hydrogen storage in light complex hydrideshj/h-school08/lecturenotes/sartori.pdf · sartori...
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Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Sabrina SartoriPhysics Department, Institute for Energy Technology,
Kjeller, Norway
Hydrogen storage in light
complex hydrides
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Solid material for hydrogen storage
Source: DoE 2007*
• Metal and complex hydrides
• Chemical hydrides
• Nanoporousstructures
*The goals are changing and also the achievements in high-temp PEM etc (meaning higher temperatures for H-desorption will be acceptable).
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
M(s) + x/2 H2 MHx(s) + energy
Storage as hydrides
Interstitial metal hydride Complex hydride
AlH4-
Li
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
• Alanates (Al): NaAlH4, LiAlH4, KAlH4,
Mg(AlH4)2, mixed alanates (Na2LiAlH6, K2LiAlH6) ;- Structures;- Undoped alanates;- Effect of additives;- Dehydrogenation/rehydrogenation
• Amides/imides (N)- Structures;- Dehydrogenation/rehydrogenation
• Borohydrides (B)- Structures;- Dehydrogenation/rehydrogenation- mixed systems
Content
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
� 2010: ≥≥≥≥ 6 wt%� 2015: ≥≥≥≥ 9 wt%
The Challenge: Goals for hydrogen storage
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Status of hydrogen storage systems
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Complex hydrides promising candidates
� > 5 wt% hydrogen:� LiAlH4: 10.6 wt%� NaAlH4: 7.5 wt%� Mg(AlH4)2: 9.3 wt%� LiNH2/Li2NH reactions (11.5 wt%)� LiBH4 (18.5 wt%), NaBH4 (10.7 wt%)� Ammonia-Borane systems: e.g. H3NBH3 (19.6 wt%)
� Why not used: problems of thermodynamic and kinetics. Not reversible at moderate conditions. Complicated desorption of H2
� Additives (Bogdanović et al., 1997):
� Reversible (NaAlH4 with Ti-additives). � Reduced desorption temperature.
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
High-energy ball-milling…
…brings about a broad variety of defects
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Al
NaD
Using neutrons to ”see” hydrogen
In contrast to X-ray, neutrons are scattered by the nuclei of the atoms. X-ray data tends to give erroneously short metal-hydrogen distances and incertainties in determination of hydrogen coordinates
JEEP-II
Powder neutron diffraction (PND)
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Synchrotron powder X-ray diffraction
Swiss-Norwegian Beamline (BM01)
Dehydrogenation reaction studied by in situ SR-XRD
Sample(capillary)
Heater
Evacuation
Heating under evacuation1˚C/min.
Diffraction data collectedevery 2min
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Structural characteristics
AlH4-
Li
Mn+(AlH4)-n
• Anions: AlH4-, AlH6
3-, BH4-,
MgH3- etc. Covalent bonded.
• Metal ions: Alkaline, alkaline earth or 3d elements. Ionic bonded.
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
NaAlD4
Hauback, Brinks, Jensen, Murphy, Maeland (2003)
� AlD4– tetrahedra
� Al-D: 1.626 Å (at 295 K).� Na+: surrounded by 8 D atoms
from 8 different AlD4– :
� Na-D: 2.439, 2.431 Å.
AlD4
Na
LiAlD4
Combined neutron and X-ray diffraction
• AlD4 – tetrahedra connected
via Li.• Li+ : surrounded by a trigonal
bipyramid of 5 D from 5 different AlD4
– :• Li-D: 1.831 – 1.978 Å.• Al-D: 1.604 – 1.637 Å
Hauback, Brinks, Fjellvåg (2002)
AlD4
Li
KAlD4
� AlD4– isolated tetrahedra
� Al-D: 1.618 Å (at 295 K).� K+: surrounded by ten D
atoms:� K-D: 2.596 Å (at 295 K).
Hauback, Brinks, et al. (2005)
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Li3AlD6
Brinks, Hauback (2003)
Li
AlD63-
• Isolated octahedra AlD63–:
• Al-D: 1.754 and 1.734 Å. • Li: 6-coordinated:
• Li-D: 1.892-2.120 Å.
