JP2020041224A - Aluminum alloy ingot - Google Patents

Aluminum alloy ingot Download PDF

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JP2020041224A
JP2020041224A JP2019218816A JP2019218816A JP2020041224A JP 2020041224 A JP2020041224 A JP 2020041224A JP 2019218816 A JP2019218816 A JP 2019218816A JP 2019218816 A JP2019218816 A JP 2019218816A JP 2020041224 A JP2020041224 A JP 2020041224A
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mass
aluminum alloy
ingot
mold
casting
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JP6978481B2 (en
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鉄浩 水野
Tetsuhiro Mizuno
鉄浩 水野
嘉公 大橋
Yoshikimi Ohashi
嘉公 大橋
義男 水野
Yoshio Mizuno
義男 水野
尚也 山下
Naoya Yamashita
尚也 山下
健太郎 平間
Kentaro Hirama
健太郎 平間
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Resonac Holdings Corp
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Showa Denko KK
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Abstract

To provide an aluminum alloy ingot that contains a low melting point element and has high surface smoothness.SOLUTION: An aluminum alloy ingot is an ingot composed of an aluminum alloy containing at least one element of Pb: 0.2 mass%-2 mass%, Bi: 0.01 mass%-3 mass%, Sn: 0.01 mass%-1.5 mass%, In: 0.01 mass%-0.2 mass%, where the ingot surface has an unevenness difference of 1.5 mm or less.SELECTED DRAWING: Figure 1

Description

本発明は低融点元素を含むアルミニウム合金鋳塊に関する。   The present invention relates to an aluminum alloy ingot containing a low melting point element.

アルミニウム合金の切削性を向上させるためにＰｂ（融点３２７℃）、Ｂｉ（融点２７１℃）、Ｓｎ（融点２３２℃）、Ｉｎ（融点１５６℃）といった低融点元素を添加することがある。これらの低融点元素およびこれらの化合物は合金中に分散しており、切削時の加工熱によって溶融してその部分を起点として亀裂が発生し伝播する。そして、亀裂発生と伝播を繰り返すことによって切り屑が分断されて切削性が向上する。切削に供されるアルミニウム合金素材の多くは、材料金属を溶解して連続鋳造した鋳塊、あるいは鋳塊を加工した押出材や圧延材である。   Low melting elements such as Pb (melting point 327 ° C.), Bi (melting point 271 ° C.), Sn (melting point 232 ° C.), and In (melting point 156 ° C.) may be added to improve the machinability of the aluminum alloy. These low-melting elements and these compounds are dispersed in the alloy, are melted by the processing heat during cutting, and cracks are generated and propagated starting from that portion. Then, by repeatedly generating and propagating cracks, the chips are cut off, and the machinability is improved. Most of the aluminum alloy materials used for cutting are ingots obtained by melting and casting a material metal continuously, or extruded materials or rolled materials obtained by processing the ingots.

アルミニウム合金の連続鋳造装置では、鋳塊の焼き付きや再溶融を防ぐために金型の内面に自己潤滑性を有するカーボン製ライナーを取り付けて潤滑性を向上させることが知られている（特許文献１、２、３参照）。   In an aluminum alloy continuous casting apparatus, it is known that a lubricating property is improved by attaching a carbon liner having self-lubricating property to an inner surface of a mold in order to prevent seizure or remelting of an ingot (Patent Document 1, 2, 3).

特許文献１には、金型本体の内周面に黒鉛製ライナーを取り付けたＡｌ−Ｍｇ系合金の連続鋳造用金型が記載されている。また、前記ライナーにはカーボン粒子と有機系接着剤を含むカーボン溶液を塗布して潤滑性を持続させている。   Patent Literature 1 discloses a mold for continuous casting of an Al-Mg-based alloy in which a graphite liner is attached to an inner peripheral surface of a mold body. Further, a lubricating property is maintained by applying a carbon solution containing carbon particles and an organic adhesive to the liner.

特許文献２には、ホットトップ連続鋳造装置において、金型の内周面に離型剤を供給するディストリビューターおよびグラファイト製の機能性リングを組み込むことが記載されている。   Patent Document 2 describes that a hot top continuous casting apparatus incorporates a distributor for supplying a release agent to the inner peripheral surface of a mold and a functional ring made of graphite.

特許文献３には、横型連続鋳造用鋳型において、冷却不足による凝固壁の弱体化を防ぐために、熱伝導度が１５１Ｗ／（ｍ・Ｋ）以上（１３０Ｋｃａｌ／ｍｈ℃以上）のカーボンスリーブを用いることが記載されている。   Patent Document 3 discloses that in a horizontal continuous casting mold, a carbon sleeve having a thermal conductivity of 151 W / (m · K) or more (130 Kcal / mh ° C or more) is used in order to prevent weakening of a solidified wall due to insufficient cooling. Is described.

特開２００９−３９７６０号公報JP 2009-39760 A 特開２００２−３０１５４７号公報JP 2002-301547 A 特開平１１−１７０００８号公報JP-A-11-170008

上述した快削性アルミニウム合金の鋳造では溶湯の凝固によってＰｂ−Ｂｉ、Ｂｉ−Ｓｎ、Ｐｂ−Ｓｎ、Ｉｎ−Ｂｉ、Ｉｎ−Ｓｎといった低融点化合物を形成する。金型からの冷却によって鋳塊の表面が凝固しても、連続的に供給される溶湯の熱によって低融点化合物の再溶融が起こり易く、再溶融した低融点化合物が金型に付着して鋳肌にキズが発生するという問題点がある。   In the casting of the above-mentioned free-cutting aluminum alloy, a low melting point compound such as Pb-Bi, Bi-Sn, Pb-Sn, In-Bi, or In-Sn is formed by solidification of the molten metal. Even if the surface of the ingot solidifies due to cooling from the mold, the remelting of the low-melting compound tends to occur due to the heat of the continuously supplied molten metal, and the remelted low-melting compound adheres to the mold and is cast. There is a problem that the skin is scratched.

特許文献１に記載された金型はＡｌ−Ｍｇ系合金用である。Ａｌ−Ｍｇ系合金では前記快削性アルミニウム合金のような低融点化合物が形成されないので、快削性アルミニウム合金の鋳造には適さない。特許文献２に記載された金型も低融点化合物の再溶融による鋳肌品質の低下を解消できるものではない。しかも、離型性の高い泡を形成するために気体と潤滑油の混合物を形成する必要があり、ホットトップ連続鋳造装置に限定されており汎用性が乏しい。また、特許文献３に記載された熱伝導度の高いカーボンスリーブは、実施例のＡｌ−Ｓｉ共晶合金の鋳造には適しているが、低融点元素を含有するアルミニウム合金の鋳造において低融点化合物の再溶融を防ぎうるものではない。   The mold described in Patent Literature 1 is for an Al-Mg based alloy. Al-Mg based alloys are not suitable for casting free-cutting aluminum alloys because low-melting compounds like the free-cutting aluminum alloys are not formed. The mold described in Patent Literature 2 cannot solve the deterioration of the casting surface quality due to the remelting of the low melting point compound. Moreover, it is necessary to form a mixture of a gas and a lubricating oil in order to form a foam having a high mold release property, and it is limited to a hot-top continuous casting apparatus, which is poor in versatility. Further, the carbon sleeve having a high thermal conductivity described in Patent Document 3 is suitable for casting the Al-Si eutectic alloy of the example, but has a low melting point compound in the casting of an aluminum alloy containing a low melting point element. It cannot prevent re-melting of the material.

