JP2021023967A - Ti-Al BASED ALLOY CASTING METHOD - Google Patents
Ti-Al BASED ALLOY CASTING METHOD Download PDFInfo
- Publication number
- JP2021023967A JP2021023967A JP2019143776A JP2019143776A JP2021023967A JP 2021023967 A JP2021023967 A JP 2021023967A JP 2019143776 A JP2019143776 A JP 2019143776A JP 2019143776 A JP2019143776 A JP 2019143776A JP 2021023967 A JP2021023967 A JP 2021023967A
- Authority
- JP
- Japan
- Prior art keywords
- casting
- ingot
- based alloy
- crucible
- molten metal
- 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.)
- Pending
Links
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
- B22D21/06—Casting non-ferrous metals with a high melting point, e.g. metallic carbides
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
- B22D21/002—Castings of light metals
- B22D21/005—Castings of light metals with high melting point, e.g. Be 1280 degrees C, Ti 1725 degrees C
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
- B22D21/02—Casting exceedingly oxidisable non-ferrous metals, e.g. in inert atmosphere
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D27/00—Treating the metal in the mould while it is molten or ductile ; Pressure or vacuum casting
- B22D27/15—Treating the metal in the mould while it is molten or ductile ; Pressure or vacuum casting by using vacuum
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D7/00—Casting ingots, e.g. from ferrous metals
- B22D7/005—Casting ingots, e.g. from ferrous metals from non-ferrous metals
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C14/00—Alloys based on titanium
Landscapes
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Manufacture And Refinement Of Metals (AREA)
Abstract
Description
本発明は、Ａｌ濃度を精度良く制御することができるＴｉ−Ａｌ基合金の鋳造方法に関するものである。 The present invention relates to a method for casting a Ti—Al base alloy capable of accurately controlling the Al concentration.
水冷銅の坩堝を用いた誘導溶解炉（ＣＣＩＭ：コールドクルーシブル誘導溶解装置）は、溶解雰囲気および坩堝から溶湯内に不純物が混入することがほとんどなく、高融点のＴｉ−Ａｌ基合金の溶解に適している。
また、誘導溶解炉は、坩堝サイズより小さな原料であれば、形状に制約なく炉内で溶解ができるため、スクラップ等の材料を原材料として有効に活用することができる。
An induction melting furnace (CCIM: cold crucible induction melting device) using a water-cooled copper crucible is suitable for melting a high melting point Ti—Al-based alloy with almost no impurities mixed in the molten metal from the melting atmosphere and the crucible. ing.
Further, in the induction melting furnace, if the raw material is smaller than the crucible size, it can be melted in the furnace regardless of the shape, so that the material such as scrap can be effectively used as the raw material.
さらに、誘導溶解炉で加熱を起こさせる電磁誘導は、溶湯を攪拌させる電磁斥力も生じさせるため、電磁斥力による攪拌で溶湯内の成分均質性を保つことも可能となる。
そのため、誘導溶解炉を用いたＴｉ−Ａｌ基合金の鋳造は、高価な原料費が故に高い歩留まりが求められるＴｉ−Ａｌ基合金の鋳塊に対して、高品質な鋳塊を高歩留まりで得るための有効な手法とされている。
Further, since the electromagnetic induction that causes heating in the induction melting furnace also generates an electromagnetic repulsive force that stirs the molten metal, it is possible to maintain the homogeneity of the components in the molten metal by stirring by the electromagnetic repulsive force.
Therefore, casting of a Ti—Al-based alloy using an induction melting furnace can obtain a high-quality ingot with a high yield as compared with an ingot of a Ti—Al-based alloy that requires a high yield due to an expensive raw material cost. It is said to be an effective method for this.
ところで、通常、金属は液体状態よりも固体状態において密度が大きいため、凝固の際に鋳造体の容積が小さくなる。つまり、凝固時に収縮が起こることで、比較的冷却速度が遅く凝固の遅れる部分には、引巣と呼ばれる空洞が鋳造時の欠陥として発生してしまう。このような引巣は、特に細径鋳塊を製造する際に鋳塊の軸心部で発生しやすい。そこで、誘導溶解炉で溶解した金属を細径鋳塊として鋳造する場合は、鋳造時の引巣を抑制するため、以下の特許文献１のような技術が開発されている。 By the way, since the density of metal is usually higher in the solid state than in the liquid state, the volume of the cast body becomes smaller during solidification. That is, due to shrinkage during solidification, cavities called nests are generated as defects during casting in the portion where the cooling rate is relatively slow and solidification is delayed. Such cavities are likely to occur at the axial center of the ingot, especially when producing a small-diameter ingot. Therefore, in the case of casting a metal melted in an induction melting furnace as a small-diameter ingot, a technique as described in Patent Document 1 below has been developed in order to suppress nesting during casting.
特許文献１は、水冷銅の坩堝を用いた誘導溶解炉において、当該坩堝の底部に設けられた出湯口から溶湯を鋳型に出湯して活性金属の鋳塊を鋳造する活性金属の鋳造方法であって、前記鋳塊は直径１０ｍｍ以上で、且つ、鋳塊高さＨと鋳塊径Ｄの比（Ｈ／Ｄ）が１．５以上であり、前記鋳造で出湯される溶湯の重量が２００ｋｇ以下とされた鋳造条件で鋳造を行うに際しては、前記鋳造時の溶湯の温度を活性金属の融点よりも高温にすると共に、前記出湯口の開口径を調整することで、前記鋳型内で鋳造が進む速度である鋳造速度Ｖ（ｍｍ／秒）を、前記鋳塊高さＨとの関係で、Ｖ≦０．１Ｈに制御しつつ前記鋳造を行う活性金属の鋳造方法を開示している。 Patent Document 1 is a method for casting an active metal in an induction melting furnace using a water-cooled copper pit, in which the molten metal is poured into a mold from a hot water outlet provided at the bottom of the pit to cast an ingot of the active metal. The ingot has a diameter of 10 mm or more, the ratio (H / D) of the ingot height H to the ingot diameter D is 1.5 or more, and the weight of the molten metal discharged in the casting is 200 kg or less. When casting is performed under the above casting conditions, the temperature of the molten metal at the time of casting is set higher than the melting point of the active metal, and the opening diameter of the outlet is adjusted so that the casting proceeds in the mold. Disclosed is a method for casting an active metal in which the casting is performed while controlling the casting speed V (mm / sec), which is the speed, to V ≦ 0.1H in relation to the ingot height H.
