1. Introduction
Global fossil fuel has been radically depleted due to massive industrialization to consume the resource and increased demand has a huge impact on the environment such as climate change caused by greenhouse gas emission [
1]. The utilization of clean energy from new and renewable sources is considered as an effective solution for the resolution of both the shortage of electrical energy and the reduction of greenhouse gas emission. Hydrogen can solve energy and environmental problems because the electrical energy can be produced from the electrochemical reactions using hydrogen and oxygen. Recently, various production technologies of hydrogen are being developed for massive supply to fuel cells [
2,
3].
Polymer electrolyte fuel cell (PEFC) is commonly used as an energy conversion device from hydrogen into electrical energy since it has the advantage that its conversion efficiency is significantly higher than conventional power generation devices [
4,
5,
6]. In order to maximize the performance of PEFC, three main irreversible losses, i.e., activation, Ohmic, and mass transport overpotential, should be minimized as catalyst layer (CL) of PEFC where main electrochemical reactions such as the oxidation of hydrogen and the reduction of oxygen take place. Both CLs are attached onto a piece of polymeric electrolyte membrane to complete membrane electrode assembly (MEA) to allow to transport proton through membrane and electron through external circuit for the complete fuel cell reactions. Most of activation overpotential in PEFC is originated from the result of oxygen reduction reaction (ORR) at cathode:
In the previous report, it was also found that ORR in CL is primarily limited by mass transport resistance [
7,
8]. Therefore, it is necessary to optimize the microstructure of CL at cathode for improved ORR, which forms the sufficient thick ionomer shell exhibiting a highly aggregated phase morphology and retains sufficient void space for unimpeded gas transport [
9]. Ionomers are commonly utilized as proton conductor in CL for membrane electrode assemblies (MEAs) to facilitate the activation of electrochemical reactions at triple phase boundary (TPB) through proton conduction as well as hydrogen and oxygen permeation. CL is highly influenced by platinum on carbon supported catalyst and ionomer formation structure. Thus, the pore size and porosity of CLs are differed with respect to the type of catalyst and ionomer [
10,
11,
12,
13].
Perfluorosulfonic acid (PFSA) ionomers, such as Nafion
® or Aquivion
®, are used as the membrane and ionomer binder in MEA due to good proton conductivity at low water uptake, chemical stability, and mechanical stability [
14]. PFSA are typically consisted of hydrophobic Teflon-like backbones and hydrophilic sulfonate (SO
3−) bearing side chains, which conducts protons through a crystalline phase-segregated structure with localized hydrophobic and hydrophilic domains [
15,
16,
17,
18]. PFSA membrane acts as a bulk proton-conducting membrane, while ionomer in CL is achieved by thin film coated on catalyst and/or catalyst support particles as well as agglomerates and filling the regions between aggregates [
9]. Nafion
® is an ionomer with long side chains (LSC) consisting of five −CF
2 groups. Aquivion
® is a short side chain (SSC) ionomer with two −CF
2 groups. These ionomers are commonly used as binders in CL and are the most widely used as ion-conductive polymers in CL of MEA [
19,
20].