本発明は、上述した背景技術に鑑み、低融点元素を含有する特定組成のアルミニウム合金からなり、鋳肌品質の良い鋳塊を提供する。   In view of the background art described above, the present invention provides an ingot made of an aluminum alloy having a specific composition containing a low melting point element and having good casting surface quality.

即ち、本発明は下記［１］〜［５］に記載の構成を有する。   That is, the present invention has the configurations described in the following [1] to [5].

［１］Ｐｂ：０．２質量％〜２質量％、Ｂｉ：０．０１質量％〜３質量％、Ｓｎ：０．０１質量％〜１．５質量％、Ｉｎ：０．０１質量％〜０．２質量％のうちの1種以上の元素を含むアルミニウム合金からなる鋳塊であり、鋳肌の凹凸差が１．５ｍｍ以下であることを特徴とするアルミニウム合金鋳塊。   [1] Pb: 0.2% to 2% by mass, Bi: 0.01% to 3% by mass, Sn: 0.01% to 1.5% by mass, In: 0.01% to 0% by mass An aluminum alloy ingot comprising an aluminum alloy containing one or more elements of 2% by mass, wherein a difference in unevenness of a casting surface is 1.5 mm or less.

［２］前記アルミニウム合金は、さらに、Ｃｕ：３．５質量％〜６．５質量％およびＺｎ：０．０１質量％〜１．２質量％を含有する前項１に記載のアルミニウム合金鋳塊。   [2] The aluminum alloy ingot according to the above item 1, wherein the aluminum alloy further contains Cu: 3.5% by mass to 6.5% by mass and Zn: 0.01% by mass to 1.2% by mass.

［３］前記アルミニウム合金は、さらに、Ｓｉ：０．０１質量％〜１．０質量％、Ｍｇ：０．０１質量％〜２．０質量％、Ｔｉ：０．０１質量％〜０．１質量％、Ｂ：０．０００１質量％〜０．０１質量％のうちの1種以上の元素を含む前項２に記載のアルミニウム合金鋳塊。   [3] The aluminum alloy further includes Si: 0.01% by mass to 1.0% by mass, Mg: 0.01% by mass to 2.0% by mass, Ti: 0.01% by mass to 0.1% by mass. %, B: the aluminum alloy ingot according to the above item 2, which contains one or more elements of 0.0001% by mass to 0.01% by mass.

［４］前記アルミニウム合金は、さらに、Ｍｇ：０．３質量％〜１．５質量％およびＳｉ：０．２質量％〜１．０質量％を含有する前項１に記載のアルミニウム合金鋳塊。   [4] The aluminum alloy ingot according to the above item 1, wherein the aluminum alloy further contains 0.3% to 1.5% by mass of Mg and 0.2% to 1.0% by mass of Si.

［５］前記アルミニウム合金は、さらに、Ｃｕ：０．０１質量％〜２．０質量％、Ｚｎ：０．０１質量％〜０．２質量％、Ｔｉ：０．０１質量％〜０．１質量％、Ｂ：０．０００１質量％〜０．０１質量％のうちの１種以上の元素を含む前項４に記載のアルミニウム合金鋳塊。   [5] The aluminum alloy further includes Cu: 0.01% by mass to 2.0% by mass, Zn: 0.01% by mass to 0.2% by mass, and Ti: 0.01% by mass to 0.1% by mass. %, B: The aluminum alloy ingot according to the above item 4, which contains one or more elements of 0.0001% by mass to 0.01% by mass.

上記［１］〜［５］に記載のアルミニウム合金鋳塊は、低融点元素を含んでいるにもかかわらず鋳肌の凹凸差が１．５ｍｍ以下であり、表面平滑性が高い。   The aluminum alloy ingot according to any one of [1] to [5] has a surface roughness of 1.5 mm or less and a high surface smoothness despite containing a low-melting element.

本発明のアルミニウム合金鋳塊の連続鋳造方法を示す断面図である。It is sectional drawing which shows the continuous casting method of the aluminum alloy ingot of this invention.

［アルミニウム合金］
本発明を適用するアルミニウム合金は低融点元素であるＰｂ、Ｂｉ、Ｓｎ、Ｉｎのうちの１種以上の元素を含む合金であり、前記低融点元素のみが添加されたアルミニウム合金または前記低融点元素以外の元素が添加されたアルミニウム合金である。 [Aluminum alloy]
The aluminum alloy to which the present invention is applied is an alloy containing one or more of the low-melting elements Pb, Bi, Sn, and In, and the aluminum alloy to which only the low-melting element is added or the low-melting element This is an aluminum alloy to which elements other than the above are added.

前記低融点元素は切削性を向上させるために添加される元素であり、１種または任意の組み合わせで２種以上が添加されている。Ｐｂの融点は３２７℃、Ｂｉの融点は２７１℃、Ｓｎの融点は２３２℃、Ｉｎの融点は１５６℃であり、これらの化合物、即ちＰｂ−Ｂｉ、Ｂｉ−Ｓｎ、Ｐｂ−Ｓｎ、Ｉｎ−Ｂｉ、Ｉｎ−Ｓｎも共晶温度が１８３℃以下の低融点化合物である。各化合物の共晶温度は、Ｐｂ−Ｂｉが１２５℃、Ｂｉ−Ｓｎが１３９℃、Ｐｂ−Ｓｎが１８３℃、Ｉｎ−Ｂｉが７２℃、Ｉｎ−Ｓｎが１１７℃である。   The low melting point element is an element added for improving the machinability, and two or more of them are added alone or in any combination. Pb has a melting point of 327 ° C., Bi has a melting point of 271 ° C., Sn has a melting point of 232 ° C., and In has a melting point of 156 ° C. These compounds, namely, Pb-Bi, Bi-Sn, Pb-Sn, and In-Bi. , In-Sn are also low melting point compounds having a eutectic temperature of 183 ° C or lower. The eutectic temperature of each compound is 125 ° C for Pb-Bi, 139 ° C for Bi-Sn, 183 ° C for Pb-Sn, 72 ° C for In-Bi, and 117 ° C for In-Sn.

アルミニウム合金中の各元素の好ましい濃度は以下のとおりである。Ｐｂ濃度は０．２質量％〜２質量％が好ましく、Ｂｉ濃度は０．０１質量％〜３質量％が好ましく、Ｓｎ濃度は０．０１質量％〜１．５質量％が好ましく、Ｉｎ濃度が０．０１質量％〜０．２質量％が好ましい。いずれの元素においても下限値未満では切削性の向上効果が乏しく、上限値を超えると押出性または耐食性が低下するおそれがある。特に好ましい濃度は、Ｐｂ濃度が０．３質量％〜１．０質量％、Ｂｉ濃度が０．１質量％〜０．６質量％、Ｓｎ濃度が０．２質量％〜１．５質量％、Ｉｎ濃度が０．０８質量％〜０．２質量％である。   Preferred concentrations of each element in the aluminum alloy are as follows. The Pb concentration is preferably 0.2% by mass to 2% by mass, the Bi concentration is preferably 0.01% by mass to 3% by mass, the Sn concentration is preferably 0.01% by mass to 1.5% by mass, and the In concentration is preferably It is preferably 0.01% by mass to 0.2% by mass. If any element is less than the lower limit, the effect of improving machinability is poor, and if it exceeds the upper limit, extrudability or corrosion resistance may be reduced. Particularly preferred concentrations are a Pb concentration of 0.3% by mass to 1.0% by mass, a Bi concentration of 0.1% by mass to 0.6% by mass, a Sn concentration of 0.2% by mass to 1.5% by mass, The In concentration is 0.08% by mass to 0.2% by mass.

