JPH06123276A - Thermal and mechanical energy transducing type driving element - Google Patents

Abstract

PURPOSE:To easily obtain a thin final product, attain quick thermal response, satisfactory thermal-mechanical energy transducing efficiency, prevent deterioration of memory, and make use for a long term even in a strong acid and alkaline environment. CONSTITUTION:Hot water 10 in which Ti-Ni-Cu alloy is molten is flame-coated onto a rotary copper roll 13 directly from a quartz nozzle 12 around which a specimen induction heating coil 11 in an atmosphere of high-purity Ar. The hot water is rapidly cooled and solidified at a molten hot water contact portion 14 with cooling speed of 10<2> to 10<6> deg.C/S, to obtain a rapid-cooled and solidified ribbon 15. The rapid-cooled and solidified ribbon 15 is utilized as a coil for opening and closing an automatic dryer, which is a thermal and mechanical energy transducing type driving element.

Description

Detailed Description of the Invention

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a thermo-mechanical energy conversion type drive element in which a shape memory material stores a shape of a key portion.

[0002]

2. Description of the Related Art In recent years, thermomechanical energy conversion type drive elements made of shape memory materials have been widely used in thermostats, automatic dryers, fire alarms, switches for protecting electric circuits, heat sinks and the like.

9 and 10 show an example in which a thermo-mechanical energy conversion type driving element is applied to an automatic dryer. The automatic drying chamber comprises a drying chamber 1 and a drying unit 2 connected to the drying chamber 1. The drying unit 2 is composed of a heater unit 3, a hygroscopic agent filling unit 4, and a link mechanism unit 5 in order from the bottom. ing. The moisture absorbent filling section 4 is opened and closed by opening and closing two doors 6 and 7 provided at the end of the link mechanism.
And it can communicate with outside air. The link mechanism portion 5 is provided with a tension spring 8 that biases the inner door 6 to a normally open state (absorption state). Further, the hygroscopic agent filling section 4 is provided with a coil 9 which operates the link mechanism against the force of the tension spring 8 by heating the heater section 3 to open the outer door 7 (dehumidification state). Has been. The coil 9 is a thermo-mechanical energy conversion type driving element made of, for example, Ti, Ni, or Cu-based shape memory alloy.

In the automatic dryer having the above-described structure, the hygroscopic agent is not heated by the heater section 3 in the normal state, and the hygroscopic state is as shown in FIG. That is, with the coil 9 extended, the inner door 6 is opened by the force of the tension spring 8 via the link mechanism, the dry moisture 1 and the hygroscopic agent filling portion 4 communicate, and the outer door 7 is opened.
Is closed and isolated from the outside air. When moisture is absorbed for a long time, the moisture absorbent deteriorates. Therefore, it is necessary to close the inner door 6 and open the outer door 7 that communicates with the outside air at regular intervals to heat the hygroscopic agent and release the absorbed moisture to the outside.

At this time, the heating of the heater portion 3 causes the coil 9 to contract as shown in FIG. 10 when the transformation temperature is reached, actuating the link mechanism against the force of the tension spring 8,
The inner door 6 is closed and the outer door 7 is opened, so that the moisture is exhausted. Then, when the heating of the heater portion 3 is stopped after the water is sufficiently discharged, the coil 9 becomes lower than the transformation temperature and becomes the extended state as shown in FIG. 9 again. As a result, the action of the tension spring 8 closes the outer door 7 and opens the inner door 6 to absorb moisture.

[0006] By the way, conventionally, the shape memory alloy forming the coil 9 is generally obtained by a melting and hot working process to obtain a product material having a final shape. According to this melting / hot working process, an ingot made by high-frequency vacuum melting or plasma melting is processed into a desired shape by hot working means such as pressing, rolling, or forging. It was

[0007]

However, when a shape memory alloy such as a Ti-Ni-Cu system is obtained by this melting / hot working process, the Ti-Ni alloy is difficult to work and therefore has a thermal responsiveness. It is difficult to obtain a good thin plate product, and particularly when Cu is 10 at% or more, it becomes brittle and extremely difficult to work, so it is difficult to obtain a thin plate final product. Further, in the melt-processed material, the polycrystal orientations constituting the material are random as shown in FIG. 10, so the transformation time throughout the material is shifted depending on the location, and as a result, transformation strain-temperature range of temperature hysteresis curve (ΔT = Af-Mf)
Is large, and the bend near the loop transformation point becomes round,
The response of the shape memory alloy with the temperature change was slow.