PFSA ionomers play an important role in CLs to determine the microstructure of consisting of pores, ionomer coated shell on catalyst particles, and ionomer aggregates. The structure of CLs could be determined by the length of PFSA side chain and the equivalent weight (EW). The performance of the MEA is therefore influenced by the microstructure of CL [
21,
22,
23]. For instance, it was reported that utilizing SSC ionomers could help reduce the formation of dense ionomer layers that impede O
2 transport and catalyst activity compared to LSC ionomers [
24,
25]. Moreover, LSC-PFSA and SSC-PFSA ionomers were utilized to investigate the mass transport behavior in the MEA during PEFC operation. SSC-PFSA ionomer-based CL demonstrated higher proton conductivity and lower gas transport resistance compared to LSC-PFSA ionomer-based CL due to a beneficial pore structure that enhanced the electrochemical reaction. This looser porous structure with larger porosity, in contrast to LSC-PFSA ionomer-based CL, contributed to the high performance of MEAs [
26,
27,
28]. Nafion
® and Aquivion
® were also utilized as binder for CL as well as solid electrolyte for MEA in PEFCs. Currently, Nafion
® ionomers such as D2021(EW1100) and D2020(EW1000) are being used as membranes and binders. Aquivion
® ionomers, named D72-25BS(EW720), D98-25BS(EW980), and D83-24B(EW830), are widely used. The result was evaluated from short- and long-term performance for CLs using SSC- or LSC-PFSA ionomers. SSC-PFSA ionomer showed higher performance because of higher ion-exchange capacity and water uptake capacity than LSC-PFSA ionomer. However, SSC-PFSA ionomer exhibited higher degradation than LSC-PFSA ionomer, indicating the influence of the length of the CF
2 chain. In other words, LSC is chemically stable and can function as both a binder and a proton conductor in the catalyst layer for long-term applications [
13,
23,
29,
30]. Despite the advantage of CLs using single type of ionomer, the studies of CLs utilizing blended ionomers are lacking to date [
31,
32]. To understand the effect of the blended ionomers in CL, ionomer aggregates, ionomer-catalyst particle interaction, and thin film structure of ionomer on catalyst and support particles should be studied.
In this work, the CLs using blended PFSA ionomers with different side chain lengths and EWs are investigated to understand how the blended ionomer forms thin films in the CLs and the thin films influence the CL performance, compared to the CLs utilizing single PFSA ionomers. Blended ionomer dispersions were prepared by mixing Nafion EW 1100 and Aquivion EW 720 as well as Aquivion EW 980 and Aquivion EW 720 to prepare LSC/SSC blended-EW 1000 and -EW 980 and SSC/SSC-EW 830. To investigate the blending effect on CL performance, CLs using various types of blended ionomers were prepared and evaluated. The physicochemical properties and electrochemical performance of single and blended ionomers and CLs were characterized in terms of proton conductivity, water uptake, ion exchange capacity, pore size distribution, voltammetry, and I-V polarization.
3. Results and discussion
To investigate the blending effect of SSC and LSC ionomers on CL performance, three different types of the blended ionomer dispersions, i.e., LSC/SSC blended-EW 1000 and -EW 980 and SSC/SSC-EW 830, were prepared by mixing Nafion D1021 (EW 1100) and Aquivion D72-25BS (EW 720) as well as Aquivion D98-25BS (EW 980) and Aquivion EW 720 and compared with the single ionomer dispersions, i.e, Nafion D2020 (EW 1000), Aquivion D98-25BS (EW 980), Aquivion D83-24B (EW 830). The IEC of the blended ionomers and the single ionomers were measured and compared to confirm whether the blended ionomers have similar EWs to the single ionomers prior to the evaluation of CL performance.
Table 1 summarizes the IEC results of the blended and the single ionomers. All values have the standard deviation less than 5%. The IEC results indicate that the IEC of the blended ionomers have similar targeted EWs so as to compare with the single ionomers.
The ion conductivity of the ionomers was evaluated at R.T., 30, 50, 70, and 90 °C with R.H. 100% and at 80 °C with R.H. 50, 75, and 100%. The effect of temperature on the ion conductivity of the ionomers is represented in
Figure 1a. It indicates that #1 (LSC+SSC, EW 1000) ionomer exhibits higher ion conductivity than #4 (LSC, EW 1000) ionomer and #2 (LSC+SSC, EW 980) and #3 (SSC+SSC, EW 830) also demonstrate higher ion conductivity than #5 (SSC, EW 980) and #6 (SSC, EW 830) at all temperatures. It is in a good agreement with the previous result that the presence of enhanced ion-cluster channels in blended ionomer led to increase the ion conductivity [
39].
Figure 1b shows that #3 (SSC+SSC, EW 830) exhibits higher ion conductivity than the other five ionomers at 80 °C with R.H. 50, 75, and 100% due to blending effect of ionomers and lower EW.
