Ground- and excited-state characteristics in photovoltaic polymer N2200

Abstract

As a classical polymer acceptor material, N2200 has received extensive attention and research in the field of polymer solar cells (PSCs). However, the intrinsic properties of ground- and excited-states in N2200, which are critical for the application of N2200 in PSCs, remain poorly understood. In this work, the ground- and excited-state properties of N2200 solution and film were studied by steady-state and time-resolved spectroscopies as well as time-dependent density functional theory (TD-DFT) calculations. The transition mechanism of absorption peaks of N2200 was evaluated through the natural transition orbitals (NTOs) and hole–electron population analysis by TD-DFT. Time-resolved photoluminescence (TRPL) study shows that the lifetimes of singlet excitons in N2200 chlorobenzene solution and film are ∼90 ps and ∼60 ps, respectively. Considering the absolute quantum yield of N2200 film, we deduce that the intrinsic lifetime of singlet exciton can be as long as ∼20 ns. By comparing the TRPL and transient absorption (TA) kinetics, we find that the decay of singlet excitons in N2200 solution is dominated by a fast non-radiative decay process, and the component induced by intersystem crossing is less than 5%. Besides that, the annihilation radius, annihilation rate and diffusion length of singlet excitons in N2200 film were evaluated as 3.6 nm, 2.5 × 10⁻⁹ cm³ s⁻¹ and 4.5 nm, respectively. Our work provides comprehensive information on the excited states of N2200, which is helpful for the application of N2200 in all-PSCs.

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1. Introduction

Over the past few decades, polymer solar cells (PSCs) including p-type conjugated polymers and n-type organic semiconductors have been widely studied by researchers due to the outstanding advantages such as lightweight, flexibility, and low cost.^1–4 Among the electron acceptor materials of PSCs, fullerenes are the most widely studied because of their good carrier mobility and electron capture ability in blend films.^5–7 However, the weak light absorption of fullerene in the visible-near infrared region limits the further improvement of the power conversion efficiency (PCE) of PSCs. Therefore, alternative materials for fullerenes need to be developed. In recent years, the rapid development of non-fullerene acceptors, such as polymers and small organic molecules, has greatly promoted the improvement of PCE of PSCs.^8–10 At present, the PCE of single-junction PSCs based on non-fullerene acceptors has reached 18%,¹¹ which is suitable for commercialization in terms of PCE.

Poly{[N,N′-bis(2-octyldodecyl)-naphthalene-1,4,5,8-bis(dicarboximide)-2,6-diyl]-alt-5,5'-(2,2′-bithiophene)} (known as Polyera ActivInk N2200, also named as P(NDI2OD-T2)), was first reported and successfully applied for transistors with a high electron mobility of 0.85 cm² V⁻¹ s⁻¹ in 2009.¹² Since then, N2200 is often employed as acceptor material in all-PSCs.^13–15 In 2011, P3HT:N2200 photovoltaic system was constructed for the application of PSCs, and a PCE of 0.16% was achieved.¹⁶ After that, the PCE of N2200-based all-PSCs have made great progresses from the development of donor material design and device optimization.^17–20 For instance, Wang et al. employed PBDTTS-FTAZ and N2200 as an absorption-complementary active layer to get a PCE of 4.8%.¹⁹ Li and co-workers selected a fluorine medium bandgap copolymer J51 as donor to match N2200, then acquiring a PCE of 8.27%.¹⁷ It is worth mentioning that the PTzBI-Si:N2200 photovoltaic system showed a milestone PCE of 11.76% after the morphology optimization.²⁰

