WO2017126501A1 - 流体分離膜、流体分離膜モジュールおよび多孔質炭素繊維 - Google Patents
流体分離膜、流体分離膜モジュールおよび多孔質炭素繊維 Download PDFInfo
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- WO2017126501A1 WO2017126501A1 PCT/JP2017/001408 JP2017001408W WO2017126501A1 WO 2017126501 A1 WO2017126501 A1 WO 2017126501A1 JP 2017001408 W JP2017001408 W JP 2017001408W WO 2017126501 A1 WO2017126501 A1 WO 2017126501A1
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- porous carbon
- carbon fiber
- separation membrane
- fluid separation
- resin
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Definitions
- the present invention relates to a fluid separation membrane, a fluid separation membrane module, and a porous carbon fiber.
- Membrane separation is used as a method for selectively separating and purifying specific components from various mixed gases and liquids.
- Membrane separation methods are attracting attention because they are energy-saving compared to other fluid separation methods.
- membrane separation methods are beginning to be used in the process of separating and purifying the water of impurities contained in alcohol and acetic acid.
- separation and purification can be performed at high pressure. It has been demanded.
- a hollow fiber-like separation membrane As a separation membrane used in the membrane separation method, a hollow fiber-like separation membrane has been proposed, and it is a composite of a sheet-like separation membrane and a ceramic substrate because it has a large membrane area per unit volume and can be manufactured continuously.
- separation membranes for example, Patent Documents 1 and 2).
- the present invention has been made in view of the above-described conventional situation, and an object to be solved is to provide a fluid separation membrane having high compressive strength in the fiber cross-sectional direction.
- the present invention relates to the following ⁇ 1> to ⁇ 14>.
- ⁇ 1> A fluid separation membrane in which an organic polymer layer is formed on the surface of a porous carbon fiber having a co-continuous porous structure.
- ⁇ 2> The fluid separation membrane according to ⁇ 1>, wherein the entire porous carbon fiber has the bicontinuous porous structure.
- ⁇ 3> The fluid separation membrane according to ⁇ 1> or ⁇ 2>, wherein the average pore diameter of the entire porous carbon fiber measured by a mercury intrusion method is 30 to 5,000 nm.
- ⁇ 4> The fluid separation according to any one of ⁇ 1> to ⁇ 3>, wherein an average pore diameter of the surface of the porous carbon fiber measured by surface observation with a scanning electron microscope is 2 to 500 nm film.
- ⁇ 5> The fluid separation membrane according to any one of ⁇ 1> to ⁇ 4>, wherein the structural period of the bicontinuous porous structure is 10 to 10,000 nm.
- ⁇ 6> The fluid separation membrane according to any one of ⁇ 1> to ⁇ 5>, wherein a half width of an X-ray scattering intensity peak of the porous carbon fiber is 5 ° or less.
- the organic polymer layer is an aromatic polyimide, cellulose acetate, polysulfone, aromatic polyamide, polyetherimide, polyethersulfone, polyacrylonitrile, polyphenylene sulfide, polyetheretherketone, polytetrafluoroethylene, or polyvinylidene fluoride.
- the fluid separation membrane according to any one of ⁇ 1> to ⁇ 6>, which is a layer comprising one or more organic polymers selected from the group consisting of these and derivatives thereof.
- the organic polymer layer is a layer containing one or more organic polymers selected from the group consisting of aromatic polyimide, aromatic polyamide and derivatives thereof.
- the fluid separation membrane according to any one of ⁇ 9> A fluid separation membrane module in which a plurality of fluid separation membranes according to any one of ⁇ 1> to ⁇ 8> are accommodated in a casing.
- ⁇ 10> A porous carbon fiber having a co-continuous porous structure as a whole.
- ⁇ 11> The porous carbon fiber according to ⁇ 10>, wherein the total average pore diameter measured by a mercury intrusion method is 30 nm to 5,000 nm.
- ⁇ 12> The porous carbon fiber according to ⁇ 10> or ⁇ 11>, wherein the average pore diameter of the surface measured by surface observation with a scanning electron microscope is 2 to 500 nm.
- a fluid separation membrane having high compressive strength in the fiber cross-sectional direction (direction orthogonal to the fiber axis) can be provided, and the durability of the fluid separation membrane module can be enhanced.
- FIG. 1 is a schematic view showing the structure of the fiber cross section of the fluid separation membrane of the present invention.
- FIG. 2 is a scanning electron micrograph of the co-continuous porous structure of the porous carbon fiber of the present invention.
- Fluid separation membrane [Porous carbon fiber]
- the fluid separation membrane of the present invention (hereinafter sometimes simply referred to as “fluid separation membrane” or “separation membrane”) is based on porous carbon fibers having a co-continuous porous structure.
- the carbon component of the porous carbon fiber is preferably 60 to 90% by weight. If it is 60% by weight or more, the heat resistance and chemical resistance of the porous carbon fiber tend to be improved.
- the carbon component of the porous carbon fiber is more preferably 65% by weight or more. Further, if it is 90% by weight or less, the flexibility is improved, the bending radius is reduced, and the handleability is improved.
- the carbon component of the porous carbon fiber is more preferably 85% by weight or less.
- the weight ratio of the carbon component when carbon, hydrogen, and nitrogen components are measured by an organic elemental analysis method is used. If the total of carbon, hydrogen, and nitrogen components does not reach 100% by weight, it means that other elements such as oxygen are present.
- the bicontinuous porous structure is a structure in which branches and pores (voids) of the carbon skeleton are continuous and intertwined regularly three-dimensionally. Specifically, as illustrated in FIG. When a cross section obtained by cleaving a sample sufficiently cooled in liquid nitrogen with tweezers or the like is observed with a scanning electron microscope, the structure is such that the branches and voids of the carbon skeleton are continuously intertwined with each other.
- the carbon skeleton branches support the entire structure and the stress is dispersed throughout the fiber. Therefore, compression and bending in the fiber cross-sectional direction (direction perpendicular to the fiber axis) It has great resistance to external forces such as, and can improve compression strength and compression specific strength. Further, since the voids communicate three-dimensionally, they have a role as a flow path for supplying or discharging a fluid such as gas or liquid in the fiber cross-sectional direction and fiber axis direction.
- the co-continuous porous structure includes a lattice shape and a monolith shape, and is not particularly limited.
- the monolith shape is preferable because the compressive strength in the fiber cross-sectional direction tends to be improved in that the above effect can be exhibited.
- Monolithic form refers to a form in which the carbon skeleton forms a three-dimensional network structure in a co-continuous porous structure, and is caused by the removal of the aggregated and connected template particles, or conversely, the aggregated and connected template particles.
- irregular structures such as those formed by open voids and surrounding skeletons.
- the porous carbon fiber has a co-continuous porous structure as a whole, and pores are opened on the surface thereof.
- the fiber surface is opened, the pressure loss of the fluid in the fiber cross-sectional direction decreases, so that the permeation rate of the fluid separation membrane can be improved.
- the fiber surface has a concavo-convex structure, the adhesion with the organic polymer layer described later is improved by the anchor effect.
- having a co-continuous porous structure as a whole means that when the surface of the porous carbon fiber is observed at 10 arbitrary positions with a scanning electron microscope, the co-continuous porous structure exists at all positions, As described later, this means that pores having an average pore diameter of 2 nm or more are observed.
- a co-continuous porous structure may be present on at least one of the outer surface and the inner surface.
- the average diameter of the entire pores forming the co-continuous porous structure of the porous carbon fiber is preferably 30 nm or more because if the pressure is too small, the pressure loss in the fiber axis direction and the fiber cross-sectional direction increases and the fluid permeability decreases. 100 nm or more is more preferable.
- the average diameter of the whole pores is too large, the effect of the carbon branches supporting the entire structure is reduced and the compressive strength is reduced, so 5,000 nm or less is preferable, and 2,500 nm or less is more preferable. preferable.
- the average diameter of the whole pore is a measured value obtained by measuring the pore size distribution of the separation membrane by the mercury intrusion method.