The activation energy of the ionomers representing the minimum energy required for proton conduction between ion cluster sites is shown in
Figure 2. Low activation energy for proton conduction reduces energy loss due to the low ionic resistance of the ionomers and improves the PEFC performance [
40]. The activation energy of the ionomers is calculated based on the temperature-dependent ion conductivity using Arrhenius plots and is summarized in
Table 2. The blended #3 (SSC+SSC, EW 830) shows the lowest activation energy value (10.86 kJ/mol) and the single #5 (SSC, EW 980) and #6 (SSC, EW 830) show values lower than 12 kJ/mol. Samples with low activation energy values were prepared using only the SSC-ionomer. The ionomers with SSC and low EW can help reduce the activation energy due to the smaller size of ion clusters compared to LSC-ionomers. Therefore, SSC-ionomers should be used for energy efficiency enhancements required for catalyst layer ionomer binders and membranes in PEFCs [
41].
Water uptake is an important ionomer’s property mainly influenced by the EW of the ionomers. Low EW ionomers have higher sulfonic acid groups to result in higher water uptake. Finally, it causes the formation of better ion clustering to enhance proton conduction. On the other hand, high EW ionomers show the opposite behavior, which is lower water uptake and poor ion clustering [
42]. The water uptake of the blended and the single ionomers as a function of temperature is shown in
Figure 3. The water uptake of all prepared ionomers increases with temperature and the blended #1, #2, and #3 ionomers show higher water uptake than the single #4, #5, and #6 ionomers. It is noted that the blended #2 (LSC+SSC, EW 980) ionomer shows higher water uptake over the entire temperature range than the single #5 (SSC, EW 980) ionomer. In particular, the blended #3 (SSC+SSC, EW 830) ionomer shows a rapid increase in water uptake as the temperature increases. Compared to the single #6 (SSC, EW 830), much higher water uptake is exhibited. Even though they have a similar EW, it implies that the blended ionomers have bulk structure to form competent free volume. The movement of proton within ionomer depends on either the vehicular mechanism which involves the transfer of hydrated protons and/or the Grotthuss mechanism which entails the rearrangement and "hopping" of protons within extensive hydration structures [
16,
43]. The presence of well-formed ion cluster channels through the blended ionomers attributes to the improved water retention in the free volume of the ionomers. It is noteworthy for the PEFC application as membrane and/or CL binder in low external relative humidity conditions due to their excellent water absorption.
The oxygen reduction reaction (ORR) requires reagents to approach through micro-pores in CL and adsorb onto the ionomer-electrocatalyst surface, followed by a charge transfer between reactants and ionomer-electrocatalyst surface and the resulting product to desorb from the surface. In this process, the cause of O
2 diffusion limitations is a major issue for oxygen reduction reactions to be related to the oxygen flux through the thin film ionomer coating on the Pt catalyst particles or the micro-pores formed in CL [
9]. The oxygen permeability through the CL varies with the type of ionomers, especially, EW and the type of side chain LSC ionomers strongly inhibit the ORR more than SSC ionomers due to dense coating on electrocatalyst [
24,
25,
44]. In addition, Yannick G. et al. reported that the SSC ionomer-based CL had higher porosity than the LSC-based ionomer-based CL primarily due to more uniform ionomer distributions in SSC-ionomer. As a result, it exhibited less oxygen resistance and lower cathode proton transport resistance. The higher porosity of the SSC ionomer-based CL leads to improve the performance and limiting current density within the mass transport region [
24,
45,
46,
47].
The porosity of CLs prepared by the blended and the single ionomers was measured since the film morphology on the surface of electrocatalysts formed by the ionomer aggregates could determine the microstructure of CLs mainly to influence O2 permeability. The measured porosity of the blended #1 (LSC+SSC, EW 1000), #2 (LSC+SSC, EW 980), and #3 (SSC+SSC, EW 830) ionomer-based CLs was 43.40, 46.85, and 45.38%, respectively, and the single #4 (LSC, EW 1000), #5 (SSC, EW 980), and #6 (SSC, EW 830) were 40.55, 42.18, and 35.73, respectively. It is observed that the blended ionomer-based CLs form higher porosity. Hence it could be expected that the blended ionomer-based CLs with higher porosity help reduce the resistance of oxygen transport and attributes to lower mass transfer loss [
48]. It is also noted that all the blended ionomers include SSC ionomers. As mentioned before, it is a good agreement with the previous results that the SSC ionomer-based CL had higher porosity than the LSC-based ionomer-based CL [
24,
45,
46,
47].
