# Patent

## Title
Regioregular pyridal[2,1,3]thiadiazole π-conjugated copolymers for organic semiconductors

## Abstract

A method of regioselectively preparing a pyridine-containing compound is provided. In particular embodiments, the method includes reacting halogen-functionalized pyridal[2,1,3]thiadiazole with organotin-functionalized cyclopenta[2,1-b:3,4-b′]dithiophene or organotin-functionalized indaceno[1,2-b:5,6-b′]dithiophene. Also provided is a method of preparing a polymer. The method includes regioselectively preparing a monomer that includes a pyridal[2,1,3]thiadiazole unit; and reacting the monomer to produce a polymer that includes a regioregular conjugated backbone section, wherein the section includes a repeat unit containing the pyridal[2,1,3]thiadiazole unit. A polymer that includes a regioregular conjugated backbone section, and electronic devices that include the polymer, are also provided.

## Background
CROSS-REFERENCE TO RELATED APPLICATIONS
This application claims the benefit of Provisional Patent Application Nos. 61/498,390, filed on Jun. 17, 2011, and 61/645,970, filed on May 11, 2012, which are incorporated by reference herein.


BACKGROUND
1. Field of the Invention
The invention relates to conjugated polymers and methods of making the same.
2. Related Art
Organic π-conjugated polymers are attractive materials for use in the active layer, as they combine good absorption and emission characteristics with efficient charge carrier mobility and have the ability to be solution processed onto flexible substrates. Recent advances in the field have seen organic field effect transistors (OFET) achieve charge carrier mobility on the order of 1.0 cm2V−1 s−1 [1] and organic photovoltaic (OPV) devices reach power conversion efficiencies over 7% [2]. While these results are promising for the field, there still exits a complexity of correlating molecular structure to optical and electronic properties. Among the available narrow band-gap materials, donor-acceptor copolymers based on cyclopenta[2,1-b:3,4-b′]dithiophene (CDT) and benzothiadiazole (BT) have attracted considerable attention due to the high charge carrier mobility and excellent photovoltaic performance. Müllen and co-workers have eloquently demonstrated that CDT-BT copolymers with linear side chains and high molecular weights, p-type FETs with mobilities on the order of 1.4-3.3 cm2 [3].
The incorporation of a nitrogen atom into the acceptor unit of CDT-BT copolymers results in the narrowing of the optical bandgap and the emergence of these materials to selectively bind Lewis acids [4]. The replacement of the BT unit with the pyridal[2,1,3]thiadiazole (PT) acceptor unit results in a higher electron affinity across the polymeric backbone leading to a decreased LUMO level of polymer. Copolymers based on PT and carbazole reported by Lerclerc et al. [5] have fairly low molecular weights (ca. 4-5 kDa), and the efficiencies of the fabricated solar cells (under 1%) are much lower than predicated. You and co-workers have demonstrated that by introducing two alkyl chains to the 4-position of the thienyl unit could lead to a more soluble PT based acceptor (DTPyT), and allows access to polymers with high molecular weights and excellent photovoltaic efficiency up to 6.32% [6]. In each case, however, the nature of the step-growth polymerization strategy leads to these polymer systems having a regiorandom origination of the pyridal-N atom along the polymeric backbone.
SUMMARY
The inventors understand that regioregularity can have a great impact on the properties of polymers [7]. For instance, enhanced regioregularity of poly(3-alkylthiophene) can impart to polymers a higher crystallinity, red-shifted optical absorption, higher conductivity, and smaller band-gap [8]. The inventors have surmised that for a polymer based on an asymmetric PT unit, a regioregular backbone structure with more effective electron localization can result in a higher charge carrier mobility and enhanced photovoltaic performance. Recognizing that for the copolymerization of distannyl CDT monomers and 4,7-dibromo-pyridal[2,1,3]thiadiazole (PTBr2) as starting material, the resulted polymer would not be truly random because the bromine at the electron-deficient C4-position of PTBr2 is more favorable for coupling than the C7-position [9], the inventors take advantage of this difference by preparing regiochemically precise backbones of PT-based polymers using specific synthetic procedures.
In one aspect, a method of preparing a regioregular polymer is provided. The method includes regioselectively preparing a monomer; and reacting the monomer to produce a polymer that includes a regioregular conjugated main chain section.
In a further aspect, a regioregular polymer that includes a regioregular conjugated main chain section is provided. Also provided is an electronic device that includes the regioregular polymer.
In some embodiments, the regioregular polymer includes a regioregular conjugated main chain section having a repeat unit that includes a pyridine of the structure




where a) Ar is a substituted or non-substituted aromatic functional group, or Ar is nothing and the valence of the pyridine ring is completed with hydrogen, and b) the pyridine is regioregularly arranged along the conjugated main chain section. The regioregularity of the main chain section can be 95% or greater, and the charge carrier mobility of the regioregular polymer can be greater than the charge carrier mobility of a regiorandom polymer of similar composition. In some embodiments of the regioregular polymer, the repeat unit further includes a dithiophene of the structure





where a) each Ar is independently a substituted or non-substituted aromatic functional group, or each Ar is independently nothing and the valence of its respective thiophene ring is completed with hydrogen, b) each R is independently hydrogen or a substituted or non-substituted alkyl, aryl or alkoxy chain, and c) X is C, Si, Ge, N or P.

In some embodiments that include the pyridine and/or the dithiophene, each substituted or non-substituted aromatic functional group of the pyridine and the dithiophene independently includes one or more alkyl or aryl chains. In particular embodiments, the one or more alkyl or aryl chains are each independently a C6-C30 substituted or non-substituted alkyl chain, —(CH2CH2O)n (n=2 ̃20), C6H5, —CnF(2n+1) (n=2 ̃20), —(CH2)nN(CH3)3Br(n=2 ̃20), —(CH2)nN(C2H5)2 (n=2 ̃20), 2-ethylhexyl, PhCmH2m+1 (m=1-20), —(CH2)nSi(CmH2m+1)3 (m, n=1 to 20), or —(CH2)nSi(OSi(CmH2m+1)3)x(CpH2p+1)y (m, n, p=1 to 20, x+y=3).
In some embodiments that include the dithiophene, the substituted or non-substituted alkyl, aryl or alkoxy chain can be a C6-C30 substituted or non-substituted alkyl, aryl or alkoxy chain, —(CH2CH2O)n (n=2 ̃20), C6H5, —CnF(2n+1) (n=2 ̃20), —(CH2)nN(CH3)3Br(n=2 ̃20), —(CH2)nN(C2H5)2 (n=2 ̃20), 2-ethylhexyl, PhCmH2m+1 (m=1-20), —(CH2)nSi(CmH2m+1)3 (m, n=1 to 20), or —(CH2)nSi(OSi(CmH2m+1)3)x(CpH2p+1)y (m, n, p=1 to 20, x+y=3).
In some embodiments that include the dithiophene, X can be C or Si.
In some embodiments of the regioregular polymer that include the pyridine, the pyridine is a pyridine unit of Table 1 (which is described below). In some embodiments, the repeat unit further includes a dithiophene unit of Table 2 (which is described below). In certain embodiments, the pyridine unit is




and the dithiophene unit is





wherein each R is independently hydrogen or a substituted or non-substituted alkyl, aryl or alkoxy chain. In some embodiments, the substituted or non-substituted alkyl, aryl or alkoxy chain is a C6-C30 substituted or non-substituted alkyl, aryl or alkoxy chain, —(CH2CH2O)n (n=2 ̃20), C6H5, —CnF(2n+1) (n=2 ̃20), —(CH2)nN(CH3)3Br(n=2 ̃20), —(CH2)nN(C2H5)2 (n=2 ̃20), 2-ethylhexyl, PhCmH2m+1 (m=1-20), —(CH2)nSi(CmH2m+1)3 (m, n=1 to 20), or —(CH2)nSi(OSi(CmH2m+1)3)x(CpH2p+1)y (m, n, p=1 to 20, x+y=3). In some embodiments, X is C or Si. In particular embodiments, each R is C12H25, each R is 2-ethylhexyl, or each R is PhC6H13.

In some embodiments of the regioregular polymer, the repeat unit includes




where each R is independently hydrogen or a substituted or non-substituted alkyl, aryl or alkoxy chain, and X is C, Si, Ge, N or P. In some embodiments, the substituted or non-substituted alkyl, aryl or alkoxy chain is a C6-C30 substituted or non-substituted alkyl, aryl or alkoxy chain, —(CH2CH2O)n (n=2 ̃20), C6H5, —CnF(2n+1) (n=2 ̃20), —(CH2)nN(CH3)3Br(n=2 ̃20), —(CH2)nN(C2H5)2 (n=2 ̃20), 2-ethylhexyl, PhCmH2m+1 (m=1-20), —(CH2)nSi(CmH2m+1)3 (m, n=1 to 20), or —(CH2)nSi(OSi(CmH2m+1)3)x(CpH2p+1)y (m, n, p=1 to 20, x+y=3). In some embodiments, X is C or Si. In particular embodiments, each R is C12H75, each R is 2-ethylhexyl, or each R is PhC6H13.

A device including any regioregular polymer described herein is provided. The device can be, but is not limited to, a field effect transistor, organic photovoltaic device, polymer light emitting diode, organic light emitting diode, organic photodetector, or biosensor. In the device, the regioregular polymer can form an active semiconducting layer.
The term “regioregular,” “regioregularly” or “regioregularity” in relation to a polymer or a section of a polymer means the non-random orientation or arrangement of the pyridal-N along the polymer backbone. In some regioregular embodiments, the nitrogen atom of the pyridine faces in the same direction in all or a majority of the repeat units of the polymer or polymer section. For example, in the repeat unit of Scheme 1 below, the pyridal nitrogen atom of the PT unit faces the CDT unit. If we define the end of PT next to the pyridal nitrogen atom as the head, and the other end as the tail, then all or a majority of the PT units in the copolymers of Scheme 1 adopted a head-to-tail arrangement next to each other. In other regioregular embodiments, all or a majority of the repeat units of the polymer or polymer section have two pyridine units, with the nitrogen atoms of the pyridine units oriented toward each other. For example, in the repeat unit of Scheme 2 below, the pyridal nitrogen atom of one PT unit is oriented towards the pyridal nitrogen atom of the other PT unit, which is a head-to-head connection through the CDT unit.



BRIEF DESCRIPTION OF THE DRAWINGS
For a more complete understanding of the present invention, reference is now made to the following descriptions taken in conjunction with the accompanying drawings, in which:
FIG. 1 is a panel of 1H NMR spectra of P1b, P2b and P3b in d-TCE at 110° C.;
FIG. 2 is a panel of UV-Vis spectra of P1a, P2a and P3a (a) in o-DCB solutions at 25° C. and (b) as casting films;
FIG. 3 is a panel showing output (a) and transfer (b) characteristics of FET devices based on P1a with PPCB as passivation layer;
FIG. 4 is a panel of UV-vis spectra of polymers (a) P1a, (b) P1b, (c) P2a, (d) P2b, (e) P3a and (f) P3b in o-DCB solutions at 25 or 110° C., and in films as casting (a.c.) or after thermal annealing (t.a.) at 110° C. for 15 min;
FIG. 5 is a panel of DSC curves of polymers with C12 side chain (a) and C16 side chain (b);
FIG. 6 is a panel of CV curves of polymers with C12 side chain (a) and C16 side chain (b);
FIG. 7 is a schematic drawing of a device structure with PPCB passivation;
FIG. 8 is a schematic drawing of a device structure with OTS-8 passivation; and
FIG. 9 is a schematic drawing of a bottom-gate, bottom contact device structure.
FIG. 10 is a composite drawing of GPC profiles of copolymers with chloroform as eluent.
FIG. 11 is a composite drawing of DSC characteristics of copolymers.
FIG. 12 is a composite drawing of UV-Vis spectra of PIPT-RG and PIPT-RA films (thickness ̃30 nm).
FIG. 13 is a panel of (a) CV curves and (b) UPS measurements of polymer films.
FIG. 14 is a panel of output and transfer characteristics (VD=−60 V) for FETs based on PIPT-RG (black dot) and PIPT-RA (red dot) at room temperature (a) and (d), thermal annealed at 100° C. for 10 min (b) and (e), and thermal annealed at 150° C. for 10 min (c) and (f). FET with channel L=20 μm, W=1 mm.
FIG. 15 is a composite drawing of grazing incident XRD of PIPT-RG and PIPT-RA polymer films.
FIG. 16 is a panel of topographic AFM images (2 μm×2 μm) of (a) PIPT-RG:PC71BM (1:4) and (b) PIPT-RA:PC71BM (1:4) (b) blend films.
FIG. 17 is a panel of TEM images of (a) PIPT-RG:PCBM (1:4) and (b) PIPT-RA:PCBM (1:4) (b) films.
FIG. 18 is a panel showing J-V characteristics (a) and IPCE (b) of thermal evaporated MoOx PSC devices based on regioregular and regiorandom PIPT polymers.
FIG. 19 is a panel showing J-V characteristics (a) and IPCE (b) of solution-processed MoOx PSC devices based on regioregular and regiorandom PIPT polymers.
FIG. 20 is a panel showing J-V characteristics of devices (a) post-thermal annealing, and (b) with additive.
FIG. 21 is a panel showing J-V characteristics (a) and IPCE (b) of inverted structure devices based on PIPT-RG polymer
FIG. 22 is a composite drawing of density-voltage (J-V) characteristics of PSC devices based on PSDTPTR-EH (A) and PSDTPT2-EH (B) copolymers.
FIG. 23 is a panel showing molecular structures of polymers and decyl(trichloro)silane, and device architecture.
FIG. 24 is a panel showing (a) the transfer characteristic of an organic TFT after annealing at 350° C., and b) the output characteristic of the same OTFT.
FIG. 25 are atomic force microscopy images of (a) the height image of a polymer film after 350° C. annealing obtained by the tapping mode of AFM, and (b) the phase image correlated to 24(a).
FIG. 26 is a panel of (a) out-of-plane XRD spectra after annealing at various temperatures, and (b) correlated in-plane XRD.
FIG. 27 is a composite drawing of contact resistances at different annealing temperatures obtained by transfer line measurement.



