JPH0435538B2 - - Google Patents
Info
- Publication number
- JPH0435538B2 JPH0435538B2 JP57118910A JP11891082A JPH0435538B2 JP H0435538 B2 JPH0435538 B2 JP H0435538B2 JP 57118910 A JP57118910 A JP 57118910A JP 11891082 A JP11891082 A JP 11891082A JP H0435538 B2 JPH0435538 B2 JP H0435538B2
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- aging precipitation
- heat treatment
- precipitation
- less
- 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 - Lifetime
Links
- 238000001556 precipitation Methods 0.000 claims description 29
- 238000000034 method Methods 0.000 claims description 28
- 229910045601 alloy Inorganic materials 0.000 claims description 25
- 239000000956 alloy Substances 0.000 claims description 25
- 230000032683 aging Effects 0.000 claims description 19
- 238000010438 heat treatment Methods 0.000 claims description 19
- 238000004519 manufacturing process Methods 0.000 claims description 15
- 238000007712 rapid solidification Methods 0.000 claims description 12
- 239000004020 conductor Substances 0.000 claims description 11
- 238000001816 cooling Methods 0.000 claims description 6
- 230000001747 exhibiting effect Effects 0.000 claims description 5
- 230000002431 foraging effect Effects 0.000 claims description 4
- 238000005482 strain hardening Methods 0.000 claims description 4
- 238000004804 winding Methods 0.000 claims description 4
- 229910052802 copper Inorganic materials 0.000 claims description 3
- 239000010949 copper Substances 0.000 claims description 3
- 210000003298 dental enamel Anatomy 0.000 claims description 3
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 2
- 229910052726 zirconium Inorganic materials 0.000 claims description 2
- 229910052751 metal Inorganic materials 0.000 description 13
- 239000002184 metal Substances 0.000 description 13
- 239000006104 solid solution Substances 0.000 description 9
- 239000000243 solution Substances 0.000 description 5
- 238000007796 conventional method Methods 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 238000011282 treatment Methods 0.000 description 4
- 239000012530 fluid Substances 0.000 description 3
- 239000007788 liquid Substances 0.000 description 3
- 229910000599 Cr alloy Inorganic materials 0.000 description 2
- 229910000640 Fe alloy Inorganic materials 0.000 description 2
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 2
- 229910001093 Zr alloy Inorganic materials 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 239000012467 final product Substances 0.000 description 2
- 229910000881 Cu alloy Inorganic materials 0.000 description 1
- 229910017813 Cu—Cr Inorganic materials 0.000 description 1