前記低融点元素のみが添加されたアルミニウム合金の残部はＡｌおよび不可避不純物である。   The balance of the aluminum alloy to which only the low melting point element is added is Al and inevitable impurities.

前記低融点元素以外に添加される元素として、Ｃｕ、Ｍｇ、Ｓｉ、Ｚｎ、Ｔｉ、Ｂを例示できる。これらの元素はいずれも強度向上に寄与する元素であり、１種または任意の２種以上の元素が添加される。これらのアルミニウム合金における低融点元素の濃度は上述した低融点元素のみを含有するアルミニウム合金における濃度に準じる。また、Ｃｕ、Ｍｇ、Ｓｉ、Ｚｎ、Ｔｉ、Ｂの好ましい濃度は以下のとおりである。   Examples of the element added in addition to the low melting point element include Cu, Mg, Si, Zn, Ti, and B. Each of these elements contributes to the improvement in strength, and one or more two or more elements are added. The concentration of the low-melting element in these aluminum alloys conforms to the concentration in the aluminum alloy containing only the low-melting element described above. The preferred concentrations of Cu, Mg, Si, Zn, Ti, and B are as follows.

２０００系のＡｌ−Ｃｕ系合金において、好ましいＣｕ濃度は３．５質量％〜６．５質量％であり、Ｚｎ濃度は０．０１質量％〜１．２質量％であり、特に好ましいＣｕ濃度は４．５質量％〜６．０質量％であり、Ｚｎ濃度は０．０１質量％〜１．０質量％である。また、ＣｕおよびＺｎの他に、０．０１質量％〜１．０質量％のＳｉ、０．０１質量％〜２．０質量％のＭｇ、０．０１質量％〜０．１質量％のＴｉ、０．０００１質量％〜０．０１質量％のＢのうちのいずれか1種以上が添加されていても良い。残部はＡｌおよび不可避不純物である。   In a 2000-series Al-Cu-based alloy, a preferable Cu concentration is 3.5% by mass to 6.5% by mass, a Zn concentration is 0.01% by mass to 1.2% by mass, and a particularly preferable Cu concentration is It is 4.5% by mass to 6.0% by mass, and the Zn concentration is 0.01% by mass to 1.0% by mass. In addition to Cu and Zn, 0.01% to 1.0% by mass of Si, 0.01% to 2.0% by mass of Mg, and 0.01% to 0.1% by mass of Ti , 0.0001% by mass to 0.01% by mass of B may be added. The balance is Al and unavoidable impurities.

６０００系のＡｌ−Ｍｇ−Ｓｉ系合金において、好ましいＭｇ濃度は０．３質量％〜１．５質量％であり、好ましいＳｉ濃度は０．２質量％〜１．０質量％である。特に好ましいＭｇ濃度は０．５質量％〜０．８質量％であり、Ｓｉ濃度は０．６質量％〜０．９質量％である。また、ＭｇおよびＳｉの他に、０．０１質量％〜２．０質量％のＣｕ、０．０１質量％〜０．２質量％のＺｎ、０．０１質量％〜０．１質量％のＴｉ、０．０００１質量％〜０．０１質量％のＢのうちのいずれか1種以上が添加されていても良い。残部はＡｌおよび不可避不純物である。   In a 6000 Al-Mg-Si alloy, a preferable Mg concentration is 0.3% by mass to 1.5% by mass, and a preferable Si concentration is 0.2% by mass to 1.0% by mass. Particularly preferred Mg concentration is 0.5% by mass to 0.8% by mass, and Si concentration is 0.6% by mass to 0.9% by mass. Further, in addition to Mg and Si, 0.01% to 2.0% by mass of Cu, 0.01% to 0.2% by mass of Zn, and 0.01% to 0.1% by mass of Ti , 0.0001% by mass to 0.01% by mass of B may be added. The balance is Al and unavoidable impurities.

また、前記低融点元素以外に添加される元素はＣｕ、Ｍｇ、Ｓｉ、Ｚｎ、Ｔｉ、Ｂに限定されず、融点が３２７℃を超える元素を添加したアルミニウム合金も本発明に含まれる。即ち、低融点元素としてＰｂ：０．２質量％〜２質量％、Ｂｉ：０．０１質量％〜３質量％、Ｓｎ：０．０１質量％〜１．５質量％、Ｉｎ：０．０１質量％〜０．２質量％のうちの１種以上を含み、さらに融点が３２７℃を超える元素を含み、残部がＡｌおよび不可避不純物からなるアルミニウム合金である。   In addition, the elements to be added other than the low melting point elements are not limited to Cu, Mg, Si, Zn, Ti, and B, and an aluminum alloy to which an element having a melting point exceeding 327 ° C. is added is also included in the present invention. That is, Pb: 0.2% by mass to 2% by mass, Bi: 0.01% by mass to 3% by mass, Sn: 0.01% by mass to 1.5% by mass, and In: 0.01% by mass as low melting point elements. % To 0.2% by mass, an aluminum alloy containing an element having a melting point of more than 327 ° C., and the balance being Al and inevitable impurities.

本発明のアルミニウム合金は上述した組成の合金に限定するものではなく、Ｐｂ、Ｂｉ、Ｓｎ、Ｉｎのうちの１種以上の元素を含む全てのアルミニウム合金に適用できる。
［金型および連続鋳造方法］
図１に、本発明のアルミニウム合金鋳塊を連続鋳造するための連続鋳造用金型およびこの金型を用いた縦型連続鋳造装置の要部を示す。 The aluminum alloy of the present invention is not limited to the alloy having the above-described composition, but can be applied to all aluminum alloys containing one or more of Pb, Bi, Sn, and In.
[Mold and continuous casting method]
FIG. 1 shows a continuous casting mold for continuously casting an aluminum alloy ingot of the present invention and a main part of a vertical continuous casting apparatus using the mold.

金型１０は、断面円形の成形孔１１の両端が開口する筒型であり、筒型の金型本体２０と、金型本体２０の成形孔１１に内嵌めされた筒型のライナー３０とにより構成されている。前記成形孔１１の一端は溶湯Ｍの注入口１２であり、他端は鋳塊Ｓの鋳出口１３である。   The mold 10 is a cylindrical shape in which both ends of a molding hole 11 having a circular cross section are opened, and includes a cylindrical mold body 20 and a cylindrical liner 30 which is fitted in the molding hole 11 of the mold body 20. It is configured. One end of the forming hole 11 is an inlet 12 for the molten metal M, and the other end is a casting outlet 13 for the ingot S.