DETAILED DESCRIPTION
In the method of preparing a regioregular polymer, a monomer is regioselectively prepared. In some embodiments, the monomer is prepared by reacting halogen-functionalized PT with organotin-functionalized cyclopenta[2,1-b:3,4-b′]dithiophene. The reaction can be carried out at a temperature in the range of about 50° C. to about 150° C., and the regioselectivity of the reaction can be 95% or greater. In other embodiments the monomer is prepared by reacting halogen-functionalized PT with organotin-functionalized indaceno[1,2-b:5,6-b′]dithiophene (IDT), where the reaction can be carried out at a temperature in the range of about 50° C. to about 150° C. and the regioselectivity of the reaction can be 95% or greater. In other embodiments the monomer is prepared by reacting halogen-functionalized PT with organoboron-functionalized cyclopenta[2,1-b:3,4-b′]dithiophene or organboron-functionalized indaceno[1,2-b:5,6-b′]dithiophene (IDT), where the reaction can be carried out at a temperature in the range of about 50° C. to about 150° C. and the regioselectivity of the reaction can be 95% or greater. In some embodiments the monomer is prepared by reacting halogen-functionalized PT with cyclopenta[2,1-b:3,4-b′]dithiophene or indaceno[1,2-b:5,6-b′]dithiophene (IDT) by direct arylation polyerization, in which direct arylation allows the formation of carbon-carbon bonds between aromatic units having activated hydrogen atoms without the use of organometallic intermediates, where the reaction can be carried out at a temperature in the range of about 50° C. to about 150° C. and the regioselectivity of the reaction can be 95% or greater.
The halogen-functionalized PT can have the following structure:




where X1 and X2 are each independently a halogen, and in particular embodiments can be I, Br, Cl, or CF3SO3.

The organotin-functionalized cyclopenta[2,1-b:3,4-b′]dithiophene can have the following structure:




or the organotin-functionalized indaceno[1,2-b:5,6-b′]dithiophene can have the following structure:





where each R is independently hydrogen or a substituted or non-substituted alkyl, aryl or alkoxy chain, each R2 is independently methyl or n-butyl, and X is C, Si, Ge, N or P. In some embodiments, the R groups can be the same and the R2 groups can be the same.

The term “alkyl” refers to a branched or unbranched saturated hydrocarbyl group such as methyl, ethyl, n-propyl, isopropyl, n-butyl, isobutyl, t-butyl, octyl, decyl and the like. The term “aryl” refers to an aromatic hydrocarbyl group containing a single aromatic ring or multiple aromatic rings that are fused together, linked covalently, or linked to a common group such as a methylene or ethylene moiety. The term “alkoxy” refers to an alkyl group bound through a single, terminal ether linkage. The term “substituted” refers to a hydrocarbyl group in which one or more bonds to a hydrogen atom contained within the group is replaced by a bond to a non-hydrogen atom of a substituent group. Examples of non-hydrogen atoms include, but are not limited to, carbon, oxygen, nitrogen, phosphorus, and sulfur. Examples of substituent groups include, but are not limited to, halo, hydroxy, amino, alkoxy, aryloxy, nitro, ester, amide, silane, siloxy, and hydrocarbyl groups. The substituent can be a functional group such as hydroxyl, alkoxy, thio, phosphino, amino, or halo.
In particular embodiments of the cyclopenta[2,1-b:3,4-b′]dithiophene or indaceno[1,2-b:5,6-b′]dithiophene: the substituted or non-substituted alkyl, aryl or alkoxy chain can be a C6-C30 substituted or non-substituted alkyl or alkoxy chain, —(CH2CH2O)n (n=2 ̃20), C6H5, —CnF(2n+1) (n=2 ̃20), —(CH2)nN(CH3)3Br(n=2 ̃20), —(CH2)nN(C2H5)2 (n=2 ̃20), 2-ethylhexyl, PhCmH2m+1 (m=1-20), —(CH2)nSi(CmH2m+1)3 (m, n=1 to 20), or —(CH2)nSi(OSi(CmH2m+1)3)x(CpH2p+1)y (m, n, p=1 to 20, x+y=3); and/or X can be Si.
In some embodiments, the halogen-functionalized PT and/or the organotin-functionalized cyclopenta[2,1-b:3,4-b′]dithiophene are compounds of Scheme 1 or 2. In other embodiments, the halogen-functionalized PT and/or the organotin-functionalized indaceno[1,2-b:5,6-b′]dithiophene are compounds of Scheme 4.
The regioselectively prepared monomer can have the following structure:




where each R is independently hydrogen or a substituted or non-substituted alkyl, aryl or alkoxy chain, each R2 is independently methyl or n-butyl, X is C, Si, Ge, N or P, and X2 is a halogen. In particular embodiments, X2 can be I, Br, Cl, or CF3SO3. In some embodiments, the monomer has the following structure:





In these embodiments, each R or R1 is independently hydrogen or a substituted or non-substituted alkyl, aryl or alkoxy chain, and each R2 is independently methyl or n-butyl. In some embodiments, the substituted or non-substituted alkyl, aryl or alkoxy chain can be a C6-C30 substituted or non-substituted alkyl or alkoxy chain, —(CH2CH2O)n (n=2 ̃20), C6H5, —CnF(2n+1) (n=2 ̃20), —(CH2)nN(CH3)3Br(n=2 ̃20), or —(CH2)nN(C2H5)2 (n=2 ̃20), 2-ethylhexyl, PhCmH2m+1 (m=1-20), —(CH2)nSi(CmH2m+1)3 (m, n=1 to 20), or —(CH2)nSi(OSi(CmH2m+1)3)x(CpH2p+1)y (m, n, p=1 to 20, x+y=3); and/or X can be Si. In some embodiments, the R groups can be the same, the R1 groups can be the same, and the R2 groups can be the same.
In the method, the monomer is regioselectively prepared, then the monomer is reacted or polymerized to form a regioregular polymer having a regioregular conjugated main chain section. To form the regioregular polymer when the monomer is a CDT-PT monomer, the monomer can be reacted to itself, or reacted to another monomer containing a cyclopenta[2,1-b:3,4-b]dithiophene unit. When the monomer is a PT-IDT-PT monomer, the monomer can be reacted to another monomer containing an IDT-PT unit. The polymerization reaction can take place at a temperature in the range of about 80° C. to about 200° C. when the monomer is a CDT-PT monomer, and can take place at a temperature in the range of about 80° C. to about 200° C. when the monomer is a PT-IDT-PT monomer. The regioregular conjugated main chain section can comprise 5-100, or more, contiguous repeat units. In some embodiments, the number of repeat units is in the range of 10-40 repeats. The regioregularity of the conjugated main chain section can be 95% or greater.
The regioregular polymer in some embodiments has a main chain section that includes a repeat unit containing a pyridine of the structure




or a dithiophene of the structure





or a combination thereof, where each Ar is independently nothing or a substituted or non-substituted aromatic functional group, each R is independently hydrogen or a substituted or non-substituted alkyl, aryl or alkoxy chain, and X is C, Si, Ge, N or P. When Ar is nothing, the valence of the respective pyridine or thiophene ring is completed with hydrogen. In some embodiments, the R groups can be the same. The substituted or non-substituted aromatic functional group can include one or more alkyl or aryl chains, each of which independently can be a C6-C30 substituted or non-substituted alkyl or aryl chain, —(CH2CH2O)n (n=2 ̃20), C6H5, —CnF(2n+1) (n=2 ̃20), —(CH2)nN(CH3)3Br(n=2 ̃20), —(CH2)nN(C2H5)2 (n=2 ̃20), 2-ethylhexyl, PhCmH2m+1 (m=1-20), —(CH2)nSi(CmH2m+1)3 (m, n=1 to 20), or —(CH2)nSi(OSi(CmH2m+1)3)x (CpH2p+1)y (m, n, p=1 to 20, x+y=3). The substituted or non-substituted alkyl, aryl or alkoxy chain can be a C6-C30 substituted or non-substituted alkyl or alkoxy chain, —(CH2CH2O)n (n=2 ̃20), C6H5, —CnF(2n+1) (n=2 ̃20), —(CH2)nN(CH3)3Br(n=2 ̃20), 2-ethylhexyl, PhCmH2m+1 (m=1-20), —(CH2)nN(C2H5)2 (n=2 ̃20), —(CH2)nSi(CmH2m+1)3 (m, n=1 to 20), or —(CH2)nSi(OSi(CmH2m+1)3)x(CpH2p+1)y (m, n, p=1 to 20, x+y=3).

In embodiments of the regioregular polymer, the repeat unit of the regioregular conjugated main chain section can contain a pyridine unit of Table 1, where each R is independently a substituted or non-substituted alkyl chain, which can be a C6-C30 substituted or non-substituted alkyl chain, —(CH2CH2O)n (n=2 ̃20), C6H5, —CnF(2n+1) (n=2 ̃20), —(CH2)nN(CH3)3Br(n=2 ̃20), —(CH2)nN(C2H5)2 (n=2 ̃20), 2-ethylhexyl, PhCmH2m+1 (m=1-20), —(CH2)nSi(CmH2m+1)3 (m, n=1 to 20), or —(CH2)nSi(OSi(CmH2m+1)3)x(CpH2p+1)y (m, n, p=1 to 20, x+y=3); in some embodiments, the R groups can be the same.







TABLE 1





Examples of pyridine units





























 














 














 














 














 














 














 














 














 














 














 














 














 














 
















 










 










 

















In embodiments of the regioregular polymer, the repeat unit of the regioregular conjugated main chain section can contain a dithiophene unit of Table 2, where each R is independently a substituted or non-substituted alkyl, aryl or alkoxy chain, which can be a C6-C30 substituted or non-substituted alkyl or alkoxy chain, —(CH2CH2O)n (n=2 ̃20), C6H5, —CnF(2n+1) (n=2 ̃20), —(CH2)nN(CH3)3Br(n=2 ̃20), —(CH2)nN(C2H5)2 (n=2 ̃20), 2-ethylhexyl, PhCmH2m+1 (m=1-20), —(CH2)nSi(CmH2m+1)3 (m, n=1 to 20), or —(CH2)nSi(OSi(CmH2m+1)3)x(CpH2p+1)y (m, n, p=1 to 20, x+y=3); in some embodiments, the R groups can be the same, and in some embodiments, a repeat unit may contain any combination of a pyridine unit of Table 1 and dithiophene unit of Table 2.







TABLE 2





Examples of dithiophene units













 








 








 








 








 








 








 








 








 








 








 








 








 








 








 








 















In some embodiments, the regioregular polymer comprises a regioregular conjugated main chain having a repeat unit of the following structure:




where each R is independently hydrogen or a substituted or non-substituted alkyl, aryl or alkoxy chain, and X is C, Si, Ge, N or P. In particular embodiments, the repeat unit has the following structure:





where each R1 is independently hydrogen or a substituted or non-substituted alkyl, aryl or alkoxy chain. In some embodiments, the R groups can be the same, and the R1 groups can be the same. In some embodiments, each R or R1 can be a C6-C30 substituted or non-substituted alkyl, aryl or alkoxy chain, —(CH2CH2O)n (n=2 ̃20), C6H5, —CnF(2n+1) (n=2 ̃20), —(CH2)nN(CH3)3Br(n=2 ̃20), or —(CH2)nN(C2H5)2 (n=2 ̃20), 2-ethylhexyl, PhCmH2m+1 (m=1-20), —(CH2)nSi(CmH2m+1)3 (m, n=1 to 20), or —(CH2)nSi(OSi(CmH2m+1)3)x(CpH2p+1)y (m, n, p=1 to 20, x+y=3); and/or X can be Si. In some embodiments, the polymer is prepared by any of the methods described herein, or shown in Scheme 1, 2, or 4.

