JPH07118773A - Production of ti or ti alloy rolled stock - Google Patents
Production of ti or ti alloy rolled stockInfo
- Publication number
- JPH07118773A JPH07118773A JP5263789A JP26378993A JPH07118773A JP H07118773 A JPH07118773 A JP H07118773A JP 5263789 A JP5263789 A JP 5263789A JP 26378993 A JP26378993 A JP 26378993A JP H07118773 A JPH07118773 A JP H07118773A
- Authority
- JP
- Japan
- Prior art keywords
- strip
- titanium
- rolled
- gas atmosphere
- alloy
- 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
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、チタンまたはチタン合
金の圧延材を、溶解と連続鋳造を直結した工程を経て製
造する方法に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing a rolled material of titanium or titanium alloy through a process in which melting and continuous casting are directly connected.
【０００２】[0002]
【従来の技術】チタンは軽くて優れた耐食性を有し、ま
たその圧延材は強度や延性にも優れていることから、化
学工業設備、各種産業機器、海洋構造物、屋根材、レジ
ャー用品等、用途が拡大し、需要が増大している。ま
た、Ｔｉ−６Ａｌ−４Ｖを代表とするチタン合金の圧延
材は、耐熱性にも優れ、さらに比強度も高いことから、
航空機部品、自動車部品等に使用され、その需要も増大
している。2. Description of the Prior Art Titanium is light and has excellent corrosion resistance, and its rolled material is also excellent in strength and ductility. Therefore, chemical industrial equipment, various industrial equipment, marine structures, roofing materials, leisure goods, etc. , The applications are expanding, and the demand is increasing. Further, since a rolled material of titanium alloy represented by Ti-6Al-4V has excellent heat resistance and high specific strength,
It is used for aircraft parts, automobile parts, etc., and its demand is increasing.
【０００３】ところで、チタンは活性金属であることか
ら、チタンおよびチタン合金は、大気との反応による酸
化や窒化を避けるため、従来はほとんどが、真空中でア
ーク溶解され鋳造されていた。すなわち、スポンジチタ
ンやチタンスクラップをプレスして固め、チタン合金の
場合は合金元素を添加して円柱形の棒状電極を製作し、
これを陰極として、真空中で水冷銅鋳型内の溶湯との間
にアークを作って電極を溶解し、該鋳型内で凝固させて
いた。鋳型は、アークの安定性確保のため、円柱形の電
極と同心円をなす円筒状であるため、得られるチタンま
たはチタン合金の鋳片は円柱形であった。また、チタン
またはチタン合金の溶解法として、電子ビーム再溶解法
（ＥＢＲ法），プラズマ溶解法等も一部で試みられてい
るが、いずれも小規模な実験的なものであった。By the way, since titanium is an active metal, most of titanium and titanium alloys have conventionally been arc-melted and cast in a vacuum in order to avoid oxidation and nitridation due to reaction with the atmosphere. That is, titanium sponge or titanium scrap is pressed and solidified, and in the case of a titanium alloy, alloy elements are added to produce a cylindrical rod electrode,
Using this as a cathode, an arc was created between the molten metal in a water-cooled copper mold and the electrode in a vacuum to melt the electrode and solidify in the mold. The mold had a cylindrical shape that was concentric with the cylindrical electrode in order to ensure the stability of the arc, and thus the obtained titanium or titanium alloy slab had a cylindrical shape. Further, as a melting method of titanium or a titanium alloy, an electron beam remelting method (EBR method), a plasma melting method, and the like have been partially tried, but all of them are small-scale experimental methods.
【０００４】[0004]
【発明が解決しようとする課題】従来のチタンまたはチ
タン合金の真空アーク溶解法においては、Ｆｅ，Ｃｒ，
Ｍｎなど分配係数の小さな元素を添加しようとする場
合、これら元素が著しい凝固偏析を生じるため、溶解可
能な成分系に限界があった。また、従来の真空アーク溶
解法で得られる鋳片は円柱状であるため、板、棒および
線等の圧延材を得るためには、鍛造や分塊圧延により、
断面を丸から長方形や正方形のスラブやビレットにし、
それらを熱間圧延していた。このため、スラブやビレッ
トの先後端クロップや、中間での再加熱時のスケールに
よるロス等で製造歩留りが非常に悪く、また製造工期が
長期に亘っていた。In the conventional vacuum arc melting method for titanium or titanium alloy, Fe, Cr,
When adding an element having a small distribution coefficient such as Mn, these elements cause remarkable solidification segregation, so that there is a limit to the soluble component system. Further, since the cast piece obtained by the conventional vacuum arc melting method has a columnar shape, in order to obtain a rolled material such as a plate, a rod and a wire, by forging or slabbing,
Change the cross section from round to rectangular or square slab or billet,
They were hot rolling. For this reason, the production yield is very poor due to the leading and trailing edge crops of the slab and billet, the loss due to the scale during reheating in the middle, and the manufacturing period is long.
【０００５】さらに、溶解が小ロットのバッチ処理であ
ったため、後工程でも小ロットの不連続処理となり、製
造条件の安定化に難があって製品の材質が不均一で、か
つ工程管理が複雑になるという問題もあった。またチタ
ン合金の場合は、一般に熱間加工性が劣り、鍛造や圧延
時に割れが生じ易く、これも製造可能成分系の限定原因
になっていた。Furthermore, since the dissolution is a batch process of a small lot, the small lot is discontinuous even in the post-process, it is difficult to stabilize the manufacturing conditions, the material of the product is non-uniform, and the process control is complicated. There was also the problem of becoming. Further, in the case of titanium alloy, in general, the hot workability is inferior and cracks are likely to occur during forging or rolling, which is also a cause of limiting the manufacturable component system.
【０００６】本発明は、チタンまたはチタン合金圧延材
の製造において、不純物元素および合金元素の偏析を軽
減し、熱間加工性の問題も解決して、チタン合金の製造
可能成分系の拡大を図り、さらに材質の向上と均一化、
製造歩留りの向上、工程管理の簡易化、省エネ等の達成
を目的とする。The present invention reduces the segregation of impurity elements and alloy elements in the production of rolled titanium or titanium alloy, solves the problem of hot workability, and expands the manufacturable component system of titanium alloy. , Further improvement and homogenization of material,
The objective is to improve manufacturing yield, simplify process control, and save energy.