Further, the discontinuity of the transformed crystal structure causes a loss in the useless transformation process, and the heat-to-mechanical energy conversion efficiency is several percent or less. Moreover, the crystal structure is coarse and the dislocation density of the matrix is low. Since it is small, the yield stress is low, and the memory effect deteriorates (memory blur) during repeated use.
The application range of A was narrowed. Also, regarding corrosion resistance,
Originally, the Ti-Ni system is good, but due to the coarse crystal grains of the processed material and the non-uniformity of the surface, there remains a problem for long-term use in an extremely strong acidic / alkaline extreme environment.

Therefore, the present invention has been made in view of the above conventional problems, and it is possible to easily obtain a thin plate final product, the response is sharp with a temperature change, and the heat / mechanical energy conversion efficiency is high. The thermo-mechanical energy of the shape memory material is good, and does not cause deterioration of memory effect (memory blurring) during repeated use, and can be used for a long period of time under extremely acidic and alkaline extreme environments. An object is to provide a conversion type driving element.

[0010]

It is understood that the material structure itself needs to be improved in order to minimize the defects of the shape memory alloy by the conventional melting and hot working. That is, in order to make the transformation strain-temperature hysteresis curve narrow and sharp, improve the energy conversion performance, and suppress fatigue deterioration, which is important for practical use, while increasing the strength, the alloy structure should be homogeneous, fine, and crystalline Should be arranged as much as possible so that the entire material simultaneously undergoes thermoelastic martensitic transformation. Further, in order to improve the thermal responsiveness of the material shape and to obtain an agile shape memory phenomenon, it is necessary to make the material thinner to increase the specific surface area and promote heat diffusion during cooling.

In order to develop a new material satisfying the above conditions, the inventors of the present invention directly inject a molten alloy system showing a shape memory phenomenon from a nozzle to a Cu cooling roll to obtain a final thin plate (about 20 to 300 microns). Rotational rapid solidification method (M)
lt-spinning Technology) was adopted. As a result, a homogeneous and extremely fine anisotropic (columnar crystal of a few microns or less) structure can be obtained by the rapid cooling effect of the rotary rapid solidification method, and the lower structure has a high dislocation density. , It is difficult to generate plastic strain due to yield, and there is no energy loss other than phase transformation.
The inventors have found that the improvement of heat / mechanical energy conversion performance, the deterioration of shape memory fatigue, and the improvement of corrosion resistance can be achieved, and the present invention has been accomplished.

That is, according to the thermo-mechanical energy conversion type drive element of the present invention, in the thermo-mechanical energy conversion type drive element in which a shape memory material stores a required shape, an alloy-type molten metal exhibiting a shape memory phenomenon is rapidly solidified. We decided to use the shape memory material obtained by doing so. Alloys exhibiting a shape memory phenomenon according to the present invention include those shown in Tables 1 and 2.

[0013]

[Table 1]

[0014]

[Table 2]

In order to rapidly solidify the alloy-type molten metal exhibiting the shape memory phenomenon, it is preferable that the cooling rate is 10 ² to 10 ⁶ ° C / sec. Further, as the shape memory material, Ti-
A Ti-Ni-based shape memory alloy obtained by rapidly solidifying a molten Ni-based alloy is suitable, and Ti (50 ± y, y ≦ ± 2 at%)-Ni is suitable as the shape-memory material.
A Ti-Ni-Cu-based shape memory alloy obtained by rapidly solidifying a (50-y-x) -Cu (xat%)-based alloy melt is particularly suitable. Here, the Cu content x is 0 <x ≦ 20.
At% is good. In this area, material embrittlement (grain boundary embrittlement, etc.) occurs in a normal melting / hot working process, making large rolling difficult.

