JPH0158833B2 - - Google Patents
Info
- Publication number
- JPH0158833B2 JPH0158833B2 JP58141133A JP14113383A JPH0158833B2 JP H0158833 B2 JPH0158833 B2 JP H0158833B2 JP 58141133 A JP58141133 A JP 58141133A JP 14113383 A JP14113383 A JP 14113383A JP H0158833 B2 JPH0158833 B2 JP H0158833B2
- Authority
- JP
- Japan
- Prior art keywords
- electrolyte
- electrolyte matrix
- matrix
- powder
- cracking
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired
Links
- 239000003792 electrolyte Substances 0.000 claims description 46
- 239000011159 matrix material Substances 0.000 claims description 29
- 239000000843 powder Substances 0.000 claims description 12
- 239000000446 fuel Substances 0.000 claims description 9
- 239000000919 ceramic Substances 0.000 claims description 7
- BVKZGUZCCUSVTD-UHFFFAOYSA-L Carbonate Chemical compound [O-]C([O-])=O BVKZGUZCCUSVTD-UHFFFAOYSA-L 0.000 claims description 6
- 239000012783 reinforcing fiber Substances 0.000 claims description 4
- 238000005336 cracking Methods 0.000 description 7
- 239000000463 material Substances 0.000 description 7
- 229910000789 Aluminium-silicon alloy Inorganic materials 0.000 description 5
- 239000007789 gas Substances 0.000 description 5
- BWHMMNNQKKPAPP-UHFFFAOYSA-L potassium carbonate Chemical compound [K+].[K+].[O-]C([O-])=O BWHMMNNQKKPAPP-UHFFFAOYSA-L 0.000 description 5
- 239000000835 fiber Substances 0.000 description 4
- 230000035882 stress Effects 0.000 description 4
- 229910010093 LiAlO Inorganic materials 0.000 description 3
- WHXSMMKQMYFTQS-UHFFFAOYSA-N Lithium Chemical compound [Li] WHXSMMKQMYFTQS-UHFFFAOYSA-N 0.000 description 3
- XGZVUEUWXADBQD-UHFFFAOYSA-L lithium carbonate Chemical compound [Li+].[Li+].[O-]C([O-])=O XGZVUEUWXADBQD-UHFFFAOYSA-L 0.000 description 3
- NBIIXXVUZAFLBC-UHFFFAOYSA-N Phosphoric acid Chemical compound OP(O)(O)=O NBIIXXVUZAFLBC-UHFFFAOYSA-N 0.000 description 2
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 2
- 150000004649 carbonic acid derivatives Chemical class 0.000 description 2
- 238000003776 cleavage reaction Methods 0.000 description 2
- 238000001035 drying Methods 0.000 description 2
- 239000001307 helium Substances 0.000 description 2
- 229910052734 helium Inorganic materials 0.000 description 2
- SWQJXJOGLNCZEY-UHFFFAOYSA-N helium atom Chemical compound [He] SWQJXJOGLNCZEY-UHFFFAOYSA-N 0.000 description 2
- 229910000953 kanthal Inorganic materials 0.000 description 2
- 229910052744 lithium Inorganic materials 0.000 description 2
- YQNQTEBHHUSESQ-UHFFFAOYSA-N lithium aluminate Chemical compound [Li+].[O-][Al]=O YQNQTEBHHUSESQ-UHFFFAOYSA-N 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 239000010445 mica Substances 0.000 description 2
- 229910052618 mica group Inorganic materials 0.000 description 2
- 238000000465 moulding Methods 0.000 description 2
- 230000001590 oxidative effect Effects 0.000 description 2
- 230000000149 penetrating effect Effects 0.000 description 2
- 229910052628 phlogopite Inorganic materials 0.000 description 2
- 229910000027 potassium carbonate Inorganic materials 0.000 description 2
- 230000002787 reinforcement Effects 0.000 description 2
- 230000007017 scission Effects 0.000 description 2
- 230000008646 thermal stress Effects 0.000 description 2
- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 1
- YCKRFDGAMUMZLT-UHFFFAOYSA-N Fluorine atom Chemical compound [F] YCKRFDGAMUMZLT-UHFFFAOYSA-N 0.000 description 1
- 229910012672 LiTiO Inorganic materials 0.000 description 1
- 229910000990 Ni alloy Inorganic materials 0.000 description 1
- CDBYLPFSWZWCQE-UHFFFAOYSA-L Sodium Carbonate Chemical compound [Na+].[Na+].[O-]C([O-])=O CDBYLPFSWZWCQE-UHFFFAOYSA-L 0.000 description 1
