintered alloy generally depends on the content of the transition metal element, and the size of the intermetallic compound generally depends on the size of the additive particles composed of the transition metal element and the sintering conditions. . If the intermetallic compound is too large, it becomes a starting point of fracture. Therefore, it is preferable to control the size of the added particles and the sintering conditions so that the maximum particle size of the intermetallic compound is 30 μm or less, preferably 10 μm or less.
[特性]
本発明焼結合金は、強固に結合されており、強度に優れる。母材組成にもよるが、例えば、引張強度が450MPa以上の焼結合金が得られる。また、本発明焼結合金の組織は、冷間サイジングや熱間サイジングを行った場合であっても、概ね維持されるため、いずれのサイジングを行っても強度に優れる部品が得られる。熱間サイジングを施した場合は、より高強度な部品が得られる。
[Characteristic]
The sintered alloy of the present invention is firmly bonded and has excellent strength. Depending on the base material composition, for example, a sintered alloy having a tensile strength of 450 MPa or more can be obtained. Moreover, since the structure of the sintered alloy of the present invention is generally maintained even when cold sizing or hot sizing is performed, a component having excellent strength can be obtained by any sizing. When hot sizing is performed, higher strength parts can be obtained.
＜焼結合金の製造方法＞
上記本発明焼結合金は、上記母材を構成する母材粉末と、上記遷移金属元素からなる添加粉末との混合粉末を成形し、この成形体を液相焼結することで製造することができる。成形は、冷間金型成形などの冷間の加圧成形などが利用できる。焼結は、液相出現温度で行えばよく、公知の条件を利用できる。代表的な条件は、窒素やアルゴンといった不活性雰囲気で、温度:550〜650℃、時間:0超〜90分が挙げられる。この焼結により、添加粉末と母材粉末とが反応してAlと添加金属元素との金属間化合物が生成される。
<Method for producing sintered alloy>
The sintered alloy of the present invention can be manufactured by forming a mixed powder of a base material powder constituting the base material and an additive powder made of the transition metal element, and liquid-phase sintering the formed body. it can. For forming, cold pressure forming such as cold mold forming can be used. Sintering may be performed at the liquid phase appearance temperature, and known conditions can be used. Typical conditions include an inert atmosphere such as nitrogen or argon, temperature: 550 to 650 ° C., time: more than 0 to 90 minutes. By this sintering, the additive powder and the base material powder react to produce an intermetallic compound of Al and the additive metal element.
[母材粉末]
母材粉末の大きさは、特に問わないが、平均粒径が40μm以上70μm以下であると、成形性や焼結性に優れて好ましい。市販のものを利用してもよい。
[Base material powder]
The size of the base material powder is not particularly limited, but an average particle size of 40 μm or more and 70 μm or less is preferable because of excellent moldability and sinterability. A commercially available product may be used.
[添加粉末]
添加粉末は、所望の組成の金属間化合物が所望の量だけ焼結合金中に存在できるように、遷移金属元素から適宜元素を選択すると共に、混合粉末全体に対して0.2体積％以上5体積％以下含有されるように添加粉末の含有量を調整する。この添加粉末は、その最大粒径が30μm以下であることが本発明粉末の最も特徴とする構成である。添加粉末の最大粒径が30μm超、特に従来のアルミニウム合金のように100μm程度の大きさの粒子を用いた場合(特許文献3では100メッシュ(約150μm)以上)、焼結合金中に添加した粒子が残存する。また、大きな金属間化合物が生成される恐れがある。これに対し、最大粒径が30μm以下の非常に微細な添加粉末を用いると、母材粉末を構成する各母材粒子の全周面を添加粉末で満遍なく覆うことができ、この状態で液相焼結を行うことで、母材粒子の旧粉末粒界上に比較的微細な金属間化合物が生成されると共に、添加粉末が実質的に残存しなくなる。添加粉末が微細であるほど、添加粉末の残存量を低減でき、10μm以下がより好ましく、下限は特に設けない。
[Additive powder]
The additive powder is appropriately selected from transition metal elements so that an intermetallic compound having a desired composition can be present in the sintered alloy in a desired amount, and 0.2 volume% or more and 5 volume% with respect to the entire mixed powder The content of the additive powder is adjusted so as to be contained below. This additive powder has the most characteristic constitution of the powder of the present invention that its maximum particle size is 30 μm or less. When the maximum particle size of the additive powder exceeds 30 μm, especially when particles with a size of about 100 μm are used as in conventional aluminum alloys (100 mesh (about 150 μm or more in Patent Document 3)), added to the sintered alloy Particles remain. In addition, a large intermetallic compound may be generated. On the other hand, when a very fine additive powder having a maximum particle size of 30 μm or less is used, the entire peripheral surface of each base material particle constituting the base material powder can be covered evenly with the additive powder. By performing the sintering, a relatively fine intermetallic compound is generated on the old powder grain boundary of the base material particles, and the additive powder does not substantially remain. As the additive powder becomes finer, the remaining amount of the additive powder can be reduced, more preferably 10 μm or less, and no lower limit is set.