Time-resolved optical techniques are important tools for understanding photoelectrical conversion properties in n-type polymer-based PSCs.^19,21–23 For example, Zhang et al. studied the carrier properties of PBDB-T:N2200 solar cells by using time-resolved microwave conductivity (TRMC), they found that the all-PSC (PBDB-T:N2200) has a longer TRMC lifetime compared with those of ITIC based (PBDB-T:ITIC) and PCBM based (PBDB-T:PCBM) devices.²¹ Kim et al. studied the photo-stability of PBDTTTPD:P(NDI2HD-T) under various light soaking conditions by using transient absorption, they found that the charge generation and transport dynamics were not changed under photo-stress, suggesting a superior photo-stability of n-type polymer (P(NDI2HD-T)) based devices under N₂ conditions.²³ Chen et al. studied exciton dissociation processes in all-PSCs by using time-resolved photoluminescence (TRPL), they found the exciton dissociation efficiency of solar cells can be enhanced by introducing a dye molecule into the n-type polymer N2200.²²

A critical step of charge photogeneration processes is related to the migration of photogeneration excitons to the donor/acceptor interface where they can be dissociated into the free charge carriers.^24,25 To realize high exciton dissociation efficiency, the excitons must diffuse and reach the interface within its lifetime.²⁶ Therefore, exciton diffusion length of neat polymer is an essential parameter for high-efficient organic photovoltaics materials and devices. Moreover, exciton diffusion characteristics are closely related to the excited-state properties of organic semiconductor materials. Although the dissociation process of N2200 exciton in blend active layer has been studied by using TRPL,²³ the excited-state properties of neat N2200 have not been systematically studied yet.

In this work, the ground- and excited-states properties of N2200 solution and film were studied by steady-state and time-resolved spectroscopies as well as time-dependent density functional theory (TD-DFT) calculations. First, hole–electron population analysis and natural transition orbitals (NTOs) by TD-DFT were employed to understand the transition mechanism of steady-state absorption peaks of N2200 solution. Then, TRPL and transient absorption (TA), were employed to understand the singlet exciton lifetime and the decay paths of the excited state in N2200 solution and film. Finally, the annihilation radius, annihilation rate and diffusion length of singlet excitons, which are closely correlated with charge photogeneration processes in N2200-based solar cells, were evaluated based on exciton annihilation dynamics of N2200 film under various excitation fluencies. Our work emphasizes the role of controlling the size of N2200 phase in active layers for developing high efficient N2200-based solar cells.

2. Materials and methods

2.1 Sample information

The polymer N2200 (M_w: 100–150 kDa; PDI: 3.0–4.5) was used as purchased from Solarmer Materials Inc. (Beijing) without further processing. For N2200 solution preparation, N2200 was dissolved in chlorobenzene (CB) solution and was put into a 1 mm cuvette for spectrum measurements. For the fabrication of N2200 film, N2200 were dissolved in CB to obtain a solution of 8 mg mL⁻¹. The glass substrates were treated by ultrasonication in detergent and washed with deionized water, acetone, ethanol, and isopropyl alcohol. Then, the dissolved N2200 solution was dropped on the glass substrate and spin-coated at 1000 rpm for 50 s to fabricate the N2200 film with a thickness of ∼105 nm that measured by a step profiler (Alpha-Step D-100). Sample preparation, dissolution, and spin-coating were all performed in a nitrogen-filled glove box.

2.2 Steady-state absorption and photoluminescence (PL) spectra measurements

Absorption spectra of N2200 solution and film were recorded on the UV-visible spectrometer Agilent 8453. For fluorescence measurements, the sample surface was at an angle of 45° with the excitation light. The excitation wavelength was 532 nm for N2200 solution and film. Photoinduced fluorescence was collected by an optical fiber spectrometer (AvaSpec-ULS2048CL-RS-EVO-UA) through a series of collection lenses. The collected fluorescence signals were all spectrally corrected by a standard light source (Ocean Optics, LS-1-CAL). All the measurements were conducted at room temperature in air.

2.3 Transient absorption (TA) measurements

TA experiments were performed on a HARPIA-TA system (Light Conversion). A 1030 nm pulsed laser with a pulse duration of 190 fs and repetition rate of 100 kHz, was used as the fundamental light source of the HARPIA-TA system. The 1030 nm laser was divided into two parts by a beam splitter. One beam was employed to pump an optical parametric amplifier system (OPA, Light Conversion) system, and the output at 720 nm and 750 nm was used for exciting N2200 solution and films, respectively. The other beam was employed to generate the probe light in the range of 500–950 nm by exciting a sapphire plate. The delay between pump and probe was regulated by a mechanical delay stage. All the measurements were conducted at room temperature in air.