【０００７】[0007]
【課題を解決するための手段】上記目的を達成するため
の本発明法は、チタンまたはチタン合金を不活性ガス雰
囲気中でプラズマ溶解し、引続き不活性ガス雰囲気中に
て連続鋳造によりストリップを製造し、ついで該ストリ
ップを圧延することを特徴とするチタンまたはチタン合
金圧延材の製造方法である。また、溶解を真空中で高周
波誘導加熱を熱源とするスカルメルト法により行い、引
続き上記方法と同様、不活性ガス雰囲気中にて連続鋳造
によりストリップを製造し、ついで該ストリップを圧延
することを特徴とするチタンまたはチタン合金圧延材の
製造方法である。そして、ストリップは、双ロール鋳造
法により厚さ１〜５mmのものを製造するのが好ましく、
さらに該ストリップの顕熱を保持して熱間圧延し、ある
いは該ストリップを冷間圧延するのが好ましい。To achieve the above object, the method of the present invention is to produce a strip by plasma-melting titanium or titanium alloy in an inert gas atmosphere and then continuously casting in the inert gas atmosphere. And then rolling the strip, which is a method for producing a rolled titanium or titanium alloy material. Further, melting is performed by a skull melt method using high-frequency induction heating as a heat source in a vacuum, and subsequently, similarly to the above method, a strip is manufactured by continuous casting in an inert gas atmosphere, and then the strip is rolled. This is a method for producing a rolled titanium or titanium alloy material. And, it is preferable to manufacture the strip with a thickness of 1 to 5 mm by a twin roll casting method,
Further, it is preferable to carry out hot rolling while maintaining the sensible heat of the strip, or to carry out cold rolling of the strip.
【０００８】[0008]
【作用】以下、本発明を図面により詳細に説明する。第
１発明を、双ロール鋳造法により行う例を図１に示す。
まず、溶解すべきチタンまたはチタン合金からなる電極
棒１を、扉１４から置換室１０に入れ、雰囲気をアルゴ
ンガス等の不活性ガスで置換する。ついで扉１５を開
け、搬送ローラー２２により電極棒１を溶解室８に搬送
する。溶解室８内は不活性ガス雰囲気に保たれていて、
先行の電極棒２を所定の速度で送りつつ、その先端をプ
ラズマトーチ２４により溶解している。溶接室８に装入
した電極棒１の先端を、先行の電極棒２の後端と接触さ
せ、先行の電極棒２と同一速度で送りつつ、溶接トーチ
２３により溶接する。このとき、溶接トーチ２３は点線
の位置から、電極棒１および２と同速度で走行させる。
溶解したチタンまたはチタン合金の溶湯３は、タンディ
ッシュ２６で受け、プラズマトーチ２５により所定の温
度に均一化する。The present invention will be described in detail below with reference to the drawings. An example in which the first invention is carried out by a twin roll casting method is shown in FIG.
First, the electrode rod 1 made of titanium or titanium alloy to be melted is put into the replacement chamber 10 through the door 14 and the atmosphere is replaced with an inert gas such as argon gas. Then, the door 15 is opened, and the electrode rod 1 is transported to the melting chamber 8 by the transport roller 22. The inside of the melting chamber 8 is kept in an inert gas atmosphere,
The leading end of the electrode rod 2 is melted by the plasma torch 24 while feeding the preceding electrode rod 2 at a predetermined speed. The tip of the electrode rod 1 loaded in the welding chamber 8 is brought into contact with the rear end of the preceding electrode rod 2, and the welding is performed by the welding torch 23 while sending the electrode rod 1 at the same speed as the preceding electrode rod 2. At this time, the welding torch 23 is run at the same speed as the electrode rods 1 and 2 from the position indicated by the dotted line.
The molten metal 3 of titanium or titanium alloy is received by the tundish 26 and homogenized to a predetermined temperature by the plasma torch 25.
【０００９】つぎに、チタンまたはチタン合金の溶湯３
を、同じく不活性ガス雰囲気に保たれている鋳造室９に
入れる。溶湯３をタンディッシュ２６から堰２７を経
て、双ロール２８により鋳造し、ピンチローラー２９で
引抜き、多段に設けた冷却ガスノズル３０により冷却し
てストリップ４を製造し、コイラー３１に巻き取り、カ
ッター３４で切断してストリップコイル５とする。コイ
ラー３１は２基設け（図は１基のみ示す）、交互に巻き
取るようにしておき、巻き終ったストリップコイル５
は、扉１６を開けて置換室１１に入れる。なお溶解室８
と鋳造室９の間は、両室の雰囲気ガスが同一なので、仕
切壁がなくてもよいが、溶解室８は溶解のために高温状
態を維持し、鋳造室９はストリップ４の冷却用ガスを使
用するため、仕切壁を設けた方がよい。Next, molten metal 3 of titanium or titanium alloy
Are placed in a casting chamber 9 which is also kept in an inert gas atmosphere. The molten metal 3 is cast from the tundish 26 through the weir 27, by twin rolls 28, drawn out by a pinch roller 29, cooled by a cooling gas nozzle 30 provided in multiple stages to manufacture a strip 4, wound on a coiler 31, and cut by a cutter 34. And cut into strip coils 5. Two coilers 31 are provided (only one is shown in the figure) and they are wound alternately, and the strip coil 5 is wound.
Opens the door 16 and enters the replacement chamber 11. The melting chamber 8
Since the atmosphere gas in both chambers is the same as that in the casting chamber 9, there is no need for a partition wall, but the melting chamber 8 maintains a high temperature state for melting, and the casting chamber 9 uses the cooling gas for the strip 4 as a cooling gas. Since it is used, it is better to provide a partition wall.