- 229910000147 aluminium phosphate Inorganic materials 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 229910052626 biotite Inorganic materials 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 239000012141 concentrate Substances 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- YGANSGVIUGARFR-UHFFFAOYSA-N dipotassium dioxosilane oxo(oxoalumanyloxy)alumane oxygen(2-) Chemical compound [O--].[K+].[K+].O=[Si]=O.O=[Al]O[Al]=O YGANSGVIUGARFR-UHFFFAOYSA-N 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000003487 electrochemical reaction Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 229910052731 fluorine Inorganic materials 0.000 description 1
- 239000011737 fluorine Substances 0.000 description 1
- 239000002737 fuel gas Substances 0.000 description 1
- 238000007731 hot pressing Methods 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 125000004435 hydrogen atom Chemical class [H]* 0.000 description 1
- 229910052629 lepidolite Inorganic materials 0.000 description 1
- 229910052808 lithium carbonate Inorganic materials 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 229910052627 muscovite Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 230000035515 penetration Effects 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 239000012779 reinforcing material Substances 0.000 description 1
- 239000007784 solid electrolyte Substances 0.000 description 1
- 239000007790 solid phase Substances 0.000 description 1
- VEALVRVVWBQVSL-UHFFFAOYSA-N strontium titanate Chemical compound [Sr+2].[O-][Ti]([O-])=O VEALVRVVWBQVSL-UHFFFAOYSA-N 0.000 description 1
Classifications
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M8/00—Fuel cells; Manufacture thereof
- H01M8/02—Details
- H01M8/0289—Means for holding the electrolyte
- H01M8/0295—Matrices for immobilising electrolyte melts
-
- 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
Landscapes
- Life Sciences & Earth Sciences (AREA)
- Engineering & Computer Science (AREA)
- Manufacturing & Machinery (AREA)
- Sustainable Development (AREA)
- Sustainable Energy (AREA)
- Chemical & Material Sciences (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Electrochemistry (AREA)
- General Chemical & Material Sciences (AREA)
- Fuel Cell (AREA)
Description
【発明の詳細な説明】
〔発明の技術分野〕
本発明は、溶融炭酸塩を電解質として用いる燃
料電池の電解質マトリツクスに係り、特に熱サイ
クルに対する強度性を向上させた電解質マトリツ
クスに関する。DETAILED DESCRIPTION OF THE INVENTION [Technical Field of the Invention] The present invention relates to an electrolyte matrix for a fuel cell using molten carbonate as an electrolyte, and particularly to an electrolyte matrix with improved strength against thermal cycles.
従来、水素のように酸化され易いガスと、酸素
のように酸化力のあるガスとを電気化学反応プロ
セスを経て反応させることにより直流電力を得る
ようにした燃料電池が広く知られている。この燃
料電池は、使用する電解質によつてリン酸型、溶
融炭酸塩型、固体電解質型等に大別される。
2. Description of the Related Art Conventionally, fuel cells that obtain DC power by reacting a gas that is easily oxidized, such as hydrogen, and a gas that has oxidizing power, such as oxygen, through an electrochemical reaction process have been widely known. Fuel cells are broadly classified into phosphoric acid type, molten carbonate type, solid electrolyte type, etc. depending on the electrolyte used.
ところで、上記のような燃料電池のうち、溶融
炭酸塩型の燃料電池は、650℃近辺の温度で動作
させるようにしたもので、その主要部は通常、炭
酸リチウム、炭酸カリウム等の炭酸塩の電解質
と、リチウムアルミネート等のセラミツクス系保
持材とを平板状に一体化してなる電解質マトリツ
クスの両面にニツケル合金等のガス拡散極を当て
がつて単位電池を構成し、この単位電池を複数
個、相互間に双極性隔離板を介在させて積層した
積層体に構成されている。 By the way, among the above-mentioned fuel cells, molten carbonate fuel cells are designed to operate at temperatures around 650°C, and their main parts are usually made of carbonates such as lithium carbonate and potassium carbonate. A unit battery is constructed by applying gas diffusion electrodes such as nickel alloy to both sides of an electrolyte matrix formed by integrating an electrolyte and a ceramic holding material such as lithium aluminate into a flat plate, and a plurality of these unit batteries are It is constructed as a laminated body with bipolar separators interposed between them.