- 229910017985 Cu—Zr Inorganic materials 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000001192 hot extrusion Methods 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 229910052749 magnesium Inorganic materials 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- 229910052709 silver Inorganic materials 0.000 description 1
- 238000005507 spraying Methods 0.000 description 1
- 239000010936 titanium Substances 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 238000005491 wire drawing Methods 0.000 description 1
- 229910052725 zinc Inorganic materials 0.000 description 1
Landscapes
- Heat Treatment Of Nonferrous Metals Or Alloys (AREA)
Description
（技術分野）
本発明は、機械、器具等の導体、部品などとし
て使用される時効析出型合金線状体の製造方法に
関するものである。
（背景技術）
近年、機器の小型化、軽量化の要求が高まり、
例えば配線用導体、巻線用導体等にも細線化の要
求が大である。又細線化に伴なつて逆に高強度材
料の要求も強まつている。又耐軟化性もしばしば
要求される。
従来高導電性、高強度、高延性、耐軟化性と言
つた上述の要求に応ずるには、Cu−Cr、Cu−Zr
合金などのいわゆる時効析出型合金がしばしば使
用されて来た。
しかし、これらの時効析出型合金は必ずしも純
金属より加工性が良いわけではなく、細線に仕上
げるためには、多数工程の加工および処理を施さ
ねばならない。
例えば時効析出型合金の厚さ0.2mmの条材を製
造しようとする場合、従来の一般的な工業的製造
工程は第３図イに示すように、インゴツトに溶
解、鋳造後、熱間圧延や熱間押出しにより熱間加
工した後、過飽和固溶体とするための溶体化熱処
理を行ない、しかる後多くの場合皮剥などの表面
酸化物の除去等を行なつた後、冷間加工し、高々
減面率90％以下の圧下毎に、中間焼鈍処理して最
終所望サイズに加工した後、最終時効析出熱処理
すると言つた多数の工程を経るのが一般的であつ
た。第３図イ，ロにおいて（ ）内は必要により
適宜実施する工程を示す。
このような方法では、多くの工程を要し、特に
多大の熱エネルギーと時間を消費する溶体化熱処
理、中間熱処理が必要であり、又冷間加工性が必
ずしも良好でないため、加工、熱処理コストの増
大により高価格となると共に、工程が多いとロス
発生率も増加する欠点があつた。
（発明の開示）
本発明は、上述の問題点を解決するため成され
たもので、時効析出挙動を呈する合金を溶湯より
直ちに線状体に急冷凝固させることにより、溶湯
から直接細線を製造し、特に面倒な溶体化処理が
不要で、工程を極度に簡素化して、設備費、製造
コストを低減すると共に、耐軟化性の良好な時効
析出型合金を製造する方法を提供せんとするもの
である。
本発明は、時効析出挙動を呈する合金を、溶融
状態から直接厚さ１mm以下又は直径１mm以下の線
状体に急冷凝固させた後、時効析出のための熱処
理を施すことを特徴とする時効析出型合金の製造
方法である。
本発明において、時効析出挙動を呈する合金と
は、銅、アルミニウム、ニツケル、チタン等の合
金で、時効析出により硬化する合金であり、例え
ばCuと、Cr、Zr、Be、Fe、Co等との合金、Al
と、Cu、Mg、Zn、Si、Fe、Zr、Ag等との合金
などである。
第３図ロは本発明方法の実施例の工程を示す図
である。本発明法では、時効析出挙動を呈する合
金を、先ず溶解し、溶融状態から直接厚さ１mm以
下又は直径１mm以下の線状体に急冷凝固する方法
（直接製線法と称す）により線状体を作成する。
この急冷凝固は、冷却速度102deg.sec.-1以上で行
なわれることが望ましい。
この急冷凝固法には種々の方法が適用され、例
えば第１図、第２図に示す方法がある。第１図に
示す方法は、溶湯の容器２の底部のノズル３より
双ロール４，４間に溶湯１を定常的に流し込むこ
とにより、ロール４，４により急冷凝固させ、ロ
ール間隔により所望厚さの条体５を得る方法であ
る。又第２図に示すものは、溶湯の容器２の底部
のノズル３より溶湯１を定常的に噴出させ、回転
体７の液流体６中に注入して急冷凝固させる方法
である。この場合、液流体６は回転体７の回転に
より遠心力で保持され、線状体８は回転体７の壁
に沿つて巻かれる。
本発明に用いられる急冷凝固法は第１図、第２
図に示す方法に限定されるものではなく、その他
の方法、例えば１個の回転ロール面に溶湯の噴流
を吹き付ける方法、層流状態の冷水中に溶湯１を
連続的に注入する方法などでも良い。
この急冷凝固により、高温での固溶元素の固溶
状態がそのまま室温まで持ち来たされ、過飽和固
溶体となるので、従来のような溶体化処理の必要
がない。
次に、急冷凝固により得られた線状体は、第３
図ロに示すように、最終的に時効析出のための熱
処理を施すか、又は必要により減面率95％以下の
冷間加工を施して最終サイズに加工した後、時効
析出熱処理を施して製品とする。又必要により時
効析出熱処理後冷間加工を加えても良い。
このような本発明方法によると、従来のイ図の
ような多くの工程を必要とせず、２〜３工程です
み、しかも簡単な設備を設けるだけで良いので、
エネルギー、工数が極度に低減される。
実施例 １
第１図に示す急冷凝固装置により、Cu−0.6％
Cr合金、Cu−0.15％Zr合金、Cu−２％Fe合金、
2011Al合金およびAl−１％Fe合金の溶湯から、
冷却速度大略103deg.sec.-1で厚さ0.5mmの条を作
成した。この状態でそれぞれの合金は過飽和に合
金元素を固溶した過飽和固溶体になつていた。こ
れをそれぞれの合金に適切な温度条件で時効析出
熱処理を施した所、導電率も回復し、析出硬化
し、引張強さが増加した。
実施例 ２
第２図に示す急冷凝固装置により、Cu−0.6％
Cr合金の溶湯より、冷却速度大略２×103deg.