[原料粉末の製造方法]
母材粉末や添加粉末は、例えば、エアアトマイズ法(大気アトマイズ法)や水アトマイズ法といったアトマイズ法(急冷凝固法)により製造することができる。特に、最大粒径が30μm以下といった微細な添加粉末を大気アトマイズ法にて得るには、通常の加圧(30MPa程度)よりも高い圧力(100MPa程度)とすることが挙げられる。
[Production method of raw material powder]
The base material powder and the additive powder can be produced, for example, by an atomizing method (rapid solidification method) such as an air atomizing method (atmospheric atomizing method) or a water atomizing method. In particular, in order to obtain a fine additive powder having a maximum particle size of 30 μm or less by the atmospheric atomization method, a pressure (about 100 MPa) higher than normal pressurization (about 30 MPa) can be mentioned.
本発明アルミニウム焼結合金は、高強度で、耐熱性及び耐摩耗性に優れるアルミニウム合金部品が得られる。また、このアルミニウム合金部品は、種々の形状を取り得る上に、寸法精度にも優れる。本発明アルミニウム焼結合金用粉末は、強度などに優れる上記本発明焼結合金を製造することができる。 The aluminum sintered alloy of the present invention provides an aluminum alloy part having high strength and excellent heat resistance and wear resistance. Moreover, this aluminum alloy part can take various shapes and is excellent in dimensional accuracy. The powder for an aluminum sintered alloy of the present invention can produce the above sintered alloy of the present invention which is excellent in strength and the like.
種々のアルミニウム焼結合金を作製し、その組織と機械的特性とを調べた。 Various sintered aluminum alloys were prepared and their structures and mechanical properties were investigated.
(試料No.1〜18)
母材粉末として、Al-6.0Zn-2.5Mg-1.75Cu-0.2Sn(単位:質量％)の組成のAl合金粉末A(ecka社製431/D、平均粒径60μm)、Al-15.0Si-2.5Cu-0.60Mg(単位:質量％)の組成のAl合金粉末B(ecka社製231、平均粒径60μm)、添加粉末として、鉄粉末(97質量％以上Feの純鉄)を用意した。鉄粉末は、アトマイズ法により作製した最大粒径が異なるもの(5,30,40μm)を用意した。
(Sample Nos. 1-18)
As a base material powder, Al alloy powder A (ecka 431 / D, average particle size 60 μm) having a composition of Al-6.0Zn-2.5Mg-1.75Cu-0.2Sn (unit: mass%), Al-15.0Si- Al alloy powder B (231 made by ecka, average particle size 60 μm) having a composition of 2.5 Cu-0.60 Mg (unit: mass%) and iron powder (pure iron of 97 mass% or more Fe) were prepared as additive powder. Iron powders with different maximum particle sizes (5, 30, 40 μm) prepared by the atomization method were prepared.
