KR101705963B1 - Tirecord and spandex using using piezoelectric fiber, energy harvester using the same and manufaturing method thereof - Google Patents

Abstract

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a tire cord, a spandex, and an energy harvesting apparatus using the ferroelectric material manufactured using the fiber manufacturing method. A composite fabric tire cord according to one aspect of the present invention is a composite fabric tire cord that is woven with a plurality of fibers to reinforce the tire, wherein the plurality of fibers comprise at least one synthetic fiber and at least one piezoelectric fiber, The fibers can generate electrical energy by deformation caused by an external force applied to the piezoelectric fibers.

Description

TECHNICAL FIELD [0001] The present invention relates to a tire cord and spandex using a piezoelectric fiber, an energy harvesting apparatus using the same, and a manufacturing method thereof,

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a tire cord and a spandex to which a ferroelectric material manufactured by using a fiber manufacturing method is applied, and an energy harvesting apparatus using the ferroelectric material. More particularly, the present invention relates to a piezoelectric fiber produced by using a ferroelectric layer, To fabricate functional fabrics in combination with fibers, and to energy harvesting using functional fabrics.

In 1920, this substance was first discovered in the substance called the shelled salt. When an electric field is applied to a material, the dipole moment generally occurs due to the electric field, resulting in electric polarization. However, there is a certain substance that spontaneously undergoes electric polarization even when no electric field is applied. This substance is called a ferroelectric substance.

In other words, ferroelectrics are materials that have electrical polarization in their natural state. These materials, which exhibit spontaneous polarization, exclude that the direction of polarization does not change in the electric field, and they exhibit piezoelectricity and superconductivity by changing polarization.

A ferroelectric is a type of dielectric that is an electrically insulating material and has a specific physical property.

Also, unlike ordinary dielectrics, dielectric polarization is not proportional to the electric field, and the relationship between the polarization and the electric field, like the ferromagnetic material, is characterized by hysteresis and saturation. To date, more than one hundred and dozens of ferroelectric materials have been discovered.

These materials are characterized not only by spontaneous polarization but also by the fact that this spontaneous polarization is reversed by an electric field.

There are many materials that have spontaneous polarization among dielectrics, but they can not be said to be ferroelectric unless they can change the direction of polarization by the electric field.

The ferroelectric exhibits a phase transition at the Curie temperature. Under the phase transition temperature, the spontaneous polarization is arranged in a specific direction through the interaction between the electric dipoles, and the spontaneous polarization is lost due to the thermal fluctuation above the temperature.

Under the Curie temperature, the spontaneous polarization is aligned in a certain direction, but a domain is formed together.

The physical properties of the ferroelectric material are piezoelectric and pyroelectric due to the reversal phenomenon of the spontaneous polarization.

Using this characteristic of the ferroelectric, it is possible to develop GPS, which is a position tracking device using a personal portable night vision goggle or satellite, and a device for securing a night vision of a car.

The ferroelectric has a high refractive index and a large nonlinear optical constant because of its excellent optical properties.

Utilizing these characteristics, it can be applied to an optical waveguide, and the frequency of the laser can be doubled.

In addition, the ferroelectric material has a large piezoelectric constant, so it is widely used in acoustic machines and is also used as a dielectric of a small capacitor by using a large dielectric constant.

In order to utilize the ferroelectric properties in various ways, it is required to develop a method for energy harvesting by the piezoelectricity of the ferroelectric in combination with the functional fiber.

It is an object of the present invention to provide a tire cord, a spandex and an energy harvesting apparatus using the ferroelectric to a user.

Specifically, it is an object of the present invention to provide a tire cord and spandex fiber having a combination of a piezoelectric fiber and a synthetic fiber both of which have characteristics of two kinds of fibers.

It is to be understood that both the foregoing general description and the following detailed description of the present invention are exemplary and explanatory and are not intended to limit the invention to the precise form disclosed. It can be understood.

A composite fabric tire cord according to one aspect of the present invention for realizing the above-mentioned object is a composite fabric tire cord that is woven with a plurality of fibers to reinforce the tire, wherein the plurality of fibers includes at least one synthetic fiber and at least one piezoelectric fiber And the piezoelectric fiber can generate electrical energy by deformation due to an external force applied to the piezoelectric fiber.

In addition, the synthetic fibers may include at least one of polyamide fibers, polyester fibers, and polyvinyl alcohol fibers.

Further, the piezoelectric fiber may be a fiber produced by a fiber manufacturing method of a ferroelectric layer.

On the other hand, a spandex fabric related to an example of the present invention for realizing the above-mentioned problems is a spandex fabric woven with a plurality of fibers, wherein the plurality of fibers comprise at least one spandex and at least one piezoelectric fiber, The fibers can generate electrical energy by deformation caused by an external force applied to the piezoelectric fibers.

Further, the piezoelectric fiber may be a fiber produced by a fiber manufacturing method of a ferroelectric layer.

In an energy harvesting apparatus according to an embodiment of the present invention for realizing the above-mentioned problems, an energy harvesting apparatus including the composite fabric tire cord or the spandex fabric is provided. The energy harvesting apparatus is electrically connected to the piezoelectric fiber, And a power storage unit for storing electrical energy generated in the fiber.

On the other hand, a method of manufacturing a composite fabric tire cord according to an embodiment of the present invention for realizing the above-

CLAIMS What is claimed is: 1. A method of making a composite fabric tire cord that is woven with a plurality of fibers to reinforce the tire, the method comprising: providing the plurality of fibers comprising at least one synthetic fiber and at least one piezoelectric fiber; And woven the composite fabric tire cord using the plurality of fibers, wherein the piezoelectric fiber is capable of generating electrical energy by deformation due to an external force applied to the piezoelectric fiber.

In addition, the synthetic fibers may include at least one of polyamide fibers, polyester fibers, and polyvinyl alcohol fibers.

The method may further include the step of fabricating the piezoelectric fiber by a fiber manufacturing method using a ferroelectric layer before the step of providing the fiber.

The method for fabricating the fiber includes at least one of rolling, extruding, and drawing, and the manufacturing method of the ferroelectric layer includes a step of forming the ferroelectric layer through a phase change step in which the crystal structure of the ferroelectric is set to? can do.

The ferroelectric layer phase change step may include: a temperature raising step of raising the temperature of the ferroelectric to a temperature equal to or higher than a temperature that forms a? Phase crystal; A first temperature decreasing step of monotonically decreasing the temperature of the ferroelectric to a? Phase crystal temperature; And a second temperature decreasing step of rapidly lowering the temperature of the ferroelectric substance.

The phase change step of the ferroelectric layer may include a temperature raising step of raising the temperature of the ferroelectric to a temperature that forms a? Phase crystal; And a temperature lowering step of rapidly lowering the temperature of the ferroelectric substance; . ≪ / RTI >

On the other hand, a method for manufacturing a spandex fabric in accordance with one aspect of the present invention for realizing the above-mentioned problem, includes the steps of: preparing a plurality of spandex fabrics woven from a fiber, the spandex comprising at least one spandex and at least one piezoelectric fiber Of fibers; And woven the spandex fabric using the plurality of fibers, wherein the piezoelectric fibers can generate electrical energy by deformation due to an external force applied to the piezoelectric fibers.

The method may further include the step of fabricating the piezoelectric fiber by a fiber manufacturing method using a ferroelectric layer before the step of providing the fiber.

The method for fabricating the fiber includes at least one of rolling, extruding, and drawing, and the manufacturing method of the ferroelectric layer includes a step of forming the ferroelectric layer through a phase change step in which the crystal structure of the ferroelectric is set to? can do.

The ferroelectric layer phase change step may include: a temperature raising step of raising the temperature of the ferroelectric to a temperature equal to or higher than a temperature that forms a? Phase crystal; A first temperature decreasing step of monotonically decreasing the temperature of the ferroelectric to a? Phase crystal temperature; And a second temperature decreasing step of rapidly lowering the temperature of the ferroelectric substance.

The phase change step of the ferroelectric layer may include a temperature raising step of raising the temperature of the ferroelectric to a temperature that forms a? Phase crystal; And a temperature lowering step of rapidly lowering the temperature of the ferroelectric substance.

The present invention can provide a tire cord and a spandex to which ferroelectrics are applied and an energy harvesting device using the same.

Specifically, a combination of a piezoelectric fiber and a synthetic fiber can provide a user with a tire cord and spandex fiber having both characteristics of the two fibers.

It should be understood, however, that the effects obtained by the present invention are not limited to the above-mentioned effects, and other effects not mentioned may be clearly understood by those skilled in the art to which the present invention belongs It will be possible.

BRIEF DESCRIPTION OF THE DRAWINGS The accompanying drawings, which are incorporated in and constitute a part of the specification, illustrate a preferred embodiment of the invention and, together with the description, serve to provide a further understanding of the technical idea of the invention, It should not be construed as limited.
1 is an example of a characteristic graph showing voltage-capacitance characteristics of a general organic material.
FIGS. 2A and 2B are graphs showing characteristic graphs showing voltage-capacitance characteristics of the ferroelectric organic material applied to the present invention. FIG.
FIGS. 3A and 3B are graphs showing characteristic graphs showing other voltage-capacitance characteristics of the ferroelectric organic material applied to the present invention. FIG.
4 is a plan view showing the positional relationship among various nozzles and tubular bodies in an air jet loom relating to the first embodiment of the present invention.
Fig. 5 is a schematic front view showing the positional relationship of various aspects of various nozzles and tubular bodies in an air jet loom usable in the present invention. Fig.
6 is a plan view showing a positional relationship between a sub nozzle and a body wing in an air jet loom usable in the present invention.
7 is a plan view showing the positional relationship between a sub nozzle and a body wing in an air jet loom usable in the present invention.
8 is a cross-sectional view showing an example of an apodo in an air jet loom usable in the present invention.
9 is a cross-sectional view showing another example of an apodo in an air jet loom usable in the present invention.
10 is a plan view showing an example of the weaving property in the present invention.
11 is a schematic longitudinal sectional view of an RTM molding apparatus according to a second embodiment of the present invention.
Fig. 12 is a schematic perspective plan view of the mold of the apparatus of Fig. 11 viewed from the upper surface side. Fig.
13 is a partially enlarged sectional view taken along the line AA in Fig.
Fig. 14 is a schematic plan view showing a process of enlarging the injection resin in the mold of Fig. 12; Fig.
15 is a schematic plan view showing an example of the expanded state of the injection resin in the conventional molding die for comparison.
16 is a schematic longitudinal sectional view of another RTM molding apparatus used for carrying out the method according to the second embodiment of the present invention.
Fig. 17 is a schematic perspective plan view of the mold of the apparatus of Fig. 16 viewed from the upper surface side. Fig.
18 is a partially enlarged sectional view taken along the line AA in Fig.
19 is a schematic plan view showing a process of enlarging the injection resin in the mold of Fig.
20 is a schematic view showing an example of a container according to the third embodiment of the present invention.
21 is a schematic view showing the arrangement of the container and the raw film according to the third embodiment of the present invention.
22 is a schematic view showing another arrangement example of the container and the raw film according to the third embodiment of the present invention.
23 is a schematic view showing an outer cylinder according to a third embodiment of the present invention.
24 is a schematic view showing a container according to a third embodiment of the present invention.
25 is a schematic view showing still another example of the container and the raw film according to the third embodiment of the present invention.
26 is a schematic view showing the relationship between a and b according to the third embodiment of the present invention.
27 is a schematic view showing a method for producing a carbonaceous film according to the third embodiment of the present invention.
28 is a schematic view for explaining stretching and carbonization and shrinkage of the film in the temperature raising process according to the third embodiment of the present invention.
Fig. 29 shows an example of a schematic view showing the rippling of the carbonaceous film according to the third embodiment of the present invention.
30 is a schematic view showing one or a plurality of ring-shaped members partially surrounding an outer circumferential surface, which is a constraining means at the outer peripheral end of the film according to the third embodiment of the present invention.
Fig. 31 is a schematic view showing a plurality of bar-like members arranged parallel to the winding core along the outer circumferential surface of the film, which is the constraining means at the outer peripheral end of the film according to the third embodiment of the present invention.
32 is a view showing a method of manufacturing a metal fiber in which a concave-convex shape is formed using a spur gear according to a fourth embodiment of the present invention.
33 (a) is an upper cross-sectional view of a metal fiber having a concavo-convex shape formed by passing through a spur gear, (b) is a side cross-sectional view of a metal fiber having a concavo-convex shape formed by passing through a spur gear, And is a perspective view of a metal fiber having a concavo-convex shape formed by passing through a gear.
34 is a view showing a method of manufacturing a metal fiber in which a concave-convex shape using a helical gear is formed.
Fig. 35A is a cross-sectional top view of a metal fiber having a concavo-convex shape formed by passing through a helical gear, Fig. 35B is a side cross-sectional view of a metal fiber having a concavo-convex shape formed by passing through a helical gear, And shows an example of a perspective view of a metal fiber having a concavo-convex shape formed by passing through a gear.
36 is a view showing a piezoelectric fiber for generating electrical energy according to an embodiment of the present invention.
37 and 38 illustrate a fabric including piezoelectric fibers according to one embodiment of the present invention.

Hereinafter, a preferred embodiment of the present invention will be described with reference to the drawings. In addition, the embodiment described below does not unduly limit the content of the present invention described in the claims, and the entire structure described in this embodiment is not necessarily essential as the solution means of the present invention.

Hereinafter, embodiments according to the present invention will be described with reference to the drawings.

1 is an example of a characteristic graph showing voltage-capacitance characteristics of a general organic material.

FIGS. 2A and 2B are graphs showing characteristic graphs showing voltage-capacitance characteristics of ferroelectric organic materials applied to the present invention. FIGS. 3A and 3B are graphs showing characteristic voltage-capacitance characteristics of ferroelectric organic materials applied to the present invention. It is an example.

First, the basic concept of the present invention will be described.

Examples of the ferroelectric material include inorganic materials such as PZT, SBT and BLT.

However, such an inorganic material has a problem in that the polarity (polarization) characteristic is deteriorated with time and the data holding time is set to be long.

In addition, such an inorganic ferroelectric is expensive, requires high-temperature treatment for forming a thin film, and requires expensive equipment for film formation.

In addition to the above-mentioned inorganic substances, various kinds of organic substances having ferroelectric properties are known. Among them, polyvinylidene (PVDF), a polymer, a copolymer or a terpolymer containing the PVDF may be mentioned, and an odd number of nylon, a cyano polymer, and a polymer or copolymer thereof may be mentioned .

PVDF and polymers, copolymers, and terpolymers of these PVDFs have been extensively studied as materials for organic semiconductors.

Information storage devices using ferroelectric polymers such as PVDF (poly (vinylidene fluoride)) or PVDF and TrFE (trifluoroethylene) PVDF-TrFE (poly (vinylidene fluoride-co-trifluoroethylene) Based process.

The ferroelectric polymer data storage structure consists of a metal / ferroelectric polymer / metal (MFM) capacitor in which a ferroelectric polymer thin film is sandwiched between two electrode arrays to enable charge signaling through the structure.

Recently, ferroelectric polymers have been used as gate insulators for forming capacitors, FeFETs (ferroelectric field effect transistors), and FeFET non-volatile memory device structures.

Since the coercive field required for PVDF and PVDF-TrFE is about 50 MV / m, it should be as thin as possible to reduce the operating voltage. The polarization behavior of the PVDF-TrFE film at temperatures below the Curie temperature is influenced by the degree of crystallinity. When the thickness of the film is 100 nm or less, the crystallinity of the film is drastically lowered, so that polarization also sharply decreases. The effective b-axis orientation of ferroelectric PVDF-TrFE crystals parallel to the electric field is critical for successful device performance. The sharp decrease in polarization in spin-cast PVDF-TrFE films is observed not only by a reduction in film thickness, but also by melting and recrystallization. The polarization dependence of the crystal orientation was also studied in Al / PVDF-TrFE / Au capacitors, where the Au bottom electrode was treated with SAMs to control the surface chemistry. It is generally known that crystal orientation formed on surfaces with polarity provides good polarization.

In order to sufficiently utilize the ferroelectric properties of the PVDF-TrFE thin film, it is necessary to maximize the degree of crystallization having effective orientation crystals for the electric field. Numerous studies have been conducted to control both the structure and the orientation of PVDF or PVDF-TrFE, including quenching, thermal gradients, solvent evaporation, etc. However, ferroelectricity Monolithic monocrystals preferably grown by the epitaxial crystallization method of the material are most useful than other methods.

Generally, in order to use a ferroelectric organic material as a material for a memory device, the organic material must have hysteresis polarity characteristics with respect to a voltage. However, in the case of the above-described PVDF, as shown in FIG. 1, the capacitance increases according to the applied voltage and does not have a hysteresis characteristic suitable for use in a memory device.

The inventors of the present application have found that PVDF has four kinds of crystal structures of alpha, beta, gamma and delta, and it has been confirmed that the crystal structure of beta phase has good hysteresis polarity. At this time, in order to determine the phase of the PVDF to be in the? -Phase, the PVDF is rapidly accelerated at a temperature of, for example, 60 to 70 占 폚, preferably about 65 占 폚, And the PVDF is determined to be the? Phase by the cooling method. However, the contents of these temperatures are only exemplary, and the contents of the present invention are not limited thereto.

FIG. 2 is a graph showing a polarization characteristic with respect to a voltage of a PVDF thin film formed according to the present invention. This graph shows a polarization characteristic of a PVDF thin film formed according to the present invention. The PVDF thin film has a β- And the upper electrode are measured by applying a predetermined voltage.

Particularly, FIG. 2A shows a case where the thickness of the PVDF thin film is about 10 nm, and FIG. 2B shows the case where the thickness of the PVDF thin film is about 60 nm. These thin films are subjected to spin coating at 3,000 rpm or less, A PVDF thin film having a predetermined thickness is formed on the hot plate, and then the temperature of the PVDF thin film is monotonically decreased on a hot plate. Then, the PVDF thin film is rapidly cooled, for example, at a temperature of 65 ° C. However, the contents of these temperatures are only exemplary, and the contents of the present invention are not limited thereto.

As can be seen from FIG. 2, the PVDF thin film produced according to the present invention has its capacitance value decreased as the applied voltage increases between about 0 V and about 1 V, and the applied voltage falls again between 0 and -1 V The capacitance value is increased, and the hysteresis characteristic is good.

FIG. 3 is a graph showing a change in the capacitance of the PVDF thin film formed over time according to time. FIGS. 3A and 3B correspond to FIGS. 2A and 2B, respectively.

As can be seen from FIG. 3, it was confirmed that the PVDF thin film produced according to the present invention was kept constant over a certain period of time without changing its capacitance value with time.

Therefore, as shown in FIGS. 2 and 3, the PVDF thin film according to the present invention has the following characteristics.

First, the PVDF thin film according to the present invention exhibits a capacitance value higher than a predetermined value at 0V. This means that the polarization of the PVDF thin film is maintained unchanged even at 0V, where no external voltage is applied. That is, the PVDF thin film according to the present invention can be usefully used as a material of a nonvolatile memory.

Second, the PVDF thin film according to the present invention exhibits memory characteristics even within a range of 1 V or less. That is, data can be recorded and erased at a very low voltage. That is, the PVDF thin film according to the present invention can be advantageously used to implement a memory device operating at a low voltage.

Thirdly, the PVDF thin film according to the present invention has a characteristic in which the capacitance value thereof is kept unchanged with time.

