Xuepeng Liuab,
Fantai Kong*a,
Zhan'ao Tanc,
Tai Chengc,
Wangchao Chenab,
Ting Yuab,
Fuling Guoa,
Jian Chena,
Jianxi Yaoc and
Songyuan Dai*ac
aKey Laboratory of Novel Thin-film Solar Cells, Institute of Applied Technology, Hefei Institutes of Physical Science, Chinese Academy of Sciences, Hefei, Anhui 230088, P. R. China. E-mail: kongfantai@163.com; Tel: +86-0551-65593222
bUniversity of Science and Technology of China, Hefei 230026, P. R. China
cBeijing Key Laboratory of Novel Thin-Film Solar Cells, North China Electric Power University, Beijing, 102206, P. R. China. E-mail: sydai@ncepu.edu.cn; Tel: +86-010-61772268
First published on 7th September 2016
Two simple small-molecular arylamine derivatives 4-methoxy-N-(4-methoxyphenyl)-N-(4-(4,4,5,5-tetramethyl-1,3,2-dioxaborolan-2-yl)phenyl)aniline (OMeTPA-DPP) and 4,4′-(4,8-bis((2-ethylhexyl)oxy)benzo[1,2-b:4,5-b′]dithiophene-2,6-diyl)bis(N,N-bis(4-methoxyphenyl)aniline) (OMeTPA-BDT) linked with diketopyrrolopyrrole or benzodithiophene moieties have been synthesized. The new compounds show better thermal stability than spiro-OMeTAD. The steady-state and time-resolved photoluminescence demonstrate that the new compounds have good hole extraction ability. The perovskite solar cells employing OMeTPA-BDT show a comparable power conversion efficiency with that of spiro-OMeTAD. After more than 200 hours of aging under one sun illumination, the residual efficiencies of the PSCs based on OMeTPA-DPP, OMeTPA-BDT and spiro-OMeTAD are 8.69%, 11.15% and 9.08%, respectively. The results demonstrate that the newly-developed compounds can act as efficient hole transporting materials for stable perovskite solar cells.
To develop cost-efficient and stable HTMs for PSCs, herein, we introduce low-cost DPP and BDT moieties as bridge into small-molecular compounds (OMeTPA-DPP, OMeTPA-BDT) and find these two compounds can act as HTM when applied in PSCs. The structures of them are shown in Fig. 1. Two molecules show better thermal stability than spiro-OMeTAD. The charge dynamics at the HTMs/perovskite interface are investigated by steady-state photoluminescence (PL) and time-resolved PL measurements. And the long-term stability of the PSCs based on new HTMs are superior to that of spiro-OMeTAD.
HTM | λmaxa/nm | λPLa,b/nm | Egc/eV | HOMOd/eV | LUMOe/eV | Tdf/°C | Tgg/°C | Tmg/°C |
---|---|---|---|---|---|---|---|---|
a UV-vis absorption spectra and fluorescence spectra were measured in CH2Cl2 solution.b Excitation at λmax.c From the intersection of absorption and emission spectra.d From CV measurement and referenced to ferrocene.e ELUMO = EHOMO + Eg.f Decomposition temperature, from TGA.g Glass-transition temperature and melting temperature, from DSC. | ||||||||
OMeTPA-DPP | 642 | 706 | 1.82 | −5.13 | −3.31 | 305 | 157 | 169 |
OMeTPA-BDT | 414 | 483 | 2.74 | −5.19 | −2.45 | 399 | 158 | 215 |
Cyclic voltammograms (CV) measurements (Fig. 2b) are carried out to get the electrochemical properties of new compounds and spiro-OMeTAD. The pair of redox peaks of OMeTPA-DPP and OMeTPA-BDT is highly reversible, indicating that they have excellent electrochemical stability. The highest occupied molecular orbital (HOMO) energy levels are calculated by the following equation:36 EHOMO = −5.1 − (Eox.HTM vs. Fc/Fc+) (eV), where Eox.HTM vs. Fc/Fc+ is onset of oxidation potential with reference to ferrocene as standard. The HOMO energy levels of them calculated from CV are −5.13 eV and −5.19 eV. Interesting, electron-withdrawing diketopyrrolopyrrole bridge do not lower HOMO level of OMeTPA-DPP compared to OMeTPA-BDT, and repeated CV data are shown in Fig. S2.† HOMO levels of new compounds are more positive than the conductive band of perovskite, indicating a favorable driving force that may generate for electron–hole separation at the HTMs/perovskite interface. And both of them are deeper than spiro-OMeTAD (−5.08 eV). It indicates that the compounds have appropriate HOMO levels relating to the valence band of perovskite and lead to higher open circuit voltage than that of spiro-OMeTAD. The lowest unoccupied molecular orbital (LUMO) levels calculated from HOMO and Eg are found to be −3.31 eV and −2.45 eV for OMeTPA-DPP and OMeTPA-BDT, respectively.
