JP2017027919A - Electrode material for redox battery - Google Patents
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Classifications
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
- Y02E60/30—Hydrogen technology
- Y02E60/50—Fuel cells
Abstract
Description
本発明は、レドックス電池に好適な活性能を有する多孔質電極材に関する。 The present invention relates to a porous electrode material having active ability suitable for a redox battery.
従来より、電極は電池の性能を左右するものとして重点的に開発されている。電極には、それ自体が活物質とならず、活物質の電気化学的反応を促進させる反応場として働くタイプのものがあり、このタイプには導電性や耐薬品性などから炭素材料がよく用いられる。特に電力貯蔵用に開発が盛んなレドックスフロー電池の電極には、耐薬品性があり、導電性を有し、かつ通液性のある炭素質繊維の不織布等が用いられている。 Conventionally, electrodes have been intensively developed as affecting the performance of batteries. There are electrode types that do not become active materials themselves but act as reaction fields that promote the electrochemical reaction of the active materials. Carbon materials are often used for this type because of their electrical conductivity and chemical resistance. It is done. In particular, the electrode of a redox flow battery, which has been actively developed for power storage, uses a carbon fiber non-woven fabric having chemical resistance, conductivity, and liquid permeability.
レドックスフロー電池は、正極に鉄の塩酸水溶液、負極にクロムの塩酸水溶液を用いたタイプから、起電力の高いバナジウムの硫酸水溶液を両極に用いるタイプに替わり、高エネルギー密度化されたが、最近さらに活物質濃度を高める開発が進み、一段と高エネルギー密度化が進んでいる。 The redox flow battery has been changed from a type that uses an aqueous hydrochloric acid solution of iron for the positive electrode and an aqueous solution of chromium hydrochloric acid for the negative electrode to a type that uses an aqueous solution of vanadium sulfuric acid with a high electromotive force for both electrodes. Development to increase the active material concentration is progressing, and energy density is further increased.
正極電解液にオキシ硫酸バナジウム、負極電解液に硫酸バナジウムの各々硫酸酸性水溶液を用いたレドックスフロー型電池の場合、放電時には、Ｖ2+を含む電解液が負極側に供給され、正極側のにはＶ5+（実際には酸素を含むイオン）を含む電解液が供給される。負極側の流路では、電極内でＶ2+が電子を放出しＶ3+に酸化される。放出された電子は外部回路を通って正極側の電極内でＶ5+をＶ4+（実際には酸素を含むイオン）に還元する。この酸化還元反応に伴って負極電解液中のＳＯ4 2-が不足し、正極電解液ではＳＯ4 2-が過剰になるため、イオン交換膜を通ってＳＯ4 2-が正極側から負極側に移動し電荷バランスが保たれる。あるいは、Ｈ+がイオン交換膜を通って負極側から正極側へ移動することによっても電荷バランスを保つことができる。充電時には放電と逆の反応が進行する。 In the case of a redox flow battery using a sulfuric acid aqueous solution of vanadium oxysulfate as the positive electrode electrolyte and vanadium sulfate as the negative electrode electrolyte, the electrolyte containing V 2+ is supplied to the negative electrode side during discharge, Is supplied with an electrolyte containing V 5+ (actually ions containing oxygen). In the negative channel, V 2+ emits electrons in the electrode and is oxidized to V 3+ . The emitted electrons pass through an external circuit and reduce V 5+ to V 4+ (actually ions containing oxygen) in the positive electrode. With this oxidation-reduction reaction, SO 4 2- in the negative electrode electrolyte becomes insufficient, and SO 4 2- becomes excessive in the positive electrode electrolyte, so that SO 4 2- passes through the ion exchange membrane from the positive electrode side to the negative electrode side. The charge balance is maintained. Alternatively, the charge balance can be maintained by moving H + through the ion exchange membrane from the negative electrode side to the positive electrode side. During charging, a reaction opposite to discharging proceeds.
レドックス電池用電極材の特性としては、特に以下に示す性能が要求される。 As the characteristics of the redox battery electrode material, the following performance is particularly required.
1)目的とする反応以外の副反応を起こさないこと（反応選択性が高いこと）、具体的には電流効率（ηI）が高いこと。
2)電極反応活性が高いこと、具体的にはセル抵抗（Ｒ）が小さいこと。すなわち電圧効率（ηV）が高いこと。
3)上記1)、2)に関連する電池エネルギー効率（ηE）が高いこと。
ηE＝ηI×ηV
4)くり返し使用に対する劣化が小さいこと（高寿命）、具体的には電池エネルギー効率（ηE）の低下量が小さいこと。
1) No side reactions other than the intended reaction should occur (high reaction selectivity), specifically high current efficiency (η I ).
2) High electrode reaction activity, specifically, low cell resistance (R). That is, the voltage efficiency (η V ) is high.
3) Battery energy efficiency (η E ) related to 1) and 2) above is high.
η E = η I × η V
4) Deterioration against repeated use is small (long life), specifically, the amount of decrease in battery energy efficiency (η E ) is small.
そして、セル抵抗（Ｒ）に関しては、炭素質繊維集合体等の繊維間及び、電極材と集電板との接触抵抗、電極材自身の導電性が寄与する導電抵抗、充放電時においてバナジウムイオンが価数変化する際の電極活性が寄与する電荷移動反応抵抗、バナジウムイオンや電解液の拡散が寄与する拡散抵抗に大別される。 As for cell resistance (R), the contact resistance between the fibers of the carbonaceous fiber aggregate and the like, the contact resistance between the electrode material and the current collector, the conductivity contributed by the conductivity of the electrode material itself, vanadium ions at the time of charge / discharge Are broadly classified into charge transfer reaction resistance contributed by electrode activity when the valence changes, and diffusion resistance contributed by diffusion of vanadium ions and electrolyte.
電荷移動反応抵抗に関しては、一般的に空気中４００〜７００℃程度で熱処理を施し、黒鉛結晶化炭素繊維表面にヒドロキシル基やカルボキシル基などの酸性官能基を導入することで活性化させ、該抵抗を低減させている。 Regarding the charge transfer reaction resistance, heat treatment is generally performed at about 400 to 700 ° C. in the air, and activated by introducing acidic functional groups such as hydroxyl groups and carboxyl groups on the surface of the graphite crystallized carbon fiber. Is reduced.
しかしながら、前述の導電抵抗と電荷移動反応抵抗は、一方を高めるともう一方の特性を著しく損なう、いわゆるトレードオフの関係にある。そこで、両者の特性をバランス良く発現させるために、種々の方法が提案されている。例えば、特許文献１には、Ｘ線広角解析より求めた＜００２＞面間隔が、平均３．７０Å以下であり、またｃ軸方向の結晶子の大きさが平均９．０Å以上の擬黒鉛微結晶を有し、かつ全酸性官能基量が少なくとも０．０１ｍｅｑ／ｇである炭素質材料をレドックスフロー電池の電極材として用いることが提案されている。 However, the above-described conductive resistance and charge transfer reaction resistance have a so-called trade-off relationship in which when one is increased, the other characteristic is remarkably impaired. Therefore, various methods have been proposed in order to express both characteristics in a well-balanced manner. For example, Patent Document 1 discloses that a pseudo-graphite fine particle whose <002> plane spacing obtained by X-ray wide-angle analysis is 3.70 mm or less on average and the crystallite size in the c-axis direction is 9.0 mm or more on average. It has been proposed to use a carbonaceous material having crystals and a total acidic functional group amount of at least 0.01 meq / g as an electrode material for a redox flow battery.