That is, the PVDF thin film according to the present invention has excellent data retention characteristics for maintaining a data value once recorded for a predetermined time or more.

In the above description, it is assumed that the ferroelectric material to which the present invention is applied is PVDF and PVDF is applied to a memory device. However, the present invention is not limited thereto.

In order to manufacture the ferroelectric layer using PVDF or PVDF-TrFE described above, complex processes and costs are required. Therefore, an efficient solution is required.

Accordingly, the present invention proposes a method of manufacturing a ferroelectric layer using PVDF or PVDF-TrFE using a fiber manufacturing method.

The ferroelectric layer fabrication method proposed by the present invention can be explained by four examples.

(1) First embodiment: Manufacturing method of ferroelectric layer using carbon fiber manufacturing method

(2) Second embodiment: Method of manufacturing ferroelectric layer using FRP manufacturing method

(3) Third embodiment: Method of manufacturing ferroelectric layer using graphite fiber manufacturing method

(4) Fourth embodiment: A method for manufacturing a ferroelectric layer using a metal fiber manufacturing method

Best Mode for Carrying Out the Invention Hereinafter, each embodiment proposed by the present invention will be described with reference to the drawings.

1st Example

The first embodiment proposed by the present invention relates to a method of manufacturing a ferroelectric layer using a carbon fiber manufacturing method.

4 is a plan view showing the positional relationship among various nozzles and tubular bodies in an air jet loom relating to the first embodiment of the present invention.

Fig. 5 is a schematic front view showing the positional relationship of various aspects of various nozzles and tubular bodies in an air jet loom usable in the present invention. Fig.

6 is a plan view showing a positional relationship between a sub nozzle and a body wing in an air jet loom usable in the present invention.

7 is a plan view showing the positional relationship between a sub nozzle and a body wing in an air jet loom usable in the present invention.

8 is a cross-sectional view showing an example of an apodo in an air jet loom usable in the present invention.

9 is a cross-sectional view showing another example of an apodo in an air jet loom usable in the present invention.

10 is a plan view showing an example of the weaving property in the present invention.

Hereinafter, for convenience of explanation, a method of producing carbon fibers will be described with reference to Figs. 4 to 10. Fig.

However, the carbon fiber manufacturing method described below can be applied to the ferroelectric layer manufacturing method according to the present invention.

In the present invention, when an unidirectional carbon fiber fabric is woven using a carbon fiber yarn having a fineness of 400 to 6,000 tex as a warp yarn and an auxiliary fiber having a fineness of 1/5 or less of the carbon fiber yarn as a weft yarn, Can be used.

In the case of producing a carbon fiber fabric using a shuttle loom or a looper loom, (1) when a shuttle loom or a looper loom is used, there is an upper limit of the physical speed for the weft insertion by the shuttle or rapier, 2) With regard to the insertion of the weft yarn, there was a problem that when the weft yarn was weighed at a high speed, the shuttle or the rapier and the warp yarn were in direct contact with each other, and the carbon fiber yarn was easily fuzzled.

However, by using an air jet loom, it is not affected by the physical speed of a shuttle, a rapier, or the like, and scratches with the warp, shuttle, rapier, or the like are essentially not generated.

If a water jet loom is used here, there is a possibility that the sizing agent (mostly water-soluble resin composition) previously attached to the carbon fiber yarn, which is a direct carbon fiber yarn, is unevenly separated and adhered, There is a problem.

In weaving using such an air-jet loom, the stopping angle of the handle at the opening of the handle is within a range of 0 to 50 degrees, preferably 0 to 25 degrees, more preferably 0 degrees. The smaller the stop angle, the better.

The heel stop angle means a position at which the movement (displacement) of the opening and closing port of the heddle is successively changed to the displacement when the one cycle of the repeated operation of the loom for inserting the weft yarn is divided by the rotation angle of the motor main shaft (crank) It refers to the angle of motionless range.

 When a shuttle loom or a rapier loom is used, a shuttle or rapier, which is a weft inserting means, and a warp yarn group are locally contacted with each other, and the tension applied to each of the warp yarns loaded at the time of weaving can not be made uniform .

In addition, in order to insert a shuttle, reef, or the like into the lower part, the opening of the hood must be large and the hood must be kept open while the shuttle or lever is moving. Therefore, for example, in a general rapier loom, the stopping angle of the hand becomes 150 to 220 deg. As a result, the movement of the weaving becomes intermittent (discontinuous) motion, and the warp becomes unstable due to the tension or loosening of the warp, and it becomes one of the causes for making the tension in each warp uneven.

Because of this point, the difference in the length of the warp yarns in the resulting carbon fiber fabric is not more than 0.15%, and the coefficient of variation of the warp length is not more than 8%, and the stopped warp yarns start to move Since the carbon fiber yarn and the scratches of the heald are so large that a lot of fluffs are generated, it is difficult to obtain a durable fabric.

On the other hand, in the air jet loom, it is not necessary to keep the open state of the handle long. That is, by using the air jet loom, there is no physical contact between the weft inserting means and the warp group, and there is no need to stop the heald for a long time in order to maintain the open state. And the tension applied to each of the warp yarns loaded at the time of weaving can be made more uniform. As a result, a carbon fiber fabric having a difference in length of the warp yarn of 0.15% or less and a variation coefficient of the warp length of 8% or less can be easily obtained. More preferably, the difference in length of the warp yarn is 0.1% or less, more preferably 0.05% or less. A more preferable coefficient of variation is 6% or less, more preferably 4% or less. The difference in the lengths and the variation coefficient of the warp in the above range can suppress the irregularities of the fabric when the fabric is stretched on the floor to a minimum so that the appearance quality is excellent and when the obtained fabric is molded into CFRP, do. The difference in length of the warp yarns and the variation coefficient of the warp yarn length are measured in the following order.

(a) The carbon fiber cloth is allowed to stand at an unsprung time of 5500 mm to prevent loosening of the fabric.

(b) As a measurement standard, cut one place vertically to the longitudinal direction of the fabric.

(c) From the measurement standard, measure 5,000 mm for each of the warp yarns at both ends in the fabric width direction, and cut with a line connecting the points. At the time of measurement, the fabric is placed under an unsprung weight so that the fabric is not loosened, and the length of 5000 mm is measured with a long scale.

(d) While disassembling the fabric, the warp yarns are sequentially pulled out at intervals of 5 from the entire width of the fabric.

(e) Measure the length of the warp yarn to 0.1 mm. At the time of measurement, the tension is applied to the warp so that the warp yarn can not be warped.

(f) Calculate the difference between the maximum value and the minimum value of the warp length. The value obtained by dividing the calculated difference by 5000 mm and multiplying by 100 is taken as the difference in the warp length (unit:%).

(g) Calculate the standard deviation and mean value of all the values of the warp length measured. The calculated standard deviation is divided by the average value and multiplied by 100 is used as the coefficient of variation (unit:%).

Originally, air jet looms have been used in the industrial manufacture of bi-directional fabrics of glass fibers, but this is not the only reason why the glass fiber used has a high elongation at break of about 4%, which makes it difficult for fluff. In addition, since the fabric of the glass fiber used has a fineness of, for example, 8 to 100 tex and has a straight density (number of warp yarns, number of weft yarns), the amount of air injected from the weft yarn is minimized (FUTURE TEXTILES, p81-84, Horita-ruo, Textile Co., Ltd.), and the condition that the weaving of the weft (curvature) does not become present. On the other hand, in the present invention, the carbon fiber yarn used has a tendency to be fluffy as compared with glass fibers, and also has a stepwise fineness, and the fabrics to be produced are unidirectional fabrics. do.

Nevertheless, in the present invention, the unidirectional carbon fiber fabric is weaved with an air jet loom, and further, the unfavorable obstacle described above is solved to realize the weaving with an air jet loom.

In the carbon fiber fabric produced in the present invention, it is preferable that the warp density is 1 to 8 / cm and the weft density is 0.4 to 8 / cm.

More preferably a warp density of 2 to 6 yarns / cm, a weft yarn density of 1 to 6 yarns / cm, more preferably a warp density of 3 to 5 yarns / cm and a weft density of 2 to 5 yarns / cm . If the warp density is too small, not only the morphological stability of the carbon fiber fabric is deteriorated but also the warp gap becomes too large and the weft insertion efficiency of the air jet loom is excessively lowered.

On the other hand, if the warp density is too large, the number of fluffs due to scratching of the carbon fiber yarn increases, and the quality of the carbon fiber fabric may be deteriorated. In addition, if the weft density is too small, the morphological stability of the carbon fiber fabric is deteriorated, and the handleability of the resultant fabric tends to deteriorate. On the other hand, if the weft density is too large, it may be difficult to make the production speed of the carbon fiber fabric at a high speed, and sometimes the warp of the weft yarn can not be completely suppressed.

The method of producing a carbon fiber fabric of the present invention is suitable for producing a carbon fiber fabric having a warp gap of 0.1 to 0.8 mm, preferably 0.15 to 0.6 mm, more preferably 0.2 to 0.5 mm. If the clearance between the warp yarns is too small in the resulting fabric, there is a case where the napping due to scratching of the carbon fiber yarn is increased and the quality of the carbon fiber fabric is impaired. In addition, the carbon fiber fabric is woven, , The impregnation property of the matrix resin may be hindered when CFRP (carbon fiber reinforced plastic) is molded.

In the case of using an air jet loom, a sub nozzle (which will be described later in detail) protruding between carbon fiber yarns at the time of weaving is peeled from the carbon fiber yarn, .

On the other hand, when the clearance between the warp yarns is too large, the napping is suppressed, but the weft insertion efficiency is lowered. Further, when CFRP is molded, the resin rich portion is formed to be large and the mechanical properties of CFRP There may be a case where it is lowered.

In the present invention, a tubular body having both open ends is disposed on the side opposite to the weft insertion side (hereinafter referred to as " semi-weft insertion side ") of the woven carbon fiber cloth, It is preferable to let the uneven weft yarn pass from one opening of the tubular body to the other opening. The loosening of the weft can be prevented by the friction between the weft and the inner wall of the tubular body. The tubular body may be one in which the axis is curved in addition to the straight line, and the tubular body in which the axis is straight is arranged such that the axis intersects (does not become parallel to) the direction of the weft.

Air is fed from at least the main nozzle 12 and the subnozzles 2a to 2b and the weft yarn 14 is fed from the weft insertion side A to the half weft yarn insertion / (B) while passing through the body wing group (1a). After the weft is transversed, the body (7) is bobbled to warp the warp and the weft (14).

Here, the main nozzle is a nozzle which is disposed at the weft insertion side of the weaving machine and which first applies pressure to the weft yarn to be weighed. In order to further continuously highlight the weft yarn being displayed by the main nozzle, .

As the air jet loom used in the present invention, one main nozzle 12 is disposed on the weft insertion side A and a plurality of sub nozzles 12 are provided between the weft insertion side A and the half weft insertion side B 2a, 2b, ...) are arranged at intervals of one fabric width of 2 to 15 cm.

The preferred spacing of sub-nozzles is one per fabric width of 3-12 cm, and more preferably one per fabric width of 4-10 cm. The total number of sub nozzles varies depending on the fabric width, but is preferably in the range of 7 to 30 when the fabric width is 100 cm and in the range of 23 to 105 when the fabric width is 350 cm.

The arrangement of the plurality of sub nozzles 2a, 2b, ... is such that the width of the body inlet of the air jet loom is wide like the range described below (within the range of the body inlet width of 100 to 350 cm) It is desirable to make the distance between the sub nozzle at the shortest end of the half weft insertion side B and the sub nozzle adjacent thereto shorter than the distance between the sub nozzle at the shortest end in the side A and the sub nozzle adjacent thereto Do.

More specifically, the arrangement intervals L2 and L3 of the sub-nozzles are not widened toward the semi-weft insertion side B from the arrangement interval L1 between the sub-nozzles on the weft insertion side A .

More preferably, it is preferable to dispose the subnozzles so that the intervals between the subnozzles are shortened in accordance with the weft insertion direction. When the plurality of sub nozzles 2a, 2b, ... are arranged in this manner, not only the air from the main nozzle 12 can be utilized efficiently but also the weft in the weft insertion side B is stabilized And the weft insertion itself can be performed stably for a long period of time. Of course, the relationship between the arrangement distances L1 to L3 of these sub-nozzles is appropriately selected in accordance with the fabric width. For example, L1> L2> L3 or L1> L2 = L3.

In the present invention, as the air jet loom, a plurality of main nozzles arranged on the weft insertion side may be used. For example, it is preferable to use another main nozzle (auxiliary main nozzle 13) on the upstream side of the main nozzle 12 arranged on the weft inserting side A in the weft direction. More preferably, air is sprayed substantially simultaneously from each of the main nozzles 12 and the auxiliary main nozzles 13 to desirably weft the wefts. By using such an auxiliary main nozzle 13, there is no need to spray sudden air to the weft waiting for waiting for the next insertion. In other words, in the case where there is only one main nozzle, it is inevitable to increase the air pressure in order to spray air at one place of the weft. However, when the auxiliary main nozzle 13 is used in combination and a plurality of main nozzles are used, the air is sprayed at a plurality of points of the weft yarn, so that the air pressure can be lowered. As a result, it is possible not only to suppress the weft yarn breakage, the weft split, the scattering, the fuzz of the weft yarn, etc., but also the weft yarn which is difficult to be visually inspected, and can freely choose the weft yarn. In addition, spraying air at substantially the same time means spraying air within a range of 20 占 within the main axis (crank) angle of the loom.

Further, in the air jet loom, it is preferable that each sub nozzle is arranged so that the center of the sub nozzle and the center of the body blade are on substantially the same straight line parallel to the longitudinal direction of the fabric. In other words, as shown in Figs. 6 and 4, which are partial enlarged views of the air jet loom showing the positional relationship between the sub nozzle and the body wing, the center of the sub nozzle 2 for jetting air and the center of the body wing 1 It is preferable to arrange the fabric so as to be arranged substantially at the same position with respect to the width direction of the fabric.

Further, in the present invention, the fact that the center of the sub nozzle and the center of the body wing are on substantially the same straight line parallel to the longitudinal direction is not limited to the state that they exist on the same straight line completely parallel to the longitudinal direction, Incidentally, as shown in Fig. 7, it is also assumed that there is a slight deviation as long as it does not cause a problem as shown in Fig. More specifically, it indicates that the center D1 of the sub nozzle 2 and the center D1 of the body wing 1 are within a range of 0 to 3 mm. More specifically, D1 is represented by the distance between the center line 4 of the sub nozzle with respect to the width direction of the fabric and the center line 3 of the body wing with respect to the width direction of the fabric. Since the sub nozzle 2 scrapes the warp yarn 5b (carbon fiber yarn) if the center of the sub nozzle 2 and the center of the body wing 1 are not arranged on substantially the same straight line, The occurrence of fluff in the fiber yarn can not be suppressed in some cases. That is, if the center of the sub nozzle 2 and the center of the body wing 1 are disposed on substantially the same straight line, scratching with the warp yarn 5a can be suppressed.

The body wing thickness of the body is preferably in the range of 0.1 to 2 mm, preferably 0.3 to 0.8 mm, more preferably 0.4 to 0.7 mm. If the thickness of the body wing is too small, the difference in the physical dimensions of the sub nozzle 2 becomes too large, and the sub nozzle 2 may protrude too much and scratch the warp yarn 5. On the other hand, if the thickness of the body wing is too large, the weight of the body itself becomes too large, the thickness of the wing 5 between the body wings 1 becomes narrow and the body wing 1 becomes too strong There are cases where it is scrubbed.

It is preferable that the body stroke stroke amount D2 in the air jet loom is in the range of 50 to 150 mm, preferably 60 to 130 mm, and more preferably 70 to 90 mm. If the body stroke stroke amount D2 is too small, there is a case that a space for weft insertion can not be formed.

On the other hand, if the body stroke stroke amount D2 is too large, the motion of the body stroke itself becomes too large, which may impede the speeding up of the present invention. In addition, the carbon fiber yarn and the body wing tend to be scratched, The lint from the yarn can not be suppressed in some cases. The body stroke stroke amount D2 refers to the straight line distance between the most advanced body position (at body scoring) and the most retracted body position (at the time of weft insertion).

Further, it is preferable that the handle opening amount D3 in the air jet loom is in the range of 10 to 75 mm, preferably 20 to 65 mm, more preferably 30 to 60 mm. When the helical opening amount D3 is in this range, scratches between adjacent warp yarns are minimized at the time of weaving at a high rotation speed, and fluffing of the carbon fiber yarn can be suppressed.

More specifically, if the opening amount is too large, the absolute value of the warp tension becomes high, so that the napping period of the carbon fiber yarn becomes large, and if the opening amount is too small, the formation of the bottom (space for passing the weft) Not only the insertion can be stably performed but also the warp of the warp yarn and the weft yarn become relatively strong and fluff may be generated. The hand opening amount D3 refers to a straight line connecting the position of the mail at the top of the opening with the position of the mail at the bottom of the closed bottom dead center.

In the air jet loom, it is preferable to provide a push bar that at least partly restrains the opening of the warp yarn introduced into the head. As shown in Figs. 8 and 9, the push bars 8a and 8b are provided between the idling rolls 11a and 11b and the head 6, So that the opening of the warp yarn 5c is smaller than the opening formed by the original oblique incisions 9a and 9b in the absence of the push bars 8a and 8b And the like. In other words, the opening by the warp yarn is suppressed to be smaller. By suppressing at least partly the opening of the warp yarns introduced into the heald, it is possible to further reduce the scratches between adjacent warp yarns 5c due to the opening movement.

8, the whole of the plurality of warp yarns 5c may be depressed to suppress the entire opening. As shown in Fig. 9, a plurality of warp yarns 5c may be provided, It is also possible to suppress some of the openings by pressing some of them.

The push bars 8a and 8b may be any ones capable of suppressing the openings. Examples of the push bars 8a and 8b include free rolls (especially those having a surface checkerboard pattern), fixed rollers And the like. From the viewpoint of minimizing the scratches on the warp and pushing bars, it is preferable that the free-rotation rolls have a checkered shape.

In order to maximize the above effect, it is necessary to provide an easing mechanism (corresponding to the easing rolls 11a and 11b capable of changing positions in Figs. 5 and 6) desirable. Even when the warp length D4 from the position where the warp starts to the heald to the heald is shortened in order to reduce the scratches between the adjacent warp yarns 5c due to the opening motion, It is possible to realize a uniform warp tension. This effect is particularly remarkable when the warp length D4 from the point where the warp starts to the heald to the heald is 10 times or less the opening amount of the heald. It is more preferable that the number of the eccentric mechanisms is the same as the number of the hands, and the eccentric mechanism is separately used for the respective hands. This easing mechanism may be a negative pole type in which the easing rolls 11a and 11b are caused to move by the tension of the warp by means of a spring or the like, but it is preferable that the eccentric type is an active mode in which the loom is forcibly moved by loom driving power or a separate motor. If it is an aggressive system, it can contribute to lint reduction even at a higher speed.

In the present invention, the width of the body inlet of the air jet loom is preferably 100 to 350 cm. More preferably in the range of 130 to 310 cm, and more preferably in the range of 150 to 260 cm. When a shuttle loom or a looper loom is used in general, there is a limit to the width of the loom, that is, the width of the body inlet of the loom, because a shuttle or looper, which is a weft insertion means,

On the other hand, in the air jet loom, since the weft yarns are inserted by air, the width of the body inlet can be easily widened simply by adding the sub nozzle in the width direction. That is, in order to maximize the effect of using an air jet loom, it is preferable to weave the fabric with a width as wide as the above range.