Further, in the present invention, regarding the thermal / mechanical energy conversion efficiency η, the Cu content x is 11.0 to 1
It is better to set it to 6.0 at%, preferably 12.0-1.
It is better to set it to 4.0 at%. When x is less than 11.0 at%, the transformation strain becomes large, but the transformation temperature difference ΔT becomes large. On the contrary, when x exceeds 16.0 at%, the transformation temperature width ΔT is small but the transformation strain sharply decreases. Not preferable. Further, x is less than 12.0 at% or 14.0a.
If it exceeds t%, the parameter η showing the thermal energy conversion performance decreases, which is not preferable because it is inconvenient for use in a closed system.

Further, in the present invention, the Cu content x
Is preferably 3.0 to 7.0 at%. That is, when recovering thermal energy from a natural release system heat source (abandoned and undeveloped low-grade heat source, for example, hot springs, factory hot drainage, etc.), this x is in the range of 3.0 to 7.0 at%. This is because the recovery performance parameter μ is the largest and is advantageous. If the Cu content x is less than 3.0 at%, the transformation temperature width ΔT becomes too large (30 ° C. or more), and the application range and its practicality are narrowed. On the other hand, when X exceeds 7.0 at%, ΔT sharply decreases, but the transformation strain and μ sharply decrease and the thermal energy recovery performance deteriorates, which is disadvantageous.

Examples of the rapid solidification method used in the present invention include, for example, a gun method in which a molten metal is directly sprayed onto a Cu cooling plate to be rapidly cooled to produce a small test piece, a rotating roll (single or twin roll) method for producing a continuous thin plate, There are a spinning submerged spinning method suitable for producing fine wires, a spray method for producing a quenched powder, and the like. Among the above quenching methods, when performing rapid solidification by the rotating roll method (single roll), the cooling rate is 20 to 50 m / s.
ec is good. If the cooling rate is less than 20 m / sec, the quenched metal structure (particularly, the crystal grain size) becomes coarse and random orientation occurs, resulting in ablation of the shape memory transformation, resulting in a shape memory effect like a polycrystal and deterioration in fatigue resistance. And corrosion resistance will be reduced. On the contrary, when the cooling rate exceeds 50 m / sec, the metal structure becomes amorphous and the shape memory phenomenon based on the crystal transformation does not appear, which is not preferable.

[0019]

In general, when the molten metal is rapidly solidified by the molten metal rapid solidification method, the metal structure is finely crystallized from the dendrite phase as the cooling speed (roll rotation speed) is increased as shown in FIG. It transforms into a crystal through a crystal at a superquenching rate (1 × 10 ⁶ ° C / sec or more). For example, the quenching rate of the Ti-Ni-Cu molten metal is 40
When m / sec (1 × 10 ⁶ ° C./sec), the metal structure becomes fine columnar crystals (crystal grain size = 2 to 3 μm) with crystal axes aligned in the plate thickness direction as shown in FIG. Even if X-ray crystal structure analysis is performed on this point, it is confirmed that the crystal directions are aligned. Therefore, the Ti-Ni-Cu-based shape memory alloy cooled at this quenching rate has such a metal structure, and thus has the following function.

Since the crystal orientations are aligned due to the formation of columnar crystals, the Ti-Ni-Cu-based shape memory alloy simultaneously undergoes uniform transformation as a whole. Therefore, if the crystal orientation with a large shape memory transformation strain is aligned with the longitudinal direction of the material by the rapid solidification method, the transformation strain can be increased as a whole material. Also, because of the fine columnar crystals, transformation occurs at the same time for the entire material,
As a result, the transformation temperature width ΔT becomes small and the hysteresis becomes sharp. Since it has a fine crystal structure,
The material yield stress is high and the load stress stability is improved.
Furthermore, as a result of the higher yield stress in the fine crystals and the uniform crystal orientation, plastic strain
Metastases are less likely to be introduced, and functional fatigue deterioration (memory blur) is less likely to occur.

