JPH0435554B2 - - Google Patents
Info
- Publication number
- JPH0435554B2 JPH0435554B2 JP57111101A JP11110182A JPH0435554B2 JP H0435554 B2 JPH0435554 B2 JP H0435554B2 JP 57111101 A JP57111101 A JP 57111101A JP 11110182 A JP11110182 A JP 11110182A JP H0435554 B2 JPH0435554 B2 JP H0435554B2
- Authority
- JP
- Japan
- Prior art keywords
- wire
- aluminum
- titanium
- titanium alloy
- alloy layer
- 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.)
- Expired
Links
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 33
- 229910052782 aluminium Inorganic materials 0.000 claims description 26
- 229910001069 Ti alloy Inorganic materials 0.000 claims description 25
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 24
- UQZIWOQVLUASCR-UHFFFAOYSA-N alumane;titanium Chemical compound [AlH3].[Ti] UQZIWOQVLUASCR-UHFFFAOYSA-N 0.000 claims description 22
- 238000004519 manufacturing process Methods 0.000 claims description 16
- 238000000034 method Methods 0.000 claims description 11
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 7
- 229910001873 dinitrogen Inorganic materials 0.000 claims description 7
- 239000011261 inert gas Substances 0.000 claims description 5
- 239000010410 layer Substances 0.000 description 20
- 229910045601 alloy Inorganic materials 0.000 description 8
- 239000000956 alloy Substances 0.000 description 8
- 238000005275 alloying Methods 0.000 description 7
- 239000003990 capacitor Substances 0.000 description 6
- 238000000635 electron micrograph Methods 0.000 description 5
- 239000000203 mixture Substances 0.000 description 5
- 238000009792 diffusion process Methods 0.000 description 4
- 238000005121 nitriding Methods 0.000 description 4
- 229910010038 TiAl Inorganic materials 0.000 description 3
- 239000010936 titanium Substances 0.000 description 3
- 239000007789 gas Substances 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000005304 joining Methods 0.000 description 2
- WABPQHHGFIMREM-UHFFFAOYSA-N lead(0) Chemical compound [Pb] WABPQHHGFIMREM-UHFFFAOYSA-N 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 150000002739 metals Chemical class 0.000 description 2
- 239000000843 powder Substances 0.000 description 2
- 238000002791 soaking Methods 0.000 description 2
- 229910052719 titanium Inorganic materials 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- 229910000838 Al alloy Inorganic materials 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 239000011247 coating layer Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 238000011109 contamination Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 229910001220 stainless steel Inorganic materials 0.000 description 1
- 238000001771 vacuum deposition Methods 0.000 description 1
- 238000005491 wire drawing Methods 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
- C23C2/12—Aluminium or alloys based thereon
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
Landscapes
- Chemical & Material Sciences (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Coating With Molten Metal (AREA)
- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
Description
【発明の詳細な説明】
本発明は、アルミニウム−チタン合金・ワイヤ
の製造方法に関するものである。DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a method for manufacturing an aluminum-titanium alloy wire.
本発明者らは既にアルミニウム−チタン合金を
陽極体とする電解コンデンサの製造方法について
提案したが、この電解コンデンサに用いられるリ
ードワイヤとしてはチタンワイヤの表面にアルミ
ニウム−チタン合金層を形成したものが望まし
い。 The present inventors have already proposed a method for manufacturing an electrolytic capacitor using an aluminum-titanium alloy as an anode body, and the lead wire used in this electrolytic capacitor is one in which an aluminum-titanium alloy layer is formed on the surface of a titanium wire. desirable.
チタン・ワイヤの表面をアルミニウムで被覆、
あるいは合金化する方法としては、次のような製
造方法が考えられる。 Coating the surface of titanium wire with aluminum,
Alternatively, as a method for alloying, the following manufacturing method can be considered.