金型本体２０は内部に冷却水Ｃを流通させるキャビティ２１を有し、上部にキャビテイィへ２１への入口２２が設けられ、前記鋳出口１３を囲んで噴出口２３が設けられている。入口２２から導入された冷却水Ｃは、キャビティ２１内を流通して成形孔１１内の溶湯Ｍを金型本体２０および成形孔１１に内嵌めされた筒型のライナー３０を介し一次冷却して凝固させ、噴出口２３から噴出して鋳出されてくる鋳塊Ｓに吹き付けられて鋳塊Ｓを二次冷却する。また、前記金型本体２０の内周面２５の鋳出口１３側の一部を除く領域に、ライナー３０の厚み相当の凹部２６が形成されている。前記金型本体２０の材料は限定されず、アルミニウム、鉄、銅等の周知金属材料を適宜用いることができる。   The mold body 20 has a cavity 21 through which the cooling water C flows, an inlet 22 to the cavity 21 is provided at an upper portion, and an injection port 23 surrounding the casting port 13 is provided. The cooling water C introduced from the inlet 22 flows through the cavity 21 and primarily cools the molten metal M in the forming hole 11 through the mold body 20 and the cylindrical liner 30 fitted in the forming hole 11. The ingot is solidified and is sprayed onto the ingot S which is ejected and ejected from the ejection port 23 to cool the ingot S secondarily. A concave portion 26 corresponding to the thickness of the liner 30 is formed in a region except for a part of the inner peripheral surface 25 of the mold main body 20 on the casting outlet 13 side. The material of the mold body 20 is not limited, and a well-known metal material such as aluminum, iron, and copper can be appropriately used.

ライナー３０は、熱伝導度が６０Ｗ／（ｍ・Ｋ）〜１３９Ｗ／（ｍ・Ｋ）のカーボン製であり、内周面３１の表面粗さはＪＩＳ Ｂ０６０１ ２００１で規定された最大高さＲｚで１μｍ〜２５μｍに調整され、平滑性の高い内周面３１が形成されている。前記ライナー３０は金型本体２０の凹部２６に焼き嵌めにより嵌合され、ライナー３０の内周面３１と金型本体２５の内周面２５の下方部とが連続する曲面を形成し、この曲面が金型１０の成形孔１１の壁面１１ａを構成している。従来の金型に用いられるカーボンライナー、例えば、特許文献３に記載されているカーボンライナー（スリーブ）の熱伝導度は１５１Ｗ／（ｍ・Ｋ）以上（１３０Ｋｃａｌ／ｍｈ℃以上）であり、前記ライナー３０は従来よりも熱伝導度の低いカーボンからなる。   The liner 30 is made of carbon having a thermal conductivity of 60 W / (m · K) to 139 W / (m · K), and the surface roughness of the inner peripheral surface 31 is the maximum height Rz specified in JIS B0601 2001. The inner peripheral surface 31 is adjusted to 1 μm to 25 μm and has high smoothness. The liner 30 is fitted into the recess 26 of the mold body 20 by shrink fitting, and forms a curved surface where the inner peripheral surface 31 of the liner 30 and the lower portion of the inner peripheral surface 25 of the mold body 25 are continuous. Constitutes the wall surface 11a of the molding hole 11 of the mold 10. A carbon liner used in a conventional mold, for example, a carbon liner (sleeve) described in Patent Document 3 has a thermal conductivity of 151 W / (m · K) or more (130 Kcal / mh ° C. or more). Numeral 30 is made of carbon having lower thermal conductivity than the conventional one.

アルミニウム合金の連続鋳造において、金型１０の注入口１２から成形孔１１に注入された溶湯Ｍは、壁面１１ａから一次冷却を受けて外周面から中心へと凝固が進行し、鋳出口１３に到達する前に、凝固収縮によって鋳塊Ｓの表面が壁面１１ａから離れる。鋳塊Ｓが壁面１１ａから離れて壁面１１ａとの間に隙間ができると、熱移動が妨げられて金型１０から受ける一次冷却能力が低下する。鋳塊Ｓが成形孔１１の壁面１１ａから離れる位置Ｐ（以下、「鋳塊の離型位置」と称する）は、金型１０への抜熱量が大きいほど溶湯Ｍの冷却が早くなって注入口１２に近くなり、逆に抜熱量が小さいほど冷却が遅くなって鋳出口１３に近くなる。一方、成形孔１１内で凝固しつつある鋳塊Ｓは表面に凝固壁が形成されていても中心部は高温の溶融状態にあり、凝固中の鋳塊Ｓの表面は金型１０から冷却を受けながらも中心部からの熱を受けている。このため、凝固壁の形成が不十分なままで鋳塊Ｓが離型すると、中心部からの熱によって鋳塊表面、特に低融点化合物が再溶融するおそれがある。   In the continuous casting of the aluminum alloy, the molten metal M injected into the molding hole 11 from the injection port 12 of the mold 10 undergoes primary cooling from the wall surface 11a and solidifies from the outer peripheral surface to the center, and reaches the casting outlet 13. Before the solidification shrinkage, the surface of the ingot S separates from the wall surface 11a. When the ingot S separates from the wall surface 11a and forms a gap between the ingot S and the wall surface 11a, heat transfer is hindered, and the primary cooling ability received from the mold 10 is reduced. At a position P where the ingot S is separated from the wall surface 11a of the molding hole 11 (hereinafter, referred to as a "ingot release position"), the larger the amount of heat removed to the mold 10, the faster the cooling of the molten metal M becomes and the more the injection port becomes. 12 and conversely, the smaller the heat removal amount, the slower the cooling and the closer to the casting outlet 13. On the other hand, the ingot S that is solidifying in the forming hole 11 has a high-temperature molten state at the center even if a solidified wall is formed on the surface, and the surface of the ingot S during solidification is cooled from the mold 10 by the mold 10. While receiving heat from the center. For this reason, if the ingot S is released from the mold while the formation of the solidified wall is insufficient, the surface of the ingot, particularly the low melting point compound, may be re-melted by heat from the center.