しかしながら、上記のように構成された従来の
電解質マトリツクスにあつては、電解質保持材と
溶融温度以下の固相状態の電解質との熱膨張率差
および電解質マトリツクスと電極、セルハウジン
グとの熱膨張率差によつて、降温時に電解質マト
リツクスに貫通割れの発生することが往々にして
あつた。そこで、このような不具合を解消するた
めに、カンタル線やアルミナ（Al2O3）繊維等を
補強用繊維として、混入し、これらによつて貫通
割れに至るまでの強度を向上させることが考えら
れている。しかし、一度微小な割れが発生する
と、この割れに応力が集中して大きな割れに発展
することに変わりはなかつた。また、補強用繊維
として用いられるカンタル線やアルミナ繊維は電
解質と化学反応を起こすため、長期にわたつて補
強の役割を果さない問題もあつた。 However, in the conventional electrolyte matrix configured as described above, there is a difference in thermal expansion coefficient between the electrolyte holding material and the electrolyte in a solid phase below the melting temperature, and a difference in thermal expansion coefficient between the electrolyte matrix, the electrodes, and the cell housing. Due to the difference, penetration cracks often occurred in the electrolyte matrix when the temperature was lowered. Therefore, in order to eliminate such problems, it is considered that reinforcing fibers such as Kanthal wire and alumina (Al 2 O 3 ) fibers are mixed in to improve the strength up to the point of penetrating cracking. It is being However, once a small crack occurs, stress concentrates on this crack and it develops into a large crack. Additionally, the Kanthal wire and alumina fibers used as reinforcing fibers cause a chemical reaction with the electrolyte, so there was a problem that they did not function as reinforcement over a long period of time.
〔発明の目的〕
本発明は、このような事情に鑑みてなされたも
ので、その目的とするところは溶融炭酸塩を電解
質として用いる燃料電池に組込まれる電解質マト
リツクスにおいて、耐熱サイクル性に勝れた電解
質マトリツクスを提供することにある。[Object of the Invention] The present invention was made in view of the above circumstances, and its purpose is to provide an electrolyte matrix that has excellent heat cycle resistance and is incorporated into a fuel cell that uses molten carbonate as an electrolyte. The purpose is to provide an electrolyte matrix.
本発明に係る電解質マトリツクスは、へき開性
を有するセラミツクス粉末が混入されてなること
を特徴としている。
The electrolyte matrix according to the present invention is characterized in that it contains a ceramic powder having cleavability.
上述したへき開性を有するセラミツクス粉末の
へき開強度は、電解質保持材と電解質との結合強
度よりも小さい。したがつて、電解質保持材と電
解質との間の熱膨張率差および電解質マトリツク
スと電極・セルホルダーとの間の熱膨張率差によ
つて、降温時に電解質マトリツクスに熱応力が発
生すると、上述したへき開性を有するセラミツク
粉末がへき開することにより熱応力を吸収し、電
解質マトリツクス全体の割れ、すなわち、貫通割
れの発生を防止する。このようなへき開面に発生
する割れは、１個当りの割れとしては小さいた
め、次の昇温時に溶融炭酸塩によつてふさがれ、
ほとんど問題とはならず、結局電解質マトリツク
スの耐熱サイクル性を向上させることができる。
また、炭酸塩に対して化学的に安定な繊維を補強
用として混入すると、貫通割れに至る強度をさら
に向上させることができる。
The cleavage strength of the ceramic powder having the above-mentioned cleavability is smaller than the bond strength between the electrolyte holding material and the electrolyte. Therefore, as mentioned above, thermal stress is generated in the electrolyte matrix when the temperature is lowered due to the difference in coefficient of thermal expansion between the electrolyte holding material and the electrolyte and the difference in coefficient of thermal expansion between the electrolyte matrix and the electrode/cell holder. By cleaving the cleavable ceramic powder, it absorbs thermal stress and prevents cracking of the entire electrolyte matrix, that is, the occurrence of through cracking. Since each crack that occurs on the cleavage plane is small, it is sealed by molten carbonate during the next temperature rise.
This poses almost no problem, and the heat cycle resistance of the electrolyte matrix can be improved after all.
Furthermore, if fibers that are chemically stable against carbonates are mixed in for reinforcement, the strength leading to through cracking can be further improved.
以下、本発明の実施例を説明する。 Examples of the present invention will be described below.