2.4 Time-resolved photoluminescence (TRPL) and absolute photoluminescence quantum yield (PLQY) measurements

TRPL was measured in a setup described in the previous works.^27,28 A fs pulsed laser (Tsunami, Spectra-Physical) with wavelength of 800 nm, pulse duration of ∼100 fs and repetitive rate of 80 MHz, was employed as the laser source. The frequency-doubled laser (400 nm) was employed as exciting light. PL signal of the sample was collected and focused into the input slit of the spectrometer (Chromex). The output PL from the spectrometer was directed into and measured by a streak camera system (Hamamatsu C6860). TRPL images have been corrected by a reference white light source (LS-1-CAL, Ocean Optics). The absolute PL quantum yield (QY) of the N2200 solution was measured by an integration sphere method. The sample was placed into the integrating sphere (F3029, Quanta-φ, HORIBA), and was excited by a CW laser with an output wavelength of 660 nm. An optical fiber spectrometer (Avaspec-ULS2048CL-RS-EVO-UA, Avantes) was used to measure the output light from the integrating sphere. All measurements were performed at room temperature in air.

3. Results and discussion

3.1 Molecular structure and frontier orbitals

The TD-DFT calculations at the B3LYP/6-311G(d,p)^29,30 level were carried out with Gaussian 16 software package³¹ for understanding the molecular orbitals properties of N2200 polymer. Considering the chain length would affect the lowest unoccupied molecular orbital (LUMO) and the highest occupied molecular orbital (HOMO) energy levels, N2200 oligomers from one to seven repeating units have been calculated. Since the alkyl branches (R = C₈H₁₇ and C₁₀H₂₁) on naphthalene diimide (NDI) unit of oligomers typically have a weak influence on the molecular orbital properties of polymers,³² alkyl branches were substituted by methyl groups during the calculations.

The calculated electron density distributions of LUMO and HOMO for NDI, bithiophene (T2) units and N2200 oligomers are shown in Fig. 1. For the NDI and T2 units, we find both the electron densities of the LUMO and HOMO wave functions are distributed over the whole units. For the N2200-1 oligomer, the electron density of the LUMO wave function tends to be localized on the NDI unit, while the electron density of the HOMO wave function is delocalized over both the NDI and T2 units. By examining the electron densities of HOMO and LUMO at various repeating units (n), we find that the electron densities of LUMO and HOMO are distributed on each repeating unit evenly when n < 4, while for longer oligomers (n > 4), the electron densities are localized on several repeating units. Moreover, we note that the LUMO energy level becomes lower, while the HOMO energy level becomes higher (as shown in Table 1), resulting in a reduced band-gap with the increase of repeating units. This result shows that when the number of repeating units increases to 6, the LUMO and HOMO energy levels of N2200 oligomers change very little.

Fig. 1 The electron density distribution of LUMO (up) and HOMO (down) energy levels for NDI, T2 units and N2200 oligomers with various repeating units by TD-DFT at the level of B3LYP/6-311G(d,p). n is the number of repeating units. The isosurface value was set at 0.01 a. u.

Table 1 LUMO and HOMO energy levels and the band gaps of the N2200 oligomers with various repetition units (n) calculated by TD-DFT/B3LYP/6-311G(d,p)

N2200-n	HOMO (eV)	LUMO (eV)	Band gap (eV)
N2200-1	−5.862	−3.569	2.293
N2200-2	−5.757	−3.644	2.113
N2200-3	−5.730	−3.677	2.053
N2200-4	−5.704	−3.693	2.011
N2200-5	−5.670	−3.703	1.997
N2200-6	−5.678	−3.708	1.970
N2200-7	−5.680	−3.706	1.974

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3.2 The steady-state optical properties