- the mercury intrusion method pressure is applied to the pores of the co-continuous porous structure to infiltrate mercury, and the pore volume and specific surface area are determined from the pressure and the amount of mercury injected.
- the pore is assumed to be a cylinder, the pore diameter obtained from the relationship between the pore volume and the specific surface area is calculated.
- a pore diameter distribution curve of 5 nm to 500 ⁇ m can be obtained. Since the organic polymer layer described later has substantially no pores, the average diameter of the pores of the entire separation membrane is substantially the same as the average diameter of the pores of the co-continuous porous structure of porous carbon fibers. it can.
- the average pore diameter on the surface is preferably 2 nm or more, more preferably 10 nm or more, and further preferably 50 nm or more. If the surface pore diameter is too large, when the organic polymer layer is formed, the organic polymer may penetrate into the porous carbon fiber and may not be uniformly laminated on the surface. Therefore, the average pore diameter on the surface is preferably 500 nm or less, more preferably 400 nm or less, and further preferably 300 nm or less.
- the average pore diameter on the surface of the porous carbon fiber a measured value analyzed by surface observation with a scanning electron microscope is used. Specifically, an image obtained by observing the surface of the porous carbon fiber at 700,000 pixels or more at a magnification of 1 ⁇ 0.1 (nm / pixel) is obtained by branching the fiber surface with the image analysis software (carbon part). ) And pores (voids). Subsequently, the average value of the areas of the pores in the image is calculated, and the diameter of a perfect circle having the same area as the average area is defined as the average pore diameter.
- an image obtained by observing at 700,000 pixels or more at a magnification of 10 ⁇ 1 (nm / pixel) is used. calculate.
- the surface organic polymer layer is dissolved or decomposed with a solvent that can be dissolved or decomposed, or the temperature at which the structure of the porous carbon fiber does not change
- the surface of the porous carbon fiber is exposed by thermally decomposing and removing the organic polymer layer, and the average pore diameter on the surface is measured.
- the fluid separation membrane is sufficiently cooled in liquid nitrogen and cleaved with tweezers or the like to expose the fiber cross section. Subsequently, the average pore diameter can be calculated by the above-described method from an image observed with a scanning electron microscope and observed near the interface between the porous carbon fiber and the organic polymer layer.
- the porous carbon fiber it is preferable that pores on the surface communicate with the fiber center.
- the presence or absence of pore communication is confirmed by the following method. That is, the gas permeation rate of the porous carbon fiber is measured using a pure gas of carbon dioxide and nitrogen, and the gas permeation rate ratio CO 2 / N 2 is 1.0 or 0.80 (ie Knudsen diffusion) Mechanism), it is determined that the pores are in communication.
- the structural period of the co-continuous porous structure of the porous carbon fiber is preferably 10 to 10,000 nm.
- the porous carbon fiber having a structural period indicates that the porous structure is highly uniform, and means that the thickness of the carbon skeleton branches and the pore size are uniform. Thereby, the effect of improving the compressive strength of the porous carbon or the fluid separation membrane can be obtained.
- the thickness of the organic polymer layer can be made uniform even in the case of a coating stock solution (organic polymer solution) having a low concentration and viscosity. .
- the structural period is 10,000 nm or less, the carbon skeleton and pores become fine structures and the compressive strength is improved. Therefore, the structural period is more preferably 5,000 nm or less, and further preferably 3,000 nm or less.
- the structural period is 10 nm or more, the pressure loss at the time of flowing the fluid through the gap is reduced, and the permeation rate of the fluid is improved. Further, when the pressure loss is reduced, the effect of separation and purification can be achieved with more energy saving. Therefore, the structural period is more preferably 100 nm or more, and further preferably 300 nm or more.
- the structural period of the bicontinuous porous structure is calculated from the scattering angle 2 ⁇ at the peak top position of the scattering intensity obtained by making X-rays incident on the porous carbon fiber of the present invention and scattering at a small angle by the following equation. Is.
- the structural period is obtained by X-ray computed tomography (X-ray CT). Specifically, after performing a Fourier transform on a three-dimensional image photographed by X-ray CT, the two-dimensional spectrum is averaged to obtain a one-dimensional spectrum. The characteristic wavelength corresponding to the position of the peak top in the one-dimensional spectrum is obtained, and the structural period is calculated as its reciprocal.
- X-ray CT X-ray computed tomography
- the uniformity of the bicontinuous porous structure can be determined by the half width of the intensity peak of the X-ray scattering intensity of the porous carbon fiber.
- the half width of the peak is preferably 5 ° or less, more preferably 1 ° or less, and further preferably 0.1 ° or less.
- the half-width of the peak in the present invention means that the peak apex is point A, a straight line parallel to the vertical axis of the graph is drawn from point A, and the intersection of the straight line and the spectrum base line is point B , The width of the peak at the midpoint C of the line segment connecting points A and B. Moreover, the width of the peak here is the length between the intersections of the straight line passing through the point C and the scattering curve parallel to the baseline.
- the average porosity of the bicontinuous porous structure is preferably 20 to 80%.
- the average porosity is 700,000 at a magnification of 1 ⁇ 0.1 (nm / pixel) of a cross section of a porous carbon fiber in which an embedded sample is precisely formed by a cross section polisher method (CP method).
- CP method cross section polisher method
- the porous carbon fiber has a hollow portion, the area of the hollow portion is not included in the area of the pores.
- Average porosity (%) A / B ⁇ 100
- the average porosity is more preferably 25% or more, and further preferably 28% or more.
- the smaller the average porosity the higher the average bulk density and the higher the compression specific strength. Therefore, the average porosity is more preferably 75% or less, and further preferably 70% or less.
- the average porosity is appropriately set according to the desired fluid permeation rate and compressive strength.
- the fluid separation membrane and the porous carbon fiber of the present invention are preferable because the compressive strength is higher because it can be used under high pressure.
- the compressive strength is preferably 10 MPa or more, more preferably 20 MPa or more, and further preferably 30 MPa or more.
- the compression strength is measured by using a micro-compression tester, sandwiching one porous carbon fiber with a jig, compressing it in the fiber cross-section direction (direction perpendicular to the fiber axis), and measuring the compression displacement and load.
- the compressive strength ⁇ is calculated by the following formula.
- ⁇ Compressive strength in the fiber cross-sectional direction
- F Fracture load
- d Fiber diameter
- l Fiber length
- / Kg or more is preferable, and 20 N ⁇ m / kg or more is more preferable.
- the compression specific strength is calculated by dividing the compression strength by the average bulk density.
- the fluid separation membrane of the present invention is based on porous carbon fibers.
- the fibers refer to those having a fiber length L (aspect ratio L / D) of 100 or more with respect to the fiber diameter D.
- the shape of the cross section of the porous carbon fiber and the fluid separation membrane is not limited, and can be any shape such as a round cross section, a polygon cross section, a multi-leaf cross section, a flat cross section, etc. Is preferable because the strength distribution becomes uniform and the compressive strength and compressive strength in the fiber cross-sectional direction are further improved.
- a separation membrane using a hollow fiber having a hollow portion as a porous carbon fiber is also an embodiment of the present invention.
- the porous carbon fiber which has a hollow part is used as a base material is demonstrated.
- the hollow portion in the present invention refers to a void portion having substantially the same diameter formed continuously in the fiber axis direction, and the hollow portion serves as a fluid flow path together with the co-continuous porous structure.
- the area ratio of the cross-sectional area A of the hollow portion to the cross-sectional area B of the porous carbon fiber is preferably 0.001 to 0.7.
- the cross-sectional area B of the porous carbon fiber is a cross-sectional area including the cross-sectional area A of the hollow portion.
- the hollow area ratio is more preferably 0.01 or more, and further preferably 0.05 or more.
- the hollow area ratio is more preferably 0.6 or less.
- the balance between compressive strength and fluid permeation rate is excellent.
- a plurality of hollow portions may be provided.
- the sum of the cross-sectional areas of the hollow portions is defined as the cross-sectional area A of the hollow portion.