sec.-1で直径0.2mmの丸線を作成した。これを0.1
mmに伸線した後、450℃にて２時間時効析出熱
処理したところ、表１に示す特性を得た。
(Technical Field) The present invention relates to a method for manufacturing an aging precipitation type alloy linear body used as a conductor, a component, etc. for machines, appliances, etc. (Background technology) In recent years, the demand for smaller and lighter equipment has increased.
For example, there is a strong demand for thinner wires for wiring conductors, winding conductors, and the like. Moreover, as wires become thinner, the demand for high-strength materials is also increasing. Softening resistance is also often required. Conventionally, in order to meet the above requirements such as high conductivity, high strength, high ductility, and softening resistance, Cu-Cr, Cu-Zr
So-called age-precipitated alloys such as alloys have often been used. However, these aged precipitation type alloys do not necessarily have better workability than pure metals, and in order to finish them into fine wires, they must be processed and processed in multiple steps. For example, when trying to manufacture a 0.2 mm thick strip of aged precipitation alloy, the conventional general industrial manufacturing process involves melting and casting into an ingot, followed by hot rolling or other processes, as shown in Figure 3A. After hot processing by hot extrusion, solution heat treatment is performed to form a supersaturated solid solution, and then, in many cases, after removal of surface oxides such as peeling, cold processing is performed to reduce the area at most. It was common to go through a number of steps, such as an intermediate annealing treatment for each reduction of 90% or less, processing to the final desired size, and a final aging precipitation heat treatment. In Figures 3A and 3B, the numbers in parentheses indicate steps to be carried out as necessary. This method requires many steps, especially solution heat treatment and intermediate heat treatment that consume a large amount of thermal energy and time, and cold workability is not necessarily good, so processing and heat treatment costs are reduced. This increase leads to high costs, and the large number of steps increases the rate of loss. (Disclosure of the Invention) The present invention has been made to solve the above-mentioned problems, and it is possible to produce fine wire directly from the molten metal by rapidly solidifying an alloy exhibiting aging precipitation behavior into a linear body immediately from the molten metal. The purpose of the present invention is to provide a method for producing an age-precipitated alloy that does not require particularly troublesome solution treatment, greatly simplifies the process, reduces equipment costs and manufacturing costs, and has good softening resistance. be. The present invention is characterized in that an alloy exhibiting aging precipitation behavior is directly rapidly solidified from a molten state into a linear body with a thickness of 1 mm or less or a diameter of 1 mm or less, and then subjected to heat treatment for aging precipitation. This is a method for manufacturing a mold alloy. In the present invention, alloys exhibiting aging precipitation behavior are alloys of copper, aluminum, nickel, titanium, etc., which harden through aging precipitation. Alloy, Al
and alloys with Cu, Mg, Zn, Si, Fe, Zr, Ag, etc. FIG. 3B is a diagram showing the steps of an embodiment of the method of the present invention. In the method of the present invention, an alloy exhibiting aging precipitation behavior is first melted, and then the wire is formed into a wire by directly rapidly solidifying it from the molten state into a wire with a thickness of 1 mm or less or a diameter of 1 mm or less (referred to as the direct wire manufacturing method). Create.
This rapid solidification is preferably performed at a cooling rate of 10 2 deg.sec. -1 or higher. Various methods can be applied to this rapid solidification method, including the methods shown in FIGS. 1 and 2, for example. In the method shown in FIG. 1, the molten metal 1 is steadily poured between twin rolls 4, 4 from a nozzle 3 at the bottom of a molten metal container 2, and the molten metal is rapidly solidified by the rolls 4, 4. This is the method of obtaining the strips 5. The method shown in FIG. 2 is a method in which molten metal 1 is constantly jetted out from a nozzle 3 at the bottom of a molten metal container 2, and is injected into a liquid fluid 6 of a rotating body 7 to rapidly solidify it. In this case, the liquid fluid 6 is held by centrifugal force due to the rotation of the rotating body 7, and the linear body 8 is wound along the wall of the rotating body 7. The rapid solidification method used in the present invention is shown in Figures 1 and 2.