(1) ステンレス等のパイプの空洞内中心線上にチ
タンワイヤを保持し、残部空洞にAl粉末を充
填し、パイプをスウエージング加工等により圧
縮成形した後、適当な熱処理によつてAl粉末
を焼結する。その後パイプから取り出し、線引
加工等により、所望の太さに加工する。この場
合、Al被覆層の厚さおよびその後の熱処理条
件等によつてワイヤ表面がAl−Ti合金層とな
るかAl層となるかが決まる。(1) Hold a titanium wire on the center line inside the cavity of a stainless steel pipe, fill the remaining cavity with Al powder, compression mold the pipe by swaging, etc., and then sinter the Al powder by appropriate heat treatment. conclude. After that, it is taken out from the pipe and processed to the desired thickness by wire drawing or the like. In this case, whether the wire surface becomes an Al--Ti alloy layer or an Al layer is determined by the thickness of the Al coating layer and the subsequent heat treatment conditions.
(2) チタン・ワイヤ表面にアルミニウムを真空蒸
着する。(2) Vacuum evaporate aluminum onto the surface of the titanium wire.
すなわち、チタン・ワイヤを真空蒸着装置内
で回転させる等の操作を行なえば、アルミニウ
ムを均一に被覆することができる。 That is, by performing operations such as rotating the titanium wire within a vacuum deposition apparatus, aluminum can be coated uniformly.
(3) チタン・ワイヤを真空中あるいは不活性ガス
中、あるいは窒素ガス中で溶融アルミニウム中
を通過させる。(3) Pass the titanium wire through molten aluminum in vacuum, inert gas, or nitrogen gas.
これら３種の製造方法の中で、一番実際的
で、量産性に富み、かつ均一なアルミニウム−
チタン合金層、あるいはアルミニウム層が得ら
れる方法は(3)の方法である。 Of these three manufacturing methods, this is the most practical, mass-producible, and uniform aluminum manufacturing method.
The method (3) is used to obtain a titanium alloy layer or an aluminum layer.
本発明者らは、この(3)の真空中あるいは不活性
ガス中あるいは窒素ガス中で、溶融したアルミニ
ウム中をチタン・ワイヤを通過させる方法により
チタン・ワイヤの外表面をアルミニウムで合金化
したワイヤの製造を試みた。チタン・ワイヤの表
面状態、溶融アルミニウム中を通過させる温度、
溶融アルミニウム・ゾーンの長さ、チタン・ワイ
ヤの送り（通過）速度等の諸条件について種々検
討した結果、次の様なことが明らかとなり、この
ままでは量産性に問題のあることがわかつた。す
なわち、純チタンは約880℃にα（六方晶系）←→
β（立方晶系）の結晶変態点があり、1000℃以上
のβ相では、すべり変形、粒成長が激しくなるた
め線材としての引張り強度が著しく低下する。従
つて、1000℃以上では、ワイヤが断線し易く、連
続処理が行えない。 The present inventors have developed a wire in which the outer surface of a titanium wire is alloyed with aluminum by the method (3) of passing the titanium wire through molten aluminum in a vacuum, an inert gas, or a nitrogen gas. attempted to manufacture. The surface condition of the titanium wire, the temperature at which it passes through molten aluminum,
As a result of various studies on various conditions such as the length of the molten aluminum zone and the feeding (passing) speed of the titanium wire, the following became clear, and it was found that there would be problems with mass production if the situation remained as it was. In other words, pure titanium changes to α (hexagonal system) at approximately 880℃ ←→
It has a β (cubic system) crystal transformation point, and in the β phase at temperatures above 1000°C, sliding deformation and grain growth become severe, resulting in a significant decrease in tensile strength as a wire rod. Therefore, at temperatures above 1000°C, the wire is likely to break and continuous processing cannot be performed.