When the width of the body inlet of the air jet loom is as wide as the above range, ear structures 19c are formed in the body inlet widths other than both ends of the body inlet width to form a plurality of carbon fiber fabrics 18a, 18b ... . Generally, the ear tissue is formed only at both ends of the body entrance width to obtain a carbon fiber fabric of one width. However, ear tissues 19c ... are also formed within the body entrance widths other than both ends, , 18b, ...) are simultaneously obtained, the productivity can be further improved. More preferably, it is in the range of 2 to 12 widths, and more preferably in the range of 3 to 7 widths. (For example, an ear tissue device, a duplex device, a "cloker" device, and the like) for forming the ear tissue within the width of the body entrance is required, In some cases, the device arrangement may be restricted.

Further, in weaving using an air jet loom, after the weft is inserted and the weft is opened and closed to weave the carbon fiber fabric, the weft yarn can be tuck-in in the fabric width. By folding the yarn back into the fabric width with the jaw device, it is possible to obtain a yarn-free fabric as if woven with a shuttle loom. The unidirectional carbon fiber fabric having the taut ear structure is used for repairing and reinforcing concrete, for example, when the unidirectional carbon fiber fabric is applied by applying the resin to the concrete, the amount of the resin to be applied is minimized can do.

In the present invention, the unidirectional carbon fiber fabric having the warp yarns and the auxiliary fibers as the weft yarns is woven into a carbon fiber yarn having a fineness of 400 to 6,000 tex. If the fineness of the carbon fiber yarn used in the present invention is too small, the warp density of the warp yarn becomes too dense, the number of fluffs of the carbon fiber yarn becomes large, and the quality of the carbon fiber fabric is deteriorated. On the other hand, if the fineness of the carbon fiber yarn used is too large, the gap of the warp yarn becomes too large, and the weft insertion efficiency of the air jet loom is lowered.

From another viewpoint, if the fineness of the carbon fiber yarn is in the above range, the carbon fiber yarn can be obtained at low cost. Weaving with an air jet loom using this range of carbon fiber yarn means further improving the productivity, and the effect of the present invention is greatly exerted.

The auxiliary fibers used in the present invention have a fineness of 1/5 or less, preferably 1/20 to 1/500, and more preferably 1/100 to 1/250, of the fineness of the carbon fiber yarn as the warp yarn. If the fineness is too large, the mechanical properties are lowered by bending the carbon fiber yarn in the unidirectional fabric. On the other hand, if the fineness is too small, it means that the strength of the auxiliary fibers is too low, and the weft yarn breakage often occurs at the time of weaving.

When the weft insertion is performed by an air jet loom, when a carbon fiber yarn is used in the weft yarn, the carbon fiber yarn easily fuzzles and the generated napping may clog the loom components such as nozzles. If the unidirectional fabric using such auxiliary fibers is used as the weft yarn, the problem does not occur even when the weft insertion is performed by the air jet loom, and the productivity of the carbon fiber fabric is not deteriorated.

Examples of such auxiliary fibers include inorganic fibers such as glass fibers and metal fibers (excluding carbon fibers), aramid fibers, PBO fibers, nylon fibers, polyester fibers, polyvinyl alcohol fibers, polyethylene fibers, polypropylene fibers , Polyphenylene sulfide fibers, and cotton fibers. Of these, inorganic fibers other than carbon fibers are preferable, which can minimize the shrinkage in the width direction of the carbon fiber cloth, In order to minimize the occurrence of fuzz, glass fibers are particularly preferable.

As the auxiliary fiber, a spun yarn, a twist yarn, an entangled yarn, or a covering yarn (composite yarn wound around the yarn) is preferable from the viewpoint of the non-elongation of the yarn by the jet of air. As specific examples, it is preferable that the yarn is a spun yarn of glass fibers and / or organic fibers, or an entangled yarn of a glass fiber and / or an organic fiber (preferably a tassen yarn). By using such an auxiliary fiber, it is possible to stably fix the birefringence caused by the air jet in comparison with a simple filament yarn.

Further, the coefficient of friction with the carbon fiber yarn after weaving can be increased, and the weft yarn as the problem of the present invention can be minimized. As another specific example, a covering yarn covered with a filament yarn of an organic fiber by inspecting a glass fiber is also preferable. In covering yarns, even if both the glass fiber and the organic fiber are in filaments, it is possible to suppress the yarn splitting and the weft lint of the weft yarn by the covering process, and to stabilize the birefringence by the air jet.

Preferable examples of the organic fiber used herein include low melting point polymer fibers (fibers composed of copolymerized polyamide, copolymerized polyester, polyolefin, and copolymer polyolefin). When such a low melting point polymer fiber is used, it is possible to fill the carbon fiber cloth and the auxiliary fiber by heating the obtained carbon fiber cloth, and the obtained carbon fiber cloth has an excellent form in which the weft is straight without being warped It is easy to maintain.

From another viewpoint, in the present invention, it is preferable to use a carbon fiber yarn having a measured tensile strength of 4,000 MPa or more, preferably 5,000 MPa or more. If the tensile strength is in this range, it is possible to produce a carbon fiber fabric which is less prone to fuzz and is of high quality.

There is no upper limit to the tensile strength, and it is preferable that the upper limit is high, but it is considered that the upper limit of 7,000 MPa is considered in the present technical range.

Conventionally, in the shuttle weaving machine or the looper weaving machine, which has been used for manufacturing carbon fiber fabrics, since the weft yarn is directly pulled and inserted, tension can be applied to the weft yarn itself. In an air jet loom, which is relatively difficult to present but can not impart tension directly to the weft in the weft insertion, this problem is likely to become present. However, in the present invention, it is preferable to solve such a problem by imparting tension to the weft yarn before and / or after weaving. Hereinafter, this will be described in detail with reference to FIG.

At first, a separate structure 19b is formed by the same weft yarn 14 as the weft yarn constituting the carbon fiber fabric, at the same time, at the end of at least the half-weft insertion side B of the woven carbon fiber fabric. At this time, the woven carbon fiber fabric or the separate fabric 19 is continuously conveyed downstream, and on the downstream side, the weft yarn is cut between the separate fabric 19b and the carbon fiber fabric 18b, The carbon fiber fabric is partially separated and twisted to separate tissues. Of course, like the half-weft insertion side B, a separate weave 19a is formed by weaving the same weft yarn 14 as the carbon fiber fabric at the end of the weft insertion side A and, at the same time, Other tissues may be weighed within other body inlet widths and twisted to separate tissues. By firing these separate pieces 19a, 19b ..., tensile force can be applied to the weft yarns 14 in the carbon fiber fabrics 18a, 18b, 18c ..., and the weft- Can be obtained more easily.

As a method of applying a twist to the separate tissue, for example, a guide having a hole is used and the guide is rotated by passing another tissue through the hole, or the upper and lower surfaces of separate tissues are sandwiched by the endless belt, Or the like can be exemplified. Among them, the former is preferable from the standpoint that the apparatus is simple and easily mounted on the air jet loom.

In order to apply the tension to the weft yarn 14, the weft yarns 14a and 14b may be separately formed so as to widen the distance between the separate fabrics 19a and 19b and the carbon fiber fabrics 18a and 18b, It is desirable to guide the organization.

As such a method of guiding the separate tissues, there is exemplified a method of increasing the kink in the downstream side or guiding the separated tissues separated from the downstream side in the direction of retracting from the carbon fiber cloths 18a, 18b . In order to exhibit the effect more efficiently, the distance between the separate tissues 19a and 19b and the carbon fiber fabrics 18a and 18b is preferably set so that the distance between the separate tissues and the carbon fiber fabric is widened before the weft is cut The method of increasing the twist is desirable.

Further, in this embodiment, it is preferable that the unidirectional carbon fiber fabrics 18a, 18b, 18c, ... are of a plain weave, twill or water weave structure, and the separate weave structures 19a, 19b ... are plain weave, . Particularly, in order to impart tension to the weft yarns as described above, it is preferable that the warp yarns 17 and the weft yarns 14 of the separate structure are often stuck or strong. Thus, it is particularly preferred that the separate tissue is a leno tissue. The warp yarns 5 of the unidirectional carbon fiber cloths 18a, 18b and 18c are carbon fiber yarns having a fineness of 400 to 6,000 tex, but the warp yarns 17 of the separate structures 19a, 19b, It is not necessary to be a fiber yarn and it is preferable to use the same one as the auxiliary fiber used in the above-mentioned weft yarn.

In addition, when the above-described fibers described as auxiliary fibers, instead of carbon fiber yarns, are used as separate warp yarns 17, the shrinkage rate upon heating is so small that contraction of the carbon fiber fabric can be minimized, Is preferably used as the warp yarn 17, but it is preferable to use the aramid fiber as the warp yarn 17 from the viewpoint of minimizing yarn breakage.

In order to impart tension to the weft yarn before and / or after weaving, as shown in Figs. 4 and 5, a tubular member 15a having both ends open at the half-weft yarn insertion side of the woven carbon fiber fabric b and the weft yarn 14 inserted to form the carbon fiber fabric is passed from one opening (inlet) to the other opening (outlet) of the tubular bodies 15a, b.

Specifically, in the embodiment shown in Fig. 4, the curved tubular body 15a is disposed on the other side (the side where the weft is not inserted) of the body 7, and the weft yarn 14 The weft yarn 14 passes through the tubular body 15a by blowing air toward the side from the side of the body using the stretch nozzle 16 or the like. 5, the straight tubular member 15b is disposed so as to intersect the non-running direction of the weft (that is, not to be parallel to the non-running direction) and also to the side of the body to be wefted , The weft yarn 14 passes through the tubular body 15b by blowing air toward the outlet of the tubular body by using a stretch nozzle (not shown) or the like to the weft yarn 14 which has reached the end of the body entrance width . In this tubular body, not only the jetting of air by the stretch nozzle, but also the pressure in the tubular body is reduced, the weft can be passed through the tubular body more efficiently and reliably.

In order to impart tension to the weft yarns before and / or after weaving, the weft yarns inserted may be directly held by clamp means (not shown) disposed on the half-weft yarn insertion side (B). It is preferable that such a clamping means moves in synchronization with a signal from a detector which detects that the weft is inserted. In addition, a force in a direction to return to the weft insertion side (A) may be imparted to the weft yarn inserted immediately before closing movement of the heald. According to this aspect, it is also possible to impart tension to the weft yarn before and / or after weaving. As a method for imparting a force in the direction of returning to the weft, there is a method in which the guide position for passing the weft, which is disposed on the weft insertion side, is moved in the direction in which the weft is returned for every bobbin thread, And a method in which tension is always given in the direction in which the weft yarn is returned, except when the weft yarn is invisible. From the point that the device is simplified, the former is preferable.

Further, in the present invention, it is preferable to bond the resin to the carbon fiber fabric to be produced in a linear or point-like form.

If the resin adheres to the fabric, the shape of the carbon fiber fabric can be stabilized and the handling property of the carbon fiber fabric can be improved.

The resin may be adhered to and adhered to the carbon fiber fabric in any form such as fiber form, particle form, emulsion form dissolved or dispersed in water, or dispersion form. Among them, it is preferable to use a solid fiber type or solid particle type resin from the viewpoint of easy adhesion and from the viewpoint of the above-described functional development, and to adhere it to the fabric. In the case of such a fiber form, the carbon fiber yarn or the auxiliary fiber may be aligned and woven together and adhered, or the composite yarn may be formed by using a carbon fiber yarn, auxiliary fibers, covering, They may all be woven and bonded. Particularly, in the case of improving the handling of fabrics, it is effective to insert the fibers in the form of a weft in a straight manner, or to insert the composite yarn into a composite yarn by covering or combining with carbon fibers or auxiliary fibers. In the case of using a resin in the form of a particle, a solid particulate resin may be applied to the surface of the woven carbon fiber fabric and adhered. Alternatively, the dispersion may be applied and adhered in a state of being dispersed in a liquid such as water do.

The resin to be adhered to the carbon fiber fabric is not particularly limited as long as it improves the handling properties of the carbon fiber fabric and / or improves the mechanical properties of the composite material using the carbon fiber fabric. A thermosetting resin and / or a thermoplastic resin may be suitably selected Can be used. From the standpoint of improving the handling of fabrics, it is preferably at least one selected from the group consisting of epoxy, unsaturated polyester, vinyl ester, phenoxy, polyamide, polyester, polyvinylformal and polyolefin, , And polyamide are particularly preferable. It is preferable that such a resin has a melting point (Tm) (glass transition point + 50 deg. C) measured at a temperature raising rate of 20 deg. C / min from the absolutely free state by DSC (differential scanning calorimetry) at 150 deg. On the other hand, the melting point (Tm) is preferably 50 ° C or more from the viewpoint of handleability in handling the carbon fiber fabric under normal circumstances.

As a method of adhering such a resin, the carbon fiber cloth may be heated in contact with a heat source, or the adhered resin may be adhered to the fabric by heating the carbon fiber cloth and the heat source without contacting them. For example, when a carbon fiber fabric is produced at a high speed of 1 m / min or more, it is preferable to heat the carbon fiber fabric and the heat source in contact with each other. More preferably, the method of heating by bringing into contact with a heat source and the method of heating without contacting are preferably used together. Since the present invention uses carbon fibers having excellent thermal conductivity, it is possible to efficiently bond the resin even at a high speed of 1 m / min or more, for example, by disposing a plurality of the heat sources successively in the manufacturing process of the carbon fiber fabric . Examples of such a heat source include a heating roll and a hot plate when brought into contact with each other. When not in contact, a radiation heat heater such as far-infrared rays or near-infrared rays can be used.

Further, in order to further increase the productivity, the woven carbon fiber fabric is wound once with a predetermined length L1, the wound carbon fiber fabric is divided into a product length L2 which is not more than half of the predetermined length L1, desirable. Since the carbon fiber fabric obtained in the present invention is mainly used as a reinforcement material of CFRP, if it is packed in a box without being wound, wrinkles or bending are generated, thereby damaging the carbon fiber yarns or disrupting the arrangement (straightness) . For this reason, it is preferable to make the rolled aspect into a product form.

On the other hand, on the assumption that winding is carried out, even if a high production speed is attained by the present invention, if the winding length is short, it is necessary to frequently stop the loom, and the effect of the present invention can not be effectively exhibited. Therefore, as described above, the predetermined length L1 having a length twice or more of the length L2 of the product is continuously woven, and once wound on an intermediate core (for example, a core tube or a steel tube) different from the product core . By doing so, the periodic frequency of the loom can be minimized and a higher production speed (number of rotations of the loom) can be achieved. It is preferable that the carbon fiber cloth of the predetermined length L1 wound once is divided into the product length L2 which is not more than half of the predetermined length L1 in the separate process and is wound again.

The predetermined length L1 is more preferably at least three times the product length L2, and more preferably at least five times. From another viewpoint, the predetermined length L1 is preferably 300 m or more, more preferably 500 m or more, and more preferably 700 m or more.

In the present invention, it is preferable that the warp yarns are guided to the loom directly by arranging the warp yarns as the warp yarns from each bobbin. When the warp yarns are guided to the loom by arranging the warp groups on the sheet after the bobbins are regularly or partially sifted (after beading), in particular, when the yarns are of the fineness of 400 to 6,000 tex, Thickness irregularity in the fiber yarn is likely to occur, and there is often a difference in yarn length between yarns. Due to this, the loosened carbon fiber yarn may be distorted during the weaving process to disturb the arrangement (straightness). In addition, unevenness may be generated in the obtained fabric itself, and the quality of the fabric may be lowered. The above problem is solved by directing the carbon fiber yarns from the bobbins to the loom directly and without weaving the regular diameter or partial regular diameter.

As described above, the method of manufacturing carbon fibers has been described in detail above, but such a method can be applied to the ferroelectric layer manufacturing method.

That is, in order to determine the phase of PVDF to be in the? -Phase, the PVDF is rapidly heated at a temperature of, for example, 60 to 70 占 폚, preferably about 65 占 폚, And the PVDF is determined to be in the? -Phase by a cooling method. By applying this method to the carbon fiber manufacturing method described above, the ferroelectric layer can be easily manufactured. However, the contents of these temperatures are only exemplary, and the contents of the present invention are not limited thereto.

SECOND EXAMPLE

The second embodiment proposed by the present invention relates to a method of manufacturing a ferroelectric layer using an FRP manufacturing method.

11 is a schematic longitudinal sectional view of an RTM molding apparatus according to a second embodiment of the present invention.

Fig. 12 is a schematic perspective plan view of the mold of the apparatus of Fig. 11 viewed from the upper surface side. Fig.

13 is a partially enlarged sectional view taken along the line A-A in Fig.

Fig. 14 is a schematic plan view showing a process of enlarging the injection resin in the mold of Fig. 12; Fig.

15 is a schematic plan view showing an example of the expanded state of the injection resin in the conventional molding die for comparison.

16 is a schematic longitudinal sectional view of another RTM molding apparatus used for carrying out the method according to the second embodiment of the present invention.

Fig. 17 is a schematic perspective plan view of the mold of the apparatus of Fig. 16 viewed from the upper surface side. Fig.

18 is a partially enlarged sectional view taken along the line A-A of Fig.

19 is a schematic plan view showing a process of enlarging the injection resin in the mold of Fig.

Hereinafter, for convenience of explanation, the FRP manufacturing method will be described with reference to Figs. 11 to 19. Fig.

However, the FRP manufacturing method described below can be applied to the ferroelectric layer manufacturing method according to the present invention.

11, the RTM molding apparatus 21 is provided with a top mold 24 and a bottom mold 25 as a molding die 23 for forming the cavity 22 and the top mold 24 is supported by a press mechanism 26 So that it can be opened and closed. In the cavity 22, a preform 27 formed of a laminated body of a reinforcing fiber base material, for example, previously formed into a predetermined shape, is disposed. The upper mold 24 is engaged with the lower mold 25 in a state where the preform 27 is disposed in the cavity 22 and the resin for constructing the FRP is supplied from the resin supply path 28. The preform 27 The resin is injected into the cavity 22 from the resin injection ports 29 as a plurality of resin injection paths opened to face one surface (two upper surfaces) of the preform 27 and impregnated into the reinforcing fiber base material constituting the preform 27. The resin injection port 29 is opened and closed by, for example, a pin-shaped valve body 210, and the periphery of the cavity 22 is sealed with a sealing material 212.

The molding die 23 is heated and cooled, for example, by a heating medium flowing through the heating medium flow passage 211. When the resin is injected, the molding die 23 is heated to impregnate the resin well. After the resin impregnation, Natural freezing is also possible), and the infiltrated and impregnated resin is cured to produce a predetermined FRP molded article.

The plurality of resin injection ports 29 are arranged, for example, on one side of the preform 27 in a plan view as shown in FIG. The preform 27 is formed so as to be larger than the outer shape 221 of the product to be molded in plan view and the inner side of the preform 27 (the inner side than the outer shape 221 of the two products) Flow resistance region 222 which makes it difficult to partially flow the resin spreading toward the outer peripheral portion of the preform 27 from the outer shape of the preform 27 at the position outside the product with respect to the outer shape 221 of the product to be molded Respectively. 13, the high flow resistance region 222 is formed so that the thickness of the outer circumferential portion of the preform 27 at the position outside the product with respect to the outer contour 222 of the product is made to be the molding die 23 (Lower mold 24, lower mold 25). However, as described above, it may be formed by increasing the density of reinforcing fibers at the outer peripheral portion of the preform at a position outside the product in advance of the outline of the product to be molded in the high flow resistance region.