Figure 4.
The pore diameter distribution of CLs prepared using the blended #1 (circle, LSC+SSC, EW 1000), #2 (triangle, LSC+SSC, EW 980), and #3 (square, SSC+SSC, EW 830) ionomers and the single #4 (pentagon, LSC, EW 1000), #5 (inverted triangle, SSC, EW 980), and #6 (diamond, SSC, EW 830) ionomers.
Figure 4.
The pore diameter distribution of CLs prepared using the blended #1 (circle, LSC+SSC, EW 1000), #2 (triangle, LSC+SSC, EW 980), and #3 (square, SSC+SSC, EW 830) ionomers and the single #4 (pentagon, LSC, EW 1000), #5 (inverted triangle, SSC, EW 980), and #6 (diamond, SSC, EW 830) ionomers.
The characterization and PEFC performance of the MEAs was finally evaluated to prove the effect of the blended ionomer-based CLs with different water uptake and porosity on the microstructure of CL. It could be influenced by the temperature of PEFC operation and the relative humidity particularly because the hydration and dehydration processes are involved in proton conduction and oxygen permeability within the cathodic CL. Insufficient proton conductivity and/or less oxygen permeability at elevated temperature and/or low relative humidity diminishes the CL activity [
49,
50]. In other words, the ionomer is a very important factor to affect the temperature and humidification conditions in relation to the performance and activity of the CL. Thus, it is important to design an ionomer capable of sufficient water management.
To evaluate fuel cell performance, the MEAs were fabricated using the blended ionomers and the single ionomers. The performance of the MEAs was evaluated at 70, 75, and 80 °C at R.H. 100% and R.H. 50 and 75% at 80 °C and was compared using the I-V polarization curves. The results of MEA evaluation are represented in
Figure 5 and summarized in
Table 3. The PEFC performance of the both types (blended and single) of MEAs at 70 and 75 °C with R.H. 100% shows no difference at 0.4, 0.6, and 0.8 V. However, the superior performance of the blended ionomer-based MEAs is shown to that of the single ones at the elevated temperature (80 °C) and lower relative humidity (50 and 75%). As discussed earlier, higher water uptake and porosity attribute to better performance. However, this behavior is not observed in comparison of the ionomers with different EWs. As shown in
Figure 1, two blended and single ionomers with EW 830 show the highest ion conductivity which generally attains higher PEFC performance due to less Ohmic resistance. Nevertheless, the structure and some properties of nanoscale ionomer thin film are significantly different from the bulk, and its exact structure and behavior is still not precisely understood [
9].
ECSA results calculated from CVs measured under the same temperature and relative humidity to I-V measurements are summarized in
Table 4. ECSA results show similar behavior to PEFC performance. It also exhibits that the ECSA of the blended ionomer-based MEAs is higher than that of the single ones at the elevated temperature (80 °C) and lower relative humidity (50 and 75%). No distinguishable increase in ECSA at lower EW is revealed.
The limiting current density in I-V polarization can be used to evaluate oxygen permeation resistance to CL. It is reported that the smaller the reduction rate of the limiting current density with oxygen concentration, the lower the oxygen permeation resistance. [
51,
52]. The limiting current density reduction rate is defined by the difference in limiting current density measured at maximum and minimum oxygen ratios.
Figure 6 shows the decreasing rates of limiting current density obtained with oxygen concentration. In general, CLs with high decreasing ratio have the disadvantage of gas permeation. The decreasing rates of limiting current density for two different types (blended and single) of MEAs are compared at 70, 75, and 80 °C at R.H. 100% and R.H. 50 and 75% at 80 °C. As summarized in
Table 5, the results indicate that the blending ionomers exhibit lower decreasing rates in all the operation conditions due to the higher porosity of the blended ionomer-based CLs compared to the single ionomer-based CLs (
Figure 4).