【００１０】このようにして製造したストリップコイル
５を、熱間圧延または冷間圧延して圧延材とする。熱間
圧延する場合は、扉１８を開けて、ストリップコイル５
を保定炉１３に入れ、所定温度で所定時間、加熱保持す
る。保定炉１３では、鋳造されたストリップ４の顕熱を
利用し、必要に応じて加熱してもよい。保定炉１３の雰
囲気は不活性ガスでも真空でもよく、前者の場合は置換
室１１を不活性ガス雰囲気のままとし、扉１８を開けて
ストリップコイル５を装入すればよく、後者の場合は、
置換室１１を真空にした後、扉１８を開けて装入する。
保定した後、扉１９を開けてストリップコイル５を取出
し、熱間圧延機（図示せず）にて圧延する。熱間圧延の
雰囲気は大気でもよい。なお、ストリップ４を鋳造室９
にて巻き取らず、不活性ガス雰囲気のルーパー（図示せ
ず）を介し、必要に応じ保定炉を通して、熱間圧延機に
導入してもよい。The strip coil 5 thus manufactured is hot-rolled or cold-rolled to obtain a rolled material. For hot rolling, open the door 18 and strip coil 5
Is placed in the holding furnace 13 and heated and held at a predetermined temperature for a predetermined time. In the holding furnace 13, sensible heat of the cast strip 4 may be used to heat the strip 4 if necessary. The atmosphere of the retaining furnace 13 may be an inert gas or a vacuum. In the former case, the replacement chamber 11 may be kept in an inert gas atmosphere, the door 18 may be opened and the strip coil 5 may be inserted. In the latter case,
After evacuating the replacement chamber 11, the door 18 is opened and charged.
After retaining, the door 19 is opened and the strip coil 5 is taken out and rolled by a hot rolling mill (not shown). The atmosphere of hot rolling may be air. The strip 4 is placed in the casting chamber 9
It may be introduced into the hot rolling mill through a looper (not shown) in an inert gas atmosphere, if necessary through a retaining furnace, without being wound.
【００１１】冷間圧延する場合は、置換室１１内あるい
は別途設けた冷却室（図示せず）の不活性ガス雰囲気中
で、酸化あるいは窒化を生じない温度域まで冷却した
後、必要に応じて表面手入れを行い、冷間圧延機（図示
せず）にて圧延する。熱間圧延あるいは冷間圧延した圧
延材は、熱処理および必要に応じて脱スケール処理を行
って圧延材製品となる。また、熱間圧延材をさらに冷間
圧延してもよい。In the case of cold rolling, after cooling to a temperature range where oxidation or nitriding does not occur in the replacement chamber 11 or in an inert gas atmosphere in a cooling chamber (not shown) provided separately, it is necessary. The surface is cleaned and rolled by a cold rolling mill (not shown). The hot-rolled or cold-rolled rolled material is subjected to a heat treatment and, if necessary, a descaling treatment to be a rolled material product. Further, the hot rolled material may be further cold rolled.
【００１２】以上述べた第１発明において、原料のプラ
ズマ溶解は、図２のように粉状あるいは小片状の原料６
を、タンディッシュ２６内の溶湯３に落し込み、プラズ
マトーチ２５を熱源として溶解する方法で行うこともで
きる。図２において、原料６は置換室１０内のホッパー
３５に収容し、不活性ガス雰囲気に置換した後、扉１５
を開き、不活性ガス雰囲気に保たれた溶解室８内の原料
装入管３６に入れ、タンディッシュ２６に落し込む。In the first invention described above, the plasma melting of the raw material is carried out by powdery or small piece raw material 6 as shown in FIG.
Can be dropped into the molten metal 3 in the tundish 26 and melted using the plasma torch 25 as a heat source. In FIG. 2, the raw material 6 is housed in the hopper 35 in the substitution chamber 10 and replaced with an inert gas atmosphere, and then the door 15
Is opened, put into the raw material charging pipe 36 in the melting chamber 8 kept in an inert gas atmosphere, and dropped into the tundish 26.
【００１３】また、連続鋳造によりストリップ４を製造
する工程は、図１の例のような双ロール法による他、双
ベルト法等により直接ストリップを製造してもよい。双
ロール法によると、板厚１〜５mm程度の表面性状のよい
ストリップが精度よく製造できる。さらに、図２のよう
に薄肉スラブ７を鋳造した後、インラインミル３３によ
り圧延してストリップ４を製造してもよい。図２におい
て、タンディッシュ２６から溶湯３を冷却鋳型３２に注
入し、プラズマトーチ２５で所定温度に均一化する。冷
却鋳型３２内で凝固シェルが形成され、ピンチローラー
２９で引抜き、冷却ガスノズル３０で冷却し、インライ
ンミル３３で圧延してストリップ４を製造する。その他
の工程は、図１で説明したとおりである。In the step of manufacturing the strip 4 by continuous casting, the strip may be directly manufactured by the twin belt method or the like as well as the twin roll method as shown in FIG. According to the twin roll method, a strip having a plate thickness of about 1 to 5 mm and good surface quality can be accurately manufactured. Further, the thin slab 7 may be cast as shown in FIG. 2 and then rolled by the in-line mill 33 to manufacture the strip 4. In FIG. 2, the molten metal 3 is poured into the cooling mold 32 from the tundish 26, and is homogenized to a predetermined temperature by the plasma torch 25. A solidified shell is formed in the cooling mold 32, drawn by the pinch roller 29, cooled by the cooling gas nozzle 30, and rolled by the in-line mill 33 to manufacture the strip 4. Other steps are as described in FIG.
【００１４】つぎに、第２発明を、双ロール鋳造法によ
り行う例を図３に示す。まずスカルメルト法について説
明する。図３（ａ）のように、チタンまたはチタン合金
の原料６を銅鋳型ルツボ３７に入れ、誘導加熱コイル３
８により真空中で高周波誘導加熱して溶解し、（ｂ）の
ように溶湯３とする。銅鋳型ルツボ３７を冷却すると
（ｃ）のようにチタンまたはチタン合金は周囲から凝固
する。このとき銅鋳型ルツボ３７を揺動させながら冷却
することにより、銅鋳型ルツボ３７のエッジまでチタン
またはチタン合金で覆われ、チタンルツボ３９が形成さ
れる（スカル法）。そして（ｄ）のように溶湯３を取出
し、このチタンルツボ３９（スカル）に、製造すべきチ
タンまたはチタン合金の原料６を装入し、扉１４から置
換室１０に入れ真空排気する。扉１５を開き、溶解室８
に入れて真空中で高周波誘導加熱により原料６を溶解す
る。Next, FIG. 3 shows an example in which the second invention is carried out by the twin roll casting method. First, the skull melt method will be described. As shown in FIG. 3A, the raw material 6 of titanium or titanium alloy is put into the copper mold crucible 37, and the induction heating coil 3
High-frequency induction heating is performed in a vacuum by means of 8 to melt, and a molten metal 3 is obtained as shown in FIG. When the copper mold crucible 37 is cooled, titanium or titanium alloy solidifies from the surroundings as shown in (c). At this time, by cooling while swinging the copper mold crucible 37, the edge of the copper mold crucible 37 is covered with titanium or a titanium alloy, and the titanium crucible 39 is formed (skull method). Then, as shown in (d), the molten metal 3 is taken out, the titanium crucible 39 (skull) is charged with the raw material 6 of titanium or titanium alloy to be produced, and the raw material 6 is put into the substitution chamber 10 through the door 14 and evacuated. Open the door 15 and melt chamber 8
And the raw material 6 is melted by high-frequency induction heating in vacuum.