The charge carrier mobility of the regioregular polymer can be greater than the charge carrier mobility of a regiorandom polymer of similar composition.
Embodiments of the polymer may be incorporated in electronic devices. Examples of electronic devices include, but are not limited to, field effect transistors, organic photovoltaic devices, polymer light emitting diodes, organic light emitting diodes, organic photodetectors and biosensors.
The electronic devices can be solution coated, where the solution coating process can be, but is not limited to, the following: spin coating, ink jet printing, blade coating, dip coating, spraying coating, slot coating, gravure coating or bar coating.
The present invention may be better understood by referring to the accompanying examples, which are intended for illustration purposes only and should not in any sense be construed as limiting the scope of the invention.
EXAMPLE 1




To develop a region regular structure, the functionalized donor-acceptor (DA) monomer 2 was targeted as a polymerization precursor. The more stable tributyltin was used as the functional group in the CDT unit because trimethyltin is not very stable during the purification procedure. An optimized Stille cross-coupling procedure (Scheme 1) was conducted in comparatively mild reaction condition as low as 70° C., which would allow for the regioselectively more preferred reaction at the C4-position of Br/PT to form DA monomers 2a and 2b since more forcing conditions were needed for the C7-position. It was found that higher temperatures result in relatively complex mixtures that require tedious separation procedures. The isolation of 2a and 2b followed by microwave assisted Stille self-polymerization with Ph(PPh3)4 as catalyst in xylenes afforded regioregular P1a and P1b with precisely controlled PT regularity along polymer backbone. It was found that P1b with longer alkyl side chain yielded a higher molecular weight of 28.1 kDa than P1a with shorter alkyl side chains (15.4 kDa), a likely result of increased solubility during the polymerization reaction.




Alternatively, the coupling of 1a and 1b with 2 equivalents of PTBr2 and regioselective reaction of PTBr2 in C4-position can lead to the symmetric acceptor-donor-acceptor (ADA) 3a and 3b (Scheme 2) in high yield, respectively. Two single sharp resonances at 8.57 ppm (H in PT unit) and 8.57 ppm (H in CDT unit) in the 1H NMR spectra of both 3a and 3b match very well with their symmetric structures. Microwave assisted Stille polymerization of 3a and 3b with distannylated CDT monomer 4a and 4b yielded regiosymmetric polymers with high molecular weights of 27.1 kDa and 55.9 kDA for P2a and P2b, respectively.
For comparison, the regiorandom copolymers P3a and P3b (Scheme 3), in which the pyridal-N atom in the PT unit is randomly aligned along the polymer backbone, were synthesized via a one-pot polymerization of PTBr2 with distannyl CDT 4a or 4b. The obtained P3a and P3b have molecular weights of 20.0 kDa and 40.2 kDA, respectively.




To gain insight into the regioregularity of the polymer structures, high temperature 1H NMR spectroscopy was utilized (FIG. 1). The experiments where performed in deuterated tetrachloroethane (d-TCE) at 110° C. For all the three polymers P1b, P2b and P3b, the resonance at approximately δ 8.99 ppm could be assigned to the proton in PT unit, and the signal at 8.67 ppm could be assigned to the proton on the CDT moiety closest to the N atom of PT unit. The peaks from the proton in CDT unit situated away from the PT unit show slightly different chemical shifts for P1b (8.14 ppm), P2b (8.16 ppm) and P3b (8.15 ppm). In comparison to the narrow peaks for well-ordered P1b and P2b, the random P3b exhibits much broader peaks which might be generated from the complicated environment of the proton in CDT unit.
The influence of the regioregular structure on the effective n-conjugated properties could also be recognized in the UV-vis-near IR absorption of the three classes of polymers (FIG. 2). In o-dichlorobenze solution and as thin films, the maximum absorption (λmax) exhibits a gradual bathochromic shift from 825 nm for random P3a to 915 nm of regular P1a, and that of P2a lies in-between. Comparing the solution and film spectra, an approximate 50 nm bathochromic shift is observed when transitioning from solution to film, which could be attributed to the polymer interchain self-aggregation. P1b, P2b and P3b with C16 side chains displayed 20-30 nm shift (FIG. 4) to low energy wavelength, such shift could be attributed to the higher molecular weight and longer conjugation along polymer backbones. The optical band-gaps determined from the onset of film absorption were in range of 1.09-1.17 eV for all polymers (Table 3).







TABLE 3







Photophysical properties of polymers












in solutiona

filmsb

















λonset
λmax
λonset
Egopt c



Polymer
λmax (nm)
(nm)
(nm)
(nm)
(eV)







P1a
915
1078
905
1112
1.12



P2a
835
1063
864
1085
1.14



P3a
825
1040
840
1060
1.17



P1b
930
1128
920
1140
1.09



P2b
885
1078
885
1108
1.12



P3b
880
1074
870
1076
1.15







aIn o-dichlorobenzene solution.



bfilms were spin-coated from o-dichlorobenzene solution.



cMeasurements performed on spin-coated films from the onset of the absorption band.






Heating the o-DCB solutions to 110° C. did not distinctly change the absorption profile of the ordered P1a and P2a. However, the random P3a exhibited a 30 nm blue-shift with respect to the 25° C. solution (FIG. 4), possibly indicating the breakup of the aggregates at this temperature. Moreover, the absorption profiles after thermal annealing the films at 110° C. for 15 min. are very similar to the as casted films for all resulted polymers, with no distinct phase transition up to 300° C. by differential scanning calorimetry (DSC) measurement for all polymers (FIG. 5), which might indicate the weak interchain π-π stacking in films.
The electrochemical properties of all polymers were investigated to gain insight into the affect of polymeric structure on the frontier molecular orbitals. Full details on the cyclic voltammetry (CV) measurements can be found in the supporting information in Example 2 (FIG. 6 and Table 9).
From the data presented in Table 4, it is clear the regioregularity of polymer backbone has minimal affect on the lowest unoccupied molecular orbital (LUMO) level, while the highest occupied molecular orbital (HOMO) level energy is decreased with decreasing backbone order. The increase of the electrochemical band-gap of the random P3a and P3b compared to P2 and P1, again implies less effective charge localization along the polymer backbone. The larger electrochemical band-gap in comparison to the optical band gap could be attributed to the interfacial barrier for charge injection during the CV measurements.







TABLE 4







GPC, CV and optical band-gap data of polymers














Mna/

EHOMOb/
ELUMOb/
Egcv c/
Egopt d/


Polymer
kDa
PDI
eV
eV
eV
eV





P1a
15.4
1.84
−5.12
−3.70
1.42
1.12


P1b
28.1
1.93
−5.10
−3.71
1.39
1.09


P2a
27.2
2.60
−5.16
−3.69
1.47
1.14


P2b
55.9
4.15
−5.16
−3.65
1.51
1.12


P3a
20.0
2.21
−5.23
−3.64
1.59
1.17


P3b
40.2
2.50
−5.22
−3.68
1.54
1.15





aDetermined by GPC (150° C. in 1,2,4-trichlorobenzene).


bCalculated from the onsets of oxidation and reduction peaks, respectively.


cCalculated as the difference of the onset of the oxidation and reduction.


dMeasurements performed on spin-coated films from the onset of the absorption band.






Next, the impact of the backbone structure on the charge carrier mobility was investigated. Considering that the low-lying LUMO energy level of polymer will improve electron injection and allow for effective electron transport, ambipolar OFETs based on these polymers were investigated as shown in FIG. 3. Bottom gate, top contact FETs with structure of Si/SiO2/passivation layer/polymer (P1a, P2a or P3a)/Ag were fabricated by spin-coating from polymer solution on a highly n-doped silicon wafer with 200 nm of thermally-grown SiO2 gate dielectrics passivated by PPCB or OTS-8. (FIGS. 7 and 8). Distinct ambipolar characteristics were found at various thermal annealing temperatures. It is noticeable that both P1a and P2a exhibit higher charge mobility than that of the random copolymer P3a (Table 5).







TABLE 5







FET mobility (cm2 V−1 s−1) of polymers with Ag electrode











25° C.
90° C.
130° C.


Polymer
μhole/μelectron
μhole/μelectron
μhole/μelectron





P1aa
5.6 × 10−3/2.7 × 10−2
1.2 × 10−4/4.9 × 10−3
2.2 × 10−2/1.2 × 10−1


P1ab
4.8 × 10−2/2.4 × 10−3
4.9 × 10−2/1.2 × 10−3
3.5 × 10−2/1.6 × 10−3


P2aa
1.0 × 10−2/3.4 × 10−3
7.7 × 10−3/1.4 × 10−2
1.7 × 10−2/9.7 × 10−2


P2ab
6.4 × 10−2/2.0 × 10−2
6.3 × 10−2/5.3 × 10−3
9.4 × 10−2/3.1 × 10−3


P3aa
1.6 × 10−4/2.8 × 10−3
1.9 × 10−4/4.9 × 10−3
2.2 × 10−4/8.3 × 10−3


P3ab
6.3 × 10−5/2.1 × 10−4
4.7 × 10−5/4.4 × 10−5
4.5 × 10−5/3.8 × 10−6





aFET device with PPCB as passivation layer;


bOTS-8 as passivation layer






The strongly dependent of mobility of P1a on the annealing temperature was found. The best efficiency was obtained after thermal annealing of the device at 130° C., and the hole and electron mobility passivated by PPCB amounts to 2.2×10−2 and 1.2×10−1 cm2V−1 s−1, respectively, which is much higher than that from as-cast films (Table 6). Moreover, for FET based on P2a with OTS-8 passivation layer, the device also shows evident ambipolar behavior, exhibiting a hole and electron mobility of 9.4×10−2 and 3.1×10−3 cm2V−1 s−1 upon PPCB passivation, which is also much higher than that of the random P3a (Table 7). The distinct improvement of charge carrier mobility might be attributed to a more uniform orientation of the polymer chains in the solid-state.







TABLE 6







PPCB passivation hole mobility/electron mobility (cm2 V−1 s−1)












Polymer
25° C.
90° C.
110° C.
130° C.
150° C.





P1a
5.6 × 10−3/
1.2 × 10−4/
1.0 × 10−4/
2.2 × 10−2/
1.9 × 10−2/



2.7 × 10−2
4.9 × 10−3
7.0 × 10−3
1.2 × 10−1
9.6 × 10−2


P2a
1.0 × 10−2/
7.7 × 10−3/
9.8 × 10−3/
1.7 × 10−2/
1.4 × 10−2/



3.4 × 10−3
1.4 × 10−2
5.1 × 10−2
9.7 × 10−2
7.3 × 10−2


P3a
1.6 × 10−4/
1.9 × 10−4/
1.0 × 10−4/
2.2 × 10−4/
1.9 × 10−4/



2.8 × 10−3
4.9 × 10−3
7.0 × 10−3
8.3 × 10−3
1.3 × 10−2
















TABLE 7







OTS-8 passivation hole mobility/electron mobility (cm2 V−1 s−1)












Polymer
25° C.
90° C.
110° C.
130° C.
150° C.





P1a
4.8 × 10−2/
4.9 × 10−2/
4.5 × 10−2/
3.5 × 10−2/
4.5 × 10−2/



2.4 × 10−3
1.2 × 10−3
2.0 × 10−3
1.6 × 10−3
1.6 × 10−3


P2a
6.4 × 10−2/
6.3 × 10−2/
6.2 × 10−2/
9.4 × 10−2/
8.8 × 10−2/



2.0 × 10−2
5.3 × 10−3
1.4 × 10−3
3.1 × 10−3
1.1 × 10−3


P3a
6.3 × 10−5/
4.7 × 10−5/
3.2 × 10−5/
4.5 × 10−5/
7.1 × 10−5/



2.1 × 10−4
4.4 × 10−5
3.7 × 10−5
3.8 × 10−6
3.3 × 10−6









The on/off ratio of the top contact device with silver electrode is approximately 500. In order to achieve a higher on/off ratio, gold with a deeper work function was selected as electrode and moreover, bottom gate, and bottom contact FETs were fabricated based on polymers with C16 side chain (FIG. 9). It was found that after thermal annealing at 110° C. for 10 min, the hole mobility reached 0.15 and 0.14 cm2V−1 s−1 for P1b and P2b, respectively, which are much higher than the 0.025 cm2V−1 s−1 obtained by random copolymer P3b. The current on/off ratios for all FETs are improved to  ̃104 for all devices (Table 8).







TABLE 8







Temperature-dependent FET hole mobilities obtained from saturation


regime (μhole, cm2 V−1 s−1), and current on/off ratios (Ion:Ioff) for polymers on


Mitsubishi bottom-contact substrate, no passivation layer, 20 μm channel length.











25° C.
90° C.
110° C.