特許文献１の技術では、鋳造速度を調整することで一方向凝固に近い鋳造が可能となり、Ｔｉ−Ａｌ基合金などの活性金属において、引け巣の発生を抑制して最大で８６%の歩留まりを実現可能としている。 In the technique of Patent Document 1, casting close to one-way solidification is possible by adjusting the casting speed, and in active metals such as Ti—Al base alloys, the occurrence of shrinkage cavities is suppressed and the yield is up to 86%. It is feasible.
ところで、特許文献１の技術は、実操業にて制御できる因子として鋳造速度に着目しており、高い歩留まりを得るために非常に有効な手法を開示している。
しかし、実際の製造で製品の良否を判断する基準には、引け巣のような形状の欠陥以外にも、例えばＡｌの濃度が規格範囲から外れているといった組成の欠陥なども存在する。
この点、特許文献１においては、鋳片の引け巣の割合で歩留まりを評価しているものの、Ａｌの偏析などの影響で鋳片におけるＡｌ濃度がどのように変化したか、言い換えればＡｌ濃度という組成の欠陥には全く考慮がなされておらず、Ａｌ濃度を制御可能な溶解条件は全く知見が得られていない。
By the way, the technique of Patent Document 1 focuses on the casting speed as a factor that can be controlled in actual operation, and discloses a very effective method for obtaining a high yield.
However, in addition to defects in the shape such as shrinkage cavities, there are also defects in the composition such that the concentration of Al is out of the standard range in the criteria for judging the quality of the product in actual manufacturing.
In this regard, in Patent Document 1, although the yield is evaluated by the ratio of shrinkage cavities of the slab, how the Al concentration in the slab changed due to the influence of segregation of Al, in other words, the Al concentration. No consideration has been given to compositional defects, and no knowledge has been obtained regarding dissolution conditions that can control the Al concentration.
つまり、Ｔｉ−Ａｌ基合金の鋳造品の品質には、形状だけでなく組成の欠陥も考慮した総合的な要求品質の向上が求められており、Ａｌ濃度を精度良く制御することが重要となっている。
本発明は、上述の問題に鑑みてなされたものであり、Ａｌ濃度が精度良く制御され、形状だけでなく組成の欠陥も考慮した総合的な品質を大きく向上させることができるＴｉ−Ａｌ基合金の鋳造方法を提供することを目的とする。
In other words, the quality of cast products of Ti—Al-based alloys is required to improve the overall required quality considering not only the shape but also the defects of the composition, and it is important to control the Al concentration accurately. ing.
The present invention has been made in view of the above-mentioned problems, and the Al concentration can be controlled with high accuracy, and the overall quality considering not only the shape but also the defect of the composition can be greatly improved. It is an object of the present invention to provide a casting method of.
上記課題を解決するため、本発明のＴｉ−Ａｌ基合金の鋳造方法は以下の技術的手段を講じている。
即ち、本発明のＴｉ−Ａｌ基合金の鋳造方法は、水冷銅の坩堝を用いた誘導溶解炉において、当該坩堝の底部に設けられた出湯口から溶湯を鋳型に出湯してＴｉ−Ａｌ基合金の鋳塊を鋳造するＴｉ−Ａｌ基合金の鋳造方法であって、前記Ｔｉ−Ａｌ基合金を溶解乃至は鋳造する際における前記誘導溶解炉内の真空度を８０〜７００torrの範囲内とし、鋳造された鋳塊のＡｌ濃度を目標値に対して±１．０mass%以内にすることを特徴とする。
In order to solve the above problems, the casting method of the Ti—Al based alloy of the present invention takes the following technical means.
That is, in the method for casting a Ti-Al-based alloy of the present invention, in an induction melting furnace using a water-cooled copper pit, molten metal is discharged from a hot water outlet provided at the bottom of the pit into a mold to form a Ti-Al-based alloy. This is a method for casting a Ti-Al-based alloy for casting the ingot of the above, in which the degree of vacuum in the induction melting furnace at the time of melting or casting the Ti-Al-based alloy is within the range of 80 to 700 torr. It is characterized in that the Al concentration of the ingot is within ± 1.0 mass% with respect to the target value.
本発明のＴｉ−Ａｌ基合金の鋳造方法によれば、鋳造品のＡｌ濃度を精度良く制御することができ、鋳造品形状に関する不良だけでなく組成に関する不良も考慮した総合的な品質を大きく向上させることができる。 According to the casting method of the Ti—Al based alloy of the present invention, the Al concentration of the cast product can be controlled with high accuracy, and the overall quality considering not only the defect related to the shape of the cast product but also the defect related to the composition is greatly improved. Can be made to.
以下、本発明にかかるＴｉ−Ａｌ基合金の鋳造方法の実施形態を、図面に基づき詳しく説明する。
本実施形態のＴｉ−Ａｌ基合金の鋳造方法は、活性高融点なチタン−アルミ系合金（Ｔｉ−Ａｌ基合金）を溶解した溶湯Ｍを鋳型４に注湯して鋳造を行うことにより、細径鋳塊Ｓ（鋳塊）を製造するものとなっている。このＴｉ−Ａｌ基合金には、さまざまなものが考えられるが、航空機部材で使用されている合金であれば、Ti-3Al-2.5V合金、Ti-6Al-6V-2Sn-0.5Fe-0.5Cu合金、Ti-3Al-10V-2Fe合金、Ti-5Al-5V-5Mo-3Cr-0.5Fe合金、Ti-3Al-8V-6Cr-4Mo-4Zr合金、Ti-3Al-15V-3Cr-3Sn合金、Ti-6Al-4V合金、Ti-3Al-15Mo-2.7Nb-0.2Si合金、Ti-5Al-2Sn-2Zr-4Mo-4Cr合金、Ti-6Al-2Sn-4Zr-6Mo合金、Ti-6Al-2Sn-4Zr-2Mo合金、Ti-6Al-5Zr-0.5Mo-0.25Si合金、Ti-5.5Al-3.5Sn-3Zr-1Nb-0.25Mo-0.3Si合金、Ti-5.8Al-4Sn-3.5Zr-0.7Nb-0.5Mo-0.35Si-0.06C合金などの合金が用いられる。
Hereinafter, embodiments of the method for casting a Ti—Al based alloy according to the present invention will be described in detail with reference to the drawings.