The blended ionomers have higher water uptake and form high porous CL structure. Those characteristics result in higher PEFC performance and better mass transport which are confirmed by the variation of I-V polarization, ECSA, and limiting current density. Compared to the single ionomer-based CLs, the blended ones could provide advantageous candidates for various PEFC applications.
Figure 1.
The ion conductivity of the blended #1 (circle, LSC+SSC, EW 1000), #2 (triangle, LSC+SSC, EW 980), and #3 (square, SSC+SSC, EW 830) ionomers and the single #4 (pentagon, LSC, EW 1000), #5 (inverted triangle, SSC, EW 980), and #6 (diamond, SSC, EW 830) ionomers as a function of temperature and R.H.
Figure 1.
The ion conductivity of the blended #1 (circle, LSC+SSC, EW 1000), #2 (triangle, LSC+SSC, EW 980), and #3 (square, SSC+SSC, EW 830) ionomers and the single #4 (pentagon, LSC, EW 1000), #5 (inverted triangle, SSC, EW 980), and #6 (diamond, SSC, EW 830) ionomers as a function of temperature and R.H.
Figure 2.
The temperature-dependent Arrhenius plots for the blended #1 (circle, LSC+SSC, EW 1000), #2 (triangle, LSC+SSC, EW 980), and #3 (square, SSC+SSC, EW 830) ionomers and the single #4 (pentagon, LSC, EW 1000), #5 (inverted triangle, SSC, EW 980), and #6 (diamond, SSC, EW 830) ionomers.
Figure 2.
The temperature-dependent Arrhenius plots for the blended #1 (circle, LSC+SSC, EW 1000), #2 (triangle, LSC+SSC, EW 980), and #3 (square, SSC+SSC, EW 830) ionomers and the single #4 (pentagon, LSC, EW 1000), #5 (inverted triangle, SSC, EW 980), and #6 (diamond, SSC, EW 830) ionomers.
Figure 3.
The water uptake of the blended #1 (circle, LSC+SSC, EW 1000), #2 (triangle, LSC+SSC, EW 980), and #3 (square, SSC+SSC, EW 830) ionomers and the single #4 (pentagon, LSC, EW 1000), #5 (inverted triangle, SSC, EW 980), and #6 (diamond, SSC, EW 830) ionomers.
Figure 3.
The water uptake of the blended #1 (circle, LSC+SSC, EW 1000), #2 (triangle, LSC+SSC, EW 980), and #3 (square, SSC+SSC, EW 830) ionomers and the single #4 (pentagon, LSC, EW 1000), #5 (inverted triangle, SSC, EW 980), and #6 (diamond, SSC, EW 830) ionomers.
Figure 5.
The I-V polarization of the MEAs based on the blended #1 (red, LSC+SSC, EW 1000), #2 (green, LSC+SSC, EW 980), and #3 (blue, SSC+SSC, EW 830) and the single #4 (orange, LSC, EW 1000), #5 (yellow, SSC, EW 980), and #6 (purple, SSC, EW 830) at the operation conditions: (a) 70 °C with R.H. 100% (b) 75 °C with R.H. 100% (c) 80 °C with R.H. 50% (d) 80 °C with R.H. 75% (e) 80 °C with R.H. 100%.
Figure 5.
The I-V polarization of the MEAs based on the blended #1 (red, LSC+SSC, EW 1000), #2 (green, LSC+SSC, EW 980), and #3 (blue, SSC+SSC, EW 830) and the single #4 (orange, LSC, EW 1000), #5 (yellow, SSC, EW 980), and #6 (purple, SSC, EW 830) at the operation conditions: (a) 70 °C with R.H. 100% (b) 75 °C with R.H. 100% (c) 80 °C with R.H. 50% (d) 80 °C with R.H. 75% (e) 80 °C with R.H. 100%.