A high flow resistance region 222 is formed on the outside of the high flow resistance region 222 by the forming die 23 so as to extend along the high flow resistance region 222, An air trap area 223 for sucking in the air that has been discharged through the air trap area 223 is formed. A suction port 225 as a suction path is provided in the air trap area 223 at a position which is distant from the one of the plurality of resin injection ports 29 by a distance 224, When the resin is discharged through the high flow resistance region 222 by the molding die 23 at or near the mounting portion of the suction port 225, it is difficult to flow the resin, A portion 226 is formed (Fig. 13, Fig. 13). It is preferable that a resin detection sensor 227 for detecting the resin when the resin is discharged through the high flow resistance region 222 is provided near the mounting portion of the suction port 225. The suction from the suction port 225 can be controlled by opening and closing operations of the valve body 228 on the pin, for example, as shown in Fig.

Although not shown, a plurality of resin injection ports 29 may be formed in a resin injection port that can be independently controlled to be openable and closable, and the ends (two flow front ends) of the flow of resin injected from the respective resin injection ports 29 are substantially simultaneously It is also possible to provide a control means for controlling the opening timing of each resin injection port 29 so as to reach the high flow resistance region 222.

In the FRP manufacturing method according to the present invention, which is performed using the RTM molding apparatus 21 thus configured, the flow of the resin injected from each of the resin injection ports 29 is, for example, As shown in Fig. As shown in Fig. 14 (2A), when the injection of resin from each resin injection port 29 is started, the shape of the flow front end 231 of the injected resin widened to a circular shape. Finally, a part of each flow front end 231 joins together and reaches the state shown in Fig. 14 (2C) through the state shown in Fig. 14 (2B). When the portion of the flow front end 231 of the resin flow which is to be widened toward the outer peripheral portion of the preform 27 reaches the high flow resistance region 222, the flow resistance of the resin suddenly increases at the reaching portion thereof, The magnification is temporarily suppressed. As shown in Fig. 14 (2D), at least the entire region within the product outer diameter 221 is covered with the high flow resistance region 222 The flow of the resin extends to a portion extending over most of the trap region 223 and further to a portion other than the vicinity of the suction port 225 of the trap region 223. [ It is preferable that suction of the suction port 225 is stopped when the flow front end 231 is enlarged to the vicinity of the suction port 225. The trap air compression portion 232 is generated as shown in Fig. 14 (2E), and the trapped air compressed portion 232 is generated sufficiently to the right side portion of the suction port 225. As a result, Is widespread.

The resin expanding from the inside of the preform 27 toward the outer periphery of the preform 27 is formed at least in the entire range of the product area to be molded So that the air contained in the preform 27 and even the air (two air bubbles) mixed in the resin can be prevented from entering the reinforcing fiber base material of the preform 27, Flow resistance region 222 located outside the range of the product, and further, it is extruded into the air trap region 223. Therefore, the injection resin is preferably impregnated into the reinforcing fiber base material of the preform without air being selectively mixed over the entire area of the product to be molded, and the advantages of excellent high-speed impregnation by the RTM multi- As the shortening is achieved, it becomes possible to obtain a desired molded article free of air trap. After the predetermined molding, the high flow resistance region 222 provided outside the outer shape 221 of the product can be removed together with the resin impregnated therewith if necessary.

Fig. 15 shows an example of enlargement of the flow front end 243 of the resin injected from the resin injection port 242 for the preform 241 in the conventional RTM molding for comparison. An air trap region 244 is generated in a portion where the resin is hardly spread even in the product region, and an undesirable flow of air as indicated by an arrow is generated, so that air tends to be trapped in the molded product.

16 shows an example of an RTM molding apparatus used for carrying out the method according to the second embodiment of the present invention. 16, the RTM molding apparatus 2101 includes a top mold 2104 and a bottom mold 2105 as a molding die 2103 forming a cavity 2102. The top mold 2104 is provided with a press mechanism 2106 So that the mold is opened and closed. The cavity 2102 is made of a reinforcing fiber base material, and is made of, for example, a laminate of a reinforcing fiber base material. For example, a preform 2107 previously shaped into a predetermined shape is disposed. The upper mold 2104 is clamped with respect to the lower mold 2105 while the preform 2107 is disposed in the cavity 2102 and the FRP 2107 is moved from the runner 2108 provided around the preform 2107 toward the preform 2107. [ And a suction port 2109 as a suction path is provided in the cavity 2102 so that the injection resin is impregnated into the reinforcing fiber base material constituting the preform 2107 through suction. The supply of the resin to the runner 2108 is performed through a resin injection port 2110 (shown in Fig. 17) opened at a suitable portion of the runner 2108. [ The suction port 2109 is opened and closed by a valve body 2111 on the pin and the periphery of the runner 2108 with respect to the cavity 2102 is sealed with a sealant 2112. The molding die 2103 is heated and cooled, for example, by a heating medium circulated in the heating medium circulation path 2113, and is heated when the resin is injected to achieve good impregnation of the resin. After resin impregnation, Cooling can be also performed), and the injected and impregnated resin is cured to produce a predetermined FRP molded article.

17, the suction port 2109 is disposed at a central portion of the preform 2107, and a portion corresponding to the periphery of the suction port 2109 of the preform 2107 itself is located at the portion Flow resistance region 2121 which makes it difficult for the resin flowing in the portion to flow from the periphery of the high flow resistance region 2121 to the portion. The high flow resistance region 2121 is formed at a position outside the product to be molded or at a position not requiring the appearance design of the product to be molded. In this embodiment, The thickness of the preform 2107 in the product region is formed by partially reducing the thickness of the high flow resistance region 2121 by the mold 2103 (the two-phase mold 2104 and the lower mold 2105). However, as described above, the high flow resistance region may be formed by increasing the density of the reinforcing fibers in the preform in the high flow resistance region in advance.

The outer shape 2123 of the product to be molded is set in the preform outer circumferential portion 2122 and the runner 2108 is formed around the preform 2107 so as to extend over the entire circumference along the preform outer circumferential portion 2122. [ Is installed.

As for the runner 2108, the resin is supplied from the resin injection port 2110 which is opened at a suitable portion of the runner 2108 as described above. A resin detection sensor 2124 for detecting the resin flowing into the high flow resistance region 2121 is provided near the mounting portion of the suction port 2109 in the high flow resistance region 2121.

In the method of manufacturing an FRP according to the present invention, which is performed using the RTM molding apparatus 2101 thus configured, the resin supplied from each resin injection port 2110 into the runner 2108 flows through the runner 2108, Is injected from the periphery of the preform 2107 toward the preform 2107 from the periphery of the preform 2107. The flow of the injection resin proceeds, for example, as shown in Figs. 19 (2A) to (2D). 19 (2A), when injection is started from the periphery of the preform 2107 toward the preform 2107 from the runner 2108, the shape of the flow front end 2131 indicating the front end of the flow of injected resin Is expanded from the preform outer peripheral portion 2122 toward the inside of the preform 2107. Impregnated region 2132 is irregularly shaped as shown in Fig. 19 (2B) as the flow front end 2131 proceeds, It gradually narrows down. Finally, a part of the flow front end 2131 reaches the high flow resistance region 2121, and the flow resistance of the resin suddenly increases at the reaching end, so that the expansion of the flow front end 2131 is temporarily suppressed. The portion of the flow front end 2131 that does not reach the high flow resistance region 2121 sequentially reaches the high flow resistance region 2121 and the flow front end portion 2131 reaches the entire flow front end portion 2131 as shown in Figure 19 (2C) Flows into the high flow resistance region 2121, and the non-impregnated region 2132 falls within the range of the high flow resistance region 2121. When it is detected by the resin detection sensor 2124 that the resin reaches the vicinity of the suction port 2109, the suction port 2109 is closed by the valve body 2111 described above, , The impregnation is stopped. 19 (2D), the flow of the resin against the suction port 2109 progresses. As a result, even if the suction is stopped, 2133 are substantially reduced to within the range of the suction port 2109. The region including the void region 2133 and the high flow resistance region 2121 may be removed after molding because it becomes, for example, the product outside region 2134, or, in the case where there is no problem in appearance, Can be left.

In the process of enlarging the flow front end 2131 in which the resin flow is intentionally controlled as described above, the resin spreading from the outer peripheral portion of the preform 2107 toward the inside of the preform 2107 is expanded in the range of the area of the product to be molded Air is sufficiently trapped without being trapped over the entirety of the area within the area where the desired surface quality is required, and is impregnated into the reinforcing fiber base material of the preform 2107. In accordance with the expansion of the preform 2107, Even air (two air bubbles) mixed in the resin is extruded to the side of the high flow resistance region 2121 which is located outside the range of the region, and further to the installation portion of the suction port 2109 Goes. Thus, it becomes possible to achieve a desired molding state without air trap, in which air is not selectively mixed over the entire target product area, and the injection resin is preferably impregnated into the reinforcing fiber base material of the preform.

As described above, the method of manufacturing FRP has been described in detail above, but such a method can be applied to a method of manufacturing a ferroelectric layer.

That is, in order to determine the phase of PVDF to be in the? -Phase, the PVDF is rapidly heated at a temperature of, for example, 60 to 70 占 폚, preferably about 65 占 폚, And the PVDF is determined to be in the? -Phase by a cooling method. By applying this method to the above-mentioned FRP manufacturing method, the ferroelectric layer can be easily manufactured. However, the contents of these temperatures are only exemplary, and the contents of the present invention are not limited thereto.

Third Example

The third embodiment proposed by the present invention relates to a method of manufacturing a ferroelectric layer using a graphite fiber production method.

20 is a schematic view showing an example of a container according to the third embodiment of the present invention.

21 is a schematic view showing the arrangement of the container and the raw film according to the third embodiment of the present invention.

22 is a schematic view showing another arrangement example of the container and the raw film according to the third embodiment of the present invention.

23 is a schematic view showing an outer cylinder according to a third embodiment of the present invention.

24 is a schematic view showing a container according to a third embodiment of the present invention.

25 is a schematic view showing still another example of the container and the raw film according to the third embodiment of the present invention.

26 is a schematic view showing the relationship between a and b according to the third embodiment of the present invention.

27 is a schematic view showing a method for producing a carbonaceous film according to the third embodiment of the present invention.

28 is a schematic view for explaining stretching and carbonization and shrinkage of the film in the temperature raising process according to the third embodiment of the present invention.

Fig. 29 shows an example of a schematic view showing the rippling of the carbonaceous film according to the third embodiment of the present invention.

30 is a schematic view showing one or a plurality of ring-shaped members partially surrounding an outer circumferential surface, which is a constraining means at the outer peripheral end of the film according to the third embodiment of the present invention.

Fig. 31 is a schematic view showing a plurality of bar-like members arranged parallel to the winding core along the outer circumferential surface of the film, which is the constraining means at the outer peripheral end of the film according to the third embodiment of the present invention.

Hereinafter, for convenience of explanation, a graphite fiber production method will be described with reference to the drawings.

However, the graphite fiber production method described below can be applied to the ferroelectric layer production method according to the present invention.

The polymer film that can be used in the present invention is not particularly limited, but may be polyimide (PI), polyamide (PA), polyoxadiazole (POD), polybenzoxazole (PBO), polybenzobisoxazole (PBBO), polythiazole (PT), polybenzothiazole (PBT), polybenzobisthiazole (PBBT), polyparaphenylenevinylene (PPV), polybenzimidazole (PBI), polybenzobisimidazole PBBI), and a heat-resistant aromatic polymer film containing at least 210 species selected from the above is preferable because the thermally conductive property of the finally obtained graphite increases. These films may be produced by a known production method.

Among these, polyimide is preferred because various types of raw materials monomers can be selected to have various structures and properties.

Further, the polyimide film tends to become graphite excellent in crystallinity and thermal conductivity, because carbonization and graphitization of the film tend to proceed more than polymer films made of other organic materials.

When the polyimide film is treated to 1000 deg. C under an inert gas, decomposition starts slowly at about 500 deg. C, and most shrinkage of the film occurs at 500 deg. C to 700 deg. C at which cracking gas is generated. Shrinkage of the film does not occur. Low-molecular organic gases such as carbon monoxide, carbon dioxide, nitrogen and ammonia, and low-molecular organic substances such as benzene, aniline, phenol and benzonitrile are observed as decomposition gases. When the temperature is around 900 DEG C, generation of these decomposition gases is almost completed, and after the treatment is finally carried out up to 1000 DEG C, a carbonaceous film having a weight reduced by about 60% is obtained. In addition to the above components, many low-molecular-weight substances that are difficult to identify are observed, and these organic components are recovered as nonvolatile tar components after the carbonization treatment.

This tar component exists as a gaseous phase or a fine combustion phase immediately after being generated as decomposition gas from the film. When the film and the film are in close contact with each other, that is, when the raw film is wound around the core, gas may remain between the films. The gas component staying in the film is agglomerated to become tar, and this tar acts like an adhesive, and solidifies and fuses together with the temperature rise. Carbonation treatment in a reduced-pressure atmosphere may be carried out in order to suppress aggregation of gas components. By carrying out the carbonization treatment under a reduced pressure, aggregation of the decomposition gas can be prevented and occurrence of fusion bonding can be greatly suppressed. The inhibition effect is higher when the decompression degree is larger. For example, when a wide polyimide film is sandwiched between a graphite plate and a carbonization treatment, it is predicted that fusion is more likely to occur because the gas is longer than the narrower polyimide film. Even in such a case, the occurrence of fusion can be suppressed by carrying out the carbonization treatment by further increasing the degree of vacuum. On the other hand, in order to obtain a graphite film having a high thermal diffusivity, it is necessary to orient the graphite in layers in the graphitization step. In order to obtain a high-quality graphite film equipped with such a graphite layer, it is preferable that the carbonization process proceeds smoothly in the carbonization process, which is the entire process of the graphitization process, and the carbon plane is developed and oriented to some extent at the time after the carbonization process .

Therefore, when the decompression degree is increased, more gas is generated from the inside of the film. However, when the decompression degree is excessively increased, a carbonaceous film in which the planar structure of carbon is partially broken is easily obtained, and it is effective to control the decompression degree to some extent to be.

The range of reduced pressure in the present invention is not particularly limited as long as it is -0.01 kPa or more, but is preferably -0.01 kPa or more to -0.08 MPa or less, more preferably -0.1 kPa or more to -0.06 MPa or less, -0.04 MPa or less.

When the decompression degree is -0.01 kPa or more, the fusion-inhibition effect is sufficiently exhibited, and when it is -0.08 MP or less, a graphite film having a good thermal diffusivity can be obtained. Here, "reduced pressure of -0.01 kPa" means that the pressure of the gas in the heating apparatus is 0.01 kPa lower than the pressure of the gas other than the heating apparatus (usually considered to be the atmospheric pressure). Similarly, the "reduced pressure of -0.08 MPa" means that the pressure of the gas in the heating device is lower than the pressure of the gas other than the heating device by 0.08 MPa.

The lower limit of the temperature range for depressurizing is preferably 400 DEG C, more preferably 500 DEG C, and the upper limit of the temperature range for depressurizing is preferably 800 DEG C Deg.] C, and more preferably 700 [deg.] C. It is particularly preferable that the heat treatment is performed in a temperature region where carbonization thermal decomposition occurs or at 500 ° C to 700 ° C. However, the contents of these temperatures are only exemplary, and the contents of the present invention are not limited thereto. By performing depressurization in a temperature region where a large amount of decomposition gas is generated, it is possible to effectively prevent the decomposition gas from staying between the films, and as a result, fusion can be suppressed. Further, as the carbonization progresses, the glass is in a fragile state. Therefore, when a certain force is applied to the fragile state, it tends to crack. Thus, in the temperature range after the progress of the carbonization thermal decomposition, a film with less cracking can be obtained by gentle heat treatment at normal pressure or a small decompression pressure. Further, when the pressure is changed from the atmospheric pressure or the pressurized state to the reduced pressure during the heat treatment, the gas staying between the films is pulled out of the system by the reduced pressure and is extruded by the gas filling the inside of the furnace.

Therefore, by switching to a reduced pressure in a temperature region where a large amount of gas is generated by carbonization thermal decomposition, fusion bonding can be prevented more effectively.

When the number of turns in the winding core increases, the adhesion between the films increases, and the fusion bonding tends to occur during the carbonization treatment. Particularly, a portion close to the core is more likely to cause fusion because it takes more force than the outer portion. When a polyimide film having a certain length or longer is processed, fusion is liable to occur. In such a case, adhesion can be more effectively prevented by performing the treatment under reduced pressure and introducing an inert gas. The inert gas is introduced from one side of the fired portion and the exhaust gas is simultaneously blown out from the other side to generate an inert gas flow path in the fired portion so that the decomposed gas staying between the films can be removed quickly from the system. At this time, it is important to adjust the flow rate of the inert gas (3V1 (unit: L / s)) and the displacement (V2 (unit: L / s)) to maintain the inside of the furnace at an appropriate reduced pressure. The larger the amount of the inert gas to be introduced, the higher the effect is, but the more the use of the inert gas is, the higher the cost becomes. When the volume of the treated product is V, the volume of the treated product and the required amount of the inert gas can be represented by a proportional relation. Here, the volume (V) of the processed product refers to the total volume of all the members arranged and heated in the heating apparatus, such as a polyimide film to be processed and a container of polyimide film. The value (unit: s) of the value (V / V1) obtained by dividing the volume V of the treated product by the flow rate V1 of the inert gas is preferably 0.01 or more and 1000 or less, more preferably 0.1 or more and 100 or less, Is 1 or more and 10 or less. When the value of V / V1 is less than 0.01, the amount of the inert gas to be introduced is too large for the treated product, which is not preferable. If the value of V / V1 is larger than 1000, the amount of the inert gas is too small, so that fusion bonding can not be sufficiently prevented. Here, the "amount of inert gas (V1)" refers to the introduction rate (L / s) of the inert gas in the pressure of the gas other than the heating device (usually considered to be the atmospheric pressure).

As for the kind of the inert gas to be used, nitrogen, argon, helium and the like can be mentioned. If the inert gas is used, no gas is used, the film is not affected during the carbonization treatment, and the same quality is obtained. Of these, nitrogen is preferably used from the viewpoint of cost.

Regarding the above-mentioned atmospheric condition, it is not always necessary to carry out the treatment under the above-mentioned atmospheric condition during the carbonization treatment, and at least 400 to 750 DEG C, preferably 400 DEG C to 700 DEG C, Condition is good. By flowing the inert gas in the temperature region where the decomposition gas is generated, it is possible to effectively prevent the decomposition gas from staying between the films, and as a result, fusion can be prevented. For example, there is a method in which a treatment is performed under a reduced pressure without introducing an inert gas to around 400 DEG C, and thereafter the predetermined reduced pressure is maintained while an inert gas is introduced, or a method in which the flow rate of the inert gas is reduced I think how to do it. With this treatment method, there is no need to continuously flow the inert gas during the treatment, and the amount of consumption of the inert gas can be reduced.