The method for casting a Ti-Al-based alloy of the present embodiment is fine by pouring molten metal M in which a titanium-aluminum-based alloy (Ti-Al-based alloy) having an active high melting point is dissolved into a mold 4 and casting. A diameter ingot S (ingot) is manufactured. Various Ti-Al base alloys can be considered, but if it is an alloy used in aircraft parts, Ti-3Al-2.5V alloy, Ti-6Al-6V-2Sn-0.5Fe-0.5Cu Alloys, Ti-3Al-10V-2Fe alloys, Ti-5Al-5V-5Mo-3Cr-0.5Fe alloys, Ti-3Al-8V-6Cr-4Mo-4Zr alloys, Ti-3Al-15V-3Cr-3Sn alloys, Ti -6Al-4V alloy, Ti-3Al-15Mo-2.7Nb-0.2Si alloy, Ti-5Al-2Sn-2Zr-4Mo-4Cr alloy, Ti-6Al-2Sn-4Zr-6Mo alloy, Ti-6Al-2Sn-4Zr -2Mo alloy, Ti-6Al-5Zr-0.5Mo-0.25Si alloy, Ti-5.5Al-3.5Sn-3Zr-1Nb-0.25Mo-0.3Si alloy, Ti-5.8Al-4Sn-3.5Zr-0.7Nb-0.5 Alloys such as Mo-0.35Si-0.06C alloys are used.
以降では、本実施形態のＴｉ−Ａｌ基合金の鋳造方法に用いられる鋳造設備１について説明する。
図１に示すように、本実施形態の鋳造方法に用いられる鋳造設備１は、水冷銅製の坩堝２を用いた誘導溶解炉３と、坩堝２の底部から出湯した溶湯Ｍが注入される鋳型４と、を有している。この鋳造設備１は、坩堝２の底部から溶湯Ｍを鋳型４に出湯してＴｉ−Ａｌ基合金の細径鋳塊Ｓを鋳造するものである。これら誘導溶解炉３及び坩堝２と、それらの下方に配備される鋳型４とは、一つの容器（真空容器）内に収められるようになっており、真空容器内の真空度を所定のものとしつつ、Ｔｉ−Ａｌ基合金の細径鋳塊Ｓを鋳造可能とする。
Hereinafter, the casting equipment 1 used in the method for casting the Ti—Al based alloy of the present embodiment will be described.
As shown in FIG. 1, the casting equipment 1 used in the casting method of the present embodiment includes an induction melting furnace 3 using a water-cooled copper crucible 2 and a mold 4 into which the molten metal M discharged from the bottom of the crucible 2 is injected. And have. In this casting facility 1, the molten metal M is discharged from the bottom of the crucible 2 into the mold 4 to cast a small-diameter ingot S of a Ti—Al-based alloy. The induction melting furnace 3 and the crucible 2 and the mold 4 placed below them are housed in one container (vacuum container), and the degree of vacuum in the vacuum container is set to a predetermined value. At the same time, the small-diameter ingot S of the Ti—Al-based alloy can be cast.
本発明は、この溶解・鋳造室内の真空度（気圧）を所定の値に制御することで、鋳塊内部のガス巻き込みなどに起因するガス欠陥を低減すると共に、鋳造品のＡｌ濃度を規格範囲に抑えることで、鋳造品の良品歩留まりを向上させることを可能とするものである。
本実施形態の鋳造設備１に用いられる誘導溶解炉３は、溶解対象となる材料の内部に誘導電流を生じさせてその抵抗発熱を利用するものであり、一般にコールドクルーシブル誘導溶解装置（Cold Crucible Induction Melting）と呼ばれるものである。この誘導溶解炉３は、水冷銅の坩堝２を用いてＴｉ−Ａｌ基合金を溶解させるものであり、一般的な溶解炉であれば坩堝２を構成する材料に多用される耐火物を用いずに、銅で形成されるものとなっている。そのため、誘導溶解炉３を用いた鋳造では、耐火物からのコンタミの影響を受け難い。
According to the present invention, by controlling the degree of vacuum (atmospheric pressure) in the melting / casting chamber to a predetermined value, gas defects caused by gas entrainment inside the ingot are reduced, and the Al concentration of the cast product is within the specified range. It is possible to improve the yield of non-defective products by suppressing the pressure to.
The induction melting furnace 3 used in the casting facility 1 of the present embodiment generates an induced current inside the material to be melted and utilizes the resistance heat generation, and is generally a cold crucible induction melting device (Cold Crucible Induction). It is called Melting). This induction melting furnace 3 melts a Ti—Al based alloy using a crucible 2 of water-cooled copper, and if it is a general melting furnace, it does not use a refractory material often used as a material constituting the crucible 2. In addition, it is made of copper. Therefore, casting using the induction melting furnace 3 is not easily affected by contamination from refractories.
上述した誘導溶解炉３に用いられる坩堝２は、図１に示すように、上方へ向かって開口した有底筒状に形成されており、内部に溶解されたＴｉ−Ａｌ基合金を収容可能となっている。
この坩堝２の壁は、前述の如く銅で形成されると共に水冷が行われている。このような水冷銅で坩堝２の壁を形成すれば、溶解されたＴｉ−Ａｌ基合金を収容していても坩堝２の内壁の温度が所定の温度（例えば２５０℃）以上に上昇することがない。具体的には、水冷銅の坩堝２に上述した溶融したＴｉ−Ａｌ基合金を入れても、坩堝２の壁の内周面と溶融金属との間にスカルといわれる凝固殻が形成され、坩堝としての役割を果たすことで溶融金属が坩堝２から汚染されることがない。
As shown in FIG. 1, the crucible 2 used in the above-mentioned induction melting furnace 3 is formed in a bottomed tubular shape that opens upward, and can accommodate a Ti—Al-based alloy dissolved inside. It has become.
The wall of the crucible 2 is made of copper and water-cooled as described above. If the wall of the crucible 2 is formed of such water-cooled copper, the temperature of the inner wall of the crucible 2 may rise to a predetermined temperature (for example, 250 ° C.) or higher even if the melted Ti—Al base alloy is contained. Absent. Specifically, even if the above-mentioned molten Ti—Al base alloy is put into the crucible 2 of water-cooled copper, a solidified shell called a skull is formed between the inner peripheral surface of the wall of the crucible 2 and the molten metal, and the crucible The molten metal is not contaminated from the crucible 2 by playing the role of.