- the cross-sectional shape of the hollow portion can be any shape such as a round cross-section, polygon, multi-leaf cross-section, flat cross-section, and the round cross-section is preferable because the compressive strength is further improved.
- the porous carbon fiber even when the porous carbon fiber has a hollow portion, it is outside from the surface of the porous carbon fiber facing the hollow portion (hereinafter sometimes referred to as “inner surface”). It is preferable that the pores communicate with the surface.
- Compressive strength improves if the average diameter of the porous carbon fiber is small. Therefore, 500 micrometers or less are preferable, 400 micrometers or less are more preferable, and 300 micrometers or less are further more preferable.
- the lower limit value of the average diameter of the fibers is not particularly limited and can be arbitrarily determined, but is preferably 10 ⁇ m or more from the viewpoint of improving the handleability when producing the separation membrane module.
- the smaller the average diameter of the porous carbon fiber and the fluid separation membrane the greater the number of fibers that can be filled per unit volume, so the membrane area per unit volume is increased and the permeate flow rate per unit volume is increased. Can do.
- the average length of the fibers can be arbitrarily determined, and is preferably 10 mm or more from the viewpoint of improving the handleability when forming a separation module and improving the fluid permeation performance.
- the porous carbon fiber serves as a base material for the separation membrane and also functions as a fluid flow path. With such a structure, the compressive strength is improved.
- the fluid separation membrane of the present invention has an organic polymer layer formed on the surface of the porous carbon fiber.
- an organic polymer layer may be formed on the inner surface.
- the material of the organic polymer layer is not particularly limited.
- density polyethylene high density polyethylene, styrene, polyethyl methacrylate, polycarbonate, polyester, aliphatic polyamide, polyvinyl alcohol, polyethylene glycol, etc.
- the absolute value of the difference in solubility parameter (SP value) between the organic polymer and the substance to be separated is smaller because the solubility of the substance to be separated is improved and the permeation rate is improved.
- the larger the absolute value of the difference in solubility parameter from a substance not to be separated the lower the permeation rate. Therefore, the organic polymer layer can be appropriately selected depending on the type of the substance to be separated.
- a glassy polymer having a high glass transition point (Tg) and a high structural order is preferable because the gap (free volume) between polymer chains can be widely controlled.
- Tg glass transition point
- the glass transition point is high, it is fragile and it is difficult to reduce the thickness of the glass transition point.
- aromatic polyimide aromatic polyimide, cellulose acetate, polysulfone, aromatic polyamide, polyetherimide, polyethersulfone, polyacrylonitrile, polyphenylene sulfide, polyetheretherketone, polytetrafluoroethylene, polyvinylidene fluoride and It is preferable to include one or more organic polymers selected from these derivatives.
- aromatic polyimide, aromatic polyamide and derivatives thereof are more preferable because they have high fluid separation properties and are excellent in heat resistance, chemical resistance and mechanical strength.
- the organic polymer layer can contain various additives such as nanoparticles in order to improve the fluid permeation rate.
- the nanoparticles include silica, titania, zeolite, metal oxide, and metal organic structure (MOF).
- MOF metal organic structure
- a bulky substituent can be introduced into the molecule to increase the free volume in the organic polymer and improve the permeation rate.
- a functional group or additive having chemical affinity with the substance to be separated can be introduced.
- functional groups having chemical affinity include various polar functional groups such as amino groups, amide groups, sulfo groups, carbonyl groups, and phenolic hydroxyl groups.
- additives include ionic liquids and alkaline groups. Metal carbonate is mentioned.
- the thickness of the organic polymer layer can be set as appropriate, and the thinner the thickness is, the better the fluid permeation rate is improved, preferably 5 ⁇ m or less, more preferably 3 ⁇ m or less, and even more preferably 1 ⁇ m or less.
- the thickness of the organic polymer layer is the arithmetic average value of the thicknesses of 20 arbitrary points in the scanning electron microscope image.
- the fluid separation membrane of the present invention includes, as an example, a step (step 1) in which a carbonizable resin and a disappearing resin are mixed to form a resin mixture, and a step in which the resin mixture in a compatible state is spun and phase-separated ( It can be produced by a production method having a step 2), a step of carbonizing by heating and firing (step 3), and a step of forming an organic polymer layer on the surface (step 4).
- Step 1 is a step in which 10 to 90% by weight of carbonizable resin and 90 to 10% by weight of disappearing resin are mixed to form a resin mixture.
- the carbonizable resin is a resin that is carbonized by firing and remains as a branch (carbon skeleton), and both a thermoplastic resin and a thermosetting resin can be used.
- thermoplastic resin it is preferable to select a resin that can be infusibilized by a simple process such as heating or irradiation with high energy rays.
- thermosetting resin infusibilization treatment is often unnecessary, and this is also a suitable material.
- thermoplastic resin examples include polyphenylene ether, polyvinyl alcohol, polyacrylonitrile, phenol resin, wholly aromatic polyester, polyimide resin, cellulose acetate, and polyetherimide.
- thermosetting resin examples include unsaturated polyester. Resins, alkyd resins, melamine resins, urea resins, polyimide resins, diallyl phthalate resins, lignin resins, urethane resins, polyfurfuryl alcohol resins, and the like can be listed. These may be used alone or in a mixed state. However, it is also preferable to mix them with a thermoplastic resin or a thermosetting resin, respectively, because of easy molding.
- thermoplastic resin from the viewpoint of carbonization yield, spinnability, and economy, it is preferable to use a thermoplastic resin, and polyphenylene ether, polyvinyl alcohol, polyacrylonitrile, and wholly aromatic polyester are more preferably used.
- the molecular weight of the carbonizable resin is preferably 10,000 or more in terms of weight average molecular weight.
- the weight average molecular weight is 10,000 or more, yarn breakage is reduced in the spinning process.
- the upper limit of the weight average molecular weight is not particularly limited, but is preferably 1,000,000 or less from the viewpoint of easy spinnability and resin extrusion.
- the disappearing resin is a resin that can be removed at any stage of the infusibilization treatment, after the infusibilization treatment, after the infusibilization treatment, or at the same time as the firing, following the step 2 described later.
- the method for removing the disappearing resin is not particularly limited, a method for chemically removing the polymer by depolymerizing it with a chemical, a method for dissolving and removing the solvent by dissolving the disappearing resin, and thermal decomposition by heating.
- a method of removing the lost resin by lowering the molecular weight is preferably used. These methods can be used alone or in combination, and when combined, they may be performed simultaneously or separately.
- a method of hydrolyzing with an acid or alkali is preferable from the viewpoints of economy and handleability.
- the resin that is susceptible to hydrolysis by acid or alkali include polyester, polycarbonate, and polyamide.
- a method of removing by adding a solvent that dissolves the disappearing resin a method of dissolving and removing the disappearing resin by continuously supplying a solvent to the mixed carbonizable resin and the disappearing resin, or by a batch method
- a preferred example is a method of mixing and dissolving and removing the disappearing resin.
- the disappearing resin suitable for the method of removing by adding a solvent include polyolefins such as polyethylene, polypropylene and polystyrene, acrylic resins, methacrylic resins, polyvinyl pyrrolidone, aliphatic polyesters, polycarbonates and the like.
- polyolefins such as polyethylene, polypropylene and polystyrene
- acrylic resins methacrylic resins
- polyvinyl pyrrolidone polyvinyl pyrrolidone
- aliphatic polyesters polycarbonates and the like.
- an amorphous resin is more preferable because of its solubility in a solvent, and examples thereof include polystyrene, methacrylic resin, and polycarbonate.
- a method of removing the lost resin by reducing the molecular weight by thermal decomposition a method in which the mixed carbonizable resin and the lost resin are heated in a batch manner to thermally decompose, or a continuously mixed carbonized resin and the lost resin are removed.
- a method of heating and thermally decomposing while continuously supplying to a heat source a method in which the mixed carbonizable resin and the lost resin are heated in a batch manner to thermally decompose, or a continuously mixed carbonized resin and the lost resin are removed.