このため、800℃〜1000℃で処理することにな
るが、この温度条件では、ワイヤが溶融アルミニ
ウム中を通過する際にアルミニウムのチタンに対
する拡散、合金化が遅く、合金化層を厚くするた
めには、溶融アルミニウム中を何回も繰り返し通
過させねがならない。また、アルミニウムの拡散
が遅いため、ワイヤの送り速度も大きくすること
も出来ないので、量産性に乏しい。更に、このよ
うにして出来上がつたワイヤは、表面の拡散、合
金層の組成的均一性および、厚みの均一性という
点でも優れたものが得にくいことがわかつた。 For this reason, processing is performed at 800℃ to 1000℃, but under this temperature condition, when the wire passes through molten aluminum, the diffusion and alloying of aluminum with titanium is slow, and in order to thicken the alloyed layer. must be passed through molten aluminum many times. Furthermore, since the diffusion of aluminum is slow, the wire feeding speed cannot be increased, resulting in poor mass productivity. Furthermore, it has been found that it is difficult to obtain wires produced in this manner that are excellent in terms of surface diffusion, compositional uniformity of the alloy layer, and thickness uniformity.
本発明の目的は、以上に説明したような問題点
を解決し、チタン・ワイヤの表面に組成および厚
み共に均一なアルミニウム合金層を、高速処理が
可能な量産性に富む方法で形成させ得る、アルミ
ニウム−チタン合金ワイヤの製造方法を提供しよ
うとするものである。 The purpose of the present invention is to solve the problems described above, and to form an aluminum alloy layer with a uniform composition and thickness on the surface of a titanium wire using a method that can be processed at high speed and is highly suitable for mass production. It is an object of the present invention to provide a method for manufacturing an aluminum-titanium alloy wire.
本発明によれば、チタン・ワイヤを真空中もし
くは不活性ガス中もしくは窒素ガス中において溶
融アルミニウム中を通過させ、ワイヤ表面をアル
ミニウム−チタン合金層とするアルミニウム−チ
タン合金ワイヤの製造方法において、チタン・ワ
イヤとして窒化処理をしたものを使用することに
より、ワイヤ表面に均一組成、均一厚みのアルミ
ニウム−チタン合金層を有し、かつ高速処理が可
能な量産性に富むアルミニウム−チタン合金ワイ
ヤの製造が可能となる。 According to the present invention, in the method for producing an aluminum-titanium alloy wire, the titanium wire is passed through molten aluminum in a vacuum, an inert gas, or a nitrogen gas to form an aluminum-titanium alloy layer on the surface of the wire.・By using a nitrided wire, it is possible to manufacture an aluminum-titanium alloy wire that has an aluminum-titanium alloy layer with a uniform composition and uniform thickness on the wire surface, and that can be processed at high speed and is highly mass-producible. It becomes possible.
電解コンデンサは通常、陽極体を形成する金属
材料と同質の材料を陽極リード・ワイヤとして使
用しているが、これは、異種金属の接合より同質
金属の接合の方が接合が行ない易く、かつ電解コ
ンデンサとしての特性の安定性、信頼性の上で優
れている。 Electrolytic capacitors usually use a material of the same quality as the metal material forming the anode body as the anode lead wire, but this is because joining of homogeneous metals is easier than joining of dissimilar metals, and electrolytic It has excellent stability and reliability as a capacitor.
従つて、本発明のアルミニウム−チタン合金ワ
イヤをアルミニウム−チタン合金電解コンデンサ
の陽極リードとして使用すれば、優れたコンデン
サ特性を得ることが期待され、実際に検討した結
果、これを確認した。 Therefore, if the aluminum-titanium alloy wire of the present invention is used as the anode lead of an aluminum-titanium alloy electrolytic capacitor, it is expected that excellent capacitor characteristics will be obtained, and this was confirmed through actual studies.
また窒化処理をしたチタン・ワイヤは、α←→
β変態温度（約880℃）、融点が高温側に移動す
る。このため、1000℃以上でも相変態を起こさず
低温相（α相）のままであり、更に窒化によつて
ワイヤそのものが硬化して引張り強度が増大する
ので1000℃以上の処理温度でも断線しない。な
お、窒化処理によつて必ずしもチタン・ワイヤの
中心部まで窒化されるとは限らない。 In addition, titanium wire that has been nitrided is α←→
β-transformation temperature (approximately 880℃), the melting point moves to the higher temperature side. For this reason, it does not undergo phase transformation even at temperatures above 1000°C and remains in the low-temperature phase (α phase), and since the wire itself hardens through nitriding and increases its tensile strength, it does not break even at processing temperatures above 1000°C. Note that the nitriding process does not necessarily nitride the titanium wire to its center.
