TWI686990B - Bipolar plate for fuel cell and method of the same - Google Patents
Bipolar plate for fuel cell and method of the same Download PDFInfo
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- TWI686990B TWI686990B TW107147567A TW107147567A TWI686990B TW I686990 B TWI686990 B TW I686990B TW 107147567 A TW107147567 A TW 107147567A TW 107147567 A TW107147567 A TW 107147567A TW I686990 B TWI686990 B TW I686990B
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Abstract
Description
本發明是有關於一種燃料電池及其製作方法,且特別是有關於一種燃料電池之雙極板及其製作方法。The invention relates to a fuel cell and a manufacturing method thereof, and in particular to a fuel cell bipolar plate and a manufacturing method thereof.
燃料電池的能量轉化效率高,具有清潔、低污染、能量密度高、啟動快、連續供電時間長等優點,因而被認為是未來可兼具能源與環境要求之理想發電裝置與能源自主的戰略選項。燃料電池可藉由使用超薄金屬板材來製作雙極板,以提高雙極板的流道密度,藉以提高電池的能量密度。然而,超薄金屬雙極板在沖壓超薄板材流道的過程中,在與模具接觸處易發生高變形,使其表面變得粗糙,而容易產生局部的腐蝕與斷裂。Fuel cells have high energy conversion efficiency, clean, low pollution, high energy density, fast start-up, and long continuous power supply time. Therefore, they are considered to be an ideal power generation device and energy independent strategic option that can meet both energy and environmental requirements in the future. . The fuel cell can be made of ultra-thin metal sheet to make the bipolar plate to increase the flow channel density of the bipolar plate, thereby increasing the energy density of the battery. However, in the process of stamping the ultra-thin sheet metal flow path, the ultra-thin metal bipolar plate is prone to high deformation at the contact with the mold, making its surface rough, and it is easy to produce local corrosion and fracture.
本發明實施例提供一種燃料電池之雙極板及其製作方法,可以提升燃料電池之雙極板抗腐蝕及壽命。The embodiments of the present invention provide a bipolar plate for a fuel cell and a manufacturing method thereof, which can improve the corrosion resistance and life span of the bipolar plate for a fuel cell.
本發明實施例提出一種燃料電池之雙極板,包括基材與抗蝕層。基材具有多個流道。抗蝕層,覆蓋於所述基材上。基材的表面粗糙度小於或等於1.2μm。An embodiment of the present invention provides a bipolar plate for a fuel cell, which includes a base material and a resist layer. The substrate has multiple flow channels. The resist layer covers the substrate. The surface roughness of the substrate is less than or equal to 1.2 μm.
本發明實施例又提出一種燃料電池之雙極板的製造方法,包括提供板材,並對所述板材進行壓延製程。對所述板材進行熱處理製程。藉由沖壓模具對所述板材進行沖壓製程,以形成基材,所述基材具有多個流道。進行脫模製程。An embodiment of the present invention further provides a method for manufacturing a bipolar plate of a fuel cell, which includes providing a plate and performing a rolling process on the plate. A heat treatment process is performed on the board. The stamping process is performed on the plate by a stamping die to form a substrate, and the substrate has a plurality of flow channels. Carry out the demoulding process.
基於上述,本發明實施例之燃料電池之雙極板及其製作方法,可以提升燃料電池之雙極板抗腐蝕及壽命。Based on the above, the fuel cell bipolar plate of the embodiment of the present invention and the manufacturing method thereof can improve the corrosion resistance and service life of the fuel cell bipolar plate.
為讓本發明的上述特徵和優點能更明顯易懂,下文特舉實施例,並配合所附圖式作詳細說明如下。In order to make the above-mentioned features and advantages of the present invention more obvious and understandable, the embodiments are specifically described below in conjunction with the accompanying drawings for detailed description as follows.
超薄金屬雙極板可用來提高燃料電池雙極板的流道密度,提高電池的能量密度,但超薄金屬板材流道密度提升則引發鍍膜的披覆均勻性受嚴峻挑戰,尤其是超薄金屬板材壓延成型後原始晶粒粗大,當高密度流道沖壓成型後可見明顯的晶粒,使流道表面粗糙,此時鍍膜的均勻性變差,雙極板的抗蝕性降低,影響使用壽命。本發明提供一種超薄金屬雙極板,其具有良好的鍍膜均勻性,可改善抗蝕性與壽命。The ultra-thin metal bipolar plate can be used to increase the flow channel density of the fuel cell bipolar plate and increase the energy density of the battery, but the increase in the ultra-thin metal plate flow channel density causes severe challenges to the uniformity of the coating, especially the ultra-thin The original grains of the metal sheet are thick after calendering. When the high-density runner is stamped and formed, obvious grains can be seen, which makes the surface of the runner rough. At this time, the uniformity of the coating becomes poor, and the corrosion resistance of the bipolar plate is reduced, which affects the use. life. The invention provides an ultra-thin metal bipolar plate, which has good coating uniformity, and can improve corrosion resistance and service life.
圖1A至圖1F是本發明實施例之燃料電池的雙極板的製造方法的流程剖面圖。1A to 1F are flow cross-sectional views of a method for manufacturing a bipolar plate of a fuel cell according to an embodiment of the invention.