- the disappearing resin is preferably a resin that disappears by thermal decomposition when carbonizing the carbonizable resin by firing in Step 3 described later, and does not cause a large chemical change during the infusibilization treatment described later, and after firing. It is preferable that the carbonization yield of the thermoplastic resin is less than 10%.
- disappearing resins include polyolefins such as polyethylene, polypropylene, and polystyrene, acrylic resins, methacrylic resins, polyacetals, polyvinylpyrrolidones, aliphatic polyesters, aromatic polyesters, aliphatic polyamides, polycarbonates, and the like. These may be used alone or in a mixed state.
- step 1 the carbonizable resin and the disappearing resin are mixed to form a resin mixture (polymer alloy).
- “Compatibilized” as used herein refers to creating a state in which the phase separation structure of the carbonizable resin and the disappearing resin is not observed with an optical microscope by appropriately selecting the temperature and / or solvent conditions.
- the carbonizable resin and the disappearing resin may be compatible by mixing only the resins, or may be compatible by adding a solvent.
- a system in which a plurality of resins are compatible includes a phase diagram of an upper critical eutectic temperature (UCST) type that is in a phase separation state at a low temperature but has one phase at a high temperature, and conversely, a phase separation state at a high temperature.
- UCT upper critical eutectic temperature
- LCST lower critical solution temperature
- the solvent to be added is not particularly limited, but the absolute value of the difference from the average value of the solubility parameter (SP value) of the carbonizable resin and the disappearing resin, which is a solubility index, is preferably within 5.0.
- the absolute value of the difference from the average SP value is preferably 3.0 or less, and more preferably 2.0 or less.
- carbonizable resin and disappearance resin are polyphenylene ether / polystyrene, polyphenylene ether / styrene-acrylonitrile copolymer, wholly aromatic polyester / polyethylene as long as they do not contain solvents.
- examples include terephthalate, wholly aromatic polyester / polyethylene naphthalate, wholly aromatic polyester / polycarbonate.
- combinations of systems containing solvents include polyacrylonitrile / polyvinyl alcohol, polyacrylonitrile / polyvinylphenol, polyacrylonitrile / polyvinylpyrrolidone, polyacrylonitrile / polylactic acid, polyvinyl alcohol / vinyl acetate-vinyl alcohol copolymer, polyvinyl Examples include alcohol / polyethylene glycol, polyvinyl alcohol / polypropylene glycol, and polyvinyl alcohol / starch.
- the method of mixing the carbonizable resin and the disappearing resin is not limited, and various known mixing methods can be adopted as long as uniform mixing is possible. Specific examples include a rotary mixer having a stirring blade and a kneading extruder using a screw.
- the temperature (mixing temperature) when mixing the carbonizable resin and the disappearing resin be equal to or higher than the temperature at which both the carbonizable resin and the disappearing resin are softened.
- the softening temperature may be appropriately selected as the melting point if the carbonizable resin or the disappearing resin is a crystalline polymer, and the glass transition temperature if it is an amorphous resin.
- the mixing temperature is not particularly limited, but is preferably 400 ° C. or lower from the viewpoint of preventing deterioration of the resin due to thermal decomposition and obtaining a precursor of porous carbon fiber having excellent quality.
- Step 1 90 to 10% by weight of the disappearing resin is mixed with 10 to 90% by weight of the carbonizable resin. It is preferable that the carbonizable resin and the disappearing resin are within the above-mentioned ranges since an optimum pore size and porosity can be arbitrarily designed.
- the carbonizable resin is 10% by weight or more, the mechanical strength of the porous carbon fiber after carbonization can be maintained and the yield is improved, which is preferable. Further, if the carbonizable resin is 90% by weight or less, it is preferable because the disappearing resin can efficiently form voids.
- the mixing ratio of the carbonizable resin and the disappearing resin can be arbitrarily selected within the above range in consideration of the compatibility of each resin. Specifically, in general, the compatibility between resins deteriorates as the composition ratio approaches 1: 1, so when a system that is not very compatible is selected as a raw material, the amount of carbonizable resin is increased. Alternatively, it is also preferable to improve the compatibility by approaching a so-called uneven composition by reducing the amount.
- a solvent when mixing the carbonizable resin and the disappearing resin. Addition of a solvent lowers the viscosity of the carbonizable resin and the disappearing resin to facilitate molding, and facilitates compatibilization of the carbonizable resin and the disappearing resin.
- the solvent here is not particularly limited as long as it is a liquid at room temperature that can dissolve and swell at least one of the carbonizable resin and the disappearing resin. It is more preferable that it can be dissolved because the compatibility of the two can be improved.
- the amount of the solvent added is preferably 20% by weight or more based on the total weight of the carbonizable resin and the disappearing resin from the viewpoint of improving the compatibility between the carbonizable resin and the disappearing resin and reducing the viscosity to improve the fluidity.
- 90% by weight or less is preferable with respect to the total weight of the carbonizable resin and the disappearing resin from the viewpoint of the cost associated with the recovery and reuse of the solvent.
- Step 2 is a step of spinning the resin mixture in a state compatible in Step 1 to form a fine phase separation structure.
- the method for spinning the resin mixture in a compatible state is not particularly limited, and a spinning method suitable for the phase separation method described later can be appropriately selected.
- melt spinning can be performed after heating to a temperature equal to or higher than the softening temperature of the resin.
- solvent is contained in the resin mixture, dry spinning, dry-wet spinning, wet spinning, or the like can be appropriately selected as the solution spinning.
- Melt spinning is a method in which a resin mixture heated and melted (flowed) using a kneading extruder or the like is extruded from a die, and wound while being cooled, and is made into fibers, and the process speed is faster than that of solution spinning. Excellent productivity. Moreover, since the volatilization of the solvent does not occur, the cost for safety measures during the process can be suppressed, and therefore, it is preferable because it can be manufactured at a low cost.
- solution spinning is a method in which a spinning dope composed of a resin mixture and a solvent prepared in advance is weighed and extruded from the die, and the phase separation state can be precisely controlled.
- dry-wet spinning using a coagulation bath and wet spinning are more preferred because the phase separation state of the precursor fibers can be precisely controlled by appropriately combining heat-induced phase separation and non-solvent-induced phase separation described later. is there.
- the method for phase separation of carbonizable resin and disappearing resin is not particularly limited.
- thermally induced phase separation method that induces phase separation by temperature change
- non-solvent induced phase separation that induces phase separation by adding non-solvent Law.
- phase separation methods can be used alone or in combination.
- Specific methods for use in combination include, for example, a method in which non-solvent induced phase separation is caused through a coagulation bath and then heat-induced phase separation is performed by heating, or a temperature in the coagulation bath is controlled to induce non-solvent induction. Examples thereof include a method of causing phase separation and thermally induced phase separation at the same time, a method of cooling the resin discharged from the die and causing thermally induced phase separation, and then contacting with a non-solvent.
- the fine structure is formed by drying, and a precursor of porous carbon fiber can be obtained.
- the coagulating liquid is not particularly limited, and examples thereof include water, ethanol, saturated saline, and a mixed solvent of these and the solvent used in Step 1.
- the spinning solution is discharged from the inner tube, and the same solvent or disappearing resin as the spinning solution is dissolved from the outer tube.
- the porous carbon fiber precursor of the present invention can be produced by using a composite spinning method in which solutions and the like are discharged simultaneously.
- the precursor of the porous carbon fiber obtained in the step 2 may be subjected to the disappearing resin removal treatment before being subjected to the carbonization step (step 3), simultaneously with the carbonization step (step 3), or both. preferable.
- the removal process method is not particularly limited. Specifically, a method of chemically decomposing and reducing the molecular weight of the disappearing resin using acid, alkali, or enzyme, a method of removing by dissolving with a solvent that dissolves the disappearing resin, electron beam, gamma ray, ultraviolet ray, infrared ray And a method of decomposing and removing the lost resin using radiation or heat.
- a heat treatment can be performed at a temperature at which 80% by weight or more of the disappearance resin disappears in advance, and a carbonization step (step 3) or infusibilization described later.
- the lost resin can be removed by pyrolysis and gasification.