また、特許文献２には、ポリアクリロニトリル系繊維を原料とする炭素質繊維で、Ｘ線広角解析より求めた＜００２＞面間隔が３．５０〜３．６０Åの擬黒鉛結晶構造を有し、炭素質材料表面の結合酸素原子数が炭素原子数の１０〜２５％となるような炭素質材をレドックスフロー電池の電極材として用いることが提案されている。 Further, Patent Document 2 is a carbonaceous fiber made from polyacrylonitrile-based fiber, and has a pseudo-graphite crystal structure with a <002> plane spacing of 3.50 to 3.60 mm determined by X-ray wide angle analysis, It has been proposed to use a carbonaceous material whose number of bonded oxygen atoms on the surface of the carbonaceous material is 10 to 25% of the number of carbon atoms as an electrode material for a redox flow battery.
さらに特許文献３には、Ｘ線広角解析より求めた＜００２＞面間隔が３．４３〜３．６０Åで、ｃ軸方向の結晶子の大きさが１５〜３３Åで、ａ軸方向の結晶子の大きさが３０〜７５Åである擬黒鉛結晶構造を有し、ＸＰＳ表面分析より求めた表面酸性官能基量が全表面炭素原子数の０．２〜１．０％であり、表面結合窒素原子数が全表面炭素原子数の３％以下である炭素質材料をバナジウム系レドックスフロー電池の電解槽用電極材として用いることが提案されている。 Further, Patent Document 3 discloses that the <002> plane spacing obtained by X-ray wide angle analysis is 3.43 to 3.60 mm, the crystallite size in the c-axis direction is 15 to 33 mm, and the crystallite in the a-axis direction. Having a pseudo-graphite crystal structure with a size of 30 to 75 mm, the amount of surface acidic functional groups determined by XPS surface analysis is 0.2 to 1.0% of the total surface carbon atoms, and surface-bound nitrogen atoms It has been proposed to use a carbonaceous material having a number of 3% or less of the total surface carbon atoms as an electrode material for an electrolytic cell of a vanadium redox flow battery.
しかしながら、特許文献１〜３の技術においても、前述のトレードオフからの脱却はできておらず、セル抵抗をさらに低減させることは困難であり、高い電池エネルギー効率を得られない。 However, even in the techniques of Patent Documents 1 to 3, it is not possible to escape from the trade-off described above, and it is difficult to further reduce the cell resistance, and high battery energy efficiency cannot be obtained.
そこで、本発明の目的は、かかる事情に鑑み、従来の酸性官能基に代わる活性化官能基を導入することで、レドックス電池のセル抵抗を低減してエネルギー効率を高めることができる炭素電極材集合体を提供することにある。 Therefore, in view of such circumstances, an object of the present invention is to introduce a carbon electrode material assembly that can reduce the cell resistance of a redox battery and increase energy efficiency by introducing an activated functional group instead of a conventional acidic functional group. To provide a body.
本発明者らは、炭素材料電極の表面に窒素原子を含有する化合物を被覆または担時し、これを熱分解させることで、レドックス電池における炭素材料の活性能が高くなることを見出した。このような方法により得られた炭素材料は、従来の活性のみを有する酸性官能基と異なり、導電性と活性能を兼ね備えたピリジン型の窒素原子を多く含んでいた。これにより、従来の酸性官能基導入にはない特性を発現させることができた。本発明は、このような知見にしたがい、さらに研究を重ね、完成されたものである。即ち、本発明は、以下の構成を包含する。 The present inventors have found that the activity of the carbon material in the redox battery is enhanced by coating or supporting a compound containing a nitrogen atom on the surface of the carbon material electrode and thermally decomposing it. Unlike conventional acidic functional groups having only activity, the carbon material obtained by such a method contained many pyridine type nitrogen atoms having both conductivity and activity. Thereby, the characteristic which is not in the conventional acidic functional group introduction | transduction was able to be expressed. The present invention has been completed by further research based on such knowledge. That is, the present invention includes the following configurations.
本発明は、以下の構成から成る。
１．Ｘ線広角解析より求めた＜００２＞面間隔が３．４３〜３．６０Åで、ｃ軸方向の結晶子の大きさが１５〜５０Åで、ａ軸方向の結晶子の大きさが３０〜７５Åである擬黒鉛結晶構造を有し、ＸＰＳ表面分析より求めた表面の結合酸素原子数が全表面炭素原子数の１．０％以上である炭素質材料の表面に窒素原子を含有する化合物を被覆または担時し、これを熱分解させて、前記炭素材料表面に窒素原子をドープし、これを電極活性点としたことを特徴とする、レドックスフロー電池用炭素電極。
２．前記窒素原子を含有する化合物が、含窒素複素環化合物であることを特徴とする、１に記載のレドックス電池用炭素電極材。
３．前記含窒素複素環化合物が、メラニン、ピロール、ピリジン、イミダゾールのいずれかを少なくとも１種以上有する低分子または高分子であることを特徴とする、２に記載のレドックス電池用炭素電極材。
４．前記炭素材料が、炭素質繊維の不織布または織布よりなる１〜３のいずれかに記載のレドックス電池用炭素電極材。
５．前記１〜４のいずれかに記載の炭素電極材を用いたレドックス電池。
The present invention has the following configuration.
1. The <002> plane spacing determined by X-ray wide angle analysis is 3.43 to 3.60 mm, the crystallite size in the c-axis direction is 15 to 50 mm, and the crystallite size in the a-axis direction is 30 to 75 mm. A compound containing nitrogen atoms is coated on the surface of a carbonaceous material having a pseudo-graphite crystal structure of which the number of bonded oxygen atoms on the surface determined by XPS surface analysis is 1.0% or more of the total surface carbon atoms. Alternatively, the carbon electrode for a redox flow battery, wherein the carbon material surface is thermally decomposed and doped with nitrogen atoms on the surface of the carbon material to serve as an electrode active point.
2. 2. The redox battery carbon electrode material according to 1, wherein the compound containing a nitrogen atom is a nitrogen-containing heterocyclic compound.
3. 3. The redox battery carbon electrode material according to 2, wherein the nitrogen-containing heterocyclic compound is a low molecule or polymer having at least one of melanin, pyrrole, pyridine, and imidazole.
4). The carbon electrode material for a redox battery according to any one of 1 to 3, wherein the carbon material is a carbon fiber non-woven fabric or woven fabric.
5. The redox battery using the carbon electrode material in any one of said 1-4.
本発明の窒素原子を導入したレドックス電池用炭素電極材は、優れた活性能を有し、結果として低抵抗な電極材が得られた。これにより、レドックス電池用炭素電極材として際立った性能を示す材料を提供することができる。 The carbon electrode material for redox batteries into which the nitrogen atom of the present invention is introduced has an excellent activity ability, and as a result, a low resistance electrode material is obtained. Thereby, the material which shows outstanding performance as a carbon electrode material for redox batteries can be provided.
