JP2004034135A - Aluminum alloy with superior formability in semi-molten state and manufacturing method of its cast ingot - Google Patents
Aluminum alloy with superior formability in semi-molten state and manufacturing method of its cast ingot Download PDFInfo
- Publication number
- JP2004034135A JP2004034135A JP2002198111A JP2002198111A JP2004034135A JP 2004034135 A JP2004034135 A JP 2004034135A JP 2002198111 A JP2002198111 A JP 2002198111A JP 2002198111 A JP2002198111 A JP 2002198111A JP 2004034135 A JP2004034135 A JP 2004034135A
- Authority
- JP
- Japan
- Prior art keywords
- aluminum alloy
- semi
- ingot
- cooling
- mold
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Images
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
- B22D11/003—Aluminium alloys
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/04—Continuous casting of metals, i.e. casting in indefinite lengths into open-ended moulds
- B22D11/049—Continuous casting of metals, i.e. casting in indefinite lengths into open-ended moulds for direct chill casting, e.g. electromagnetic casting
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/04—Continuous casting of metals, i.e. casting in indefinite lengths into open-ended moulds
- B22D11/055—Cooling the moulds
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/16—Controlling or regulating processes or operations
- B22D11/22—Controlling or regulating processes or operations for cooling cast stock or mould
- B22D11/225—Controlling or regulating processes or operations for cooling cast stock or mould for secondary cooling
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/12—Making non-ferrous alloys by processing in a semi-solid state, e.g. holding the alloy in the solid-liquid phase
Landscapes
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Chemical & Material Sciences (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Continuous Casting (AREA)
Abstract
Description
【０００１】
【発明の属する技術分野】
本発明は、半溶融成型性に優れたアルミニウム合金及びその鋳塊の製造方法に関するものである。
【０００２】
【従来の技術】
半溶融成型ビレットを用いるチクソキャスト法は、従来の金型鋳造法と比較し鋳造偏析やガス巻き込み、引け巣等の内部欠陥が少なく、機械的特性や寸法精度も向上し、しかも金型寿命が長いなどの利点があり、最近注目をあびてきている技術である。
【０００３】
これに使用するビレットの鋳造方法は、ペシネーやアルマックス方式のように、ビレット段階で初晶α（Ａｌ）相を球状化するため、半溶融温度域で電磁撹拌を行う方法（方式Ａ）が良く知られており既に実用化されている。
また、特許第３２１６６８４号には、アルミニウム合金の給湯時に液相線より３０℃を越えない温度領域に限定し、１℃／秒以上の凝固区間冷却速度で冷却固化し、さらに溶解度線から固相線温度までを０．５℃／分以上の速度で昇温し、さらに固相線を越える温度領域まで昇温するとともに５〜６０分間保持して初晶を球状化した後、液相線以下の成型温度まで更に昇温し半溶融状態になった溶湯を成型する方法で、そのアルミニウム合金にはＴｉ，Ｂを添加する方法（方式Ｂ）が開示されている。
【０００４】