上述した溶湯Ｍの凝固過程において、ライナー３０の熱伝導度が高い程抜熱量が大きく冷却が早くなって鋳塊Ｓの離型位置Ｐが注入口１２に近くなる。逆に、ライナー３０の熱伝導度が低い程抜熱量が小さく冷却が遅くなって鋳塊Ｓの離型位置Ｐが鋳出口１３に近くなる。本発明のアルミニウム合金鋳塊を製造するに際し、金型１０は、従来のカーボンライナー、例えば上記の熱伝導度が１６２Ｗ／（ｍ・Ｋ）のカーボンライナーよりも熱伝導度の低いライナー３０を用いているので、従来の連続鋳造よりも鋳塊Ｓの離型位置Ｐが鋳出口１３側に移動する。そして、鋳塊Ｓの離型位置Ｐが鋳出口１３側に移動することで、一次冷却を受ける時間が長くなり離型によって一次冷却能力が低下する期間が短縮されるので、金型１０から十分な冷却を受けることができる。また、鋳塊Ｓの離型位置Ｐが鋳出口１３に近くなることで噴出口２３までの距離が短くなるので、離型した鋳塊Ｓが冷却水Ｃによる二次冷却を受けるまでの時間が短縮される。従って、熱伝導度の低いライナー３０を用いることにより、成形孔１１の壁面１１ａから冷却される一次冷却時間が長くなり、離型によって一次冷却能力が低下する期間が短縮され、かつ一次冷却後に二次冷却を受けるまでの時間が短縮される。その結果、鋳塊Ｓが十分に冷却されて低融点化合物の再溶融が抑制され、再溶融による湯漏れや鋳肌の荒れが抑制される。   In the solidification process of the molten metal M described above, the higher the thermal conductivity of the liner 30 is, the larger the heat removal amount is, the faster the cooling is, and the release position P of the ingot S is closer to the injection port 12. Conversely, the lower the thermal conductivity of the liner 30 is, the smaller the heat removal amount is, the slower the cooling is, and the release position P of the ingot S is closer to the casting outlet 13. In manufacturing the aluminum alloy ingot of the present invention, the mold 10 uses a liner 30 having a lower thermal conductivity than a conventional carbon liner, for example, the above-described carbon liner having a thermal conductivity of 162 W / (m · K). Therefore, the mold release position P of the ingot S moves to the casting outlet 13 side as compared with the conventional continuous casting. When the mold release position P of the ingot S moves to the casting outlet 13 side, the time during which the primary cooling is received becomes longer, and the period during which the primary cooling capacity is reduced by the mold release is shortened. Cooling can be received. Further, since the mold release position P of the ingot S is closer to the casting outlet 13, the distance to the injection port 23 is shortened. Therefore, the time until the released ingot S receives the secondary cooling by the cooling water C is reduced. Be shortened. Therefore, by using the liner 30 having a low thermal conductivity, the primary cooling time for cooling from the wall surface 11a of the molding hole 11 is lengthened, the period during which the primary cooling capacity is reduced by the mold release is shortened, and the primary cooling time is reduced after the primary cooling. The time until the next cooling is received is reduced. As a result, the ingot S is sufficiently cooled and remelting of the low melting point compound is suppressed, and leakage of molten metal and roughening of the casting surface due to remelting are suppressed.

さらに、前記ライナー３０は表面平滑性が高く、カーボン自体がもつ自己潤滑性と表面平滑性により溶湯Ｍや凝固壁の滑りが良く、これらの付着が抑制されて表面平滑性の高い鋳肌が得られる。   Further, the liner 30 has high surface smoothness, and the self-lubricating property and surface smoothness of carbon itself make the molten metal M and the solidified wall slip well, so that the adhesion of these is suppressed and a casting surface with high surface smoothness is obtained. Can be

上述したように、前記ライナー３０は熱伝導度が６０Ｗ／（ｍ・Ｋ）〜１３９Ｗ／（ｍ・Ｋ）のカーボンで構成されている。ライナー３０の熱伝導度が６０Ｗ／（ｍ・Ｋ）未満のカーボンでは一次冷却による冷却が弱く凝固壁の形成が不完全となり、湯漏れによる鋳造失敗の危険があり、１３９Ｗ／（ｍ・Ｋ）を超えるカーボンでは鋳塊Ｓの離型位置Ｐを鋳出口１３側に移動させる効果が小さい。特に好ましい熱伝導度は８０Ｗ／（ｍ・Ｋ）〜１３０Ｗ／（ｍ・Ｋ）である。また、前記ライナー３０の表面は、ＪＩＳ Ｂ０６０１ ２００１で規定された最大高さＲｚが１μｍ〜２５μｍである。最大高さＲｚが１μｍ未満では鋳造時に供給する潤滑油がライナー表面に保持されず、また研磨加工等で平滑な表面を得ようとした場合加工費用が大幅に上がってしまう。２５μｍを超えると上記効果が乏しい。特に好ましい表面の最大高さＲｚは５μｍ〜２５μｍである。   As described above, the liner 30 is made of carbon having a thermal conductivity of 60 W / (m · K) to 139 W / (m · K). If the thermal conductivity of the liner 30 is less than 60 W / (m · K), the cooling by the primary cooling is weak, and the formation of the solidified wall is incomplete. Carbon has a small effect of moving the mold release position P of the ingot S to the casting outlet 13 side. Particularly preferred thermal conductivity is 80 W / (m · K) to 130 W / (m · K). The surface of the liner 30 has a maximum height Rz defined by JIS B0601 2001 of 1 μm to 25 μm. If the maximum height Rz is less than 1 μm, lubricating oil supplied at the time of casting is not retained on the surface of the liner, and if a smooth surface is to be obtained by polishing or the like, the processing cost will be significantly increased. If it exceeds 25 μm, the above effect is poor. Particularly preferred maximum surface height Rz is 5 μm to 25 μm.

前記ライナー３０の製造方法は問わないが、最大高さＲｚが１μｍ〜２５μｍの平滑表面を得るには、冷間等方圧加圧法（ＣＩＰ）による成形品または熱間等方圧加圧法（ＨＩＰ）による成形品であることが好ましい。ＣＩＰ成形およびＨＩＰ成形は等方加圧しているために押出成形に比べて緻密な構造となり、平滑表面が得やすいためである。   Although there is no limitation on the method of manufacturing the liner 30, in order to obtain a smooth surface having a maximum height Rz of 1 μm to 25 μm, a molded product by cold isostatic pressing (CIP) or hot isostatic pressing (HIP) )). This is because the CIP molding and the HIP molding have a more dense structure than is the case with the extrusion molding due to the isotropic pressing, and a smooth surface is easily obtained.

また、前記ライナー３０は、金型本体２０とライナー３０の熱膨張率の差を利用して焼き嵌めることにより金型本体２０に取り付けることが好ましい。カーボンは金型本体２０を構成する金属よりも熱膨張率が小さいので、常温において鋳型本体２０の内径をライナー３０の外径よりも小さく設定し、加熱により内径が拡大した金型本体２０ライナー３０を内嵌めすると、金型１０の温度低下によりライナー３０が金型本体２０に締め付けられた状態で固定される。焼き嵌めで取り付けると金型本体２０とライナー３０とが密着して両者間に隙間ができないので、連続鋳造時にライナー３０から金型本体２０への熱移動が速やかに行われる。また、周方向の全域で金型本体２０とライナー３０が密着するので、周方向における冷却ムラが生じない。
［連続鋳造方法］
図１の縦型連続鋳造装置は溶湯Ｍの供給装置の記載を省略しているが、フロートによるＤＣ鋳造法、ホットトップ鋳造法、気体加圧式ホットトップ鋳造法等の溶湯の供給方式は何ら限定されない。また、前記金型およびアルミニウム合金の連続鋳造方法は鋳造方向を垂直方向に限定するものではなく、水平連続鋳造にも適用できる。前記金型はライナーの熱伝導度および表面粗さに特徴を有しており、どのような鋳造方式の金型にも適用できる。 Further, it is preferable that the liner 30 is attached to the mold body 20 by shrink-fitting using the difference in the coefficient of thermal expansion between the mold body 20 and the liner 30. Since carbon has a smaller coefficient of thermal expansion than the metal constituting the mold body 20, the inner diameter of the mold body 20 is set to be smaller than the outer diameter of the liner 30 at room temperature, and the inner diameter of the mold body 20 is increased by heating. When the inside is fitted, the liner 30 is fixed to the mold body 20 in a state where the temperature of the mold 10 decreases. When shrink fitting is applied, the mold body 20 and the liner 30 are in close contact with each other and there is no gap therebetween, so that the heat transfer from the liner 30 to the mold body 20 is performed quickly during continuous casting. In addition, since the mold body 20 and the liner 30 are in close contact with each other in the entire circumferential direction, uneven cooling in the circumferential direction does not occur.
[Continuous casting method]
The vertical continuous casting apparatus in FIG. 1 omits the description of the apparatus for supplying the molten metal M, but the supply method of the molten metal such as a DC casting method using a float, a hot top casting method, and a gas pressurized hot top casting method is limited at all. Not done. Further, the continuous casting method of the mold and the aluminum alloy is not limited to a vertical casting direction, but can be applied to horizontal continuous casting. The mold is characterized by the thermal conductivity and the surface roughness of the liner, and can be applied to any casting mold.