The thermal properties of the compounds are investigated by thermogravimetric analysis (TGA) and differential scanning calorimetry (DSC). As demonstrated in Fig. 2c and S1,† the results show that these two HTMs exhibit more than 150 °C of glass-transition temperature (Tg) and more than 300 °C of decomposition temperature, respectively. The spiro-OMeTAD show a low Tg of 122 °C (shown in Fig. S1†), which is similar with the reported value (Tg = 126 °C).37 The introduction of DPP or BDT moieties into these new molecules as cores can lower the twisting force and increase the π-conjugation ability than spiro-core. Moreover, the existence of heterocyclic aromatic DPP or BDT into molecular main chain could decrease mobility of chain segment and molecular flexibility of these two new compounds than spiro-OMeTAD, which lead to high Tg than spiro-OMeTAD.38,39 And high thermal stability is beneficial to the long-term durability of PSCs.
Fig. 3 (a) Time-integrated PL spectra. Excitation wavelength: 600 nm. (b) Time-resolved PL spectra. Monitored at 765 nm, excitation at 445 nm. |
Fig. 3b shows the time-resolved PL decay spectra of perovskite film coated with OMeTPA-DPP, OMeTPA-BDT and one without any HTM layer. In the absence of HTM layer, the excited perovskite has no other possibility than recombining with electron within perovskite layer, indicating a longer decay time. Pristine perovskite exhibits a lifetime of 3.77 ns, illustrates relatively slow carrier recombination in perovskite layer. However, when the HTMs exhibit, the perovskite can be quenched by the HTMs layer, resulting in a faster decay process. All the perovskite coated with HTMs show significantly reduced lifetime, meaning faster decay rates (1.99 ns for OMeTPA-DPP and 0.96 ns for OMeTPA-BDT). Combined with the steady-state PL spectra, the faster decay rates of perovskite coating with new HTMs show the dynamical possibility of the charge transfer at HTM/perovskite interface.
Fig. 4 (a) Cross-sectional SEM image of the perovskite solar cells. (b) Scheme of the PSCs configuration. (c) Energy level diagram of the corresponding materials used in devices. |
Fig. 5a shows the current-density–voltage (J–V) curves of fore-mentioned devices. The photovoltaic parameters of the PSCs are summarized in Table 2. As the PSCs have exhibited a greatly improvement in PCE by increasing the hole-conductivity of HTMs via doping the additives such as lithium bis(trifluoromethanesulfonyl)imide (Li-TFSI) and 4-tert-butylpiridine (TBP). We fabricate the devices by doping the two additives into OMeTPA-DPP and OMeTPA-BDT, spiro-OMeTAD HTMs to enhance cells performance.
HTM | Voc (V) | Jsc (mA cm−2) | FF (%) | PCE (%) |
---|---|---|---|---|
No HTM | 0.75 | 11.21 | 63.9 | 5.41 |
OMeTPA-DPP | 0.92 | 14.87 | 63.0 | 8.63 |
OMeTPA-BDT | 0.96 | 16.60 | 68.5 | 10.89 |
Spiro-OMeTAD | 0.95 | 19.93 | 71.1 | 13.45 |
After preliminary optimization of devices, the PCEs of the PSCs with OMeTPA-DPP, OMeTPA-BDT and spiro-OMeTAD as HTM are 8.63%, 10.89% and 13.45%, respectively. The device fabricated without any HTM shows a PCE of only 5.41%. Obviously, the improved PCEs of devices with OMeTPA-DPP or OMeTPA-BDT than a device without HTM demonstrate that the new compounds have the potential to be efficient HTMs in PSCs. The short circuit current (Jsc) of the devices fabricated with OMeTPA-DPP, OMeTPA-BDT and spiro-OMeTAD are 14.87, 16.60, and 19.93 mA cm−2. The incident photon to current efficiency (IPCE) spectra represents the ratio of extracted electrons to incident photons at the electrode surface at a given wavelength. And corresponding IPCE spectra of the devices with OMeTPA-DPP, OMeTPA-BDT, spiro-OMeTAD and without HTMs is shown in Fig. 5b. Compared with hole-conductor-free device, the IPCE spectra of the PSCs with HTMs are significantly improved in 400-800 nm. The devices with new compounds show lower IPCE response in 400–800 nm than that of spiro-MeOTAD, which may result from lower HOMO level of them than spiro-OMeTAD. So there is lower driving force for electron injection efficiency between the perovskite layer and the OMeTPA-DPP/OMeTPA-BDT layer. In addition, the integrated IPCE spectra of the devices are in good agreement with the Jsc from each device. In perovskite solar cells, the open circuit voltage (Voc) mainly depends on the HOMO energy level of HTMs and the Fermi level of TiO2. The HOMO energy level of OMeTPA-BDT is lower than that of spiro-OMeTAD by about 150 mV. Therefore, the difference of 110 meV between them lead to the average Voc of device based on OMeTPA-BDT are higher than that of spiro-OMeTAD. The hysteresis characteristics of the PSC devices with new HTMs and spiro-OMeTAD were evaluated from the forward and reverse scan directions, as shown in Fig. S3 and Table S1.† There are similar hysteresis behavior among the devices with new HTMs and spiro-OMeTAD.