- the carbonization step (step 3) or the infusibilization treatment described later it is preferable that the lost resin is thermally decomposed and gasified and removed simultaneously with the heat treatment because productivity increases.
- step 2 the porous carbon fiber precursor is preferably subjected to infusibilization before being subjected to the carbonization step (step 3).
- the method of infusibilization treatment is not particularly limited, and a known method can be used.
- Specific methods include a method of causing oxidative crosslinking by heating in the presence of oxygen, a method of forming a crosslinked structure by irradiating high energy rays such as electron beams and gamma rays, and impregnating a substance having a reactive group, Examples thereof include a method of forming a crosslinked structure by mixing, and among them, a method of causing oxidative crosslinking by heating in the presence of oxygen is preferable because the process is simple and the production cost can be reduced. These techniques may be used alone or in combination, and each may be used simultaneously or separately.
- the heating temperature in the method of causing oxidative crosslinking by heating in the presence of oxygen is preferably 150 ° C. or higher from the viewpoint of efficiently promoting the crosslinking reaction, and the yield is deteriorated due to weight loss due to thermal decomposition, combustion, etc. of carbonizable resin. From the viewpoint of preventing this, 350 ° C. or lower is preferable.
- the oxygen concentration during the treatment is not particularly limited, but it is preferable to supply a gas having an oxygen concentration of 18% by volume or more because the manufacturing cost can be kept low.
- the gas supply method is not particularly limited, and examples thereof include a method of supplying air directly into the heating device and a method of supplying pure oxygen into the heating device using a cylinder or the like.
- the carbonizable resin is irradiated with an electron beam or gamma ray using a commercially available electron beam generator or gamma ray generator. And a method of inducing cross-linking.
- the lower limit of the irradiation intensity is preferably 1 kGy or more, and from the viewpoint of preventing the strength of the porous carbon fiber from being reduced due to a decrease in molecular weight due to cleavage of the main chain, 1 1,000 kGy or less is preferable.
- the resin mixture is impregnated with a low molecular weight compound having a reactive group, and the crosslinking reaction is promoted by heating or irradiation with high energy rays.
- the crosslinking reaction is promoted by heating or irradiation with high energy rays. Examples thereof include a method in which a low molecular weight compound having a reactive group is mixed in advance, and a crosslinking reaction is promoted by heating or irradiation with high energy rays.
- step 3 the precursor of the porous carbon fiber obtained in step 2 or, if necessary, the precursor subjected to the removal and / or infusibilization treatment of the lost resin is fired and carbonized to obtain the porous carbon fiber. It is the process of obtaining.
- Calcination is preferably performed by heating in an inert gas atmosphere in order to carbonize the precursor of the porous carbon fiber.
- the inert gas refers to a substance that is chemically inert when heated, and specific examples include helium, neon, nitrogen, argon, krypton, and xenon. Among these, nitrogen and argon are preferably used from the economical viewpoint. When the carbonization temperature is 1,500 ° C. or higher, argon is preferably used from the viewpoint of suppressing nitride formation.
- the flow rate of the inert gas may be an amount that can sufficiently reduce the oxygen concentration in the heating device, and it is preferable to select an optimal value appropriately depending on the size of the heating device, the amount of raw material supplied, the heating temperature, and the like. .
- the upper limit of the flow rate is not particularly limited, it is preferably set as appropriate in accordance with the temperature distribution and the design of the heating device, from the viewpoint of economical efficiency and reducing the temperature change in the heating device.
- the gas generated during carbonization can be sufficiently discharged out of the system because porous carbon fibers having excellent quality can be obtained. Therefore, it is preferable to determine the flow rate of the inert gas so that the generated gas concentration in the system is 3,000 ppm or less.
- the active gas oxygen, carbon dioxide, water vapor, air, or combustion gas can be used.
- the heating temperature is not particularly limited as long as it exceeds the temperature at which the disappearing resin is thermally decomposed, but is preferably 300 ° C. or higher, more preferably 400 ° C. or higher. Moreover, although the upper limit of heating temperature is not limited, if it is 1500 degrees C or less, since a special process is not required for an installation, it is preferable from an economical viewpoint.
- the heating method in the case of continuously performing carbonization treatment it is a method of taking out porous carbon fiber while continuously supplying it using a roller, a conveyor, etc. in a heating device maintained at a constant temperature, It is preferable because productivity can be increased.
- the rate of temperature rise or temperature drop when batch processing is performed in the heating apparatus there is no limitation on the rate of temperature rise or temperature drop when batch processing is performed in the heating apparatus, and productivity can be increased by shortening the time required for temperature rise or temperature fall, so that it is 1 ° C./min or more. Speed is preferred.
- the upper limit of a temperature increase rate and a temperature decrease rate is not specifically limited, It can set suitably in the range which does not produce defects, such as a crack.
- the holding time of the carbonization temperature can be arbitrarily set. If the holding time is long, the shrinkage of the porous carbon fiber proceeds, and the pore diameter on the fiber surface tends to be reduced.
- Step 4 is a step of forming an organic polymer layer on the surface of the porous carbon fiber produced in Step 3.
- the method for forming the organic polymer layer is not particularly limited.
- a general method is to coat the organic polymer itself on the surface of the porous carbon fiber. After coating the organic polymer precursor on the porous carbon fiber, the precursor is reacted to react with the organic polymer. You may take the method made into a molecule
- Examples of the coating method of the organic polymer or organic polymer precursor include a dip coating method, a spray method, and a vapor deposition method.
- the dip coating method is preferable because the manufacturing method is relatively easy.
- the dip coating method is roughly divided into a melting method and a solution method.
- a melting method an organic polymer or a precursor thereof is melted and laminated at a temperature equal to or higher than the melting point, and then cooled to a temperature equal to or lower than the melting point to produce a fluid separation membrane.
- a fluid separation membrane is manufactured by dissolving and laminating an organic polymer or a precursor thereof in a solvent in which the organic polymer or a precursor thereof is soluble, and then drying the solvent appropriately to remove the solvent.
- additives may be added to improve functions such as permeation speed and fluid separation performance.
- the viscosity of the coating stock solution can be appropriately selected depending on conditions such as the surface roughness of the porous carbon support, the coating speed, and the desired film thickness. Since the uniform organic polymer layer can be formed as the viscosity of the coating stock solution is higher, it is preferably 10 mPa ⁇ s or more, and more preferably 50 mPa ⁇ s or more. Further, the lower the viscosity of the coating stock solution, the thinner the film and the higher the fluid permeation rate. Therefore, the shear viscosity at a shear rate of 0.1 s ⁇ 1 is preferably 1,000 mPa ⁇ s or less, and more preferably 800 mPa ⁇ s or less.
- the reaction method can be appropriately selected according to the type of the precursor, and the fluid separation of the present invention is promoted by promoting polymerization, cyclization, or crosslinking reaction using heating or a catalyst.
- a membrane is manufactured.
- the porous carbon fiber may be subjected to a surface treatment before the organic polymer layer is formed.
- the surface treatment include oxidation treatment and chemical coating treatment.
- the oxidation treatment include chemical oxidation using nitric acid, electrolytic oxidation, vapor phase oxidation, and the like.
- a sizing agent can be applied as the chemical solution coating treatment.
- Such surface treatment can improve wettability and improve adhesiveness with the organic polymer layer, so that the compressive strength of the fluid separation membrane can be further improved.
- the fluid separation membrane module of the present invention is formed by housing a plurality of fluid separation membranes of the present invention in a casing.
- a plurality of fluid separation membranes are connected and housed in a casing and used as a fluid separation membrane module.
- the compressive strength of the fluid separation membrane was measured by using a micro compression tester MCTW-500 manufactured by Shimadzu Corporation, sandwiching one porous carbon fiber with a jig, using a flat indenter made of diamond of ⁇ 500 ⁇ m, and a load speed of 41
- the compression displacement and load were measured by compressing in the fiber cross-sectional direction by a constant load speed method of .482 mN / s, and the compression strength ⁇ was calculated by the following equation.