Ti (50 ± y, y ≦ ± 2 at of the present invention
%)-Ni (50-y-x) -Cu (xat%) based alloy, if the addition amount x of Cu is 5 at%, the transformation route in the cooling process follows the route from cubic to monoclinic.
This transformation mechanism is a one-step transformation mechanism, and although a large transformation strain can be obtained, a large heat source from the outside is required for that, so the transformation temperature width is large.

On the other hand, Ti (50 ± y, y ≦ ± of the present invention
2 at%)-Ni (50-y-x) -Cu (xat%)
In a system alloy, if the addition amount x of Cu is about 15 at%,
In the vicinity, the route from cubic to orthorhombic and then to monoclinic is followed. In this case, the transformation strain is small, but the transformation history, that is, the transformation temperature width is small because the crystal nucleation and growth in the transformation process are suppressed in sequence, and the smooth transformation process is followed, resulting in energy conversion. It is presumed that the performance will be good.

[0023]

EXAMPLE A molten Ti—Ni—Cu alloy 10 having the composition shown in Table 1 obtained by arc melting a TiNiCu ingot material in an Ar atmosphere using the rotary rapid solidification apparatus shown in FIG.
In a high-purity Ar atmosphere, the sample induction heating coil 11
Rotating copper roll 13 directly from quartz nozzle 12 around which is wound
And was rapidly cooled and solidified at the molten metal contact portion 14 to obtain a rapidly solidified ribbon 15. At that time, the cooling rate is 1
It is set to × 10 ⁴ to 1 × 10 ⁶ ° C / sec, a roll speed is 20 to 40 m / sec, and a rotating copper roll for cooling (diameter =
(200 mm) The rotation speed was 2000 to 4000 rpm. The dimensions of the obtained Ti-Ni-Cu-based shape memory alloy ribbon were 0.03 mm in plate thickness, 2.0 mm in width, and 200 mm in length. The ribbon was subjected to shape memory treatment to manufacture the coil 9 of the automatic dryer shown in FIG. Various properties shown in Table 2 were evaluated for the alloy ribbon.

[0024]

[Table 1] (Alloy chemical composition)

[0025]

[Table 2] (Evaluation characteristics and evaluation conditions or evaluation methods)

The evaluation results of the above various characteristics are shown in FIGS. As shown in FIG. 2, the hysteresis curve of the quenched material is stable against an increase in stress, and the hysteresis loop of the rapidly solidified Ti—Ni—Cu-based shape memory alloy is narrow and sharp as compared with the hysteresis loop of the melt-processed material. Moreover, the transformation temperature difference ΔT is kept small, and it can be said that the stability of the characteristics and functions against external load stress is high.

Further, as shown in FIGS. 3 and 4, each transformation point is the lowest at around 313 K at around Cu 13%. From this data, Ti (50 ± y, y ≦ ± 2at%)-Ni (5
In the 0-y-x) -Cu (xat%)-based alloy, the transformation point can be further adjusted to a low temperature level below room temperature by adjusting the y component or adding the fourth element (Co, Fe, etc.). For example, a thermomechanical energy conversion element that can be driven with a temperature difference near room temperature will be realized.

Next, FIG. 5 shows an evaluation of hysteresis loop, thermal energy conversion / recovery performance and ΔT change, etc., when the Cu addition amount of the Ti—Ni—Cu type shape memory alloy is changed to 0 to 20 at%. The results are shown.

In FIG. 5, the heat energy recovery performance (performance in the natural heat energy release system) parameter μ is expressed by the equation (1). μ = σ · ε / 2 (1) σ: Load stress ε: Transformation strain width (here, defined between the reverse transformation processes As and Af)

Further, in FIG. 5, heat energy conversion performance (performance of extracting mechanical energy by introducing heat from the outside in a closed system).
The parameter η is defined by the equation (2). η = (σ · ε) / Δq (2) Δq: Amount of heat absorbed per unit mass during transformation (DSC
(Measurement) As shown in FIG. 5, the transformation strain Δε is maximum at Cu 5%, and the transformation temperature difference ΔT is 10 at Cu 10 at% or more.
The temperature became lower than 0 ° C and reached a minimum value of 6 ° C at Cu = 15 to 17 at%.