本実施形態の坩堝２は底部出湯型となっており、坩堝２の底部には収容されたＴｉ−Ａｌ基合金を下方に案内可能な出湯口５が形成されている。この出湯口５は、開口径を調整可能とされており、下方に案内される溶湯Ｍの量を調整可能とされている。この出湯口５は、電磁式や機械式で開口径を調整可能なものでも良いし、開口径が異なる複数の弁部材を予め用意しておいて、弁部材を取り替えることで開口径を調整するようにしても良い。 The crucible 2 of the present embodiment has a bottom hot water outlet type, and a hot water outlet 5 capable of guiding the contained Ti—Al base alloy downward is formed at the bottom of the crucible 2. The opening diameter of the hot water outlet 5 can be adjusted, and the amount of molten metal M guided downward can be adjusted. The outlet 5 may be electromagnetically or mechanically adjustable in opening diameter, or a plurality of valve members having different opening diameters may be prepared in advance and the opening diameter may be adjusted by replacing the valve members. You may do so.
鋳型４は上方に向かって開口した有底円筒状に形成されている。
鋳型４の内寸法は、様々なものが考えられるが、鋳塊Ｓの直径をＤ、鋳塊Ｓの高さをＨ、溶湯Ｍの重量をＷとした場合に、以下の適用範囲に収まる程度のサイズとされるのが望ましい。
鋳塊径Ｄ（ｍｍ）： １０≦Ｄ≦１５０
鋳塊高さＨ（ｍｍ）：１５≦Ｈ≦１６００
溶湯重量Ｗ（ｋｇ）： ０．２≦Ｗ≦２００
次に、上述した誘導溶解炉３を用いて活性金属を鋳造する場合の手順、言い換えればＴｉ−Ａｌ基合金の鋳造方法について説明する。
The mold 4 is formed in a bottomed cylindrical shape that opens upward.
Various internal dimensions of the mold 4 can be considered, but when the diameter of the ingot S is D, the height of the ingot S is H, and the weight of the molten metal M is W, the internal dimensions fall within the following applicable range. It is desirable that the size is.
Ingot diameter D (mm): 10 ≤ D ≤ 150
Ingot height H (mm): 15 ≤ H ≤ 1600
Molten metal weight W (kg): 0.2 ≤ W ≤ 200
Next, a procedure for casting an active metal using the induction melting furnace 3 described above, in other words, a method for casting a Ti—Al base alloy will be described.
本実施形態のＴｉ−Ａｌ基合金の鋳造方法は、水冷銅の坩堝２を用いた誘導溶解炉３において、当該坩堝２の底部から溶湯Ｍを鋳型４に出湯して活性金属の細径の鋳塊Ｓを鋳造するものである。このとき鋳造される細径の鋳塊Ｓは直径１０ｍｍ以上で、且つ、鋳塊Ｓの高さ（Ｈ）と鋳塊Ｓの直径（Ｄ）の比Ｈ／Ｄが１．５以上であり、鋳造で出湯される溶湯Ｍの重量が２００ｋｇ以下とされた鋳造条件で鋳造が行われる。また、鋳造を行うに際しては、坩堝２の底部に、開口径を調整可能な出湯口５を設けておき、鋳造時の溶湯Ｍの温度を活性金属の融点よりも高温にすると共に、出湯口５の開口径を調整することで、鋳型４内で鋳造が進む速度である鋳造速度Ｖ（kg／秒）を、鋳塊Ｓの高さとの関係で、Ｖ≦０．１Ｈに制御しつつ鋳造を行い、鋳塊Ｓの内部の引巣を低減すると共に鋳造歩留まりを向上させるものとなっている。なお、鋳造時に出湯された溶湯が詰まって溶湯が流れなくなる「湯詰まり」を起こさないようにするためには、鋳造時の溶湯Ｍの温度を好ましくは活性金属の融点より２０℃以上高温、より好ましくは４０℃以上高温にするとよい。 In the method for casting a Ti—Al based alloy of the present embodiment, in an induction melting furnace 3 using a water-cooled copper crucible 2, molten metal M is discharged from the bottom of the crucible 2 into a mold 4 to cast a small diameter active metal. The mass S is cast. The small-diameter ingot S cast at this time has a diameter of 10 mm or more, and the ratio H / D of the height (H) of the ingot S to the diameter (D) of the ingot S is 1.5 or more. Casting is performed under casting conditions in which the weight of the molten metal M discharged by casting is 200 kg or less. Further, when casting, a hot water outlet 5 having an adjustable opening diameter is provided at the bottom of the crucible 2, so that the temperature of the molten metal M at the time of casting is higher than the melting point of the active metal, and the hot water outlet 5 is used. By adjusting the opening diameter of the casting, the casting speed V (kg / sec), which is the speed at which casting proceeds in the mold 4, is controlled to V ≦ 0.1H in relation to the height of the ingot S. This is performed to reduce the crucible inside the ingot S and improve the casting yield. In order to prevent "clogging" in which the molten metal discharged during casting is clogged and the molten metal does not flow, the temperature of the molten metal M during casting is preferably 20 ° C. or higher higher than the melting point of the active metal. It is preferable to raise the temperature to 40 ° C. or higher.
ところで、上述した鋳造速度Ｖ（kg／秒）でＴｉ−Ａｌ基合金の鋳塊Ｓを鋳造する場合でも、炉内が真空状態になっていると溶湯からＡｌが蒸発するため、Ａｌ濃度は鋳造中に徐々に低下し、最終的には鋳造品の組成が目標とするＡｌ濃度の規格値を下回る可能性がある。そこで、本実施形態のＴｉ−Ａｌ基合金の鋳造方法では、水冷銅の坩堝２を用いた誘導溶解炉３において、この坩堝２の底部に設けられた出湯口５から溶湯Ｍを鋳型４に出湯してＴｉ−Ａｌ基合金の鋳造品（鋳塊）を鋳造するに際して、Ｔｉ−Ａｌ基合金を溶解乃至は鋳造する際における誘導溶解炉３内の真空度を８０torr〜７００torrの範囲内とし、鋳造された鋳造品（鋳塊）のＡｌ濃度を目標値に対して±１．０mass%以内にするものとしている。 By the way, even when the ingot S of the Ti—Al base alloy is cast at the above-mentioned casting speed V (kg / sec), Al evaporates from the molten metal when the inside of the furnace is in a vacuum state, so that the Al concentration is cast. There is a possibility that the composition of the cast product will eventually fall below the target Al concentration standard value. Therefore, in the method for casting a Ti—Al based alloy of the present embodiment, in the induction melting furnace 3 using the water-cooled copper pit 2, the molten metal M is discharged into the mold 4 from the hot water outlet 5 provided at the bottom of the pit 2. Then, when casting a cast product (ingot) of the Ti—Al base alloy, the degree of vacuum in the induction melting furnace 3 when melting or casting the Ti—Al base alloy is set within the range of 80 torr to 700 torr. The Al concentration of the cast product (ingot) is set to be within ± 1.0 mass% with respect to the target value.