In the case where a large number of polyimide films are processed, it is presumed that the gas is temporarily brought into an atmospheric pressure or a pressurized state. Prediction of the amount of decomposition gas and keeping the processing atmosphere in a reduced pressure state as much as possible is also a point for improving foreign matter and fusion bonding. Therefore, in order to further exert the effects of the present invention, it is preferable to optimize the inert gas flow path in the furnace. It is more effective to design the inert gas introducing port and the exhaust port in accordance with the shape of the fired portion or the container to be fired or to make the container itself into which the polyimide film is inserted to have a structure having improved air permeability.

The larger the thickness of the raw polyimide film is, the larger the amount of decomposition gas generated in the carbonization treatment becomes, and the more the fusion is likely to occur. The thermal diffusivity of the graphite film itself is expressed by the thermal conductivity (unit: W / (mK)), but the ability to actually transport heat is the value obtained by multiplying the value of the thermal conductivity by the thickness of the graphite film. For example, even if the graphite film has a thermal conductivity of 1000 W / (m 占)) having the same thermal conductivity in the plane direction, the graphite film having a thickness of 25 占 퐉 and 40 占 퐉 has a high heat-transporting ability. That is, when the same area is used, the graphite film of 40 mu m is more likely to diffuse heat from the heat source. From the viewpoint of carrying out a large amount of heat transport with a minimum area, it is very useful to produce a thick graphite film.

Generally, when a film having a thick finished thickness is produced by the polymer graphite method, it is necessary to use a thick polyimide film as a raw material. As described above, the polyimide film having a large thickness tends to cause fusion more easily in the carbonization treatment. For example, a separator (a sheet or a film sandwiched between raw films, for example, a graphite film or a graphite sheet) may be used to solve this problem. Further, since the thickness of the polyimide film having a large thickness is thin, the processing length in the same volume is lowered. Therefore, it is preferable that the separator and the like sandwiching the film are not used as much as possible. By using the carbonization method under reduced pressure of the present invention, even a thick polyimide film can be carbonized without using a separator.

Even in this case, the decompression carbonization treatment while flowing the inert gas is very effective. In the case of processing a polyimide film having a large thickness, the flow rate of the inert gas may be increased more than when the film is thin.

The thickness of the polymer film used in the present invention is preferably 10 占 퐉 to 250 占 퐉, more preferably 20 占 퐉 to 200 占 퐉, 20 占 퐉 to 100 占 퐉, further preferably 30 占 퐉 to 150 占 퐉, Most preferably not less than 30 μm and not more than 80 μm. If the thickness of the polymer film is 10 占 퐉 or more, the heat dissipation capability of the finished graphite film becomes sufficiently high. Further, when the thickness is 250 m or less, it becomes possible to form a highly oriented graphite layer. At the time of control of fusion control of the film, the thickness of the polymer film is preferably 10 mu m to 100 mu m, more preferably 10 mu m to 80 mu m, further preferably 10 mu m to 60 mu m, desirable.

The method of producing the graphite film by winding the polymer film on the core of the present invention has the advantage of being able to produce a long and large graphite film which is difficult to manufacture as a sheet type. However, if a polymer film of a certain length is not used, the area of the raw film that can be processed in the same volume may be reduced as compared with the sheet type. Therefore, the length of the raw film to be used is preferably 10 m or more, more preferably 20 m or more, and further preferably 50 m or more. It is needless to say that as the length wound on the core increases, the raw films tend to melt and bond during the carbonization treatment, and the production method of the present invention becomes more effective at that time.

With respect to the exhaust method, all known methods can be used provided that the safety of the calciner itself is not impaired, such as a method using a vacuum pump or an exhaust fan. In particular, various types of vacuum pumps are commercially available from each company, and they are used in the present invention (3 favorably) in view of simplicity of operation. Examples of the vacuum pump that can be used in the pressure range (-0.01 kPa to -0.08 MPa) of the present invention include an aspirator (three-flow pump), a dry vacuum pump, a mechanical booster pump, ) Pump, and an ejector pump.

The degree of decompression can be adjusted by attaching a valve to the exhaust part of the vacuum pump and regulating the exhaust amount. Here, "pressure -0.01 kPa" means that the pressure is reduced by 0.01 kPa with a vacuum pump, and "pressure -0.08 MPa" means that the pressure is reduced by 0.08 MPa with a vacuum pump.

The decomposition gas of the polyimide film contains various low molecular weight substances in addition to the above-mentioned components. When the polyimide film is subjected to the carbonization treatment, these substances are obtained as nonvolatile tar substances. When a large number of sheets of polyimide film are carbonized at one time, the treatment of the resulting tar is a problem. Many components of tar are toxic, so it is necessary to treat effluent gas efficiently considering the trouble of cleaning and the risk to human body. There is also a concern that deterioration may be promoted if the continuous operation is continued with the tar adhered to the heater or the heat insulating material. In this respect, it is necessary to induce the decomposition gas at the time of carbonization to the outside of the furnace quickly after the generation. In this case, in order to induce the outflow gas well out of the furnace, it is preferable to introduce an inert gas from one side and exhaust the air from one side to make the flow of the inert gas in the furnace. As a result, the exhaust gas generated is quickly discharged to the outside, and the risk of polluting the inside of the furnace is greatly reduced. In the carbonization treatment method of the present invention, treatment of decomposition gas can also be effectively performed.

When a polymer film such as a polyimide film is carbonized to 1000 deg. C, the polymer film undergoes linear expansion along with heating. In the case of a long polymer film, the film is stretched once as shown in Fig. 9B until the carbonization shrinkage starts by pyrolysis .

For example, when a polyimide film having a length of 50 m is heat-treated to 500 캜, its elongation is about 1 m. For this reason, the polymer film initially tightly wound on the core becomes elongated and loosens near the temperature at which carbonization shrinkage occurs.

Thereafter, as carbonization progresses, the film length finally shrinks to about 80% of the initial length as shown in Fig. 9C. Thus, when the long polymer film is subjected to the carbonization treatment with the core wound, the outer circumferential end of the film is initially loosened by stretching the film, and if there is nothing bound to the outer circumferential end as shown in Fig. 9D, State. Thereafter, as the carbonization progresses, the polymer film shrinks. Since the number of windings of the film is reduced by the shrinkage, the outer peripheral edge of the film greatly retreats the outer peripheral surface of the wound film, thereby reducing the number of windings. As described above, since the outer peripheral edge of the polymer film moves largely during the carbonization process, cracks are likely to occur, and since the films are not in close contact with each other, friction between the films does not act. As a result, E, a carbonaceous film having a large wave at its ends is obtained. Therefore, when the long polymer film is carbonized by winding on the core, the outer end of the film is bound to the outer circumferential surface without interfering with the movement, so that the long carbonaceous film can be obtained as a film in which cracking or waviness is suppressed. 2101, one or a plurality of ring-shaped members 381 partially surrounding the outer circumferential surface of the film 330, as shown in Figure 2102 A plurality of rod-like members 382 arranged parallel to the winding core 310 along the outer peripheral surface of the film 330 as shown in Fig. Among these binding means, a cylindrical outer tube is more preferable because it can uniformly contact the outer circumferential end portion of the film and equally bind. Hereinafter, the outer tube will be further described.

In the present specification, the container is referred to as a container including a core and an outer tube.

Further, when at least a part of the carbonization step is performed under a reduced pressure and the capturing means is provided at the outer peripheral end of the long polymer film, the fusion of the film can be suppressed in addition to cracking and waved needle.

As described later, in the production of the carbonaceous film, problems of waving and fusion of the film are likely to occur. As a method for solving these problems, in the present invention, as shown in Fig. 7, a value obtained by dividing the inner diameter (3R) of the outer tube by the diameter (r) (B / a) obtained by dividing b by a is an important factor when the thickness is b (mm).

From the viewpoint of both the prevention of waviness and adhesion of the carbonaceous film, the value of (3b / a) is preferably 0.2 to 0.9.

If it is 0.2 or more, even if the film is loosened, it is supported on the outer cylinder, so that it is difficult to remain loosened, and a long carbonaceous film free from waviness and wrinkles can be obtained. If it is 0.9 or less, gaps between the film and the film are avoided, and the films are hardly fused together. Hereinafter, the wave needles and fusion will be described in detail.

When the polyimide film cut to a size of 200 mm is heat-treated at a temperature of 1000 캜 without fixing the film at all, a wavy carbonaceous film can be obtained. This wavy needle is solved by applying a pressing load of a certain load from above to heat-treat the film. In this case, however, it is difficult to obtain a woven sheet type wrinkle-free carbonaceous film such as fine wrinkles at its ends Do. On the other hand, it is possible to obtain a long carbonaceous film free from waved needle or wrinkle by selecting a treatment method well as a long type in which a polymer film is wound around a core and heat treatment is performed. The mechanism will be described below.

When the long raw film wound on the core is carbonized, the friction between the films acts on the film in the longitudinal direction and against the force of the shrinkage in the opposite direction. As a result, a constant tension is generated on the film. It is possible to obtain a long carbonaceous film having high planarity and having a surface free from wrinkles or distortion in the film by progressing carbonization and shrinkage of the film with constant tension. As can be seen from comparison between B and D in FIGS. 9A and 9B and C and E in FIG. 9, since the film is in contact with a certain extent in B and C having the constraining means for constraining the outer peripheral end, It is preferable that friction occurs. In the sheet type, even when the films are laminated and carbonized, no tension is applied on the film because no frictional force acts between the films at the time of shrinking (or, even if they work, they become separate vectors). Further, in order to generate tensile force, even if carbonization treatment is carried out by fixing the end portion of the raw film, the carbonaceous film is in a glass phase, so that the film is split at the time of contraction. In the case of the long type, since the wound films can move with each other at the time of shrinkage, the film is not insulated by shrinkage, and a certain tensile force acts on the film, thereby making it possible to obtain a carbonaceous film free from wrinkles and waviness.

When a polymer film such as a polyimide film is carbonized to 1000 deg. C, the length of the polymer film shrinks to about 80% as described above. However, because the polymer film undergoes thermal expansion along with heating, It will grow. For example, when a polyimide film 50 m having a coefficient of linear expansion of 40 ppm / ° C is heat-treated to 500 ° C, its elongation is about 1 m. Therefore, the raw film initially tightly wound around the core becomes elongated and loosens near the temperature at which the carbonization shrinkage occurs. On the other hand, in the case where the polyimide film is wrapped around the cylindrical core and the heat treatment is performed in the transverse direction, even if the raw film is wrapped tightly around the core at first, the film is stretched just before the thermal decomposition shrinkage, It is loosened and becomes a state of being stretched. When the carbonization treatment is carried out in this way, frictional force does not act between the films because the films are not in close contact with each other, and as a result, a long carbonaceous film with wavy needles is obtained. Further, in the case of a long film, shrinkage of the film in the longitudinal direction is hindered by wrinkles or wavy streaks entered during carbonization, and as a result, there is a possibility that the films are thermally insulated from each other.

Further, after the carbonization treatment, the carbonaceous film can be further converted to a graphite film by treatment at 2400 DEG C or higher. The graphite layer is lifted by the generation of N2 that does not form a graphite skeleton at the final stage (2600 DEG C or more) of the graphitization process and internal gas such as a filler (phosphoric acid series) added to the raw film, and the film is foamed. A graphite film excellent in flex resistance can be obtained by subjecting the graphitized expanded graphite film to compression treatment. The reason why the foamed material is obtained by removing the foaming by compressing the foamed graphite film is that since there is a small space between the layers of the graphite after compression, distortion of the graphite layer applied at the time of bending (three folding) can be avoided Because. However, if the carbonaceous film contains waviness or wrinkles in the carbonization treatment process, the waviness and wrinkles remain after the graphitization. Even if the compression treatment is performed after that, the waviness and wrinkles are not solved Deep wrinkles get in.

Next, as shown in Fig. 21, the case where the polymer film 330 is carbonized by using the container having the core 310 and the outer cylinder 320 will be described. The film 330 wound on the winding core 310 elongates and elongates before the initiation of the pyrolytic shrinkage of the carbonization. However, when the container of Fig. 21 is used, this sagging can be supported by the outer tube 320, It is possible to perform carbonization in one operation. It is possible to obtain a carbonaceous film free from waviness and wrinkles even when the film is stretched and loosened during the treatment due to the film being subjected to a certain tensile force by causing the film to shrink while closely adhering thereto.

In order to support the loosened film and closely adhere the films, it is necessary to appropriately select the inner diameter of the outer tube.

If the inner diameter of the outer tube is too large, the film becomes loose and only the wavy film is obtained.

If the ratio (b / a) is 0.2 or more, even if the film is loosened, it is supported on the outer tube, so that it is difficult to remain loosened and a long carbonaceous film free from waviness and wrinkles can be obtained.

From the viewpoint of waving the carbonaceous film, the value of (b / a) is more preferably 0.5 to 0.8. If it is 0.5 or more, the degree of adhesion between the film and the outer cylinder is increased, and a long carbonaceous film free from waviness and wrinkles can be obtained. If it is 0.8 or less, it is possible to obtain a smooth carbonaceous film free from distortion and without distortion due to the contact of the loosened film with the outer passage.

As described above, the polyimide film generates various decomposition gases at the time of thermal decomposition, and becomes a non-volatile tar component after the carbonization treatment, and functions as an adhesive to fuse the films together. In the case of carbonization treatment in which the polymer film is wound around the core, since the films adhere closely to each other, fusion is likely to occur. Further, in order to obtain a long carbonaceous film, when the number of turns of the raw film is increased, fusion is more likely to occur. Normally, as described above, an inert gas is flowed at the time of treatment to seize the decomposition gas to prevent fusion. However, in the case where the polyimide film wrapped around the core is covered with the outer tube and the gas permeability of the entire container is deteriorated as in the present invention, even if the carbonization treatment is performed while flowing the inert gas, the outgassing gas stays in the vessel, There is a possibility that fusion is caused. This problem is solved by providing a gap between the inside of the container and the outflow gas, that is, by increasing the inner diameter of the outer tube.

(b / a) is 0.9 or less, the gap between the film and the exit gas from the film is secured, and the films are hardly caused to adhere to each other. From the viewpoint of prevention of fusion bonding of the carbonaceous film, it is more preferably 0.3 to 0.7. If it is 0.7 or less, the gap between the film and the exit gas from the film is sufficiently secured, and the films are hardly fused together. If the ratio is 0.3 or more, the film is loosened and is not well supported by the outer tube, so that the film is excessively wavy and can be prevented from being welded due to contact between the wavy films.

As for the shape of the outer tube, there is no particular limitation. However, since the loosened film is supported on the inner surface of the outer tube, the shape of the inner surface is an important factor for determining the surface of the carbonaceous film. If there is unevenness on the inner surface of the outer cylinder, the surface of the obtained carbonaceous film may be uneven. In order to clean the shape of the carbonaceous film, it is preferable that the inner surface of the outer cylinder is as close to a cylinder as possible. However, it is not necessary to have a cylindrical shape and it may have the same shape as an elliptical column. With respect to the case where the cross section is not circular like the ellipse, as shown in Fig. 23, when the center of the crimp is the point A, and the intersection of the waterline from the point A and the outer passage is the point B, A value corresponding to the inner diameter of the outer tube can be set by the distance.

In order to prevent fusion of the films, it is effective to increase the inner diameter of the outer tube to take a space inside the container and to improve the gas escape. At this time, it is more preferable to provide a hole for ventilation in the outer cylinder to improve the gas escape. However, the shape of the inner surface of the outer cylinder may be transferred to the surface of the carbonaceous film. Therefore, if a large ventilation hole is taken out, large unevenness may be transferred to the film surface, or the carbonaceous film may be caught and cracked. When the vent hole is formed, the area of each hole is made small, so that the uneven transfer to the film can be minimized, and cracking due to the engagement can be prevented. The area is preferably 20 mm or less, more preferably 10 mm or less, and further preferably 5 mm or less. There is no particular limitation on the shape of the hole, but it is more preferable that the shape of the hole is less circular than the square. In the case of the container as shown in Fig. 24, a portion where the film does not directly contact, that is, an upper portion of the outer tube 320 in the case of longitudinal arrangement, Providing a ventilation hole in the portion of the disk 315 serving as a lid of the outer cylinder 320 does not affect the film. In this case, there is no fear that the film is caught, so there is no limitation on the area of the hole, and if it is wider, the ventilation is preferable.

The shape of the winding core is required to be a cylindrical shape in the present invention, but the shape of the winding core need not necessarily be a circle, but may be a slightly oval shape, a distorted shape, or a shape having a groove. As the weight of the container increases, the load on the heater increases. Therefore, it is effective to make the inside of the core a hollow structure from the viewpoint of reducing the weight of the entire container or to make a small hole in the core. When the carbonization is carried out by using a small-diameter core, and subsequently the graphitization treatment is carried out, the winding property and the winding property are improved. Is obtained. The graphite film having such properties has a problem that wrinkles tend to enter in the following compression softening step. This problem can be solved by using a winding having a certain diameter, and it is possible to perform softening without wrinkles in the subsequent compression step. Examples of the method for softening the film include a method of rolling the film and a method of compressing the film. In particular, since graphite tends to be easily torn, a method of compression is preferable in order to obtain long graphite having no thickness irregularity without tearing. Particularly, as a compression method, a method of interposing with a polymer film and compressing it in a plane is preferable. The compression is not applied with a shearing force such as rolling, and the graphite can be softened without causing tearing or thickness unevenness of the graphite.

The diameter of the winding core is preferably 70 mm or more, more preferably 80 mm or more, and even more preferably 90 mm or more. When the diameter is larger than 70 mm, the property of winding the obtained carbonaceous film is difficult to be obtained. Although there is no upper limit on the diameter, the diameter of the winding core is preferably 300 mm or less, and more preferably 200 mm or less, in order to secure a throughput per unit volume. In such a case, it is possible to effectively utilize the space by inserting the core into the hollow and further inserting the core in the inside, thereby making it possible to increase the throughput one time.

As a condition of the material of the winding core used in the present invention, those resistant to the continuous use environment at 500 DEG C or higher can be cited. Examples of the material of the container that satisfies this condition include isotropic graphite materials such as extruded products, molded products and cold isostatic pressing products, and alumina (Al2O3), zirconia (ZrO2), quartz (SiO2), silicon carbide (SiC) (MgO), silicon nitride (Si3N4), aluminum nitride (AlN), yttria (Y2O3), mullite (3Al2O3.2SiO2), cordierite (2MgO.2Al2O3.5SiO2), stearate SiO2) and forsterite (2MgO.SiO2), and composite C / C com- posite in which graphite is reinforced with carbon fiber. Among them, carbon is used in a satisfactory manner in view of ease of processing, manufacturing cost, and versatility.

There is a possibility that the carbonaceous film which has been treated at a temperature of 1000 ° C or higher once again is subjected to the heat treatment The carbonaceous film may be changed to another container made of a material resistant to the graphitization temperature after the carbonaceous film is prepared and graphitized. The graphitization process may be carried out after the carbonization process is performed after the temperature is lowered and the container is taken out, and the graphitization may be continuously performed without removing it.

In order to make the carbonization treatment method of the present invention effective, the direction of the container set in the furnace becomes very important. When heating is performed from the outside of the container as in the present invention, for example, when the container is set in the longitudinal direction in the furnace as shown in Fig. 22, it is natural that the outer tube can not support the loose- Only a proton carbonaceous film is obtained. Further, when the container is placed in the longitudinal direction, the heat from the heater is conducted from the lower portion of the container, so that temperature unevenness occurs at the lower end portion and the upper end portion of the film, and wrinkles or cracks are likely to occur.