ワイヤ中心部（内部側）が純Tiの状態であつ
たとしても、外表面から一定の距離にわたつて一
定の窒化状態になつていさえすれば、ここで説明
した効果は充分ある。 Even if the center (inside) of the wire is pure Ti, the effects described here are sufficient as long as the wire is in a constant nitrided state over a certain distance from the outer surface.
また真空中又は不活性ガス中、又は窒素ガス中
で処理すれば、酸素汚染等が少いという点で、よ
り質の良いアルミニウム−チタン合金ワイヤが得
られる。さらに窒素ガス雰囲気中で処理を行え
ば、使用する電気炉の均熱温度範囲の距離、処理
温度、ワイヤ送り速度等を調整することにより、
チタン・ワイヤの窒化処理、溶融アルミニウム通
過による合金化処理を同時に連続して行うことが
できる。 Further, if the wire is treated in vacuum, inert gas, or nitrogen gas, an aluminum-titanium alloy wire of better quality can be obtained in that there is less oxygen contamination. Furthermore, if processing is performed in a nitrogen gas atmosphere, by adjusting the soaking temperature range distance of the electric furnace used, processing temperature, wire feed speed, etc.
Nitriding treatment of titanium wire and alloying treatment by passing through molten aluminum can be carried out simultaneously and continuously.
以下、実施例に基づき、本発明の内容を更に詳
しく説明する。 Hereinafter, the content of the present invention will be explained in more detail based on Examples.
先ず、窒化処理チタン・ワイヤを次の様にして
作製した。 First, a nitrided titanium wire was produced as follows.
均熱温度範囲約200cmの電気炉に窒素ガスを流
し、炉温1300℃、送り速度約500cm／分でチタ
ン・ワイヤを送り、連続窒化処理を行つた。使用
したチタン・ワイヤ値径は0.3mmφである。 Nitrogen gas was flowed through an electric furnace with a soaking temperature range of approximately 200 cm, and the titanium wire was fed at a furnace temperature of 1300°C and a feed speed of approximately 500 cm/min to perform continuous nitriding treatment. The diameter of the titanium wire used was 0.3 mmφ.
次に、この窒化処理したチタン・ワイヤを、
Arガス雰囲気中1100℃で溶融したアルミニウム
中を、送り速度約900cm／分で１回通過させ、連
続合金化処理を行つた。 Next, this nitrided titanium wire is
Continuous alloying treatment was performed by passing through aluminum melted at 1100° C. in an Ar gas atmosphere once at a feed rate of approximately 900 cm/min.
このようにして得られた、アルミニウム−チタ
ン合金ワイヤの径方向断面の電子顕微鏡写真を第
１図（倍率；300倍）に示す。ワイヤの表面から
約10μｍにわたつて均一な組成、厚みのアルミニ
ウム−チタンの合金層が形成されている。この均
一な合金組成はXMA分析の結果、TiAl3相
（75at％Al）であることがわかつた。 An electron micrograph of a radial cross section of the aluminum-titanium alloy wire thus obtained is shown in FIG. 1 (magnification: 300x). An aluminum-titanium alloy layer having a uniform composition and thickness is formed over a distance of approximately 10 μm from the surface of the wire. As a result of XMA analysis, this uniform alloy composition was found to be TiAl three- phase (75 at% Al).
一方、比較のために、純チタン・ワイヤを同じ
Arガス雰囲気中で、溶融アルミニウム中を通過
させて得られるアルミニウム−チタン合金ワイヤ
の場合の例を示す。 Meanwhile, for comparison, pure titanium wire was
An example of an aluminum-titanium alloy wire obtained by passing it through molten aluminum in an Ar gas atmosphere will be shown.
合金化処理条件は次のようなものである。 The alloying treatment conditions are as follows.