Al合金粉末Aに対して各鉄粉末を0.5〜6体積％含有させた混合粉末を直径φ35mmの金型成形(加圧:4ton/cm2)にて成形し、窒素雰囲気中で615±5℃×10分の条件で焼結を行った後、T6処理を行い、試料No.1〜16の焼結合金を得た。また、Al合金粉末Bに対して各鉄粉末を1.5〜3.0体積％含有させた混合粉末を直径φ35mmの金型成形(加圧:6ton/cm2)にて成形し、窒素雰囲気中で560±5℃×20分の条件で焼結を行った後、T6処理を行い、試料No.17,18の焼結合金を得た。 A mixed powder containing 0.5-6% by volume of each iron powder with respect to Al alloy powder A was molded by die molding (pressure: 4 ton / cm 2 ) with a diameter of 35 mm, and 615 ± 5 ° C in a nitrogen atmosphere After sintering under the condition of × 10 minutes, T6 treatment was performed to obtain sintered alloys of sample Nos. 1-16. Further, a mixed powder containing 1.5 to 3.0% by volume of each iron powder with respect to the Al alloy powder B was molded by die molding (pressure: 6 ton / cm 2 ) with a diameter of 35 mm, and 560 ± in a nitrogen atmosphere. After sintering under conditions of 5 ° C. × 20 minutes, T6 treatment was performed to obtain sintered alloys of Sample Nos. 17 and 18.
(試料No.100,200)
上記試料No.1〜16の母材粉末と同じAl合金粉末Aを用意し、鉄粉末を含有させずに、試料No.1〜16と同じ条件で成形、焼結、T6処理を行い、試料No.100の焼結合金を得た。また、上記試料No.17,18の母材粉末と同じAl合金粉末Bを用意し、鉄粉末を含有させずに、試料No.17,18と同じ条件で成形、焼結、T6処理を行い、試料No.200の焼結合金を得た。
(Sample No.100,200)
Prepare the same Al alloy powder A as the base material powder of the above sample No. 1-16, do not contain iron powder, perform molding, sintering, T6 treatment under the same conditions as sample No. 1-16, sample A No. 100 sintered alloy was obtained. Also, prepare the same Al alloy powder B as the base material powder of sample No. 17 and 18 above, and perform molding, sintering and T6 treatment under the same conditions as sample No. 17 and 18 without containing iron powder A sintered alloy of Sample No. 200 was obtained.
(試料No.300)
母材粉末として、Feを1.8体積％含有するAl-Si-Fe合金粉末C(Al-15Si-5Fe-2.5Cu-1Mg(単位:質量％)の組成)を用意した。このAl-Si-Fe合金粉末Cは、アトマイズ法により作製した(平均粒径60μm)。得られたAl-Si-Fe合金粉末Cを試料No.17,18と同じ条件で成形、焼結、T6処理を行い、試料No.300の焼結合金を得た。なお、Al-Si-Fe合金粉末CにおいてFe成分は、金属間化合物(Al3Fe)として存在する。
(Sample No. 300)
As a base material powder, Al—Si—Fe alloy powder C (composition of Al-15Si-5Fe-2.5Cu-1Mg (unit: mass%)) containing 1.8 vol% Fe was prepared. This Al—Si—Fe alloy powder C was produced by an atomizing method (average particle size 60 μm). The obtained Al—Si—Fe alloy powder C was molded, sintered, and T6 treated under the same conditions as Sample Nos. 17 and 18, and a sintered alloy of Sample No. 300 was obtained. In the Al—Si—Fe alloy powder C, the Fe component exists as an intermetallic compound (Al 3 Fe).
得られた各焼結合金の断面の光学顕微鏡写真を図1〜図4に示す。図1は、最大粒径5μmの鉄粉末を混合した試料No.1、図2は、最大粒径30μmの鉄粉末を混合した試料No.5、図3は、鉄粉末を混合しなかった試料No.100、図4は、Al-Si-Fe合金粉末Cを用いた試料No.300を示す。図1〜3において、筋状に連続して見える部分は、母材粒子の旧粉末粒界gb、図1,2,4において濃色の(暗い)塊部分は、金属間化合物imc、図1〜4において黒い塊部分は、気孔(ポア)Pである。 Optical micrographs of cross sections of the obtained sintered alloys are shown in FIGS. Fig. 1 shows sample No. 1 mixed with iron powder with a maximum particle size of 5 µm, Fig. 2 shows sample No. 5 mixed with iron powder with a maximum particle size of 30 µm, and Fig. 3 shows a sample without iron powder mixed. No. 100 and FIG. 4 show Sample No. 300 using Al—Si—Fe alloy powder C. In FIGS. 1 to 3, the portion that appears continuously in a streak shape is the old powder grain boundary gb of the base material particles, and in FIG. 1, 2, and 4, the dark (dark) lump portion is the intermetallic compound imc, In ˜4, the black lump portion is a pore P.