アルミニウム合金の連続鋳造において、鋳造温度（溶湯Ｍの温度）は６５０℃〜７５０℃の範囲が好ましく、鋳造速度は１０ｍｍ／ｍｉｎ〜２００ｍｍ／ｍｉｎの範囲が好ましい。また、金型１０の噴出口１３噴出させる冷却水量は０．０１ｍ３／ｍｉｎ〜０．５ｍ３／ｍｉｎの範囲が好ましい。これらは凝固に影響を及ぼす条件であり、鋳造温度が７５０℃を超え、鋳造速度が２００ｍｍ／ｍｉｎを超え、冷却水量が０．０１ｍ３／ｍｉｎ未満になると、凝固が遅く成りすぎて平滑性の高い鋳肌の鋳塊鋳造が困難になる。一方、鋳造温度が６５０℃未満、鋳造速度が１０ｍｍ／ｍｉｎ未満、冷却水量が０．５ｍ３／ｍｉｎを超えると凝固が早くなりすぎる。縦型連続鋳造装置においては、溶湯上部まで凝固が進行し平滑性の高い鋳塊鋳造が困難となり、溶湯供給装置まで凝固が進行した場合鋳塊が下降せず、支持台に追従せずに鋳造失敗する可能性がある。 In continuous casting of an aluminum alloy, the casting temperature (temperature of the molten metal M) is preferably in a range of 650 ° C. to 750 ° C., and the casting speed is preferably in a range of 10 mm / min to 200 mm / min. The cooling water which spout 13 is ejected in the die 10 is preferably in the range of 0.01m 3 /min~0.5m 3 / min. These are conditions that affect solidification. If the casting temperature exceeds 750 ° C., the casting speed exceeds 200 mm / min, and the cooling water amount becomes less than 0.01 m 3 / min, solidification becomes too slow and the smoothness decreases. Ingot casting with a high casting surface becomes difficult. On the other hand, when the casting temperature is lower than 650 ° C., the casting speed is lower than 10 mm / min, and the cooling water amount is higher than 0.5 m 3 / min, the solidification is too fast. In the vertical continuous casting device, solidification proceeds to the upper part of the molten metal, making it difficult to cast ingots with high smoothness.If solidification proceeds to the molten metal supply device, the ingot does not descend and does not follow the support table. May fail.

上述した低融点元素を含有するアルミニウム合金を前記金型１０を用いて連続鋳造して作製された鋳塊Ｓは表面平滑性が高く、鋳肌の凹凸差、即ち最も高い凸部から最も低い凹部までの距離は１．５ｍｍ以下である。   The ingot S produced by continuously casting the above-described aluminum alloy containing the low-melting element using the mold 10 has a high surface smoothness, and a difference in unevenness of the casting surface, that is, the highest convex portion to the lowest concave portion. Is 1.5 mm or less.

低融点元素を含有するアルミニウム合金で表面平滑性の高い鋳塊を連続鋳造するに際し、好適な連続鋳造用金型および連続鋳造方法の構成、ならびにそれらの効果は以下に記載したとおりである。   In continuous casting of an ingot having a high surface smoothness with an aluminum alloy containing a low-melting element, preferred configurations of a continuous casting mold and a continuous casting method, and their effects are as described below.

［１］成形孔の一端が溶湯の注入口となされ他端が鋳塊の鋳出口となされた金型本体と、前記金型本体の成形孔に取り付けられたライナーとを備えるアルミニウム合金の連続鋳造用金型であり、
前記ライナーは、熱伝導度が６０Ｗ／（ｍ・Ｋ）〜１３９Ｗ／（ｍ・Ｋ）のカーボンからなり、内周面はＪＩＳ Ｂ０６０１ ２００１で規定された最大高さＲｚが１μｍ〜２５μｍであることを特徴とする連続鋳造用金型。 [1] Continuous casting of an aluminum alloy including a mold body in which one end of a forming hole is used as an injection port of a molten metal and the other end is used as a casting outlet of an ingot, and a liner attached to the forming hole of the mold body. Mold
The liner is made of carbon having a thermal conductivity of 60 W / (m · K) to 139 W / (m · K), and the inner peripheral surface has a maximum height Rz defined by JIS B0601 2001 of 1 μm to 25 μm. A continuous casting mold characterized by the following.

［２］前記鋳出口の周囲に冷却水の噴出口が設けられている前項１に記載の連続鋳造用金型。   [2] The continuous casting mold according to the above item 1, wherein a cooling water outlet is provided around the casting outlet.

［３］前記ライナーは冷間等方圧加圧法または熱間等方圧加圧法による成形品である前項１または２に記載の連続鋳造用金型。   [3] The continuous casting mold according to the above item 1 or 2, wherein the liner is a molded product obtained by a cold isostatic pressing method or a hot isostatic pressing method.

［４］前記ライナーは金型本体に焼き嵌めによって取り付けられている前項１〜３のうちのいずれか１項に記載の連続鋳造用金型。   [4] The continuous casting mold according to any one of Items 1 to 3, wherein the liner is attached to the mold body by shrink fitting.

［５］Ｐｂ、Ｂｉ、Ｓｎ、Ｉｎのうちの１種以上の元素を含むアルミニウム合金を、前項１〜４のうちのいずれか１項に記載の連続鋳造用金型を用いて連続鋳造することを特徴とするアルミニウム合金の連続鋳造方法。   [5] Continuously casting an aluminum alloy containing one or more elements of Pb, Bi, Sn, and In using the continuous casting mold according to any one of the preceding items 1 to 4. A continuous casting method of an aluminum alloy, characterized by the following.

上記［１］に記載の連続鋳造用金型は、成形孔に取り付けられているライナーの熱伝導度が従来のライナーの熱伝導度よりも低いので、冷却が遅くなって鋳塊の離型位置が鋳出口側に近づく。このため、成形孔の壁面から抜熱される一次冷却時間が長くなり離型によって一次冷却能力が低下する期間が短縮される。その結果、鋳塊が十分に冷却されて鋳塊表面の再溶融が抑制され、再溶融による湯漏れや鋳肌の荒れが抑制される。しかも、ライナーの内周面の表面粗さがＪＩＳ Ｂ０６０１ ２００１で規定された最大高さＲｚで１μｍ〜２５μｍの平滑面で形成されているので鋳塊の滑りが良く、鋳肌の凹凸差の小さい鋳塊を連続鋳造することができる。   In the continuous casting mold according to the above [1], since the thermal conductivity of the liner attached to the molding hole is lower than the thermal conductivity of the conventional liner, cooling is slow and the mold release position of the ingot. Approaches the casting outlet side. For this reason, the primary cooling time in which heat is removed from the wall surface of the forming hole is increased, and the period during which the primary cooling capacity is reduced by mold release is shortened. As a result, the ingot is sufficiently cooled and remelting of the ingot surface is suppressed, and leakage of molten metal and roughening of the casting surface due to remelting are suppressed. Moreover, since the surface roughness of the inner peripheral surface of the liner is formed with a smooth surface of 1 μm to 25 μm at the maximum height Rz specified in JIS B0601 2001, the ingot has good slippage and the difference in unevenness of the casting surface is small. The ingot can be continuously cast.