以下、本発明を詳細に説明する。本発明は、優れた活性能を有し、レドックス電池用炭素電極材として際立った性能を示す材料を提供することができる。すなわち、Ｘ線広角解析より求めた＜００２＞面間隔が３．４３〜３．６０Åで、ｃ軸方向の結晶子の大きさが１５〜５０Åで、ａ軸方向の結晶子の大きさが３０〜７５Åである擬黒鉛結晶構造を有し、ＸＰＳ表面分析より求めた表面の結合酸素原子数が全表面炭素原子数の１．０％以上である炭素質材料からなる炭素材料電極の表面に窒素原子を含有する化合物を被覆または担時し、これを熱分解させることで、導電性と活性能を兼ね備えたピリジン型の窒素原子を含むグラフェン構造を繊維上に導入する。これにより、従来の酸性官能基導入にはない特性を発現させることができ、結果として、低抵抗なレドックス電池用炭素電極材を提供することができる。そして、本発明の炭素電極材はフロータイプおよびノンフロータイプのレッドクス電池、またはリチウム、キャパシタ、燃料電池のシステムと複合化されたようなレドックス電池に好適に用いられるものである。これにより、従来の酸性官能基導入材料にはない特性を発現させることができ、結果として、低抵抗なレドックス電池用炭素電極材を提供することができる。 Hereinafter, the present invention will be described in detail. The present invention can provide a material having excellent activity and exhibiting outstanding performance as a carbon electrode material for a redox battery. That is, the <002> plane spacing obtained by X-ray wide angle analysis is 3.43 to 3.60 mm, the crystallite size in the c-axis direction is 15 to 50 mm, and the crystallite size in the a-axis direction is 30. Nitrogen is formed on the surface of a carbon material electrode having a pseudo-graphite crystal structure of ˜75% and having a carbonaceous material having 1.0% or more of total surface carbon atoms as determined by XPS surface analysis. By covering or supporting a compound containing an atom and thermally decomposing it, a graphene structure containing a pyridine type nitrogen atom having both conductivity and activity is introduced onto the fiber. Thereby, the characteristic which is not in the conventional acidic functional group introduction | transduction can be expressed, As a result, the low resistance carbon electrode material for redox batteries can be provided. The carbon electrode material of the present invention is suitably used for flow type and non-flow type Redox batteries, or redox batteries that are combined with lithium, capacitor, and fuel cell systems. Thereby, the characteristic which the conventional acidic functional group introduction | transduction material does not have can be expressed, As a result, the carbon electrode material for redox batteries with low resistance can be provided.
すなわち、本発明のレドックス電池用炭素電極材は、以下の特徴を有したピリジン型の窒素原子を含有する炭素電極材である。 That is, the carbon electrode material for a redox battery of the present invention is a carbon electrode material containing a pyridine type nitrogen atom having the following characteristics.
本発明のレドックス電池用炭素電極材を使用した電解槽は、その一例として図１に示す構造である。前記電解槽は、相対する二枚の集電板１、１間にイオン交換膜３が配設され、イオン交換膜３の両側にスペーサー２によって集電板１、１の内面に沿った電解液の通液路が形成されている。該通液路の少なくとも一方には本発明のレドックス電池用炭素電極材５が配設されており、このようにして電解槽が構成されている。なお、集電板１には、電解液の液流入口と液流出口とが設けられている。 An electrolytic cell using the carbon electrode material for a redox battery of the present invention has a structure shown in FIG. 1 as an example. In the electrolytic cell, an ion exchange membrane 3 is disposed between two opposing current collector plates 1 and 1, and an electrolytic solution is provided along the inner surface of the current collector plates 1 and 1 by spacers 2 on both sides of the ion exchange membrane 3. Is formed. At least one of the liquid passages is provided with the carbon electrode material 5 for a redox battery of the present invention, and thus an electrolytic cell is configured. The current collector plate 1 is provided with a liquid inlet and a liquid outlet for the electrolyte.
本発明のレドックス電池用炭素電極材５は、炭素質材料からなり、その構成組織は特に限定されないが、電極表面積を大きくできるものが好ましい。具体的には、炭素質繊維よりなる紡績糸、フィラメント集束糸、不織布、編物、織物、特殊編織物（例えば、特許文献４）またはこれらの混成組織からなる炭素質繊維集合体、多孔質炭素体、炭素−炭素複合体、粒子状炭素材料等を挙げることができる。これらのうち、炭素質繊維集合体が好ましく、なかでも炭素質繊維よりなるシート状物である炭素質繊維よりなる不織布、編物、織物、特殊織編物、またはこれらの混成組織からなる炭素質繊維集合体が、取り扱いや加工性、製造性等の点からより好ましい。 The carbon electrode material 5 for a redox battery of the present invention is made of a carbonaceous material, and the constitutional structure thereof is not particularly limited, but is preferably one that can increase the electrode surface area. Specifically, a spun yarn, a filament bundle yarn, a nonwoven fabric, a knitted fabric, a woven fabric, a special knitted fabric (for example, Patent Document 4) made of carbonaceous fibers, or a carbonaceous fiber assembly or a porous carbon body made of a hybrid structure thereof. , Carbon-carbon composites, particulate carbon materials, and the like. Among these, a carbonaceous fiber aggregate is preferable, and in particular, a non-woven fabric, a knitted fabric, a woven fabric, a special woven or knitted fabric composed of carbonaceous fibers, which is a sheet-shaped material composed of carbonaceous fibers, or a carbonaceous fiber assembly composed of a hybrid structure thereof. The body is more preferable in terms of handling, processability, manufacturability and the like.
前記炭素質材料の目付量は構成組織にもよるが、図１の集電板１とイオン交換膜３に挟まれたスペーサー２の厚み（以下、「スペーサー２の厚み」と言う）を０．３〜３ｍｍで使用する場合、５０〜１０００ｇ／ｍ2が好ましく、構成組織が編物の場合は５０〜１０００ｇ／ｍ2、織物の場合は５０〜８００ｇ／ｍ2、不織布の場合は５０〜６００ｇ／ｍ2が好ましい。また、炭素質材料として、片面に凹溝加工が施された不織布を使用することも通液性からより好ましい。その場合の溝幅、溝深さは少なくとも０．１ｍｍ以上が好ましい。 Although the basis weight of the carbonaceous material depends on the structure, the thickness of the spacer 2 sandwiched between the current collector plate 1 and the ion exchange membrane 3 in FIG. when used in 3～3Mm, preferably 50 to 1000 g / m 2, when construction organization of knitting 50 to 1000 g / m 2, in the case of textile 50 to 800 g / m 2, in the case of non-woven fabric 50～600G / m 2 is preferred. Moreover, it is more preferable from a liquid-permeable property to use the nonwoven fabric by which the concave groove process was given to the single side | surface as a carbonaceous material. In that case, the groove width and groove depth are preferably at least 0.1 mm.