Polymer
μhole
Ion:Ioff
μhole
Ion:Ioff
μhole
Ion:Ioff





P1b
1.2 × 10−2
4.0 × 103
9.3 × 10−3
3.7 × 104
1.5 × 10−1
1.0 × 104


P2b
1.3 × 10−2
5.0 × 104
1.7 × 10−2
3.2 × 104
1.4 × 10−1
3.8 × 104


P3b
2.6 × 10−3
1.2 × 104
1.5 × 10−3
6.0 × 103
2.5 × 10−2
4.0 × 104





* The devices were post-annealed.






In summary, CDT and PT based narrow band-gap polymers with well-ordered main chain were prepared by precisely controlled regioselective chemistry. The resulted copolymers with regioregular structures show much longer conjugation length and better charge localization along the polymer backbone. The low-lying LUMO energy levels were realized for all polymers with the strong electron PT as acceptor, which resulted in the emergence of ambipolar properties for OFET devices. It was found that the regioregular polymers show much higher mobilities than the random copolymers under different OFET device configurations.
EXAMPLE 2
Instruments
Nuclear magnetic resonance (NMR) spectra were obtained on Bruker Avance DMX500 MHz spectrometer. Microwave assisted polymerizations were performed in a Biotage Initiator TM microwave reactor. Gel permeation chromatography (135° C. in 1,2,4-trichlorobenzene) was performed on a Polymer Laboratories PL220 Chromatograph. Differential scanning calorimetry (DSC) was determined by a TA Instruments DSC (Model Q-20) with about 5 mg polymers samples at a rate of 10° C./min in the temperature range of −20 to 300° C. UV-Vis absorption spectra were recorded on a Shimadzu UV-2401 PC dual beam spectrometer. Cyclic voltammetry (CVs) measurements were conducted using a standard three-electrode configuration under an argon atmosphere. A three-electrode cell equipped with a glassy carbon working electrode, a Ag wire reference electrode, and a Pt wire counterelectrode was employed. The measurements were performed in absolute acetonitrile with tetrabutylammonium hexafluorophosphate (0.1 M) as the supporting electrolyte at a scan rate of 50-100 mV/s. Polymer films were drop-cast onto the glassy carbon working electrode from a 2 mg/ml chloroform solution. The ferrocene/ferrocenium (Fc/Fc+) redox couple was used as an internal reference (see FIG. 6 and Table 9).







TABLE 9







CV data of polymers

















EHOMOf/


ELUMOf
Ege


Polymer
Eonseta/V
E1/2b/V
eV
Eonsetc/V
E1/2d/V
[eV]
[eV]





P1a
0.32
0.62
−5.12
−1.10
−1.36
−3.70
1.42


P2a
0.36
0.63
−5.16
−1.11
−1.33
−3.69
1.47


P3a
0.43
0.65
−5.23
−1.16
−1.36
−3.64
1.59


P1b
0.30
0.67
−5.10
−1.09
−1.38
−3.71
1.39


P2b
0.36
0.70
−5.16
−1.15
−1.38
−3.65
1.51


P3b
0.42
0.81
−5.22
−1.12
−1.32
−3.68
1.54





athe oxidation onset potential;


bthe oxidation redox potential E1/2 = (Epa + Epc)/2;


cthe reduction onset potential;


dthe reduction redox potential E1/2 = (Epa + Epc)/2;


ethe band-gap was calculated by the difference between the onset of oxidation and reduction potential;


fEHOMO = −e(Eox + 4.80) (eV), ELUMO = −e(Ered + 4.80) (eV), the potential of Ag reference calibrated by Fc/Fc+.