Fig. 2 shows the normalized UV-vis absorption and PL spectra of N2200 in CB solution and thin-film. It can be seen that the absorption spectrum exhibits two distinct absorption peaks at around 390 and 700 nm in both solution and film. To understand the transition mechanism of these absorption peaks, the absorption spectra of N2200 oligomers with a dielectric constant of 5.6968 (CB solution) were simulated by TD-DFT at the level of B3LYP/6-311G(d,p), as shown in Fig. 2(a) and ESI Fig. S1.† It can be seen that the main absorption peaks are red-shifted with increasing the oligomer length. TD-DFT calculations show that, with the increase of oligomer length, LUMO energy level becomes lower and HOMO energy level becomes higher (as shown in Table 1), which will result in a reduced band-gap with the increase of repeating units. The reduced band-gap induces the redshift of the main absorption peaks with the increase of oligomer length. We also noted that the simulated UV-vis absorption spectra are red-shifted compared with the experimental data. This could origin from the rough description of charge transfer and Rydberg states presented by B3LYP.³³

Fig. 2 (a) The experimental (solid lines) and simulated (dot line) absorption and PL spectra of N2200 in chlorobenzene solution; the simulation was performed by TD-DFT at the level of B3LYP/6-311G(d,p) and a Gaussian function with a full width at half-maximum of 0.45 eV was used. (b) Steady-state absorption (black line) and PL (red line) spectra of N2200 thin film. The excitation wavelength for PL measurements of N2200 solution and film is 532 nm.

By examining the calculation of N2200 oligomer with three repeating units, the absorption characteristics are assigned. The absorption peak of 700 nm (experimental value) in N2200 solution is characterized by S₀ → S₁ transition mainly contributed by HOMO (H) → LUMO (L) (83.9%) and H−1 → L+1 (6.9%) molecular orbital transitions. In addition, the absorption band at around 390 nm (experimental value) is predicted by the transition from the S₀ to S₁₆ excited state, that mainly contributed by H−3 → L+1 (14.6%), H → L+4 (14.5%), H−11 → L (10.9%) and H → L+3 (10.5%). To get a better insight into the electronic excitation process of these two absorption peaks in the N2200 solution, the NTOs³⁴ and hole–electron population analysis³⁵ were calculated in Multiwfn (version 3.7)³⁶ and VMD (version 1.9.4)³⁷ software, as shown in ESI Fig. S2 and S3.† For the S₀ → S₁ transition, the hole distribution of the NTO and overlap electron–hole density map are more clearly localized on the T2 donor unit, while the electron tends to distribute on the NDI acceptor unit, due to the large twists between the T2 and NDI units in N2200 monomer hindering the delocalization along the backbone.³⁸ From the analysis of the overlap of electron–hole density, we find both the absorption peaks at around 390 and 700 nm exhibit the characteristics of the charge transfer transitions. Comparing with the absorption in solution, the absorption maximum of N2200 film slightly redshifts (∼5 nm). This can be attributed to stronger intermolecular interactions and better coplanar structures in the solid-state.^39,40 Meanwhile, we observe a pronounced Stokes shift of the emission spectrum in both solution and film (∼160 nm for the solution, ∼145 nm for the film), which is due to energy losses between excitation and emission.^41,42