前記炭素質材料の厚みは、スペーサー２の厚みより少なくとも大きいこと、不織布等の密度の低いものの場合はスペーサー２の厚みの１．５〜６．０倍が好ましい。しかしながら、厚みが厚すぎるとシート状物の圧縮応力のよりイオン交換膜３を突き破ってしまうことがあるので、シート状物の圧縮応力を９．８Ｎ／ｃｍ2以下のものを使用するのが好ましい。炭素質材料によっては、目付量・厚み・圧縮応力を調整するために、炭素質材料を２層や３層など積層して用いることも可能であり、また別の形態の炭素質材料との組み合わせも可能である。 The thickness of the carbonaceous material is preferably at least larger than the thickness of the spacer 2 and 1.5 to 6.0 times the thickness of the spacer 2 in the case of a low-density material such as a nonwoven fabric. However, if the thickness is too thick, it may break through the ion exchange membrane 3 due to the compressive stress of the sheet material, so it is preferable to use a sheet material having a compressive stress of 9.8 N / cm 2 or less. . Depending on the carbonaceous material, two or three layers of carbonaceous materials can be used to adjust the basis weight, thickness, and compressive stress, and combinations with other forms of carbonaceous materials Is also possible.
本発明の炭素電極に用いられる炭素質繊維集合体は、炭素質繊維で構成されるものである。炭素質繊維は、有機繊維のプレカーサーを加熱炭素化処理して得られる質量比で９０％以上が炭素で構成される繊維を意味する（ＪＩＳ Ｌ ０２０４−２）。炭素質繊維の原料となる有機繊維のプレカーサーとしては、ポリアクリロニトリル等のアクリル繊維；フェノール繊維；ポリパラフェニレンベンゾビスオキサゾール（ＰＢＯ）等のＰＢＯ繊維；芳香族ポリアミド繊維；等方性ピッチ、メソフェーズピッチ等のピッチ繊維；セルロース繊維；等を使用することができる。中でも、炭素質繊維の強度・弾性率に優れ、炭素質繊維集合体を形成することが容易となる観点から、有機繊維のプレカーサーとしては、アクリル繊維、ピッチ繊維が好ましく、アクリル繊維がより好ましい。アクリル繊維としては、アクリロニトリルを主成分として含有するものであれば特に限定されないが、アクリル繊維を形成する原料単量体中、アクリロニトリルの含有量が９５質量％以上であることが好ましく、９８質量％以上であることがより好ましい。
有機繊維の質量平均分子量は、特に限定されないが、１００００以上、１０００００以下であることが好ましく、１５０００以上、８００００以下であることがより好ましく、２００００以上、５００００以下であることがさらに好ましい。
The carbonaceous fiber assembly used for the carbon electrode of the present invention is composed of carbonaceous fibers. The carbonaceous fiber means a fiber in which 90% or more is composed of carbon by a mass ratio obtained by heating and carbonizing an organic fiber precursor (JIS L 0204-2). Organic fiber precursors used as raw materials for carbonaceous fibers include acrylic fibers such as polyacrylonitrile; phenol fibers; PBO fibers such as polyparaphenylenebenzobisoxazole (PBO); aromatic polyamide fibers; isotropic pitch and mesophase pitch. Pitch fibers such as cellulose fibers, etc. can be used. Among these, from the viewpoint of excellent strength and elastic modulus of the carbonaceous fiber and easy formation of the carbonaceous fiber aggregate, the organic fiber precursor is preferably an acrylic fiber or a pitch fiber, and more preferably an acrylic fiber. The acrylic fiber is not particularly limited as long as it contains acrylonitrile as a main component, but in the raw material monomer that forms the acrylic fiber, the content of acrylonitrile is preferably 95% by mass or more, and 98% by mass. More preferably.
The mass average molecular weight of the organic fiber is not particularly limited, but is preferably 10,000 or more and 100,000 or less, more preferably 15000 or more and 80000 or less, and further preferably 20,000 or more and 50000 or less.
炭素質材料として炭素質繊維を使用する場合、その平均繊維径は０．５〜２０μｍが好ましく、平均繊維長は３０〜１００ｍｍが好ましい。 When carbonaceous fibers are used as the carbonaceous material, the average fiber diameter is preferably 0.5 to 20 μm, and the average fiber length is preferably 30 to 100 mm.
特に、加熱炭素化処理は、少なくとも、耐炎化工程、および、炭素化工程を含むことが好ましい。 In particular, the heat carbonization treatment preferably includes at least a flameproofing step and a carbonization step.
前記耐炎化工程は、空気雰囲気下、有機繊維のプレカーサーを１８０℃以上３５０℃以下の温度で加熱し、耐炎化有機繊維を得る工程を意味する。熱処理温度は、１９０℃以上であることがより好ましく、２００℃以上であることがさらに好ましい。また、３３０℃以下であることが好ましく、３００℃以下であることがさらに好ましい。前記温度範囲で加熱することにより、有機繊維が熱分解することなく炭素質繊維の形態を保持したまま有機繊維中の窒素、水素の含有率を低減し、炭素化率を向上することができる。耐炎化工程の際、有機繊維が熱収縮し分子配向が崩壊して、炭素質繊維の導電性が低下する場合があることから、有機繊維を緊張下ないし延伸下で耐炎化処理することが好ましく、緊張下で耐炎化処理することがより好ましい。 The flameproofing step means a step of obtaining a flameproof organic fiber by heating a precursor of an organic fiber at a temperature of 180 ° C. or higher and 350 ° C. or lower in an air atmosphere. The heat treatment temperature is more preferably 190 ° C. or higher, and further preferably 200 ° C. or higher. Moreover, it is preferable that it is 330 degrees C or less, and it is more preferable that it is 300 degrees C or less. By heating in the said temperature range, the content rate of nitrogen and hydrogen in an organic fiber can be reduced and the carbonization rate can be improved, maintaining the form of a carbonaceous fiber, without organic fiber thermally decomposing. During the flameproofing step, the organic fibers may be thermally shrunk, the molecular orientation may be collapsed, and the conductivity of the carbonaceous fibers may be reduced. Therefore, it is preferable to flameproof the organic fibers under tension or stretching. More preferably, the flameproofing treatment is performed under tension.
前記炭素化工程は、不活性雰囲気下（好ましくは窒素雰囲気下）、耐炎化有機繊維を１０００℃以上２０００℃以下の温度で加熱し、炭素質繊維を得る工程を意味する。加熱温度は、１１００℃以上であることがより好ましく、１２００℃以上であることがさらに好ましい。また、より好ましくは１９００℃以下である。前記温度範囲で炭素化工程を行うことにより、有機繊維の炭素化が進行し、擬黒鉛結晶構造を有する炭素質繊維を得ることができる。
有機繊維は、それぞれ異なる結晶性を有するため、加熱温度は、原料とする有機繊維の種類に応じて選択することができる。
例えば、有機繊維としてアクリル樹脂（好ましくはポリアクリロニトリル）を使用する場合、加熱温度は２０００℃以下であることが好ましく、１８００℃以下であることがさらに好ましい。
The carbonization step means a step of heating the flame-resistant organic fiber at a temperature of 1000 ° C. or higher and 2000 ° C. or lower in an inert atmosphere (preferably in a nitrogen atmosphere) to obtain a carbonaceous fiber. The heating temperature is more preferably 1100 ° C. or higher, and further preferably 1200 ° C. or higher. Moreover, it is 1900 degrees C or less more preferably. By performing the carbonization step in the above temperature range, carbonization of the organic fiber proceeds, and a carbonaceous fiber having a pseudographite crystal structure can be obtained.