To study the stability of devices base on different HTMs, we further optimize the device fabrication and gain a PCE of 10.05%, 12.81% and 14.20% for OMeTPA-DPP, OMeTPA-BDT and spiro-OMeTAD, respectively (shown in Fig. S5†). Then we put these cells without encapsulation under one sun illumination. As shown in Fig. 6 and Table S5,† we noted that the devices with OMeTPA-DPP and OMeTPA-BDT show a 14% and 13% loss of PCE, however, the spiro-OMeTAD-based showed the most significant deterioration (36% loss of PCE) after 10 days of aging. The excellent stability of the OMeTPA-DPP and OMeTPA-BDT based cells than that of spiro-OMeTAD are attributable to excellent thermal stability and the existence of hydrophobic alkyl chains on them.
Synthesis of 4-methoxy-N-(4-methoxyphenyl)-N-(4-(4,4,5,5-tetramethyl-1,3,2-dioxaborolan-2-yl)phenyl)aniline (compound 2). Under the protection of Ar, compound 1 (3 mmol, 1.728 g), bis(pinacolato)diboron (3.75 mmol, 0.96 g), KOAc (9.36 mmol, 0.9 g), dry 1,4-dioxane were added into a 50 mL flask. Then Pd2dba3 (14 mg) and X-Phos (30 mg) were added to the system and stirring at 80 °C overnight. The reaction mixture was then cooled down to room temperature and extracted with CH2Cl2, remove the solvent. The residue mixture was purified by column chromatography (CH2Cl2/hexane = 1:1) to obtain the white solid (product 2, 1.10 g, 74%). 1H NMR (400 MHz, DMSO) δ 7.47 (d, 2H), 6.93 (d, 4H), 6.70 (d, 4H), 6.68 (d, 2H), 3.76 (s, 6H), 1.26 (s, 12H). 13C NMR (100 MHz, CDCl3) δ 156.23, 151.44, 140.43, 135.80, 127.20, 119.47, 118.65, 114.77, 83.41, 55.48, 24.89.
Synthesis of 3,6-bis(5-(4-(bis(4-methoxyphenyl)amino)phenyl)thiophen-2-yl)-2,5-bis(2-ethylhexyl)pyrrole [3,4-c]pyrrole-1,4(2H,5H)-dione (OMeTPA-DPP). Compound 2 (1.2 mmol, 0.517 g), compound 3 (0.5 mmol, 0.34 g), 2 M solution of K2CO3 (8 mmol, 1.1 g) in H2O, [Pd(PPh3)4] (0.05 mmol, 58 mg), DMF (20 mL) were added into a 100 mL Ar-protected flask. The reaction solution was kept with stirring at 90 °C overnight. The reaction mixture was then cooled down to room temperature and poured into cool water, extracted with CH2Cl2. The organic layer was dried with MgSO4, and the solvent was removed by rotary evaporator. The residue mixture was purified by column chromatography (CH2Cl2/hexane = 1:1) to obtain the product as atropurpureus solid (OMeTPA-DPP, 415 mg, 73%). 1H NMR (400 MHz, CDCl3) δ 7.44 (d, 4H), 7.29 (d, 4H), 7.10 (d, 8H), 6.87 (t, 12H), 4.06 (m, 4H), 3.81 (s, 12H), 1.95 (s, 2H), 1.47–1.27 (m, 16H), 0.95–0.81 (m, 12H). 13C NMR (100 MHz, CDCl3) δ 161.69, 156.38, 150.18, 149.40, 140.06, 139.49, 137.07, 127.34, 127.05, 126.78, 124.70, 122.87, 119.69, 114.84, 107.71, 55.49, 45.93, 40.93, 39.19, 30.30, 28.48, 23.08, 14.07, 10.60. HRMS (MALDI-TOF): [M − H] m/z calcd for C70H73N4O6S2: 1130.4898; found: 1130.4796.