請參照圖1A,提供板材10。板材10例如為平板狀的導電材料。導電材料包括金屬、金屬的衍生物、介金屬或其組合。金屬例如是不鏽鋼、鈦合金、鎳合金、鋁合金或其組合。不鏽鋼可以是430不鏽鋼、304不鏽鋼、316不鏽鋼或其組合;鈦合金包含:純鈦、鈦鋁釩合金(Ti
6Al
4V)、鈦鈀合金或相關合金;鎳合金包含:純鎳、鎳鉻合金、鎳鉬合金或相關合金;鋁合金包含:純鋁、鋁鎂矽合金、鋁銅鎂合金或相關合金。衍生物可以包括碳化物、氮化物、氮氧化物或氰化物。在板材10為導電材料的衍生物的實施例中,板材10例如是鈦或鋁之碳化物、氮化物、氮氧化物或氰化物。在板材10為導電材料的介金屬的實施例中,板材10例如是鈦鎳之介金屬或鈦鋁之介金屬。板材10的厚度範圍例如是100微米(mm)至1000微米。板材10之晶粒之粒徑例如是0.5mm至200mm。板材10的晶粒平均粒徑範圍例如是1mm至100mm。板材10的厚度例如是50mm至500mm。
Referring to FIG. 1A, a
請參照圖1B,對板材10進行壓延製程13,使板材10經過壓延而薄化,並且使得板材10產生動態再結晶,以使晶粒細化,而形成板材10a。壓延製程13可以藉由壓延機來加工。壓延機可以是雙輥壓延機、3輥軋成型機或滾壓成型機。在一些實施例中,進行壓延製程的壓力範圍為100MPa至3000MPa。在一些實施例中,進行壓延製程的壓力範圍為100MPa至1500MPa。在另一些實施例中,進行壓延製程的壓力範圍為200MPa至1000MPa。在又一些實施例中,進行壓延製程的壓力維持在一定值,例如是300MPa、600MPa或800MPa。進行壓延製程的溫度範圍例如是攝氏20度至攝氏900度。Referring to FIG. 1B, a
壓延後之板材10a的厚度可以是壓延前板材10的厚度的1/20至1/2。壓延後之板材10a的厚度可以是小於或等於200mm。在一些實施例中,板材10a的厚度為20mm至300mm。板材10a的晶粒之粒徑範圍例如5mm至100mm、1mm至50mm或1mm至20mm。板材10a的晶粒平均粒徑範圍例如是5mm至50mm、1mm至20mm或0.5mm至10mm。The thickness of the
在一些實施例中,板材10中還添加微量的析出物。析出物係添加於晶界中,以避免在進行壓延製程中產生再結晶,而造成區域晶粒過度成長的現象,從而限制晶粒的尺寸。析出物例如是金屬碳化物、合金或金屬硼化物。金屬碳化物例如是M(Fe、Cr、Mo..)
23C
6、Fe
3C、Cr
3C或Mo
3C。合金例如是Ti
2Pd或Ti
3Al。金屬硼化物例如是Ti
3B、Zr
3B等。
In some embodiments, a small amount of precipitate is added to the
請參照圖1C,在進行壓延製程之後,對壓延製程後的板材10a進行熱處理(熱處理製程)14,以改變板材10a的微結構。熱處理14可以是回火處理或退火熱處理。更具體地說,熱處理14可使板材10a的晶粒再生與重整,使壓延後的應變能轉換為再生晶粒的動能,以使晶粒細化,從而使得熱處理後的板材10b的晶粒之粒徑控制在一定的範圍內。熱處理14例如是在真空的環境下進行。熱處理14的真空度例如是小於1´10
-2torr。在一些實施中,熱處理14的真空度例如是 1´10
-5torr至1´10
-2torr。熱處理14的溫度例如是小於攝氏600度之低溫回火。在一些實施中,熱處理14的溫度範圍例如是攝氏300度至550度。在又一些實施中,熱處理的溫度範圍例如是攝氏300度至400度。熱處理14的時間範圍例如是1小時至6小時。熱處理14的方式可以採用連續爐或熱處理爐等。
Referring to FIG. 1C, after the rolling process is performed, a heat treatment (heat treatment process) 14 is performed on the
在一些實施例中,經熱處理後的板材10b的晶粒之粒徑約為壓延前的板材10的晶粒之粒徑的1/50至1/2。此外,熱處理後的板材10b的晶粒之粒徑約為處理前(壓延後)的板材10a的晶粒之粒徑的1/30至1/2。熱處理後的板材10b的晶粒之粒徑範圍例如是1mm至7mm、1mm至5mm或0.1mm至3mm。板材10b的晶粒平均粒徑範圍例如是1mm至6mm、2mm至4mm或0.1mm至1mm。In some embodiments, the grain size of the
請參照圖1D與圖2,在進行熱處理之後,對板材10b進行沖壓製程。沖壓製程可以藉由使用沖壓模具來實施。沖壓模具包括上模具(未繪示)與下模具12。上模具的形狀與下模具大至相對應。下模具12包括主體部12B與多個凸部12P。凸部12P凸出於主體部12B。凸部12P是間隔設置於主體部12B上,因此與主體部12B形成凹凸的表面12T。凸部12P的側壁12S與主體部12B表面連接。Referring to FIGS. 1D and 2, after the heat treatment, a stamping process is performed on the
請參照圖1D與圖2,凸部12P的頂面12Pt可以是單一個或是多個的平面、曲面或其組合。凸部12P的頂角a’可以是一個倒角,倒角為鈍角或是圓化的鈍角。在凸部12P的頂角a’是圓化的鈍角的實施例中,凸部12P的頂面12Pt包括位於兩個頂角a’之間的平面Ft’。平面Ft’的寬度例如是0.2mm至3mm。頂角a’為圓化的鈍角,其曲率半徑範圍可以是0.01mm至0.5mm,例如是0.1mm、0.2mm或0.25mm。Please refer to FIGS. 1D and 2, the top surface 12Pt of the
在剖視圖中,凸部12P的側壁12S呈傾斜的直線、弧線或拋物線。換言之,凸部12P的側壁12S可以是傾斜面、曲面或是拋物面。凸部12P的高度H’,即凸部12P的頂面12Pt與主體12B的表面12Bb之間的距離範圍可以是0.2mm至3mm、0.2mm至2mm或0.2mm至0.8mm,例如是0.35mm、0.45mm或0.55mm。在一些實施例中,凸部12P的高度H’又稱為凸部12P的側壁12S的高度。In the cross-sectional view, the
兩個相鄰的凸部12P之間的主體部12B,可以稱為凹部12B。凹部12B的底面(表面)12Bb可以是單一個或是多個的平面、曲面或其組合。凹部12B的底角b’可以是倒角,倒角為鈍角或是圓化的鈍角。凹部12B的底角b’的角度範圍例如是90度至150度。在凹部12B的底角b’是圓化的鈍角的實施例中,凹部12B的底面12Bb包括位於兩個底角b’之間的平面Fb’。平面Fb’的寬度範圍可以是0.2mm至3mm,例如是0.5mm、1mm或2mm。底角b’是圓化的鈍角,其曲率半徑範圍可以是0.01mm至0.5mm,例如是0.1mm、0.2mm或0.25mm。底角b’與頂角a’的曲率半徑可以相同或是相異。The