Since the organic fibers have different crystallinity, the heating temperature can be selected according to the type of organic fiber used as a raw material.
For example, when an acrylic resin (preferably polyacrylonitrile) is used as the organic fiber, the heating temperature is preferably 2000 ° C. or lower, and more preferably 1800 ° C. or lower.
前記耐炎化処理工程と炭素化工程とは、連続的に行うことが好ましく、耐炎化温度から炭素化温度へ昇温するときの昇温速度は、２０℃／分以下であることが好ましく、より好ましくは１５℃分／以下である。昇温速度を前記範囲とすることにより、有機繊維の形状を保持し、かつ機械的性質に優れた炭素質繊維を得ることができる。 The flameproofing treatment step and the carbonization step are preferably carried out continuously, and the rate of temperature rise when raising the temperature from the flameproofing temperature to the carbonization temperature is preferably 20 ° C./min or less, more Preferably, it is 15 ° C./min. By setting the heating rate within the above range, it is possible to obtain a carbonaceous fiber that maintains the shape of the organic fiber and is excellent in mechanical properties.
加熱炭素化処理は、さらに乾式酸化処理工程を含むことが好ましい。乾式酸化処理工程は、空気雰囲気下、炭素質繊維を５００℃以上、９００℃以下で加熱する工程を意味する。乾式酸化処理温度は、６００℃以上であることがより好ましく、６５０℃以上であることがさらに好ましい。また、８００℃以下であることがより好ましく、７５０℃以下であることが好ましい。前記温度範囲で炭素質繊維を乾式酸化処理することにより、炭素質繊維中の低結晶性部分が酸化消耗され、さらに結晶性に優れた炭素質繊維を得ることができる。
乾式酸化処理工程においては、炭素質繊維の機械的強度を維持する観点から、酸化前後の質量収率を９０％以上、９６％以下に調整することが好ましい。
The heating carbonization treatment preferably further includes a dry oxidation treatment step. The dry oxidation treatment step means a step of heating the carbonaceous fiber at 500 ° C. or more and 900 ° C. or less in an air atmosphere. The dry oxidation treatment temperature is more preferably 600 ° C. or higher, and further preferably 650 ° C. or higher. Moreover, it is more preferable that it is 800 degrees C or less, and it is preferable that it is 750 degrees C or less. By subjecting the carbonaceous fiber to a dry oxidation treatment within the above temperature range, the low crystalline portion in the carbonaceous fiber is oxidized and consumed, and a carbonaceous fiber having excellent crystallinity can be obtained.
In the dry oxidation treatment step, the mass yield before and after oxidation is preferably adjusted to 90% or more and 96% or less from the viewpoint of maintaining the mechanical strength of the carbonaceous fiber.
前記炭素質材料は、電池の中に圧接されて組み込まれ、その薄い隙間を粘度の高い電解液が流れるため、炭素質材料が脱落しないためには炭素質材料の引張強度を０．４９Ｎ／ｃｍ2以上にすることが好ましい。また集電板との接触抵抗を良くするために、炭素質材料が不織布組織の場合、密度を０．０１ｇ／ｃｍ3以上に、電極面に対する反発力を０．９８Ｎ／ｃｍ2以上にすることが好ましい。 The carbonaceous material is assembled by being pressed into the battery, and a high-viscosity electrolyte flows through the thin gap. Therefore, in order for the carbonaceous material not to fall off, the tensile strength of the carbonaceous material is 0.49 N / cm. It is preferable to make it 2 or more. Further, in order to improve the contact resistance with the current collector plate, when the carbonaceous material is a nonwoven fabric structure, the density should be 0.01 g / cm 3 or more and the repulsive force against the electrode surface should be 0.98 N / cm 2 or more. Is preferred.
本発明の炭素繊維の結晶構造が、Ｘ線広角解析より求めた＜００２＞面間隔が３．６０Åより大きい、ｃ軸方向の結晶子の大きさが１５Åより小さいか、またはａ軸方向の結晶子の大きさが５０Åより小さい場合、電池内部抵抗（セル抵抗）の内の電極材導電抵抗成分が無視できないようになり、その結果セル抵抗が増加し（電圧効率が低下し）、エネルギー効率が低下する。 The crystal structure of the carbon fiber of the present invention is such that the <002> plane spacing obtained by X-ray wide angle analysis is greater than 3.60 mm, the crystallite size in the c-axis direction is less than 15 mm, or the crystal in the a-axis direction. When the size of the child is smaller than 50 mm, the electrode material conductive resistance component in the battery internal resistance (cell resistance) cannot be ignored, resulting in an increase in cell resistance (decrease in voltage efficiency) and energy efficiency. descend.
また、本発明の炭素繊維の結晶構造が、Ｘ線広角解析より求めた＜００２＞面間隔が３．４３Åより小さいか、ｃ軸方向の結晶子の大きさが５０Åより大きいか、またはａ軸方向の結晶子の大きさが７５Åより大きい場合、充放電サイクルの繰り返しにより、セル抵抗は増加していき、エネルギー効率は低下していってしまう。これは、上述のような結晶構造を持つ炭素質材料では結晶構造内に歪みを持つか、黒鉛に近い構造を取るため、例えばレドックス電池の電解液に用いられる硫酸による分解を引き起こしやすいからであると考えられる。 Further, in the crystal structure of the carbon fiber of the present invention, the <002> plane spacing obtained by X-ray wide angle analysis is smaller than 3.43 mm, the crystallite size in the c-axis direction is larger than 50 mm, or the a-axis When the size of the crystallite in the direction is larger than 75 mm, the cell resistance increases and the energy efficiency decreases due to repeated charge / discharge cycles. This is because the carbonaceous material having the crystal structure as described above has a distortion in the crystal structure or has a structure close to that of graphite, so that it is likely to cause decomposition by sulfuric acid used in an electrolyte solution of a redox battery, for example. it is conceivable that.
本発明の炭素質材料は、ＸＰＳ（Ｘ線光電子分光法）表面分析より求めた炭素質材料表面の結合酸素原子数が全表面炭素原子数の１．０％以上であることが必要である。結合酸素原子数が全表面炭素原子数の１．０％以上の炭素系材料を電極材に用いることにより、電極反応速度を著しく高め得ることができる。ＸＰＳ表面分析より求めた炭素質材料表面の結合酸素原子数が全表面炭素原子数の１．０％未満の酸素濃度の低い炭素質材料を用いる場合は放電時の電極反応速度が小さく、電極反応活性を高めることはできない。このように材料表面に酸素原子を多く結合させた炭素質材料を電極材として用いることにより電極反応活性、いいかえれば電圧効率が高められる理由については明らかでないが、炭素質材料と電解液との親和性、電子の授受、錯イオンの炭素材料からの脱離、錯交換反応等に表面の酸素原子が有効に働いているものと考えられる。 The carbonaceous material of the present invention requires that the number of bonded oxygen atoms on the surface of the carbonaceous material determined by XPS (X-ray photoelectron spectroscopy) surface analysis is 1.0% or more of the total number of surface carbon atoms. The electrode reaction rate can be remarkably increased by using a carbon-based material having the number of bonded oxygen atoms of 1.0% or more of the total number of surface carbon atoms for the electrode material. When a carbonaceous material having a low oxygen concentration, in which the number of bonded oxygen atoms on the surface of the carbonaceous material obtained by XPS surface analysis is less than 1.0% of the total number of carbon atoms, the electrode reaction rate during discharge is small, and the electrode reaction The activity cannot be increased. The reason why the electrode reaction activity, in other words, the voltage efficiency is increased by using a carbonaceous material having many oxygen atoms bonded to the surface of the material as described above is not clear, but the affinity between the carbonaceous material and the electrolyte is not clear. It is considered that oxygen atoms on the surface are effectively working in the properties, electron transfer, desorption of complex ions from carbon materials, complex exchange reactions, and the like.