なお、上述したＡｌ濃度は、厳密には、鋳造品に鋳造された状態（固体状態）と、溶湯の状態（液体状態）とでは、異なるものとなる。しかし、本実施形態では、固体、液体、いずれの場合でも±１．０mass%以内とするものとする。
上述した誘導溶解炉３内の真空度を８０torr〜７００torrの範囲内に規定するのは以下の理由による。
Strictly speaking, the Al concentration described above differs between the state of being cast into a cast product (solid state) and the state of molten metal (liquid state). However, in this embodiment, it shall be within ± 1.0 mass% in both solid and liquid cases.
The vacuum degree in the induction melting furnace 3 described above is defined in the range of 80 torr to 700 torr for the following reasons.
すなわち、本実施形態では、鋳造に用いられる溶湯の重量は５０kgとした。この溶湯を全て鋳塊Ｓとして鋳造し終わるまでには、１５分という鋳造時間が必要となる。この鋳造時間は、ノズルの径によって変化することは言うまでもない。この１５分間の鋳造時間中にも溶湯のＡｌ濃度は蒸発によって徐々に低下する。ただ、蒸発によって失われたＡｌ濃度の低下量がＡｌ濃度の規格値の変動許容範囲内に収まるのであれば、鋳造後の鋳造品（鋳塊）はＴｉ−Ａｌ基合金として適正な組成を持ったものとして扱うことができる。 That is, in the present embodiment, the weight of the molten metal used for casting is 50 kg. It takes 15 minutes to complete casting all of this molten metal as ingot S. It goes without saying that this casting time varies depending on the diameter of the nozzle. Even during this 15-minute casting time, the Al concentration of the molten metal gradually decreases due to evaporation. However, if the amount of decrease in Al concentration lost due to evaporation is within the permissible range of fluctuation of the standard value of Al concentration, the cast product (ingot) after casting has an appropriate composition as a Ti—Al base alloy. Can be treated as a casting.
なお、Ｔｉ−Ａｌ基合金のＡｌ濃度の規格値（目標値）は、鋳造しようとする鋳造品の合金種によって高い場合もあれば低い場合もある。しかし、一般には２３．３mass%〜４３．３mass%の規格値に対して±１．０mass%以内に収めれば、Ｔｉ−Ａｌ基合金として適正な組成が得られることを出願人は確認している。例えば、３０mass%というＡｌ濃度の規格値を目標とした場合であっても、規格値に対して実際の鋳造品に許容されるＡｌ濃度の変動範囲は±１．０mass%以内となる。 The standard value (target value) of the Al concentration of the Ti—Al base alloy may be high or low depending on the alloy type of the cast product to be cast. However, in general, the applicant confirms that an appropriate composition as a Ti—Al base alloy can be obtained if it is kept within ± 1.0 mass% with respect to the standard value of 23.3 mass% to 43.3 mass%. There is. For example, even when the standard value of Al concentration of 30 mass% is targeted, the fluctuation range of Al concentration allowed in the actual cast product is within ± 1.0 mass% with respect to the standard value.
ここで、本実施形態の鋳造方法では、まず規格値に対して許容される変動範囲の上限と下限との差、言い換えればＡｌ濃度の変動幅を求める。このようにして求められた２．０mass%という変動幅を１５分間という鋳造時間で除算する。これは１５分間という鋳造時間でＡｌ濃度が低下しても、この低下幅がＡｌ濃度の変動範囲を超えないようなＡｌ濃度の変化速度を求めることにほかならない。上述した計算の結果得られるＡｌ濃度の変化速度は、２．０mass%÷１５min＝０．１３mass%／min以下となる。 Here, in the casting method of the present embodiment, first, the difference between the upper limit and the lower limit of the fluctuation range allowed with respect to the standard value, in other words, the fluctuation range of the Al concentration is obtained. The fluctuation range of 2.0 mass% obtained in this way is divided by the casting time of 15 minutes. This is nothing but finding the rate of change of the Al concentration so that even if the Al concentration decreases in the casting time of 15 minutes, the decrease range does not exceed the fluctuation range of the Al concentration. The rate of change of the Al concentration obtained as a result of the above calculation is 2.0 mass% ÷ 15 min = 0.13 mass% / min or less.
上述した０．１３mass%／minが算出されたら、Ａｌ濃度の変化速度が０．１３mass%／min以下となる真空度を、実際に実験を行って求めるとよい。このようにして実験により求められた鋳造の真空度が、上述した８０torr〜７００torrとなる。上述した真空度の範囲を決定する実験については、後述する実施例において詳しく説明する。
上述した真空度（真空容器内の気圧）が８０torr以下となる条件で鋳造を行うと、溶湯中のＡｌが鋳造中に大量に蒸発するため、溶湯組成が鋳造中に大きく変動し、鋳造品の組成の変動も無視できなくなる。その結果、鋳造品の組成（Ａｌ濃度）が規格値から外れ、組成面で不良となる鋳造品が発生しやすくなり、歩留まりの低下に繋がる。
After the above-mentioned 0.13 mass% / min is calculated, it is advisable to actually carry out an experiment to determine the degree of vacuum at which the rate of change of the Al concentration is 0.13 mass% / min or less. The degree of vacuum of the casting thus obtained by the experiment is 80 torr to 700 torr described above. The experiment for determining the range of the degree of vacuum described above will be described in detail in Examples described later.
When casting is performed under the condition that the above-mentioned degree of vacuum (atmospheric pressure in the vacuum vessel) is 80 torr or less, a large amount of Al in the molten metal evaporates during casting, so that the composition of the molten metal fluctuates greatly during casting, and the cast product Fluctuations in composition cannot be ignored. As a result, the composition (Al concentration) of the cast product deviates from the standard value, and a cast product having a defect in composition is likely to occur, leading to a decrease in yield.