下模具12的凸部12P的底角g’,亦即凸部12P的側壁12S與主體部12B表面的延伸線所夾的角度,可稱之為拔模角g’,或稱為脫模角(draft angle)g’。在本發明的一些實施例中,拔模角g’範圍例如是大於或等於30度,或是大於或等於40度。在一些示例中,拔模角g’例如是40度90至度之間。在又一些示例中,拔模角g’可以在40度至80度之間。拔模角g’例如是70度、60度、45度。The bottom angle g'of the
此外,相鄰兩個凸部12P的間距P’可以小於或等於3mm。在一些實施例中,相鄰兩個凸部12P的間距P’例如是1mm至2.4mm。在另一些實施例中,相鄰兩個凸部12P的間距P’例如是1.2mm至2mm。In addition, the pitch P'of two adjacent
在一些實施力中,沖壓模具係安裝在沖壓機上。在進行沖壓時,沖壓機對板材10施加壓力,使板材10產生塑性變形。沖壓機可以是機械壓力機或是液壓壓力機。施加於板材10的壓力例如是100MPa至1000MPa。進行沖壓製程可以在室溫或更高的溫度下進行。更具體地說,進行沖壓製程的溫度例如是攝氏20度至攝氏300度。In some implementations, the stamping die is installed on the stamping machine. When punching, the punching machine applies pressure to the
由於板材10b的晶粒經過細化且尺寸均勻,因此,板材10b的高曲率之處,例如是拔模處也不易在沖壓過程中斷裂,因此可以產生塑性變形,從形成具有流道圖案且厚度均勻的基材11。Since the grains of the
基材11的厚度可以例如是小於或等於200mm。在一些實施例中,基材11的厚度範圍是40mm至200mm。在另一些實施例中,基材11的厚度範圍是150mm至200mm。在又一些實施例中,基材11的厚度範圍是50mm至100mm。基材11的晶粒粒徑範圍例如是0.3mm至15mm、1mm至6mm或0.1mm至8mm。基材11的晶粒平均粒徑範圍例如是0.3mm至5mm。基材11的表面粗糙度Ra例如是1.2mm以下。在一些實施例中,基材11的表面粗糙度Ra的範圍例如是0.156mm至1.171mm、0.242mm至0.739mm或0.1mm至1.2mm。The thickness of the
接著,請參照圖1E,在進行沖壓製程之後,在一些實施例中,還在基材11的表面上形成抗蝕層20。抗蝕層20的導電度例如為1´10
3S/cm至1´10
5S/cm。抗蝕層20的材料例如是碳、金屬碳化合物、金屬氮化物或金屬的碳氮混合物。抗蝕層20可以利用乾式鍍膜或是濕式鍍膜的方式來形成。舉例來說,乾式鍍膜可以是物理氣相沉積法,例如是蒸鍍或是濺鍍,或是利用化學氣相沉積法,例如是電漿增強型化學氣相沉積法。濕式鍍膜的方式可以是電化學法,例如化學電鍍法、無電電鍍法、熔鹽法等。
Next, referring to FIG. 1E, after performing the stamping process, in some embodiments, a resist
在一些實施例中,抗蝕層20的厚度範圍例如是0.1mm至5mm。由於基材11的晶粒和表面粗糙度皆很小,因此,抗蝕層20的階梯披覆性高,可以有效將基材11的表面覆蓋住。因此,抗蝕層20並不需要太厚即可將基材11覆蓋住。在一些實施例中,抗蝕層20的厚度例如是小於或等於3mm。抗蝕層20的厚度範圍例如是3mm至0.2mm。在一些實施例中,抗蝕層20的厚度小於0.5mm。In some embodiments, the thickness of the resist
進行退模製程,將覆蓋著抗蝕層20的基材11從沖壓模具中取出,以形成具流道的雙極板30。In the mold release process, the
在本發明的實施例中,採用具有較大拔模角q的沖壓模進行沖壓,因此在退模之後可以使得所形成之雙極板30的流道16之間具有較小的間距。In the embodiment of the present invention, a stamping die with a larger draft angle q is used for stamping, so that after the die is removed, the
請參照圖3,更具體地說,雙極板30的基材11具有凸部11P與凹部11R。凹部11R與凸部11P共用側壁11S。也就是側壁11S連接凹部11R的底面11Rb與凸部11P的頂面11Pt。Please refer to FIG. 3. More specifically, the
凸部11P的頂面11Pt可以是單一個或是多個的平面、曲面或其組合。凸部11P的頂角a可以是一個倒角,倒角為鈍角或是圓化的鈍角。在凸部11P的頂角a是圓化的鈍角的實施例中,凸部11P的頂面11Pt包括位於兩個頂a角之間的平面Ft。平面Ft的寬度例如是0.2mm至3mm。頂角a為圓化的鈍角,其曲率半徑範圍可以是0.01mm至0.5mm,例如是0.1mm、0.2mm或0.25mm。The top surface 11Pt of the
側壁11S可以是一個平滑的表面。更具體地說,側壁11S可以是單一個或是多個的斜面、曲面或其組合。側壁11S的高度H,亦即凹部11R的底面11Rb與凸部11P的頂面11Pt之間的垂直距離,其可以是0.2mm至3mm,例如是0.35mm、0.45mm或0.55mm。The
凹部11R,此處又可以稱之為雙極板的流道。凹部11R的底面11Rb可以是單一個或是多個的平面、曲面或其組合。凹部11R的底角b可以是倒角,倒角為鈍角或是圓化的鈍角。凹部11R的底角b的角度範圍例如是90度至150度。在凹部11R的底角b是圓化的鈍角的實施例中,凹部11R的底面11Rb包括位於兩個底角b之間的平面Fb。平面Fb的寬度範圍可以是0.2mm至3mm,例如是0.5mm、1mm或2mm。底角b是圓化的鈍角,其曲率半徑範圍可以是0.01mm至0.5mm,例如是0.1mm、0.2mm或0.25mm。底角b與頂角a的曲率半徑可以相同或是相異。The
此外,凹部(流道)11R底面11Rb水平延伸線與側壁11S的夾角又稱為拔模角g。在一些實施例中拔模角g範圍例如是大於或等於30度,或是大於或等於40度。在一些示例中,拔模角g例如是40度至90度之間。在又一些示例中,拔模角g例如是40度至80度之間。拔模角g例如是70度、60度、45度。In addition, the angle between the horizontal extension line of the bottom surface 11Rb of the concave portion (flow channel) 11R and the