本発明のレドックス電池用炭素電極材においては、炭素がｓｐ2混成軌道により化学結合し、二次元に広がった六角網面構造を有する炭素原子の集合体であるグラフェンが存在することが好ましい。この六角網面構造に窒素原子が導入されると、ピリジン型、第４級型、ピロール型、酸化型等の構造を取り、これによってより優れた活性能を示す。なお、これらの構成比は、例えば、Ｘ線光電子分光測定（ＸＰＳ）等により測定することができる。 In the carbon electrode material for a redox battery according to the present invention, it is preferable that graphene that is an aggregate of carbon atoms having a hexagonal network structure that is two-dimensionally spread by chemically bonding carbon by sp 2 hybrid orbitals is present. When a nitrogen atom is introduced into this hexagonal network structure, it takes a pyridine type, quaternary type, pyrrole type, oxidized type or the like structure, thereby exhibiting better activity. In addition, these composition ratios can be measured by, for example, X-ray photoelectron spectroscopy (XPS).
窒素原子を含有する化合物に関しては、公知の含窒素化合物であれば特に制限はない。中でも、含窒素複素環化合物の方が、熱分解の際に窒素原子が導入されやすくなるため好ましい。また、窒素原子が構成単位中にできるだけ多い方がよく、ピロール、ピリジン、イミダゾール、ピリミジン、トリアゾールなどがより好ましい。 The compound containing a nitrogen atom is not particularly limited as long as it is a known nitrogen-containing compound. Among these, a nitrogen-containing heterocyclic compound is preferable because a nitrogen atom is easily introduced during thermal decomposition. Further, it is preferable that the number of nitrogen atoms is as large as possible in the structural unit, and pyrrole, pyridine, imidazole, pyrimidine, triazole, and the like are more preferable.
炭素材料電極の表面に窒素原子を含有する化合物を被覆または担時させる手法については、公知の任意の方法であれば、特に制限はない。例えば、前述の含窒素複素環化合物が低分子、高分子いずれの場合でも、粉末状で炭素材料表面に吹き付けることで担時させることができる。または、前述の含窒素複素環化合物を溶液とした後に、該炭素材料電極を溶液中に浸漬することで担時させることもできる。炭素材料電極の内部まで均一に担持できることから、溶液による担持方法が好ましい。 There is no particular limitation on the method of coating or supporting a compound containing a nitrogen atom on the surface of the carbon material electrode as long as it is a known arbitrary method. For example, in the case where the above-mentioned nitrogen-containing heterocyclic compound is either a low molecule or a high molecule, the nitrogen-containing heterocyclic compound can be loaded on the surface of the carbon material in a powder form. Or after making the above-mentioned nitrogen-containing heterocyclic compound into a solution, the carbon material electrode can be immersed in the solution, and it can be made to carry. Since it can carry | support uniformly to the inside of a carbon material electrode, the carrying | support method by a solution is preferable.
窒素原子を含有する化合物の熱分解温度は、５００℃以上が好ましく、７００℃以上がより好ましい。熱分解温度を上記以上とすることで、ピリジン型の窒素原子を含むグラフェン構造を十分に成長させることができる。また、熱分解時の雰囲気は、窒素ガスやアルゴンガスなど不活性雰囲気下で実施することが、同様の理由で好ましい。 The thermal decomposition temperature of the compound containing a nitrogen atom is preferably 500 ° C. or higher, and more preferably 700 ° C. or higher. By setting the thermal decomposition temperature to the above or higher, a graphene structure containing a pyridine type nitrogen atom can be sufficiently grown. Moreover, it is preferable for the same reason that the atmosphere at the time of thermal decomposition is carried out under an inert atmosphere such as nitrogen gas or argon gas.
本発明のレドックス電池用炭素電極材の形状は、多孔質形態であれば特に制限はなく、織布、不織布、紙、多孔フィルムなど多様な形状を採用することができるが、電解液の通液しやすさの観点から、繊維からなる織布や不織布であることが好ましい。 The shape of the carbon electrode material for a redox battery of the present invention is not particularly limited as long as it is a porous form, and various shapes such as a woven fabric, a nonwoven fabric, paper, and a porous film can be adopted. From the viewpoint of ease of use, a woven fabric or a nonwoven fabric made of fibers is preferable.
本発明における、繊維からなる織布や不織布は、平均繊維径は０．５〜２０μｍ、特に１〜１０μｍが好ましい。上記の範囲内とすることで、電極材としての強度を十分保てると共に、活性能を左右する繊維表面積も十分量確保することができる。 In the present invention, the woven fabric or non-woven fabric made of fibers preferably has an average fiber diameter of 0.5 to 20 μm, particularly 1 to 10 μm. By being within the above range, it is possible to sufficiently maintain the strength as an electrode material and to secure a sufficient amount of the fiber surface area that affects the activity ability.
本発明では、炭素材料電極の表面に窒素原子を含有する化合物を被覆または担時し、これを熱分解させる工程の前後で賦活処理を施してもよい。賦活処理を施すことにより、比表面積をより増大させ、活性能をより向上させることができる。 In the present invention, the activation treatment may be performed before and after the step of coating or carrying a compound containing a nitrogen atom on the surface of the carbon material electrode and thermally decomposing it. By performing the activation treatment, the specific surface area can be further increased and the activity ability can be further improved.
賦活処理としては、特に制限されない。例えば、水蒸気ガスによる賦活、炭酸ガスによる賦活、アルカリによる賦活、空気酸化による賦活等がいずれも採用できる。 The activation process is not particularly limited. For example, activation by water vapor gas, activation by carbon dioxide gas, activation by alkali, activation by air oxidation, etc. can be employed.
賦活温度は、特に制限されるわけではないが、７００〜１０００℃程度が好ましく、７５０〜９５０℃程度がより好ましい。賦活温度をこの範囲とすれば、比表面積をより増大させ、活性能をより向上させることができる。 The activation temperature is not particularly limited, but is preferably about 700 to 1000 ° C, more preferably about 750 to 950 ° C. If the activation temperature is within this range, the specific surface area can be further increased and the activity ability can be further improved.