【発明が解決しようとする課題】
上記従来の方法の中、方式Ａでは工程が非常に煩雑で、設備費も高価で製造コストが高くなるという問題があった。
また、方式Ｂでは多量のＡｌ−Ｔｉ−Ｂを添加するため、炉内でのＴｉＢ２沈降による品質不安定が発生し、更に液相線近傍温度で冷却と昇温を行うため温度制御が複雑で、しかも作業工程が煩雑なため量産化や低コスト化が図れないという問題があった。
【０００５】
本発明は、以上の点に鑑みて創案されたものであって、上記従来技術の欠点を解消し、工程が簡素でしかも低コスト化が達成でき、得られる成型品が均質で高品質な半溶融成型性に優れたアルミニウム合金及びその鋳塊の製造方法を提供することを目的とし、特に半溶融成型用アルミニウム合金ビレットの半連続鋳造時に結晶粒微細化剤として添加するＴｉとＢの添加方法を規制し、添加量を適量に配合し、ＴｉＢ２の形状とサイズと組成比を限定することと、その後アルミニウム合金ビレットを鋳造する際、鋳造条件のコントロールを調整することにより微細化した鋳造組織を得ることを目的とするものである。
【０００６】
【課題を解決するための手段】
上記目的を達成するため本願発明の第１発明は、Ｔｉ０．００５〜０．５ｗｔ％、Ｂ０．０００１〜０．１ｗｔ％を含み、残部が実質的にアルミニウムから成ることを特徴とする半溶融成型性に優れたアルミニウム合金を採用する。
【０００７】
ここで、上記アルミニウム合金には、ＴｉとＢを適量含有するので、合金の結晶粒を微細化できるものである。
【０００８】
また、上記目的を達成するため本願発明の第２発明は、アルミニウム合金の結晶粒微細化のために添加されるＴｉは、Ａｌ−Ｔｉ母合金で添加し、更にＡｌ−Ｔｉ−Ｂ母合金で添加されることを特徴とする第１発明に記載の半溶融成型性に優れたアルミニウム合金を採用する。
【０００９】
ここで、上記アルミニウム合金には、ＴｉをまずＡｌ−Ｔｉ母合金で添加し、次いでＡｌ−Ｔｉ−Ｂ母合金を添加しているので、より微細な鋳造組織とすることができる。
【００１０】
また、上記目的を達成するため本願発明の第３発明は、アルミニウム合金の結晶粒微細化のために添加されるＴｉ，Ｂ量はＴｉ／Ｂ比が３〜４０であり、（Ａｌｘ・Ｔｉｙ）Ｂ２（ｘ＝１〜７，ｙ＝１〜９）化合物のサイズが１０μｍ以下の粒状で、しかもＡｌｘ／Ｔｉｙの原子量比が０．２〜２．５であることを特徴とする第１発明又は第２発明に記載の半溶融成型性に優れたアルミニウム合金を採用する。
【００１１】
また、上記目的を達成するため本願発明の第４発明は、Ｔｉ０．００５〜０．５ｗｔ％、Ｂ０．０００１〜０．１ｗｔ％を含み、残部が実質的にアルミニウムから成るアルミニウム合金を半連続鋳造するに際し、アルミニウム合金の溶湯を筒形状の強制冷却鋳型内に上方から注湯し、鋳型により一次冷却して表面凝固層を形成すると共に、該凝固層を形成した鋳塊をその下端を支える下型と共に、前記鋳型から引き下ろし、該鋳塊の表面に冷媒を供給し二次冷却する際、一次冷却と二次冷却までの距離を１５０ｍｍ以内とし、二次冷却用冷媒が鋳塊に当たる角度を鋳造方向に対して２０°以上で８０°未満とすることを特徴とする半溶融成型性に優れたアルミニウム合金鋳塊の製造方法を採用する。
【００１２】
また、上記目的を達成するため本願発明の第５発明は、アルミニウム合金のＴｉは、Ａｌ−Ｔｉ母合金で添加し、更にＡｌ−Ｔｉ−Ｂ母合金で添加されることを特徴とする第４発明に記載の半溶融成型性に優れたアルミニウム合金鋳塊の製造方法を採用する。
【００１３】
また、上記目的を達成するため本願発明の第６発明は、アルミニウム合金のＴｉ，Ｂ量は、Ｔｉ／Ｂ比が３〜４０であり、（Ａｌｘ・Ｔｉｙ）Ｂ２（ｘ＝１〜７，ｙ＝１〜９）化合物のサイズが１０μｍ以下の粒状で、しかもＡｌｘ／Ｔｉｙの原子量比が０．２〜２．５であることを特徴とする第４発明又は第５発明に記載の半溶融成型性に優れたアルミニウム合金鋳塊の製造方法を採用する。
【００１４】
また、上記目的を達成するため本願発明の第７発明は、アルミニウム合金を半連続鋳造するに際し、二次冷却した後、更に鋳塊の冷却を強化するため三次冷却用冷媒を鋳造方向に対して２０°以上で８０°未満の角度で鋳塊に当てることを特徴とする第４発明、第５発明又は第６発明に記載の半溶融成型性に優れたアルミニウム合金鋳塊の製造方法を採用する。
【００１５】
また、上記目的を達成するため本願発明の第８発明は、アルミニウム合金を半連続鋳造するに際し、筒形状の強制冷却鋳型内に上方から注湯し、鋳型により一次冷却して表面凝固層を形成させる際に、鋳型内の給湯面に配設した浮子式溶湯分配器から溶湯を流出させる溶湯レベル制御において、浮子式溶湯分配器からの溶湯の射出角度が鋳造方向に対して２０°以上で８０°未満であることを特徴とする第４発明、第５発明、第６発明又は第７発明に記載の半溶融成型性に優れたアルミニウム合金鋳塊の製造方法を採用する。
【００１６】
【発明の実施の形態】
以下本発明で用いるアルミニウム合金の成分量の数値限定等種々の数値限定理由について詳述し、本発明の理解に供する。
【００１７】
Ｔｉ成分は、鋳塊の組織を微細化し、鋳塊割れの発生を防止するが、０．００５ｗｔ％未満ではその効果は少なく、一方０．５ｗｔ％を越えるとＴｉＡｌ３の巨大な晶出物の発生を促進させるため、０．００５〜０．５ｗｔ％とした。
【００１８】
Ｂ成分もまたＴｉ成分とともに鋳塊の組織を微細化し、鋳塊割れの発生を防止するが、０．０００１ｗｔ％未満ではその効果が顕著ではなく、一方０．１ｗｔ％を越えて添加してもそれ以上の効果は期待できないので０．０００１〜０．１ｗｔ％とした。
【００１９】
