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All-solid Sn/Pb halide perovskite sensitized solar cells Yuhei Ogomi I, Atsushi Morital, Shota Tsukamotol Takahiro Saithol, Naotaka Fujikawal, Shen Qing2,4,
Taro Toyoda2,4, Kenji Yoshino3,4, Shyam S. Pandeyl, Tingli Mal, and Shuzi Hayase*I,4
I Graduate School of Life Science and Systems Engineering, Kyushu Institute of Technology, 2-4 Hibikino,
Wakamatsu-ku, Kitakyushu, Fukuoka 808-0196, Japan 2 Graduate School of Informatics and Engineering, University of Electro-Communications, 1-5-1
Chofugaoka, Chofu, Tokyo 182-8585, Japan. 3 Department of Electrical and Electronic Engineering, University of Miyazaki, 1-1, Gakuen Kibanadai
Nishi, Miyazaki, 889-2192, Japan 4CREST, Japan Science and Technology Agency (JST), 4-1-8 Honcho Kawaguchi, Saitama 332-0012,
Japan
Abstract - We have succeeded in harvesting energy in near infrared region (NIR) by using air stable Sn doped metal halide perovskite materials. The edge of the incident photon to current efficiency (IPCE) edge reached 1060 nm. 4.18 % efficiency is reported. The photovoltaic performance was compared with Pb halide perovskite solar cell with 14.4% efficiency, leading to the conclusion that the low FF and Voc are associated with low shunt resistance (Rsh). One of the methods to suppress the charge recombination will be reported, which includes passivation of porous titania surface states with aminoacid HI salts. The relationship among the surface states of titaniaor alumina, and crystallinity of the perovskites induced by surface passivation molecules, and photovoltaic performances are discussed.
Index Terms - perovskite, passivation, crystal grow, Sn, dye sensitized solar cell
I. INTRODUCTION
All-solid state solar cells consisting of perovskite have
recently attracted interest because of the high efficiency
reaching 12_16%.1.9 Perovskite solar cells consist of compact
titania layer, porous metal oxide layer, perovskite layer and p
type organic semi-conductor layer. When porous titania layer
was used, electrons are collected by the porous titania layer.
N.G. Park and his coworkers have reported perovskite solar
cells with 9.7% efficiency, where, the cell is composed of
Ti02/ CH3NH3PbI3 /(2,2',7,7'- Tetrakis[N,N-di (4-methoxy
phenyl) amino] - 9,9'- spirobifluorene) (SPIRO)? The
efficiency has further increased to 14.14 % (Certified
efficiency) by using two-step perovskite fabrication process.4
When the perovskite layer was fabricated on porous alumina
layer, electrons are collected by the perovskite layer itself
covering the porous alumina surface. 5,6 Perovskite solar cells
with flat heterojunction structure prepared by a co-evaporation
process under vacuum have been reported and the efficiency
reached 15.4 %.9 However, light absorption spectrum edge for
Pb halide solar cells is limited to 800 nm. It has been reported
that Sn halide perovskites have the light absorption up to
1200nm.JO·J6 However, it has been reported that CH3NH3SnI3
is not stable for handling in air. We noticed that the Sn halide
978-1-4799-4398-2/14/$31.00 ©2014 IEEE
P3HT
PorousTi02 and CH3NH3Sn/PbI3
Fig. 1. Structure of Cocktail Sn/Pb perovskite solar cells
perovskite became stable in air when Pb halide perovskite was
added. This prompted us to evaluate cocktail SnlPb
perovskite solar cells.
II. PREP ARA TTON OF COCKTAIL PEROVSKITE SOLAR CELLS
Figure 1 shows the structure of cocktail SnlPb perovskite
solar cells which consists of FTO glass/ compact Ti02
layer/porous Ti02 layer containing CH3NH3SnxPb(l'
x)I3/P3HT/AgiAu. In this report, CH3NH3SnxPb(l.x)I3 is
P3HT in Chlorobenzene solution (spin coating)
I Ag(lOnm)/Au(40nm) (Thermal evaporation) I
In air '-------------'
Fig. 2. Procedure of cell preparation
0151
abbreviated as MASnPb(x/(1-x)).