The method is not limited to the one shown in the figure, and other methods may also be used, such as a method of spraying a jet of molten metal onto the surface of one rotating roll, or a method of continuously pouring molten metal 1 into cold water in a laminar flow state. . Due to this rapid solidification, the solid solution state of the solid solution element at high temperature is brought directly to room temperature and becomes a supersaturated solid solution, so there is no need for solution treatment as in the conventional method. Next, the linear body obtained by rapid solidification is
As shown in Figure B, the final product is either subjected to heat treatment for aging precipitation or, if necessary, subjected to cold working with an area reduction rate of 95% or less to reach the final size, and then subjected to aging precipitation heat treatment. shall be. Further, if necessary, cold working may be added after the aging precipitation heat treatment. According to the method of the present invention, there is no need for many steps as in the conventional method shown in Fig. 1, and only 2 to 3 steps are required, and simple equipment is required.
Energy and man-hours are extremely reduced. Example 1 Cu-0.6% was
Cr alloy, Cu-0.15% Zr alloy, Cu-2% Fe alloy,
From molten metal of 2011Al alloy and Al-1%Fe alloy,
A strip with a thickness of 0.5 mm was created at a cooling rate of approximately 10 3 deg.sec. -1 . In this state, each alloy had become a supersaturated solid solution containing supersaturated alloying elements. When this alloy was subjected to aging precipitation heat treatment under appropriate temperature conditions, the electrical conductivity was restored, precipitation hardened, and the tensile strength increased. Example 2 Cu-0.6% was produced using the rapid solidification apparatus shown in Fig.
The cooling rate for molten Cr alloy is approximately 2×10 3 deg.
A round wire with a diameter of 0.2 mm was created at sec. -1 . This is 0.1
After drawing the wire to a diameter of mm, the wire was subjected to aging precipitation heat treatment at 450°C for 2 hours, and the properties shown in Table 1 were obtained.
【表】
実施例 ３
第２図に示す急冷凝固装置により、Cu−0.15％
Zr合金の溶湯より、冷却速度大略５×103deg.
sec.-1で直径0.1mmの丸線を作成した。これを0.02
mmに伸線した後、温度650℃のトンネル軟化炉
中を連続的に走行させて時効析出させ、直ちにエ
ナメル焼付装置を通過させてエナメル塗布、焼付
したところ、導体外径0.02mm巻線を得た。得られ
た巻線の導体は導電率90.2％IACSで、しかも引
張強さが42Kg／mm2で、従来の軟銅導体の約２倍の
強度を有し、高速のコイリング作業時の断線も従
来に比べ非常に少なかつた。
（発明の効果）
上述のように構成された本発明の時効析出型合
金の製造方法は次のような効果がある。
(イ) 時効析出挙動を呈する合金を、溶融状態から
直接厚さ１mm以下又は直径１mm以下の線状体に
急冷凝固させるため、溶湯から僅か一工程で細
線が製造でき、しかも急冷凝固により高温での
固溶元素の固溶状態がそのまま室温に持ち来た
され、過飽和固溶体となつているので、従来の
ような面倒な溶体化処理が必要でなく、工程が
著しく簡素化されるので、設備費、製造コスト
が著しく低減される。
(ロ) 急冷凝固された細い線状体は、必要により若
干の冷間加工を施され、最終サイズに仕上げら
れるのみであるので、細線でも伸線工数が大幅
に削減される。
(ハ) 熱処理は時効析出のための熱処理だけであ
り、従来法では高加工に耐えられない場合も多
く、その場合、特に条材では繰返し中間熱処理
を必要としたが、これが一切不要となるため、
省エネルギーの効果が大きい。
(ニ) 急冷凝固により過飽和固溶体となり、中間熱
処理を行なう場合は最終製品の耐軟化性を損な
う場合があるが、本発明方法では上述のように
熱処理が少ないので、耐軟化性も良好なものが
得られる。
(ホ) 急冷により、過飽和状態で結晶粒の微細なも
のが得られ、それを時効析出熱処理するので、
高機械的特性のものが得られる。
従つて本発明方法は、強度、導電性、耐軟化
性に優れた細い線状体を容易に安価に製造し
得、特に電気、電子機器内配線用導体（例、オ
ーデイオ機器、コンピユータ等用）、電子機器
用巻線導体、自動車配線用導体などに適用して
多大の効果を有するものである。[Table] Example 3 Cu-0.15% was produced using the rapid solidification equipment shown in Figure 2.