鋳塊の結晶粒微細化のために添加されるＴｉは、まずＡｌ−Ｔｉ母合金で添加することが重要である。一度に所定量をＡｌ−Ｔｉ−Ｂ母合金で添加すると、母合金中のＴｉＢ２が溶湯中に沈降して添加量に見合った微細化効果が得られない。このため、まずＡｌ−Ｔｉ母合金で添加して結晶粒を微細化させ、次にＡｌ−Ｔｉ−Ｂ母合金を添加することにより微細な鋳造組織を得ることが出来る。このため微細な結晶粒組織を得るための微細化剤添加法は、Ａｌ−Ｔｉ母合金でまず添加し、続いてＡｌ−Ｔｉ−Ｂ母合金で適量添加することとした。
【００２０】
鋳塊の結晶粒微細化のために添加されるＴｉ，Ｂ量はＴｉ／Ｂ比が重要で、Ｔｉ／Ｂ比が３未満では十分な微細化効果は得られず、一方Ｔｉ／Ｂ比が４０を越えると微細化効果は飽和するため、Ｔｉ／Ｂ比を３〜４０とした。
【００２１】
次に添加される（Ａｌｘ・Ｔｉｙ）Ｂ２化合物のサイズであるが、（Ａｌｘ・Ｔｉｙ）Ｂ２のサイズも結晶粒の微細化に影響を及ぼし、１０μｍを越えると微細化効果は著しく低下するとともに、結晶粒微細化の核となる（Ａｌｘ・Ｔｉｙ）Ｂ２の形状が粒状でないと微細化能は低下するため、（Ａｌｘ・Ｔｉｙ）Ｂ２のサイズは１０μｍ以下でしかも形状を粒状とした。
ここで、（Ａｌｘ・Ｔｉｙ）Ｂ２のｘ，ｙについてだが、ｘ＝１〜７，ｙ＝１〜９とした。その理由は、ｘ，ｙともにその範囲を外れると得られる鋳塊の結晶粒微細化効果が劣るようになるからである。
（Ａｌｘ・Ｔｉｙ）Ｂ２化合物を構成するＡｌｘとＴｉｙの原子量比も結晶粒の微細化に大きく寄与し、Ａｌｘ／Ｔｉｙが０．２未満では微細化効果が少なく、一方２．５を越えても微細化効果が劣るためにＡｌｘ／Ｔｉｙ比を０．２〜２．５とした。
【００２２】
鋳塊の結晶粒微細化は微細化剤の添加とともに鋳造時の冷却を強化し、アルミニウム溶湯の凝固速度を早め、結晶成長を抑制することも重要な要因の一つである。
アルミニウム合金の半連続鋳造に当たり、アルミニウム合金溶湯を上下が開放された冷却鋳型（モールド）を使用し、鋳型下部を閉塞するよう下型を配設し、アルミニウム合金溶湯を出湯ノズルから鋳型内に導入して下型上に供給し、鋳型内の溶湯レベルを鋳型内に配設したフロート分配器のような浮子式溶湯分配器により制御しながら、鋳型内壁からの冷却（一次冷却）により鋳塊殻を形成し、下型を降下させて凝固した鋳塊を鋳型から引き出し、鋳型から引き出された鋳塊を更に冷媒で冷却し（二次冷却）鋳塊全体を凝固させる鋳造方法をとっている。溶湯がモールドに接して冷却される一次冷却と冷媒が直接鋳塊に当たって冷却される二次冷却までの距離は短いほど冷却は早まり結晶粒は微細化されるが、１５０ｍｍを越えると一次冷却から二次冷却までの時間が長くなり、鋳造時の冷却が弱くなるため微細な結晶粒組織が得られない。そのため、一次冷却と二次冷却までの距離は１５０ｍｍ以内とした。
また、冷媒が鋳塊表面に当たる角度によっても二次冷却の程度が変動し、鋳造方向に対して２０°未満か８０°以上では冷却水が鋳塊表面にうまく当たらず冷却能が低下するため２０°以上で８０°未満とした。
【００２３】
二次冷却された後、更に冷却を強化するため三次冷媒を鋳塊表面に当てるが、三次冷媒が鋳造方向に対して２０°未満では冷却能が低下する。一方８０°以上の角度で鋳塊に当てると冷媒は鋳塊に沿って当たらないために、三次冷媒は鋳造方向に対して２０°以上で８０°未満とした。
【００２４】
前記アルミニウム合金の半連続鋳造に当たり、鋳型内の給湯面に配設した浮子式溶湯分配器（フロート）から溶湯を流出させて溶湯レベル制御において、浮子式溶湯分配器（フロート）からの鋳型内に溶湯を噴射するが、射出角度により溶湯の冷却能が大きく変化する。鋳造方向に対して２０°未満の射出角度では、溶湯は鋳造方向に強く落下するためズンプが深くなり、冷却が弱くなる。一方、８０°以上では溶湯が鋳型に強く当たるため鋳塊の外観が悪くなる。このため、モールド内に給湯された溶湯のメタルレベル制御に用いるフロートからの溶湯の射出角度は鋳造方向に対して２０°以上で８０°未満とした。
【００２５】
一般的には、鋳造は半連続鋳造で行われ、鋳型内の溶湯レベル制御は浮子式溶湯分配器（フロート）を使用するが、浮子式溶湯分配器（フロート）を用いないＨＯＴ−ＴＯＰ鋳造法を用いると、冷却は強化され凝固速度が速くなり結晶粒は微細化される。
【００２６】
Ｔｉ，Ｂの適量添加及び最適鋳造条件の選択により鋳塊の結晶を微細化するもので、アルミニウム合金は特に限定しないが、アルミニウムに添加される主要添加元素はＭｇ，Ｓｉ，Ｍｎ，Ｚｎ，Ｃｕ，Ｆｅ，Ｃｒ，Ｎｉ，Ｌｉ，Ｖ，Ｚｒ，Ｓｎ，Ｐｂ，Ｂｉ，Ｃｏ，Ｓｒ等である。
【００２７】
【実施例】
以下本発明の具体的な実施例を比較例と共に示す。
【００２８】
鋳塊組成をそれぞれ下記表１に示すような合金組成にＴｉ，Ｂを添加し、半連続鋳造にてアルミニウム合金ビレットを鋳造した。
【００２９】
【表１】
アルミニウム合金ビレットを下記表２に示す条件で鋳造し、半溶融成型時の成型性、半溶融成型後の初晶α（Ａｌ）相の形状を評価した結果も表２に併記した。
【００３１】
【表２】
表２に示した鋳塊の外観評価は表面が引っ掻き、冷接等の欠陥が無くスムースなものを○と判定した。また、鋳塊の結晶粒は３００μｍ以下を○と判定し、それを越える場合を×と判定した。
半溶融成型の成型性は、良好なものを○と判定し、成型性の悪いものを×と判定した。
半溶融成型後の初晶α（Ａｌ）相の形状は、球状化が認められるものを○とし、球状化が不十分であるものを×と判定した。半溶融成型後の初晶α（Ａｌ）相の微細均一化では、初晶α（Ａｌ）相のサイズが５００μｍ以下を○と判定し、５００μｍを越えるサイズのものを×と判定した。
【００３３】
図１は、初晶α（Ａｌ）相の微細均一化が○評価の代表例写真を示し、図２は、初晶α（Ａｌ）相の微細均一化が×評価の代表例写真を示す。