Further, as shown in FIG. 5, the heat energy recovery performance parameter μ becomes maximum at around Cu 5%, while the heat energy conversion performance parameter η is Cu 13 at%.
It shows the maximum value before and after, and is 2 to 10 at Cu = 0.10 at% as compared with the melt-processed material indicated by ○ in the lower part of the figure.
A significant improvement of up to 5 to 6 times is recognized in the narrow chemical structure region of 3 times, and further in the vicinity of Cu = 13 at%. Therefore, in FIG. 5, it can be said that the hatched portion is the characteristic superior region of the rapidly solidified material of the embodiment of the present invention.

FIGS. 6 and 7 show Ti-Ni-based shape memory alloys and Ti-Ni- alloys as examples of rapidly solidified shape memory alloys.
The fatigue deterioration resistance of the Cu-based shape memory alloy is also shown in comparison with the melt-processed material. In FIG. 6, ΔD _N represents the shape memory transformation strain width in the Nth heat cycle, and ΔD ₁ represents the shape memory transformation strain width in the _first heat cycle. N is the number of thermal cycles, Nf is the number of thermal cycles required for fracture, and N /
Nf represents a fatigue life ratio. In FIG. 7, L ₀ indicates the initial reference length, U indicates the elongation amount, and U / L ₀ indicates the elongation strain amount. As shown in FIG. 6, in the rapidly solidified Ti-Ni-Cu-based shape memory alloy, the deterioration of the transformation strain ΔD _N / ΔD ₁ changes and maintains approximately 1.0, while the melt-processed material gradually increases. Increase to. Further, as shown in FIG. 7, the rapidly solidified Ti-Ni-based shape memory alloy and the rapidly solidified Ti-Ni are used.
In the Cu-based shape memory alloy, almost no repeated elongation deterioration U / L ₀ is observed, whereas the melt-processed material also shows remarkable repeated elongation deterioration.

FIG. 8 shows the polarization curve of the Ti—Ni—Cu type shape memory alloy of this example measured in hydrochloric acid (1N / HCl). As shown in the figure, even if the lowest point of each polarization curve, that is, the so-called natural electrode potential level is compared, the corrosion resistance can be greatly improved by 100 times to 10,000 times as compared with the conventional melt processed material. To be understood.

FIG. 11 shows an embodiment in which the shape memory alloy element of the present invention is applied to an automatic wind direction adjusting type outlet. Figure 1
As shown in FIG. 1, a vane 21 is attached to the blowout port 20, and the vane 21 determines the blowing direction of cold air or warm air. That is, the vane 21 is actuated by the shape memory alloy wire spring 22 and the bias spring 23 to which the shape memory alloy element of the present invention is applied, the vane 21 is directed vertically downward during heating, while the vane 21 is inclined during cooling.

Therefore, horizontal air can be blown out so as not to be too cold just below the air outlet during cooling, and conversely, hot air can be blown vertically downward during heating.

12 and 13 show an example of using the shape memory alloy element of the present invention with a heat sink. When the shape memory alloy element is used in high vacuum in space, the cooling rate of the element becomes the biggest problem. The solid line in FIG. 13 is a diagram showing changes in the amount of strain due to cooling under constant stress with the atmospheric pressure as a parameter. As can be seen from this figure, it takes about 30 seconds to obtain a sufficient strain amount in the atmosphere, and about 5 minutes in the vacuum (especially 10 ⁻⁵ Torr). Therefore,
For example, it can be used as it is for applications such as sun tracking with slow operation, but it cannot be used for manipulators and the like that require high response speed.

FIG. 13 shows a mode in which a heat sink 31 is provided as a heating means for the shape memory alloy element 30 as a measure against such a problem. In this case, the thermal conductivity of the thermal conductive medium between the heat sink 31 and the shape memory alloy element 30 is important, and if the thermal conductivity is too large, heating cannot be performed. As the heat transfer medium, grease 32 having a heat conductivity about three times that of the atmosphere and an extremely low vapor pressure can be used. By doing so, FIG.
As indicated by the broken line in Fig. 3, a sufficient amount of strain was obtained in about one fifth of the time in atmospheric pressure.