【００１５】このとき、誘導加熱コイル３８には、コイ
ルの中心部が加熱される条件で通電すると、チタンの熱
伝導がわるいことからチタンルツボ３９は溶解せず、不
純物の混入が避けられる。チタンルツボ３９を傾けて溶
湯３をタンディッシュ２６に注入し、空のチタンルツボ
３９は扉２０を開いて置換室１２に入れ、扉２１を開け
て取出し、再度原料６を装入し、置換室１０に入れて繰
返し使用することができる。なお、スカルメルト法によ
る溶解を、不活性ガス雰囲気中で、アーク溶解により行
うこともできるが、電極から不純物元素が混入するおそ
れがあるので、本発明では不採用とする。At this time, when the induction heating coil 38 is energized under the condition that the central portion of the coil is heated, the titanium crucible 39 is not melted because the heat conduction of titanium is poor, and the mixing of impurities is avoided. The titanium crucible 39 is tilted to inject the molten metal 3 into the tundish 26, and the empty titanium crucible 39 opens the door 20 and puts it in the substitution chamber 12, opens the door 21 and takes it out, and again charges the raw material 6 into the substitution chamber 10. It can be put in and used repeatedly. It should be noted that the melting by the skull melt method can be performed by arc melting in an inert gas atmosphere, but it is not adopted in the present invention because an impurity element may be mixed from the electrode.
【００１６】タンディッシュ２６内の溶湯３は第１発明
と同様に、堰２７を経て双ロール２８により鋳造してス
トリップ４を製造してもよく、また、図２のように冷却
鋳型３２に注入して薄肉スラブ７としインラインミル３
３で圧延してストリップ４を製造してもよい。ストリッ
プ４の圧延については、上記第１発明と同様に行うこと
ができる。The molten metal 3 in the tundish 26 may be cast by the twin rolls 28 through the weir 27 to produce the strip 4 as in the first invention, and may be poured into the cooling mold 32 as shown in FIG. To make thin slab 7 and in-line mill 3
The strip 4 may be manufactured by rolling at 3. The strip 4 can be rolled in the same manner as in the first invention.
【００１７】本発明法により製造することのできる材料
は、通常の商用純チタンのほか、各種チタン合金があ
る。前述のように、従来は成分偏析等により溶解が困難
であったＦｅ，Ｃｒ，Ｍｎなど分配係数の小さな元素を
添加した原料も、本発明によれば、連続的に溶解するの
で、均一な成分のものが安定して溶解できる。また、溶
湯から直接ストリップを製造するか、あるいは薄肉スラ
ブを鋳造した後、インラインミルで圧延してストリップ
を製造するので、熱間加工性の問題も生じない。したが
って、本発明によると、従来は鋳造性あるいは熱間加工
性が劣悪なため製造することが極めて困難であったつぎ
のようなチタン合金の圧延材が、製造歩留りよく、安定
して製造できる。 （１） Ｔｉ−５Ｎｂ−５Ｆｅ−３Ａｌ （２） Ｔｉ−６Ａｌ−２Ｓｎ−２Ｃｒ−２Ｆｅ−１Ｍ
ｏ （３） Ｔｉ−１０Ｖ−２Ｆｅ−３Ａｌ （４） Ｔｉ−８Ａｌ−１Ｎｂ−１Ｍｏ−１Ｖ （５） Ｔｉ−２０Ａｌ−５Ｎｂ−５Ｖ−１Ｆｅ このようなストリップを圧延して得られた製品は、幅方
向および長さ方向の成分および材質が均質である。ま
た、製造工程においては、スケールロスや先後端のクロ
ップが少なく製造歩留りが高い。The materials that can be produced by the method of the present invention include various commercial titanium alloys in addition to ordinary commercial pure titanium. As described above, according to the present invention, a raw material to which an element having a small distribution coefficient such as Fe, Cr, and Mn, which has been difficult to dissolve due to segregation of components, is dissolved continuously according to the present invention. Can be dissolved stably. Further, since the strip is manufactured directly from the molten metal or the thin slab is cast and then rolled by an in-line mill to manufacture the strip, there is no problem of hot workability. Therefore, according to the present invention, the following rolled titanium alloy material, which has been extremely difficult to manufacture due to poor castability or hot workability, can be manufactured stably with good manufacturing yield. (1) Ti-5Nb-5Fe-3Al (2) Ti-6Al-2Sn-2Cr-2Fe-1M
o (3) Ti-10V-2Fe-3Al (4) Ti-8Al-1Nb-1Mo-1V (5) Ti-20Al-5Nb-5V-1Fe The product obtained by rolling such a strip has a width The direction and length components and materials are homogeneous. Further, in the manufacturing process, there is little scale loss and front and rear end crops, and the manufacturing yield is high.