【００３４】
【発明の効果】
以上述べてきた如く、本発明によれば、従来の半溶融ビレットよりも工程が簡素化され、しかも低コスト化が図れる。
また得られる組織も初晶α（Ａｌ）相サイズが平均５００μｍ以下で、かつ面積率５０％の均一球状化組織となっており、広い範囲の用途に使用可能であるという効果を奏するものである。
【図面の簡単な説明】
【図１】初晶α（Ａｌ）相の微細均一化が○評価の代表例の顕微鏡組織写真である。
【図２】初晶α（Ａｌ）相の微細均一化が×評価の代表例の顕微鏡組織写真である。[0001]
TECHNICAL FIELD OF THE INVENTION
The present invention relates to an aluminum alloy excellent in semi-solid moldability and a method for producing an ingot thereof.
[0002]
[Prior art]
The thixocasting method using a semi-molten molded billet has fewer internal defects such as casting segregation, gas entrapment, shrinkage cavities, mechanical properties and dimensional accuracy, and longer mold life than conventional mold casting methods. It has advantages such as long, and is a technology that has attracted attention recently.
[0003]
As a method of casting a billet used in this method, a method of performing electromagnetic stirring in a semi-melting temperature range (method A) is used to form a primary α (Al) phase into a spheroid at a billet stage, as in the case of the Pescine or Almax method. It is well known and has already been put to practical use.
Also, Japanese Patent No. 3216684 discloses that when hot water is supplied from an aluminum alloy, the temperature is limited to a temperature range not exceeding 30 ° C. from the liquidus line, and the aluminum alloy is cooled and solidified at a solidification zone cooling rate of 1 ° C./sec or more. The temperature is increased up to the linear temperature at a rate of 0.5 ° C./min or more, and further raised to a temperature range exceeding the solidus temperature, and is maintained for 5 to 60 minutes to form primary crystals into spheroids. A method of forming a molten metal in a semi-molten state by further raising the temperature to the forming temperature of (a), and adding Ti and B to the aluminum alloy (method B) is disclosed.
[0004]
[Problems to be solved by the invention]
Among the above conventional methods, the method A has a problem that the steps are very complicated, the equipment cost is high, and the manufacturing cost is high.
Further, in order to add a large amount of Al-TiB In mode B, the quality instability occurs due to TiB 2 precipitation in the furnace, complicated further temperature control for performing cooling and heated at liquidus temperature near In addition, there is a problem that mass production and cost reduction cannot be achieved due to complicated operation steps.