Materials

4H-Cyclopenta[2,1-b:3,4-b′]dithiophene (CDT) was purchased from WuXi AppTec Corporation. Toluene, THF and xylenes were purified according to standard procedures and distilled under nitrogen before use.
Synthesis of Monomers
(4,4-Didodecyl-4H-cyclopenta[1,2-b:5,4-b′]dithiophene-2,6-diyl)bis(tributylstannane) (1a)
A dry three-neck round bottom flask was equipped with a Schlenk adapter, dropping funnel, and rubber septum. Under nitrogen, 4,4-didodecyl-4H-cyclopenta[1,2-b:5,4-b]dithiophene (0.51 g, 1 mmol) was dissolved in dry THF (12 ml) and cooled −78° C. using a dry ice/acetone cold bath. Under nitrogen, a solution of t-butyllithium (1.7 M in pentane, 1.25 ml, 2.1 mmol) was added dropwise over 15 minutes to the reaction vessel. The reaction was stirred at −78° C. under nitrogen for one hour and at 25° C. for 5 hours. Then tributyltin chloride (0.81 g, 2.5 mmol) was added dropwise over 5 minutes to the reaction vessel via syringe at −78° C. The reaction was stirred at −78° C. under nitrogen for 1 hour and subsequently warmed to room temperature and stirred overnight. The mixture was then poured into deionized water (3×100 ml) and the organic phase was extracted with hexanes (3×100 ml). The organic phases were collected and washed with deionized water (5×100 ml), dried over sodium sulphate, filtered, and concentrated. The crude product was purified by flash column chromatography (Silica should be pretreated with 10 v/v % triethylamine/hexane solution) and dried under high vacuum to give 1.04 g of final product as yellowish oil, yield 95%. 1H NMR (500 MHz, CDCl3) δ (ppm): 6.93 (s, 2H), 1.81-1.78 (m, 4H), 1.61-1.56 (m, 12H), 1.36-1.08 (m, 60H), 0.98-0.75 (m, 28H).
(4,4-Dihexadecyl-4H-cyclopenta[1,2-b:5,4-b′]dithiophene-2,6-diyl)bis(tributylstannane) (1b)
A dry three-neck round bottom flask was equipped with a Schlenk adapter, dropping funnel, and rubber septum. Under nitrogen, 4,4-didodecyl-4H-cyclopenta[1,2-b:5,4-b]dithiophene (0.63 g, 1 mmol) was dissolved in dry THF (12 ml) and cooled −78° C. using a dry ice/acetone cold bath. Under nitrogen, a solution of t-butyllithium (1.7 M in pentane, 1.25 ml, 2.1 mmol) was added dropwise over 15 minutes to the reaction vessel. The reaction was stirred at −78° C. under nitrogen for one hour and at 25° C. for 5 hours. Then tributyltin chloride (0.81 g, 2.5 mmol) was added dropwise over 5 minutes to the reaction vessel via syringe at −78° C. The reaction was stirred at −78° C. under nitrogen for 1 hour and subsequently warmed to room temperature and stirred overnight. The mixture was then poured into deionized water (3×100 ml) and the organic phase was extracted with hexanes (3×100 ml). The organic phases were collected and washed with deionized water (5×100 ml), dried over sodium sulphate, filtered, and concentrated. The crude product was purified by flash column chromatography (Silica should be pretreated with 10 v/v % triethylamine/hexane solution) and dried under high vacuum to give 1.14 g of final product as yellowish oil, yield 95%. 1H NMR (500 MHz, CDCl3) δ (ppm): 6.98 (s, 2H), 1.86 (m, 4H), 1.78-1.52 (m, 12H), 1.46-1.12 (m, 80H), 1.01-0.88 (m, 24H). 13C NMR (125 MHz, CDCl3) (ppm): 158.34, 140.37, 133.89, 127.78, 50.13, 35.90, 32.76, 30.02, 29.68, 28.20, 27.80, 27.75, 27.55, 27.46, 27.18, 27.09, 27.00, 25.94, 25.52, 25.33, 25.30, 25.07, 24.94, 23.37, 22.76.
7-Bromo-4-(4,4-didodecyl-6-(tributylstannyl)-4H-cyclopenta[1,2-b:5,4-b′]dithiophen-2-yl)-[1,2,5]thiadiazolo[3,4-c]pyridine (2a)
To a solution of 4,7-dibromo-pyridal[2,1,3]thiadiazole (0.28 g, 0.95 mmol) and 1a (1.04 g, 0.95 mmol) in freshly distilled toluene (10 ml) was added Pd(PPh3)4 (109.8 mg, 0.095 mmol) under nitrogen, and then capped with a rubber septum. The reaction mixture was stirred at 75° C. for 10 hours. The solvent was removed and purified by column chromatography (silica was pretreated by 10 v/v % triethylamine/hexane solution) with hexane as eluent. The column separation was repeated for 3 times to give 0.31 g of viscous purple oil, yield 30%. 1H NMR (500 MHz, CD2Cl2) δ (ppm): 8.55 (s, 1H), 8.53 (s, 1H), 7.01 (s, 1H), 1.95-1.91 (m, 4H), 1.63-1.56 (m, 6H), 1.37-1.31 (m, 6H), 1.26-1.12 (m, 42H), 1.08-0.97 (m, 4H), 0.91-0.82 (m, 15H); 13C NMR (CDCl3, 125 MHz) δ (ppm): 163.11, 160.01, 156.33, 148.10, 147.92, 145.92, 143.99, 142.26, 141.81, 140.27, 129.80, 127.62, 106.17, 37.85, 31.88, 29.96, 29.61, 29.52, 29.34, 29.31, 28.98, 27.21, 24.57, 22.66, 13.85, 13.44, 10.95.
7-Bromo-4-(4,4-dihexadecyl-6-(tributylstannyl)-4H-cyclopenta[1,2-b:5,4-b′]dithiophen-2-yl)-[1,2,5]thiadiazolo[3,4-c]pyridine (2b)
To a solution of 4,7-dibromo-pyridal[2,1,3]thiadiazole (0.28 g, 0.95 mmol) and 1b (1.14 g, 0.95 mmol) in freshly distilled toluene (10 ml) was added Pd(PPh3)4 (109.8 mg, 0.095 mmol) under nitrogen, and then capped with a rubber septum. The reaction mixture was stirred at 75° C. for 10 hours. The solvent was removed and purified by column chromatography (silica was pretreated by 10 v/v % triethylamine/hexane solution) with hexane as eluent. The column separation was run for 3 times to give 268 mg of viscous purple oil, with yield of 25%. 1H NMR (500 MHz, CDCl3) δ (ppm): 8.92 (s, 1H), 8.49 (s, 1H), 7.39 (s, 1H), 2.21 (m, 4H), 1.77 (m, 6H), 1.54-1.25 (m, 68H), 1.12-1.01 (m, 15H). 13C NMR (125 MHz, CD2Cl2) δ (ppm): 163.10, 160.00, 156.32, 148.09, 147.92, 145.93, 144.00, 142.24, 141.83, 140.28, 129.79, 127.62, 106.17, 53.53, 37.86, 31.92, 29.97, 29.66, 29.63, 29.59, 29.54, 29.42, 29.39, 29.35, 29.32, 29.29, 29.02, 28.99, 27.21, 24.58, 22.69, 22.65, 13.88, 13.45, 10.96.
4,4′-(4,4-Didodecyl-4H-cyclopenta[1,2-b:5,4-H]dithiophene-2,6-diyl)bis(7-bromo-[1,2,5]thiadiazolo[3,4-c]pyridine) (3a)
To a solution of 4,7-dibromo-pyridal[2,1,3]thiadiazole (0.22 g, 0.75 mmol) and 1a (0.27 g, 0.25 mmol) in freshly distilled toluene (10 ml) was added Pd(PPh3)4 (28.9 mg, 0.025 mmol) under nitrogen. The reaction mixture was stirred at 75° C. for 48 hours. Then the solvent was removed and the mixture was purified by column chromatography with chloroform/hexane (from 0 to 60 v/v %). Then the crude product was precipitated from dichloromethane and methanol to give 0.17 mg of purple oil, yield 72%. 1H NMR (500 MHz, CDCl3) δ (ppm): 8.63 (s, 2H), 8.57 (s, 2H), 2.06-2.03 (m, 4H), 1.26-1.13 (m, 40H), 1.09 (t, J=4.0 Hz, 6H); 13C NMR (125 MHz, CD2Cl2) δ (ppm): 162.05, 156.40, 147.88, 147.69, 146.03, 143.60, 143.09, 126.80, 107.39, 54.63, 37.83, 31.87, 29.96, 29.63, 29.59, 29.56, 29.52, 29.34, 29.31, 24.66, 22.66, 14.10.
4,4′-(4,4-Dihexadecyl-4H-cyclopenta[1,2-b:5,4-b]dithiophene-2,6-diyl)bis(7-bromo-[1,2,5]thiadiazolo[3,4-c]pyridine) (3b)
To a solution of 4,7-dibromo-pyridal[2,1,3]thiadiazole (0.44 g, 1.5 mmol) and 1b (0.60 g, 0.5 mmol) in freshly distilled toluene (10 ml) was added Pd(PPh3)4 (57.8 mg, 0.05 mmol) under nitrogen. The reaction mixture was stirred at 75° C. for 48 hours. Then the solvent was removed and the mixture was purified by column chromatography with chloroform/hexane (from 0 to 60 v/v %). Then the crude product was precipitated from dichloromethane and methanol to give 280 mg of purple solid, yield 53%. 1H NMR (500 MHz, CDCl3) δ (ppm): 8.66 (s, 2H), 8.59 (s, 2H), 2.07 (m, 4H), 2.07 (m, 4H), 1.32-1.08 (m, 56H), 0.89 (t, J=6.70 Hz, 6H). 13C NMR (125 MHz, CD2Cl2) δ (ppm): 162.04, 156.34, 147.81, 147.59, 145.96, 143.59, 143.13, 126.79, 107.34, 54.60, 37.80, 31.92, 30.04, 29.65, 29.60, 29.35, 24.73, 22.69, 14.13.
(4,4-Didodecyl-4H-cyclopenta[1,2-b:5,4-b′]dithiophene-2,6-diyl)bis(trimethylstannane) (4a)
A dry three-neck round bottom flask was equipped with a Schlenk adapter, dropping funnel, and rubber septum. Under nitrogen, 4,4-didodecyl-4H-cyclopenta[1,2-b:5,4-b′]dithiophene (0.51 g, 1 mmol) was dissolved in dry THF (12 ml) and cooled −78° C. using a dry ice/acetone cold bath. Under nitrogen, a solution of t-butyllithium (1.7 M in pentane, 2.35 ml, 4 mmol) was added dropwise over 15 minutes to the reaction vessel. The reaction was stirred at −78° C. under nitrogen for one hour and stirred at room temperature for 3 hours. Under nitrogen, a solution of trimethyltin chloride (1.0 g, 5 mmol) in dry pentane (2 ml) was added dropwise over 5 minutes to the reaction vessel at −78° C. The reaction was stirred at −78° C. under nitrogen for 1 hour and subsequently warmed to room temperature and stirred overnight. The mixture was then poured into deionized water (3×100 ml) and the organic phase extracted with hexanes (3×50 ml). The organic phases were collected and washed with deionized water (3×50 ml), dried over sodium sulphate, filtered, and concentrated. The product was dried under high vacuum with agitation for 48 hours to give 0.80 g of product as colorless oil, yield 95%. 1H NMR (500 MHz, CD2Cl2) δ (ppm): 6.94 (s, 2H), 1.79-1.76 (m, 4H), 1.29-1.15 (m, 36H), 1.08-1.02 (m, 4H), 0.88 (t, J=6.0 Hz, 6H), 0.39 (s, 18H).
(4,4-Dihexadecyl-4H-cyclopenta[1,2-b:5,4-b′]dithiophene-2,6-diyl)bis(trimethylstannane) (4b)
A dry three-neck round bottom flask was equipped with a Schlenk adapter, dropping funnel, and rubber septum. Under nitrogen, 4,4-didodecyl-4H-cyclopenta[1,2-b:5,4-b]dithiophene (0.63 g, 1 mmol) was dissolved in dry THF (12 ml) and cooled −78° C. using a dry ice/acetone cold bath. Under nitrogen, a solution of t-butyllithium (1.7 M in pentane, 2.35 ml, 4 mmol) was added dropwise over 15 minutes to the reaction vessel. The reaction was stirred at −78° C. under nitrogen for one hour and stirred at room temperature for 3 hours. Under nitrogen, a solution of trimethyltin chloride (1.0 g, 5 mmol) in dry pentane (2 ml) was added dropwise over 5 minutes to the reaction vessel at −78° C. The reaction was stirred at −78° C. under nitrogen for 1 hour and subsequently warmed to room temperature and stirred overnight. The mixture was then poured into deionized water (3×100 ml) and the organic phase extracted with hexanes (3×50 ml). The organic phases were collected and washed with deionized water (3×50 ml), dried over sodium sulphate, filtered, and concentrated. The product was dried under high vacuum with agitation for 48 hours to give 0.92 g of white solid, yield 97%. 1H NMR (500 MHz, CD2Cl2) δ (ppm): 7.03 (s, 2H), 1.85 (m, 4H), 1.46-1.18 (m, 52H), 1.04 (m, 4H), 0.92 (t, J=6.65 Hz, 6H), 0.42 (t, 18H). 13C NMR (125 MHz, CD2Cl2) δ (ppm): 160.57, 142.11, 137.21, 129.58, 52.21, 37.62, 34.63, 34.57, 31.97, 31.94, 31.59, 30.03, 29.69, 29.63, 29.59, 29.36, 25.24, 24.63, 22.66, 20.42, 13.88.
Polymerization of P1a
Monomer 2a (0.16 g, 0.16 mmol) was carefully weighed and added to a 2-5 mL microwave tube. The tube was transferred into a glovebox, and then Pd(PPh3)4 (4.4 mg, 0.005 mmol), and 3.2 mL of xylenes were added into the microwave tube. The tube was sealed, removed from the glovebox and subjected to the following reaction conditions in a microwave reactor: 80° C. for 2 min, 120° C. for 2 min, 160° C. for 2 min and 200° C. for 40 min. The reaction was allowed to cool leaving a viscous liquid containing some solid material. After the polymerization, 2-bromothiophene (1.9 μl 0.02 mmol) and 2 mL of xylenes was added, the mixture was stirred at 110° C. for 2 hours. And then tributyl(thiophen-2-yl)stannane (0.01 mL, 0.04 mmol) was added dropwise and stirred at 110° C. for 2 hours. Then the mixture was dissolved in hot 1,2-dichlorobenzene, then precipitated into methanol and collected via centrifugation. The residual solid was loaded into a cellulose extraction thimble and washed successively with methanol (3 hrs), hexanes (16 hrs), and acetone (3 hrs). The remaining polymer was dried on a high vacuum line overnight. Yield 92 mg (88%). 1H NMR (500 MHz, C2D2Cl4, 110° C.) δ (ppm): 9.00 (s, 1H), 8.67 (s, 1H), 8.14 (s, 1H), 2.30-0.76 (m, 50H). 13C NMR (Solid-state, 75 MHz), δ (ppm): 159.57, 151.45, 145.77, 142.29, 138.67, 124.42, 116.17, 113.81, 52.57, 36.06, 29.83, 25.53, 22.61, 13.84.
Polymerization of P1b
Monomer 2b (128 mg, 0.11 mmol) and Pd2(dba)3 (5.2 mg, 0.0057 mmol), P(o-Tol)3 (6.9 mg, 0.023 mmol) and freshly distilled xylenes (4 ml) was added to a 2-5 ml microwave tube under nitrogen. The mixture was heated to 95° C. on the oil bath and stirred for 12 hours. After that, tributyl(thiophen-2-yl)stannane (20 μl) was added and the reaction was stirred at 95° C. for 6 hours, then 2-bromothiophene (20 μl) was added and the reaction was stirred for another 6 hours. The mixture was precipitated in methanol, the resulted dark green fibers were collected and was re-dissolved in hot 1,2-dichlorobenzene. Then re-precipitated in methanol and collected via centrifugation. The collected solid fibers were loaded into a cellulose extraction thimble and washed successively with methanol (6 hours), acetone (6 hours), hexanes (12 hours) and chloroform (24 hours). The solid residue in the thimble was collected and dried followed by re-dissolved in hot 1,2-dichlorobenzene, filtrated and re-precipitated in methanol. Then the resulted dark-green fibers were collected via centrifugation, dried over high vacuum line to give 61 mg of polymers, yield 80%. 1H NMR (500 MHz, C2D2Cl4, 110° C.) δ (ppm): 8.99 (s, 11-f), 8.67 (s, 1H), 8.14 (s, 1H), 2.26-0.82 (m, 66H).
Polymerization of P2a
The polymer was prepared following a previously reported microwave assisted polymerization technique. Two monomers 3a (0.18 g, 0.19 mmol) and 4a (0.17 g, 0.20 mmol) were carefully weighed and added to a 2-5 mL microwave tube. The tube was transferred into a glovebox, and then Pd(PPh3)4 (9 mg, 0.008 mmol) and 3 mL of Xylenes were added into the microwave tube. The tube was sealed, removed from the glovebox and subjected to the following reaction conditions in a microwave reactor: 80° C. for 2 min, 120° C. for 2 min, 160° C. for 2 min and 200° C. for 40 min. The reaction was allowed to cool leaving a viscous liquid containing some solid material. After the polymerization, 2-bromothiophene (1.9 μl, 0.02 mmol) and 2 mL of xylenes was added, the mixture was stirred at 110° C. for 2 hours. And then tributyl(thiophen-2-yl)stannane (0.01 mL, 0.04 mmol) was added dropwise and stirred at 110° C. for 2 hours. The mixture was dissolved in hot 1,2-dichlorobenzene, then precipitated into methanol and collected via centrifugation. The residual solid was loaded into a cellulose extraction thimble and washed successively with methanol (4 hrs), hexanes (16 hrs), and acetone (3 hrs). The remaining polymer was dried on a high vacuum line overnight. Yield 225 mg (91%). 1H NMR (500 MHz, C2D2Cl4, 110° C.) δ (ppm): 8.99 (s, 1H), 8.67 (s, 1H), 8.16 (s, 1H), 2.30-0.72 (m, 50H). 13C NMR (Solid-state, 75 MHz) δ (ppm): 158.76, 151.90, 143.27, 138.063, 123.15, 117.44, 52.74, 36.06, 29.75, 25.53, 22.55, 13.78.
Polymerization of P2b
Monomers 3b (158.3 mg, 0.15 mmol) and 4b (142.9 mg, 0.15 mmol) were added to a 2-5 mL microwave tube, then Pd(PPh3)4 (8.7 mg, 0.0075 mmol) and freshly distilled xylenes (4 ml) were added into the microwave tube. The tube was sealed and subjected to the following reaction conditions in a microwave reactor: 80° C. for 2 min, 130° C. for 2 min, 170° C. for 2 min and 200° C. for 40 min. The reaction was allowed to cool to room temperature, then tributyl(thiophen-2-yl)stannane (20 μl) was added and the reaction was subjected to the following reaction conditions in a microwave reactor: 80° C. for 2 min, 130° C. for 2 min, 170° C. for 2 min and 200° C. for 20 min. After the reaction was cooled to room temperature, 2-bromothiophene (20 μl) was added and the end-capping procedure was repeated once again. The mixture was precipitated in methanol, collected via centrifugation. The collected solid fibers were loaded into a cellulose extraction thimble and washed successively with methanol (6 hours), acetone (6 hours), hexanes (12 hours), and the polymer comes out with chloroform (within 2 hours) from the thimble. Chloroform was removed under reduced pressure and resulted dark-green solid was dried over high vacuum line to give 130 mg of polymer, yield 85%. 1H NMR (500 MHz, C2D2Cl4, 110° C.) δ (ppm): 8.99 (s, 1H), 8.67 (s, 1H), 8.16 (s, 1H), 2.30-0.81 (m, 66H).
Polymerization of P3a
The polymerization was performed following the procedure for P2a in microwave reactor, just replacing monomer 3a by 4,7-dibromo-pyridal[2,1,3]thiadiazole (44.2 mg, 0.15 mmole). The resulted dark-green solid was dried over high vacuum line to give 91 mg of polymer, yield 80%. 1H NMR (500 MHz, C2D2Cl4, 110° C.) δ (ppm): 8.99 (s, 1H), 8.67 (s, 1H), 8.15 (s, 1H), 2.32-0.79 (m, 50H). 13C NMR (Solid-state, 75 MHz) δ (ppm): 159.04, 152.06, 142.95, 138.39, 124.16, 117.54, 52.87, 36.01, 29.72, 25.67, 22.53, 13.76.
Polymerization of P3b
The polymerization was performed following the procedure for P2b in microwave reactor, just replacing monomer 3b by 4,7-dibromo-pyridal[2,1,3]thiadiazole (44.2 mg, 0.15 mmole). The resulted dark-green solid was dried over high vacuum line to give 101 mg of polymer, yield 86%. 1H NMR (500 MHz, C2D2Cl4, 110° C.) δ (ppm): 8.99 (s, 1H), 8.67 (s, 1H), 8.15 (s, 1H), 2.35-0.84 (m, 66H).
EXAMPLE 3A
To apply the regioregular PT based copolymer in an OPV device, we chose indacene-PT based copolymers due to (1) the broad narrow-bandgap absorption, (2) the two thiophene rings rigidified together with a central phenyl ring, which can provide strong intermolecular interactions for ordered packing to improve the charge carrier mobility, and (3) the low-lying HOMO level of the copolymer will provide high open-circuit voltage (Voc) (see Jen et al. [11])
Result and Discussion
As shown in Scheme 4, the copolymerization of dibromo monomer Br-PT-IDT-PT-Br (M2) with bis(stannyl) monomer Me3Sn-IDT-SnMe3 (M1) was based on microwave assisted Stille coupling reaction to generate the regioregular indacenothiophene-PT based copolymer (PIPT-RG), which has the N-atom in the PT units selectively faced to the same indacene core. The reference polymer (PIPT-RA) was synthesized based on microwave assisted step-growth Stille copolymerization of M1 and 4,7-dibromo-pyridal[2,1,3]thiadiazole (PTBr2), thus providing the polymer with the N-atom in the PT units randomly distributed along the polymer main chain. Both copolymers were purified by Soxhlet extraction using methanol, acetone, hexane and finally collected by chloroform. The polymer structures are shown in Scheme 5.