図1,2に示すように、微細な鉄粉末を用いた試料は、母材粒子の旧粉末粒界gb上に金属間化合物imcが点在していることが分かる。また、鉄粉末の粒径が大きくなると、大きな金属間化合物が生成されることが分かる。更に、鉄粉末の最大粒径が30μm以下の試料では、添加した鉄粉末の95％以上が金属間化合物として存在すること、及び鉄粉末の最大粒径が30μm超の試料では、鉄成分が多く残存することが確認された。なお、金属間化合物(ここではAl3Fe)の存在は、例えば、X線回折などで分析することで確認できる。また、添加粉末の構成成分(ここでは鉄成分)の存在は、例えば、EDX(エネルギー分散型蛍光X線分析)などにより分析することで確認できる。 As shown in FIGS. 1 and 2, it can be seen that the sample using fine iron powder is interspersed with the intermetallic compound imc on the old powder grain boundary gb of the base material particles. Moreover, it turns out that a big intermetallic compound is produced | generated when the particle size of iron powder becomes large. Furthermore, in the sample whose maximum particle size of iron powder is 30 μm or less, 95% or more of the added iron powder exists as an intermetallic compound, and in the sample whose maximum particle size of iron powder exceeds 30 μm, there are many iron components. It was confirmed that it remained. Note that the presence of an intermetallic compound (here, Al 3 Fe) can be confirmed by analysis by, for example, X-ray diffraction. In addition, the presence of a constituent component (here, iron component) of the additive powder can be confirmed by analyzing by, for example, EDX (energy dispersive X-ray fluorescence analysis).
一方、図3に示すように微細な鉄粉末を混合しなかった試料No.100は、金属間化合物がほとんど存在しないことが分かる。また、この試料No.100は、旧粉末粒界が非常に明確であることが分かる。 On the other hand, as shown in FIG. 3, Sample No. 100 in which the fine iron powder was not mixed shows that there is almost no intermetallic compound. Moreover, this sample No. 100 shows that the old powder grain boundary is very clear.
他方、図4に示すようにAl-Si-Fe合金粉末Cを用いた試料No.300は、母材全体に金属間化合物imcが分散して存在し、旧粉末粒界上にはほとんど存在しないことが分かる。この母材全体に分散している金属間化合物は、粉末段階で存在したものがそのまま残存していると考えられる。 On the other hand, as shown in FIG. 4, sample No. 300 using Al-Si-Fe alloy powder C has the intermetallic compound imc dispersed in the entire base material and hardly exists on the old powder grain boundary. I understand that. It is considered that the intermetallic compound dispersed in the entire base material remains as it is at the powder stage.