[0005]
The present invention has been made in view of the above points, and solves the above-mentioned drawbacks of the prior art, can achieve simple and low-cost processes, and can obtain a molded product having a uniform and high-quality semi-finished product. A method for producing an aluminum alloy excellent in melt moldability and a method for producing an ingot thereof, particularly a method for adding Ti and B to be added as a grain refiner during semi-continuous casting of an aluminum alloy billet for semi-solid molding regulate, blended amount in an appropriate amount, and to limit the shape and size and the composition ratio of TiB 2, then when casting aluminum alloy billet, the cast structure was refined by adjusting the control of the casting conditions The purpose is to obtain.
[0006]
[Means for Solving the Problems]
According to a first aspect of the present invention, there is provided a semi-solid molding comprising 0.005 to 0.5% by weight of Ti and 0.0001 to 0.1% by weight of B, with the balance substantially consisting of aluminum. Uses an aluminum alloy with excellent properties.
[0007]
Here, since the aluminum alloy contains Ti and B in appropriate amounts, crystal grains of the alloy can be refined.
[0008]
In order to achieve the above object, a second invention of the present invention is directed to a method of manufacturing a semiconductor device, wherein Ti added for refining the crystal grains of an aluminum alloy is added in an Al-Ti master alloy, and further Ti is added in an Al-Ti-B master alloy. The aluminum alloy having excellent semi-solid moldability according to the first invention is characterized by being added.
[0009]
Here, since Ti is first added to the aluminum alloy as an Al-Ti mother alloy and then an Al-Ti-B mother alloy is added, a finer cast structure can be obtained.
[0010]
In order to achieve the above object, a third invention of the present invention is directed to a method of manufacturing a semiconductor device according to the present invention, wherein the amount of Ti and B added for refining the crystal grain of the aluminum alloy is such that the Ti / B ratio is 3 to 40, and (Al x Ti y) B 2 (x = 1~7 , and characterized in that y = 1 to 9) the size of the compounds in the following granular 10 [mu] m, yet the atomic weight ratio of Al x / Ti y is 0.2 to 2.5 The aluminum alloy excellent in semi-solid moldability described in the first invention or the second invention is used.
[0011]
In order to achieve the above object, a fourth invention of the present invention is a semi-continuous casting of an aluminum alloy containing 0.005 to 0.5 wt% of Ti and 0.0001 to 0.1 wt% of B and the balance substantially consisting of aluminum. In doing so, a molten aluminum alloy is poured from above into a cylindrical forced cooling mold, and primary cooled by the mold to form a surface solidified layer, and the ingot having the solidified layer formed thereon is supported by the lower end thereof. Along with the mold, it is pulled down from the mold, and when supplying the refrigerant to the surface of the ingot and performing secondary cooling, the distance between the primary cooling and the secondary cooling is set within 150 mm, and the angle at which the secondary cooling refrigerant hits the ingot is cast. A method for producing an aluminum alloy ingot excellent in semi-solid moldability, characterized by being at least 20 ° and less than 80 ° with respect to the direction.
[0012]
In order to achieve the above object, a fifth invention of the present invention is directed to the fourth invention, wherein Ti of the aluminum alloy is added by an Al-Ti mother alloy, and further added by an Al-Ti-B mother alloy. The method for producing an aluminum alloy ingot excellent in semi-solid moldability according to the invention is employed.
[0013]
In order to achieve the above object, according to a sixth aspect of the present invention, the Ti / B ratio of the aluminum alloy is such that the Ti / B ratio is 3 to 40, and (Al x · Ti y ) B 2 (x = 1 to 7, y = 1-9) The fourth invention or the fifth invention, characterized in that the compound is in the form of granules having a size of 10 μm or less and the Al x / Ti y atomic ratio is 0.2-2.5. The method for producing an aluminum alloy ingot excellent in semi-solid moldability described above is employed.
[0014]
Further, in order to achieve the above object, the seventh invention of the present invention provides a semi-continuous casting of an aluminum alloy, after secondary cooling, further strengthening the cooling of the ingot with a tertiary cooling refrigerant in the casting direction. The method for manufacturing an aluminum alloy ingot excellent in semi-solid moldability according to the fourth, fifth or sixth invention, wherein the ingot is applied to the ingot at an angle of 20 ° or more and less than 80 °. .
[0015]
In order to achieve the above object, an eighth invention of the present invention is directed to a semi-continuous casting of an aluminum alloy, in which a molten metal is poured into a cylindrical forced cooling mold from above and primary cooled by the mold to form a surface solidified layer. In this case, in the molten metal level control for causing the molten metal to flow out of the floating molten metal distributor disposed on the molten metal supply surface in the mold, the injection angle of the molten metal from the floating molten metal distributor is not less than 20 ° with respect to the casting direction, and The method for producing an aluminum alloy ingot excellent in semi-solid moldability according to the fourth, fifth, sixth or seventh invention, wherein the angle is less than 0 ° is adopted.
[0016]
BEST MODE FOR CARRYING OUT THE INVENTION
Hereinafter, various reasons for limiting the numerical values, such as limiting the numerical values of the components of the aluminum alloy used in the present invention, will be described in detail to provide an understanding of the present invention.