また、真空度（真空容器内の気圧）が７００torr以上となる条件で鋳造を行うと、Ｔｉ−Ａｌ基合金の鋳造をガスが多く存在する環境で行うことになり、溶湯が鋳型内で凝固する際に周囲に存在するガスを巻き込む可能性が高くなって、ガス欠陥が増加してかえって歩留まりが低下する。
このガス欠陥は、溶湯が鋳型４内で凝固する際に、周囲に存在するガスを巻き込むことで発生するものであり、鋳型表層部に形成される場合が多い。そのため、溶解・鋳造時の炉内の真空度が高ければ、巻き込まれるガスも少なくなる。つまり、炉内の真空度を上げることで、ガス欠陥を低減させることは可能である。ガス欠陥が低減すると、ガス欠陥を鋳造品から取り除くべく鋳造品を切削する量も減少するため、鋳造品の歩留まりが向上可能となる。
Further, if casting is performed under the condition that the degree of vacuum (atmospheric pressure in the vacuum vessel) is 700 torr or more, the Ti—Al group alloy is cast in an environment where a large amount of gas is present, and the molten metal solidifies in the mold. In some cases, the possibility of entraining the surrounding gas increases, gas defects increase, and the yield decreases.
This gas defect is generated by entraining the gas existing in the surroundings when the molten metal solidifies in the mold 4, and is often formed on the surface layer of the mold. Therefore, the higher the degree of vacuum in the furnace during melting and casting, the less gas is involved. That is, it is possible to reduce gas defects by increasing the degree of vacuum in the furnace. When the gas defects are reduced, the amount of cutting the casting to remove the gas defects from the casting is also reduced, so that the yield of the casting can be improved.
なお、大気圧で鋳造した場合のガス欠陥の数の定量評価結果が無いため定性的な議論となるが、鋳造する鋳造環境を大気圧から真空にすればするほど、ガス欠陥の数は減少する傾向がある。従って、溶解乃至は鋳造を行う際の真空度を上述した７００torrより高真空度（７００torrより小さく）することにより、７６０torr（大気圧）以上の場合に比較してガス欠陥の数を大幅に低減することが可能と考えることができる。 It is a qualitative discussion because there is no quantitative evaluation result of the number of gas defects when casting at atmospheric pressure, but the number of gas defects decreases as the casting environment for casting is changed from atmospheric pressure to vacuum. Tend. Therefore, by making the degree of vacuum at the time of melting or casting higher than the above-mentioned 700 torr (less than 700 torr), the number of gas defects is significantly reduced as compared with the case of 760 torr (atmospheric pressure) or more. Can be considered possible.
以上のことから、真空度（真空容器内の気圧）を８０torr〜７００torrにして鋳造を行うことで、ガス欠陥の発生を抑えつつ、鋳造品の組成（Ａｌ濃度）を規格値に適正に制御することが可能となり、組成に関する不良も考慮した総合的な品質を大きく向上させることができる。 From the above, by casting with the degree of vacuum (atmospheric pressure in the vacuum vessel) set to 80 torr to 700 torr, the composition (Al concentration) of the cast product is appropriately controlled to the standard value while suppressing the occurrence of gas defects. This makes it possible to greatly improve the overall quality in consideration of defects in composition.
実施例は、最大５０ｋｇのＴｉ−Ａｌ基合金の材料（Ti-33.3Al-4.8Nb-2.55Cr(mass%)）を溶解し、溶解によって得られた溶湯を鋳造に用いたものである。
具体的には、図１に示すコールドクルーシブル式の誘導溶解炉３内で、上述した材料を水冷銅の坩堝２を用いて加熱し、真空度を0.001torr〜700torrの範囲で変化させた炉内に、加熱により溶解した溶湯を保持して、溶湯のＡｌ濃度を計測し、炉内の真空度とＡｌ蒸発速度との関係を調査した。結果を図２に示す。
In the example, a maximum of 50 kg of a Ti—Al base alloy material (Ti-33.3Al-4.8Nb-2.55Cr (mass%)) was melted, and the molten metal obtained by the melting was used for casting.
Specifically, in the cold crucible type induction melting furnace 3 shown in FIG. 1, the above-mentioned material is heated using a water-cooled copper crucible 2 and the degree of vacuum is changed in the range of 0.001 torr to 700 torr. In addition, the molten metal melted by heating was retained, the Al concentration of the molten metal was measured, and the relationship between the degree of vacuum in the furnace and the Al evaporation rate was investigated. The results are shown in FIG.
図２に示すように、炉内の真空度とＡｌ蒸発速度との間には、炉内の真空度を高くすればするほど、Ａｌ蒸発速度が低下するという関係があることがわかる。また、得られたデータに基づけば、炉内の真空度が0.001torrの場合でもＡｌ蒸発速度は0.13mass%/min以下となるが、鋳造を安全かつ確実に行えるように、80torrの場合をＡｌ蒸発速度が0.13mass%/min以下となる真空度の下限値と考え、真空度の制御範囲を80torr以上とした。 As shown in FIG. 2, it can be seen that there is a relationship between the degree of vacuum in the furnace and the Al evaporation rate that the higher the degree of vacuum in the furnace, the lower the Al evaporation rate. In addition, based on the obtained data, the Al evaporation rate is 0.13 mass% / min or less even when the degree of vacuum in the furnace is 0.001 torr, but in the case of 80 torr, Al is used so that casting can be performed safely and reliably. Considering that the lower limit of the degree of vacuum at which the evaporation rate is 0.13 mass% / min or less, the control range of the degree of vacuum was set to 80 torr or more.
上述した手順で炉内の真空度とＡｌ蒸発速度との関係を予め求めた上で、実際に鋳型４に出湯して鋳造品（鋳塊）の鋳造を行った。
なお、鋳造は、溶湯が封入された坩堝２の底部に設置してある黒鉛製のノズル（出湯口５）から出湯し、坩堝２の下方に位置する黒鉛製の鋳型４で凝固させて鋳造を行った。この鋳造も、減圧されたＡｒ雰囲気下、言い換えれば真空度が0.001 torr〜700 torrの範囲に制御されたＡｒ雰囲気下で行った。また、作製される鋳造品（鋳塊）は、黒鉛製の鋳型４の形状に合わせて変化させることができるが、本実施形態ではノズルの開口形状が矩形のものと、円形のものとの２種類で鋳造を行い鋳塊を作製した。具体的なノズルの開口形状は、矩形の場合は65mmx65mmと、55mmx55mmとの２種類であり、円形の場合はφ72mmとφ50mmとの２種類である。ノズルの開口形状が円形の場合は円柱状の鋳塊が、また開口形状が矩形の場合は角柱状の鋳塊が得られる。
After obtaining the relationship between the degree of vacuum in the furnace and the Al evaporation rate in advance by the above procedure, hot water was actually discharged into the mold 4 to cast a cast product (ingot).