Figure 6.
The oxygen ratio-dependent limiting current density of the blended and the single ionomer-based MEAs at (a) 70 °C with R.H. 100% (b) 75 °C with R.H. 100% (c) 80 °C with R.H. 50% (d) 80 °C with R.H. 75% (e) 80 °C with R.H. 100% for the blended #1 (circle, LSC+SSC, EW 1000), #2 (triangle, LSC+SSC, EW 980), and #3 (square, SSC+SSC, EW 830) ionomer and the single #4 (pentagon, LSC, EW 1000), #5 (inverted triangle, SSC, EW 980), and #6 (diamond, SSC, EW 830) ionomer.
Figure 6.
The oxygen ratio-dependent limiting current density of the blended and the single ionomer-based MEAs at (a) 70 °C with R.H. 100% (b) 75 °C with R.H. 100% (c) 80 °C with R.H. 50% (d) 80 °C with R.H. 75% (e) 80 °C with R.H. 100% for the blended #1 (circle, LSC+SSC, EW 1000), #2 (triangle, LSC+SSC, EW 980), and #3 (square, SSC+SSC, EW 830) ionomer and the single #4 (pentagon, LSC, EW 1000), #5 (inverted triangle, SSC, EW 980), and #6 (diamond, SSC, EW 830) ionomer.
Table 1.
Ion exchange capacity of the blended and the single ionomers.
Table 1.
Ion exchange capacity of the blended and the single ionomers.
Theoretical EW of ionomers |
Measured EW |
Blended ionomer |
Single ionomer |
1000 |
1027 (#1) |
1015 (#4) |
980 |
937 (#2) |
998 (#5) |
830 |
832 (#3) |
866 (#6) |
Table 2.
The activation energy of the blended and the single ionomers calculated using Arrhenius plots.
Table 2.
The activation energy of the blended and the single ionomers calculated using Arrhenius plots.
EW of ionomers |
Activation energy (kJ/mol) |
Blended ionomer |
Single ionomer |
1000 |
12.55 (#1) |
11.04 (#4) |
980 |
12.72 (#2) |
11.09 (#5) |
830 |
10.86 (#3) |
11.84 (#6) |
Table 3.
Current density from I-V polarization curves of the blended and the single ionomer-based MEAs measured at (a) 70 °C with R.H. 100% (b) 75 °C with R.H. 100% (c) 80 °C with R.H. 50% (d) 80 °C with R.H. 75% (e) 80 °C with R.H. 100%.
Table 3.
Current density from I-V polarization curves of the blended and the single ionomer-based MEAs measured at (a) 70 °C with R.H. 100% (b) 75 °C with R.H. 100% (c) 80 °C with R.H. 50% (d) 80 °C with R.H. 75% (e) 80 °C with R.H. 100%.
Operating condition |
Current density (A/cm2) |
Blended ionomer |
Single ionomer |
EW1000 (#1) LSC+SSC |
EW980 (#2) LSC+SSC |
EW830 (#3) SSC+SSC |
EW1000 (#4) LSC |
EW980 (#5) SSC |
EW830 (#6) SSC |
70 °C R.H. 100% |
0.8 V |
0.244 |
0.244 |
0.199 |
0.266 |
0.233 |
0.155 |
0.6 V |
0.976 |
0.998 |
0.854 |
1.021 |
0.920 |
0.909 |
0.4 V |
1.309 |
1.342 |
1.253 |
1.387 |
1.286 |
1.363 |
75 °C R.H. 100% |
0.8 V |
0.222 |
0.244 |
0.222 |
0.211 |
0.222 |
0.244 |
0.6 V |
1.021 |
1.009 |
0.988 |
1.01 |
1.01 |
0.976 |
0.4 V |
1.309 |
1.353 |
1.298 |
1.387 |
1.409 |
1.364 |
80 °C R.H. 100% |
0.8 V |
0.244 |
0.255 |
0.244 |
0.155 |
0.222 |
0.244 |
0.6 V |
1.043 |
1.021 |
1.054 |
0.921 |
0.999 |
1.01 |
0.4 V |
1.353 |
1.331 |
1.364 |
1.287 |
1.398 |
1.387 |
80 °C R.H. 75% |
0.8 V |
0.144 |
0.177 |
0.144 |
0.133 |
0.133 |
0.133 |
0.6 V |
0.909 |
0.898 |
0.821 |
0.699 |
0.876 |
0.887 |
0.4 V |
1.341 |
1.253 |
1.486 |
1.109 |
1.430 |
1.386 |
80 °C R.H. 50% |
0.8 V |
0.122 |
0.122 |
0.116 |
0.122 |
0.100 |
0.111 |
0.6 V |
0.643 |
0.643 |
0.721 |
0.566 |
0.632 |
0.632 |
0.4 V |
1.131 |
1.087 |
1.264 |
0.898 |
1.153 |
1.109 |
Table 4.
