new membranes for aqueous batteries -...
TRANSCRIPT
New Membranes for Aqueous BatteriesMichael A. Hickner
Associate Professor, Corning Faculty FellowDepartment of Materials Science and EngineeringAssociate Director – Materials Research Institute
The Pennsylvania State [email protected]
Hickner Research Group @ Penn State
2Industry Sponsors
EERE Award # DE-EE0006958ARPA-E Award # DE-AR0000121
Membranes in energy applications
3Environ. Sci. Technol. Lett. 2014
ACS Appl. Mater. Interfaces 2013J. Am. Chem. Soc. 2013
Flow Batteries
Reverse Osmosis
Fuel Cells
SaltWater
ACS Macro Lett. 2016
Electrodialysis
Disabb-Miller, Hickner, et al., Macromolecules 2013.Moore, Saito, Hickner, J. Mater. Chem. 2010.
Macromolecules 2010.
Li, Hickner, et al., J. Am. Chem. Soc. 2013.Leng, C-Y Wang, Hickner, et al., J. Am. Chem. Soc. 2012.
Zha, Disabb-Miller, Tew, Hickner, J. Am. Chem. Soc. 2012.
New membranes through polymer synthesis
Wang, Hickner, Polym. Chem. 2014.Wang, Hickner, Soft Matter. 2016.
4
0.0 0.2 0.4 0.6 0.8 1.0 1.2 1.4
10-2
10-1
100
I(q
) (au
)
q(nm-1)
q
2q
3q4q
0.0 0.2 0.4 0.6 0.8 1.0 1.2 1.410-3
10-2
10-1
100
I(q) (
au)
q(nm-1)
q
2q3q
4qHickner, et al.Soft Matter. 2016.
SDAPP3, 1.8 meq g-1Nafion, 0.91 meq g-1
Kreuer, J. Membrane Sci. 2001.
--
-
-
-- -
- - - ---
-
Membrane structure and function
Fujimoto, et al. Macromolecules 2005.Hickner, et al. Polymer 2006. 6
Good capacity maintenance with small channels
Chen, Hickner, Agar, Kumbur, ACS Appl. Mater. & Int. 2013.
Increasing vanadium crossover causes large capacity fade
7
Low permeability channels
High permeability channels
Vanadium Redox Flow Battery Capacity Fade
H2 → 2 H+ + 2 e-
½ O2 + 2 e- + 2 H+ → H2OH2 + ½ O2 → H2O
Polymer electrolyte membrane fuel cellsAnion Exchange Membrane (AEM)Proton Exchange Membrane (PEM)
QA Radel®Nafion®
H2 + 2 OH- → 2 H2O + 2 e-
½ O2 + H2O + 2 e- → 2 OH-
H2 + ½ O2 → H2O
PEM fuel cells need new catalysts that are stable at pH ~ 0
AEM fuel cells need new membranes that are stable at pH ~ 9-14
8
Water battery – reversible fuel cell
9
Need a very low-cost system with no precious metals in both fuel cell and electrolyzer modes.
Can optimize the material for anion exchange or cation exchange
10
Chemical structures of polymer backbones and cations for anion exchange membranes
11
12
1. Bromination of benzylic methyl groups
2. Quaternizationwith different cationic moieties
Need to evaluate ionic group and backbone stability
Chen, D., M. A. Hickner, “Degradation of Imidazolium and Quaternary Ammonium Functionalized Poly(fluorenyl ether ketone sulfone)s for Anion Exchange Membranes,” ACS Appl. Mater. Int. 2012.
Need to evaluate ionic group and backbone stability
Lifetime of anion-conducting polymers
Leng, Chen, Mendoza, Tighe, Hickner, Wang, “Solid-State Water Electrolysis with an Alkaline Membrane,” J. Am. Chem. Soc. 2012.
QA-Radel
QA-Radel 1
QA-Radel 2
QA-Radel 3
QA-Radel
What caused the short lifetime of the ionomer?
Ionomer testing with Tokuyama membrane
14
965 970 975 980 985 990
0.00
0.02
0.04
0.06
0.08
0.10
0.12
Abso
rban
ce (a
.u.)
Wavenumber (cm-1)
0 h 2 h 4 h 6 h 8 h 10 h 11 h 21 h
AS-4
960 965 970 975 980 985
0.00
0.02
0.04
Abso
rban
ce (a
.u.)