具体的な賦活処理の方法としては、例えば、不活性ガスの雰囲気下、毎時４００℃以下程度（特に毎時３００℃以下程度）の昇温条件で賦活温度（好ましくは７００〜１０００℃）まで昇温し、例えば水蒸気賦活を行う場合は水蒸気を吹き込んで数時間保持すればよい。この際使用できる還元ガスは、上記したものが挙げられる。 As a specific activation method, for example, the temperature is increased to an activation temperature (preferably 700 to 1000 ° C.) under an inert gas atmosphere under a temperature increase condition of about 400 ° C. or less (particularly about 300 ° C. or less). For example, when steam activation is performed, steam may be blown and held for several hours. Examples of the reducing gas that can be used at this time include those described above.
賦活する方法は、特に限定されない。例えば、典型例として、水蒸気賦活する場合には、上記賦活温度まで昇温後、５〜５０Vol％、好ましくは１０〜３０Vol％の濃度になるように水蒸気ガスを吹き込めばよい。 The method for activation is not particularly limited. For example, as a typical example, when steam activation is performed, steam gas may be blown to a concentration of 5 to 50 Vol%, preferably 10 to 30 Vol% after raising the temperature to the activation temperature.
以下に実施例及び比較例を挙げて、本発明をより詳細に説明する。なお、本発明は、以下の実施例に限定されるものではない。 Hereinafter, the present invention will be described in more detail with reference to Examples and Comparative Examples. The present invention is not limited to the following examples.
本発明において採用される＜００２＞面間隔（ｄ００２）、ｃ軸方向の結晶子の大きさ（Ｌｃ）、ａ軸方向の結晶子の大きさ（Ｌａ）、ＸＰＳ表面分析、水銀圧入法、電流効率、電圧効率（セル抵抗Ｒ）、エネルギー効率および充放電サイクルの経時変化の各測定法について説明する。 <002> spacing (d002) employed in the present invention, crystallite size in the c-axis direction (Lc), crystallite size in the a-axis direction (La), XPS surface analysis, mercury intrusion method, current Each measuring method of efficiency, voltage efficiency (cell resistance R), energy efficiency, and change with time of the charge / discharge cycle will be described.
（１）＜００２＞面間隔（ｄ００２）、結晶子の大きさ（Ｌｃ）、ａ軸方向の結晶子の大きさ（Ｌａ）
電極材料をメノウ乳鉢で、粒径１０μｍ程度になるまで粉砕し、試料に対して約５重量％のＸ線標準用高純度シリコン粉末を内部標準物質として混合し、試料セルに詰め、ＣｕＫα線を線源として、ディフラクトメーター法によって広角Ｘ線を測定する。
(1) <002> spacing (d002), crystallite size (Lc), crystallite size in the a-axis direction (La)
The electrode material is pulverized in an agate mortar until the particle size becomes about 10 μm, and about 5% by weight of X-ray standard high-purity silicon powder is mixed as an internal standard substance, packed in a sample cell, and CuKα rays As a radiation source, wide-angle X-rays are measured by a diffractometer method.
曲線の補正には、いわゆるローレンツ因子、偏光因子、吸収因子、原子散乱因子等に関する補正を行わず、次の簡便法を用いる。すなわち、＜００２＞回折に相当するピークのベースラインからの実質強度をプロットし直して＜００２＞補正強度曲線を得る。この曲線のピーク高さの２／３の高さに引いた角度軸に平行な線が補正強度曲線と交わる線分の中点を求め、中点の角度を内部標準で補正し、これを回折角の２倍とし、ＣｕＫαの波長λとから数式１のＢｒａｇｇの式によって＜００２＞面間隔を求める。 For the correction of the curve, the following simple method is used without correcting the so-called Lorentz factor, polarization factor, absorption factor, atomic scattering factor and the like. That is, the actual intensity from the baseline of the peak corresponding to <002> diffraction is re-plotted to obtain a <002> corrected intensity curve. Find the midpoint of the line segment where the line parallel to the angle axis drawn to 2/3 of the peak height of this curve intersects the correction intensity curve, and correct the midpoint angle with the internal standard. The <002> plane spacing is obtained from the Bragg equation of Formula 1 from the wavelength λ of CuKα, which is twice the folding angle.
さらに、ピーク高さの１／２の高さに引いた角度軸に平行な線が、補正強度曲線と交わる線分の長さ（半値幅β）から、数式２によってｃ軸方向の結晶子の大きさＬｃを求める。 Further, from the length of the line segment intersecting with the correction intensity curve (half-value width β), the line parallel to the angle axis drawn to ½ the height of the peak height, the value of the crystallite in the c-axis direction is calculated according to Equation 2. The size Lc is obtained.
また＜１０＞回折に相当するピークのベースラインからの実質強度をプロットし直して＜１０＞補正強度曲線を得る。ピーク高さの１／２の高さに引いた角度軸に平行な線が補正強度曲線と交わる線分の長さ（半値幅β）から数式３によってａ軸方向の結晶子の大きさＬａを求める。 Also, the actual intensity from the baseline of the peak corresponding to <10> diffraction is re-plotted to obtain a <10> corrected intensity curve. The crystallite size La in the a-axis direction is calculated by Equation 3 from the length (half-value width β) of the line segment where the line parallel to the angle axis drawn to ½ the peak height intersects the correction intensity curve. Ask.
（２）ＸＰＳ表面分析
ＥＳＣＡまたはＸＰＳと略称されているＸ線光電子分光法の測定に用いた装置はアルバック・ファイ５８０１ＭＣである。
試料をサンプルホルダー上にＭｏ板で固定し、予備排気室にて十分に排気後、測定室のチャンバーに投入した。線源にはモノクロ化ＡｌＫα線を用い、出力は１４ｋＶ、１２ｍＡ、装置内真空度は１０-8ｔｏｒｒとする。
全元素スキャンを行い表面元素の構成を調べ、検出された元素ならびに予想される元素についてナロースキャンを実施し、存在比率を評価する。
全表面炭素原子数に対する表面結合酸素原子数の比を百分率（％）で算出する。
(2) XPS surface analysis The apparatus used for the measurement of the X-ray photoelectron spectroscopy abbreviated as ESCA or XPS is ULVAC-PHI 5801MC.
The sample was fixed on the sample holder with a Mo plate, exhausted sufficiently in the preliminary exhaust chamber, and then put into the chamber of the measurement chamber. A monochromatic AlKα ray is used as the radiation source, the output is 14 kV, 12 mA, and the vacuum in the apparatus is 10 −8 torr.
A full element scan is performed to examine the composition of the surface elements, a narrow scan is performed on the detected and expected elements, and the abundance ratio is evaluated.
The ratio of the number of surface-bound oxygen atoms to the total number of surface carbon atoms is calculated as a percentage (%).