The perovskite solar cells were prepared in the procedure
shown in Figure 2. The perovskite layer was prepared under
N2 atmosphere. SnI2, PbI2, and methylammonium iodide
(MA) were mixed and spincoated on the porous titania layer
(one pot process). P3HT polymers were employed as the hole
transporting layer instead of SPIRO. Photovoltaic
performances were evaluated in air without encapsulation.
III. PHOTOVOL T AlC PERFORMANCES
Figure 3 shows the stability of perovskite layers in air.
900nm absorption of MASn(1/0) decreased rapidly in air and
became zero in 60 min. However, MASnPb(0.5/0.5) survived
1.1 1.0
11 0.9 ..: 0.8 ." 0.7 � 0.6 � O.S 50.4 Z 0.3
0.2 0.1 0.0
A=900nm
o 10 20 30 40 SO 60
Time [min] Fig. 3. Stability of perovskite layers in air
in air and was able to handle in air.
Figure 4 shows absorption spectra for MASnPb(x/(l-x)).
The spectrum edge shifted from 800 nm to 1200 nm when x
was changed from 0 to 1, demonstrated that the edge (band
gap) is tunable by changing the x. MASnPb(0.5/0.5) have
1050 nm edge and was able to be handled in air. 2 e in XRD changed from 14.45 to 15.56 gradually when x increased from
o to 1, which shows that the repeating unit distance decreases
with the increase in x. This reflects that Pb ion (ionic radius:
1.3-1.5 A) is replaced partially with Sn ion (ionic radius: 0.93
A). XPS peaks for Sn 3d shifted from 492.33 eV to 492.91 eV
(higher binding energy) when x was changed from 0.3 to 1.0,
suggesting that Sn4+ content may increase with higher x valuel7.
Sn:Pb=O.7/0.3 Sn:Pb=O.5/0.5 Sn:Pb=O.9/0.1
_________ Sn:Pb=O.3/0.7 1.2 ,
I
1.0
0.$
0.6
0.'
0.2
Sn:Pb=O/l
-C1t .... '''H,Pbl, -C1£ .... '"H,SIro,Pb...J, - CI[r'14,s.o,Pbt�, - O£,'''H,s.o,'''-joI,
O[,'''H,s.oA1I, _C1r .... '"H,SaI,
0.0 '---�� -'-.......,,-----' 400 ,SOO (i(IO iOO 3(10 9(IC) 1000 1100 1200 UOO
Waveleoglh (nm)
Sn:Pb=l/O
fOCI 1000 llOO 1* IlOO \\"' ..... '-
Fig. 4 Absorption spectra of MASnPb(X/(l-X)
978-1-4799-4398-2/14/$31.00 ©2014 IEEE
ME � g .� = ..
"0
': .. ... ... = u
150
100
50
0
-50
-100
-150
. . . . Sn:Pb=O.7 /0.3 "
. Sn:Pb=0.5/0.5 .
' . Sn:Pb=0.9/0.1
Sn:Pb=0.3/:·
;·'·...
' •
• \ - ••••••
e_e_.. ••••• _-�
CH3NH3Pb'3 CH3NH3S''o,Pb07'3 CH3NH3Sno,Pbo,13 CH3NH3Sno.7Pb0.3'3 CH3NH3Sno9Pbo"3 CH3NH3Sn'3
Sn:Pb=O/l �. .... ;-..� .�� ...
.. �
.. ':
..
�
. ..
'
�
'. . . . . . . .
.. '.
I:: . e::;
-0.5 -0.4 -0.3 -0.2 -0.1 0.0 0.1 0.2 0.3 0.4 0.5 Voltage (V)
Fig. 5. Dark current for MASnPb{x/{l-x)) solar cells
Figure 5 shows dark current for various MASnPb(x/(1-x).
Cocktail perovskite solar cells with higher x (1,0.9, and 0.7)
did not show any diode properties, which is consistent to the
speculation that Sn4+ content of cocktail perovskite with high x
value is higher and conductivity increased with an increase in
the Sn4+ content'6. It has been reported that Sn4+ is associated
with the conductivity. Diode performance was improved when
x is lower than X:0.5.