【００１８】[0018]
（本発明例１） Ｔｉ−５Ｆｅ−５Ｎｂ−３Ａｌの組成
（重量％）を目標として配合した粉末原料を、冷間静水
圧プレスして電極棒を作成し、アルゴンガス雰囲気のハ
ース炉で溶解し、直径５０mmの棒材を鋳造した。図１に
示すような装置において、この棒材を電極棒１としてア
ルゴンガス雰囲気でプラズマ溶解し、双ロール法でスト
リップを製造した。プラズマトーチ２４および２５は、
ともに２７０ｋＷのものを使用し、タンディッシュ２６
内の温度を１５１０℃に保持した。双ロール２８は銅製
で内部を水冷とし、鋳造速度０．５ｍ／分で、板厚３m
m、板幅６００mmのストリップ４を鋳造した。(Invention Example 1) A powder raw material having a composition of Ti-5Fe-5Nb-3Al (weight%) as a target was cold isostatically pressed to prepare an electrode rod, which was melted in a hearth furnace in an argon gas atmosphere. A bar material having a diameter of 50 mm was cast. In the apparatus as shown in FIG. 1, this rod was used as the electrode rod 1 and plasma-melted in an argon gas atmosphere to produce a strip by the twin roll method. Plasma torches 24 and 25
Both used 270 kW, tundish 26
The internal temperature was maintained at 1510 ° C. The twin roll 28 is made of copper, the inside is water-cooled, the casting speed is 0.5 m / min, and the plate thickness is 3 m.
A strip 4 having m and a plate width of 600 mm was cast.
【００１９】冷却ガスノズル３０からアルゴンガスを吹
き付け、コイラー３１による巻取り温度を６５０℃に制
御した。プラズマ切断機からなるカッター３４でストリ
ップ４を切断し、ストリップコイル５を置換室１１を経
てアルゴンガス雰囲気の保定炉１３に装入した。装入温
度は７５０℃であり、保定炉１３からの抽出温度８００
℃まで２０分保定し、この間の加熱はしなかった。抽出
後、直ちに大気中にて、板厚１．５mmまで熱間圧延して
圧延材を製造した。圧延材の分析結果は表１のとおりで
あり、トップ（Ｔ）、ミドル（Ｍ）、ボトム（Ｂ）各片
とも偏析のない均一な組成からなる目標成分の材料が得
られた。また、熱間圧延後、放冷した材料、および放冷
後８５０℃で１時間加熱の溶体化後、水冷し、５５０℃
で８時間の時効処理をした材料の機械的性質は、表２に
示すとおりであり、溶体化および時効処理により高強度
材が得られた。なお、表中のσＢは引張強さ、σ0.2 は
０．２％耐力、εｌは伸びを示す。Argon gas was blown from the cooling gas nozzle 30 and the coiling temperature by the coiler 31 was controlled to 650 ° C. The strip 4 was cut by a cutter 34 composed of a plasma cutting machine, and the strip coil 5 was loaded into the retaining furnace 13 in an argon gas atmosphere through the displacement chamber 11. The charging temperature is 750 ° C, and the extraction temperature from the retention furnace 13 is 800
The temperature was kept at 20 ° C. for 20 minutes, and heating was not performed during this period. Immediately after the extraction, the rolled material was manufactured by hot rolling in the air to a plate thickness of 1.5 mm. The results of analysis of the rolled material are shown in Table 1, and a target component material having a uniform composition without segregation was obtained in each of the top (T), middle (M), and bottom (B) pieces. In addition, after hot rolling, the material is allowed to cool, and after being left to cool, it is heated at 850 ° C. for 1 hour to be a solution, and then cooled with water to 550 ° C.
The mechanical properties of the material that had been aged for 8 hours were as shown in Table 2, and a high strength material was obtained by solution treatment and aging treatment. In the table, σ B is tensile strength, σ 0.2 is 0.2% proof stress, and εl is elongation.
【００２０】[0020]
【表１】 [Table 1]
【００２１】[0021]
【表２】 [Table 2]
【００２２】（本発明例２） Ｔｉ−１０Ｖ−２Ｆｅ−
３Ａｌの組成（重量％）を持つ板の端材（スクラップ）
を、図３に示す真空中の高周波誘導加熱によるスカル炉
中で溶解し、双ロール法を用いてストリップを製造し
た。双ロール２８は銅製の内部を水冷とし、鋳造速度
０．５ｍ／分で、板厚３mm、板幅６００mmのストリップ
４を鋳造した。冷却ガスノズル３０から、アルゴンガス
を吹き付け、コイラー３１による巻取温度を７００℃に
制御した。(Invention Example 2) Ti-10V-2Fe-
Plate scraps (scrap) with a composition of 3Al (wt%)
Was melted in a skull furnace by high-frequency induction heating in vacuum shown in FIG. 3, and a strip was manufactured using a twin roll method. The twin roll 28 was made of copper and was water-cooled inside, and the strip 4 having a plate thickness of 3 mm and a plate width of 600 mm was cast at a casting speed of 0.5 m / min. Argon gas was blown from the cooling gas nozzle 30 to control the coiling temperature by the coiler 31 at 700 ° C.
【００２３】プラズマ切断機からなるカッター３４でス
トリップ４を切断し、ストリップコイル５を、置換室１
１を経てアルゴンガス雰囲気の保定炉１３に装入した。
装入温度は７５０℃であり、保定炉１３からの抽出温度
８００℃まで２０分間保定した。抽出後、直ちに大気中
にて１．５mmまで熱間圧延し圧延材を製造した。圧延材
の分析結果は、表３のとおりで、トップ（Ｔ）、ミドル
（Ｍ）、ボトム（Ｂ）各片とも偏析のない均一組成から
なる材料が得られた。The strip 4 is cut by the cutter 34, which is a plasma cutting machine, and the strip coil 5 is replaced with the replacement chamber 1.
It was charged into the retaining furnace 13 in an argon gas atmosphere through 1.
The charging temperature was 750 ° C. and the extraction temperature from the retaining furnace 13 was maintained at 800 ° C. for 20 minutes. Immediately after extraction, the material was hot-rolled to 1.5 mm in the atmosphere to produce a rolled material. The results of analysis of the rolled material are shown in Table 3, and a material having a uniform composition without segregation was obtained in each of the top (T), middle (M), and bottom (B) pieces.
【００２４】熱間圧延後、７８０℃で１時間加熱溶体化
し、空冷し、５２０℃で８時間の時効処理を施した材料
の機械的性質は、表４に示すとおりであり、溶体化およ
び時効処理により高強度・高靭性材が得られた。After hot rolling, the solution was heated to a solution at 780 ° C. for 1 hour, air-cooled, and aged for 8 hours at 520 ° C. The mechanical properties of the material are shown in Table 4. A high strength and high toughness material was obtained by the treatment.