試料No.1〜10,及び試料No.300について、母材粒子の旧粉末粒界上に存在する金属間化合物が旧粉末粒界を切断する長さを切断長とし、旧粉末粒界の粒界長に対する切断長の割合(切断長割合)を調べた。その結果を表1に示す。切断長割合の算出は、以下のように行った。焼結合金の任意の断面における顕微鏡写真(400倍)の観察像を画像解析し、観察像中の全ての旧粉末粒界長の合計長さを算出する。また、旧粉末粒界ごとにその粒界上に存在する全ての金属間化合物の切断長の合計を算出する。そして、(金属間化合物の切断長の合計の総和)/(旧粉末粒界長の合計長さ)をその観察像の切断長割合とし、10個の観察像の切断長割合を求め、その平均をその焼結合金の切断長割合とする。金属間化合物の切断長は、旧粉末粒界上に存在する金属間化合物において旧粉末粒界と交わる二つの交点の最短距離を利用する。 For sample No. 1 to 10 and sample No. 300, the length at which the intermetallic compound existing on the old powder grain boundary of the base material particle cuts the old powder grain boundary is defined as the cutting length, and the grain of the old powder grain boundary The ratio of the cutting length to the field length (cutting length ratio) was examined. The results are shown in Table 1. The cutting length ratio was calculated as follows. Image analysis is performed on an observation image of a micrograph (400 times) in an arbitrary cross section of the sintered alloy, and a total length of all old powder grain boundary lengths in the observation image is calculated. Moreover, the sum total of the cutting length of all the intermetallic compounds which exist on the grain boundary for every old powder grain boundary is calculated. Then, (total sum of cutting lengths of intermetallic compounds) / (total length of old powder grain boundary length) as the cutting length ratio of the observed image, to determine the cutting length ratio of 10 observation images, the average Is the cutting length ratio of the sintered alloy. The cutting length of the intermetallic compound uses the shortest distance between two intersections that intersect the old powder grain boundary in the intermetallic compound existing on the old powder grain boundary.
得られた各焼結合金について、室温での引張強度、130℃での引張強度、室温での破断伸び、耐摩耗性、硬度HRBを調べた。その結果を表1、及び図6〜9のグラフに示す。図6〜9のグラフは、母材粉末として、Al合金粉末Aを用いた試料の結果を示す。 Each obtained sintered alloy was examined for tensile strength at room temperature, tensile strength at 130 ° C., elongation at break at room temperature, wear resistance, and hardness HRB. The results are shown in Table 1 and the graphs of FIGS. The graphs of FIGS. 6 to 9 show the results of samples using Al alloy powder A as the base material powder.
耐摩耗性は、以下のように測定した。図5は、耐摩耗性の測定方法を説明する説明図である。試料ごとに評価材1を用意し、評価材1の表面に一対の相手材2を離間して配置し、各相手材2に同じ荷重を加えた状態で、評価材1を所定の距離だけ回転させる。その後、評価材1の表面に生じた摩耗跡の深さを形状測定器にて測定した。この摩耗跡の深さを摩耗量として耐摩耗性の評価に用いる。評価材1は、直径φ35mm、厚さ10mmとし、相手材2は、5mm×10mm×7mm(評価材1との接触面:5mm×10mm)とし、窒化鋼(HV=900)で作製した。回転条件は、速度:14.5cm/sec、回転距離:260m、荷重:50kg/相手材1個、雰囲気:油中(市販のエンジンオイルを使用)、温度:室温(約20℃)とした。 The wear resistance was measured as follows. FIG. 5 is an explanatory view for explaining a method for measuring wear resistance. Prepare evaluation material 1 for each sample, place a pair of opposing materials 2 apart on the surface of evaluation material 1, and rotate evaluation material 1 by a predetermined distance while applying the same load to each opposing material 2. Let Thereafter, the depth of wear marks generated on the surface of the evaluation material 1 was measured with a shape measuring instrument. The depth of this wear trace is used as an amount of wear for evaluation of wear resistance. The evaluation material 1 had a diameter of 35 mm and a thickness of 10 mm, the counterpart material 2 had a size of 5 mm × 10 mm × 7 mm (contact surface with the evaluation material 1: 5 mm × 10 mm), and was made of nitrided steel (HV = 900). The rotation conditions were as follows: speed: 14.5 cm / sec, rotation distance: 260 m, load: 50 kg / part 1 material, atmosphere: in oil (using commercially available engine oil), temperature: room temperature (about 20 ° C.).
表1及び図6〜9のグラフに示すように、最大粒径が30μm以下の添加粉末(ここでは鉄粉末)を用いることで、強度が飛躍的に向上することが分かる。この理由は、焼結合金中に添加粉末の粒子が実質的に残存せず、かつ旧粉末粒界上に金属間化合物が点在することで母材粒子が金属間化合物を介して強固に結合されると共に、金属間化合物や旧粉末粒界に沿った割れの進展などが生じ難くなったためであると考えられる。試料No.100は、旧粉末粒界が明確であることから、旧粉末粒界に沿った割れが生じ易いと考えられる。 As shown in the graphs of Table 1 and FIGS. 6 to 9, it can be seen that the strength is drastically improved by using an additive powder (here, iron powder) having a maximum particle size of 30 μm or less. The reason for this is that substantially no added powder particles remain in the sintered alloy, and the intermetallic compound is scattered on the old powder grain boundary, so that the base material particles are firmly bonded via the intermetallic compound. In addition, it is considered that the progress of cracks along the intermetallic compound and the old powder grain boundary is less likely to occur. In Sample No. 100, since the old powder grain boundary is clear, it is considered that cracking along the old powder grain boundary is likely to occur.