此外,相鄰兩個凸部11P的間距P可以小於或等於3mm。在一些實施例中,相鄰兩個凸部11P的間距P例如是1mm至2.4mm。在另一些實施例中,相鄰兩個凸部11P的間距P例如是1.2mm至2mm。當雙極板30應用於燃料電池時,流道16之間的間距縮小有助於提高電池的電流密度。In addition, the pitch P of two adjacent
圖4A是依照本發明的實施例的一種燃料電池單元的剖面示意圖。請參照圖4A,燃料電池100包括膜電極組(membrane electrode assembly,MEA)102以及一對雙極板組130a與130b。膜電極組102包括質子交換膜(proton exchange membrane,PEM)104以及氣體擴散層106a與106b。質子交換膜104可以是全氟磺酸離子膜(Nafion)。氣體擴散層106a與106b分別設置於質子交換膜104的兩側。氣體擴散層106a與106b可以是石墨纖維、鈦金屬纖維或貴金屬(例如是Ag、Au、Pt)纖維。雙極板組130a與130b分別設置於氣體擴散層106a與106b的外側。4A is a schematic cross-sectional view of a fuel cell unit according to an embodiment of the present invention. Referring to FIG. 4A, the
雙極板組130a包括雙極板131a以及132a。雙極板131a以及132a可以採用上述實施例之雙極板30。雙極板131a位於氣體擴散層106a與雙極板132a之間。雙極板131a以及132a具有第一冷卻流道116a以及第一氣體流道118a。第一冷卻流道116a以及第一氣體流道118a是相互交錯配置。具體來說,雙極板131a的凸部131P
1與雙極板132a的凹部132R
1相對應設置,且雙極板131a的凸部131P
1與氣體擴散層106a之間做為第一氣體流道118a。雙極板131a的凹部131R
1與雙極板132a的凸部132P
1相對應設置,且其所形成的容置空間做為第一冷卻流道116a。
The
同樣地,雙極板組130b包括雙極板131b以及132b。雙極板131b位於氣體擴散層106b與雙極板132b之間。雙極板131b以及132b具有第二冷卻流道116b以及第二氣體流道118b。第二冷卻流道116b與第二氣體流道118b例如是相互交錯配置。具體來說,雙極板131b的凹部131R
2與雙極板132b的凸部132P
2相對應設置,且雙極板131b的凹部131R
2與氣體擴散層106b之間做為第二氣體流道118b。雙極板131b的凸部131P
2與雙極板132b的凹部132R
2相對應設置,且其所形成的容置空間做為第二冷卻流道116b。
Similarly, the
請參照圖5A與圖5B,在一些實施例中,雙極板組(圖中僅繪出雙極板131a)之流道Ca的延伸方向可以與雙極板組(圖中僅繪出雙極板131b)之流道Cb的延伸方向相同,如圖5A所示。在本實施例中,流道Ca/Cb的延伸方向指第一冷卻流道116a/第二冷卻流道116b以及/或第一氣體流道118a/第二氣體流道118b的延伸方向。在圖5A中,雙極板131a之流道Ca與雙極板131b之流道Cb均是沿著第一方向D1延伸。此外,第一冷卻流道116a與第二冷卻流道116b以上下相對齊的方式設置;第一氣體流道118a與第二氣體流道118b也以上下相對應且對齊的方式設置,然而,本發明實施例不以此為限。Please refer to FIGS. 5A and 5B. In some embodiments, the extending direction of the flow channel Ca of the bipolar plate group (only the
在其它實施例中,雙極板131a之流道與雙極板131b之流道可以均是沿著第一方向D1延伸。但是,第一冷卻流道116a與第二冷卻流道116b以上下平行但是相錯位的方式設置;第一氣體流道118a與第二氣體流道118b也以上下平行但是相錯位的方式設置。In other embodiments, the flow path of the
在另一些實施例中,雙極板組(圖中僅繪出雙極板131a)之流道Ca’的延伸方向可以與雙極板組(圖中僅繪出雙極板131b)之流道Cb’的延伸方向不同,如圖5B所示。在圖5B中,雙極板131a之流道Ca’沿著第一方向D1延伸;而雙極板131b之流道Cb’沿著第二方向D2延伸。第一方向D1與第二方向D2不同。在一些實施例中,第一方向D1與第二方向D2垂直,然而,本發明實施例不以此為限。In other embodiments, the extending direction of the flow channel Ca' of the bipolar plate group (only the
此外,請參照圖4B,雙極板組130a之第一冷卻流道116a的間距P
c1可以與雙極板組130b之第二冷卻流道116b的間距P
c2相同或相異。雙極板組130a之第一氣體流道118a的間距P
g1可以與雙極板組130b之第二氣體流道118b的間距P
g2相同或相異。
In addition, referring to FIG. 4B, the pitch P c1 of the first
另外,圖6是依照本發明的一些實施例的一種燃料電池組的剖面示意圖。在圖6中,燃料電池組包括堆疊的多個燃料電池200。另外,在第三實施例的燃料電池組外側還可設置如單極板、集電板(collector plate)、端板(end plate)等構造,但本發明並不限於此。In addition, FIG. 6 is a schematic cross-sectional view of a fuel cell stack according to some embodiments of the present invention. In FIG. 6, the fuel cell stack includes a plurality of stacked
以下列舉幾個實例來確認本發明的功效,但本發明的範圍並不侷限於以下內容。Several examples are listed below to confirm the efficacy of the present invention, but the scope of the present invention is not limited to the following.