- ⁇ compressive strength in the fiber cross-sectional direction
- F fracture load
- d fiber diameter
- l fiber length
- the compression specific strength was calculated by dividing the compression strength by the average bulk density.
- the measurement of the average bulk density was performed by photographing 20 arbitrary cross sections of the fluid separation membrane with a scanning electron microscope and calculating the respective cross sectional areas by image processing. Subsequently, the bulk density was calculated by the following formula. And the bulk density was measured about 20 fluid separation membranes, and the average value was made into the average bulk density of a fluid separation membrane.
- ⁇ b Bulk density of fluid separation membrane
- W Weight of fluid separation membrane
- S Average cross-sectional area
- l Fiber length
- a porous carbon fiber was fixed to a sample plate, and the positions of the light source, the sample, and the two-dimensional detector were adjusted so that information with a scattering angle of less than 10 ° was obtained from an X-ray source obtained from a CuK ⁇ ray light source. From the image data (luminance information) obtained from the two-dimensional detector, the central portion affected by the beam stopper is excluded, a moving radius is provided from the beam center, and a luminance value of 360 ° is obtained for each angle of 1 °. In total, a scattering intensity distribution curve with respect to the scattering angle 2 ⁇ was obtained. From the scattering angle 2 ⁇ at a position having a peak in the obtained curve, the structural period of the continuous structure portion was obtained by the following equation.
- the porous carbon fiber is tomographed with X-ray CT, the three-dimensional image is subjected to Fourier transform, and the circular average of the two-dimensional spectrum is taken. An original spectrum was obtained. The characteristic wavelength corresponding to the position of the peak top in the one-dimensional spectrum was obtained, and the structural period was calculated as the reciprocal thereof.
- Porous carbon fiber is embedded in resin, and then the fiber cross section is exposed with a razor.
- An argon ion beam is applied to the sample surface at an acceleration voltage of 5.5 kV using a cross section polisher device SM-09010 manufactured by JEOL Ltd. Irradiation and etching are performed.
- the cross-section of the obtained fiber was 700,000 pixels with an enlargement ratio adjusted so that the center of the fiber cross-section would be 1 ⁇ 0.1 (nm / pixel) using a scanning microscope S-5500 manufactured by Hitachi High-Technologies Corporation From the image observed at the above resolution, the fiber cross section necessary for the calculation is set in 512 pixels square, the area of the pore part is A, the area of the carbon part is B, and the average porosity is calculated by the following formula: It was calculated from the arithmetic mean value of 20 arbitrary cross sections.
- Fiber diameter D Twenty porous carbon fibers were measured with a micrometer, and the arithmetic average value was defined as a fiber diameter D.
- the average value of the area of the pores in the image was calculated, and the diameter of a perfect circle having the same area as the average area was taken as the average pore diameter.
- the calculation was performed using an image obtained by observing at 700,000 pixels or more at a magnification of 10 ⁇ 1 (nm / pixel).
- the fluid separation membrane was wound around a cylinder of various diameters by 180 ° or more, and it was observed whether the membrane was broken.
- the bending radius is indicated by the value of the radius of a cylinder having the smallest radius among the cylinders in which the film does not break.
- Carbon dioxide and methane are used as measurement gases, and the pressure change on the permeate side of carbon dioxide and methane per unit time is measured with an external pressure method at a measurement temperature of 25 ° C in accordance with the pressure sensor method of JIS K7126-1 (2006). did.
- the pressure difference between the supply side and the transmission side was set to 0.11 MPa (82.5 cmHg).
- the permeation rate Q of the permeated gas was calculated according to the following formula, and the separation factor ⁇ was calculated as the ratio of the permeation rate of each component gas.
- STP means standard conditions.
- Permeation rate Q [gas permeation flow rate (cm 3 ⁇ STP)] / [membrane area (cm 2 ) ⁇ time (s) ⁇ pressure difference (cmHg)
- Micromid® 5218 refers to 3,3 ′, 4,4′-benzophenonetetracarboxylic dianhydride and 5 (6) -amino-1- (4′-aminophenyl) -1 , 3,3′-trimethylindane).
- Aromatic Polyimide Solution 25 wt% Aromatic polyimide “Matrimid®” 5218 was dissolved in N-methylpyrrolidone (NMP) to prepare a 25.0 wt% aromatic polyimide solution. .
- NMP N-methylpyrrolidone
- Example 1 70 g of polyacrylonitrile (MW 150,000) manufactured by Polyscience, 70 g of polyvinyl pyrrolidone (MW 40,000) manufactured by Sigma-Aldrich, and 400 g of dimethyl sulfoxide (DMSO) manufactured by Wakken as a solvent were put into a separable flask. A uniform and transparent solution was prepared at 150 ° C. while stirring and refluxing for 3 hours. At this time, the concentration of polyacrylonitrile and the concentration of polyvinylpyrrolidone were 10% by weight, respectively.
- DMSO dimethyl sulfoxide
- the polymer solution was discharged from the inner tube of the core-sheath double cap at 3 mL / min, and the DMSO 90 wt% aqueous solution was 5.3 mL / min from the outer tube.
- a coagulation bath made of pure water at 25 ° C., then taken up at a speed of 5 m / min, and wound on a roller to obtain a raw yarn.
- the air gap was 5 mm
- the immersion length in the coagulation bath was 15 cm.
- the obtained raw yarn was translucent and caused phase separation.
- the obtained raw yarn was washed with water and then dried at 25 ° C. for 24 hours in a circulation dryer to prepare a dried raw yarn.
- the dried raw yarn was passed through an electric furnace at 250 ° C. and heated in an oxygen atmosphere for 1 hour to effect infusibilization.
- a porous carbon fiber was produced by carbonizing the infusible raw material under the conditions of a nitrogen flow rate of 1 L / min, a heating rate of 10 ° C./min, an ultimate temperature of 500 ° C., and a holding time of 1 min.
- Example 2 Porous carbon fibers were produced in the same manner as in Example 1 except that spinning was performed using a polymer solution having a polyacrylonitrile concentration and a polyvinylpyrrolidone concentration of 11.5% by weight, respectively.
- Example 3 Spinning was performed using a polymer solution having a polyacrylonitrile concentration and a polyvinylpyrrolidone concentration of 13% by weight, respectively, and porous carbon fibers were produced in the same manner as in Example 1 except that the ultimate temperature was 700 ° C.
- Example 4 The same as in Example 1 except that the solution was discharged from the inner tube of the core-sheath type double cap at 5 mL / min and the 90 wt% DMSO aqueous solution was simultaneously discharged from the outer tube at 8.8 mL / min to perform spinning. Porous carbon fibers were prepared by this method.
- Example 5 Using a core-sheath type triple mouthpiece, an 85 wt% DMSO aqueous solution is discharged from the inner tube at 1 mL / min, a polymer solution is discharged from the inner tube at 3 mL / min, and a 90 wt% DMSO aqueous solution is 5.3 mL / min from the outer tube.
- a porous carbon fiber was produced in the same manner as in Example 1 except that a hollow fiber-like porous carbon fiber discharged simultaneously was produced.
- Example 6 A porous carbon fiber was produced in the same manner as in Example 1 except that spinning was performed using a polymer solution having a concentration of 10% by weight of polyacrylonitrile and polyvinylpyrrolidone using a single hole cap of ⁇ 0.6 mm. . A dense layer was formed on the surface of the obtained porous carbon fiber, and no pores were confirmed.
- AN acrylonitrile
- AN acrylonitrile
- 4 parts of sodium sulfate was further added, followed by stirring for 30 minutes.
- the polymer was taken out, filtered, washed with water and dried to prepare a MMA / AN block copolymer (compatibilizer) (C) having a polymerization rate of 65.7% and a specific viscosity of 0.19.
- dimethylformamide was added to adjust the polymer polymer concentration to 26% by weight.
- the air gap was 5 mm, and the immersion length in the coagulation bath was 15 cm.
- the obtained raw yarn was washed with water and then dried at 25 ° C. for 24 hours in a circulation dryer to prepare a dried raw yarn.