3.3 Excited-state properties of N2200 solution and film

In PSCs, the exciton dissociation efficiency of the blended active layer is closely related to the lifetime of exciton in the neat donor (or neat acceptor) film. Assuming phase separation and exciton diffusion coefficient are the same for the blended active layers, a longer the exciton lifetime of the neat electron-donor (or neat electron-acceptor) film would have a longer exciton diffusion length and thus a higher exciton dissociation efficiency in the blend film, which could increase the PCE of PSCs.¹⁹ The TRPL measurements were first conducted to study the lifetime of singlet emissive excitons in N2200 solution and film, as shown in Fig. 3(a). We find that the kinetics of the N2200 solution and film can be fitted by single exponential decay functions. This suggests the kinetics are dominated by the first-order reaction process, and the higher-order reaction processes such as exciton annihilation can be neglected under the applied excitation fluence.^43,44 It is shown that the PL lifetimes of N2200 solution and film are ∼90 ps and ∼60 ps, respectively. We note the lifetime of N2200 film is much shorter than some classic donor polymers, such as P3HT (∼470 ps),⁴⁵ MEH-PPV (∼450 ps),⁴⁶ and APFO-3 (∼500 ps).⁴⁷ The fast decay rate of film could be dominated by either radiative recombination rate of N2200, non-radiative decay rate, or both. In the previous studies, the absolute PLQY of N2200 film is found to be ∼0.31%,¹⁹ which is much lower than regular polymer donors. Considering the PLQY (0.3%) and TRPL lifetime (∼60 ps) of N2200 film, the intrinsic exciton lifetime of N2200 film is deduced as 20 ns. Low PLQY of N2200, suggests the measured PL lifetime of N2200 film (∼60 ps) is dominated by non-radiative channels, for example, inter-system crossover processes, charge separation in the neat polymer film, etc.

Fig. 3 (a) TRPL kinetics of N2200 solution and film at indicated probe wavelength. The excited wavelength was 780 and 400 nm for N2200 solution and film, respectively. The solid lines are fitting curves based on single exponential decay functions. (b) TA spectrum of N2200 in CB solution at indicated delay time after photoexcitation at 720 nm with an excitation fluency of 8.49 × 10¹³ photons per cm² per pulse. (c) Comparison of the TRPL and TA kinetics in the N2200 solution. (d) TA spectrum of N2200 film at indicated delay time after photoexcitation at 750 nm with an excitation fluency of 3.16 × 10¹³ photons per cm² per pulse.

TA measurements of N2200 solution and film were conducted for a better understanding of the excited-state decay processes. Fig. 3(b) shows the TA spectrum of N2200 solution at various delay times. It can be seen that a broad positive absorption band and a negative bleaching band appear immediately in the wavelength range of 600–950 nm after photoexcitation, and then the bands decay with time. To assign the absorption band, TA kinetics at 850 nm is compared with TRPL kinetics, which is induced by the emission of singlet excitons, as shown in Fig. 3(c). We find that the TA kinetics at 850 nm is similar to the TRPL kinetics in N2200 solution, strongly supporting that the absorption band in the wavelength range of >760 nm origin from the absorption of S₁ excitons. Since TA kinetics at 850 nm can be fitted by the single exponential decay function, the exciton annihilation process can be also neglected for the measurement under the employed excitation fluency. By comparing TRPL kinetics with TA bleaching kinetics at 700 nm, we find that there is a long-lived component of TA kinetics at 700 nm besides the fast decay component corresponding to the decay component of TRPL kinetics, as shown in ESI Fig. S5.† The long-lived component is most likely induced by the formation of triplet excitons. It should be noted that the proportion of the long-lived component is less than 5%, indicating the intersystem crossing induced S₁ exciton loss is less than 5%. In other words, the PLQY could achieve >95% if the intersystem crossing is the only loss channel of S₁ exciton. However, the PLQY of N2200 solution is measured as 0.68% after photoexcitation at 660 nm by using integration sphere methods. This suggest inter-system crossing is not the dominant loss channel, decay of TRPL kinetics is dominated by other non-radiative recombination processes, such as internal-conversion induced fast non-radiative decay.

The TA spectrum of N2200 film (Fig. 3(d)) exhibits a bleaching band at ∼700 nm and an absorption band at ∼850 nm that can be attributed to the absorption of singlet excitons (see ESI Fig. S6†). By examining the kinetics at 700 nm under various excitation fluencies (Fig. 4(a)), we find the decay becomes faster with increasing excitation power at an early timescale, which can be attributed to the exciton–exciton annihilation under high excitation power.

Fig. 4 (a) TA kinetics of N2200 film at a probe wavelength of 700 nm after photoexcitation at 750 nm under various excitation fluencies. (b) Reciprocal of exciton density vs. exp(kt) of N2200 film under various excitation fluencies. The solid lines are linear fitting curves.