AlD63-
Li
The structure can be described as a distorted bcc structure of AlD6
3–
units with all tetrahedral sites filled with Li
Each Li atom is connected to two corners and two edges of AlD6
3–
octahedra with in total six D atoms in the coordination sphere
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Mg(AlH4)2• Isolated AlH4
- tetrahedra.• Mg surrounded by 6 H.• MgH6 octahedra share one
corner with each of six AlH4
- tetrahedra.• Sheet like structure along
c-axis.• Al – H: 1.561, 1.671 Å.
Fichtner et al. (2003)Fossdal, Brinks, Fichtner, Hauback (2005)
Sheets interconnected by van der Waals forces
• Mg(AlH4)2: Solvent-free and fast synthesis
• Details of thermal and isothermal decomposition of Mg(AlH4 )2
• Scale-up strategies promising, but reversibility not sufficient
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Mixed alanates Na2LiAlD6 and K2NaAlH6
• Synthesized from NaAlD4+ LiAlD4
• Synthesized by ball milling KH+NaAlH4.
• SR-PXD + PND• Both Fm-3m.• Different size of
octahedron AlD6- and
LiD6-
• fcc geometry of AlD6
• K in tetrahedral sites• Na in octahedral sites
Brinks, Hauback, Jensen, Zidan (2005)Sørby, Brinks, Fossdal, Thorshaug, Hauback (2006)
AlD6
LiD6
Na
Na2LiAlD6 K2NaAlH6
a = 8.118(1) Åa = 7.3848(1) Å
Isostructural to Na2LiAlD6
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Dehydrogenation and
rehydrogenation- Undoped alanates
Desorption ALANATES, e.g. NaAlH4 ( 7.5 wt%):3 NaAlH4 →→→→ Na3 AlH6 + 2 Al + 3 H2 3.7w% 180-230°°°°C
Na3 AlH6 →→→→ 3 NaH + Al + 3/2 H2 1.9wt% 230-250°°°°C
NaH →→→→ Na + ½H2 1.9wt% 425°°°°C
The reaction temperatures depend strongly on the heating rate
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Study of dehydrogenation LiAlD4 - In-situ PXD
Brinks, Hauback, Fjellvåg, Norby (2003)
2θ
220°C
160°C
130°C
LiAlD4
Li3AlD6+Al
LiD +Al
0.5 °C/min.. T
•3LiAlH4 = Li3AlH6 + 2Al + 3H2 150ºC (R1) 5.3 wt%
•Li3AlH6 = 3LiH + Al + 3/2H2 210ºC (R2) 2.6 wt%
•3LiH +3Al= 3LiAl + 3/2H2 350ºC (R3) 2.6 wt%
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Thermolysis of KAlH4 releases hydrogen and it consist on three steps of dehydrogenation,
3KAlH4 →→→→ K3AlH6 + 2Al + 3H2 (2.9 wt.%) at 300 ºC (1)K3AlH6 →→→→ 3KH + Al + 3/2H2 (1.4 wt.%) (2)3KH →→→→ 3K + 3/2H2 (1.4 wt.%) (3)
In step 1, KAlH4 decomposes to K3AlH6, followed by decomposition to KH in step 2. KAlH4 was found to be reversible without a catalyst. In situ diffraction investigations of KAlH4 powders published by Mamathaet al. J. Alloys Comp. (2006) revealed the appearance of unidentified phases during decomposition.