The number average molecular weight (Mn) estimated by gel permeation chromatography (GPC) with chloroform as eluent and linear polystyrene as the reference at 35° C. is 68 kDa (PDI=2.4) for PIPT-RG and 59 kDa (PDI=2.5) for PIPT-RA; the GPC profiles are shown in FIG. 10. In contrast, GPC in 1,2,4-trichlorobenze (1,2,4-TCB) as eluent at 150° C. gave 46 kDa and 42 kDa for PIPT-RG and PIPT-RA, with a polydispersity of 2.3 and 2.8, respectively. The slightly lower Mn can be attributed to less aggregation in high temperature 1,2,4-TCB solution. Interestingly, both copolymers exhibited excellent solubility of higher than 15 mg/ml in xylenes, chloroform, chlorobenzene as well as 1,2-dichlorobenzene, which provides the opportunity to fabricate thick films based solution process procedures. No noticeable phase transitions were observed by differential scanning calorimetry up to 300° C. in both cases (FIG. 11).
UV-Vis absorption profiles of PIPT-RG and PIPT-RA in thin films are shown in FIG. 12. The absorption profile shapes are essentially the same for both copolymers. The short wavelength absorption bas ( ̃417 nm) is assigned to a delocalized excitonic π-π* transition and the long wavelength absorption band ( ̃715 nm) is ascribed to intramolecular charge transfer (ICT) interactions between the donor and acceptor moieties. However, the absorption intensity of PIPT-RG is much stronger than that of PIPT-RA, indicating a much higher molar absorption coefficient of PIPT-RG. The optical band gaps (Eg) calculated from the absorption onset are determined to be 1.60 eV for PIPT-RG, which is slightly lower than that of 1.62 eV for PIPT-RA.
Cyclic voltammetry (CV) and ultraviolet photoelectron spectroscopy (UPS) were employed to evaluate the oxidation/reduction properties and electrical stability of the polymers. As can be seen in the CV curves in FIG. 13a, the onset of reduction (Ered) of the two copolymers were nearly identical and was located at about −1.20 V versus Ag/Ag+, while the onset of oxidation (Eox) were 0.45 V and 0.55 V for PIPT-RG and PIPT-RA, respectively. The slightly higher Eox of PIPT-RA to that of PIPT-RG might be attributed to the more disordered vector of the PT unit along the polymer main chain, which would disturb the π-conjugated electron distribution along the polymer backbone leading to a slightly raised Eox. The highest occupied molecular orbital energy level (EHOMO) and the lowest unoccupied molecular orbital energy level (ELUMO) were calculated from the Eox and Ered, on the basis of the assumption that EHOMO of ferrocene/ferrocenium (Fc/Fc+) is at 4.8 eV relative to vacuum. The calculated EHOMO are −5.25 eV and −5.35 eV for PIPT-RG and PIPT-RA, respectively, and the ELUMO are both at −3.60 eV. This is understandable since for such “donor-acceptor” based copolymers, the LUMO is mainly located in the acceptor and the HOMO is well-delocalized along the conjugated backbone, thus the two copolymers exhibited nearly identical ELUMO while slightly different EHOMO. Further evaluation by ultraviolet photoelectron spectroscopy (UPS) measurements (FIG. 13b) demonstrated that the EHOMO of the two copolymers are quite similar, located at −5.31 eV and −5.33 eV for PIPT-RG and PIPT-RA, respectively, Nevertheless, the relatively low-lying EHOMO indicated that high Voc could be realized.
The field-effect hole mobilities of PIPT-RG and PIPT-RA were extracted from the transfer characteristics (FIG. 14) of field-effect transistors (FETs) fabricated with bottom contact, bottom gate geometry using Au electrodes. It was noted that the calculated mobilities for PIPT-RG at room temperature of 0.13 cm2/Vs improved to 0.18 and 0.20 cm2/Vs after thermal annealing at 100° C. and 150° C. for 10 min, respectively. These are higher than for devices prepared under the same conditions with a PIPT-RA copolymer film of 0.04 cm2/Vs at room temperature, and 0.09 and 0.04 cm2/Vs attained after thermal annealing at 100° C. and 150° C. for 10 min, respectively. The higher carrier mobility achieved with regioregular PIPT-RG than the regiorandom counterpart PIPT-RA indicates that better charge transport in the active layer could be achieved. The detailed FET data were summarized in Table 10.







TABLE 10







FET performances of bottom gate top-contact device structures












polymer
Tanneal (° C.)
μhole (cm2/Vs)
Ion/Ioff







PIPT-RG
—
0.13
4 × 104




100
0.18
1 × 104




150
0.20
4 × 103



PIPT-RA
—
0.04
1 × 104




100
0.09
7 × 103




150
0.04
2 × 103










The microstructures of two copolymer films were investigated by grazing incident X-ray diffraction (XRD). The samples were prepared on the top of (n-decyl)trichlorosilane (DTS) treated silicon substrate according to the same procedure of FET devices. The films were thermally annealed at 100° C. for 10 min. As shown in FIG. 15, the scattering features with two distinct peaks centered at q values of 0.42 Å−1 (spacing of 14.9 Å) and 1.42 Å−1 (spacing of 4.4 Å) were realized for both copolymers. However, more fine structures could be realized for the random copolymer PIPT-RA, which shows small bumpy scattering features with q values of 0.63 Å−1 (spacing of 9.9 Å) and 1.21 Å−1 (spacing of 5.2 Å). Such relatively weak scattering features might be attributed to the combination of various structures in random copolymers.
In considering that the copolymers were used as donor materials for bulk heterojunction solar cells, the contact of active layer with following deposited metal is of particular importance. The surface morphologies of copolymer:PC71BM (1:4 in wt:wt) films were studies by tapping-mode atomic force microscopy (AFM), and the films were spin-casted from copolymer:PC71BM solution on the top of ITO/MoOx layer and followed the optimized conditions for solar cell devices. Even though the solar cell devices based on PIPT-RG:PC71BM as active layer showed much higher power conversion efficiency (5.1%) than that of achieved by PIPT-RA:PC71BM device (3.4%), we noted that both films were quite smooth with root-mean-square (rms) value ̃0.3 nm (FIG. 16).
To further understand the microstructure differences in both films, we used transmission electron microscopy (TEM) to investigate the microstructure inside both films. It was realized that both PIPT-RG:PC71BM (FIG. 17a) and PIPT-RA:PC71BM (FIG. 17b) films exhibited relatively uniform images. It should be noted that the dark spots with size of 10 ̃20 nm in FIG. 17(a) might be attributed to the metallic residue.
EXAMPLE 3B
Materials and Methods for Example 3A
Instruments
Nuclear magnetic resonance (NMR) spectra were obtained on Bruker Avance DMX500 MHz spectrometer. Gel permeation chromatography (150° C. in 1,2,4-trichlorobenzene) was performed on a Polymer Laboratories PL220 Chromatograph. GPC with chloroform as eluent was performed in chloroform (with 0.25 v/v % triethylamine) on a Waters system, and the molecular weight of polymers were estimated relative to linear PS standards. Differential scanning calorimetry (DSC) was determined by a TA Instruments DSC (Model Q-20) with about 5 mg polymers samples at a rate of 10° C./min in the temperature range of −20 to 300° C. UV-Vis absorption spectra were recorded on a Shimadzu UV-2401 PC dual beam spectrometer. Cyclic voltammetry (CV) measurements were conducted using a standard three-electrode configuration under an argon atmosphere. A three-electrode cell equipped with a glassy carbon working electrode, a Ag wire reference electrode, and a Pt wire counterelectrode was employed. The measurements were performed in absolute acetonitrile with tetrabutylammonium hexafluorophosphate (0.1 M) as the supporting electrolyte at a scan rate of 50-100 mV/s. Polymer films for CV test were drop-casted onto the glassy carbon working electrode from a 2 mg/mL chloroform solution. The absolute energy level of ferrocene/ferrocenium (Fc/Fc+) to be 4.8 eV below vacuum. Grazing incident X-ray diffraction was performed on Rigaku Smart instrument. Atomic force microscopy (AFM) was recorded on Asylum MFP3D instrument. All the samples were prepared identical to optimized device structure and conditions prior to electrode deposition. Transmission Electron Microscope (TEM) was performed on FEI Tecnai G2 Sphera Microscope instrument. The samples were prepared by spin-casting on the top of glass substrate and floated in water, following by put on the top of copper grid.
Synthesis of Monomers
(4,4,9,9-Tetrakis(4-hexylphenyl)-4,9-dihydro-s-indaceno[1,2-b′]dithiophene-2,7-diyl)bis(trimethylstannane) (M1)
A dry three-neck round bottom flask was equipped with a Schlenk adapter, dropping funnel, and rubber septum. Under nitrogen, 2,7-dibromo-4,4,9,9-tetrakis(4-hexylphenyl)-4,9-dihydro-s-indaceno[1,2-b:5,6-b′]dithiophene (1.06 g, 1 mmol) was dissolved in dry TI-IF (20 mL) and cooled −78° C. using a dry ice/acetone cold bath. Under nitrogen, a solution of n-butyllithium (1.6 M in hexane, 1.50 mL, 2.4 mmol) was added dropwise over 15 minutes to the reaction vessel. The reaction was stirred at −78° C. under nitrogen for one hour. Then trimethyltin chloride (0.60 g, 3.0 mmol) was added dropwise over 5 minutes to the reaction vessel via syringe at −78° C. The reaction was stirred at −78° C. under nitrogen for 1 hour and subsequently warmed to room temperature and stirred overnight. The mixture was then poured into deionized water (3×100 mL) and the organic phase was extracted with hexanes (3×100 mL). The organic phases were collected and washed with deionized water (5×100 mL), dried over sodium sulphate, filtered, and concentrated. The crude product was recrystallized from hexane/ethanol (10/90) and dried under high vacuum to give 1.07 g of final product as white needles, yield 87%. NMR (500 MHz, CDCl3) δ (ppm): 7.48 (s, 2H), 7.21 (d, 8H), 7.13 (d, 8H), 2.63 (t, J=7.75 Hz, 8H), 1.66-1.57 (m, 8H), 1.42-1.30 (m, 24H), 0.89 (m, 12H), 0.41 (s, 18H). 13C NMR (125 MHz, CD2Cl2) δ (ppm): 157.64, 153.75, 147.14, 142.31, 141.90, 141.54, 134.71, 130.44, 128.35, 128.28, 127.81, 127.75, 117.65, 62.19, 35.48, 31.76, 31.66, 29.16, 22.64, 13.89, −8.39. HRMS (FD) m/z, calcd for Chemical Formula: C70H90S2Sn2 (M+): 1232.45. found: 1232.5.
4,4′-(4,4,9,9-Tetrakis(4-hexylphenyl)-4,9-dihydro-s-indaceno[1,2-b:5,6-b′]dithiophene-2,7-diyl)bis(7-bromo-[1,2,5]thiadiazolo[3,4-c]pyridine) (M2)
To a 10-20 mL microwave tube was added M1 (0.616 g, 0.5 mmol), 4,7-dibromo-pyridal[2,1,3]thiadiazole (0.295 g, 1 mmol), Pd(PPh3)4 (57.8 mg, 0.05 mmol) and freshly distilled toluene (10 mL) under the protection of nitrogen, then the microwave tube was sealed. The microwave assisted Stille coupling was performed in the following procedure: 120° C. for 10 min, 140° C. for 10 min, 160° C. for 10 min and 170° C. for 40 min. The reaction was cooled down to room temperature, extracted with chloroform (100 mL×3), washed with deionized water (100 mL×3) and dried over with anhydrous magnesium sulfate. After removing solvent under reduced pressure, the mixture was separated by silica column with hexane/chloroform (form 100/0 to 0/100 in v/v) to give 0.553 g of dark-red oil, yield of 83%. 1H NMR (500 MHz, CDCl3) δ (ppm): 8.64 (s, 2H), 8.60 (s, 2H), 7.65 (s, 2H), 7.31 (s, 8H), 7.16 (s, 8H), 2.61 (s, 8H), 1.63 (s, 8H), 1.45-1.26 (m, 24H), 0.90 (s, 121-1). 13C NMR (125 MHz, CD2Cl2) δ (ppm): 158.11, 156.29, 154.63, 147.74, 147.54, 147.38, 145.91, 143.86, 141.84, 141.37, 136.01, 128.69, 128.55, 127.95, 127.95, 118.61, 107.54, 63.27, 35.60, 31.73, 31.35, 29.17, 22.61, 14.11. HRMS (FD) m/z, calcd for C74H74Br2N6S4 (M+): 1334.32. found: 1334.3.
Polymerization of PIPT-RG
Monomer M1 (123.3 mg, 0.1 mmol), M2 (133.4 mg, 0.1 mmol), Pd(PPh3)4 (5.8 mg, 0.005 mmol) and freshly distilled xylenes (3 mL) was added to a 2-5 mL microwave tube under nitrogen. The tube was sealed and subjected to the following reaction conditions in a microwave reactor: 80° C. for 2 min, 120° C. for 2 min, 160° C. for 2 min and 180° C. for 40 min. The reaction was allowed to cool to room temperature, then freshly distilled xylenes (2 mL) and tributyl(thiophen-2-yl)stannane (20 μl) was added and the reaction was subjected to the following reaction conditions in a microwave reactor: 80° C. for 2 min, 130° C. for 2 min, 170° C. for 2 min and 200° C. for 20 min. After the reaction was cooled to room temperature, 2-bromothiophene (20 μl) was added and the reaction was subjected to the following reaction conditions in a microwave reactor: 80° C. for 2 min, 130° C. for 2 min, 170° C. for 2 min and 200° C. for 20 min. The mixture was precipitated in methanol, collected via centrifugation, then re-dissolved in hot 1,2-dichlorobenzene and re-precipitated in methanol and collected via centrifugation. The collected solid fibers were loaded into a cellulose extraction thimble and washed successively with methanol (12 hours), acetone (12 hours) and hexanes (12 hours), and then chloroform (2 hours) to collected the copolymer. The solid residue in the thimble was collected and dried followed by re-dissolved in hot 1,2-dichlorobenzene, filtrated and re-precipitated in methanol. Then the resulted dark-green fibers were collected via centrifugation, dried over high vacuum line to give 156 mg of polymers, yield 75%. GPC with chloroform as eluent showed the Mn=68 kDa (PDI=2.4). 1H NMR (500 MHz, 1,2-dichlorobenzene-d4, 110° C.) δ (ppm): 8.90 (s, 1H), 8.84 (s, 1H), 8.40 (s, 1H), 8.12 (s, 1H), 8.04 (s, 1H), 7.80-7.50 (br s, 8H), 7.30-7.15 (br s, 8H), 2.70 (br s, 8H), 1.71 (s, 8H), 1.55-1.32 (m, 24H), 0.98 (s, 12H). 13C NMR (125 MHz, 1,2-dichlorobenzene-d4, 110° C.) δ (ppm): 180.06, 169.02, 163.49, 157.70, 141.59, 132.15, 130.04, 129.84, 129.71, 129.63, 129.42, 127.32, 127.22, 127.12, 127.05, 126.95, 126.85, 126.75, 126.65, 126.40, 102.74, 63.62, 35.38, 31.49, 30.98, 30.79, 28.88, 22.31, 13.61.
Polymerization of PIPT-RA
The polymerization was performed following the procedure for PIPT-RG in microwave reactor. The monomer M1 (246.6 mg, 0.2 mmol), and replacing monomer M2 by 4,7-dibromo-pyridal[2,1,3]thiadiazole (59.0 mg, 0.2 mmol), Pd(PPh3)4 (11.5 mg, 0.01 mmol) and xylenes (3 mL). The resulted dark-green solid was dried over high vacuum line to give 168.5 mg of polymer, yield 81%. GPC with chloroform as eluent showed the Mn=59 kDa (PDI=2.5). 1H NMR (500 MHz, 1,2-dichlorobenzene-d4, 110° C.) δ (ppm): 8.86 (s, 1H), 8.81 (s, 1H), 8.35 (s, 1H), 8.12 (s, 1H), 8.03 (s, 1H), 7.82-7.49 (br s, 8H), 7.36-7.18 (br s, 8H), 2.66 (br s, 8H), 1.70 (s, 8H), 1.52-1.38 (m, 24H), 0.92 (s, 121-1). 13C NMR (125 MHz, 1,2-dichlorobenzene-d4, 110° C.) δ (ppm): 180.07, 169.03, 163.50, 157.99, 141.56, 132.19, 130.24, 129.94, 129.81, 129.80, 129.58, 127.45, 127.32, 127.22, 127.18, 127.06, 126.97, 126.86, 126.72, 126.51, 102.83, 63.84, 35.39, 32.38, 31.50, 29.10, 22.47, 13.74.
UPS Characterization
An Au film of 75 nm was deposited on a precleaned Si substrate with a thin native Oxide. A solution containing a mixture of PIPT-RA (or PIPT-RG):PC71BM (1:4) in ODCB solvent with a concentration of 2 mg/mL was then spin-casted atop the Au film. The total time of spin coating was kept at 60 s for the two samples. Film fabrication was done in a N2-atmosphere glove box. To minimize possible influence by exposure to air, the films were then transferred from the N2-atmosphere dry box to the analysis chamber inside an air-free sample holder. Subsequently, the samples were kept inside a high-vacuum chamber overnight, to remove solvent. The UPS analysis chamber was equipped with a hemispherical electron-energy analyzer (Kratos Ultra spectrometer), and was maintained at 1.33×10−7 Pa. The UPS was measured using the He I (hv=21.1 eV) source, and he electron energy analyzer was operated at constant pass energy of 10 eV. During the measurements, a sample bias of −9 V was used in order to separate the sample and the secondary edge for the analyzer. In order to confirm reproducibility of UPS spectra, we repeated these measurements twice on two sets of samples.
FET Device Fabrication
Semiconducting polymers, 0.5 wt % PIPT-RG or PIPT-RA dissolved in chlorobenzene. The copolymers were stirring under 110° C. before usage. Heavily doped n-type silicon substrates with 200 nm thermally grown SiO2 were prepared as bottom gate electrode. After SiO2 dielectric was passivated by OTS8 (octyl(trichlorosilane)), all three polymers were spun onto substrates by 2000 rpm/1 min. 60 nm thick film was created. Coated substrates were sequentially heated under 80° C. for 10 min. Thermal evaporator was applied to deposit 100 nm metal contacts on polymer layer through a silicon shadow mask. Defined channel was 20 μm long and 1 mm wide. Devices were tested on a Signatone probe station inside a nitrogen glovebox with atmosphere <1 ppm oxygen concentration. Data were all collected by a Keithley 4200 system. Mobility was extracted from saturation regime based on the following equation,