Moreover, since the thermo-mechanical energy conversion type driving element of the present invention has a far more sensitive response than the conventional material, it can be sufficiently applied to such use in outer space. That is, by applying the thermo-mechanical energy conversion type driving element of the present invention to this shape memory alloy element 30, since the transformation temperature width is narrower than that of a usual melt-processed material, it operates sensitively to temperature changes and is repeatedly used. Significantly reduced functional deterioration (memory blur) (1/10)
It will be extremely long life. The oxidizing atmosphere (1
Corrosion resistance in N-Hcl) hydrochloric acid is significantly improved (100-
10,000 times). FIG. 14 shows an application example of a shape memory manipulator suitable for grasping a soft object such as a living body, a cell, or an egg. The shape memory alloy (wire, plate) covered with polymer or silicone rubber bends inward by electric heating from the outside, making it possible to operate as if it were a finger. It should be noted that when the electric heating is stopped, the original shape can be restored by the elasticity of the embedded polymer and silicon rubber. Further, FIG. 15 shows an example in which a current-carrying shape memory alloy is set in the grip portion at the tip of a gripping device for foreign matter or the like. For example, it is suitable for extracting a calculus or the like inside a living body, but the plate (blade) of the grip portion is made of a shape memory alloy alone or as shown in FIG.
As shown in Fig. 3, a polymer base (base) shape memory thin plate and a wire are incorporated, and a lead wire (conductor wire) connected to the rear side of the polymer base heats the resistance resistance and heats the shape memory operation to grasp. To examine the properties inside the ureter that connect to the rectum, esophagus, bronchi, and even the bladder and kidneys
It is indispensable to develop an endoscope (endroscope) that can perform a sufficient examination while minimizing the discomfort given to the patient by the intricately bent living body cavity, but the mechanical control increases the weight and size, There was a drawback that it became difficult to bend. FIG. 17 shows a method 3 utilizing shape memory deformation devised for that purpose.
1 shows an example of a schematic diagram of a three-dimensionally actively operable endoscope.
As a bendable internal structure therefor, a method in which a universal joint (flexible joint) shown in FIG. 18 is combined with a shape memory spring, or a conducting wire as shown in FIG. 19 (also used for bias restoring force) Therefore, a spiral deformation control method can be considered. As shown in FIG. 20, the material itself is deformed instead of the mechanical valve for adjusting or stopping the liquid flow rate in the pipe, and it is effective for use as an artificial muscle in which the flow rate cross-sectional area can be freely adjusted. In this case as well, it is necessary to change the temperature due to external energization or heat ray irradiation as shown in the figure. That,
FIG. 21 shows an example of the structure of the artificial muscle portion. Between the shape memory alloy wire and the plate, a metal or polymer for reaction force (bias) that promotes shape recovery during cooling is required. However,
This is not necessary if a two-way shape memory material is used.

[0039]

As described above, according to the thermo-mechanical energy conversion type driving element of the present invention, the following excellent effects are exhibited. 1. The performance of converting the absorbed heat per unit volume during transformation into mechanical work is improved, and the heat energy recovery performance from the low temperature difference heat resource medium is 2-3 times higher (up to 5 at Cu = 13 at%).
~ 6 times) improved. 2. The transformation temperature width is narrower than that of ordinary melt-processed materials, and the transformation temperature width ΔT is at least 6 ° C near Cu = 15 to 17 at%.
It is sensitive to temperature changes, has a rapid transformation strain expansion / contraction function, and has a transformation strain larger than that of the melt-processed material. 3. Functional deterioration (memory blur) due to repeated use is greatly reduced (about 1/10). 4. Corrosion resistance in oxidizing atmosphere (1N-Hcl) hydrochloric acid is significantly improved (100 to 10,000 times).