KAlH4
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Mg(AlH4)2 – In situ PXD
MgH2
MgH2NaCl
AlMg(AlH4)2
Fossdal, Brinks, Fichtner, Hauback (2005)
Mg(AlH4)2 → MgH2 + 2Al + 3H2 135-163 ºC (R1) 7.0 wt%
(without the involvement of AlH63-, as an intermediate phase)
MgH2 + 2Al → AlxMgy + AlaMgb + H2 270-310 ºC (R2) 2.3 wt%
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Additives in alanates
ball milling apparatus
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Effect of additives – NaAlH4 +Ti-compounds
Bogdanovic et al. (1997)
undoped
The undoped NaAlH4 sample at 160 °C delivers H2 at an almost negligible rate and, even at 200 °C, the H2 evolution takes 22-24 h until completion. In contrast samples doped with Ti(OBu)4 is completed at 160 °C within 6-8 h and at 180 and 200 °C within 2-3 and 1 h respectively
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Effect of TiCl3 in NaAlH4 (ball milled)
H2 desorptionT=125°°°°C
Bogdanovic et al. (1997); Sandrock et al. (2002); Srinivasan, Brinks, Hauback, Jensen (2004)
Multiple order-of-magnitude increases in kinetics. Decrease desorption temperatures
H2 absorptionT=125°°°°C, P=8 MPa
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Doped NaAlH4
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
PCT at 160 ºC for 6 different mol% doping level of Ti
Bogdanovic et al., (2007)
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Van’t Hoff plot
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
0
0.5
1
1.5
2
2.5
3
3.5
4
4.5
5
0 20 40 60 80 100
Cycle number
Rel
ease
d h
yd
rog
en, w
t.%
100 cycles
Improve significantly reversibility (NaAlH4). Up to 4.5 wt% cyclic H-capacity
Effect of TiCl3 in NaAlH4 (ball milled)
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
NaAlH4 + TiCl3
Solid solution
Na1-3xTixAlH4
NaAl1-xTixAlH4
Could improve kinetics in grains.
PXD: Changes in unit-cell dimension of NaAlH4
Heterogenous catalyst
Catalyzing hydrogen splitting/combination and/or diffusion of metal- containing species.
PXD: Detection of secondary Ti-containing phases.
� The effect of the additives NOT understood:� Dopant or catalyst?� Solid solution or secondary phase?
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
11.3113(3)5.0102(1)NaAlD4 + 6% TiCl4
11.3069(2)5.0090(1)NaAlD4
11.3498(2)5.0233(1)NaH+Al+2%Ti(OBu)4@ 7 cycles
11.3493(2)5.0234(1)+ 6% TiF3
11.3493(2)5.0234(1)+ 6% TiCl4
11.3481(2)5.0231(1)+ 6% TiCl3
11.3483(2)5.0232(1)NaAlH4
c (Å)a (Å)
� NaAlH4 + TiCl3/TiCl4/TiF3/Ti(OBu)4�No significant changes in unit-cell dimensions of NaAlH4
•No significant solid-solution of Ti into NaAlH4
Brinks, Jensen, Srinivasan, Hauback, Sun, Murphy (2004)
Nature of additives – NaAlH4 +Ti-compounds
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Ti-doped
Sc-doped
In comparison toTiCl3-doped NaAlH4, ScCl3and CeCl3dopants reduce hydrogenation times by a factor of 2 at high pressure and by a factor of 10 at low pressure.
Others additives NaAlH4
As TiCl3 is the best Ti-precursor compound (together with Ti-nanoparticles), trichlorides of the first-row transition metals are investigated as alternative dopants. ScCl3 results highly efficient, both with respect to storage capacity and kinetics.
Bogdanovic at al. (2006)
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Sodium Alanate
• Synthesis of NaAlD4 with improved kinetics and reversibility (4 wt% H2)
• Improved synthesis of catalyst: Ti13*6THF
• 2NaAlH4+LiH+2mol%TiF3 leads to the formation of reversible Na2LiAlH6 (2.8 wt%)
• Adjustment of the stability of complex hydrides by anion substitution (H/F). Na3AlH6-xFx less stable than Na3AlH6
Na2LiAlD6
LiD6
Na
AlD6
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
LiAlD4 with additives
� VCl3 reduces thedesorptiontemperature more efficiently
� 3TiCl3•AlCl3decomposes more LiAlD4 into Li3AlD6during ball-milling (from PXD data) 0 100 200 300 400 500
0
2
4 Milled LiAlD
4 (/10)
LiAlD4 w/ 2% VCl
3
LiAlD4 w/ 5% VCl
3
LiAlD4 w/ 2% 3TiCl
3·AlCl
3
LiAlD4 w/ 5% 3TiCl
3·AlCl
3
P/
10
-4 m
bar
T/ OC
Thermal desorption spectroscopy
Blanchard, Brinks, Hauback, Norby Mater. Sci. Eng. B (2004) 2°C/min
Three separate peaks of hydrogen desorption in agreement with the 3 decomposition steps
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
LiAlD4 with additives - In-situ SR PXD
Blanchard, Brinks, Hauback, Norby (2004)
• VCl3 and TiCl3·1/3AlCl3 reduce desorption temperature by 60 and 50 °C respectively .