【００２５】[0025]
【表３】 [Table 3]
【００２６】[0026]
【表４】 [Table 4]
【００２７】（本発明例３） 本発明例２と同様の方法
により、 Ｔｉ−６Ａｌ−２Ｓｎ−２Ｃｒ−２Ｆｅ−１Ｍｏ Ｔｉ−８Ａｌ−１Ｎｂ−１Ｍｏ−１Ｖ Ｔｉ−２０Ａｌ−５Ｎｂ−５Ｖ−１Ｆｅ の、３種類のチタン合金をスカル溶解し、双ロール法を
用いてストリップを製造した。板厚３mm、板幅６００mm
のストリップ材を鋳造後、プラズマ切断機からなるカッ
ター３４でストリップ４を切断し、ストリップコイル５
を、置換室１１を経てアルゴンガス雰囲気の保定炉１３
に装入した。装入温度は７５０℃であり、保定炉１３か
らの抽出温度８００℃まで２０分間保定した。抽出後、
直ちに大気中にて１．５mmまで熱間圧延し圧延材を製造
した。圧延材の分析結果は表５〜表７のとおりで、トッ
プ（Ｔ）、ミドル（Ｍ）、ボトム（Ｂ）各片とも偏析の
ない均一組成からなる材料が得られた。また、熱間圧延
後放冷した材料および各種熱処理を行った材料の機械的
性質は、表８〜表１０に示すように、優れたものであっ
た。(Invention Example 3) Ti-6Al-2Sn-2Cr-2Fe-1Mo Ti-8Al-1Nb-1Mo-1V Ti-20Al-5Nb-5V-1Fe was prepared by the same method as in Invention Example 2. Three types of titanium alloys were skull-melted and a strip was manufactured using a twin roll method. Board thickness 3 mm, board width 600 mm
After casting the strip material, the strip 4 is cut by the cutter 34 composed of a plasma cutting machine, and the strip coil 5 is cut.
Through the substitution chamber 11 and a holding furnace 13 in an argon gas atmosphere.
Charged into. The charging temperature was 750 ° C. and the extraction temperature from the retaining furnace 13 was maintained at 800 ° C. for 20 minutes. After extraction,
Immediately, hot rolling was performed to 1.5 mm in the atmosphere to produce a rolled material. The analysis results of the rolled material are shown in Tables 5 to 7, and the top (T), middle (M), and bottom (B) pieces each had a material having a uniform composition without segregation. Further, as shown in Tables 8 to 10, the mechanical properties of the material that was allowed to cool after hot rolling and the material that was subjected to various heat treatments were excellent.
【００２８】[0028]
【表５】 [Table 5]
【００２９】[0029]
【表６】 [Table 6]
【００３０】[0030]
【表７】 [Table 7]
【００３１】[0031]
【表８】 [Table 8]
【００３２】[0032]
【表９】 [Table 9]
【００３３】[0033]
【表１０】 [Table 10]
【００３４】（本発明例４） 純チタン板のスクラップ
を用い、アルゴンガス雰囲気中でのプラズマトーチを用
いたハース炉で溶解し、直径５０mmの棒材とした。図１
に示すような装置において、この棒材を電極棒として、
再度プラズマ溶解し、双ロール法でストリップを製造し
た。プラズマトーチ２４および２５はともに２７０ｋＷ
のものを用い、タンディッシュ２６内の温度を１７００
℃に保持した。双ロール２８は銅製で内部を水冷とし、
鋳造速度０．６ｍ／分で板厚４mm、板幅６００mmのスト
リップ４を鋳造した。(Inventive Example 4) Using a scrap of pure titanium plate, it was melted in a hearth furnace using a plasma torch in an argon gas atmosphere to obtain a bar material having a diameter of 50 mm. Figure 1
In the device as shown in, this rod is used as an electrode rod,
Plasma melting was performed again, and a strip was manufactured by the twin roll method. Plasma torches 24 and 25 are both 270 kW
The temperature in the tundish 26 is set to 1700
Hold at ℃. The twin roll 28 is made of copper and the inside is water-cooled,
A strip 4 having a plate thickness of 4 mm and a plate width of 600 mm was cast at a casting speed of 0.6 m / min.
【００３５】冷却ガスノズル３０からアルゴンガスを吹
き付け、コイラー３１による巻取温度を６００℃に制御
した。プラズマ切断機からなるカッター３４でストリッ
プ４を切断し、ストリップコイル５を置換室１１を経て
アルゴンガス雰囲気の保定炉１３に装入した。装入温度
は７００℃であり、保定炉からの抽出温度は８００℃
で、抽出後、直ちに大気中にて１．５mmまで熱間圧延し
圧延材を製造した。圧延後、６５０℃で３０分間焼鈍し
た。この圧延材の分析結果は表１１のとおりであり、含
有元素の鋳造長さ方向でのバラツキが非常に少ないこと
がわかる。なお成分分析の試料は、図４に示す鋳片位置
から採取したものである。Argon gas was blown from the cooling gas nozzle 30 to control the coiling temperature of the coiler 31 at 600 ° C. The strip 4 was cut by a cutter 34 composed of a plasma cutting machine, and the strip coil 5 was loaded into the retaining furnace 13 in an argon gas atmosphere through the displacement chamber 11. The charging temperature is 700 ° C, and the extraction temperature from the retaining furnace is 800 ° C.
Then, immediately after extraction, hot rolling was performed to 1.5 mm in the atmosphere to produce a rolled material. After rolling, it was annealed at 650 ° C. for 30 minutes. The results of analysis of this rolled material are shown in Table 11, and it can be seen that there is very little variation in the contained elements in the casting length direction. The sample for the component analysis was taken from the slab position shown in FIG.