Since the thermo-mechanical energy conversion type drive element of the present invention has the above-mentioned excellent functions, it can be applied to the following examples in addition to the automatic dryer of the embodiment, the automatic wind direction adjusting type outlet, and the like. Become. (1) Thermo-mechanical application Using a shape memory alloy that has both a temperature sensor and a driving element as a thermal actuator (thermo-mechanical driving element), a thermostat, a fire alarm, an electric circuit protection switch, a pipe joint, and a robot. When used as an artificial muscle for use (ultra-small thermal actuator by heating / cooling electric resistance), the above-mentioned features work advantageously. That is, for example, as a temperature sensor, the transformation ends within a very narrow temperature range (As near Cu = 13 at%).
→ Af point, Ms → Mf point is within 1 ° C, and the transformation temperature range is within 10 ° C (10 at% or more, minimum = 6 ° C, Cu
= 13 at%), it is possible to react extremely sensitively to changes in the external temperature. Further, repeated memory blurring is greatly suppressed (about 1/10 of the melt-processed material), so that long-term repeated use and its reliability are increased. In addition, the corrosion resistance is significantly improved even in a strongly acidic environment (up to 1
Therefore, it can be seen that it can be used as a thermo-mechanical energy conversion driving element that can be used even in a very bad environment.

Furthermore, since the efficiency of converting heat into mechanical energy is about three times better than that of conventional materials, it is possible to drive the robot actuator with a heat source (heating power consumption) smaller than in the prior art, and energy can be saved. . Also,
The thermo-mechanical energy conversion type drive element of the present invention can form an extremely thin strip (20 to 300 μm), which is impossible by melting processing, so that heat is easily diffused from the surface during cooling, and the response in the transformation cycle is high. It can greatly improve the sex.

(2) Application example of thermal energy conversion material By applying the thermoelastic martensite transformation of the thermomechanical energy conversion type driving element of the present invention, so-called low temperature difference heat from factory wastewater, power plant, hot spring, etc. Mechanical energy can be extracted from energy. From the various characteristics of the thermo-mechanical energy conversion type driving element of the present invention, the transformation cycle is completed within a narrower temperature range (10 ° C. or less) than that of the conventional melting / processing material. Energy can be recovered and fatigue deterioration can be suppressed, so that it can be used for a long time. Further, since a large transformation strain can be obtained, a large energy recovery rate from the open system heat source becomes possible.

[Brief description of drawings]

FIG. 1 is a schematic diagram of a rapid solidification apparatus used to obtain a Ti—Ni—Cu-based shape memory alloy as an example of a rapidly solidified shape memory alloy applied to the present invention.

FIG. 2 is a diagram showing a comparison between a hysteresis loop of a Ti—Ni—Cu-based shape memory alloy as an example of a rapidly solidified shape memory alloy applied to the present invention and a hysteresis loop of a conventional material.

FIG. 3 is a Ti-Ni-Cu-based shape memory alloy as an example of a rapidly solidified shape memory alloy applied to the present invention.
It is a figure which shows the change of a hysteresis loop when changing the addition amount to 0-20%.

FIG. 4 is a Ti-Ni-Cu-based shape memory alloy Cu which is an example of a rapidly solidified shape memory alloy applied to the present invention.
It is a figure which shows synthetically the change of each transformation temperature when changing the addition amount to 0-20%.

FIG. 5 is a Ti-Ni-Cu-based shape memory alloy Cu as an example of a rapidly solidified shape memory alloy applied to the present invention.
It is a figure which shows synthetically the change of the heat energy recovery performance (micro | micron | mu), heat energy conversion performance (eta), and transformation temperature difference (DELTA) T when changing the addition amount to 0-20%.

FIG. 6 is a diagram showing fatigue deterioration resistance of a Ti—Ni—Cu-based shape memory alloy as an example of a rapidly solidified shape memory alloy applied to the present invention.

FIG. 7 is another diagram showing fatigue deterioration resistance of a Ti—Ni—Cu-based shape memory alloy as an example of the rapidly solidified shape memory alloy applied to the present invention.

FIG. 8 is a diagram showing a polarization curve of a Ti—Ni—Cu-based shape memory alloy in hydrochloric acid (1N / HCl) as an example of a rapidly solidified shape memory alloy applied to the present invention.