詳細な説明で説明したように、1000℃以上の温
度では、ワイヤが断線し易いので、先ず850℃で
溶融アルミニウム中をワイヤ送り速度80cm／分で
２回（１往復）通過させた後、950℃で更に４回
（２往復）通過させる。この方法で得られたアル
ミニウム−チタン合金ワイヤの径方向断面の電子
顕微鏡写真を第２図（倍率；300倍）に示す。こ
の場合もやはり表面から約10〜15μｍにわたりア
ルミニウム−チタン合金層を形成してはいるが、
合金層厚みにムラがある上、更にXMA分析の結
果、この合金層はTiAl3相（75at％Al）と純Alと
の混合相であり、均一な合金層にはなつていなか
つた。合金層部分の拡大写真を第３図（倍率；
3000倍）に示す。写真中、拡散、合金層の中の明
るい部分（粒子）がTiAl3相であり、暗く見える
部分が純Al相である。 As explained in the detailed explanation, the wire tends to break at temperatures above 1000℃, so first the wire is passed through molten aluminum at 850℃ twice (one round trip) at a feed rate of 80cm/min, then Pass 4 more times (2 round trips) at ℃. An electron micrograph of a radial cross section of the aluminum-titanium alloy wire obtained by this method is shown in FIG. 2 (magnification: 300 times). In this case as well, an aluminum-titanium alloy layer is formed approximately 10 to 15 μm from the surface, but
In addition to the uneven thickness of the alloy layer, XMA analysis revealed that the alloy layer was a mixed phase of TiAl 3- phase (75 at% Al) and pure Al, and was not a uniform alloy layer. Figure 3 shows an enlarged photograph of the alloy layer (magnification;
3000x). In the photograph, the bright parts (particles) in the diffusion and alloy layers are the TiAl 3 phase, and the dark parts are the pure Al phase.
窒化処理したチタン・ワイヤを使用した場合と
純チタン・ワイヤを使用した場合とで合金化処理
能力を比較してみると、窒化処理チタン・ワイヤ
の方が純チタン・ワイヤに比べて、溶融アルミニ
ウム中のワイヤ送り速度で約11倍、通過回数が1/
６と少いことで６倍、すなわち60〜70倍も処理能
力が大きいことがわかる。 Comparing the alloying performance of nitrided titanium wire and pure titanium wire, nitrided titanium wire has a higher alloying capacity than pure titanium wire. Approximately 11 times faster at medium wire feed speed, and 1/times the number of passes
It can be seen that the small number of 6 means that the processing capacity is 6 times greater, that is, 60 to 70 times greater.
以上、説明したように、本発明によれば、窒化
処理したチタン・ワイヤを使用することにより、
溶融アルミニウム中を通過させて表面部にアルミ
ニウム−チタン合金層を形成させるアルミニウム
−チタン合金ワイヤの製造方法の生産能力が、純
チタン・ワイヤを使用する場合に比べて50〜100
倍となつて量産性が著しく向上する。また、ワイ
ヤ表面部に形成されるアルミニウム−チタン合金
層の組成および厚みの均一性も更に一段と優れた
ものが得られる。従つて本発明のアルミニウム−
チタン合金ワイヤの製造方法は極めて優れたもの
であり、その有用性の大きいことは明らかであ
る。 As explained above, according to the present invention, by using nitrided titanium wire,
The production capacity of the method for manufacturing aluminum-titanium alloy wire, which passes through molten aluminum to form an aluminum-titanium alloy layer on the surface, is 50 to 100 times faster than when using pure titanium wire.
This will significantly improve mass productivity. Furthermore, the uniformity of the composition and thickness of the aluminum-titanium alloy layer formed on the surface of the wire can be further improved. Therefore, the aluminum of the present invention
It is clear that the method for producing titanium alloy wire is extremely superior and has great utility.
第１図；窒化処理したチタン・ワイヤを溶融ア
ルミニウム中を１回通過させて得られたワイヤの
径方向断面の電子顕微鏡写真。第２図；純チタ
ン・ワイヤを溶融アルミニウム中を６回（３往
復）通過させて得られたワイヤの径方向断面の電
子顕微鏡写真。第３図；第２図のワイヤ断面にお
ける合金層部分を拡大した電子顕微鏡写真。
FIG. 1: Electron micrograph of a radial cross section of a nitrided titanium wire obtained by passing it once through molten aluminum. FIG. 2: Electron micrograph of a radial cross section of a pure titanium wire obtained by passing it through molten aluminum six times (three reciprocations). FIG. 3: An enlarged electron micrograph of the alloy layer in the wire cross section of FIG. 2.