• Amount and type of additive important for the decomposition.
2 % VCl3
Heating rate 1 °C/min
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
TiF3 in Na2LiAlH6: thermal data
• Na2LiAlH6: (Diss enthalpy) ∆H0 = 56.4 kJ/mol H2 (more stable) • Na3AlH6: ∆H0 = 47 kJ/mol H2 (Bogdanovic 2000)Reversible decomposition, sample rehydrogenated in 1-2 h at 200 °CNa2LiAlH6 = 2NaH + LiH + Al + 3/2H2
1.90 1.95 2.00 2.05 2.10 2.15 2.20 2.25 2.30
1.0
1.5
2.0
2.5
3.0
3.5
4.0
170oC
200oC
250oC
lnP
1000/T (K-1)
TiF3 catalyst
Fossdal, Brinks, Hauback (2005)
van’t Hoff plotPCT data
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
K2NaAlH6: Stability
• Reaction reversible
• Very stable• Fast desorption
kinetics (60 min at 325°C and 90 min at 280°C)
1.66 1.68 1.70 1.72 1.74 1.76 1.78 1.80 1.82
-3.4
-3.2
-3.0
-2.8
-2.6
-2.4
-2.2
-2.0
-1.8
-1.6325ºC (170 mbar)
280ºC
K2NaAlH
6
∆Hº = 98.2 kJ/mol-H2
∆Sº = 149.9 J/K mol-H2
ln p
1000/T (K-1)
2 3 4 5 6
0.1
1
10
p (
bar
)
H / FU
Sørby, Brinks, Hauback (2006)
+ 1mol% TiF3
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Amides - Structures
LiNH2
Mg(NH2)2
Li4BN3H10
Mechanical milling of LiNH2 and LiBH4in varying combination ratio
LiND2, Mg(ND2)2 and Li2ND(H) can be described as (pseudo-)fcc packing of amide/imide anions with cations in tetrahedral sites. Pure, well-crystallineMgND is hard to obtain from decomposition of Mg(ND2)2.
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
200 °C (better with TiCl3 )
320 °C
But competitive reaction: Li-amide decomposes in 2LiNH2 Li2NH + NH3Ammonia depletes one of the reactants and diminishes the hydrogen absorption capacity
Li-amide/imide systems
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
The Li-amide/imide – systems:
- LiNH2 + LiH dehydrogenation begins at approx. 277 ˚C (10 ˚C/min under Ar);
- Increasing Mg concentration, the temp. is decreased to c.a. 100 ˚C ;
- Mg(NH2)2 + 4LiH n=4, the main weight loss below 230 ˚C.
New systems:
Partial Mg-substitution and Mg-amide/imides.
•Amides of alkali or alkali-earth metals, e.g. LiNH2, Mg(NH2)2, Ca(NH2)2, react with metal hydrides to release hydrogen. • Among several combinations, reactions of Mg(NH2)2 with LiH have an advantage of providing a high capacity in wt%. However, the reaction mechanism is still not clear.