The cooling rate of molten Zr alloy is approximately 5×10 3 deg.
A round wire with a diameter of 0.1 mm was created at sec. -1 . This is 0.02
After drawing the wire to a diameter of 1.5 mm, the wire was continuously passed through a tunnel softening furnace at a temperature of 650°C to cause aging precipitation, and then immediately passed through an enamel baking device to be coated with enamel and baked. As a result, a winding wire with a conductor outer diameter of 0.02 mm was obtained. Ta. The resulting winding conductor has a conductivity of 90.2% IACS and a tensile strength of 42 kg/ mm2 , which is approximately twice the strength of conventional annealed copper conductors, and it is less susceptible to wire breakage during high-speed coiling than conventional conductors. There were very few in comparison. (Effects of the Invention) The method for producing an aged precipitation alloy of the present invention configured as described above has the following effects. (b) Since the alloy that exhibits aging precipitation behavior is rapidly solidified directly from the molten state into a linear body with a thickness of 1 mm or less or a diameter of 1 mm or less, thin wires can be produced from the molten metal in just one step, and at high temperatures due to rapid solidification. Since the solid solution state of the solid solution elements is brought directly to room temperature and becomes a supersaturated solid solution, there is no need for the troublesome solution treatment as in the past, and the process is significantly simplified, reducing equipment costs. , manufacturing costs are significantly reduced. (b) The rapidly solidified thin wire body is only subjected to some cold working if necessary and finished to the final size, so the number of wire drawing steps can be significantly reduced even for thin wires. (c) Heat treatment is only for aging precipitation, and in many cases conventional methods cannot withstand high processing.In such cases, repeated intermediate heat treatments were required, especially for strips, but this is no longer necessary. ,
Great energy saving effect. (d) It becomes a supersaturated solid solution by rapid solidification, and if an intermediate heat treatment is performed, the softening resistance of the final product may be impaired, but as the method of the present invention requires less heat treatment as described above, products with good softening resistance can be obtained. can get. (e) By rapid cooling, fine crystal grains are obtained in a supersaturated state, which is then subjected to aging precipitation heat treatment.
High mechanical properties can be obtained. Therefore, the method of the present invention can easily and inexpensively produce thin linear bodies with excellent strength, conductivity, and softening resistance, and is particularly suitable for use as conductors for wiring in electrical and electronic equipment (e.g., for audio equipment, computers, etc.). It has great effects when applied to wire-wound conductors for electronic devices, conductors for automobile wiring, and the like.
第１図および第２図はそれぞれ本発明方法の実
施例に用いられる急冷凝固方法の例を説明するた
めの断面図である。第３図イ，ロは製造方法の工
程を示す図で、イ図は従来法の例、ロ図は本発明
方法の実施例を示すものである。
１……溶湯、２……容器、３……ノズル、４…
…ロール、５……条体、６……液流体、７……回
転体、８……線状体。
FIGS. 1 and 2 are cross-sectional views for explaining an example of a rapid solidification method used in an embodiment of the method of the present invention, respectively. Figures 3A and 3B are diagrams showing the steps of the manufacturing method, where Figure A shows an example of the conventional method and Figure 3 shows an example of the method of the present invention. 1... Molten metal, 2... Container, 3... Nozzle, 4...
...roll, 5...stripe body, 6...liquid fluid, 7...rotating body, 8...linear body.