  
    I
    D
  
  =
  
    
      1
      2
    
    ⁢
    μ
    ⁢
    
      
    
    ⁢
    C
    ⁢
    
      W
      L
    
    ⁢
    
      
        (
        
          
            V
            G
          
          -
          
            V
            T
          
        
        )
      
      2
    
  




where, W is the channel width (1 mm), L is the channel length (20 μm), μ is the carrier mobility, VG is the gate voltage, and VT is the threshold voltage. The capacitance, C, of the SiO2 is 14 nF/cm2.

EXAMPLE 3C
Polymer Solar Cells
Device Architecture: ITO/Thermal Evaporated MoOx/Polymer:PCBM/Al (Conventional)
Fabrication of PSCs: Polymer solar cells with conventional device architecture of ITO/MoOx/polymer:PCBM/Al were fabricated according to the following procedure. The ITO-coated glass substrates were firstly cleaned by ultrasonic treatment in detergent, deionized water, acetone and isopropyl alcohol for 30 minutes each, and subsequently dried in an oven overnight. MoOx film was deposited onto ITO substrates by thermal evaporation in a vacuum of about 1×10−6 Torr. The evaporation rate was 0.1 Å/s. Two solutions containing a mixture of PIPT-RA:PC71BM (1:4) and PIPT-RG:PC71BM (1:4) in o-DCB with a concentration of 10 mg/ml were spin-casted on top of MoOx film, respectively. The thickness of blend films were controlled by the spin-casting speed and optimized at 80 nm. After that, the BHJ films were annealing at 100° C. for 10 min. Finally, the cathode (Al,  ̃100 nm) was deposited through a shadow mask by thermal evaporation in a vacuum of about 3×10−6 Torr. The active area of device was 0.106 cm2.
PSCs Characterization: The thickness of the multilayer was measured with a profilometer and Atomic Force Microscope (AFM), respectively. Current density-voltage (J-V) characteristics were measured using a Keithley 2602 Source measure Unit, under solar simulation conditions of 100 mW/cm2AM 1.5 G using a 300 W Xe arc lamp with an AM 1.5 global filter. The illumination intensity of the solar simulator was measured using a standard silicon photovoltaic with a protective KG1 filter calibrated by the National renewable Energy Laboratory.
Devices data: FIG. 18 (a) illustrates the characteristics of the optimized BHJ solar cell using PIPT-RG as donor materials. The optimized blend ratio of PIPT and fullerene is 1:4. Detailed comparisons of different blend ratio are not shown here. Using PIPT-RG as donor materials shows a PCE of 5.5%. Moreover, the IPCE spectrum shown in FIG. 12 18(b) is in good agreement with the J-V values.
Device Architecture: ITO/Solution Processed MoOx/Polymer:PCBM/Al (Conventional)
Preparation of MoOx solution: The aqueous MoOx solution was prepared by hydration method according to the procedure reported by Liu et al (Fengmin Liu, Zhiyuan Xie, et al. Solar Energy Materials & Solar Cells. 2010, 94, 94842-845, incorporated by reference herein). Ammonium molybdate ((NH4)6Mo7O24) was dissolved in water to form 0.01 mol/L solution, marked as solution A. 2 mol/L hydrochloric acid (HCl) water solution was marked as solution B. Solution B was dropped into solution A until the pH value of the mixed solution was adjusted between 1.5 and 2.0. This mixed solution was marked as solution C, which is the aqueous MoOx solution
Fabrication of PSCs (Pre-thermal annealing): Polymer solar cells with conventional device architecture of ITO/MoO3/polymer:PCBM//Al were fabricated according to the following procedure. The ITO-coated glass substrates were firstly cleaned by ultrasonic treatment in detergent, deionized water, acetone and isopropyl alcohol for 30 minutes each, and subsequently dried in an oven overnight. After treatment with UV/ozone for 20 min, MoOx (filtered at 0.45 μm) was spin-coated from aqueous solution at 5000 rpm for 40 s to form a film of  ̃8 nm thickness. The substrates were then baked at 160° C. for 25 min in air, and moved into a glovebox for spin-casting the active layer. Two solutions containing a mixture of PIPT-RA:PC71BM and PIPT-RG:PC71BM with different blend ratios in o-DCB with a concentration of 10 mg/ml were spin-casted on top of MoOx layer, respectively. The film thickness of  ̃90 nm was optimized by controlling the spin-casting speed. After that, the BHJ films were annealed at 100° C. for 10 min. Finally, the cathode (Al,  ̃100 nm) was deposited through a shadow mask by thermal evaporation in a vacuum of about 3×10−6 Torr. The active area of the devices was 0.106 cm2.
Fabrication of PSCs (Post-thermal annealing): Polymer solar cells with conventional device architecture of ITO/MoO3/polymer:PCBM//Al were fabricated according to the following procedure. The ITO-coated glass substrates were firstly cleaned by ultrasonic treatment in detergent, deionized water, acetone and isopropyl alcohol for 30 minutes each, and subsequently dried in an oven overnight. After treated with UV/ozone for 20 min, MoOx (filtered at 0.45 μm) was spin-coated from aqueous solution at 5000 rpm for 40 to form a film of  ̃8 nm thickness. The substrates were then barked at 160° C. for 25 min in air, and moved into a glovebox for spin-casting the active layer. Two solutions containing a mixture of PIPT-RA:PC71BM and PIPT-RG:PC71BM with different blend ratio in o-DCB with a concentration of 10 mg/ml were spin-casted on top of MoOx layer, respectively. The film thickness of  ̃90 nm was optimized by controlling the spin-casting speed. After that, the cathode (Al,  ̃100 nm) was deposited through a shadow mask by thermal evaporation in a vacuum of about 3×10−6 Torr. Finally, the devices were annealing at 100° C. for 10 min. The active area of device was 0.106 cm2.
Fabrication of PSCs (Additive): Polymer solar cells with conventional device architecture of ITO/MoO3/polymer:PCBM/Al were fabricated according to the following procedure. The ITO-coated glass substrates were firstly cleaned by ultrasonic treatment in detergent, deionized water, acetone and isopropyl alcohol for 30 minutes each, and subsequently dried in an oven overnight. After treated with UV/ozone for 20 min, MoOx (filtered at 0.45 μm) was spin-coated from aqueous solution at 5000 rpm for 40 s to form a film of  ̃8 nm thickness. The substrates were then barked at 160° C. for 25 min in air, and moved into a glovebox for spin-casting the active layer. The solutions containing a mixture of PIPT-RG:PC71BM (1:4) with different amount of additive in o-DCB with a concentration of 10 mg/ml were spin-casted on top of MoOx layer, respectively. The film thickness of  ̃90 nm was optimized by controlling the spin-casting speed. After that, the BHJ films were annealing at 100° C. for 10 min. Finally, the cathode (Al,  ̃100 nm) was deposited through a shadow mask by thermal evaporation in a vacuum of about 3×10−6 Torr. The active area of device was 0.106 cm2.
Fabrication of PSCs (CPE): Polymer solar cells with conventional device architecture of ITO/MoO3/polymer:PCBM/Al were fabricated according to the following procedure. The ITO-coated glass substrates were firstly cleaned by ultrasonic treatment in detergent, deionized water, acetone and isopropyl alcohol for 30 minutes each, and subsequently dried in an oven overnight. After treated with UV/ozone for 20 min, MoOx (filtered at 0.45 μm) was spin-coated from aqueous solution at 5000 rpm for 40 s to form a film of  ̃8 nm thickness. The substrates were then barked at 160° C. for 25 min in air, and moved into a glovebox for spin-casting the active layer. Two solutions containing a mixture of PIPT-RA:PC71BM and PIPT-RG:PC71BM with different blend ratio in o-DCB with a concentration of 10 mg/ml were spin-casted on top of MoOx layer, respectively. The film thickness of  ̃90 nm was optimized by controlling the spin-casting speed. After that, the BHJ films were annealing at 100° C. for 10 min. Then, CPE was spin-casting on the active layer to form a very thin interfacial layer. Finally, the cathode (Al,  ̃100 nm) was deposited through a shadow mask by thermal evaporation in a vacuum of about 3×10−6 Torr. The active area of device was 0.106 cm2.
PSCs Characterization: The thickness of the multilayer was measured with a profilometer and Atomic Force Microscope (AFM), respectively. Current density-voltage (J-V) characteristics were measured using a Keithley 2602 Source measure Unit, under solar simulation conditions of 100 mW/cm2AM 1.5 G using a 300 W Xe arc lamp with an AM 1.5 global filter. The illumination intensity of the solar simulator was measured using a standard silicon photovoltaic with a protective KG1 filter calibrated by the National renewable Energy Laboratory.
Device data: FIG. 19(a) illustrates the J-V characteristics of the optimized BHJ solar cell based on PIPT-RA and PIPT-RG as donor materials, respectively. Detailed comparisons of different blend ratio are summarized in Table 11. It could be seen that the performance of PIPT-RG devices is much better than that of PIPT-RA devices, corresponding to PCE increases of from 3.4% to 5.1%. From FIG. 19(b) we could see that the IPCE spectrum of PIPT-RG based devices is more broadened than that of PIPT-RA based devices, which is in good agreement with the increased JSC.







