JPS6083752A - Production of functional alloy member - Google Patents

Abstract

PURPOSE:To produce simply and easily a TiNi functional alloy member by drawing out the melt of an alloy which consists principally of specifically composed Ni and Ti and causes thermoelastic type martensite transformation while solidifying said metal near the outlet of a capillary. CONSTITUTION:The melt 1 of an alloy which causes thermoelastic type martensite transformation and consists of 50-60wt% Ni and the balance Ti or is substd. of a part of said Ni or Ti with >=1 kind among Cu, Al, V, Zr, Mo, Cr, Fe, Co and rare earth element is contained into a vessel 2 consisting of a refractory material which does not react with said melt. The melt is heated and held by a heater 3. A pressure 5 is exerted to the vessel 2 from one end thereof to force the melt 2 to the outlet from the inside of a capillary 4 formed at the other end. The melt is solidified at the solidification boundary 7 near the outlet and is drawn out into a vacuum atmosphere. A TiNi functional alloy member 6 having an optional shape such as a pipe, long-sized material, etc. regulated by the shape of the drawing outlet is continuously obtd.

Description

DETAILED DESCRIPTION OF THE INVENTION Field of the Invention This invention relates to a method of manufacturing a T1Ni functional alloy member.

Description of the Prior Art DINi alloys with shape memory effects (including associated superelastic effects and anti-vibration effects) are generally hard and have excellent wear resistance, so they cannot be subjected to machining such as cutting. That is difficult. Therefore, it is difficult to fabricate pipe-shaped or other complicated-shaped members. Furthermore, when this T1Ni alloy is machined, it tends to become brittle due to the heat generated during processing. Therefore, when a TI Nl alloy is subjected to mechanical processing such as cutting or drilling, there is a problem in that the processed surface is likely to crack.

Furthermore, if a linear or plate-shaped member is obtained instead of the pipe shape or other complicated shapes as described above, machining may not be particularly necessary. However, in general, in order to obtain a member of a specific shape made of TINI alloy, melting, homogenizing annealing, hot rolling, cold rolling, and intermediate softening (this intermediate softening process and cold rolling process are repeated many times) are required. ), and on top of that, it is necessary to process the wire or plate-shaped member by 1q.

In this way, even if machining such as cutting is performed afterwards, a large number of processes are required up to the stage where this machining is performed, so manufacturing takes time and costs are inevitably high. Become something.

OBJECTS OF THE INVENTION Therefore, it is an object of the present invention to provide various shapes of TiN1
It is an object of the present invention to provide a method for easily manufacturing a functional alloy member using a significantly reduced number of steps.

Summary of the Invention In the method for manufacturing a functional alloy member of the present invention, 150 to 60% by weight of N, which undergoes thermoelastic martensitic transformation, and the balance T1.
or a part of N1 or Ti is C'
+ A', V, Z r, MO.

A molten alloy made of an alloy substituted with one or more elements selected from the group consisting of Cr, l"e, Qo, and rare earth elements is heated under pressure from the inside of a capillary made of a refractory material that does not react with the alloy toward the outlet. It is characterized in that it is allowed to reach a temperature of 50% and is solidified near the exit of the capillary while being pulled out from the capillary.This will be explained in more detail with reference to FIG.

The molten metal 1 of the Tzyt alloy is stored in a container 2 made of a refractory material that does not react with the molten metal 1, and is heated to a heater 3.
placed under heat. A capillary 4 is formed at one end of the container 2, and a pressure 5 is applied to the other end of the container 2. This pressure 5 causes [11 to move towards the exit of the capillary 4. And near this exit,
The molten metal 1 is drawn out from the capillary 4 while being solidified, and a desired functional alloy member 6 is obtained. In addition, in FIG. 1, the solidification interface is indicated by the reference numeral 7.

As is clear from the above description, according to the present invention,
Since the final shape (or a shape close to the RI shape) can be obtained directly from the molten metal, the number of steps can be significantly reduced compared to when machining is involved. Therefore, the yield is also improved.

In addition, by changing the shape of the capillary, the cross-sectional shape of the desired member can be easily changed. Even long bodies can be manufactured efficiently.

Further, according to the present invention, if necessary, it is easy to obtain a single-crystal functional alloy member. In general, it is known that for copper-based functional alloys, if they are made into single crystals, it is possible to improve fatigue resistance and increase the amount of shape recovery deformation. The method for obtaining single crystals in this way is as follows:
There are zone melting methods (zone melting method) and the Bridgman method, but with the zone melting method it is impossible to manufacture parts with irregular cross sections. Manufacturer cannot be inferior. However, even in a polycrystalline state, the 1-iNi alloy has excellent fatigue resistance and a large amount of shape recovery deformation, so there is no advantage in intentionally turning it into a single crystal.

Therefore, if there is no need for single crystallization in this way,
The temperature of the solidification part (solidification interface, solid-liquid interface) mentioned above! +J
There is no need to be strict about control.

In addition, in the case of the one-shot body shown in the first factor mentioned above, the drawing direction of the molten metal 1 is upward, and a pressure 5 is applied separately to draw out the molten metal 1.
Although this was carried out in a state where a slight force was applied to the melt 1, the melt 1 may be pulled down while the drawing direction is set downward and the weight of the melt and the surface tension are balanced. Note that this will be made clear with reference to FIG. 3 in the explanation to be described later.

Also, in preferred embodiments, the withdrawal of the molten metal is performed in a non-oxidizing or reducing atmosphere. However, since it does not contain a metal with a high vapor pressure like 7-n, there is no need to use an expensive gas atmosphere, and a simple vacuum atmosphere is sufficient.

In the present invention, the alloy that undergoes thermoelastic martensitic transformation has a composition of 50 to 60% by weight of N+ and the balance T1. The reason why N1 is limited within the above-mentioned range is that outside this range, it is difficult to exhibit the shape memory effect.