[0017]
The Ti component refines the structure of the ingot and prevents the occurrence of cracks in the ingot, but the effect is small when the content is less than 0.005 wt%, while when it exceeds 0.5 wt%, a large crystallized substance of TiAl 3 is formed. In order to promote the generation, the content was made 0.005 to 0.5 wt%.
[0018]
The B component also refines the structure of the ingot together with the Ti component and prevents the occurrence of cracks in the ingot. However, if the content is less than 0.0001% by weight, the effect is not remarkable. Since no further effect can be expected, the content is set to 0.0001 to 0.1 wt%.
[0019]
It is important that Ti added for refining the crystal grains of the ingot is first added in an Al-Ti master alloy. The addition of a predetermined amount of Al-TiB master alloys at once, TiB 2 in the matrix alloy can not be obtained refining effect commensurate with the added amount is settled in the melt. For this reason, a fine cast structure can be obtained by first adding an Al-Ti master alloy to refine the crystal grains and then adding an Al-Ti-B master alloy. For this reason, as a method of adding a refiner for obtaining a fine crystal grain structure, an Al-Ti mother alloy is first added, and then an appropriate amount is added using an Al-Ti-B mother alloy.
[0020]
The Ti / B ratio is important for the amounts of Ti and B added for refining the crystal grains of the ingot, and if the Ti / B ratio is less than 3, a sufficient refining effect cannot be obtained. If it exceeds 40, the effect of miniaturization is saturated, so the Ti / B ratio is set to 3 to 40.
[0021]
Next, the size of the (Al x · Ti y ) B 2 compound to be added, the size of the (Al x · Ti y ) B 2 also affects the refinement of the crystal grains. Is remarkably reduced, and the refining ability is reduced unless the shape of (Al x · Ti y ) B 2 , which is the core of grain refinement, is not granular, so that the size of (Al x · Ti y ) B 2 is 10 μm. Below, the shape was granular.
Here, x and y of (Al x · Ti y ) B 2 were set as x = 1 to 7, and y = 1 to 9. The reason is that if both x and y are out of the range, the effect of refining the crystal grain of the obtained ingot becomes inferior.
The atomic weight ratio of Al x to Ti y constituting the (Al x .Ti y ) B 2 compound also greatly contributes to the refinement of the crystal grains. When Al x / T y is less than 0.2, the effect of the refinement is small, while Even if it exceeds 2.5, the Al x / T y ratio is set to 0.2 to 2.5 because the effect of miniaturization is inferior.
[0022]
One of the important factors for the refinement of the crystal grain size of the ingot is to enhance the cooling during casting together with the addition of a refining agent, increase the solidification rate of the aluminum melt, and suppress the crystal growth.
In semi-continuous casting of aluminum alloy, a lower mold is used to close the lower part of the mold using a cooling mold (mold) with an open top and bottom, and the molten aluminum alloy is introduced into the mold from a tapping nozzle. The molten metal in the mold is supplied to the lower mold, and the molten metal level in the mold is controlled by a float type molten metal distributor such as a float distributor disposed in the mold, while the ingot shell is cooled by cooling from the inner wall of the mold (primary cooling). Is formed, the lower mold is lowered, the solidified ingot is drawn out of the mold, and the ingot drawn from the mold is further cooled with a refrigerant (secondary cooling) to solidify the entire ingot. The shorter the distance between the primary cooling, in which the molten metal is in contact with the mold and cooling, and the secondary cooling, in which the refrigerant directly hits the ingot, the faster the cooling and the finer the crystal grains. The time until the next cooling becomes longer and the cooling during casting becomes weaker, so that a fine grain structure cannot be obtained. Therefore, the distance between the primary cooling and the secondary cooling was set to within 150 mm.
Also, the degree of secondary cooling varies depending on the angle at which the refrigerant hits the ingot surface, and if it is less than 20 ° or more than 80 ° with respect to the casting direction, the cooling water does not come into contact with the ingot surface, and the cooling capacity is reduced. At least 80 ° and less than 80 °.
[0023]
After the secondary cooling, a tertiary refrigerant is applied to the surface of the ingot to further enhance the cooling. However, when the tertiary refrigerant is less than 20 ° with respect to the casting direction, the cooling capacity is reduced. On the other hand, when the refrigerant is applied to the ingot at an angle of 80 ° or more, the refrigerant does not hit along the ingot. Therefore, the tertiary refrigerant is set at 20 ° or more and less than 80 ° with respect to the casting direction.
[0024]
In the semi-continuous casting of the aluminum alloy, the molten metal flows out from a float type molten metal distributor (float) disposed on a hot water supply surface in the mold to control the molten metal level. When the molten metal is injected, the cooling ability of the molten metal changes greatly depending on the injection angle. At an injection angle of less than 20 ° with respect to the casting direction, the molten metal drops strongly in the casting direction, so that the zump becomes deep and the cooling becomes weak. On the other hand, at 80 ° or more, the appearance of the ingot deteriorates because the molten metal hits the mold strongly. For this reason, the angle of injection of the molten metal from the float used for controlling the metal level of the molten metal supplied into the mold was set to 20 ° or more and less than 80 ° with respect to the casting direction.