<實例1><Example 1>
提供尺寸為25cm´60cm、厚度為200微米的316L不銹鋼板材,不銹鋼板的原始晶粒範圍為25微米至60微米,原始晶粒的平均晶粒範圍為30微米至50微米。在攝氏900度的環境中,以1350MPa力量對不銹鋼板材壓延至厚度為100微米,之後爐冷至室溫,取出板材。測得壓延後的板材之平均晶粒範圍為20微米至45微米。取上述部分壓延後的板材,於攝氏550度、真空度為1´10
-2torr的環境下進行退火處理3小時。並使用油壓機在攝氏20度且壓力為225MPa的條件下,進行壓延與退火處理後的不銹鋼板材進行流道沖壓成型,以形成具有流道的不銹鋼基材。沖壓所使用的模具如圖2所示。請參照圖2,在此實例中,所採用的模具的下模具類似下模具12的凸部12P,其高度(亦即流道的深度)H’為0.5mm。凸部(流道)12P的頂角a’是圓化的鈍角,其曲率半徑為0.25mm。此外,相鄰兩個凸部12P之間的主體部12B的平面(或稱為平坦面)Fb’的寬度為1mm。此外,所採用的模具具有多組具有不同間距P’與拔模角g’的圖案。實例1的拔模角g’/間距P’分別為70度/2.36mm。其後,測量晶粒之粒徑,並使用接觸式探針量測儀(α-stepper, Kosaka Laboratory Ltd.生產,型號ET-4000A)進行表面粗糙度分析。
Provide 316L stainless steel plate with a size of 25cm´60cm and a thickness of 200 microns. The original grain size of the stainless steel plate is 25 microns to 60 microns, and the average grain size of the original grain is 30 microns to 50 microns. In an environment of 900 degrees Celsius, the stainless steel sheet was rolled to a thickness of 100 microns with a force of 1350 MPa, and then the furnace was cooled to room temperature, and the sheet was taken out. The average grain size of the rolled sheet is measured to be 20 microns to 45 microns. Take the above partially rolled sheet and anneal it for 3 hours in an environment of 550 degrees Celsius and a vacuum of 1´10 -2 torr. And using a hydraulic press under the conditions of 20 degrees Celsius and a pressure of 225MPa, the stainless steel sheet after the rolling and annealing treatment is punched into a runner to form a stainless steel substrate with a runner. The die used for stamping is shown in Figure 2. Please refer to FIG. 2. In this example, the lower mold of the adopted mold is similar to the
<實例2><Example 2>
提供尺寸為25cm´60cm、厚度為200微米的316L不銹鋼板材,不銹鋼板的原始晶粒範圍為25微米至60微米,原始晶粒的平均晶粒範圍為30微米至50微米。在攝氏900度的環境中,以1350MPa力量對不銹鋼板材壓延至厚度為100微米,之後爐冷至室溫,取出板材。測得壓延後的板材之平均晶粒範圍為20微米至45微米。取上述部分壓延後的板材,於攝氏550度、真空度為1´10
-2torr的環境下進行退火處理3小時。並使用油壓機在攝氏20度且壓力為225MPa的條件下,進行壓延與退火處理後的不銹鋼板材進行流道沖壓成型,以形成具有流道的不銹鋼基材。沖壓所使用的模具如圖2所示。請參照圖2,在此實例中,所採用的模具類似模具12的凸部12P,其高度(亦即流道的深度)H’為0.5mm。凸部(流道)12P的頂角a’是圓化的鈍角,其曲率半徑為0.25mm。此外,相鄰兩個凸部12P之間的主體部12B的平面(或稱為平坦面)Fb’的寬度為1mm。此外,所採用的模具具有多組具有不同間距P’與拔模角g’的圖案。實例2的拔模角g’/間距P’分別為45度/3mm。其後,測量晶粒之粒徑,並使用接觸式探針量測儀(α-stepper, Kosaka Laboratory Ltd.生產,型號ET-4000A)進行表面粗糙度分析。
Provide 316L stainless steel plate with a size of 25cm´60cm and a thickness of 200 microns. The original grain size of the stainless steel plate is 25 microns to 60 microns, and the average grain size of the original grain is 30 microns to 50 microns. In an environment of 900 degrees Celsius, the stainless steel sheet was rolled to a thickness of 100 microns with a force of 1350 MPa, and then the furnace was cooled to room temperature, and the sheet was taken out. The average grain size of the rolled sheet is measured to be 20 microns to 45 microns. Take the above partially rolled sheet and anneal it for 3 hours in an environment of 550 degrees Celsius and a vacuum of 1´10 -2 torr. And using a hydraulic press under the conditions of 20 degrees Celsius and a pressure of 225MPa, the stainless steel sheet after the rolling and annealing treatment is punched into a runner to form a stainless steel substrate with a runner. The die used for stamping is shown in Figure 2. Please refer to FIG. 2. In this example, the mold used is similar to the
<比較例1><Comparative Example 1>
相似於實例1,但在壓延之後、進行沖壓之前不進行退火處理。使用油壓機在攝氏20度且壓力為225MPa的條件下,對實例1之進行壓延與退火處理後的不銹鋼板材進行流道沖壓成型,以形成具有流道的不銹鋼基材。沖壓所使用的模具如圖2所示。請參照圖2,在此實例中,所採用的模具類似模具12的凸部12P,其高度(亦即流道的深度)H’為0.5mm。凸部(流道)12P的頂角a’是圓化的鈍角,其曲率半徑為0.25mm。此外,相鄰兩個凸部12P之間的主體部12B的平面(或稱為平坦面)Fb’的寬度為1mm。此外,所採用的模具具有多組具有不同間距P’與拔模角g’的圖案。實例1的拔模角g’/間距P’分別為70度/2.36mm。其後,測量晶粒之粒徑,並使用接觸式探針量測儀(α-stepper, Kosaka Laboratory Ltd.生產,型號ET-4000A)進行表面粗糙度分析。Similar to Example 1, but no annealing treatment is performed after rolling but before stamping. Using a hydraulic press under the conditions of 20 degrees Celsius and a pressure of 225 MPa, the stainless steel sheet after the rolling and annealing treatment of Example 1 was runner-pressed to form a stainless steel substrate with a runner. The die used for stamping is shown in Figure 2. Referring to FIG. 2, in this example, the mold used is similar to the
<實例3><Example 3>
在上述實例1之不銹鋼板材上,以鹽浴法於攝氏350度的碳酸鹽中形成3微米之碳膜,以做為抗蝕膜,進行電化學腐蝕測試,推估腐蝕壽命。電化學腐蝕測試是在攝氏80度濃度為1M的氫氧化鉀溶液中進行。表面粗糙度分析是使用接觸式探針量測儀(α-stepper, Kosaka Laboratory Ltd.生產,型號ET-4000A)來進行。其結果如表2所示。On the stainless steel plate of Example 1 above, a 3 micron carbon film was formed in the carbonate at 350 degrees Celsius by the salt bath method as a resist film, and an electrochemical corrosion test was conducted to estimate the corrosion life. The electrochemical corrosion test is carried out in a potassium hydroxide solution with a concentration of 1M at 80 degrees Celsius. The surface roughness analysis was performed using a contact probe measuring instrument (α-stepper, manufactured by Kosaka Laboratory Ltd., model ET-4000A). The results are shown in Table 2.
<比較例2><Comparative example 2>
類似實例3,但以比較例1之未進行熱處理之不銹鋼板材取代實例1之有進行熱處理的不銹鋼板材。其結果如表2所示。Similar to Example 3, but replacing the stainless steel plate with heat treatment of Example 1 with the stainless steel plate with no heat treatment of Comparative Example 1. The results are shown in Table 2.