実施例 １
へき開性を有するセラミツクスとしての弗素金
雲母〔KMg3（AlSi3O10）F2、80meshパス〕粉末
と、電解質保持材としてのγ−リチウムアルミネ
ート（γ−LiAlO2）粉末と、電解質としての炭
酸リチウム（Li2CO3）粉末、炭酸カリウム
（K2CO3）粉末とを体積比が10.0：26.6：31.8：
31.6となるよう湿式混合して、乾燥したのち、
440℃、300Kg／cm2、15分の条件で加熱加圧成形し
て直径60m、厚さ3.1mmの電解質マトリツクスを
得た。Example 1 Fluorophlogopite [KMg 3 (AlSi 3 O 10 ) F 2 , 80mesh pass] powder as a ceramic having cleavability, γ-lithium aluminate (γ-LiAlO 2 ) powder as an electrolyte holding material, The volume ratio of lithium carbonate (Li 2 CO 3 ) powder and potassium carbonate (K 2 CO 3 ) powder as electrolyte was 10.0:26.6:31.8:
After wet mixing to obtain 31.6 and drying,
An electrolyte matrix having a diameter of 60 m and a thickness of 3.1 mm was obtained by heat-pressing molding at 440° C., 300 kg/cm 2 for 15 minutes.
実施例 ２
へき開性を有するセラミツクスとしての弗素金
雲母粉末と、電解質保持材としてのγ−リチウム
アルミネート粉末と、電解質としての炭酸リチウ
ム粉末、炭酸カリウム粉末と、補強材としてのリ
チウムジルコネート繊維とを体積比が10.0：
21.6：31.8：31.6：5.0となるよう湿式混合して、
乾燥したのち、440℃、300Kg／cm2、15分の条件
で、ホツトプレスして、直径60m、厚さ3.4mmの
電解質マトリツクスを得た。Example 2 Fluorine phlogopite powder as ceramics with cleavability, γ-lithium aluminate powder as electrolyte holding material, lithium carbonate powder and potassium carbonate powder as electrolyte, and lithium zirconate fiber as reinforcing material. The volume ratio is 10.0:
Wet mix so that the ratio is 21.6:31.8:31.6:5.0,
After drying, it was hot pressed at 440° C., 300 kg/cm 2 for 15 minutes to obtain an electrolyte matrix with a diameter of 60 m and a thickness of 3.4 mm.
このようにして得られた実施例１、２の電解質
マトリツクスおよび従来の電解質マトリツクスに
ついて、歪み率と応力との関係を測定したところ
図に示す結果を得た。なお、図中×印点が貫通割
れの生じた値を示している。この図から、従来例
に比べ、実施例１の電解質マトリツクスでは歪み
率で約0.4％大きい変形に耐えられることが確認
された。また実施例２の電解質マトリツクスで
は、貫通割れに至る強度の向上も確認された。 When the relationship between strain rate and stress was measured for the electrolyte matrices of Examples 1 and 2 and the conventional electrolyte matrix thus obtained, the results shown in the figure were obtained. Note that the x marks in the figure indicate the values at which through cracking occurred. From this figure, it was confirmed that the electrolyte matrix of Example 1 could withstand deformation that was approximately 0.4% larger in strain rate than the conventional example. Furthermore, in the electrolyte matrix of Example 2, an improvement in strength leading to through cracking was also confirmed.
一方、耐熱サイクル性を確認するため、実施例
１の電解質マトリツクスと従来例の電解質マトリ
ツクスとを用いて、単セルを形成し、室温から
650℃に昇温後、室温に降温する熱サイクルを加
えたところ、従来例の電解質マトリツクスを使用
したセルでは３回の熱サイクル後、燃料ガスに５
体積％含有したヘリウムが酸化剤ガスの出口ガス
中に、0.5体積％含有されているのが検出され、
電解質マトリツクスに貫通割れの生していること
が、確認された。しかし実施例１の電解質マトリ
ツクスを使用したセルについては、６回の熱サイ
クル後も、ヘリウムは0.02体積％以下で、貫通割
れの発生していないことが確認され本発明の有用
性が立証された。 On the other hand, in order to confirm heat cycle resistance, a single cell was formed using the electrolyte matrix of Example 1 and the electrolyte matrix of the conventional example, and
When a thermal cycle was applied in which the temperature was raised to 650°C and then lowered to room temperature, in the cell using the conventional electrolyte matrix, after three thermal cycles, the fuel gas
0.5% by volume of helium contained in the oxidizing gas outlet gas was detected,
It was confirmed that there were penetrating cracks in the electrolyte matrix. However, in the cell using the electrolyte matrix of Example 1, even after six thermal cycles, it was confirmed that the helium content was 0.02% by volume or less, and no through cracking occurred, proving the usefulness of the present invention. .