- the obtained raw yarn was subjected to infusibilization treatment and carbonization treatment in the same manner as in Example 1 to produce a hollow fiber-like porous carbon fiber.
- the air gap was 200 mm, and the immersion length in the coagulation bath was 15 cm.
- the obtained raw yarn was washed with water and then dried at 50 ° C. for 24 hours to prepare an aromatic polyimide hollow fiber membrane.
- the pores were independent of each other.
- the film surface was dense and no pores were observed, and the film thickness was 5.5 ⁇ m.
- Table 1 shows the configurations and various evaluation results of the fluid separation membranes produced in each of the examples and comparative examples.
- Fluid separation membrane 2 Porous carbon fiber 3: Organic polymer layer
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Abstract
Description
<1>共連続多孔構造を有する多孔質炭素繊維の表面に、有機高分子層が形成されてなる流体分離膜。
<2>前記多孔質炭素繊維の全体に前記共連続多孔構造を有する、<1>に記載の流体分離膜。
<3>水銀圧入法により測定される前記多孔質炭素繊維の全体の平均細孔直径が30~5,000nmである、<1>または<2>に記載の流体分離膜。
<4>走査型電子顕微鏡による表面観察によって測定される前記多孔質炭素繊維の表面の平均細孔直径が2~500nmである、<1>~<3>のいずれか1つに記載の流体分離膜。
<5>前記共連続多孔構造の構造周期が10~10,000nmである、<1>~<4>のいずれか1つに記載の流体分離膜。
<6>前記多孔質炭素繊維のX線散乱の強度ピークの半値幅が5°以下である、<1>~<5>のいずれか1つに記載の流体分離膜。
<7>前記有機高分子層が、芳香族ポリイミド、酢酸セルロース、ポリスルホン、芳香族ポリアミド、ポリエーテルイミド、ポリエーテルスルホン、ポリアクリロニトリル、ポリフェニレンスルフィド、ポリエーテルエーテルケトン、ポリテトラフルオロエチレン、ポリフッ化ビニリデンおよびこれらの誘導体からなる群より選択される1種または2種以上の有機高分子を含む層である、<1>~<6>のいずれか1つに記載の流体分離膜。
<8>前記有機高分子層が、芳香族ポリイミド、芳香族ポリアミドおよびこれらの誘導体からなる群より選択される1種または2種以上の有機高分子を含む層である、<1>~<7>のいずれか1つに記載の流体分離膜。
<9>ケーシング内に<1>~<8>のいずれか1つに記載の流体分離膜を複数本収容してなる流体分離膜モジュール。
<10>全体に共連続多孔構造を有する多孔質炭素繊維。
<11>水銀圧入法により測定される全体の平均細孔直径が30nm~5,000nmである、<10>に記載の多孔質炭素繊維。
<12>走査型電子顕微鏡による表面観察によって測定される表面の平均細孔直径が2~500nmである、<10>または<11>に記載の多孔質炭素繊維。
<13>前記共連続多孔構造の構造周期が10~10,000nmである、<10>~<12>のいずれか1つに記載の多孔質炭素繊維。
<14>X線散乱の強度ピークの半値幅が5°以下である、<10>~<13>のいずれか1つに記載の多孔質炭素繊維。
〔多孔質炭素繊維〕
本発明の流体分離膜(以下、単に「流体分離膜」または「分離膜」ということがある。)は、共連続多孔構造を有する多孔質炭素繊維を基材とする。
ただし、構造周期が大きくて小角での散乱が観測できない場合がある。その場合はX線コンピュータ断層撮影(X線CT)によって構造周期を得る。具体的には、X線CTによって撮影した三次元画像をフーリエ変換した後に、その二次元スペクトルの円環平均を取り、一次元スペクトルを得る。その一次元スペクトルにおけるピークトップの位置に対応する特性波長を求め、その逆数として構造周期を算出する。
平均空隙率とは、包埋した試料をクロスセクションポリッシャー法(CP法)により精密に形成させた多孔質炭素繊維の断面を、1±0.1(nm/画素)となる倍率にて70万画素以上で観察し、その画像から計算に必要な着目領域を512画素四方で設定し、細孔部分の面積をA、炭素部分の面積をBとして以下の式で算出し、任意の断面20箇所の算術平均値により算出した値である。ここで、多孔質炭素繊維が中空部を有する場合、中空部分の面積は細孔の面積には含めない。
平均空隙率(%)=A/B×100
また、圧縮比強度が高いほど軽くて強度が高い材料であるため、圧縮比強度は一例として10N・m/kg以上が好ましく、20N・m/kg以上がより好ましい。ここで、圧縮比強度は圧縮強度を平均かさ密度で除して算出する。
本発明の流体分離膜は多孔質炭素繊維を基材とするが、ここで、繊維とは繊維直径Dに対する繊維長さL(アスペクト比L/D)が100以上のものを指す。多孔質炭素繊維および流体分離膜の断面の形状は制限されず、丸断面、多角形断面、多葉断面、扁平断面など任意の形状とすることが可能であるが、丸断面であると断面内の強度分布が均一になり、繊維断面方向の圧縮強度および圧縮比強度がより向上するため好ましい。
本発明の流体分離膜は、上記の多孔質炭素繊維の表面に有機高分子層が形成されてなる。多孔質炭素繊維が中空部を有する中空糸である場合は、内表面に有機高分子層が形成されていてもよい。
本発明の流体分離膜は、一例として、炭化可能樹脂と消失樹脂とを相溶させて樹脂混合物とする工程(工程1)と、相溶した状態の樹脂混合物を紡糸し、相分離させる工程(工程2)と、加熱焼成により炭化する工程(工程3)と、表面に有機高分子層を形成する工程(工程4)とを有する製造方法により製造することができる。
工程1は、炭化可能樹脂10~90重量%と消失樹脂90~10重量%を相溶させ、樹脂混合物とする工程である。
工程2は、工程1において相溶させた状態の樹脂混合物を紡糸し、微細な相分離構造を形成する工程である。
工程2において得られた多孔質炭素繊維の前駆体は、炭化工程(工程3)に供される前、または炭化工程(工程3)と同時、またはその両方で消失樹脂の除去処理を行うことが好ましい。
工程2において多孔質炭素繊維の前駆体は、炭化工程(工程3)に供される前に不融化処理を行うことが好ましい。
工程3は、工程2において得られた多孔質炭素繊維の前駆体、あるいは必要に応じて消失樹脂の除去および/または不融化処理に供された前駆体を焼成し、炭化して多孔質炭素繊維を得る工程である。
工程4は、工程3により製造した多孔質炭素繊維の表面に有機高分子層を形成する工程である。
本発明の流体分離膜モジュールは、ケーシング内に本発明の流体分離膜を複数本収容してなる。
本発明の流体分離膜を用いて実際に流体分離を行う際には、複数本の流体分離膜を接続しケーシング内に収納して流体分離膜モジュールとして使用する。
(共連続多孔構造の有無)
流体分離膜または多孔質炭素繊維を液体窒素中で充分に冷却後、ピンセットで割断して形成した断面の多孔質炭素繊維部分を走査型電子顕微鏡で表面観察し、炭素骨格の枝部と細孔部(空隙部)がそれぞれ連続しつつ三次元的に規則的に絡み合った構造であった場合、共連続多孔構造を有していると判定した。
流体分離膜の圧縮強度の測定は、株式会社島津製作所製の微小圧縮試験機MCTW-500を用い、多孔質炭素繊維1本を治具で挟み、φ500μmのダイヤモンド製平面圧子を用い、負荷速度41.482mN/sの負荷速度一定方式にて繊維断面方向に圧縮して圧縮変位と荷重を測定し、圧縮強度σを下記の式により算出した。