Wavenumber (cm-1)
0 h 2 h 4 h 6 h 8 h 10 h 11 h 21 h
Thermal degradation of cast ionomers at 135˚C (low humidity)
• Ex-situ FTIR analysis of thermally degraded ionomers.• 974-977 cm-1 peak corresponds to asymmetric C-N+ stretching of QA
groups.
QA-Radel
15
Expected QA-based AEM degradation pathways
16
Stability ranking of AEMs
Nuñez, S. A. & Hickner, M. A. “Quantitative 1H NMR Analysis of Chemical Stabilities in Anion-Exchange Membranes,” ACS Macro Lett. 2013, 2, 49–52.
17
Sterics play a role in stabilizing membranes
Zhuang, et al. Acc. Chem Res. 2012 DOI: 10.1021/ar200201x
O
CH3
CH3
CH3
O100-x x
14
N
O
CH3
CH3
CH3
O100-x x
4
N
O
CH3
CH3
CH3
O100-x x
8
N
Hickner, et al. J. Am. Chem. Soc. 2013 DOI: dx.doi.org/10.1021/ja403671u18
PPO-based AEMs
O
CH3
CH3
CH3
O100-x x
14
N
O
CH3
CH3
CH3
O100-x x
4
N
O
CH3
CH3
CH3
O100-x x
8
N
Short Medium Long
C6 Dx C10 Dx C16 Dx
Li, N., Y. Leng, M. A. Hickner, C.-Y. Wang, “Highly Stable, Anion Conductive Comb-shaped Copolymers for Alkaline Fuel Cells,” J. Am. Chem. Soc. 2013, 135 (27), 10124–10133.
C denotes side chain length.D denotes functionalization, e.g. 40 = 0.4 cationic groups
per repeat unit.
19
Phase separation observed with longer alkyl side chains
d-spacingC16D40 3.3 nmC10D40 2.3 nm C6D40 1.7 nm
Roughly correspond to extended side chain lengths.
No separation observed for benzyltrimethyl ammonium (BTMA) cations – as seen in other aromatic AEMs.
20
d
Good conductivity and reasonable stability with alkyl side chains
21
Fuel cell power density and stability are reasonable but more development is needed
Still work to be done to optimize the fuel cell MEA construction and operating conditions
50 °C, air, Pt catalysts
100 mA/cm2 constant current
22
20 30 40 50 60 70 8050
100
150
200
250
300
350
T (ºC)
T20NC6NC5N, IEC 2.52 T30NC6NC6, IEC 2.47 S60NC6, IEC 2.60
Wat
er u
ptak
e (w
t %)
(a)
20 30 40 50 60 70 80-40
0
40
80
120
160
200
240
T (oC)
T20NC6NC5N, IEC 2.52 D30NC6NC6, IEC 2.47 S60NC6, IEC 2.60
Swel
ling
degr
ee(%
)
(b)
Double and triple cation side chains constrain swelling with temperature increases
CH3
CH3
O
CH3
CH2
O
NBr
NBr
3m
X100-X
DxNC6NC6
CH3
CH3
O
CH3
CH2
O
NBr
4
SxNC6
X100-X
CH3
CH3
O
CH3
CH2
O100-X
NBr
NBr
n2
N Br
X
TxNC6NC5N
23
1.6 2.0 2.4 2.8 3.2 3.60
20
40
60
80
100
DF30
DF25
DF20
DF15
DF60
DF40DF20
DF30DF35
DF40
σ O
H - (m
S/cm
)
IEC (mmol/g)
TxNC6NC5N DxNC6NC6 SxNC6
OH- Conductivity with Increasing Cation NumberOverswelling decreases conductivity due to ion dilution.
24
Microscopy Confirms Structured AEMs With Addition of Side Chains
BTMA40 S60NC6
D30 T20
25
Microscopy Confirms Structured AEMs With Addition of Side Chains
26
0 200 400 600 800 1000 1200 1400 16000.0
0.2
0.4
0.6
0.8
1.0
1.2
T20NC6NC5N D30NC6NC6 S60XN6
Current density (mA/cm2)
Cell
volta
ge (V
)
0
50
100
150
200
250
300
350
400
AEMFC @ 60oC, 0.1 MPa
Pow
er d
ensi
ty ( m
W/c
m2 )
H2/O2 Fuel Cell Performance
Many demonstrations of fuel cell performance with power densities between 150-500 mW/cm2.
There appears to be an optimization barrier to obtain higher power densities.