[0025]
Generally, casting is performed by semi-continuous casting, and the level of molten metal in the mold is controlled using a float type molten metal distributor (float), but the HOT-TOP casting method without using the float type molten metal distributor (float) is used. With the use of, the cooling is enhanced, the solidification rate is increased, and the crystal grains are refined.
[0026]
It is to refine the crystal of the ingot by adding appropriate amounts of Ti and B and selecting the optimal casting conditions. The aluminum alloy is not particularly limited, but the main additive elements added to aluminum are Mg, Si, Mn, Zn, and Cu. , Fe, Cr, Ni, Li, V, Zr, Sn, Pb, Bi, Co, Sr and the like.
[0027]
【Example】
Hereinafter, specific examples of the present invention will be described together with comparative examples.
[0028]
Ti and B were added to the ingot compositions shown in Table 1 below, and aluminum alloy billets were cast by semi-continuous casting.
[0029]
[Table 1]
The aluminum alloy billet was cast under the conditions shown in Table 2 below, and the results of evaluation of the moldability during semi-solid molding and the shape of the primary α (Al) phase after semi-solid molding are also shown in Table 2.
[0031]
[Table 2]
In the appearance evaluation of the ingot shown in Table 2, the surface was scratched, and a smooth ingot free from defects such as cold welding was judged as ○. The crystal grain size of the ingot was determined to be ○ when the grain size was 300 μm or less, and was determined to be × when the grain size exceeded 300 μm.
Regarding the moldability of the semi-solid molding, good ones were judged to be good, and poor moldability were judged to be bad.
The shape of the primary crystal α (Al) phase after semi-solid molding was evaluated as も の when spheroidization was observed, and as × when spheroidization was insufficient. In the fine homogenization of the primary crystal α (Al) phase after semi-solid molding, the primary crystal α (Al) phase was determined to be ○ when the size of the primary crystal α (Al) phase was 500 μm or less, and was determined to be × when the size exceeded 500 μm.
[0033]
FIG. 1 shows a photograph of a typical example in which fine uniformization of the primary crystal α (Al) phase was evaluated as ○, and FIG. 2 shows a photograph of a typical example in which fine uniformity of the primary crystal α (Al) phase was evaluated as x.
[0034]
【The invention's effect】
As described above, according to the present invention, the process can be simplified and the cost can be reduced as compared with the conventional semi-molten billet.
Also, the obtained structure is a uniform spheroidized structure having an average primary crystal α (Al) phase size of 500 μm or less and an area ratio of 50%, and has an effect that it can be used for a wide range of applications. .
[Brief description of the drawings]
FIG. 1 is a photomicrograph of a representative example of the evaluation of o for fine uniformity of the primary α (Al) phase.
FIG. 2 is a photomicrograph of a representative example of a case where fine homogenization of a primary crystal α (Al) phase is evaluated as x.
Claims (8)
Priority Applications (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2002198111A JP3696844B2 (en) | 2002-07-08 | 2002-07-08 | Aluminum alloy with excellent semi-melt formability |
| US11/048,538 US20060032559A1 (en) | 2002-07-08 | 2005-01-31 | Method for producing aluminum alloy having improved semi-solid molding capability and billet thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2002198111A JP3696844B2 (en) | 2002-07-08 | 2002-07-08 | Aluminum alloy with excellent semi-melt formability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2004034135A true JP2004034135A (en) | 2004-02-05 |
| JP3696844B2 JP3696844B2 (en) | 2005-09-21 |
Family
ID=31705652
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2002198111A Expired - Fee Related JP3696844B2 (en) | 2002-07-08 | 2002-07-08 | Aluminum alloy with excellent semi-melt formability |
Country Status (2)
| Country | Link |
|---|---|
| US (1) | US20060032559A1 (en) |
| JP (1) | JP3696844B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110343881A (en) * | 2019-08-29 | 2019-10-18 | 重庆丰禾铝业有限公司 | A kind of processing method of superelevation width-thickness ratio cast aluminium alloy flat ingot |
Families Citing this family (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20220415563A1 (en) * | 2007-04-05 | 2022-12-29 | Grant A. MacLennan | Method of forming a cast inductor apparatus |
| US11501911B2 (en) * | 2007-04-05 | 2022-11-15 | Grant A. MacLennan | Method of forming a cast inductor apparatus |
| US12051533B2 (en) * | 2007-04-05 | 2024-07-30 | Grant A. MacLennan | Cast winding inductor apparatus and method of use thereof |
| FR2985443B1 (en) * | 2012-01-10 | 2014-01-31 | Constellium France | DOUBLE-JET COOLING DEVICE FOR VERTICAL SEMI-CONTINUE CASTING MOLD |
| WO2015079071A2 (en) * | 2014-03-27 | 2015-06-04 | Primetals Technologies Austria GmbH | Semi-continuous casting of a steel strip |