In addition, since the outflow gas from the lower portion of the film is difficult to escape, fusion is liable to occur as compared with the case where the film is placed in the transverse direction. On the other hand, when the film is placed in the transverse direction, the temperature difference in the film is less likely to occur than in the longitudinal direction, and wrinkles and cracks are unlikely to occur. Further, when the film is set in the longitudinal direction, there is a fear that the lower part of the film may be rubbed against the container and may be separated at the time of contraction of the film. Even when the container is placed horizontally, both ends of the film are not brought into contact with the container as much as possible, which is a point for preventing fusion of the film without causing cracking and facilitating release of the outgas. From the above, it is preferable to arrange them in a horizontal arrangement rather than a vertical arrangement. Here, the horizontal arrangement refers to a state in which the winding core is placed almost horizontally, and the vertical arrangement refers to a state in which the winding core is disposed substantially vertically.

When the container is placed on a flat surface, the outer shape of the outer tube is advantageous in that the rectangular parallelepiped is more stable than the cylinder and has good thermal contact. However, in the case of a rectangular parallelepiped shape, since the weight of the container is larger than that of the cylindrical shape, the load on the heater may increase. Considering the workability and the weight of the container, the outer cylinder is preferably cylindrical.

When the polyimide film wrapped around the core is directly subjected to carbonization treatment in an electric furnace, a carbonaceous film having a wider end and a wider end than the core is obtained as described above. In a furnace which is heated by energizing the heater, there is a possibility that the expanded film comes into contact with the heater and may cause a short-circuit. Therefore, it is preferable to carry out the carbonization by inserting the winding core into the outer cylinder for preventing contact.

As described above, the graphite fiber production method has been described in detail above, but such a method can be applied to the ferroelectric layer production method.

That is, in order to determine the phase of PVDF to be in the? -Phase, the PVDF is rapidly heated at a temperature of, for example, 60 to 70 占 폚, preferably about 65 占 폚, And the PVDF is determined to be in the? -Phase by a cooling method. By applying this method to the graphite fiber production method described above, the ferroelectric layer can be easily manufactured. However, the contents of these temperatures are only exemplary, and the contents of the present invention are not limited thereto.

Fourth embodiment

The fourth embodiment proposed by the present invention relates to a method of manufacturing a ferroelectric layer using a metal fiber manufacturing method.

32 is a view showing a method of manufacturing a metal fiber in which a concave-convex shape is formed using a spur gear according to a fourth embodiment of the present invention.

33 (a) is an upper cross-sectional view of a metal fiber having a concavo-convex shape formed by passing through a spur gear, (b) is a side cross-sectional view of a metal fiber having a concavo-convex shape formed by passing through a spur gear, And is a perspective view of a metal fiber having a concavo-convex shape formed by passing through a gear.

34 is a view showing a method of manufacturing a metal fiber in which a concave-convex shape using a helical gear is formed.

Fig. 35A is a cross-sectional top view of a metal fiber having a concavo-convex shape formed by passing through a helical gear, Fig. 35B is a side cross-sectional view of a metal fiber having a concavo-convex shape formed by passing through a helical gear, And shows an example of a perspective view of a metal fiber having a concavo-convex shape formed by passing through a gear.

Hereinafter, for convenience of explanation, a metal fiber manufacturing method will be described with reference to the drawings.

However, the metal fiber manufacturing method described below can be applied to the ferroelectric layer manufacturing method according to the present invention.

According to one embodiment of the present invention, metal fibers having irregularities formed at regular intervals, specifically 0.3 mm to 50 mm intervals, in the longitudinal direction of the metal fibers are provided. It is preferable that the irregularities for the metal fibers are formed at uniform intervals along the length direction of the metal fibers so as to exhibit uniform friction force between the metal fibers and excellent high porosity in yarns and fabrics including metal fibers. That is, the irregular shape may be repeated at intervals of 0.3 mm to 50 mm along the longitudinal direction of the metal fiber.

The concavo-convex shape of the metal fibers may be specifically formed at an interval of 0.3 mm to 50 mm, preferably 0.3 mm to 30 mm, more preferably 0.5 mm to 18 mm.

If the irregularities are formed at intervals of less than 0.3 mm, it is not preferable because stable stretching can not be performed due to the increased frictional force between the metal fibers due to many irregularities. If the concavoconvex shape is formed at an interval exceeding 50 mm, the metal fibers may escape from the metal fiber yarn since the frictional force and entanglement between the metal fibers are insufficient.

The concavoconvex shape is not limited to this, but it can be formed by passing a bundle of metal fibers through the gear. The types of gears are not particularly limited, and irregularities can be formed on any kind of metal fibers. The metal fiber bundle which is to pass through the gear to form a concave-convex shape in the longitudinal direction of the metal fiber may be made of any number of metal fibers, and the number of metal fibers is particularly limited in the bundle of metal fibers forming the concave- It is not.

A method of forming a convexo-concave shape in a metal fiber by passing a bundle of metal fibers through a gear, and a metal fiber bundle in which a convexo-concave shape is formed.

For example, the metal fiber bundle may be passed through a spur gear or passed through a helical gear as shown in FIG. 34 to form a concave-convex shape on the metal fiber, although not limited thereto . When the metal fiber bundle 12 is passed through the spur gear 11, a metal fiber bundle in which the concavo-convex shape is formed is obtained. That is, the shape of the concave-convex side surface of the metal fiber is formed perpendicular to the longitudinal direction of the metal fiber. When the metal fiber bundle 32 is passed through the helical gear 31, a metal fiber bundle in which the concavo-convex shape is formed as shown in Figs. 35 (b) and 35 (c) is obtained. That is, as shown in the side sectional view 35 (b) of the metal fiber, the concave and convex shape is formed by inclining at a vertical line with respect to the longitudinal direction of the metal fiber.

The concavo-convex shape of the metal fiber having the irregular shape according to the present invention may vary depending on the shape of the gear through which the metal fiber is passed, and the specific shape of the concavo-convex shape is not limited. For example, , Can be any shape.

The concave-convex shape may be formed on any metal fiber generally known in the technical field and / or metal fiber produced by any method. In one embodiment, the metal fiber may be a metal fiber of any kind of Fecralloy alloy, which is an iron-chrome-aluminum-based alloy. The Fecralloy alloys are generally known, for example, 18-27% by weight of chromium (Cr), 3-7% by weight, preferably 5-7% by weight of aluminum (Al) .

Further, an improved Fecralloy may be used, which additionally contains 0.05-0.5 wt%, preferably 0.1-0.3 wt% of zirconium (Zr), yttrium (Y) or the like in the Fecralloy alloy composition. In another embodiment, stainless steel metal fibers, specifically stainless steel 316L metal fibers, may be used as the metal fibers.

Further, although not limited thereto, for example, irregularities may be imparted to the metal fibers produced by the cutting method, the drawing method and the melt extraction method.

The surface of the metal fiber formed by the cutting method or the mechanical working method of the drawing method is smooth without projections. Therefore, the metal fiber having such a smooth surface has no frictional force between the metal fibers, and thus it has been difficult to fabricate the metal fiber in the prior art.

In addition, although the surface of the metal fiber produced by the conventional melt extraction method has a height of micron level, specifically, a large number of protrusions, there is a problem that the metal fiber is escaped from the metal fiber yarn due to insufficient frictional force between the metal fibers.

On the other hand, when the metal fiber yarn is produced using the metal melt produced by the conventional melt extraction method, the friction force between the metal fibers is insufficient, so that one strand of the yarn should be made of a relatively large number of 50 to 100 metal fibers, Even in this case, there is a problem that the shape of the metal fiber yarn is not maintained because the metal fiber is missing from the metal fiber yarn.

However, as in the present invention, since the metal fibers produced by the melt extraction method as well as the metal fibers produced by the mechanical working method such as the cutting method or the drawing method are provided with sufficient frictional force and entanglement by forming the concave- Not only the metal fiber yarn can be produced but also the metal fiber does not fall out from the metal fiber yarn and the number of the metal fibers used for forming one yarn is not limited. Specifically, it can be easily produced with a yarn comprising any number of metal fibers, more specifically about 10 to 250 strands or more, of metal fibers. In addition, in the production of metal fiber yarns, yarns can be produced without using a separate binder and / or polymer.

Further, the metal fiber yarn made of the metal fiber having the irregular shape according to the present invention is excellent in porosity due to the uneven shape, and also has many very fine and uniform pores formed in the metal fiber yarns and fabrics do.

Further, due to the weak frictional force, entanglement and workability (specifically, workability in the metal fiber yarn) of the metal fiber yarn in the conventional metal fiber yarn, the diameter and the length of the metal fiber that can be used in the production of the metal fiber yarn are limited .

Specifically, conventional metal fiber yarns have been made of metal fibers having diameters in the range of 10 탆 to 100 탆, preferably in the range of 30 탆 to 100 탆, and lengths of 10 cm to 100 cm. However, the diameter and the length of the metal fiber which can be used for forming the metal fiber yarn due to the friction force, the entanglement property and the workability increase between the metal fibers are not particularly limited. That is, metal fiber yarns having a diameter of less than 10 mu m and metal fibers having a diameter of more than 100 mu m can be easily manufactured, as well as metal fibers having a diameter of 10 mu m to 100 mu m. In addition, metal fiber yarns can be easily produced using not only metal fibers having a length of 10 cm-100 cm, but also metal fibers having a length of less than 10 cm and metal fibers having a length of more than 100 cm.

However, in terms of excellent fine and uniform pore formation of fabrics made of metal fiber yarns and metal fiber yarns, it is preferred that in the same equivalent diameter yarns, a number of fine metal fibers are used instead of yarns comprising a small number of coarse metal fibers Is preferred. Specifically, for example, in a number of fine and uniform pore-forming planes fabricated from fabrics, yarns of 200 yarns (20 microns in diameter) having a diameter of 20 microns (yarn diameter of about 0.1 mm) Fabrics made with a yarn diameter of about 0.1 mm are preferred.

Further, the metal fiber having the concavo-convex shape according to the present invention has excellent elasticity due to the concavo-convex shape. Due to the elasticity, the metal fiber yarn and the metal fabric using the metal fiber yarn can be easily processed, The fabricated metal fiber yarns and the metal fabrics using them have a smooth texture.

The metal fiber on which the irregular shape according to the present invention is formed can be stretched and twisted to produce a metal fiber yarn. On the other hand, conventional metal fiber yarns are insufficient in frictional force and entanglement between metal fibers and can not be made of false twist yarns, and can be produced only by twisting yarns. However, in the case of using the metal fiber on which the concavo-convex shape is formed according to the present invention, due to the increased frictional force and entanglement between the metal fibers, it can be made into a twist yarn as well as a twist yarn. In the twist yarn and false twist yarn made of the metal fiber according to the present invention, the separation of the metal fibers is prevented and the shape of the yarn is stably maintained.

The metal fiber according to the present invention improves the frictional force between the metal fibers and has excellent entanglement, so that the twist ratio is not particularly limited in the production of the yarn. On the other hand, as is generally known in the art, false twists are produced by stretching and twisting metal fibers to produce metal fiber yarns and then twisting.

As described above, the twist rate of the metal fiber yarn in the production of the metal fiber yarn according to the present invention is not particularly limited. Depending on the use of the metal fiber fabric produced from the metal fiber yarn, the porosity and pore distribution A twist can be imparted.

For example, in the case of using a metal fiber yarn to produce a metal fiber fabric to be used as a burner material, the metal fiber yarn comprising the metal fiber according to the present invention may be used for ejecting, For example, 3-5 turns / m at the time of production into a yarn, though it is not limited thereto, in consideration of differential pressure, combustion efficiency, and the like.

As another example, when a metal fiber yarn used as a filter material is to be manufactured using metal fiber yarns, the metal fiber yarn comprising the metal fibers according to the present invention is preferably used for filtering and / But may be made of a twist yarn or a twist yarn, though not limited thereto, in consideration of a differential pressure increase due to the accumulation of dust and / or foreign matter in the pores. It is also possible to produce, for example but not limited to, twisted yarns at the time of production, for example, at 1-15 turns / m, preferably at 10-15 turns / m.

As the pores of the metal fiber yarn and / or the fabric become smaller, the filtration performance and the combustion efficiency of the fine dust and / or the foreign substance are improved, but the differential pressure and the differential pressure increase rate increase as dust and / or foreign matter accumulates. Depending on the application of the metal fabric, specifically the use of the metal fabric to the burner material and / or the filter material, so as to ensure filtration performance and combustion efficiency as well as to minimize the differential pressure rise rate, To produce a twist yarn or a twist yarn.

The metal fiber yarn according to the present invention preferably has a length of 0.45 m-10.0 m (0.45 Nm-10.0 Nm) per 1 g. If the length per 1 g of the yarn is less than 0.45 m, the thickness of the yarn becomes thick, which is not preferable from the viewpoint of porosity. If the length exceeds 10.0 m, the yarn is not formed.

The metal fiber yarn can be produced by continuously and finely stretching metal fibers having a concavo-convex shape formed thereon and twisting them. On the other hand, a false twist yarn is produced by stretching a metal fiber, twisting it, and then twisting it.

The metal fiber yarn 81 made of the metal fiber 82 having the concavoconvex shape is well entangled with each other due to the irregular shape of the metal fiber and the fiber is not pulled out from the yarn due to the increased frictional force between the metal fibers, But also a plurality of fine and uniform pores are formed between the metal fibers constituting the yarn due to the concavo-convex shape of the metal fibers constituting the yarn, thereby exhibiting excellent and high porosity. Further, the metal fiber having the irregular shape according to the present invention is not only easy to be processed subsequently due to elasticity, but also has a smooth texture.

Meanwhile, the metal fiber yarn of the present invention can be produced by weaving the fabric by a general method known in the art.

As a specific example, but not limited thereto, the fabrics according to the present invention can be produced by weaving warp yarns and weft yarns perpendicular to each other using metal fiber yarns as warp yarns (B) and weft yarns (B '). The metal fiber fabric may comprise from 5 to 30 strands (5 to 30 strands / inch) of metal fiber yarns as warp and weft yarns per inch of fabric. If the number of metal fiber yarns in the metal fabric is less than 5 strands / inch, if the diameter of the yarn is small, pores of the fabric are too large. If the number of metal fiber yarns is more than 30 strands / inch, It is not preferable in terms of blocking too much.

During weaving, wefts (A, A ') are formed on both sides of the weft yarn (A, A') with weft yarns and warp yarns arranged substantially vertically and with two weft yarns parallel to two parallel yarns. Dyeonggong refers to a part of the fabric that is slightly concave at the bottom and top. The slit has a width to height ratio of 10: 1 or less, preferably 1: 1-10: 1. If the ratio of the longitudinal length to the longitudinal length of the air gap is more than 10, there is a problem that the structure of the fabric is loosened due to the formation of the air holes through the lower yarn of 3 to 4 strands. On the other hand, as long as the porosity is not an issue, it can be produced with a fabric having a pore size of 10: 1 or less in any transverse to longitudinal length ratio.

As described above, since the metal fiber yarn is produced using the metal fiber having the irregular shape according to the present invention, the thickness and / or the length of the metal fiber used for the production of the metal fiber yarn are not limited, It is possible to use metal fibers that are thinner than the metal fibers used in the production of the metal fiber yarns and can also form morphologically stable metal fiber yarns even when a smaller number of metal fibers are used. Thus, the metal fiber yarn produced using a small number of metal fibers and / or fine metal fibers can be used to fabricate a low density metal fiber fabric having a lower density than the conventional one.

Low density metal fiber fabrics have the advantage of being capable of ultra low load combustion, especially when used as a burner material. For example, although not limited thereto, the density of the fabric may be 4.0 kg / m 2 or less, specifically 0.1-4.0 kg / m 2.

When the fabric is used as a burner material or a filter material, the lower limit of the fabric density is not particularly limited because the smaller the fabric density is, the smaller the fabric pressure is, the lower the pressure difference. However, if the fabric density is less than 0.1 kg / The gap between the fiber yarns is too wide and the smooth combustion or dust filtration performance may be insufficient, so that the density of the fabric is more preferably 0.1 kg / m 2 or more. On the other hand, if the density of the fabric exceeds 4.0 kg / m < 2 >, the interval between the metal fiber yarns becomes too narrow to lower the porosity and the differential pressure, which is not preferable from the viewpoint of fuel gas ejection and filtration performance. Fabrics made with a density of 0.1 - 4.0 kg / m 2 will have a thickness of 0.3-2.5 mm. The porosity of the fabric is 75-95%.

The fabric according to the present invention can be used as a filter material and / or a burner material, specifically, a membrane for a surface combustion burner, a pre-filter for water treatment, and a filter for a soot reduction device.

On the other hand, when a conventional metal fiber fabric is used as a burner material or a filter material, a metal mesh is placed on both sides of the metal fiber fabric, and the metal fiber fabric is processed into a corrugated form Has been used. However, there has been a problem that the metal mesh, which is sandwiched on both sides of the metal fiber fabric, is easily damaged when the fabric is processed.

Therefore, in the production of the metal fiber fabric according to the present invention, the metal fiber yarn is woven together with the metal wire by using a metal wire instead of the metal fiber yarn used as the warp and / or weft, Can be manufactured. The metal wire may be used for warp and / or weft. That is, the fabric according to one aspect of the present invention is characterized in that the metal wire is used in both at least one of a plurality of warps and wefts, at least one weft or at least one warp, and at least one weft, metal wire. < / RTI > The number of the metal wires that can be used in the production of the metal fiber fabric is not particularly limited and may be selected from the range of inclination and / or thickness in consideration of physical properties required when used as a burner material or filter material, such as combustion performance, Or any location in the weft, at any interval and / or in any number of ways. The metal wire is made of the same kind of metal as the metal fiber yarn.

The metal wire preferably has a diameter of 0.07 mm to 3 mm. When the diameter of the metal wire is less than 0.07 mm, the diameter is small and the tensile force is weak. Therefore, there is no great difference between the metal wire and the metal fiber. When the diameter is more than 3 mm, the diameter of the metal wire is large. The metal fiber fabric including the metal wire does not require a separate metal mesh that is conventionally required when used as a burner material or a filter material because the fabric itself includes a metal wire. Therefore, there is no fear of breakage of the material due to the breakage problem of the metal mesh at the time of shaping into the burner material or the filter material, so that the formability into the material is improved. Also, the strength of the metal wire in the metal fiber fabric improves, and the combustion efficiency of the burner material and the filtration efficiency of the filter material are further improved due to the dense pores in the metal fabric due to the metal wire.

On the other hand, although not limited thereto, a fabric in which a metal wire is used as a warp (C) instead of a metal fiber yarn, and a fabric in which a metal wire is used as a warp (C ') in place of the metal fiber yarn.

The metal fiber fabrics made of yams containing metal fibers having irregularities according to the present invention include many uniform and uniform micropores, and are therefore suitable as filter materials for filtering fine dust and / or foreign matter. In addition, since the fuel gas is ejected finely and uniformly through the micropores, the flow rate of the gas between the metal fibers increases even when a small amount of fuel is supplied, so that the gas is stably burned. Furthermore, the fine pores between the metal fibers having the concavoconvex shape formed therein act as fine spheres, thereby exhibiting a wide range of combustion characteristics over the entire region of high load-low load, and further improved heating due to uniform flame distribution and flame splitting effect Effect. It also shows improved differential pressure performance (differential pressure reduction).