【００３６】板厚１．５mmの圧延−焼鈍板を酸洗後、タ
ンデム圧延機を用いて、圧下率５０％の冷間圧延を行
い、０．７mmの板を製造した。この冷延板を６５０℃で
３０分間焼鈍して、機械的性質を調べた結果を表１２に
示す。従来工程材は、真空アーク溶解−鋳造（円柱ビレ
ット）−分塊−熱延−冷延を経て製造したものであり、
本発明工程材は、同様の成分系の従来工程材の機械的性
質とほとんど同じ水準を示すものであった。A rolled-annealed plate having a plate thickness of 1.5 mm was pickled, and then cold-rolled at a rolling reduction of 50% using a tandem rolling machine to manufacture a 0.7 mm plate. The cold rolled sheet is annealed at 650 ° C. for 30 minutes and the mechanical properties are examined. The results are shown in Table 12. Conventional process material is manufactured through vacuum arc melting-casting (cylindrical billet) -lumping-hot rolling-cold rolling,
The process material of the present invention showed almost the same level as the mechanical properties of the conventional process material having the same component system.
【００３７】[0037]
【表１１】 [Table 11]
【００３８】[0038]
【表１２】 [Table 12]
【００３９】[0039]
【発明の効果】本発明によれば、チタンまたはチタン合
金圧延材の製造において、不純物元素および合金元素の
偏析が軽減され、熱間加工性の問題も解決されるので、
従来は鋳造性あるいは熱間加工性が劣悪なため製造する
ことが極めて困難であった成分系のストリップが、製造
歩留りよく、安定して製造できる。これを圧延して得ら
れた製品は、幅方向および長さ方向の成分および材質が
均質である。また、製造工程においては、スケールロス
や先後端のクロップが少なく製造歩留りが高い。さらに
工程管理の簡易化、省エネ等が達成される。EFFECTS OF THE INVENTION According to the present invention, segregation of impurity elements and alloy elements is reduced in the production of rolled titanium or titanium alloy, and the problem of hot workability is solved.
The component-based strip, which has been extremely difficult to manufacture due to poor castability or hot workability in the past, can be manufactured stably with good manufacturing yield. The product obtained by rolling this is homogeneous in the components and materials in the width direction and the length direction. Further, in the manufacturing process, there is little scale loss and front and rear end crops, and the manufacturing yield is high. Furthermore, simplification of process control and energy saving are achieved.
【図１】本発明の第１発明を実施する装置の例を示す図
である。FIG. 1 is a diagram showing an example of an apparatus for carrying out a first invention of the present invention.
【図２】本発明の第１発明を実施する装置の別の例を示
す図である。FIG. 2 is a diagram showing another example of an apparatus for carrying out the first invention of the present invention.
【図３】本発明の第２発明を実施する装置の例を示す図
である。FIG. 3 is a diagram showing an example of an apparatus for carrying out a second invention of the present invention.
【図４】本発明の実施例における成分分析用試料の採取
位置を示す図である。FIG. 4 is a diagram showing a sampling position of a sample for component analysis in an example of the present invention.
１，２：電極棒 ３：溶湯 ４：ストリップ ５：ストリップコイル ６：原料 ７：薄肉スラブ ８：溶解室 ９：鋳造室 １０，１１，１２：置換室 １３：保定炉 １４〜２１：扉 ２２：搬送ローラー ２３：溶接トーチ ２４，２５：プラズマトーチ ２６：タンディッシュ ２７：堰 ２８：双ロール ２９：ピンチローラー ３０：冷却ガスノズル ３１：コイラー ３２：冷却鋳型 ３３：インラインミル ３４：カッター ３５：ホッパー ３６：原料装入管 ３７：銅鋳型ルツボ ３８：誘導加熱コイル ３９：チタンルツボ 1,2: Electrode rod 3: Molten metal 4: Strip 5: Strip coil 6: Raw material 7: Thin slab 8: Melting chamber 9: Casting chamber 10, 11, 12: Replacement chamber 13: Restoration furnace 14-21: Door 22: Conveyor roller 23: Welding torch 24, 25: Plasma torch 26: Tundish 27: Weir 28: Twin roll 29: Pinch roller 30: Cooling gas nozzle 31: Coiler 32: Cooling mold 33: In-line mill 34: Cutter 35: Hopper 36: Raw material charging pipe 37: Copper mold crucible 38: Induction heating coil 39: Titanium crucible
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.6 識別記号 庁内整理番号 ＦＩ 技術表示箇所 Ｂ２２Ｄ 11/12 Ａ 7362−4Ｅ Ｃ２２Ｂ 9/22 Ｃ２２Ｃ 14/00 Ｚ Ｃ２２Ｆ 1/18 Ｈ ─────────────────────────────────────────────────── ─── Continuation of the front page (51) Int.Cl. 6 Identification code Office reference number FI technical display location B22D 11/12 A 7362-4E C22B 9/22 C22C 14/00 Z C22F 1/18 H
Claims (5)
囲気中でプラズマ溶解し、引続き不活性ガス雰囲気中に
て連続鋳造によりストリップを製造し、ついで該ストリ
ップを圧延することを特徴とするチタンまたはチタン合
金圧延材の製造方法。1. Titanium or titanium, characterized in that titanium or a titanium alloy is plasma-melted in an inert gas atmosphere, a strip is subsequently produced by continuous casting in an inert gas atmosphere, and then the strip is rolled. Manufacturing method of rolled alloy material.
波誘導加熱を熱源とするスカルメルト法により溶解し、
引続き不活性ガス雰囲気中にて連続鋳造によりストリッ
プを製造し、ついで該ストリップを圧延することを特徴
とするチタンまたはチタン合金圧延材の製造方法。2. Titanium or a titanium alloy is melted in a vacuum by a skull melt method using high frequency induction heating as a heat source,
A method for producing a titanium or titanium alloy rolled material, which comprises continuously producing a strip by continuous casting in an inert gas atmosphere, and then rolling the strip.
トリップを製造することを特徴とする請求項１または請
求項２記載のチタンまたはチタン合金圧延材の製造方
法。3. The method for producing a rolled titanium or titanium alloy material according to claim 1, wherein a strip having a thickness of 1 to 5 mm is produced by a twin roll casting method.
間圧延することを特徴とする請求項３記載のチタンまた
はチタン合金圧延材の製造方法。4. The method for producing a rolled titanium or titanium alloy material according to claim 3, wherein the sensible heat of the cast strip is retained and hot-rolled.