W U !!:
0.9
0.8
0.7
0.6
0.5 A
0.4
0.3
0.2
0.1
0.0 +----r--..----r--.---+---.-�__I 300 400 500 600 700 800 900 1000 1100
Wavelength [nm]
Fig. 6. Comparison of IPCE between
MASnPb(0.5/0.5)(A) and MASnPb(O/l)(B)
IPCE of MASnPb(0.5/0.5) covers from 300 nm to 1060 nm
where the wavelength region longer than 800 nm was not
photoactive for conventional MASnPb(OIl), demonstrating
that the cocktail perovskite solar cells are useful for
photoconversion in the area of NIR. Figure 7 shows the
photovoltaic performance and the details are summarized in
Table l. Jsc of both solar cells were almost the same and
about 20 mA/cm2
was observed. However, Voc and FF (0.42
V and 0.50) were lower than those of MASnPb(OIl) (0.98 V,
0.69). Series resistances (Rs) of both solar cells were almost
the same, around 6 ncm, however, large difference was
observed in shunt resistance (Rsh). The former (168.2 ncm)
was extremely low, compared with the latter (1873.6 Ocm).
This suggests that charge recombination frequently occur at
some interfaces, which have to be suppressed for further
0152
25.0 120.0 u
115.0 >- 10.0 .... ·iii :ii 5.0
" .... c 0.0 f ... <3 -5.0
-10.0 -0.2 0.0 0.2 0.4 0.6 Voltage M
0.8 1.0
Fig. 7. Comparison of IV curves between
MASnPb(O.5jO.5)(A) and MASnPb(Ojl)(B)
improvements.
HOMO of P3HT is at -4.67 from vacuum level which is
much lower than that of SPIRO (-5.22). The difference
between Ti02 conduction band (-4.0) and P3HT HOMO (-
4.67) is 0.67 V which corresponds to the expected maximum
Voc for MASnPb(0.5/0.5). The difference between the
expected 0.67 V and the experimentally obtained Voc (0.42 V)
is 0.25 V. The Voc loss is large compared with other solar
cells. For improving the Voc further, to employ hole
transporting materials with deep HOMO and to suppress
charge recombination are needed.
TABLE 1
COMPARION of IV CURVES BETWEEN MASNPB(0.5/0.5)(A) AND
MASNPB(O/l)(B)
Jse Voe Efficiency Rs Rsh FF
[mA/em') [V) [%) [Oem') [Oem')
A 20.04 0.42 0.50 4.18 6.00 168.2
B 21.15 0.98 0.69 14.28 6.21 1873.6
III. SUPPRESSION OF CHARGE RECOMBINATION
In conventional dye-sensitized solar cells, organic dyes are
bonded onto porous titania surface with anchoring groups such
as carboxylic moieties '. Since swift electron injection is
realized by bonding these dye molecules to titania surfaces, the
selections of these anchor groups and the substitution positions
is a key issue for developing high efficiency DSCs '. There
have been no discussions on how the perovskite is bonded to
the porous titania surface. In addition, crystal growth of
perovskite should be influenced by the surface condition of
porous titania. This prompted us to consider the interface
structure between them. We inserted amino acid HI salts as an
anchoring group between the porous titania or alumina and the
978-1-4799-4398-2/14/$31.00 ©2014 )EEE
perovskite layer. The relationship between the interface
structure and the photovoltaic performance was discussed.
Porous Ti02
Fig. 8. Structure of titania anode where aminoacid HI salts were inserted between perovskite and porous titania
Figure 8 shows the schematic diagram of the anode structure
we fabricated. Three amino acid HI salts (alanine HI salt
(AHI salt), �-glycine HI salt (GHI salt), y-amino butyric acid
(GABAHI salt)) (Figure 9) were employed as the anchoring
group. The adsorption of these amino acid IH salts onto titania
surface was confirmed by infrared (lR) spectroscopy.
CH3NH3PbI3 (PEROVI3) has a perovskite structure as shown
in Figure 1 and some of CH3NH3 + groups facing on titania
were replaced by NH3 + moiety of the amino acid HI salt grown
from the surface of the porous titania surface. The bonding
length between the perovskite and titania surface was varied
from one methylene of alanine HI (AHI salt) salt to three
methylene of glycine HI salt (GABAHI salt).