As described above, the method of manufacturing a metal fiber has been described in detail above, but such a method can be applied to a method of manufacturing a ferroelectric layer.

That is, in order to determine the phase of PVDF to be in the? -Phase, the PVDF is rapidly heated at a temperature of, for example, 60 to 70 占 폚, preferably about 65 占 폚, And the PVDF is determined to be in the? -Phase by a cooling method. By applying this method to the above-described method of manufacturing a metal fiber, a ferroelectric layer can be easily manufactured. However, the contents of these temperatures are only exemplary, and the contents of the present invention are not limited thereto.

additional information

Rolling, extrusion, drawing, and the like may be used for the method of manufacturing the carbon fiber used for manufacturing the ferroelectric layer.

First, rolling is performed by using the plasticity of a metal material having a high temperature or a room temperature passing between two rotating rolls to form a plate, a rod, a pipe, a shape, and the like , Which is faster than casting or forging and has a low production cost

Next, it is said that the extrusion was made by J. Brahma of England in 1797 by melting the lead and pumping it out to make the lead pipe. Then in England, Th. Birr actually manufactured the linkage in 1820 using an extrusion process. Generally, a material (material) is put into a container (container) and is pushed out from a hole of a die to make a product having a sectional area smaller than a material and having a constant length.

This processing method is largely divided into a positive extrusion method and a reverse extrusion method. The former is the case where the direction of the metal to be extruded is the same as the direction in which pressure is applied from the outside, and the latter is the opposite direction.

Since the shape of the product section is the same as the shape of the hole of the die, it is possible to make a round bar, a square bar, a shape member, a pipe or any other by changing the hole shape of the die appropriately. However, pushing the metal material out of the hole requires a very large force, which is not only a large-scale machine, but also has the drawback of using tools that withstand high temperatures and high pressures.

Hot extrusion is performed at a high temperature, and cold extrusion is performed at a room temperature. During the Second World War, cold extrusion processing technology of hard metal was rapidly developed in Germany, and cold extrusion of special steel was used to mass produce high dimensional precision products and to produce military materials.

Finally, drawing refers to a processing method in which a rod or tube is passed through a die having a smaller cross-sectional area than that of the die or pipe, thereby obtaining a cross-sectional product having the same shape as the die bore. Drawing of thin-walled wire is especially called drawing. Generally, there are many cold draws. It applies to most of carbon steel, alloy steel and nonferrous metals. In some cases, nickel or copper plating or copper plating is performed on the rods or pipes before drawing. There is an effect of improving the lubricity and preventing the oxidation of the material during normal processing.

The rolling, extrusion, and drawing methods described above can be used variously to produce the ferroelectric layer, and the manufacturing method of the rod invention is not limited by any one method.

The above-described ferroelectric layer using PVDF or PVDF-TrFE can exhibit unique characteristics. The details are as follows.

(1) It shows a strong characteristic to the acid. That is, it is resistant to high acidity and resistant to acid.

(2) There is a characteristic that can be used for flameproofing which can be prevented from being ignited.

(3) There is a characteristic that fluorine decontamination can be efficiently performed.

(4) Since the physical properties of steel have piezoelectric due to the reversal phenomenon of spontaneous polarization, it is possible to apply the ferroelectric to the garment (for example, shoes) and to provide the characteristic of energy harvesting .

(5) Further, when a ferroelectric material is woven with a fiber, there is a characteristic that it is lighter in weight than other materials and provides high strength and can provide a piezoelectric effect.

Further, the ferroelectric layer using PVDF or PVDF-TrFE can be used in various fields other than those used for semiconductor devices, such as a region for treating chemicals, a region for performing flame retardation, and a region for performing a fire-fighting operation. It can also be used for energy harvesting.

That is, by using a ferroelectric layer using PVDF or PVDF-TrFE as a material for clothing, a person who handles chemical agents, a person who performs flame-retarding work, a person who performs fire-fighting work is used for maximizing effects in the field, it becomes possible to use the battery for energy harvesting.

Hereinafter, a method for fabricating a fabric using the above-described ferroelectric layer and fabricating a fabric including the piezoelectric fiber and manufacturing an apparatus and an apparatus for energy harvesting using the fabric will be described.

First, the energy harvesting technology using a piezoelectric element utilizes mechanical energy applied to a piezoelectric element to generate mechanical energy such as abandoned power, pressure, vibration, etc., .

Next, the piezoelectric fiber produced by the fiber manufacturing method generates electrical energy will be described with reference to the drawings. However, not only the above-described manufacturing methods of the first to fourth embodiments but also piezoelectric fibers manufactured by other fiber manufacturing methods may be used as the piezoelectric fibers.

36 is a view showing a piezoelectric fiber for generating electrical energy according to an embodiment of the present invention.

36 (a) shows a piezoelectric fiber 110 that generates electrical energy by deformation by an external force.

As the piezoelectric fibers 5110, various kinds of fibers may be used. The piezoelectric fibers 5110 may include at least one selected from among piezoelectric fibers obtained from a piezoelectric material alone, fibers coated with a piezoelectric material, and combinations thereof. In the drawing, a piezoelectric fiber obtained from a piezoelectric material alone as the piezoelectric fiber 5110 is shown as an example. As another embodiment, unlike the drawing shown in the drawings, a general fiber coated with a piezoelectric material as the piezoelectric fiber 5110 or a combination of a piezoelectric fiber obtained from a piezoelectric material alone and a general fiber coated with a piezoelectric material may be used.

The piezoelectric material may be PVDF (polyvinylidene fluoride), lead zirconate titanate (PZT), or the like. The fibers coated with the piezoelectric material may be various fibers generally used. As an example for the understanding of the above example, various materials other than the above-mentioned examples can be used.

Piezoelectric material refers to a material in which the polarization of electric charge is generated by mechanical deformation or, on the other hand, mechanical deformation is caused by an electric field. Piezoelectric effect is the phenomenon that the polarization of charge is generated by mechanical deformation or, conversely, the mechanical deformation occurs by electric field. For example, as shown in the figure, when a piezoelectric material having a polarization in the Z-axis direction (or upward in the drawing) is elongated by an external force, a negative charge and a positive charge A polarization phenomenon of a charge induced by a magnetic field is induced. Also, when the piezoelectric material is compressed in length by an external force, a polarization phenomenon of positive and negative charges induced in the upper and lower portions of the piezoelectric material appears.

That is, when tensile and compressive are repeatedly applied to the piezoelectric material, the polarization of the electric charge generated in the piezoelectric material is repeatedly changed in polarity. With repeated tension and compression, the piezoelectric material can generate alternating electrical signals. The piezoelectric material disposed on the surface of the object according to the change of the length may undergo mechanical deformation when the piezoelectric material is disposed on the surface of the object whose elongation and compression are repeated. Due to the mechanical deformation, the polarization of electric charges may occur in the piezoelectric material. In other words, when the piezoelectric material is disposed on the surface of the object and the object is repeatedly stretched or compressed, the piezoelectric material disposed on the surface of the object repeatedly experiences tension and compression. When the piezoelectric material is repeatedly subjected to tension and compression, the polarity of the charge generated in the piezoelectric material is changed repeatedly. With repeated tension and compression, the piezoelectric material can generate alternating electrical signals.

Next, referring to FIG. 36 (b), when the fabric is woven using the piezoelectric fibers 5110, the piezoelectric fibers 5110 may cross each other to form a curved surface. As shown in the drawing, the piezoelectric fiber 5110 can be divided into an upper portion 5114 and a lower portion 5116 around a central surface 5112 whose length is not deformed. In this case, when a tensile force is applied to the piezoelectric fiber 5110 as an external force, the length of the upper portion 5114 is increased and the length of the lower portion 5116 is contracted.

As another example, when compressive force is applied to the piezoelectric fiber 5110 as an external force, the upper portion 5114 is contracted in length and the lower portion 5116 is increased in length, unlike the case shown in the drawings. Polarization phenomena of charges generated in the upper portion 5114 and the lower portion 5116 by the tensile force or the compressive force have opposite polarities.

In this way, the piezoelectric fibers can generate electrical energy.

Next, a fabric woven with piezoelectric fibers that generate electric energy by deformation by an external force as described above will be described with reference to Figs. 37 and 38. Fig.

37 and 38 illustrate a fabric including piezoelectric fibers according to one embodiment of the present invention.

The fabric of Fig. 37 is composed of yarns in which some of the weft yarns and the warp yarns are made of piezoelectric fibers, and the fabric of Fig. 38 is formed of yarns including both of the weft yarns and the warp yarns.

37 (a) is a conceptual diagram of an energy harvesting apparatus according to an embodiment of the present invention. 37 (b) is a view showing a stack structure of the weft yarn and the warp yarn. Referring to FIG. 37 (a), the energy harvesting apparatus 5200 includes a fabric 5250. In some embodiments, the energy harvesting device 5200 may further optionally include a first electrode 5220 and a second electrode 5230. In this case, the energy harvesting apparatus 5200 may further include a power storage unit 5240.

Fabric 5250 is woven into a plurality of chambers. At least some of the plurality of chambers include fibers 5210A that generate electrical energy by deformation by an external force. In one embodiment, the fibers 5210A may comprise fibers that produce electrical energy having different polarities due to the deformation by the external force. In other words, the fibers 5210A may comprise fibers wherein the polarization of the charge occurs opposite to each other when the same external force is applied. Hereinafter, these fibers are referred to as a first fiber and a second fiber, respectively. The first fiber and the second fiber may be obtained, for example, from piezoelectric fibers that have been polarized in opposite directions, respectively. Further, the fibers 5210A may include fibers having negative voltage portions when pulled on both sides and portions having positive voltage portions when contracted. In one example, the fibers can be obtained by laminating the first fibers or by laminating the second fibers. As another example, the fibers may be obtained by mixing and laminating the first fibers and the second fibers. Each of the first fibers or the second fibers to be laminated may have polarities of different sizes. The fibers 5210A may also include fibers having positive voltage portions when drawn to both sides and negative voltage portions when contracted. In one example, the fibers can be obtained by laminating the first fibers or by laminating the second fibers. As another example, the fibers may be obtained by mixing and laminating the first fibers and the second fibers. Each of the first fibers or the second fibers to be laminated may have polarities of different sizes. In the figure, the plurality of yarn-woven fabrics 5250 comprising the fibers 5210A and the general fibers 5210B that produce the electrical energy by the deformation by the external force as the fabric 5250 are represented as an example have. As another example, as shown in the figures, the fabric 5250 may be woven into the plurality of yarns including only the fibers 5210A.

The first electrode 5220 and the second electrode 5230 may be spaced apart from each other on the surface of the fiber 5210A. The first electrode 5220 and the second electrode 5230 can perform the function of providing the electric energy generated by the fiber 5210A to the external circuit from the deformation due to the external force. In one embodiment, the first electrode 5220 and the second electrode 5230 may provide the electrical energy generated by the fiber 5210A to the power storage unit 5240 from the deformation by the external force. The materials, functions, structures, and positional relationships of the first electrode 5220 and the second electrode 5230 are the same as those of the first electrode 5120 and the second electrode 5130 described with reference to FIG. The detailed description thereof will be omitted for convenience of explanation.

The power storage unit 5240 may be electrically connected to the first electrode 5220 and the second electrode 5230. Power storage unit 5240 can store the electrical energy generated by fiber 5210A. In one embodiment, the first electrode 5220 and the second electrode 5230 may be electrically connected to different electrodes of the power storage unit 5240, respectively. In the drawing, a power storage unit 5240 including a first electrode 5241 and a second electrode 5242 is illustrated as an example of a power storage unit 5240. The first electrode 5241 and the second electrode 5242 may be electrically connected to the first electrode 5220 and the second electrode 5230, respectively. In this case, an alternating electrical signal generated by the fiber 5210A due to the deformation may be stored in the power storage unit 5240 through the first electrode 5241 and the second electrode 5242. [

In one embodiment, power storage unit 5240 includes at least one diode (not shown) that receives current generated by fiber 5210A and at least one capacitor (not shown) that stores the current output from the diode . The diode rectifies the AC electrical signal generated by fiber 5210A and provides it to the capacitor, which can store electrical energy from the rectified electrical signal.

Referring to Figure 37 (b), the fabric 5250 woven with the plurality of yarns comprising the fibers 5210A can generate electrical energy by deformation by external forces. In one embodiment, the energy harvesting device 5200 can harvest the energy at the intersection of the weft and warp yarns. Fabric 5250 may be woven, for example, by crossing a warp and a warp. In this case, the weft and warp meet at the intersection. The fibers 5212A included in the weft yarns and the fibers 5214A included in the warp yarns at the intersections form a stack structure. In this case, the fabric 5250 can generate the electrical energy by the deformation by the external force. In one embodiment, for the same external force, the fibers 5212A included in the weft yarns and the fibers 5214A included in the warp yarns can generate electrical energy having different characteristics. For example, as shown in the figure, the fibers 5212A included in the weft yarns may be formed of a portion having a negative voltage when drawn to both sides and a portion having a positive voltage when contracted. The fibers 5214A included in the warp yarn may be formed of a portion having a positive voltage when drawn to both sides and a portion having a negative voltage when contracted. In this case, a negative voltage may be applied to the first electrode 5220, and a positive voltage may be applied to the second electrode 5230. When the fabric 5250 is repeatedly stretched and compressed, the polarity of the voltage applied to the first electrode 5220 and the second electrode 5230 is repeatedly changed. An AC electrical signal may be generated at both ends of the first electrode 5220 and the second electrode 5230. As another example, as shown in the drawings, the fibers 5212A included in the weft yarns may be composed of a portion that is positive voltage and a portion that is negative voltage when contracted. The fibers 5214A included in the warp yarns may be formed of a portion having a negative voltage when drawn to both sides and a portion having a positive voltage when contracted.

As described above, when the fibers 5210A having different characteristics are used alternately to the weft yarns and the warp yarns, the energy harvesting apparatus 5200 generates electric energy according to the movement, contraction, expansion, etc. of the wool structure at the intersections do. The plain weave structure, which crosses the weft and warp yarns one by one, is structurally robust and can collect a large amount of energy in the same area compared to other structures because there are many intersections between the weft yarn and the warp yarns. The weft and warp yarns can be processed in a flexible and maximally resilient form. The material, function, structure and characteristics of the fiber 5212A and the fiber 5214A are substantially the same as those of the fiber 5110A described above with reference to Fig. 1, For the sake of simplicity.

With the advancement of medical technology, a number of sensors are in the process of being inserted or attached to the human body. Also, due to the development of portable electronic devices, there is an increasing demand and research for electronic devices that can be worn on human body or clothes such as wearable computer, smart wear, and the like. Electronic devices such as human body attachment sensors, wearable computers, and smart wear require power supply media for driving them. The slower power generation rate of the power supply medium causes a problem of the necessity of continuous replacement of the power supply and the increase of the maintenance cost. When energy is supplied to the above-mentioned electronic devices through energy harvesting technology using human body energy, it is possible to supply energy continuously without being restricted by time and space. The fabric 5250 comprising the fibers 5210A may be worn on the human body in the form of a garment or the like. In this case, the energy harvesting device using the fabric 5250 can harvest the human energy generated by conscious or unconscious behavior of a person. This allows for continuous power supply devices that are free of time and space constraints. In general, the human body has characteristics of extremely low frequency movement, intermittent movement in non-resonance mode, and free direction movement. Conventional energy collection devices are designed to efficiently capture energy when the frequency of the collection device matches the frequency of the given environment at high frequencies. Therefore, when the energy collecting device is designed based on the motion of the human body, the energy collection efficiency is very low and it is insufficient to drive the electronic device. The energy harvesting apparatus 5200 described above with reference to FIG. 37 has many intersection points, so that it is possible to obtain sufficient energy for driving the electronic apparatus by increasing energy collection efficiency.

Referring again to FIG. 37, the first electrode 5220 and the second electrode 5230 may be spaced apart from each other on the surface of the fiber 5210A. In the figure, a first electrode 5220 disposed on one side of the fiber 5210A included in the weft yarn and a second electrode 5230 disposed on one side of the fiber 5210A included in the warp yarn are shown as an example. The first electrode 5220 and the second electrode 5230 may be disposed on one side of the fiber 5210A to efficiently provide electrical energy generated at the intersection to the power storage unit 5240. [ When the weft yarns and the numerous crossing points of the warp yarns are connected to each other, there are problems such as complicated wiring structure, difficulty in fabrication, and reduction in efficiency. The first electrode 5220 and the second electrode 5230 may be disposed on the one surface of the fiber 5210A to solve the above problem. The first electrode 5220 and the second electrode 5230 may be connected to the power storage unit 5240 to store electrical energy generated by the fiber 5210A.

38 is a view showing an energy harvesting apparatus according to yet another embodiment. Fig. 38 shows an example of configuring a piezoelectric material in a wool-like form so that the generated electric energy is not canceled each other. Referring to FIG. 38, the energy harvesting apparatus 5300 includes a fabric 5350. In some embodiments, the energy harvesting device 5300 may further optionally include a first electrode 5320 and a second electrode 5330. In this case, the energy harvesting apparatus 5300 may further include a power storage unit 5340.

The fabric 5350 is woven into a plurality of chambers. At least some of the plurality of chambers include fibers 5310A that generate electrical energy by deformation by external force. The fabric 5350 including the fibers 5310A can generate electrical energy by deformation by an external force as described above with reference to Fig. In one embodiment, the fibers 5310A may comprise fibers 5312A, 5314A that produce electrical energy having opposite polarities due to the deformation by the external force. For example, the fiber 5312A can be formed of a portion that has a negative voltage when pulled to both sides and a portion that has a positive voltage when it contracts. Fiber 5314A can be made of a positive voltage portion when pulled on both sides and a negative voltage portion when contracted. As another example, the fibers 5312A can be made up of a positive voltage portion when drawn to both sides and a negative voltage portion when contracted. The fiber 5314A can be made of a negative voltage portion when pulled on both sides and a positive voltage portion when contracted. The figure shows, by way of example, a fabric woven from warp yarns comprising a weft yarn comprising fibers 5312A as fabric 5350 and fibers 5314A. In this case, the weft and warp meet at the intersection.

At the intersection, the fibers 5312A and the fibers 5314A form a stack structure with each other. By the stacked structure of the fibers 5312A and the fibers 5314A at the intersection, the fabric 5350 makes it possible to effectively generate electrical energy from deformation due to external forces. When the fibers 5312A and 5314A having different characteristics are used alternately in the weft yarns and the warp yarns, the energy harvesting device 5300 generates electric energy according to the movement, contraction, expansion, etc. of the wool structure at the intersection do. The plain weave structure, which crosses the weft and warp threads one by one, is structurally robust and has many of the intersections between weft and warp. Therefore, a plain weave structure that crosses the warp and weft can collect a lot of energy in the same area as other structures. The weft and warp yarns can be processed in a flexible and maximally resilient form.

The first electrode 5320 and the second electrode 5330 may be spaced apart from each other on the surface of the fiber 5310A. In one embodiment, the first electrode 5320 and the second electrode 5330 may be disposed on one side of the fibers 5312A included in the weft yarns and the fibers 5314A included in the warp yarns, respectively. The first electrode 5320 and the second electrode 5330 can perform the function of providing the electric energy generated by the fiber 5310A to the external circuit due to the deformation caused by the external force. The first electrode 5320 and the second electrode 5330 may provide the electrical energy generated by the fiber 5310A to the power storage unit 5340 due to the deformation caused by the external force. The materials, functions, structures, and positional relationships of the first electrode 5320 and the second electrode 5330 are the same as those of the first electrode 5220 and the second electrode 5230, The detailed description thereof will be omitted for convenience of explanation.