を特徴とする請求項３記載のチタンまたはチタン合金圧
延材の製造方法。5. The method for producing a titanium or titanium alloy rolled material according to claim 3, wherein the cast strip is cold-rolled.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5263789A JPH07118773A (en) | 1993-10-21 | 1993-10-21 | Production of ti or ti alloy rolled stock |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5263789A JPH07118773A (en) | 1993-10-21 | 1993-10-21 | Production of ti or ti alloy rolled stock |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH07118773A true JPH07118773A (en) | 1995-05-09 |
Family
ID=17394284
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP5263789A Pending JPH07118773A (en) | 1993-10-21 | 1993-10-21 | Production of ti or ti alloy rolled stock |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH07118773A (en) |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2000158098A (en) * | 1998-12-01 | 2000-06-13 | Shin Etsu Chem Co Ltd | Apparatus for producing hydrogen-storage alloy and production thereof |
| JP2002126858A (en) * | 2000-10-23 | 2002-05-08 | Ulvac Japan Ltd | Cooling vessel for sheetlike cast piece |
| JP2004512953A (en) * | 2000-09-19 | 2004-04-30 | メイン・マネジメント・インスピレーション・アクチェンゲゼルシャフト | Sheet metal casting machine for the production of sheet metal |
| KR100920638B1 (en) * | 2002-12-23 | 2009-10-08 | 주식회사 포스코 | Methods of manufacturing non-ferrous metal strip sheet with twin roll strip casting apparatus |
| JP2013052417A (en) * | 2011-09-05 | 2013-03-21 | Kobe Steel Ltd | Casting mold for continuous casting of ingot of titanium or titanium alloy, and continuous casting apparatus with the same |
| WO2013151061A1 (en) | 2012-04-02 | 2013-10-10 | 株式会社神戸製鋼所 | Mold for continuous casting of titanium or titanium alloy ingot, and continuous casting device provided with same |
| JP2014172093A (en) * | 2013-03-05 | 2014-09-22 | Rti Internat Metals Inc | Method of making long ingots by cutting in furnace |
| JP2014172092A (en) * | 2013-03-05 | 2014-09-22 | Rti Internat Metals Inc | Continuous casting furnace for long ingot casting |
| CN110947764A (en) * | 2019-12-03 | 2020-04-03 | 西安庄信新材料科技有限公司 | Titanium strip coil slitting method |
| US20200376528A1 (en) * | 2016-03-03 | 2020-12-03 | Michael Thomas Stawovy | Fabrication of metallic parts by additive manufacturing |
| CN112458322A (en) * | 2020-10-27 | 2021-03-09 | 新疆湘润新材料科技有限公司 | Preparation method for improving uniformity of oxygen elements of titanium and titanium alloy ingots |
| CN113210576A (en) * | 2021-05-17 | 2021-08-06 | 上海大学 | Method and device for producing metal thin strip |
| CN113272085A (en) * | 2018-12-13 | 2021-08-17 | 赛峰飞机发动机公司 | Semi-continuous casting of ingots by compressing the metal during solidification |
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-
1993
- 1993-10-21 JP JP5263789A patent/JPH07118773A/en active Pending
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2000158098A (en) * | 1998-12-01 | 2000-06-13 | Shin Etsu Chem Co Ltd | Apparatus for producing hydrogen-storage alloy and production thereof |
| JP2004512953A (en) * | 2000-09-19 | 2004-04-30 | メイン・マネジメント・インスピレーション・アクチェンゲゼルシャフト | Sheet metal casting machine for the production of sheet metal |
| JP2002126858A (en) * | 2000-10-23 | 2002-05-08 | Ulvac Japan Ltd | Cooling vessel for sheetlike cast piece |
| JP4527868B2 (en) * | 2000-10-23 | 2010-08-18 | 株式会社アルバック | Slab cooling vessel |
| KR100920638B1 (en) * | 2002-12-23 | 2009-10-08 | 주식회사 포스코 | Methods of manufacturing non-ferrous metal strip sheet with twin roll strip casting apparatus |
| JP2013052417A (en) * | 2011-09-05 | 2013-03-21 | Kobe Steel Ltd | Casting mold for continuous casting of ingot of titanium or titanium alloy, and continuous casting apparatus with the same |
| WO2013151061A1 (en) | 2012-04-02 | 2013-10-10 | 株式会社神戸製鋼所 | Mold for continuous casting of titanium or titanium alloy ingot, and continuous casting device provided with same |
| US9156081B2 (en) | 2012-04-02 | 2015-10-13 | Kobe Steel, Ltd. | Mold for continuous casting of titanium or titanium alloy ingot, and continuous casting device provided with same |
| JP2014172092A (en) * | 2013-03-05 | 2014-09-22 | Rti Internat Metals Inc | Continuous casting furnace for long ingot casting |
| JP2014172093A (en) * | 2013-03-05 | 2014-09-22 | Rti Internat Metals Inc | Method of making long ingots by cutting in furnace |
| US20200376528A1 (en) * | 2016-03-03 | 2020-12-03 | Michael Thomas Stawovy | Fabrication of metallic parts by additive manufacturing |
| US11554397B2 (en) * | 2016-03-03 | 2023-01-17 | H.C. Starck Solutions Coldwater LLC | Fabrication of metallic parts by additive manufacturing |
| US11919070B2 (en) | 2016-03-03 | 2024-03-05 | H.C. Starck Solutions Coldwater, LLC | Fabrication of metallic parts by additive manufacturing |
| CN113272085A (en) * | 2018-12-13 | 2021-08-17 | 赛峰飞机发动机公司 | Semi-continuous casting of ingots by compressing the metal during solidification |
| CN113272085B (en) * | 2018-12-13 | 2023-11-24 | 赛峰飞机发动机公司 | Semi-continuous casting of ingots by compression of metal during solidification |
| CN110947764A (en) * | 2019-12-03 | 2020-04-03 | 西安庄信新材料科技有限公司 | Titanium strip coil slitting method |
| CN112458322A (en) * | 2020-10-27 | 2021-03-09 | 新疆湘润新材料科技有限公司 | Preparation method for improving uniformity of oxygen elements of titanium and titanium alloy ingots |
| CN113210576A (en) * | 2021-05-17 | 2021-08-06 | 上海大学 | Method and device for producing metal thin strip |
| CN114178456A (en) * | 2021-11-26 | 2022-03-15 | 湖南金天钛业科技有限公司 | Forging processing method for oversized titanium alloy forging stock |
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