表1
表2
圖7A是實例1之不銹鋼晶粒之SEM的影像圖。圖7B是比較例1之不銹鋼晶粒之SEM的影像圖。由圖7A與圖7B的結果顯示壓延後進行熱處理之實例1的不銹鋼晶粒粒徑遠小於壓延後沒有進行熱處理之比較例1之不銹鋼晶粒的粒徑。7A is an SEM image of the stainless steel grain of Example 1. FIG. 7B is an SEM image of stainless steel crystal grains of Comparative Example 1. FIG. The results of FIG. 7A and FIG. 7B show that the grain size of the stainless steel grain of Example 1 which is heat-treated after rolling is much smaller than that of the stainless steel grain of Comparative Example 1 which is not heat-treated after rolling.
圖8A是實例1之不銹鋼基材的表面粗糙度分析。圖8B是比較例1之不銹鋼基材的表面粗糙度分析。由圖8A與圖8B的結果顯示壓延後進行熱處理之實例1的不銹鋼基材的表面粗糙度遠小於壓延後沒有進行熱處理之比較例1之不銹鋼基材的表面粗糙度。8A is an analysis of the surface roughness of the stainless steel substrate of Example 1. FIG. 8B is a surface roughness analysis of the stainless steel substrate of Comparative Example 1. FIG. The results of FIGS. 8A and 8B show that the surface roughness of the stainless steel substrate of Example 1 which is heat-treated after rolling is much smaller than that of the stainless steel substrate of Comparative Example 1 which is not heat-treated after rolling.
圖9A是實例2之以具有45度拔模角之模具沖壓後所得不銹鋼基材的光學顯微鏡的影像圖。圖9B是實例1之以具有70度拔模角之模具沖壓後所得不銹鋼基材的光學顯微鏡的影像圖。由圖9A與9B的結果顯示沖壓後之不銹鋼基材連續且厚度均勻。9A is an image view of an optical microscope of a stainless steel substrate obtained in Example 2 after being stamped with a die having a draft angle of 45 degrees. 9B is an image view of an optical microscope of a stainless steel substrate obtained by punching with a mold having a draft angle of 70 degrees in Example 1. FIG. The results of FIGS. 9A and 9B show that the stainless steel substrate after punching is continuous and uniform in thickness.
另外,由表2的電化學腐蝕結果與壽命預測結果顯示:壓延後進行熱處理之實例3的電化學腐蝕速率低於壓延後沒有進行熱處理之比較例2的電化學腐蝕速率,其壽命可以提升約33.1%。其增加的原因推測是熱處理後不銹鋼晶粒被細化,表面粗糙度降低,使得電化學腐蝕速率下降所致。In addition, the electrochemical corrosion results and life prediction results from Table 2 show that the electrochemical corrosion rate of Example 3 which is heat-treated after rolling is lower than that of Comparative Example 2 which is not heat-treated after rolling, and its life can be increased by about 33.1%. The reason for this increase is presumed to be that the stainless steel grains are refined after heat treatment, and the surface roughness is reduced, resulting in a decrease in the electrochemical corrosion rate.
<實例4>取厚度100微米的鈦板材,原始晶粒範圍為6微米至20微米,原始晶粒的平均晶粒範圍為9微米至15微米。取上述部分鈦板材於攝氏350度、真空度為1´10
-2torr的環境下進行退火處理1小時,形成晶粒的平均晶粒範圍為0.1微米至3微米。沖壓所使用的模具如圖2所示。請參照圖2,在此實例中,所採用的模具類似模具12的凸部12P,其高度(亦即流道的深度)H’為0.5mm。凸部(流道)12P的頂角a’是圓化的鈍角,其曲率半徑為0.25mm。此外,相鄰兩個凸部12P之間的主體部12B的平面(或稱為平坦面)Fb’的寬度為1mm。此外,所採用的模具具有多組具有不同間距P’與拔模角g’的圖案。實例1的拔模角g’/間距P’分別為70度/2.36mm。其結果如表3所示。
<Example 4> A titanium plate with a thickness of 100 μm is taken. The original grain range is 6 μm to 20 μm, and the average grain size of the original grains is 9 μm to 15 μm. Taking the above-mentioned part of the titanium plate for annealing for 1 hour in an environment of 350 degrees Celsius and a vacuum of 1´10 -2 torr, the average grain size of the formed grains is 0.1 μm to 3 μm. The die used for stamping is shown in Figure 2. Please refer to FIG. 2. In this example, the mold used is similar to the
<實例5><Example 5>
取厚度100微米的鈦板材,原始晶粒範圍為6微米至20微米,原始晶粒的平均晶粒範圍為9微米至15微米。取上述部分鈦板材於攝氏350度、真空度為1´10
-2torr的環境下進行退火處理1小時,形成晶粒的平均晶粒範圍為0.1微米至3微米。沖壓所使用的模具如圖2所示。請參照圖2,在此實例中,所採用的模具類似模具12的凸部12P,其高度(亦即流道的深度)H’為0.5mm。凸部(流道)12P的頂角a’是圓化的鈍角,其曲率半徑為0.25mm。此外,相鄰兩個凸部12P之間的主體部12B的平面(或稱為平坦面)Fb’的寬度為1mm。此外,所採用的模具具有多組具有不同間距P’與拔模角g’的圖案。實例2的拔模角g’/間距P’分別為45度/3mm。其後,測量晶粒之粒徑,並使用接觸式探針量測儀(α-stepper, Kosaka Laboratory Ltd.生產,型號ET-4000A)進行表面粗糙度分析。
Taking a titanium plate with a thickness of 100 microns, the original grains range from 6 microns to 20 microns, and the average grain size of the original grains ranges from 9 microns to 15 microns. Taking the above-mentioned part of the titanium plate for annealing for 1 hour in an environment of 350 degrees Celsius and a vacuum of 1´10 -2 torr, the average grain size of the formed grains is 0.1 μm to 3 μm. The die used for stamping is shown in Figure 2. Please refer to FIG. 2. In this example, the mold used is similar to the
<比較例3>相似於實例4,但鈦板材不進行退火處理。其結果如表3所示。沖壓所使用的模具如圖2所示。請參照圖2,在此實例中,所採用的模具類似模具12的凸部12P,其高度(亦即流道的深度)H’為0.5mm。凸部(流道)12P的頂角a’是圓化的鈍角,其曲率半徑為0.25mm。此外,相鄰兩個凸部12P之間的主體部12B的平面(或稱為平坦面)Fb’的寬度為1mm。此外,所採用的模具具有多組具有不同間距P’與拔模角g’的圖案。實例1的拔模角g’/間距P’分別為70度/2.36mm。其後,測量晶粒之粒徑,並使用接觸式探針量測儀(α-stepper, Kosaka Laboratory Ltd.生產,型號ET-4000A)進行表面粗糙度分析。<Comparative Example 3> It is similar to Example 4, but the titanium sheet is not annealed. The results are shown in Table 3. The die used for stamping is shown in Figure 2. Referring to FIG. 2, in this example, the mold used is similar to the
<實例6><Example 6>
取實施例4之另一部分鈦板材,依照上述實施3之方式形成抗蝕膜鍍之製程,並進行電化學腐蝕測試,推估耐腐蝕壽命分析。其結果如表4所示。Taking another part of the titanium plate of Example 4, the process of forming a resist film plating according to the above-mentioned Embodiment 3, and performing an electrochemical corrosion test to estimate the corrosion resistance life analysis. The results are shown in Table 4.