| CN115558811B (en) * | 2022-09-10 | 2023-06-16 | 哈尔滨工业大学 | Equipment and method for preparing TiAl semi-solid material by utilizing ultrasonic and electromagnetic field |
Family Cites Families (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR2509207A1 (en) * | 1981-07-09 | 1983-01-14 | Pechiney Aluminium | HIGH SPEED VERTICAL CONTINUOUS CASTING PROCESS OF ALUMINUM AND ITS ALLOYS |
| NO950843L (en) * | 1994-09-09 | 1996-03-11 | Ube Industries | Method of Treating Metal in Semi-Solid State and Method of Casting Metal Bars for Use in This Method |
| CA2327950A1 (en) * | 2000-12-08 | 2002-06-08 | Groupe Minutia Inc. | Grain refining agent for cast aluminum or magnesium products |
-
2002
- 2002-07-08 JP JP2002198111A patent/JP3696844B2/en not_active Expired - Fee Related
-
2005
- 2005-01-31 US US11/048,538 patent/US20060032559A1/en not_active Abandoned
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110343881A (en) * | 2019-08-29 | 2019-10-18 | 重庆丰禾铝业有限公司 | A kind of processing method of superelevation width-thickness ratio cast aluminium alloy flat ingot |
Also Published As
| Publication number | Publication date |
|---|---|
| JP3696844B2 (en) | 2005-09-21 |
| US20060032559A1 (en) | 2006-02-16 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN105525158A (en) | Semi-solid die-casting aluminum alloy material and die-casting molding method using same | |
| JP2001158930A (en) | HIGH STRENGTH Mg BASE ALLOY, Mg BASE CAST ALLOY AND ARTICLE | |
| CN102424924A (en) | Addition of WN2And LiBH4Powdered high strength aluminum alloy and method of making same | |
| CN108300884B (en) | A kind of hypoeutectic Al-Mg2The rotten and thinning method of Si alloy | |
| CN110373579A (en) | A kind of high conductive high strength aluminum alloy materials and preparation method thereof | |
| CN115927936A (en) | High-strength and high-toughness aluminum alloy and preparation method thereof | |
| US20060032559A1 (en) | Method for producing aluminum alloy having improved semi-solid molding capability and billet thereof | |
| CN112030047A (en) | Preparation method of high-hardness fine-grain rare earth aluminum alloy material | |
| CN102660693B (en) | Aluminum alloy treated by using TiN powder and BeH2 powder, and preparation method thereof | |
| JP3246363B2 (en) | Forming method of semi-molten metal | |
| CN102534310B (en) | High-strength aluminum alloy doped with Mo2C and MgH2 and preparation method thereof | |
| CN1224730C (en) | Evaporative pattern casting magnesium alloy and smelting method thereof | |
| JPH09137239A (en) | Method for molding half-molten metal | |
| JP4510541B2 (en) | Aluminum alloy casting molding method | |
| CN113005315B (en) | Preparation method of efficient Al-10Sr intermediate alloy | |
| CN112442612B (en) | Method for improving fluidity of cast aluminum-copper alloy | |
| CN103014391B (en) | The alloy preparation method of a kind of improvement 2618 aluminium alloy micostructure | |
| CN102433471A (en) | High-toughness aluminum alloy and preparation method thereof | |
| CN102517476A (en) | High strength aluminum alloy capable of reducing porosity and dispersed shrinkage and preparation method thereof | |
| CN102517475A (en) | ZrC-doped high strength aluminum alloy and preparation method thereof | |
| JP3416503B2 (en) | Hypereutectic Al-Si alloy die casting member and method of manufacturing the same | |
| JP5035508B2 (en) | Solidified aluminum alloy and method for producing the same | |
| JP3053063B2 (en) | Manufacturing method of aluminum alloy casting material suitable for semi-solid molding | |
| CN102424925B (en) | Co2N-doped aluminium alloy and smelting method thereof | |
| JP3339333B2 (en) | Method for forming molten metal |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A977 | Report on retrieval |
Free format text: JAPANESE INTERMEDIATE CODE: A971007 Effective date: 20040615 |
|
| A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20040625 |
|
| A521 | Request for written amendment filed |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20040823 |
|
| TRDD | Decision of grant or rejection written | ||
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 Effective date: 20050628 |
|
| A61 | First payment of annual fees (during grant procedure) |
Free format text: JAPANESE INTERMEDIATE CODE: A61 Effective date: 20050630 |
|
| R150 | Certificate of patent or registration of utility model |
Free format text: JAPANESE INTERMEDIATE CODE: R150 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20090708 Year of fee payment: 4 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20090708 Year of fee payment: 4 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20100708 Year of fee payment: 5 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20110708 Year of fee payment: 6 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20110708 Year of fee payment: 6 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20120708 Year of fee payment: 7 |
|
| LAPS | Cancellation because of no payment of annual fees |