For casting, hot water is discharged from a graphite nozzle (outlet port 5) installed at the bottom of the crucible 2 in which the molten metal is sealed, and solidified with a graphite mold 4 located below the crucible 2 for casting. went. This casting was also performed in an Ar atmosphere under reduced pressure, in other words, in an Ar atmosphere in which the degree of vacuum was controlled in the range of 0.001 torr to 700 torr. Further, the cast product (ingot) to be produced can be changed according to the shape of the graphite mold 4, but in the present embodiment, the nozzle opening shape is rectangular or circular. Ingots were produced by casting by type. There are two types of specific nozzle opening shapes, 65 mmx65 mm and 55 mmx55 mm for a rectangular shape, and φ72 mm and φ50 mm for a circular shape. When the opening shape of the nozzle is circular, a columnar ingot is obtained, and when the opening shape is rectangular, a prismatic ingot is obtained.
また、実験毎に異なるが、鋳塊の高さは620 mmから1520 mmの間であり、また鋳塊の鋳造速度は0.18%/s〜0.4%/sの範囲となっている。
得られた鋳塊品について、本実施形態の真空度の範囲では、Ａｌ蒸発速度が抑えられ、Ａｌ濃度が目標値に対して±1.0mass%の範囲に制御された鋳塊が得られることを出願人は確認している。Al濃度目標値の33.3mass%のTi-Al合金を本願発明方法で80 torrで鋳造した際に目標値の33.3mass%に対して、±1mass%以内に収まり32.79mass%であった。
The ingot height is between 620 mm and 1520 mm, and the ingot casting speed is in the range of 0.18% / s to 0.4% / s, although it varies from experiment to experiment.
Regarding the obtained ingot product, in the range of the degree of vacuum of the present embodiment, the Al evaporation rate is suppressed, and the ingot whose Al concentration is controlled in the range of ± 1.0 mass% with respect to the target value can be obtained. The applicant has confirmed. When a Ti-Al alloy having an Al concentration target value of 33.3 mass% was cast at 80 torr by the method of the present invention, it was within ± 1 mass% with respect to the target value of 33.3 mass%, which was 32.79 mass%.
また、得られた鋳塊品のうち、真空度が200torrで鋳造された鋳造品について、鋳塊の単位高さ当たりのガス欠陥の数を計測したところ、30個/mm以下となった。これは大気圧下で鋳造した場合のガス欠陥の数が数百個レベルであるのに対して、その数が大幅に低減されており、ガス欠陥の発生が抑制された結果を示すものとなっている。
以上の結果から、水冷銅の坩堝２を用いた誘導溶解炉３において、当該坩堝２の底部に設けられた出湯口５から溶湯を鋳型４に出湯してＴｉ−Ａｌ基合金の鋳塊を鋳造する際には、Ｔｉ−Ａｌ基合金を溶解乃至は鋳造する際における誘導溶解炉３内の真空度を80〜700torrの範囲内とし、鋳造された鋳塊のＡｌ濃度を目標値に対して±１．０mass%以内にすることで、Ａｌ濃度が精度良く制御され、形状だけでなく組成の欠陥も考慮した総合的な鋳造品の品質を大きく向上させることができる。
In addition, among the obtained ingot products, the number of gas defects per unit height of the ingot was measured for the cast products cast at a vacuum degree of 200 torr, and the number was 30 pieces / mm or less. This shows that the number of gas defects when casting under atmospheric pressure is on the order of several hundreds, but the number is significantly reduced, and the occurrence of gas defects is suppressed. ing.
From the above results, in the induction melting furnace 3 using the water-cooled copper crucible 2, the molten metal is poured into the mold 4 from the hot water outlet 5 provided at the bottom of the crucible 2 to cast an ingot of Ti—Al base alloy. When melting or casting a Ti—Al base alloy, the degree of vacuum in the induction melting furnace 3 should be within the range of 80 to 700 torr, and the Al concentration of the cast ingot should be ± with respect to the target value. By setting it within 1.0 mass%, the Al concentration can be controlled with high accuracy, and the quality of the overall cast product considering not only the shape but also the defect of the composition can be greatly improved.
なお、今回開示された実施形態はすべての点で例示であって制限的なものではないと考えられるべきである。特に、今回開示された実施形態において、明示的に開示されていない事項、例えば、運転条件や操業条件、各種パラメータ、構成物の寸法、重量、体積などは、当業者が通常実施する範囲を逸脱するものではなく、通常の当業者であれば、容易に想定することが可能な値を採用している。 It should be noted that the embodiments disclosed this time are exemplary in all respects and are not restrictive. In particular, in the embodiments disclosed this time, matters not explicitly disclosed, such as operating conditions, operating conditions, various parameters, dimensions, weights, volumes of components, etc., deviate from the scope normally implemented by those skilled in the art. A value that can be easily assumed by a person skilled in the art is adopted.
１ 鋳造設備
２ 坩堝
３ 誘導溶解炉
４ 鋳型
５ 出湯口
Ｍ 溶湯
Ｓ 鋳造品（鋳塊）
1 Casting equipment 2 Crucible 3 Induction melting furnace 4 Mold 5 Outlet M Hot metal S Casting product (ingot)
Claims (1)
前記Ｔｉ−Ａｌ基合金を溶解乃至は鋳造する際における前記誘導溶解炉内の真空度を８０〜７００torrの範囲内とし、鋳造された鋳塊のＡｌ濃度を目標値に対して±１．０mass%以内にする
ことを特徴とするＴｉ−Ａｌ基合金の鋳造方法。 In an induction melting furnace using a water-cooled copper crucible, a Ti-Al-based alloy casting method is used in which molten metal is poured into a mold from a hot water outlet provided at the bottom of the crucible to cast an ingot of a Ti-Al-based alloy. There,
The degree of vacuum in the induction melting furnace when melting or casting the Ti—Al base alloy is set in the range of 80 to 700 torr, and the Al concentration of the cast ingot is ± 1.0 mass% with respect to the target value. A method for casting a Ti—Al based alloy, which is characterized by being within the range.