The power storage unit 5340 may be electrically connected to the first electrode 5320 and the second electrode 5330. Power storage unit 5340 can store the electrical energy generated by fiber 5310A. In one embodiment, the first electrode 5320 and the second electrode 5330 may be electrically connected to different electrodes of the power storage unit 5340, respectively. In the drawing, a power storage unit 5340 including a first electrode 5341 and a second electrode 5342 as an electricity storage unit 5340 is shown as an example. The first electrode 5320 and the second electrode 5330 may be electrically connected to the first electrode 5341 and the second electrode 5342, respectively. In this case, an AC electrical signal generated by the fiber 5310A due to the deformation may be stored in the power storage unit 5340 through the first electrode 5341 and the second electrode 5342. In one embodiment, the power storage unit 5340 may include a diode (not shown) and a capacitor (not shown). The diode rectifies the AC electrical signal generated by the fiber 5310A to provide it to the capacitor, which can store electrical energy from the rectified electrical signal. In some other embodiments, the charger may be omitted if the AC electrical signal is directly used in a circuit such as a wireless sensor network using electrical energy. The function, structure, and characteristics of the power storage unit 5340 are substantially the same as those of the power storage unit 5140 described above with reference to FIG. 1. Therefore, detailed description thereof will be omitted for the sake of convenience.

Referring again to Fig. 38, an energy harvesting apparatus 5300 including fibers 5312A and 5314A generating electrical energy having different polarities or intensities by deformation by external force is shown as an example. The fibers 5312A and 5314A may form a stacked structure at the intersection. The fibers 5312A and 5314A can generate electrical energy of opposite polarity due to the movement, contraction, expansion, etc. of the wool structure at the intersection. For example, when the woolen structure contracts, one of the first electrode 5320 and the second electrode 5330 may have a relatively positive potential, and the other electrode may have a relatively negative potential . In this case, when the woolen structure expands, the one electrode has a relatively negative potential, and the other electrode has a relatively positive potential. That is, when repetitive stretching and compression are applied to the fabric 5350, the polarity of the voltage applied to the first electrode 5320 and the second electrode 5330 is changed repeatedly. Thus, an AC electric signal can be generated at both ends of the first electrode 5320 and the second electrode 5330.

The energy harvesting device 5300 uses a stack structure at the intersection of the weft yarn and the warp yarn for more energy harvesting when given an external force deformation. The weft yarns and the warp yarns comprise fibers 5312A and fibers 5314A, respectively. The first electrode 5320 and the second electrode 5330 are connected to the fiber 5312A and the fiber 5312A to efficiently transmit the electrical energy generated by the fiber 5312A and the fiber 5314A at the intersection to the power storage unit 5340. [ May be disposed on the above-mentioned one surface of the base plate 5314A. In order to provide electrical energy generated from the fibers 5312A and 5314A to the power storage unit 5340, complicated wiring connecting the weft yarns and innumerable crossing points of the warp yarns may be required. The complicated wiring can make it difficult to fabricate the energy harvesting device 5300, or reduce the energy collection efficiency. When the first electrode 5320 and the second electrode 5330 are placed on the one side of the fiber 5312A and the fiber 5314A, the first electrode 5320 and the second electrode 5330 are connected to the power storage unit 5340). That is, the power storage unit 5340 can store electric energy generated in the fiber strand unit. Through this, the energy harvesting apparatus 5300 can be easily manufactured and the energy collection efficiency can be improved.

In other words, if the first electrode 5320 and the second electrode 5330 are disposed on the one surface of the fiber 5312A and the fiber 5314A, the electrical connection is not made at each intersection but the electrical wiring is connected to the fiber strand unit . For example, the fiber 5312A can be a portion of negative voltage when pulled on both sides and a portion of positive voltage when contracted. Fiber 5314A can be made of a positive voltage portion when pulled on both sides and a negative voltage portion when contracted. In this case, when the fabric 5350 is contracted, a negative voltage may be applied to the first electrode 5320, and a positive voltage may be applied to the second electrode 5330. When the fabric 5350 is repeatedly stretched and compressed, the polarity of the voltage applied to the first electrode 5320 and the second electrode 5330 is changed repeatedly. Thus, an AC electric signal can be generated at both ends of the first electrode 5320 and the second electrode 5330. The first electrode 5320 and the second electrode 5330 disposed on the one surface of the fiber 5312A and the fiber 5314A are connected to the first electrode 5341 and the second electrode 5342 of the power storage unit 5340, When connected, power storage unit 5340 can store the AC electrical signal. In other words, if repetitive stretching and compression are applied to the fabric 5350, the polarity of the voltage applied to the first electrode 5320 and the second electrode 5330 will be repeatedly changed. That is, the first electrode 5320 and the second electrode 5330 have a relatively negative or positive electric potential in accordance with the contraction and expansion of the wool structure of the fabric 5350. When the first electrode 5320 and the second electrode 5330 are connected to the first electrode 5341 and the second electrode 5342, the power storage unit 5340 is connected to the fiber 5312A and the fiber 5314A at the intersection It is possible to store the generated electric energy. Accordingly, the energy harvesting apparatus 5300 can efficiently convert the human body energy generated by the extremely low-frequency movement of the human body, the intermittent movement of the non-resonant mode, the free direction movement, and the like into electric energy. Since the energy harvesting device 5300 forms the wool structure after the first electrode 5320 and the second electrode 5330 are formed in the fiber stranded state, the time required for the electrode forming step can be shortened. Also, the first electrode 5320 and the second electrode 5330 connected in a fiber strand unit are simple in structure, and the designer can easily place the power storage unit 5340 at a desired portion. Therefore, the proposed electrode integration structure is suitable for a case where the energy harvesting apparatus 5300 is used in a wide area in a form that can be worn on a garment or a human body. The energy harvesting apparatus 5300 using the electrode integrated structure design proposed in this specification has a simple connection because the electrodes 5320 and 5330 are located on the surface of the fiber strands. In addition, since the energy harvesting apparatus 5300 can easily select the position where the power storage unit 5340 can be attached, it is possible to unconsciously harvest the human body energy with a high wearing feeling.

Body joints, sides, abdomen, and repeatedly repeated expansion and contraction. At this time, the clothing around the body repeatedly expands and contracts according to the movement of the body. If the garment comprises fibers 5310A, fiber 5310A will repeat expansion and contraction as the body moves. In this case, the fiber 5310A generates alternating electrical energy at the intersection of the fiber 5312A and the fiber 5314A, and the generated alternating electrical energy can be collected by the electricity accumulator 5340. In one embodiment, the fibers 5310A can be fibers that have been processed into a flexible, maximally resilient form. The energy harvesting apparatus 5300 can efficiently collect energy generated due to volume and pressure changes such as bending, contraction, expansion, and the like occurring in human body motion. Also, the energy harvesting apparatus 5300 can supply the energy required for the electronic apparatus by using the energy due to the volume and the pressure change such as bending, shrinkage, expansion, etc. occurring in the human body motion.

The figure shows, by way of example, a fabric 5350 woven into a plurality of yarns comprising fibers 5312A, 5314A that produce electrical energy having different polarities or intensities by deformation by external forces as fabric 5350 . As another example, as shown in the figures, fabric 5350 may be woven into a plurality of yarns including fibers 5312A and 5314A and common fibers 5210B. In one example, fabric 5350 may be woven using fibers 5312A and 5210B as weft yarns and fibers 5314A and fibers 5210B as warp yarns. In this case, fabric 5350 can be woven using fibers 5312A, fibers 5314A, and fibers 5210B as separate members. Alternatively, the fabric 5350 can be woven using fibers obtained by mixing fibers 5312A and 5210B and fibers obtained by mixing fibers 5314A and 5210B, respectively, as weft yarns and warp yarns. The above example is for the sake of understanding, and in addition to the above example, fabric 5350 can be woven in a variety of ways using fibers 5312A, 5314A and fiber 5210B. That is, as long as the fibers 5312A and 5314A, which generate electrical energy having different polarities or intensities by the above-described deformation, are arranged in the weft yarns and the warp yarns, there is no limitation in the arrangement method.

As described above, an energy harvesting device can be manufactured by manufacturing piezoelectric fibers using a ferroelectric layer, and weaving the fabrics using such piezoelectric fibers.

The energy harvesting apparatus thus manufactured can be used in various fields in which the fabric is used to perform energy harvesting. For example, when an energy harvesting device is used in clothes, it can harvest energy using human body movements.

Further, if the warp yarns of the fabric are made of piezoelectric fibers and the weft yarns are made of functional fibers such as carbon fibers, a fabric exhibiting the function of functional fibers used as weft yarns can be obtained by energy harvesting.

Hereinafter, an embodiment in which a fabric comprising a combination of a piezoelectric fiber and a general fiber is applied using the above-described method will be described.

First embodiment: tire cord

Example 2: Spandex

Example 3: Socks and sneakers

First Embodiment

Early automotive tires were made out of pure rubber, but there were homework assignments that required short life spans. So I put the material of the fiber material inside the rubber to improve the durability, this became the beginning of the tire cord now. At first, I used a piece of thick cotton yarn woven with a tire cord, which was easily worn away by friction between tire cords.

Thereafter, durability, tensile strength of the fiber itself, resistance to water resistance and heat are required. On the other hand, synthetic fibers such as rayon, nylon (polyamide) and polyester are sequentially used it started. The material of the tire cord which is mainly used today is polyester nylon.

At present, the material of radial tire cord for automobile is excellent in shape stability and polyester cord of relatively low price is mainly composed of 90%. Nylon cord is used mainly for truck, bus, heavy equipment and bias tires of aircraft because of strength and heat resistance, and it is mainly used for tires such as bicycles and motorcycles.

39 shows a tire cord inside the tire.

As described above, in order to extend the life of the tire, a tire cord may be incorporated in the tire, and a tire cord such as a steel tire cord, a polyester tire cord, and a bead wire tire cord may be incorporated as shown in FIG.

Among them, polyester tire cord is manufactured using polyester which is a synthetic fiber, and a tire cord capable of producing the advantages of polyester and the advantages of piezoelectric fiber can be manufactured by combining the above-mentioned piezoelectric fibers with a polyester tire cord.

Figure 40 shows a fabric woven using polyester and piezoelectric fibers according to an embodiment of the present invention.

Referring to FIG. 40, a piezoelectric fiber 610 may be used as a warp yarn of a fabric constituting a tire cord, and a polyester 620 may be used as a weft yarn. The piezoelectric fiber 610 may be used as the weft yarn, and the polyester 620 may be used as the warp yarn. In addition, some of the plurality of warp yarns may be made of polyester 620, the rest of the plurality of weft yarns may be used as the piezoelectric fibers 610, some of the plurality of warp yarns may be made of polyester 620, And the polyester 620 and the piezoelectric fiber 610 can be used in various combinations such as a part of the piezoelectric fiber 610. However, polyamide fibers as well as polyamide fibers and polyvinyl alcohol fibers may be used.

Such a woven polyester polyester tire cord not only exhibits tensile strength, water resistance and resistance to heat, which are advantages of the polyester 620, but also includes the piezoelectric fibers 610, Energy can be harvested by pressure. Thus, it is possible to acquire the electric energy necessary for the automobile by collecting energy during running of the automobile.

Second Example

As another example, piezoelectric fibers can be combined with spandex.

Spandex is a type of polyurethane fiber, and since 1959 it has started to produce under the brand name Lycra in the name of spandex, the elastic urethane fiber made by DuPont of the United States. It is an unusual fiber with elasticity similar to rubber. It has very high tensile strength (ultimate strength). That is, it has a quality higher than that of a conventional rubber thread, such as being lighter than an elastic band and having a strong anti-aging property. Therefore, it is widely used as raw yarn such as underwear, swimwear, and sportswear using rubber seals.

Such fabrics can be fabricated by combining spandex and piezoelectric fibers and fabricating clothes using these fabrics.

40, the piezoelectric fiber 610 may be used as the warp yarn of the fabric, and the spandex 630 may be used as the weft yarn. Further, the piezoelectric fiber 610 may be used as the weft yarn, and the spandex 630 may be used as the warp yarn. In addition, a part of the plurality of weft yarns may be spandex 630, the rest of the weft yarns may be used as the piezoelectric fiber 610, a part of the plurality of warp yarns may be spandex 630, The piezoelectric fiber 610 and the spandex 630 can be woven using various combinations such as using the spandex 630 and the piezoelectric fiber 610.

The fabric thus woven exhibits high tensile strength and strong aging resistance which are advantages of the spandex 630. Since the piezoelectric fabric 610 is included, an external force is applied to the piezoelectric fibers 610 according to the movement of the human body, Energy harvesting is possible.

If the fabric woven as described above is used for clothing such as underwear that sticks to the human body, the energy hubbing can be performed by all the movements of the human body, and the biometric information of the human body can be measured as follows. For example, the electrocardiogram measuring apparatus can be configured using the fabric as described above.

An electrocardiogram measuring apparatus according to an embodiment of the present invention may include a human body joint, an electrocardiogram measuring electrode, an energy harvesting unit, a charge unit, and an electrocardiogram measuring / transmitting unit.

The body joint is a patch-shaped nonwoven fabric having a thin thickness. At least three electrocardiogram electrodes are included on one side of the patch for sensing the heartbeat (biological motion) of the patient as an analog signal (vibration) A biocompatible adhesive may be applied to the patch surface.

At this time, the electrocardiogram measuring electrodes generate vibrations (analog signals) in accordance with heartbeats (movements of living bodies) rather than general electrodes, and various electrodes for biometrics such as pressure sensors are applicable.

That is, the vibration (vibration signal) generated through the electrocardiogram measuring electrode is converted into electric energy (piezoelectric sensor), and the corresponding biometric information is acquired through the vibration.

Next, the energy harvesting portion is constituted to generate electric energy by using the motion of the human body, and this corresponds to the piezoelectric fiber.

Then, the battery unit (charging unit) charges the electric energy output from the energy harvesting unit, and the electric energy thus charged is supplied to the electrocardiograph measurement / transfer unit. Here, the battery section (charge section) is a charge section (power section) in terms of supplying the electric energy to the electrocardiograph measurement / transfer section and a charge section in terms of storing the electric energy according to the biomedical motion. It can be called either.

By converting the biological movement as described above into electric energy, the inconvenience such as battery replacement can be solved.

Next, the electrocardiogram measuring / transmitting unit measures the electrocardiogram and transmits the measurement result to the outside.

In the above description, the heartbeat is taken as an example. However, the electric energy can be charged through various movements of the living body, and the heartbeat can be used for measuring the living body information (for example, body temperature measurement). It is also possible to fill electrical energy through a first biological movement (e.g., heartbeat) and use it to measure other biometric information (e.g., body temperature measurement)

Third Example

As another example, piezoelectric fibers can be combined with fibers used in socks or shoes. That is, it combines piezoelectric fibers with cotton or nylon which is often used in socks and shoes.

As a method of producing a fabric by combining a cotton or nylon and a piezoelectric fiber, a method of woven a fabric using a part of the piezoelectric fibers as in the first and second embodiments can be used. Alternatively, a part of the yarn making up the fabric may be made of piezoelectric fibers and the remaining part of the fabric may be made of cotton or nylon.

In this way, when a sock or a shoe is made using a fabric containing a piezoelectric fiber, electric energy is generated by the piezoelectric fiber every time the person walks, so energy harvesting can be performed.

The present invention can also be embodied as computer-readable codes on a computer-readable recording medium. A computer-readable recording medium includes all kinds of recording apparatuses in which data that can be read by a computer system is stored. Examples of the computer-readable recording medium include a ROM, a RAM, a CD-ROM, a magnetic tape, a floppy disk, an optical data storage device, and the like, and may be implemented in the form of a carrier wave (for example, transmission over the Internet) . In addition, the computer-readable recording medium may be distributed over network-connected computer systems so that computer readable codes can be stored and executed in a distributed manner. In addition, functional programs, codes, and code segments for implementing the present invention can be easily inferred by programmers of the technical field to which the present invention belongs.

The tire cord and the spandex and the energy harvesting apparatus using the ferroelectric material manufactured using the fiber manufacturing method described above are not limited to the configuration and the method of the embodiments described above, All or some of the embodiments may be selectively combined so that various modifications can be made.

Claims (20)

A method of making a composite fabric tire cord that is woven with a plurality of fibers to reinforce the tire,
The plurality of fibers comprising at least one synthetic fiber and at least one piezoelectric fiber; And
And woven the composite fabric tire cord using the plurality of fibers,
Wherein the piezoelectric fibers generate electrical energy by deformation due to an external force applied to the piezoelectric fibers,
Wherein the synthetic fibers comprise at least one of polyamide fibers, polyester fibers, and polyvinyl alcohol fibers,
Further comprising the step of fabricating the piezoelectric fiber by a fiber manufacturing method using a ferroelectric layer before the step of providing the fiber,
The fiber manufacturing method uses at least one of rolling, extrusion and drawing,
The method for manufacturing the ferroelectric layer includes a step of forming the ferroelectric layer through a phase change step in which the crystal structure of the ferroelectric is set to?
The ferroelectric layer phase change step is performed by the first method or the second method,
In the first method,
A temperature raising step of raising the temperature of the ferroelectric to a temperature equal to or higher than a temperature which forms a? Phase crystal;
A first temperature decreasing step of monotonically decreasing the temperature of the ferroelectric to a? Phase crystal temperature; And
And a second temperature decreasing step of rapidly lowering the temperature of the ferroelectric substance,
In the second method,
A temperature raising step of raising the temperature of the ferroelectric to a temperature which forms a? Phase crystal; And
A temperature lowering step of rapidly lowering the temperature of the ferroelectric; ≪ RTI ID = 0.0 &
A method of making a spandex fabric woven from a plurality of fibers,
The plurality of fibers comprising at least one spandex and at least one piezoelectric fiber; And
And woven the spandex fabric using the plurality of fibers,
Wherein the piezoelectric fibers generate electrical energy by deformation due to an external force applied to the piezoelectric fibers,
Further comprising the step of fabricating the piezoelectric fiber by a fiber manufacturing method using a ferroelectric layer before the step of providing the fiber,
The fiber manufacturing method uses at least one of rolling, extrusion and drawing,
The method for manufacturing the ferroelectric layer includes a step of forming the ferroelectric layer through a phase change step in which the crystal structure of the ferroelectric is set to?
The ferroelectric layer phase change step is performed by the first method or the second method,
In the first method,
A temperature raising step of raising the temperature of the ferroelectric to a temperature equal to or higher than a temperature which forms a? Phase crystal;
A first temperature decreasing step of monotonically decreasing the temperature of the ferroelectric to a? Phase crystal temperature; And
And a second temperature decreasing step of rapidly lowering the temperature of the ferroelectric substance,
In the second method,
A temperature raising step of raising the temperature of the ferroelectric to a temperature which forms a? Phase crystal; And
A temperature lowering step of rapidly lowering the temperature of the ferroelectric; ≪ / RTI > A method of manufacturing an energy harvesting device comprising the method of manufacturing a composite fabric tire cord according to any one of claims 1 to 5,
And electrically connecting a power storage unit that stores electric energy generated from the piezoelectric fiber to the piezoelectric fiber. delete delete delete delete delete delete delete delete delete delete delete delete delete delete delete delete delete

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