Claims (1)
直接厚さ１mm以下又は直径１mm以下の線状体に急
冷凝固させた後、時効析出のための熱処理を施す
ことを特徴とする時効析出型合金の製造方法。 ２ 急冷凝固が、冷却速度102deg.sec.-1以上で行
なわれる特許請求の範囲第１項記載の時効析出型
合金の製造方法。 ３ 急冷凝固後熱処理の前に、減面率95％以下の
冷間加工を施す特許請求の範囲第１項又は第２項
記載の時効析出型合金の製造方法。 ４ 時効析出型合金が、Cr又はZrを0.03〜１％含
有し、残部が本質的に銅より成る特許請求の範囲
第１項又、第２項又は第３項記載の時効析出型合
金の製造方法。 ５ 時効析出型合金が、巻線用導体であり、熱処
理後エナメル塗付、焼付けを施す特許請求の範囲
第１項、第２項、第３項又は第４項記載の時効析
出型合金の製造方法。[Claims] 1. An alloy exhibiting aging precipitation behavior is directly rapidly solidified from a molten state into a linear body with a thickness of 1 mm or less or a diameter of 1 mm or less, and then subjected to heat treatment for aging precipitation. A method for producing an aged precipitation alloy. 2. The method for producing an aged precipitation alloy according to claim 1, wherein the rapid solidification is performed at a cooling rate of 10 2 deg.sec. -1 or more. 3. The method for producing an age-precipitated alloy according to claim 1 or 2, wherein cold working with an area reduction rate of 95% or less is performed before the heat treatment after rapid solidification. 4. Manufacture of an aging precipitation alloy according to claim 1, 2 or 3, wherein the aging precipitation alloy contains 0.03 to 1% of Cr or Zr, and the remainder is essentially copper. Method. 5. Manufacture of an aging precipitation alloy according to claim 1, 2, 3, or 4, wherein the aging precipitation alloy is a conductor for winding, and is coated with enamel and baked after heat treatment. Method.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP11891082A JPS599137A (en) | 1982-07-07 | 1982-07-07 | Manufacturing method of aged precipitation alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP11891082A JPS599137A (en) | 1982-07-07 | 1982-07-07 | Manufacturing method of aged precipitation alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS599137A JPS599137A (en) | 1984-01-18 |
| JPH0435538B2 true JPH0435538B2 (en) | 1992-06-11 |
Family
ID=14748190
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP11891082A Granted JPS599137A (en) | 1982-07-07 | 1982-07-07 | Manufacturing method of aged precipitation alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS599137A (en) |
Families Citing this family (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH081528Y2 (en) * | 1991-01-24 | 1996-01-17 | タツタ電線株式会社 | Cable for painting robot |
| JPH04266827A (en) * | 1991-02-20 | 1992-09-22 | Sanyo Chem Ind Ltd | Antimicrobial agent |
| JPH04133316U (en) * | 1991-05-29 | 1992-12-11 | タツタ電線株式会社 | Composite cable for mobile equipment |
| JPH0520208U (en) * | 1991-06-27 | 1993-03-12 | タツタ電線株式会社 | Flex resistance instrumentation cable |
| JPH0547232A (en) * | 1991-08-12 | 1993-02-26 | Tatsuta Electric Wire & Cable Co Ltd | Heat-resistant / flexible / wear-resistant insulated wire |
| JPH081530Y2 (en) * | 1991-09-05 | 1996-01-17 | タツタ電線株式会社 | Heat-resistant / flexible / wear-resistant coating robot cables |
| JPH081531Y2 (en) * | 1991-09-09 | 1996-01-17 | タツタ電線株式会社 | Heat-resistant / flexible / wear-resistant coating robot cables |
| JPH0523337U (en) * | 1991-09-09 | 1993-03-26 | タツタ電線株式会社 | Heat-resistant / flexible / wear-resistant coated robot cable |
-
1982
- 1982-07-07 JP JP11891082A patent/JPS599137A/en active Granted
Non-Patent Citations (1)
| Title |
|---|
| METALLURGICAL TRANSACTIONS A=1982 * |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS599137A (en) | 1984-01-18 |
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