Priority Applications (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2019143776A JP2021023967A (en) | 2019-08-05 | 2019-08-05 | Ti-Al BASED ALLOY CASTING METHOD |
| EP20850248.4A EP3995227A4 (en) | 2019-08-05 | 2020-07-10 | Method for casting ti-al based alloy |
| US17/630,322 US20220250141A1 (en) | 2019-08-05 | 2020-07-10 | METHOD FOR CASTING Ti-Al BASED ALLOY |
| PCT/JP2020/027164 WO2021024704A1 (en) | 2019-08-05 | 2020-07-10 | METHOD FOR CASTING Ti-AL BASED ALLOY |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2019143776A JP2021023967A (en) | 2019-08-05 | 2019-08-05 | Ti-Al BASED ALLOY CASTING METHOD |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JP2021023967A true JP2021023967A (en) | 2021-02-22 |
Family
ID=74502616
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2019143776A Pending JP2021023967A (en) | 2019-08-05 | 2019-08-05 | Ti-Al BASED ALLOY CASTING METHOD |
Country Status (4)
| Country | Link |
|---|---|
| US (1) | US20220250141A1 (en) |
| EP (1) | EP3995227A4 (en) |
| JP (1) | JP2021023967A (en) |
| WO (1) | WO2021024704A1 (en) |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS63273562A (en) * | 1987-04-30 | 1988-11-10 | Daido Steel Co Ltd | Production of ti-al alloy casting |
| JPH08238553A (en) * | 1995-03-02 | 1996-09-17 | Honda Motor Co Ltd | Directional solidified casting method |
| JP2008142717A (en) * | 2006-12-06 | 2008-06-26 | Daido Steel Co Ltd | METHOD AND APPARATUS FOR MAKING INGOT OF Ti AND Ti ALLOY OR TiAl |
| WO2018110370A1 (en) * | 2016-12-13 | 2018-06-21 | 株式会社神戸製鋼所 | Casting method for active metal |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP3125394B2 (en) * | 1991-12-06 | 2001-01-15 | 日本鋼管株式会社 | Casting method of titanium-aluminum alloy casting |
| JP3125393B2 (en) * | 1991-12-06 | 2001-01-15 | 日本鋼管株式会社 | Casting method of titanium-aluminum alloy casting |
| JP7043217B2 (en) | 2016-12-13 | 2022-03-29 | 株式会社神戸製鋼所 | How to cast active metal |
| JP2019143776A (en) | 2018-02-23 | 2019-08-29 | Ntn株式会社 | Rolling bearing |
-
2019
- 2019-08-05 JP JP2019143776A patent/JP2021023967A/en active Pending
-
2020
- 2020-07-10 WO PCT/JP2020/027164 patent/WO2021024704A1/en unknown
- 2020-07-10 EP EP20850248.4A patent/EP3995227A4/en active Pending
- 2020-07-10 US US17/630,322 patent/US20220250141A1/en not_active Abandoned
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS63273562A (en) * | 1987-04-30 | 1988-11-10 | Daido Steel Co Ltd | Production of ti-al alloy casting |
| JPH08238553A (en) * | 1995-03-02 | 1996-09-17 | Honda Motor Co Ltd | Directional solidified casting method |
| JP2008142717A (en) * | 2006-12-06 | 2008-06-26 | Daido Steel Co Ltd | METHOD AND APPARATUS FOR MAKING INGOT OF Ti AND Ti ALLOY OR TiAl |
| WO2018110370A1 (en) * | 2016-12-13 | 2018-06-21 | 株式会社神戸製鋼所 | Casting method for active metal |
Also Published As
| Publication number | Publication date |
|---|---|
| US20220250141A1 (en) | 2022-08-11 |
| EP3995227A1 (en) | 2022-05-11 |
| WO2021024704A1 (en) | 2021-02-11 |
| EP3995227A4 (en) | 2022-08-17 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| RU2490350C2 (en) | METHOD FOR OBTAINING BASIC β-γ-TiAl-ALLOY | |
| JP2020514551A (en) | Aluminum-scandium alloys having high homogeneity and elemental content and articles thereof | |
| CN112430767B (en) | Large-size hollow ingot casting and ingot casting method | |
| RU2729246C1 (en) | Casting method for active metal | |
| JP6994392B2 (en) | Ingot made of an alloy containing titanium as the main component, and its manufacturing method | |
| WO2021024704A1 (en) | METHOD FOR CASTING Ti-AL BASED ALLOY | |
| CN101121969A (en) | Liquid state hydrogen-replacing thinning solidifying tissue method in Ti-6Al-4V alloy induction shell smelting process | |
| WO2021192875A1 (en) | Graphite nozzle for bottom tapping and ti-al alloy casting method | |
| CN112760456B (en) | Bismuth-containing oriented silicon steel smelting method enabling bismuth yield to be not less than 70% | |
| JP2018188725A (en) | Ingot consisting of alloy of high melting point active metal and manufacturing method therefor | |
| RU2697144C1 (en) | Method for semi-continuous casting of ingots from aluminum alloys | |
| JPH08176810A (en) | Production of aluminum-high melting point metal alloy ingot and target material | |
| WO2018110370A1 (en) | Casting method for active metal | |
| JP7406073B2 (en) | Manufacturing method for titanium ingots | |
| JP2008018453A (en) | Continuous casting method for molten metal, and immersion lance for continuous casting | |
| JP2023149111A (en) | Alloy ingot production method and alloy ingot production bottom tap nozzle | |
| JP7406074B2 (en) | Titanium ingot manufacturing method and titanium ingot manufacturing mold | |
| JP7471946B2 (en) | Manufacturing method of titanium ingot | |
| RU2762956C1 (en) | Method for manufacturing cast billets from antifriction bronze | |
| RU2778039C1 (en) | Method for modifying the structure of cast blanks from antifriction bronze for diffusion welding with steel (options) | |
| JP2012228722A (en) | Melting furnace for smelting metal | |
| JP7417056B2 (en) | titanium alloy ingot | |
| JP7406075B2 (en) | Titanium ingot manufacturing method and titanium ingot manufacturing mold | |
| JP2005028452A (en) | CONTINUOUS CASTING METHOD OF Al-Mg-Si ALLOY AND Al-Mg-Si ALLOY INGOT, MANUFACTURING METHOD OF Al-Mg-Si ALLOY SHEET AND Al-Mg-Si ALLOY SHEET, AND MANUFACTURING METHOD OF HEAT RADIATION MATERIAL AND HEAT RADIATION MATERIAL | |
| JPH0531568A (en) | Plasma melting/casting method |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A621 | Written request for application examination |
Free format text: JAPANESE INTERMEDIATE CODE: A621 Effective date: 20211026 |
|
| A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20220726 |
|
| A521 | Request for written amendment filed |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20220916 |
|
| A02 | Decision of refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A02 Effective date: 20221101 |