DESCRIPTION OF EMBODIMENTS Example 1 Example 1 is shown in FIG. 1! [was used. As the capillary 4 in FIG. 1, one having the shape shown in FIG. 2 was selected. That is, the diameter a is 3 + n,
A polycrystalline filament-shaped functional alloy member 6 of Ti-50,0 atomic % Ni alloy was produced in a vacuum atmosphere using a capillary with a length b of 2511 mm. In addition, capillary 4
Graphite coated with ■IN was used. The obtained filament was continuously wound up to 200 m
It can be manufactured without disconnection up to 60°C ± 2.
It was possible to control the temperature within ℃.

Note that the length of functional alloy members such as filaments that can be produced at one time depends on the reactivity between the capillary and the molten metal, and in this sense, a substance that does not react with the molten metal is used for the capillary.

Example 2 In this Example 2, the apparatus shown in FIG. 3 is used, and in particular, the capillary shown in FIG. 4 is applied to obtain stripes.

Referring to FIG. 3, a container 9 containing melt a8 is placed in a state where it is heated by a heater having a heater coil 10. As shown in FIG. A capillary 11 is formed at the lower end of this container 9 so as to face downward. This capillary 11
A heater coil 12 for the fine coagulation part m mark sl'a is arranged around the area where is located.

Capillary 11 is shown enlarged in FIG.

The capillary 11 has a thickness C of 0.51 - and a width d of 20111.

As shown in FIG. 3, the molten metal 8 is drawn out from the capillary 11 in a state where its own weight and surface tension are balanced. In Figures 3 and 4, the solidification interface is 13
Below this solidification interface 13, there is a strip 14.
is formed.

Using such a device, T1-48, O
A single-crystal strip 14 of W, %Ni-2 atomic%l''a alloy was produced.While this strip 14 was restrained in a straight state, it was
After heat treatment at 0° C. for 15 min, this restraint was removed and it showed good superelastic behavior at room temperature.

Example 3 In this Example 3, the apparatus shown in FIG. 1 was used again, and the capillaries shown in FIGS. 5 to 7 were used. Note that FIG. 5 is a perspective view partially showing the vicinity of the solidification interface 7 at the tip of the capillary 4. FIG. 6 is a top view of the capillary 4, and FIG. 7 is a top view of the capillary 4, and FIG.
It is a sectional view along y-■.

The gear pillar 4 shown in these drawings is designed to obtain a functional alloy member 6 having a circular cross-section and a hollow pipe shape, as partially shown in FIG. As shown in FIGS. 6 and 7, the capillary 4 is formed with a plurality of passages 1s15 that communicate with the inside of the container 2 (FIG. 1), and above the passages 15, a functional alloy member 6 is formed. A molding space 16 having a cross-sectional shape is formed.

Using such an apparatus, a polycrystalline vibro of Tl-50, 8 atomic % N1 alloy was created. A slit 17 as shown in FIG. 8 was provided in this vibro, and the slit was heat-treated (memory treated) at 450° C. for 30 minutes while maintaining the diameter at that time. Next, after expanding the inner diameter by 4% in (dry ice + alcohol) and returning to room temperature, the inner diameter shrank to the memorized state.

This invention has been explained above in relation to Examples 1 to 3, but
The functional alloy member obtained by this invention is, for example,
It can be used for various purposes such as connectors and actuators. Any member may be used as long as it has at least one of a shape memory effect, a superelastic effect, and a vibration damping effect.

[Brief explanation of drawings]

FIG. 1 shows an apparatus used in one embodiment of the invention, and corresponds to embodiments 1 and 3. FIG. 2 shows the capillary 4 used in Example 1, and shows the vicinity of the solidification interface 7 at the tip of the capillary 4. 3 and 4 correspond to Example 2, with FIG. 3 showing the entire device and FIG. 4 being a perspective view showing the vicinity of the solidification interface 13 at the tip of the capillary 11. 5 to 8 correspond to Example 3, FIG. 5 is a perspective view showing the vicinity of the solidification interface 7 at the tip of the capillary 4, and FIG. 6 is a top view of the capillary 4, FIG. 7 is a sectional view taken along the line (--yH) in FIG. 6, and FIG. 8 is a perspective view showing the vibro in which the slit 17 is formed. In the figure, 1 and 8 are molten metal, 4 and 11 are capillaries, and 5
(6 is the viewing alloy member (filament or pipe), 7.13 is the solidification interface, and 14 is the strip. Foil 1 Figure Volume 20 Figure 3 Figure 5゜ Figure 6

Claims (5)

[Claims] (1) Ni 50 undergoes thermoelastic martensitic transformation
~60% by weight, the balance is T1, or a part of N1 or C'T' i is C0, AI, V, zr s
An R8 tank made of an alloy substituted with one or more elements selected from the group consisting of Mo, Qr%Fe%co%rare earth elements is exposed under pressure from the inside of a capillary made of a refractory material that does not react with the alloy. 1. A method for manufacturing a functional alloy member, the method comprising: drawing the functional alloy member from the capillary while solidifying it near the exit of the capillary. (2) The method for manufacturing a functional alloy member according to claim 1, wherein the drawing direction is upward, and the pressurization is performed by separately applying pressure to the molten metal. (3) The function according to claim 1, wherein the drawing direction is downward, and the pressurization is applied by the weight of the molten metal, by applying pressure to the molten metal, or by drawing the solidified part downward. Method for manufacturing alloy parts. (4) The method for manufacturing a functional alloy member according to any one of claims 1 to 3, wherein the drawing is performed in a vacuum. (5) The method for manufacturing a functional alloy member according to any one of claims 1 to 4, wherein the functional alloy member is elongated.