Figure 10 summarizes the photovoltaic performances of
perovskite sensitized solar cells (PEROV-S-DSC) with and
without amino acid HI salt-anchor-groups. When alanine HI
salt (AHI salts), glycine HI salt (GHI salts), or GABA HI salts
was inserted between the perovskite (PEROVI3) and porous
titania, the efficiency increased in the following order; GHI
salt<AHI salt < GABAHI salt, leading to the conclusion that
longer methylene group is effective for increasing the
efficiency.
Figure 11 shows the photovoltaic performances for Pb
perovskite solar cells
prepared on porous HJ�r""COOH alumina. In these HI glycine solar cells, electrons
H N�COOH J Hill-alanine
are collected through
perovskite layers
fabricated on porous
alumina layer
(insulator).
(3-aminopropanoic acid)
Pb perovskite solar
cell efficiency
increased as follows:
GHI salt<AHI salt <
GABAHI salt, which
was the same trend as
HIGABA
(y-aminobutyric acid )
Fig.9. Structure of amino acid HI
0153
• without • amino acid
• • * GABA t
Alanine •
• •
Glycine
11.0 20.0 10.0 I 18.0 9.0 without 16.0
� 8.0 amino acid � 14.0 GA8A * � 7.0 • t � 12.0 � 6.0 • � c: • oct 10.0 .. 5.0 • .§. 8.0 'u IS 4.0
Alanine • lil 6.0 3.0 • 2.0 4.0 Glycine 1.0 2.0
0.0 0.0 1.0 0.7
•
I a I • GABA *
• �
without • aminoaci
Alanine Glycine
0.9 • • I 0.6 0.8 • 0.7 Alanine without 0.5
Glycine amino acid 2: 0.6 0.4 u 0.5 ... ... g 0.4 0.3
0.3 0.2 0.2 0.1 0.1 0.0 0.0 L-______ _
Fig. 10. Photovoltaic performances of Pb perovskite sensitized solar
cells with amino acid HI salt anchoring layer
5.0 12.0 Alanin Q GABA
Alanin 10.0 0 4.0 0 GABA 0
*' Glycine 0 'N8.0 � �3.0 0 E 0 0 .:i 6.0 � c: 0 Glycine ..
E :g 2.0 without a 'i4.0 without a is minoacid 0 amino acid 0 0 0 1.0 a 2.0 a b �
'" a '" a
0.0 0.0 0.7 9 Q e 0.8 � GABA 0.6 8 a
� a
GABA without Alanine 0.5 9 Q 0.6 amino acid Glycine
without 0 2: ... 0.4 minoacid Alanine g 0.4 ... 0.3 Glycine
0.2 0.2 0.1 0.0 0.0
Fig. 1 1. Photovoltaic performances of Pb perovskite solar cells
fabricated on porous alumina. Aminoacid HI salts were inserted
between perovskite and porous alumina.
that of Pb perovskite solar cells fabricated on porous titania.
This suggests that perovskite crystal grows better on GABA
passivation surface than on bare porous alumina. Long alkyl
groups may assist better alignment of amino acid -NH3 +r groups from which perovskite layer grows.
The effect of GABA HI salt-anchor- group is summarized as
follows.
1. Passivation of surface trap of porous titania layers working
as charge carrier layer.
2. Increase in surface coverage area and uniform crystal
growth of perovskite materials on porous metal oxide layer.
3. Retardation of charge recombination by alkyl groups.
Electron injection from perovikite to titania actually occurs,
however, we are not able to exclude the possibility that
perovskite are also involved in the carrier diffusions, as far as
cells fabricated under our experimental conditions are
concerned.
978-1-4799-4398-2/14/$31.00 ©2014 IEEE
Perovskite
Defect
With GABA passivation Without GABA passivation
Fig. 12. Difference in perovskite layer fabricated on alumina
IV. CONCLUSION
Cocktail SnPb perovskite solar cells were proved to harvest
the light up to lO60 nm, maintaining the stability in air. The
band edge is tunable, which is effective for improving
efficiency of single cells and tandem cells. In order to
improve the efficiency, Rsh has to increase and suppress the
charge recombination. It was proves that surface passivation of
alumina and porous titania with aminoacid HI salts were
effective for the suppression of charge recombination as well
as crystal growth of perovskite layers.
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