上記［２］に記載の連続鋳造用金型によれば、鋳塊の離型位置が鋳出口側に近づくことで、冷却水の吹きつけによる二次冷却を受けるまでの時間が短縮されるので、鋳塊が十分に冷却されて鋳塊表面の再溶融が抑制される。   According to the continuous casting mold described in the above [2], since the mold release position of the ingot approaches the casting outlet side, the time until secondary cooling by spraying cooling water is reduced. In addition, the ingot is sufficiently cooled and remelting of the ingot surface is suppressed.

上記［３］に記載の連続鋳造用金型はライナーが冷間等方圧加圧法または熱間等方圧加圧法による成形品であるから表面平滑性が高い。   The mold for continuous casting according to the above [3] has a high surface smoothness because the liner is a molded product by a cold isostatic pressing method or a hot isostatic pressing method.

上記［４］に記載の連続鋳造用金型は、ライナーが鋳型本体に焼き嵌めによって取り付けられているので、両者間の密着性が高く熱移動が速やかに行われるとともに、周方向における冷却ムラが生じない。   In the continuous casting mold according to the above [4], since the liner is attached to the mold body by shrink fitting, the adhesion between the two is high, heat transfer is performed quickly, and cooling unevenness in the circumferential direction is reduced. Does not occur.

上記［５］に記載のアルミニウム合金の連続鋳造方法は、低融点元素であるＢｉ、Ｓｎ、ＰｂおよびＩｎのうちの１種以上を含むアルミニウム合金を上記の金型を用いて連続鋳造を行う。連続鋳造用金型は、成形孔に取り付けられているライナーの熱伝導度が従来のライナーの熱伝導度よりも低いので、冷却が遅くなって鋳塊の離型位置が鋳出口側に近づく。このため、成形孔の壁面から抜熱される一次冷却時間が長くなり離型によって一次冷却能力が低下する期間が短縮される。その結果、鋳塊が十分に冷却されて鋳塊表面の低融点化合物の再溶融が抑制され、再溶融による湯漏れや鋳肌の荒れが抑制される。しかも、ライナーの内周面の表面粗さがＪＩＳ Ｂ０６０１ ２００１で規定された最大高さＲｚで１μｍ〜２５μｍの平滑面で形成されているので鋳塊の滑りが良く、鋳肌の凹凸差の小さい鋳塊を連続鋳造することができる。   In the continuous casting method for an aluminum alloy according to the above [5], an aluminum alloy containing at least one of Bi, Sn, Pb and In, which are low-melting elements, is continuously cast using the above-mentioned mold. In the continuous casting mold, since the thermal conductivity of the liner attached to the molding hole is lower than the thermal conductivity of the conventional liner, cooling is slow and the mold release position of the ingot approaches the casting outlet side. For this reason, the primary cooling time in which heat is removed from the wall surface of the forming hole is increased, and the period during which the primary cooling capacity is reduced by mold release is shortened. As a result, the ingot is sufficiently cooled and remelting of the low melting point compound on the surface of the ingot is suppressed, so that leakage of molten metal and roughness of the casting surface due to remelting are suppressed. Moreover, since the surface roughness of the inner peripheral surface of the liner is formed with a smooth surface of 1 μm to 25 μm at the maximum height Rz specified in JIS B0601 2001, the ingot has good slippage and the difference in unevenness of the casting surface is small. The ingot can be continuously cast.

図１に参照されるフロート型の縦型連続鋳造装置を用い、実施例１〜１６および比較例１〜１８のアルミニウム合金の連続鋳造を行った。   The aluminum alloys of Examples 1 to 16 and Comparative Examples 1 to 18 were continuously cast using the float type vertical continuous casting apparatus shown in FIG.

アルミニウム合金は表１に示す４種類を用いた。これらのアルミニウム合金は、強度向上のためにＳｉ、Ｃｕ、ＭｇおよびＺｎが添加され、切削性向上のために、Ｂｉ、Ｓｎ、ＰｂおよびＩｎが添加された快削性アルミニウム合金である。   Four types of aluminum alloys shown in Table 1 were used. These aluminum alloys are free-cutting aluminum alloys to which Si, Cu, Mg and Zn are added for improving the strength, and Bi, Sn, Pb and In are added for improving the machinability.

Figure 2020041224
Figure 2020041224

金型１０は、アルミニウムからなる円筒型の金型本体２０にカーボン製の円筒型ライナー３０が取りつけられている。前記金型１０は、成形孔１１の直径が１７０ｍｍ、３００ｍｍ、３８０ｍｍの３種類である。各例で用いた金型１０の成形孔１１の直径は表２に示すとおりである。   In the mold 10, a cylindrical mold liner 30 made of carbon is attached to a cylindrical mold body 20 made of aluminum. The molds 10 are of three types having a diameter of the forming hole 11 of 170 mm, 300 mm, and 380 mm. The diameter of the molding hole 11 of the mold 10 used in each example is as shown in Table 2.

前記金型本体２０は冷却水用のキャビティ１２を有し、入口２２から導入した冷却水Ｃによって成形孔１１内の溶湯Ｍを一次冷却し、噴出口２３から噴出させた冷却水Ｃで鋳出された鋳塊Ｓを二次冷却する構造である。また、内周面２５にライナー３０を内嵌めするための凹部２６が形成されている。前記冷却水Ｃの流量は図外の制御装置によって調節される。   The mold body 20 has a cavity 12 for cooling water. The molten metal M in the forming hole 11 is primarily cooled by the cooling water C introduced from the inlet 22, and is cast with the cooling water C ejected from the ejection port 23. This is a structure for secondary cooling the ingot S that has been cooled. In addition, a concave portion 26 for internally fitting the liner 30 is formed on the inner peripheral surface 25. The flow rate of the cooling water C is adjusted by a controller (not shown).

ライナー３０は、鋳造方向の長さが１００ｍｍで、内径が成形孔１１の直径相当の円筒型であり、厚みは５ｍｍである。前記ライナ３０はカーボン粉をＣＩＰ成形によって押し固めた成形品であり、各ライナー３０の熱伝導度は表２に示すとおりであり、内周面３１が表２に記載した表面高さＲｚに調整されている。前記表面高さＲｚはＪＩＳ Ｂ０６０１ ２００１で規定された表面粗さである。   The liner 30 is a cylindrical type having a length in the casting direction of 100 mm, an inner diameter corresponding to the diameter of the forming hole 11, and a thickness of 5 mm. The liner 30 is a molded product obtained by compacting carbon powder by CIP molding. The thermal conductivity of each liner 30 is as shown in Table 2, and the inner peripheral surface 31 is adjusted to the surface height Rz described in Table 2. Have been. The surface height Rz is a surface roughness specified in JIS B0601 2001.