3.4 Exciton diffusion in N2200 film

After photoexcitation, singlet excitons generated in the polymer films. The photogenerated excitons can diffuse along the single conjugated chain or among different chains within the exciton lifetime. The exciton diffusion processes are influenced by many exciton decay processes, such as recombine back to the ground state through radiative or nonradiative channels, transit into triplet states through intersystem crossing. When the two excitons encounter each other in the polymer films, exciton–exciton annihilation can happen. As a result, the energy of one exciton transfers to the other and recombine back to the ground state, meanwhile, the other exciton acquires the energy and transits into a higher excited state. Thus, half of the amounts of excitons will be lost during exciton–exciton annihilation processes. Apparently, exciton–exciton annihilation is a second-order processes, and a higher exciton concentration could lead to a more pronounced annihilation phenomenon.^43,44

In conjugated polymers, exciton–exciton annihilation can be employed to estimate the diffusion length of singlet exciton.^{26,44,48–51} The singlet exciton dynamics can be described as⁴⁴

where n(t) is singlet exciton concentration, γ represents the rate constant of annihilation, k is the first-order exciton decay rate, which is 1.67 × 10¹⁰ s⁻¹ for N2200 film that determined from TRPL measurement. The solution of eqn (1) can be expressed in the form as⁵⁰

Apparently, the time-independent annihilation rate γ can be determined from the linear fit when n(0) and n(t) are known. In this work, exciton dynamics that measured by transient absorption were employed to analyze the exciton–exciton annihilation properties of N2200 film. Fig. 4(a) shows the TA kinetics of the N2200 film under various excitation fluencies ranging from 3.85 × 10¹² to 2.32 × 10¹⁴ photons per cm² per pulse probing at 700 nm. As the excitation fluency is increasing above 10¹³ photons per cm² per pulse, it can be seen that the TA kinetics decays faster with increasing excitation fluency in the time range of <200 ps, due to more pronounced exciton–exciton annihilation under higher excitation power. Meanwhile, no pronounced differences were observed for the kinetics in the time range of >200 ps among the different excitation fluence.

The exciton density n(t) can be determined from the ΔOD(t) in TA kinetics using the known initial singlet exciton concentration n(0). Then, TA kinetics in the time range of <200 ps in Fig. 4(a) can be rearranged as Fig. 4(b) and ESI Fig. S9.† The rate constant of annihilation γ is determined as (2.4 ± 0.2) × 10⁻⁹ cm³ s⁻¹ for N2200 film by fitting the kinetics in Fig. 4(b) with eqn (2). The figure including the y-intercept at the exp(kt) = 0 can be found in ESI Fig. S9.† According to eqn (2), y-intercept at the exp(kt) = 0 represents the −γ/k, where γ represents the rate constant of annihilation, k is the first-order exciton decay rate. The annihilation rate can be correlated with diffusion coefficient as⁵¹

γ = 4πDR_a (3)

where D is the diffusion coefficient, and R_a is the annihilation radius, corresponding to the exciton delocalization size. To determine diffusion coefficient of N2200, the annihilation radius R_a needs to be determined. In this work, the annihilation radius R_a is estimated from excitation power-dependent maximal bleaching at the delay time of 0.2 ps, as shown in ESI Fig. S8.† At this delay time, due to the localization of excitons, the reduction of exciton density origin from the exciton–exciton annihilation by the direct contact of excitons, rather than that induced by exciton diffusion.⁵² When the excitation fluency is 8.05 × 10¹³ photons per cm² per pulse, the −ΔOD starts to deviate from the linear dependence between −ΔOD and excitation fluency in the low excitation range. This suggests that the adjacent excitons begin to overlap at this excitation fluency. According to excitation conditions at the threshold, exciton density and the averaged volume (V) for one exciton can be calculated. Assuming a cubic model for the volume of each exciton, the annihilation radius R_a can be calculated as , which is ∼3.6 nm under the photoexcitation at 750 nm. By substituting parameters γ and R_a into eqn (3), the diffusion constant for the singlet exciton of N2200 film was estimated as D = (5.3 ± 0.4) × 10⁻⁴ cm² s⁻¹. This allows us to estimate the three-dimensional exciton diffusion length by using L_d = (6Dτ)^1/2, which characterizes the mean effective distance for the exciton diffusion within its lifetime,⁴⁹ that is 4.3 ± 0.2 nm in terms of the exciton lifetime of 60 ps.