FIG. 9 is an operation explanatory view of an automatic dryer as an example to which the shape memory alloy element of the present invention is applied.

FIG. 10 is also an operation explanatory view of an automatic dryer as an example to which the shape memory alloy element of the present invention is applied.

FIG. 11 is an operation explanatory view of an automatic wind direction adjustment type blowout port as an example to which the shape memory alloy element of the present invention is applied.

FIG. 12 is a diagram showing the time variation of the strain amount due to cooling under constant stress of the shape memory alloy element of the present invention with the atmospheric pressure as a parameter.

FIG. 13 is a diagram showing a case where a heat sink is used as an example of an application mode of the shape memory alloy element of the present invention.

FIG. 14 is a diagram showing an application example of a shape memory manipulator suitable for grasping a soft object such as a living body, a cell, or an egg.

FIG. 15 is a diagram showing an example in which a current-carrying shape memory alloy is set in the grip portion of the tip of a gripping tool for foreign matter or the like.

FIG. 16 shows a polymer based shape memory lamella.

FIG. 17 shows an example of a schematic diagram of a three-dimensionally active endoscope using shape memory deformation.

FIG. 18 shows a system in which a universal joint (flexible joint) and a shape memory spring are combined.

FIG. 19 shows a conducting wire (also used for bias restoring force) and a spiral deformation control system.

FIG. 20 shows the use as an artificial muscle in which the material itself is deformed in place of a mechanical valve for adjusting or stopping the liquid flow rate in the pipe, and the flow rate cross-sectional area can be freely adjusted.

FIG. 21 shows an example of the structure of the artificial muscle portion.

FIG. 22 is a schematic diagram showing a structural change with a rapid cooling rate of a Ti—Ni-based shape memory alloy as an example of a rapidly solidified shape memory alloy applied to the present invention.

[Explanation of symbols]

 11 Sample Induction Heating Coil 12 Quartz Nozzle 13 Rotating Cu Roll 14 Molten Metal Contact Part 15 Rapidly Solidified Ribbon

 ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Yasufumi Furuya, 14-1-33 Sanjo-cho, Aoba-ku, Sendai-shi, Miyagi (72) Inventor Yoshikatsu Tanahashi 10-26 (72) Kasumi-cho, Yagiyama, Taihaku-ku, Sendai, Miyagi ) Inventor Ken Masumoto 3-8-22, Uesugi, Aoba-ku, Sendai City, Miyagi Prefecture

Claims (7)

[Claims] 1. A thermo-mechanical energy conversion type drive element in which a desired shape is stored in a shape memory material, wherein a shape memory material obtained by rapid solidification of an alloy-based molten metal exhibiting a shape memory phenomenon is used. A thermo-mechanical energy conversion type driving element. 2. A cooling rate of 10 ² to 10 ⁶ ° C./se for rapid solidification of an alloy-based molten metal exhibiting a shape memory phenomenon.
The thermo-mechanical energy conversion type drive element according to claim 1, wherein c is c. 3. A thermo-mechanical energy conversion type drive element in which a shape memory material stores a required shape, and a Ti-Ni type shape obtained by quenching and solidifying a Ti-Ni type alloy melt as the shape memory material. The thermomechanical energy conversion type drive element according to claim 1, wherein a memory alloy is used. 4. A thermo-mechanical energy conversion type driving element in which a shape memory material stores a desired shape, wherein Ti (50 ± y, y ≦ ± 2 at) is used as the shape memory material.
%)-Ni (50-y-x) -Cu (xat%)-based alloy molten metal is used, and a Ti-Ni-Cu-based shape memory alloy obtained by rapid solidification is used. . 5. The thermomechanical energy conversion type drive element according to claim 3, wherein the Cu content x is 0 <x ≦ 20 at%. 6. The Cu content x is 11.0 to 16.0a.
The thermo-mechanical energy conversion type driving element according to claim 3, wherein the driving element is t%. 7. The Cu content x is 3.0 to 7.0 at%.
The thermo-mechanical energy conversion type drive element according to claim 3.