<比較例4><Comparative Example 4>
相似於實例6,但以比較例3之未經熱處理之板材取代實例4之板材。其結果如表4所示。Similar to Example 6, but replacing the plate of Example 4 with the unheated plate of Comparative Example 3. The results are shown in Table 4.
表3
表4
圖10A是實例4之鈦晶粒之SEM影像圖。圖10B是比較例3之鈦晶粒之SEM影像圖。由圖10A與圖10B的結果顯示壓延後進行熱處理之實例4的鈦晶粒的粒徑遠小於沒有進行熱處理之比較例3之鈦晶粒的粒徑。10A is an SEM image of titanium grains of Example 4. FIG. FIG. 10B is an SEM image of titanium crystal grains of Comparative Example 3. FIG. The results of FIGS. 10A and 10B show that the particle size of titanium crystal grains of Example 4 subjected to heat treatment after rolling is much smaller than that of Comparative Example 3 without heat treatment.
圖11A是實例4之鈦基材的表面粗糙度分析。圖11B是比較例3之鈦基材的表面粗糙度分析。由圖11A與圖11B的結果顯示進行熱處理之實例4的鈦基材的表面粗糙度遠小於沒有進行熱處理之比較例3之鈦基材的表面粗糙度。11A is an analysis of the surface roughness of the titanium substrate of Example 4. FIG. 11B is an analysis of the surface roughness of the titanium substrate of Comparative Example 3. FIG. The results of FIGS. 11A and 11B show that the surface roughness of the titanium substrate of Example 4 subjected to heat treatment is much smaller than that of the titanium substrate of Comparative Example 3 without heat treatment.
圖12A是實例5之以具有45度拔模角流道圖案之模具沖壓後所得鈦基材的光學顯微鏡的影像圖。圖12B是實例4之以具有70度拔模角流道圖案之模具沖壓後所得鈦基材的光學顯微鏡的影像圖。由圖12A與12B的結果顯示沖壓後之鈦基材連續且厚度均勻。FIG. 12A is an optical microscope image of a titanium substrate obtained after punching with a die having a 45-degree draft angle runner pattern in Example 5. FIG. 12B is an optical microscope image of a titanium substrate obtained after punching with a mold having a 70-degree draft angle runner pattern in Example 4. FIG. The results of FIGS. 12A and 12B show that the titanium substrate after stamping is continuous and uniform in thickness.
另外,表4的電化學腐蝕結果與壽命預測結果顯示:有進行熱處理之實例6的電化學腐蝕速率低於沒有進行熱處理之比較例4的電化學腐蝕速率,其壽命可以提升約47.6%。其增加的原因推測是熱處理後鈦晶粒被細化,表面粗糙度降低,使得電化學腐蝕速率下降所致。In addition, the electrochemical corrosion results and life prediction results in Table 4 show that the electrochemical corrosion rate of Example 6 with heat treatment is lower than that of Comparative Example 4 without heat treatment, and its life can be increased by about 47.6%. The reason for its increase is presumed to be that the titanium grains are refined after heat treatment, and the surface roughness is reduced, resulting in a decrease in the electrochemical corrosion rate.
綜合以上所述,本發明實施例之燃料電池可以提升雙極板的抗腐蝕及壽命。在一些實施例中,本發明之燃料電池可應用於200微米以下之超薄金屬雙極板組,透過將金屬板材晶粒細化(晶粒<15微米),使流道沖壓後的表面粗糙度降低(Ra< 1.2um),並配合鍍膜層材料選擇於流道拔模角度大於≧40度時,促使抗蝕層鍍膜的披覆性(coverage)更高,更抗蝕。In summary, the fuel cell of the embodiment of the present invention can improve the corrosion resistance and life of the bipolar plate. In some embodiments, the fuel cell of the present invention can be applied to ultra-thin metal bipolar plate assemblies under 200 microns, by refining the grain of the metal sheet (grain <15 microns), the surface of the runner after stamping is rough The degree of reduction (Ra <1.2um), and the coating layer material is selected when the draft angle of the flow channel is greater than ≧40 degrees, which promotes a higher coating coverage of the resist layer and more corrosion resistance.
雖然本發明已以實施例揭露如上,然其並非用以限定本發明,任何所屬技術領域中具有通常知識者,在不脫離本發明的精神和範圍內,當可作些許的更動與潤飾,故本發明的保護範圍當視後附的申請專利範圍所界定者為準。Although the present invention has been disclosed as above with examples, it is not intended to limit the present invention. Any person with ordinary knowledge in the technical field can make some changes and modifications without departing from the spirit and scope of the present invention. The scope of protection of the present invention shall be subject to the scope defined in the appended patent application.