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
3Mg(NH2)2 + 8LiH 4Li2NH + Mg3N2 + 8H2
Reaction between Mg(NH2)2 and LiH in
different ratios
(n=8/3; 6.9 wt% Tdes > 400 ˚̊̊̊C) [2]
Mg(NH2)2 + 2LiH Li2Mg(NH)2 + 2H2 (n=2; 5.6 wt%
Tdes > 200 ˚̊̊̊C) [1]
[1] Xiong et al., Adv. Mater., 16 (2004) 1522. [2] Leng et al., J. Phys Chem B, 108 (2004) 8763. [3] Y. Nakamori et al., J. Alloys Compd., 370 (2004) 271.
3Mg(NH2)2 + 12LiH 4LiN3 + Mg3N2 + 12H2 (n= 4; 9.1 wt%
Tdes > 500 ˚̊̊̊C) [3]-What is an intermediate phase for each?
-Depends on the [Mg]/[Li] ratio or not ?
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Reports for the 1:2 (n=2) systemMg(NH2)2 + 2LiH �� Li2MgN2H3.2 + 1.4H2
Li2MgN2H3.2 �� Li2Mg(NH)2 + 0.6H2
Rijssenbeek et al (GE, USA)[5]
From P-C itotherm and XRD
Luo et al (Sandia NL, USA)[4]
[4] Luo et al, J. Alloys Compd., 407 (2006) 274.
[5] Rijssenbeek et al , MH2006
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Sample preparation
3Mg +8LiNH2: ball-milled,
dehydrogenated at 250 ˚C in vac
and rehydrogenated at 200 ˚C, 10 MPa H2
[Sample I]
3Mg(NH2)2 + 8LiH: ball-milled in 1 MPaH2 for 2h
[Sample II]
Synthesized from 3Mg +8LiND2 in a similar process to Sample II
A Li-Mg-N-D phase prepared by dehydrogenated at 200˚C in vac for
8h
a mixture of Mg(NH2)2 and LiH (+ Li-Mg-N-H) [1]
[Sample III, Deuterated sample]
[1] Okamoto et al. J.Alloys Compd.
Fully hydrogenated
Partly dehydrogenated
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
In situ SR-PXD for Sample I (prepared by milling Mg(NH2)2 and LiH)
10 20 30 402θ / deg
0
5000
10000
15000
20000
25000
Inte
nsity
/ a.
u.
Amorphousphase
LiH
Li2O MgO
New phase
200˚̊̊̊C
240˚̊̊̊C
100˚̊̊̊C
140˚̊̊̊C
Li2O MgO
The patterns of the new phase from 180 ˚̊̊̊C to 240 ˚̊̊̊C
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
In situ SR-PXD for Sample II(prepared from Mg and LiNH2)
Li2O MgO
Mg(NH2)2
LiH
Li-Mg-N-H
110˚̊̊̊C
Inte
nsity
/ a.
u.
0
5000
10000
15000
20000
5 10 15 20 25 30
2 θ / deg
New phase
210˚̊̊̊C
290˚̊̊̊C
150˚̊̊̊C
250˚̊̊̊C
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Mg(NH2)2 + 2LiH Li2Mg (NH)2 + 2H2
1 : 2 ratio
3 : 8 ratio
3Mg(NH2)2 + 8LiH 3Li(2+x)MgN2H(2-x) + (2-3x) LiH + 3(2+x)H2
X depends on the condition0 x 2/3< ~<
LiH rich
Investigate by Chen, Luo et al., Zhao et al.