多孔質炭素繊維を試料プレートに固定し、CuKα線光源から得られたX線源から散乱角度10°未満の情報が得られるように、光源、試料および二次元検出器の位置を調整した。二次元検出器から得られた画像データ(輝度情報)から、ビームストッパーの影響を受けている中心部分を除外して、ビーム中心から動径を設け、角度1°毎に360°の輝度値を合算して散乱角度2θに対する散乱強度分布曲線を得た。得られた曲線においてピークを持つ位置の散乱角度2θより、連続構造部分の構造周期を下記の式によって得た。
上記のX線散乱より得られた散乱角度2θ(横軸)と散乱強度(縦軸)からなる散乱強度分布曲線において、散乱強度のピークの頂点を点Aとし、点Aからグラフの縦軸に平行な直線を引き、該直線とスペクトルのベースラインとの交点を点Bとしたとき、点Aと点Bを結ぶ線分の中点Cにおけるピークの幅をX線散乱の強度ピーク半値幅とした。
多孔質炭素繊維を樹脂中に包埋し、その後カミソリで繊維断面を露出させ、日本電子株式会社製クロスセクションポリッシャー装置SM-09010を用いて加速電圧5.5kVにて試料表面にアルゴンイオンビームを照射、エッチングを施す。
平均空隙率(%)=A/B×100
多孔質炭素繊維を300℃、5時間の条件で真空乾燥を行うことで吸着したガス成分を除去した。その後、株式会社島津製作所製の自動ポロシメータ(オートポアIV9500)を用いて水銀圧入法にて細孔直径分布曲線を取得した。
多孔質炭素繊維20本をマイクロメーターで測定し、その算術平均値を繊維直径Dとした。
株式会社日立ハイテクノロジーズ製の走査型電子顕微鏡S-5500を用い、多孔質炭素繊維表面を1±0.1(nm/画素)となる倍率にて70万画素以上で観察して取得した画像を画像解析ソフト“ImageJ”によって繊維表面を枝部(炭素部)および細孔部(空隙部)に分離した。
流体分離膜を種々の直径の円柱に180°以上巻きつけて、膜が破断するかどうかを観測した。曲げ半径は、膜が破断しない円柱において最小の半径を有する円柱を求め、その円柱の半径の値で示した。
長さ10cmの流体分離膜を20本束ねて外径φ6mm、肉厚1mmのステンレス製のケーシング内に収容し、束ねた流体分離膜の端をエポキシ樹脂系接着剤でケーシング内面に固定するとともにケーシングの両端を封止して、流体分離膜モジュールを作製し、ガス透過速度を測定した。
透過速度Q=[ガス透過流量(cm3・STP)]/[膜面積(cm2)×時間(s)×圧力差(cmHg)
芳香族ポリイミド“Matrimid(登録商標)”5218をN-メチルピロリドン(NMP)に溶解させて10.0重量%の芳香族ポリイミド溶液を作製した。
芳香族ポリイミド“Matrimid(登録商標)”5218をN-メチルピロリドン(NMP)に溶解させて25.0重量%の芳香族ポリイミド溶液を作製した。
70gのポリサイエンス社製ポリアクリロニトリル(MW15万)と70gのシグマ・アルドリッチ社製ポリビニルピロリドン(MW4万)、及び、溶媒として400gの和研薬製ジメチルスルホキシド(DMSO)をセパラブルフラスコに投入し、3時間攪拌および還流を行いながら150℃で均一かつ透明な溶液を調製した。このときポリアクリロニトリルの濃度、ポリビニルピロリドンの濃度はそれぞれ10重量%であった。
ポリアクリロニトリルおよびポリビニルピロリドンの濃度がそれぞれ11.5重量%のポリマー溶液を用いて紡糸を行った以外は実施例1と同様の手法で多孔質炭素繊維を作製した。
ポリアクリロニトリルおよびポリビニルピロリドンの濃度がそれぞれ13重量%のポリマー溶液を用いて紡糸を行い、到達温度を700℃とした以外は実施例1と同様の手法で多孔質炭素繊維を作製した。
芯鞘型の二重口金の内管から5mL/分で溶液を吐出し、外管からDMSO90重量%水溶液を8.8mL/分で同時に吐出して紡糸を行った以外は実施例1と同様の手法で多孔質炭素繊維を作製した。
芯鞘型の三重口金を用い、内管からDMSO85重量%水溶液を1mL/分で吐出し、中管からポリマー溶液を3mL/分で吐出し、外管からDMSO90重量%水溶液を5.3mL/分で同時に吐出した中空糸状の多孔質炭素繊維を作製した以外は実施例1と同様の手法で多孔質炭素繊維を作製した。
φ0.6mmの一穴の口金を用いてポリアクリロニトリルおよびポリビニルピロリドンの濃度がそれぞれ10重量%のポリマー溶液を用いて紡糸を行った以外は実施例1と同様の手法で多孔質炭素繊維を作製した。得られた多孔質炭素繊維の表面には緻密な層が形成されており、細孔は確認されなかった。
シクロヘキサノンパーオキシド(パーオキサH、日本油脂株式会社製)1部を、メチルメタクリレート(以下MMAと略記する)100部に溶かし、純水800部と乳化剤としてペレックスOTP(日本油脂株式会社製)1部を反応釜に加えて、不活性ガスで十分に置換した後、40℃に保持し、ロンガリット0.76部と硫酸水溶液でpH3とした後、重合を開始した。そのまま攪拌を続け、150分で第一段目の乳化重合を完結させた。
調製例2で作製した芳香族ポリイミド溶液を50℃に加温し、芯鞘型の二重口金の内管からは純水を4mL/分で吐出し、外管からは前記芳香族ポリイミドを8mL/分で同時に吐出した後、25℃の純水からなる凝固浴へ導き、ローラーに巻き取ることで原糸を得た。
2:多孔質炭素繊維
3:有機高分子層
Claims (14)
- 共連続多孔構造を有する多孔質炭素繊維の表面に、有機高分子層が形成されてなる流体分離膜。
- 前記多孔質炭素繊維の全体に前記共連続多孔構造を有する、請求項1に記載の流体分離膜。
- 水銀圧入法により測定される前記多孔質炭素繊維の全体の平均細孔直径が30~5,000nmである、請求項1または2に記載の流体分離膜。
- 走査型電子顕微鏡による表面観察によって測定される前記多孔質炭素繊維の表面の平均細孔直径が2~500nmである、請求項1~3のいずれか1項に記載の流体分離膜。
- 前記共連続多孔構造の構造周期が10~10,000nmである、請求項1~4のいずれか1項に記載の流体分離膜。
- 前記多孔質炭素繊維のX線散乱の強度ピークの半値幅が5°以下である、請求項1~5のいずれか1項に記載の流体分離膜。
- 前記有機高分子層が、芳香族ポリイミド、酢酸セルロース、ポリスルホン、芳香族ポリアミド、ポリエーテルイミド、ポリエーテルスルホン、ポリアクリロニトリル、ポリフェニレンスルフィド、ポリエーテルエーテルケトン、ポリテトラフルオロエチレン、ポリフッ化ビニリデンおよびこれらの誘導体からなる群より選択される1種または2種以上の有機高分子を含む層である、請求項1~6のいずれか1項に記載の流体分離膜。
- 前記有機高分子層が、芳香族ポリイミド、芳香族ポリアミドおよびこれらの誘導体からなる群より選択される1種または2種以上の有機高分子を含む層である、請求項1~7のいずれか1項に記載の流体分離膜。
- ケーシング内に請求項1~8のいずれか1項に記載の流体分離膜を複数本収容してなる流体分離膜モジュール。
- 全体に共連続多孔構造を有する多孔質炭素繊維。
- 水銀圧入法により測定される全体の平均細孔直径が30nm~5,000nmである、請求項10に記載の多孔質炭素繊維。
- 走査型電子顕微鏡による表面観察によって測定される表面の平均細孔直径が2~500nmである、請求項10または11に記載の多孔質炭素繊維。
- 前記共連続多孔構造の構造周期が10~10,000nmである、請求項10~12のいずれか1項に記載の多孔質炭素繊維。
- X線散乱の強度ピークの半値幅が5°以下である、請求項10~13のいずれか1項に記載の多孔質炭素繊維。
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US16/070,695 US10835874B2 (en) | 2016-01-22 | 2017-01-17 | Fluid separation membrane, fluid separation membrane module, and porous carbon fiber |
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