Triple cation side chain AEMs show reasonable fuel cell performance
27
NegativePositiveV4+
V5+ V2+
V3+
H+
e2HVOOHVO 222 ++↔+ +++ ++ ↔+ 2VeV3
• Independently Tunable Power and Energy
• No Solid Reaction Indefinite Lifetime
• No Contamination due to Single Element (V)
• Fast Response• Low Energy density
Load
Stationary Application for Renewable
Smart Grid (Wind, Sun)
VRFB stores energy by employing vanadium redox reactions at two opposite electrodes that are separated by a proton ion exchange membrane.
281.7 M V in ~3.3 M H2SO4
Vanadium Redox Flow Battery (VRFB) require permselective or conductive-selective
membranes
http://global-sei.com/news/press/12/prs069_s.html
Sumitomo Electric – 200 kW CSP array and 1 MW * 5 h flow battery
29
0 20 40 60 80 100 1200.00
0.01
0.02
0.03
0.04
0.05
0.06
Pretreated N117 DI water soaked N117 S-Radel
Conc
entra
tion
of V
O2+ [M
]
Time(hrs)
Lower V-ion permeability increases the efficiency of flow batteries
Low permeability of S-Radel
Kim, S., J. Yan, B. Schwenzer, J. Zhang, L. Li, J. Liu, Z. Yang, M. A. Hickner, Electrochem. Comm. 2010.and J. Appl. Electrochem. 2011.
S-Radel – small pores
Nafion – large pores
CF2 CF2 CF CF2
OCF2 CF
CF3
O(CF2)2 SO3H
x y n
S O
O
O n
O
HO3S R
R =
H or -SO3H
SDAPP3, 1.8 meq g-1Nafion, 0.91 meq g-1
Kreuer, J. Membrane Sci. 2001.
--
-
-
-- -
- - - ---
-
Ionic pores in sulfonated polymers
Fujimoto, et al. Macromolecules 2005.Hickner, et al. Polymer 2006. 31
Small single-cycle gains add up in long-term testing
0 5 10 15 20 25 30 35 40 450.0
0.5
1.0
1.5
2.0
2.5
3.0
Capa
city
(Ah)
Cycles
S-Radel N117
• Due to higher ion selectivity of S-Radel, capacity loss per cycle of S-Radel was 6.4 mAhcycle-1, half of that of Nafion (13 mAh cycle-1).
• Lower capacity loss translates to ½ the maintenance interval for devices with S-Radelmembranes.
25 50 75 10070
75
80
85
90
95
100
Effic
ienc
y (%
)
Discharging current density (mA/cm2)
N117 Coulombic N117 Energy SRadel Coulombic SRadel Energy
32
50 cycles
activearea
25 cycles
Degradation of aromatic PEMs in VRFBsActive area cracking and failure after extended cycling.
D. Chen, M. A. Hickner, Phys. Chem. Chem. Phys. 2013. 33
Improved cycling performance with fluorinated aromatic polymers
Chen, Kim, Li, Yang, Hickner, “Stable Fluorinated Sulfonated Poly(arylene ether) Membranes for Vanadium Redox Flow Batteries,” RSC Advances 2012, 2, 8087-8094.
Sulfonated fluorinated poly(arylene ether)(SFPAE)
O O
F
F F
F F
F F
F HO3S R
n
R =
H or -SO3H
34
Low vanadium cation crossover due to Donnan exclusion
Need membranes with permselective properties for high H+
or SO42- conductivity and high Vn+ exclusion
35
Route to scale-up with commercial starting materials
36
Can widely vary the conductivity and permeability.
Transport selectivity = σ/P
Give us a handle to explore performance tradeoffs.
110016.921.6
Large-scale AEM synthesis
37
Need kg-scale AEM synthesis with m2 membrane capability
Good capacity maintenance with low IEC AEMs
Low IEC membranes are desirable for long cycle life with no electrolyte maintenance.
Chen, Hickner, Agar, Kumbur, ACS Appl. Mater. & Int. 2013.
increasing crossover
38
Must balance conductivity and crossoverHigher power densities and low capacity fade with optimized
permselective membrane
39
Optimized trade-off in conductivity and crossover
-110016.921.6
Transport selectivityσ/P
Conclusions
• Membranes offer a gateway to new energy storage and conversion devices with low cost – can see real performance improvements with optimized materials in targeted applications.
• There are lots of parameters in ionic polymers to influence ion and water transport.
block copolymers, new cationic groups, backbone polarity, crosslinking…
• There is more work to do in AEM technology especially in regards to cost and device performance.
• We need tools for targeted design of new membranes for unique flow battery chemistries.
• Teaming with polymer specialists can pay dividends!
40