また、図6〜9のグラフに示すように、鉄粉末の添加量が0.2〜5体積％の範囲であると、室温における破断伸びの低下を少なく抑えて室温での引張強度に優れると共に、130℃での引張強度、耐摩耗性、硬度HRBといった機械的特性に優れることが確認できた。 In addition, as shown in the graphs of FIGS. 6 to 9, when the addition amount of the iron powder is in the range of 0.2 to 5% by volume, the decrease in breaking elongation at room temperature is suppressed to be excellent in tensile strength at room temperature, and 130 It was confirmed that the mechanical properties such as tensile strength at ℃, wear resistance, and hardness HRB were excellent.
更に、試料No.1〜9について冷間サイジング(室温(RT),8ton/cm2)を行ったところ、冷間サイジングを十分に行えた。このことから、本発明焼結合金は、高強度で、寸法精度に優れるアルミニウム合金部品の実現に貢献することができると期待される。 Further, when the samples No. 1 to 9 were subjected to cold sizing (room temperature (RT), 8 ton / cm 2 ), the cold sizing was sufficiently performed. Therefore, the sintered alloy of the present invention is expected to contribute to the realization of an aluminum alloy part having high strength and excellent dimensional accuracy.
なお、上述した実施形態は、本発明の要旨を逸脱することなく、適宜変更することが可能であり、上述した構成に限定されるものではない。例えば、母材の組成や添加粉末の組成、含有量を適宜変更することができる。 The above-described embodiment can be appropriately changed without departing from the gist of the present invention, and is not limited to the above-described configuration. For example, the composition of the base material, the composition of the additive powder, and the content can be changed as appropriate.
本発明アルミニウム焼結合金は、軽量化が望まれる種々の部品、例えば、自動二輪車や自動四輪車といった車両の内燃機関の構成部品、例えば、カムスプロケット、VVTロータやハウジング、オイルポンプローターなどの素材などに好適に利用することができる。本発明アルミニウム焼結合金用粉末は、本発明アルミニウム焼結合金の製造に好適に利用することができる。 The aluminum sintered alloy of the present invention is used for various parts that are desired to be reduced in weight, for example, components of internal combustion engines of vehicles such as motorcycles and automobiles, such as cam sprockets, VVT rotors, housings, oil pump rotors, etc. It can use suitably for a raw material etc. The powder for sintered aluminum alloy of the present invention can be suitably used for producing the sintered aluminum alloy of the present invention.
1 評価材 2 相手材 gb 旧粉末粒界 imc 金属間化合物 P ポア
100 旧粉末粒界
1 Evaluation material 2 Mating material gb Old grain boundary imc Intermetallic compound P Pore
100 Old powder grain boundary
Claims (4)
遷移金属元素を0.2体積％以上5体積％以下含有し、
母材を構成する母材粒子の旧粉末粒界上に、Alと前記遷移金属元素とを含む金属間化合物が点在しており、
前記旧粉末粒界上に存在する金属間化合物が旧粉末粒界を切断する長さを切断長とするとき、前記旧粉末粒界の粒界長に対する前記切断長の割合が3％以上50％以下であることを特徴とするアルミニウム焼結合金。 An aluminum sintered alloy whose base material is Al or Al alloy,
Containing transition metal elements in an amount of 0.2% to 5% by volume,
Intermetallic compounds containing Al and the transition metal element are scattered on the old powder grain boundary of the base material particles constituting the base material,
When the length at which the intermetallic compound existing on the old powder grain boundary cuts the old powder grain boundary is a cutting length, the ratio of the cutting length to the grain boundary length of the old powder grain boundary is 3% or more and 50% An aluminum sintered alloy characterized by:
Al又はAl合金からなる母材粉末と、遷移金属元素からなる添加粉末とが混合されてなり、
前記添加粉末は、0.2体積％以上5体積％以下含有され、
前記添加粉末の最大粒径が30μm以下であることを特徴とするアルミニウム焼結合金用粉末。 A powder for an aluminum sintered alloy used for an aluminum sintered alloy whose base material is Al or an Al alloy,
A base material powder made of Al or an Al alloy and an additive powder made of a transition metal element are mixed,
The additive powder is contained in an amount of 0.2% to 5% by volume,
A powder for an aluminum sintered alloy, wherein the additive powder has a maximum particle size of 30 μm or less.