なお、上述した実施例では、へき開性を有する
セラミツクス粉末として、弗素金雲母〔KMg
（AlSi3O10）F2〕を用いているが、白雲母〔KAl2
（AlSi3O10）（OH）2〕、ソーダ雲母〔NaAl2
（AlSi3O10）（OH）2〕、金雲母〔KMg3（AlSi3O10）
（OH）2〕、黒雲母〔KMg3K（Mg、Fo）3（AlS3O10）
（OH）2〕、鱗雲母〔KLi2Al（Si4O10）（OH）2〕、弗
素四ケイ素雲母〔KMg25（Si4O10）F2〕、テニオ
ライト〔KMg2Li（Si4O10）F2〕等を用いてもよ
い。また、補強繊維としては、リチウムジルコネ
ートのかわりに、リチウムアルミネート
（LiAlO2）、チタン酸ストロンチウム（SrTiO3）、
BN、Si3N4、SiC、LiTiO3、等を用いてもよい。
さらに電解質保持材はLiAlO2粉末に限らないし、
成形法もホツトプレスに限られるものではない。 In the above-mentioned examples, fluorophlogopite [KMg
(AlSi 3 O 10 )F 2 ], but muscovite [KAl 2
(AlSi 3 O 10 ) (OH) 2 ], soda mica [NaAl 2
(AlSi 3 O 10 ) (OH) 2 ], Phlogopite [KMg 3 (AlSi 3 O 10 )
(OH) 2 ], biotite [KMg 3 K (Mg, Fo) 3 (AlS 3 O 10 )
(OH) 2 ], lepidolite [KLi 2 Al (Si 4 O 10 ) (OH) 2 ], fluorotetrasilicon mica [KMg 25 (Si 4 O 10 )F 2 ], teniolite [KMg 2 Li (Si 4 O 10 ) F 2 ] etc. may also be used. In addition, as reinforcing fibers, instead of lithium zirconate, lithium aluminate (LiAlO 2 ), strontium titanate (SrTiO 3 ),
BN, Si 3 N 4 , SiC, LiTiO 3 , etc. may also be used.
Furthermore, the electrolyte holding material is not limited to LiAlO 2 powder,
The molding method is not limited to hot pressing either.
図は本発明に係る電解質マトリツクスの応力・
歪み率特性と、従来の電解質マトリツクスのそれ
とを比較して示す図である。
The figure shows the stress and stress of the electrolyte matrix according to the present invention.
FIG. 3 is a diagram showing a comparison of strain rate characteristics and that of a conventional electrolyte matrix.
Claims (1)
電解質マトリツクスにおいて、へき開性を有する
セラミツクス粉末が混入されてなることを特徴と
する燃料電池用電解質マトリツクス。 ２ 前記マトリツクスには、補強用繊維も混入さ
れてなることを特徴とする特許請求の範囲第１項
記載の燃料電池用電解質マトリツクス。[Scope of Claims] 1. An electrolyte matrix for a fuel cell, characterized in that a ceramic powder having cleavability is mixed in the electrolyte matrix for a fuel cell using molten carbonate as an electrolyte. 2. The electrolyte matrix for a fuel cell according to claim 1, wherein reinforcing fibers are also mixed in the matrix.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP58141133A JPS6035468A (en) | 1983-08-03 | 1983-08-03 | Electrolyte matrix for fuel cell |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP58141133A JPS6035468A (en) | 1983-08-03 | 1983-08-03 | Electrolyte matrix for fuel cell |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS6035468A JPS6035468A (en) | 1985-02-23 |
| JPH0158833B2 true JPH0158833B2 (en) | 1989-12-13 |
Family
ID=15284931
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP58141133A Granted JPS6035468A (en) | 1983-08-03 | 1983-08-03 | Electrolyte matrix for fuel cell |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6035468A (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2585226B2 (en) * | 1986-07-07 | 1997-02-26 | 株式会社東芝 | Electrolyte matrix for molten carbonate fuel cells |
| JP2615935B2 (en) * | 1988-11-04 | 1997-06-04 | 石川島播磨重工業株式会社 | Electrolyte plate for molten carbonate fuel cell |
-
1983
- 1983-08-03 JP JP58141133A patent/JPS6035468A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPS6035468A (en) | 1985-02-23 |
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