（実施例１）
耐炎化ポリアクリロニトリルからなるフェルト（厚さ４．５ｍｍ、坪量６００ｇ／ｍ2）を窒素雰囲気下で、１００℃／ｈ以下の昇温温度で１５００℃まで昇温した。その後１時間焼成して炭素化後、常温まで空冷した。その後、メラニンをＮ−メチル−２−ピロリドンに溶解させ、本溶液中に上記の電極材を浸漬し、超音波処理により脱泡を行った。浸漬後の電極材に付着した余分なメラニン溶液を拭き取り、これを１００℃で２時間乾燥させた。メラニン担持後の該電極材料を、窒素ガス雰囲気下で９００℃で１時間焼成し、目的とする窒素ドープされた電極材料を得た。得られた電極材料の＜００２＞面間隔は３．５５Åで、Ｌｃは２３Å、Ｌａは４５Å、ＸＰＳ表面分析の結果、窒素原子数は２５％、酸素原子数は８％であった。
Example 1
A felt made of flame-resistant polyacrylonitrile (thickness 4.5 mm, basis weight 600 g / m 2 ) was heated to 1500 ° C. at a temperature rising temperature of 100 ° C./h or less in a nitrogen atmosphere. Thereafter, the mixture was baked for 1 hour, carbonized, and then cooled to room temperature. Thereafter, melanin was dissolved in N-methyl-2-pyrrolidone, the electrode material was immersed in this solution, and defoamed by ultrasonic treatment. The excess melanin solution adhering to the electrode material after immersion was wiped off and dried at 100 ° C. for 2 hours. The electrode material after supporting melanin was baked at 900 ° C. for 1 hour in a nitrogen gas atmosphere to obtain a target nitrogen-doped electrode material. The obtained electrode material had a <002> plane spacing of 3.55 mm, Lc of 23 mm, La of 45 mm, and as a result of XPS surface analysis, the number of nitrogen atoms was 25% and the number of oxygen atoms was 8%.
（実施例２）
メラニンの替わりにポリベンズイミダゾール（佐藤ライト社製）を用いた以外は、実施例１と同様にした。ＸＰＳ表面分析の結果、窒素原子数は２３％、酸素原子数は８％であった。
(Example 2)
The same procedure as in Example 1 was performed except that polybenzimidazole (manufactured by Sato Light Co., Ltd.) was used instead of melanin. As a result of XPS surface analysis, the number of nitrogen atoms was 23% and the number of oxygen atoms was 8%.
（比較例１）
含窒素化合物の担持を行わないこと以外は実施例１と同様にした。
(Comparative Example 1)
The same procedure as in Example 1 was performed except that no nitrogen-containing compound was supported.
（試験例１）
実施例１〜２及び比較例１で得られた電極材料を、上下方向（通液方向）に１０ｃｍ、幅方向に１．６ｃｍの電極面積１６ｃｍ2 に切り出し、図１で示したようなセルを組み立てた。イオン交換膜はナフィオン２１２膜を用い、スペーサー厚みは２．５ｍｍとした。７０ｍＡ／ｃｍ2で１．４５Ｖまで充電を行い、ソーラートロン社製交流インピーダンス装置を用いて、導電抵抗、拡散抵抗、電荷移動反応抵抗をそれぞれ分離した。その結果を表１に示した。また、正極電解液には１．７ｍｏｌ／ｌのオキシ硫酸バナジウムの２．５ｍｏｌ／ｌ硫酸水溶液を用い、負極電解液には１．７ｍｏｌ／ｌの硫酸バナジウムの２．５ｍｏｌ／ｌ硫酸水溶液を用いた。電解液量はセル、配管に対して大過剰とした。液流量は毎分６．２mlとし、３０℃で測定を行った。
(Test Example 1)
The electrode materials obtained in Examples 1 and 2 and Comparative Example 1 were cut into an electrode area of 16 cm 2 of 10 cm in the vertical direction (liquid passing direction) and 1.6 cm in the width direction, and the cell as shown in FIG. Assembled. The ion exchange membrane was a Nafion 212 membrane and the spacer thickness was 2.5 mm. The battery was charged to 1.45 V at 70 mA / cm 2 , and the conductive resistance, diffusion resistance, and charge transfer reaction resistance were each separated using an AC impedance device manufactured by Solartron. The results are shown in Table 1. Also, a 2.5 mol / l sulfuric acid aqueous solution of 1.7 mol / l vanadium oxysulfate was used for the positive electrode electrolyte, and a 2.5 mol / l sulfuric acid aqueous solution of 1.7 mol / l vanadium sulfate was used for the negative electrode electrolyte. It was. The amount of the electrolytic solution was excessively large with respect to the cell and the piping. The liquid flow rate was 6.2 ml per minute, and the measurement was performed at 30 ° C.
表１から明らかなように、炭素材料電極の表面に窒素原子を含有する化合物を被覆または担時し、これを熱分解させて、前記炭素材料表面に窒素原子をドープし、これを電極活性点とした実施例１〜２については、非常に低い電荷移動反応抵抗を示し、結果として、低い全セル抵抗を示した。これは、ピリジン型の窒素原子が導入されたことで、従来の酸性官能基導入型よりも高活性化されたと考えられる。一方、比較例１については、導電抵抗と拡散抵抗は実施例１〜２と同等であるものの、電荷移動反応抵抗が大きいため全セル抵抗は大きい結果となった。 As is apparent from Table 1, the surface of the carbon material electrode is coated or supported with a compound containing nitrogen atoms, thermally decomposed, and doped with nitrogen atoms on the surface of the carbon material. Examples 1 and 2 indicated very low charge transfer reaction resistance and, as a result, low total cell resistance. This is probably because the introduction of a pyridine type nitrogen atom resulted in higher activation than the conventional acidic functional group introduction type. On the other hand, in Comparative Example 1, although the conductive resistance and the diffusion resistance were the same as those in Examples 1 and 2, the total cell resistance was large because the charge transfer reaction resistance was large.
本発明のレドックス電池用炭素電極材は、アンモニア処理により、導電性と活性能を兼ね備えたピリジン型の窒素原子を含むグラフェン構造を繊維上に導入する。これにより、初期充放電時のセル抵抗を低下させ、電池エネルギー効率を向上させることを可能とするものである。そして、本発明の炭素電極材はフロータイプおよびノンフロータイプのレッドクス電池、またはリチウム、キャパシタ、燃料電池のシステムと複合化されたようなレドックス電池に好適に用いられ、電池性能を向上させることが可能となり、産業界への寄与大である。 The carbon electrode material for a redox battery of the present invention introduces a graphene structure containing a pyridine-type nitrogen atom having both conductivity and activity into a fiber by ammonia treatment. Thereby, the cell resistance at the time of initial charge / discharge can be reduced, and the battery energy efficiency can be improved. The carbon electrode material of the present invention is suitably used for flow type and non-flow type Redox batteries, or redox batteries that are combined with lithium, capacitor, and fuel cell systems to improve battery performance. It becomes possible and contributes greatly to the industry.
１…集電板、２…スペーサ、３…イオン交換膜、４ａ，ｂ…通液路、５…電極
材、６…正極液タンク、７…負極液タンク、８，９…ポンプ、１０…液流入口、１１…液流出口
DESCRIPTION OF SYMBOLS 1 ... Current collecting plate, 2 ... Spacer, 3 ... Ion exchange membrane, 4a, b ... Liquid passage, 5 ... Electrode material, 6 ... Positive electrode liquid tank, 7 ... Negative electrode liquid tank, 8, 9 ... Pump, 10 ... Liquid Inlet, 11 ... Liquid outlet
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