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
SR-PXD
Structure of the new intermediate phaseRefinement combined PND and SR-PXD
x~0.6 forLi(2+x)MgN2D(2-x)
PND
Li rich and D poor imide
Primitive cubica = 5.0246(2) Å
Li2.6MgN2D1.4
Li
Li or Mg
N
Mg
D
Rwp = 7.29%
Rwp = 10.4%
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
PCI: Mg(NH2)2 + nLiH (n=2, 8/3, 4)
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Schematic view of the
reaction process
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
2LiNH2 +MgH2
Thermodynamic characterization
Luo (2006)
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Borohydrides
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
LiBH4
• LiBH4 = LiH + B + 3/2 H2 (13.9 wt%)• Peq = 1 bar @ 410°C• Slow kinetics < 600°C
• NaBH4 and KBH4 more stable (670/830°C)
• LiBH4 “destabilized” by stabilizing the products• LiBH4 + ½ Mg = LiH + ½ MgB2 + 3/2 H2
• LiBH4 + ½ MgH2 = LiH + ½ MgB2 + 5/2 H2
• Cycled at 330°C • TiCl3 used as catalyst
J.J. Vajo, S.L. Skeith J. Phys. Chem. B 2005
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Low- and high-temperature
structures of LiBH4
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Dehydrogenation reactions
M(BH4) MgH + B + 3/2H2
A(BH4) AB + 2H2
M(BH4)2 MH2 + 2B + 3H2
M(BH4)2 MB2 + 4H2
M(BH4)2 2/3MH2 + 1/3MB6 + 10/3H2
Alkali metal borohydrides:
Alkaline earth borohydrides:
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Thermal desorption from LiBH4
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Ca(BH4)2
Riktor (2007)
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Mg(BH4)2
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Mixed systems MgH2 - LiBH4 for
changing the stability
Bösenberg, Acta Materialia (2007)
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Upscaling of Solid Storage Tank
8 kg alanate Pilot tank (currently manufactured)
Length: 129 cm, Diameter: 34 cm. Capacity: 0.4 kg H2
Design and development of operational prototype solid storage tanksLaboratory tank for 0.5 kg of alanate
Length: 40 cm / Diameter: 6 cm Capacity: 20 g H2
0 10 20 30 40 50 600
1
2
3
4
5
simple preparation from NaH/Alwith TiCl
4, 125°C
100 bar (STORHY)
preparation from NaAlH
4
with Ti-nanoclusters, 100°C, 100 bar(Fichtner et al.)
H2-c
once
ntra
tion
[wt.%
]
Time [min.]
preparation from NaAlH
4 with TiCl
3, 125°C, 79-88 bar
(Sandrock et al.)
2nd absorption
Evaluation of low cost (< 1 Euro/kg) production routes for complex hydrides using catalysed NaAlH4 as model material
Up-scaling to kg amounts demonstrated
Concept for upscaling of material production processes
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Safety experiments
t=0 ms
t=30 ms
t=320 ms
Ti doped NaAlH4High speed images at different times are shown on the left, the corresponding infrared images are shown on the right.
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
Estimation for system capacities in different
hydrogen storage systemsSolid materials:• Good safety aspect;• High volumetric density;• Other projects such as
NessHy/NanoHy/FlyHy learned a lot from StorHy work and indicate possibilities in improvement also in gravimetric densities
•Porosity of the bed: 20 % (compressing the powder)•Maximum operating pressure: 50 bars•Maximum temperature : 215 °C •Capacities of 0.0356 kg/L
Improved tank ?
Actual• Gravimetric capacity of the material: 4 wt%• Material density: 1270 kg/m3.• Porosity of the bed: 53 %• Maximum temperature: 300 °C• Heat transfer coefficient: 0.55 W/mK • Operating pressure: 100 bar, design pressure 150 bar.• Capacities of 0.0214 kg/L
Vision
Sartori Sabrina, Summer School on Materials for the Hydrogen Society, Reykjavik, June 19-23, 2008
�At present, no solid storage material fulfils the major targets for automotive applications;
�Up to now, storage densities of ~2 wt.% are achievable on system level with complex hydrides on alanate basis (capacity of the material 4 wt%);
�Further research for novel storage materials with improved storage densities, kinetics and thermodynamic behaviour as well as for advanced system components, e.g. heat exchanger, is still required;
�For on-board storage in fuel -cell-driven vehicles, the hydrogen in thealanates needs to be reversibly charged and discharged, which is only possible for the pure system under extreme conditions. To make the material reversible under practical conditions, it has to be added with a catalyst. Still not understood the effect of additives;
�For technical applications is not acceptable that after low-pressurerehydrogenation, the system is not rehydrogenated as quickly as prior (system without cycle stability);
�High charging rates under low pressures are still a challenge on the way to a practicable solid-state hydrogen- storage material for fuel-cell-powered cars.
Conclusion