Claims (1)
中もしくは窒素ガス中において溶融アルミニウム
中を通過させ、ワイヤ表面をアルミニウム−チタ
ン合金層とするアルミニウム−チタン合金ワイヤ
の製造方法において、前記チタン・ワイヤとして
窒化処理をしたチタン・ワイヤを用いることを特
徴とするアルミニウム−チタン合金ワイヤの製造
方法。1. A method for producing an aluminum-titanium alloy wire in which a titanium wire is passed through molten aluminum in a vacuum, an inert gas, or a nitrogen gas to form an aluminum-titanium alloy layer on the wire surface, wherein the titanium wire is nitrided. A method for producing an aluminum-titanium alloy wire, the method comprising using a treated titanium wire.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP57111101A JPS591670A (en) | 1982-06-28 | 1982-06-28 | Manufacture of aluminum-titanium alloy wire |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP57111101A JPS591670A (en) | 1982-06-28 | 1982-06-28 | Manufacture of aluminum-titanium alloy wire |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS591670A JPS591670A (en) | 1984-01-07 |
| JPH0435554B2 true JPH0435554B2 (en) | 1992-06-11 |
Family
ID=14552413
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP57111101A Granted JPS591670A (en) | 1982-06-28 | 1982-06-28 | Manufacture of aluminum-titanium alloy wire |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS591670A (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP4157522B2 (en) | 2004-12-28 | 2008-10-01 | サクラテック株式会社 | High corrosion resistance / high workability plated steel wire, plating bath composition, high corrosion resistance / high workability plated steel wire manufacturing method, and wire mesh product |
-
1982
- 1982-06-28 JP JP57111101A patent/JPS591670A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPS591670A (en) | 1984-01-07 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US7067197B2 (en) | Powder metallurgy sputtering targets and methods of producing same | |
| CN1328409C (en) | High purity niobium and products containing the same, and methods of making the same | |
| US10100438B2 (en) | Metallic crucibles and methods of forming the same | |
| JPH07103468B2 (en) | Coated cemented carbide and method for producing the same | |
| JPH03135041A (en) | Manufacture of bonding fine wire for semiconductor use | |
| JPH03150356A (en) | Tungsten or molybdenum target and production thereof | |
| JP2509799B2 (en) | Silver-metal oxide material used for electrical contacts | |
| CN114986022A (en) | Manufacturing method of flux-cored wire suitable for steel structure | |
| JPH0435554B2 (en) | ||
| US4808225A (en) | Method for producing an alloy product of improved ductility from metal powder | |
| US20050194075A1 (en) | Method of hardening a beta titanium member | |
| US20070234542A1 (en) | Method for Producing Metallic Flat Wires or Strips with a Cube Texture | |
| Powell et al. | The deposition of tantalum and columbium from their volatilized halides | |
| JPH0421756A (en) | Production of tial intermetallic compound layer | |
| JPH0813055A (en) | Method for hardening surface of ti-al intermetallic compound and product produced by the method | |
| JP2000198027A (en) | Electrode wire for electric discharge machining and manufacture of it | |
| JPH0660324B2 (en) | Method for manufacturing Ni-Ti based shape memory alloy sintered body | |
| JPS60145338A (en) | Manufacture of alloy having concentration gradient in composition | |
| JP2742117B2 (en) | Method of manufacturing copper-coated steel trolley wire | |
| JPH01180909A (en) | Manufacturing method of corrosion-resistant zinc alloy coated steel wire | |
| JP2001164303A (en) | Sintered material and manufacturing method thereof | |
| JPH05125479A (en) | Production of high-carbon steel products | |
| JP2002352649A (en) | Method for producing MgB2 superconducting wire | |
| JPS58122102A (en) | Production of wire or bar material | |
| JPS62162424A (en) | Electric discharge electrode wire and manufacture thereof |