The ECSAs of the blended and the single ionomer-based MEAs from CVs measured at (a) 70 °C with R.H. 100% (b) 75 °C with R.H. 100% (c) 80 °C with R.H. 50% (d) 80 °C with R.H. 75% (e) 80 °C with R.H. 100%.
Table 4.
The ECSAs of the blended and the single ionomer-based MEAs from CVs measured at (a) 70 °C with R.H. 100% (b) 75 °C with R.H. 100% (c) 80 °C with R.H. 50% (d) 80 °C with R.H. 75% (e) 80 °C with R.H. 100%.
Operating condition |
ECSA (m2/gpt) |
Blended ionomer |
Single ionomer |
EW1000 (#1) LSC+SSC |
EW980 (#2) LSC+SSC |
EW830 (#3) SSC+SSC |
EW1000 (#4) LSC |
EW980 (#5) SSC |
EW830 (#6) SSC |
70 °C, R.H. 100% |
60.60 |
69.95 |
55.02 |
75.70 |
65.11 |
58.08 |
75 °C, R.H. 100% |
90.18 |
81.09 |
96.04 |
71.08 |
73.34 |
89.28 |
80 °C, R.H. 100% |
55.94 |
65.22 |
58.37 |
47.38 |
61.53 |
56.95 |
80 °C, R.H. 75% |
48.22 |
57.50 |
44.47 |
36.37 |
46.61 |
39.97 |
80 °C, R.H. 50% |
32.95 |
39.98 |
37.06 |
32.63 |
22.75 |
36.30 |
Table 5.
The decreasing rates of limiting current density of the blended and the single ionomer-based MEAs at (a) 70 °C with R.H. 100% (b) 75 °C with R.H. 100% (c) 80 °C with R.H. 50% (d) 80 °C with R.H. 75% (e) 80 °C with R.H. 100%.
Table 5.
The decreasing rates of limiting current density of the blended and the single ionomer-based MEAs at (a) 70 °C with R.H. 100% (b) 75 °C with R.H. 100% (c) 80 °C with R.H. 50% (d) 80 °C with R.H. 75% (e) 80 °C with R.H. 100%.
Operating condition |
Decrease rate of limiting current density (%) |
Blended ionomer |
Single ionomer |
EW1000 (#1) LSC+SSC |
EW980 (#2) LSC+SSC |
EW830 (#3) SSC+SSC |
EW1000 (#4) LSC |
EW980 (#5) SSC |
EW830 (#6) SSC |
70 ℃, R.H. 100% |
55.2 |
49.1 |
55.8 |
56.3 |
58.2 |
57.8 |
75 ℃, R.H. 100% |
53.0 |
54.3 |
53.2 |
56.7 |
55.7 |
58.4 |
80 ℃, R.H. 100% |
52.6 |
49.4 |
50.2 |
53.7 |
52.2 |
53.5 |
80 ℃, R.H. 75% |
49.6 |
50.2 |
48.8 |
49.7 |
52.6 |
51.8 |
80 ℃, R.H. 50% |
48.4 |
45.2 |
44.1 |
53.4 |
47.1 |
47.8 |