10、10a、10b:板材10, 10a, 10b: plate
11:基材11: substrate
11P:凸部11P: convex part
11R、131R 1、131R 2、132R 1、132R 2:凹部11R, 131R 1 , 131R 2 , 132R 1 , 132R 2 : recess
11Pt:頂面11Pt: top surface
11Rb:底面11Rb: bottom surface
11S:側壁11S: Side wall
12:下模具12: Lower mold
12B:主體部12B: Main body
12P、131P 1、131P 2、132P 1、132P 2:凸部12P, 131P 1 , 131P 2 , 132P 1 , 132P 2 : convex part
12Pt:頂面12Pt: top surface
12Rb:底面12Rb: bottom surface
12S:側壁12S: Side wall
12Bb、12T:表面12Bb, 12T: surface
13:壓延製程13: Rolling process
14:熱處理製程14: Heat treatment process
16:流道16: flow channel
20:抗蝕層20: Anti-corrosion layer
30、131a、131b、132a、132b:雙極板30, 131a, 131b, 132a, 132b: bipolar plate
102:膜電極組102: Membrane electrode group
104:質子交換膜104: Proton exchange membrane
106a、106b:氣體擴散層106a, 106b: gas diffusion layer
116a:第一冷卻流道116a: the first cooling channel
116b:第二冷卻流道116b: Second cooling channel
118a:第一氣體流道118a: the first gas flow path
118b:第二氣體流道118b: Second gas flow path
130a、130b:雙極板組130a, 130b: Bipolar plate group
200:燃料電池200: fuel cell
Ca’、Cb’:流道Ca’, Cb’: flow channel
D1:第一方向D1: First direction
D2:第二方向D2: Second direction
P、P’、Pc1、Pc2、Pg1、Pg2:間距P, P’, Pc1, Pc2, Pg1, Pg2: pitch
a、a’:頂角a, a’: vertex angle
b、b’:底角b, b’: bottom corner
g、g’:拔模角g, g’: draft angle
Ft、Ft’、Fb、Fb’:平面Ft, Ft’, Fb, Fb’: plane
H、H’:高度H, H’: height
圖1A至圖1F是依據本發明實施例之燃料電池的雙極板的製造方法的流程剖面圖。 圖2是依據本發明實施例之模具的剖面圖。 圖3是依據本發明實施例之具有流道的基材的剖面圖。 圖4A是依據本發明實施例之燃料電池的剖面示意圖。 圖4B是依據本發明實施例之雙極板的流道相對應設置之燃料電池的剖面示意圖。 圖5A是依據本發明實施例之雙極板流道方向平行之燃料電池的剖面示意圖。 圖5B是依據本發明實施例之雙極板流道方向垂直之燃料電池的剖面示意圖。 圖6是依照本發明實施例的一種燃料電池組的剖面示意圖。 圖7A是實例1之不銹鋼晶粒之SEM影像圖。 圖7B是比較例1之不銹鋼晶粒之SEM影像圖。 圖8A是實例1之不銹鋼基材的表面粗糙度分析。 圖8B是比較例1之不銹鋼基材的表面粗糙度分析。 圖9A是實例2之以具有45度拔模角之模具沖壓後所得不銹鋼基材的光學顯微鏡(OM)的影像圖。 圖9B是實例1之以具有70度拔模角之模具沖壓後所得不銹鋼基材的光學顯微鏡的影像圖。 圖10A是實例4之鈦晶粒之SEM的影像圖。 圖10B是比較例3之鈦晶粒之SEM的影像圖。 圖11A是實例4之鈦基材的表面粗糙度分析。 圖11B是比較例3之鈦基材的表面粗糙度分析。 圖12A是實例5之以具45度拔模角流道圖案之模具沖壓後所得鈦基材的光學顯微鏡的影像圖。 圖12B是實例4之以具70度拔模角流道圖案之模具沖壓後所得鈦基材的光學顯微鏡的影像圖。1A to 1F are cross-sectional views of the flow of a method for manufacturing a bipolar plate of a fuel cell according to an embodiment of the invention. 2 is a cross-sectional view of a mold according to an embodiment of the invention. 3 is a cross-sectional view of a substrate with flow channels according to an embodiment of the invention. 4A is a schematic cross-sectional view of a fuel cell according to an embodiment of the invention. 4B is a schematic cross-sectional view of a fuel cell corresponding to the flow path of a bipolar plate according to an embodiment of the present invention. 5A is a schematic cross-sectional view of a fuel cell with parallel flow paths of bipolar plates according to an embodiment of the present invention. FIG. 5B is a schematic cross-sectional view of a fuel cell having a bipolar plate with a perpendicular flow channel according to an embodiment of the present invention. 6 is a schematic cross-sectional view of a fuel cell stack according to an embodiment of the present invention. 7A is an SEM image of the stainless steel grain of Example 1. FIG. 7B is an SEM image of stainless steel grains of Comparative Example 1. FIG. 8A is an analysis of the surface roughness of the stainless steel substrate of Example 1. FIG. 8B is a surface roughness analysis of the stainless steel substrate of Comparative Example 1. FIG. 9A is an optical microscope (OM) image of a stainless steel substrate obtained after punching with a die having a draft angle of 45 degrees in Example 2. FIG. 9B is an image view of an optical microscope of a stainless steel substrate obtained by punching with a mold having a draft angle of 70 degrees in Example 1. FIG. FIG. 10A is an SEM image of titanium grains of Example 4. FIG. FIG. 10B is an SEM image of titanium crystal grains of Comparative Example 3. FIG. 11A is an analysis of the surface roughness of the titanium substrate of Example 4. FIG. 11B is an analysis of the surface roughness of the titanium substrate of Comparative Example 3. FIG. 12A is an optical microscope image of a titanium substrate obtained by punching a mold with a 45-degree draft angle runner pattern in Example 5. FIG. 12B is an optical microscope image of a titanium substrate obtained after punching with a mold having a 70-degree draft angle runner pattern in Example 4. FIG.
11:基材 11: substrate
11P:凸部 11P: convex part
11R:凹部 11R: recess
11S:側壁 11S: Side wall
16:流道 16: flow channel
20:抗蝕膜層 20: resist film
30:雙極板組 30: Bipolar plate group
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CN103548193A (en) * | 2011-04-20 | 2014-01-29 | 托普索燃料电池股份有限公司 | Process for surface conditioning of a plate or sheet of stainless steel and application of a layer onto the surface, interconnect plate made by the process and use of the interconnect plate in fuel cell stacks |
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CN101136479A (en) * | 2007-05-23 | 2008-03-05 | 山东大学 | Process of producing double pole plates for fuel cell |
CN103548193A (en) * | 2011-04-20 | 2014-01-29 | 托普索燃料电池股份有限公司 | Process for surface conditioning of a plate or sheet of stainless steel and application of a layer onto the surface, interconnect plate made by the process and use of the interconnect plate in fuel cell stacks |
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