実施例１〜１６および比較例１〜１８の各金型１０は、表２に記載した金型本体２０とライナー３０を組み合わせ、ライナー３０が金型本体２０の凹部２６に焼き嵌めにより取り付けられている。   Each of the molds 10 of Examples 1 to 16 and Comparative Examples 1 to 18 is a combination of the mold body 20 and the liner 30 described in Table 2, and the liner 30 is attached to the recess 26 of the mold body 20 by shrink fitting. I have.

各金型１０を図１に参照される縦型連続鋳造装置に組み込み、表１のアルミニウム合金を連続鋳造した。表２に各例の金型１０とアルミニウム合金を示す。また、各例の連続鋳造条件は、表２に示す鋳造温度、鋳造速度および冷却水量とした。   Each mold 10 was incorporated in the vertical continuous casting apparatus shown in FIG. 1 to continuously cast the aluminum alloy shown in Table 1. Table 2 shows the mold 10 and the aluminum alloy of each example. The continuous casting conditions in each example were a casting temperature, a casting speed, and a cooling water amount shown in Table 2.

各例の連続鋳造について湯漏れの有無を調べた。さらに湯漏れの無かった連続鋳造については鋳塊の鋳肌の凹凸を調べ、凹凸差が１．５ｍｍ以下の鋳塊を良好（〇）、凹凸差が１．５ｍｍを超える鋳塊を不良（×）と評価した。評価結果を表２に示す。   The continuous casting of each example was examined for the presence or absence of molten metal leakage. Further, for continuous casting with no molten metal leakage, the unevenness of the casting surface of the ingot was examined, and the ingot with a difference of 1.5 mm or less was good (〇), and the ingot with a difference of more than 1.5 mm was poor (× ). Table 2 shows the evaluation results.

Figure 2020041224
Figure 2020041224

表２に示した結果より、ライナーの熱伝導度および表面粗さを規定することによって凝固壁の再溶融による湯漏れを防ぎ、平滑性の高い鋳塊を連続鋳造できることを確認した。   From the results shown in Table 2, it was confirmed that by specifying the thermal conductivity and the surface roughness of the liner, it was possible to prevent the molten metal from leaking due to the remelting of the solidified wall and continuously cast an ingot having high smoothness.

本発明のアルミニウム合金鋳塊は、低融点元素を含有する快削性アルミニウム合金として利用できる。   The aluminum alloy ingot of the present invention can be used as a free-cutting aluminum alloy containing a low-melting element.

１０…金型
１１…成形孔
１２…注入口
１３…鋳出口
２０…金型本体
２１…キャビティ
２３…噴出口
３０…ライナー
Ｍ…溶湯
Ｓ…鋳塊
Ｃ…冷却水
DESCRIPTION OF SYMBOLS 10 ... Die 11 ... Molding hole 12 ... Injection port 13 ... Casting outlet 20 ... Die main body 21 ... Cavity 23 ... Spouting outlet 30 ... Liner M ... Melt S ... Ingot C ... Cooling water

Claims (5)

Ｐｂ：０．２質量％〜２質量％、Ｂｉ：０．０１質量％〜３質量％、Ｓｎ：０．０１質量％〜１．５質量％、Ｉｎ：０．０１質量％〜０．２質量％のうちの1種以上の元素を含むアルミニウム合金からなる鋳塊であり、鋳肌の凹凸差が１．５ｍｍ以下であることを特徴とするアルミニウム合金鋳塊。   Pb: 0.2% by mass to 2% by mass, Bi: 0.01% by mass to 3% by mass, Sn: 0.01% by mass to 1.5% by mass, In: 0.01% by mass to 0.2% by mass %, Which is an ingot made of an aluminum alloy containing one or more of the elements described above, wherein the difference in unevenness of the casting surface is 1.5 mm or less. 前記アルミニウム合金は、さらに、Ｃｕ：３．５質量％〜６．５質量％およびＺｎ：０．０１質量％〜１．２質量％を含有する請求項１に記載のアルミニウム合金鋳塊。   The aluminum alloy ingot according to claim 1, wherein the aluminum alloy further contains Cu: 3.5% by mass to 6.5% by mass and Zn: 0.01% by mass to 1.2% by mass. 前記アルミニウム合金は、さらに、Ｓｉ：０．０１質量％〜１．０質量％、Ｍｇ：０．０１質量％〜２．０質量％、Ｔｉ：０．０１質量％〜０．１質量％、Ｂ：０．０００１質量％〜０．０１質量％のうちの1種以上の元素を含む請求項２に記載のアルミニウム合金鋳塊。   The aluminum alloy further contains Si: 0.01% to 1.0% by mass, Mg: 0.01% to 2.0% by mass, Ti: 0.01% to 0.1% by mass, : The aluminum alloy ingot according to claim 2, which contains one or more elements of 0.0001% by mass to 0.01% by mass. 前記アルミニウム合金は、さらに、Ｍｇ：０．３質量％〜１．５質量％およびＳｉ：０．２質量％〜１．０質量％を含有する請求項１に記載のアルミニウム合金鋳塊。   The aluminum alloy ingot according to claim 1, wherein the aluminum alloy further contains 0.3% to 1.5% by mass of Mg and 0.2% to 1.0% by mass of Si. 前記アルミニウム合金は、さらに、Ｃｕ：０．０１質量％〜２．０質量％、Ｚｎ：０．０１質量％〜０．２質量％、Ｔｉ：０．０１質量％〜０．１質量％、Ｂ：０．０００１質量％〜０．０１質量％のうちの１種以上の元素を含む請求項４に記載のアルミニウム合金鋳塊。
The aluminum alloy further contains Cu: 0.01% to 2.0% by mass, Zn: 0.01% to 0.2% by mass, Ti: 0.01% to 0.1% by mass, B: : The aluminum alloy ingot according to claim 4, which contains one or more elements of 0.0001% by mass to 0.01% by mass.
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Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH04371351A (en) * 1991-06-20 1992-12-24 Furukawa Electric Co Ltd:The Horizontal type continuous casting method
JPH10265884A (en) * 1997-03-26 1998-10-06 Nippon Light Metal Co Ltd Aluminum alloy material excellent in machinability and its production
JP2004052054A (en) * 2002-07-22 2004-02-19 Honda Motor Co Ltd Aluminum alloy material for forging and method of continuously casting the same
JP2011038130A (en) * 2009-08-06 2011-02-24 Furukawa-Sky Aluminum Corp Aluminum alloy having excellent machinability and high temperature embrittlement resistance

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH04371351A (en) * 1991-06-20 1992-12-24 Furukawa Electric Co Ltd:The Horizontal type continuous casting method
JPH10265884A (en) * 1997-03-26 1998-10-06 Nippon Light Metal Co Ltd Aluminum alloy material excellent in machinability and its production
JP2004052054A (en) * 2002-07-22 2004-02-19 Honda Motor Co Ltd Aluminum alloy material for forging and method of continuously casting the same
JP2011038130A (en) * 2009-08-06 2011-02-24 Furukawa-Sky Aluminum Corp Aluminum alloy having excellent machinability and high temperature embrittlement resistance

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