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2014504334A (en) * | 2010-12-13 | 2014-02-20 | ジーケーエヌ シンター メタルズ、エル・エル・シー | Aluminum alloy powder metal with high thermal conductivity |
| JP2017155270A (en) * | 2016-02-29 | 2017-09-07 | 昭和電工株式会社 | Aluminum alloy atomized powder for extrusion material, manufacturing method of aluminum alloy atomized powder for extrusion material, manufacturing method of extrusion material, manufacturing method of forging article and forging article |
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| JPS5941432A (en) * | 1982-08-30 | 1984-03-07 | Mitsubishi Metal Corp | Sintered al alloy useful as sliding member |
| JPS62224602A (en) * | 1986-03-26 | 1987-10-02 | Showa Denko Kk | Production of sintered aluminum alloy forging |
| JPH0344441A (en) * | 1989-07-11 | 1991-02-26 | Kobe Steel Ltd | Formed body of aluminum alloy with high strength and heat resistance and its production |
| JPH07278713A (en) * | 1994-04-07 | 1995-10-24 | Sumitomo Electric Ind Ltd | Aluminum powder alloy and method for producing the same |
| JP2001240902A (en) * | 2000-02-29 | 2001-09-04 | Toyota Central Res & Dev Lab Inc | Low thermal conductivity aluminum sintered material, method for producing the same, and piston top surface material |
| JP2003328053A (en) * | 2002-05-14 | 2003-11-19 | Hitachi Powdered Metals Co Ltd | Manufacturing method of sintered aluminum alloy |
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Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5941432A (en) * | 1982-08-30 | 1984-03-07 | Mitsubishi Metal Corp | Sintered al alloy useful as sliding member |
| JPS62224602A (en) * | 1986-03-26 | 1987-10-02 | Showa Denko Kk | Production of sintered aluminum alloy forging |
| JPH0344441A (en) * | 1989-07-11 | 1991-02-26 | Kobe Steel Ltd | Formed body of aluminum alloy with high strength and heat resistance and its production |
| JPH07278713A (en) * | 1994-04-07 | 1995-10-24 | Sumitomo Electric Ind Ltd | Aluminum powder alloy and method for producing the same |
| JP2001240902A (en) * | 2000-02-29 | 2001-09-04 | Toyota Central Res & Dev Lab Inc | Low thermal conductivity aluminum sintered material, method for producing the same, and piston top surface material |
| JP2003328053A (en) * | 2002-05-14 | 2003-11-19 | Hitachi Powdered Metals Co Ltd | Manufacturing method of sintered aluminum alloy |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2014504334A (en) * | 2010-12-13 | 2014-02-20 | ジーケーエヌ シンター メタルズ、エル・エル・シー | Aluminum alloy powder metal with high thermal conductivity |
| US10058916B2 (en) | 2010-12-13 | 2018-08-28 | Gkn Sinter Metals, Llc | Aluminum alloy powder metal with high thermal conductivity |
| JP2017155270A (en) * | 2016-02-29 | 2017-09-07 | 昭和電工株式会社 | Aluminum alloy atomized powder for extrusion material, manufacturing method of aluminum alloy atomized powder for extrusion material, manufacturing method of extrusion material, manufacturing method of forging article and forging article |
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| JP5560549B2 (en) | 2014-07-30 |
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