Synthesis of 4,4′-(4,8-bis((2-ethylhexyl)oxy)benzo[1,2-b:4,5-b′]dithiophene-2,6-diyl)bis(N,N-bis(4-methoxyphenyl)aniline) (OMeTPA-BDT).
Compound 4 (0.6 mmol, 0.36 g), compound 2 (1.5 mmol, 0.65 g), 2 M solution of K2CO3 (8 mmol, 1.1 g) in H2O, [Pd(PPh3)4] (0.05 mmol, 58 mg), DMF (20 mL) were added into a 50 mL Ar-protected flask and following the same procedure to make OMeTPA-DPP. The OMeTPA-BDT was obtained as a green solid (554 mg, 88%). 1H NMR (400 MHz, CDCl3) δ 7.60–7.46 (m, 6H), 7.10 (d, 8H), 6.95 (d, 4H), 6.85 (d, 8H), 4.18 (s, 4H), 3.81 (s, 12H), 1.82 (dd, 2H), 1.75–1.65 (m, 2H), 1.58 (dd, 4H), 1.53 (d, 2H), 1.40 (s, 8H), 1.02 (t, 6H), 0.93 (d, 6H). 13C NMR (100 MHz, CDCl3) δ 156.22, 148.93, 143.96, 143.36, 140.50, 132.60, 129.17, 127.08, 126.99, 126.21, 120.16, 114.83, 113.95, 75.92, 55.52, 40.71, 30.52, 29.26, 23.93, 23.19, 14.21, 11.38. HRMS (MALDI-TOF): [M − H] m/z calcd for C66H71N2O6S2: 1052.4177; found: 1052.4655.
The compact TiO2 layer was deposited on the etched FTO substrate by aerosol spray-pyrolysis using O2 as the carrier gas at 450 °C from a precursor solution of 1.2 mL titanium diisopropoxide and 0.8 mL bis(acetylacetonate) in 14 mL anhydrous isopropanol, and then sintered at 510 °C for 30 min. The mesoporous TiO2 film was deposited by spin coating at 4000 rpm for 30 s with a ramp of 2000 rpm s−1 from a diluted commercial TiO2 paste in ethanol (Dyesol 18NR-T, 2:7, weight ratio), gradually heated to 510 °C, keep 15 min and cooled to room temperature in air. Then the TiO2 films were treated in a 0.04 M aqueous solution of TiCl4 at 70 °C for 30 min, rinsed with deionized water and following annealed at 510 °C for 30 min.
The PbI2 in DMF solution (461 mg mL−1) was dropped on the TiO2/FTO substrate by spin-coated at 3000 rpm for 30 s, put in room temperature for 5 min, annealed on a hot plate at 70 °C for 30 min. After cooling down, the film was dipped in 9 mg mL−1 CH3NH3I (prepared according to the previously reports44) in 2-propanol solution for 30 s, spin coating at 3000 rpm for 30 s and dried at 70 °C for 30 min. The HTM layer was coated by spin-coating at 5000 rpm for 30 s. The concentration of new HTMs and spiro-OMeTAD are 70 mg mL−1 in 1 mL of chlorobenzene with heating to70 °C overnight, then 28.8 μL of 4-tert-butylpyridine, 17.5 μL of lithium bis(trifluoromethylsulphonyl)imide (520 mg Li-TFSI in 1 mL of acetonitrile) were added to the solution. The HTMs were spin-coated on the CH3NH3PbI3/TiO2/FTO substrate at 4000 rpm for 30 s. All device fabrications were performed below 15% of relative humidity.
Finally, Au layer with a thickness of 60 nm was deposited on HTM layer by thermal evaporator to form the back contact. The active area of the device was defined by a black mask with a size of 0.09 cm2 for all measurement.
Footnote |
† Electronic supplementary information (ESI) available. See DOI: 10.1039/c6ra18823k |
This journal is © The Royal Society of Chemistry 2016 |