In PSCs, exciton dissociation is a critical process determining the PCE of devices. In order to make the device have high energy conversion efficiency, the exciton dissociation efficiency should be as high as possible. In other words, the excitons generated in N2200 phase of the blend film need to reach the interface within its diffusion length to ensure high exciton dissociation efficiency. The diffusion length of 4.3 ± 0.2 nm in N2200 film suggest the size of N2200 phase should be controlled within 4.3 ± 0.2 nm when optimizing the morphology of N2200 based devices. Many methods, such as thermal annealing,⁵³ adding the additive of DIO,⁵⁴ can be employed to for regulating the scale of donor (or acceptor) phase in the blended active layers. We note that exciton diffusion coefficient of N2200 can be comparable with some polymer semiconductors, such as POMeOPT (6.0 × 10⁻⁴ cm² s⁻¹)⁵⁵ and PCE11 (1.0 × 10⁻³ cm² s⁻¹).⁵⁶ Although the diffusion coefficient of N2200 film can be compared with these two polymers, the diffusion length of N2200 exciton is much smaller due to a shorter exciton lifetime in N2200 film. At the same time, we note that the exciton diffusion length of N2200 is much smaller than that of classical non-fullerene small molecule acceptors, such as ITIC (18.2 nm)⁵⁷ and IT-4F (18.8 nm).⁵⁷ Therefore, compared with PSCs based on small molecule acceptors, N2200 based solar cells should strictly control the size of acceptor phase in active layer.

4. Conclusion

We have studied the excited-states properties in N2200 solution and film by the optical spectroscopies as well as TD-DFT calculations. The transition mechanism of the absorption peaks of N2200 was evaluated through the NTOs and hole–electron population analysis by TD-DFT. The lifetime of singlet exciton in N2200 solution and film are found to be ∼90 ps and ∼60 ps, respectively. The short lifetime of N2200 is due to the fast non-radiative decay process. The annihilation radius, annihilation rate and diffusion length of singlet exciton in N2200 film were evaluated as 3.6 nm, 2.5 × 10⁻⁹ cm³ s⁻¹ and 4.5 nm, respectively. Our work emphasizes the role of controlling the size of N2200 phase in active layers for developing high efficient N2200 based solar cells.

Author contributions

Guanzhao Wen: software, investigation, data curation, funding acquisition, writing – original draft. Xianshao Zou: investigation, data curation, writing – review & editing. Rong Hu: investigation, data curation, funding acquisition, writing – review &editing. Jun Peng: methodology, writing – review & editing. Zhifeng Chen: methodology, funding acquisition. Xiaochuan He: investigation. Geng Dong: supervision, software, writing – review & editing. Wei Zhang: conceptualization, writing – review & editing, supervision, funding acquisition.

Conflicts of interest

The authors declare that they have no known competing financial interests or personal relationships that could have appeared to influence the work reported in this paper.

Acknowledgements

This work was supported by the funding from Natural Science Foundation of China (Grant No. 21603020, 21903017), Natural Science Foundation of Guangdong Province (Grant No. 2020A1515010411, 2019A1515010783), Key Research Project of Guangzhou University (Grant No. YK2020003), Young Talents Program of Guangzhou University (Grant No. RQ2020080), Guangzhou Municipal Science and Technology Project (Grant No. 202001010002), Science and Technology Research Program of Chongqing Municipal Education Commission (Grant No. KJQN201901319, KJQN202001323) and Innovation Research for the Postgraduates of Guangzhou University (Grant No. 2020GDJC-M50).

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Footnotes

† Electronic supplementary information (ESI) available. See DOI: 10.1039/d1ra01474a

‡ These authors contributed equally to this work.

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