TABLE 11







Summary of solar cell device performance with different blend ratios
















Ratio
Voc
Jsc
FF
PCE
Thickness
Rs
Rsh


Device
(x:y)
(V)
(mA/cm2)
(%)
(%)
(nm)
(KΩ)
(KΩ)


















PIPT-
1:1
0.82
5.11
30
1.3
63




RR:PC71BM
1:2
0.84
8.89
39
2.9
80



1:3
0.88
10.68
45
4.2
85



1:4
0.88
12.11
48
5.1
91
0.07
639


PIPT-Ra:PC71BM
1:3
0.74
8.35
37
2.3
90



1:4
0.82
10.08
40
3.4
87
0.13
545









To achieve a better FF, more fabrication methods are used, such as post-thermal annealing (annealing devices after evaporation cathode), adding a different amount of additive (DIO), and spin-casting CPE as interfacial layer between the active layer and cathode, et al. From a starting rough experiment value showed in FIG. 20, we find that post-thermal annealing is not as good as the pre-thermal annealing (annealing active layer before Al evaporation), whereas adding a proper amount of DIO to the fresh solution is a good way to get a better morphology of blend film.
Device Architecture: ITO/ZnO/PIPT-RG:PCBM/MoO//Ag (Inverted)
Preparation of ZnO precursor: Preparation of the ZnO Precursor: The ZnO precursor was prepared by dissolving zinc acetate dihydrate (Zn(CH3 COO)2.2H2O, Aldrich, 99.9%, 1 g) and ethanolamine (NH2CH2CH2OH, Aldrich, 99.5%, 0.28 g in 2-methoxyethanol (CH3OCH2CH2OH, Aldrich, 99.8%, 10 mL) under vigorous stirring for 12 h for the hydrolysis reaction in air.
Fabrication of Inverted PSCs: Inverted solar cells were fabricated on ITO-coated glass substrates. The ITO-coated glass substrates were first cleaned with detergent, ultrasonicated in water, actone and isopropyl alcohol, and subsequently dried overnight in an oven. The ZnO precursor solution was spin-cast on top of the ITO-glass substrate. The films were annealed at 150° C. for 1 h in air. The ZnO film thickness was approximately 30 nm, as determined by a profilometer. The ZnO-coated substrates were transferred into a glove box. A solution containing a mixture of PIPT-RG:PC71BM (1:4) in o-DCB with a concentration of 10 mg/ml was spin-casted on top of a ZnO film with thickness of approximately 80 nm, respectively. The BHJ film was heated at 100° C. for 10 min. Then, a thin layer of MoOx film (≈6 nm) was evaporated on top of the BHJ layer. Finally, the anode (Ag, ≈60 nm) was deposited through a shadow mask by thermal evaporation in a vacuum of about 3×10−6 Torr. The active area of device was 0.05 cm2.
PSCs Characterization: The thickness of multilayers was measured with a profilometer and Atomic Force Microscope (AFM), respectively. Current density-voltage (J-V) characteristics were measured using a Keithley 2602 Source measure Unit, under solar simulation conditions of 100 mW/cm2 AM 1.5 G using a 300 W Xe arc lamp with an AM 1.5 global filter. The illumination intensity of the solar simulator was measured using a standard silicon photovoltaic with a protective KG1 filter calibrated by the National renewable Energy Laboratory.
Device data: FIG. 21(a) illustrates the J-V characteristics of the optimized BHJ solar cell based on PIPT-RG as donor material. The device shows a nice open circle voltage of 0.88 V and short circle current Of 14.1 mA/cm2. Although the FF is relatively low, the PCE is up to 6.2%, which is very comparable to our conventional devices. This consistent value indicated that even when using different device structures, region-regular PIDTPT polymer can distinctly improved OPV devices.
EXAMPLE 4
The inventors recognize that achieving structurally more precise narrow band materials is relevant within the context of bulk heterojunction polymer solar cells, where improved charge carrier transport could potentially impart higher short circuit currency (JSC) and power conversion efficiencies (PCE). Copolymers based on cyclopenta[2,1-b:3,4-b′]dithiophene (CDT) as donor showed a relatively low open circuit voltage (Voc) of about 0.4 V. The inventors realize that replacement of the carbon bridge in CDT unit by a silicon bridge, with the new donor of silolo[3,2-b:4,5-b′]dithiophene (SDT), might decrease the highest occupied molecular orbital (HOMO) energy level, and that OPVs incorporating SDT-PT-based conjugated copolymers might show higher Voc values than that of CDT-PT copolymers. Thus, using of SDT-PT-based regioregular copolymers as the active layer can achieve improved JSC and PCE in OPVs.
Experimental
Synthesis of PSDTPT2-EH
Monomers 4,4-bis(2-ethylhexyl)-2,6-bis(trimethylstannyl)-4H-silolo[3,2-b:4,5-b′]dithiophene (74.4 mg, 0.1 mmol) and 4,4′-(4,4-bis(2-ethylhexyl)-4H-silolo[3,2-b:4,5-b′]dithiophene-2,6-diyl)bis(7-bromo-[1,2,5]thiadiazolo[3,4-c]pyridine) (84.6 mg, 0.1 mmol) were added to a 2-5 mL microwave tube, then Pd(PPh3)4 (5.8 mg, 0.005 mmol) and freshly distilled xylenes (3 ml) were added into the microwave tube. The tube was sealed and subjected to the following reaction conditions in a microwave reactor: 80° C. for 2 min, 130° C. for 2 min, 170° C. for 2 min and 200° C. for 40 min. The reaction was allowed to cool to room temperature, then tributyl(thiophen-2-yl)stannane (20 μl) was added and the reaction was subjected to the following reaction conditions in a microwave reactor: 80° C. for 2 min, 130° C. for 2 min, 170° C. for 2 min and 200° C. for 20 min. After the reaction was cooled to room temperature, 2-bromothiophene (20 μl) was added and the end-capping procedure was repeated once again. The mixture was precipitated in methanol, collected via centrifugation. The collected solid fibers were loaded into a cellulose extraction thimble and washed successively with methanol (6 hours), acetone (6 hours), hexanes (12 hours), and the polymer comes out with chloroform (within 2 hours) from the thimble. Chloroform was removed under reduced pressure and resulted solid was dried over high vacuum line to final products with yield of 85%. GPC with 1,2,4-trichlorobenzene as eluent at 150° C. showed number average molecular weight (Mn) of 22 KDa with polydispersity (PDI) of 1.9.
Synthesis of PSDTPTR-EH
Monomers 4,4-bis(2-ethylhexyl)-2,6-bis(trimethylstannyl)-4H-silolo[3,2-b:4,5-b]dithiophene (74.4 mg, 0.1 mmol) and 4,7-dibromo-pyridal[2,1,3]thiadiazole (29.5 mg, 0.1 mmol) were added to a 2-5 mL microwave tube, then Pd(PPh3)4 (5.8 mg, 0.005 mmol) and freshly distilled xylenes (3 ml) were added into the microwave tube. The tube was sealed and subjected to the following reaction conditions in a microwave reactor: 80° C. for 2 min, 130° C. for 2 min, 170° C. for 2 min and 200° C. for 40 min. The reaction was allowed to cool to room temperature, then tributyl(thiophen-2-yl)stannane (20 μl) was added and the reaction was subjected to the following reaction conditions in a microwave reactor: 80° C. for 2 min, 130° C. for 2 min, 170° C. for 2 min and 200° C. for 20 min. After the reaction was cooled to room temperature, 2-bromothiophene (20 μl) was added and the end-capping procedure was repeated once again. The mixture was precipitated in methanol, collected via centrifugation. The collected solid fibers were loaded into a cellulose extraction thimble and washed successively with methanol (6 hours), acetone (6 hours), hexanes (12 hours), and the polymer comes out with chloroform (within 2 hours) from the thimble. Chloroform was removed under reduced pressure and resulted solid was dried over high vacuum line to final products with yield of 80%. GPC with 1,2,4-trichlorobenzene as eluent at 150° C. showed number average molecular weight (Mn) of 27 KDa with polydispersity (PDI) of 2.1.
PC7IBM (99.5%) was purchased from Nano-C. Chlorobenzene (CB, anhydrous, 99%) was supplied by Sigma-Aldrich Company. All materials were used as received.
The structures of the regiorandom polymer PSDTPTR-EH and the regioregular polymer PSDTPT2-EH used in this study are shown in Scheme 6.




Device Architecture: ITO/PEDOT:PSS/PSDTPT:PCBM/Al (Conventional)

Fabrication of PSCs: Polymer solar cells with conventional device architecture of ITO/PEDOT:PSS/PSDTPT:PCBM/Al were fabricated according to the following procedure. The ITO-coated glass substrates were firstly cleaned by ultrasonic treatment in detergent, deionized water, acetone and isopropyl alcohol for 30 minutes each, and subsequently dried in an oven overnight. After treated with UV/ozone for 20 min, PEDOT:PSS (Baytron P VP AI 4083, filtered at 0.45 μm) was spin-coated from aqueous solution at 4000 rpm for 40 s to form a film of  ̃40 nm thickness. The substrates were barked at 140° C. for 10 min in air, and then moved into a glovebox for spin-casting the active layer. Two solution containing with PSDTPT2-EH:PC71BM (1:1, w/w) and PSDTPTR-EH:PC71BM (1:1, w/w) in CB with a concentration of 10 mg/ml were then spin-casted on top of PEDOT:PSS layer, which were marked as device I and device II, respectively. The film thickness of  ̃80 nm was controlled by adjusting the spin-casting speed. In order to evaporate the solvent quickly, the BHJ films were dried at 70° C. for 10 min. After that, the cathode (Al,  ̃100 nm) was deposited through a shadow mask by thermal evaporation in a vacuum of about 3×10−6 Torr. The active area of device was 0.106 cm2.
PSCs Characterization: The thickness of the active layer and PEDOT:PSS was measured with a profilometer. Current density-voltage (J-V) characteristics were measured using a Keithley 2602 Source measure Unit, under solar simulation conditions of 100 mW/cm2 AM 1.5 G using a 300 W Xe arc lamp with an AM 1.5 global filter. The illumination intensity of the solar simulator was measured using a standard silicon photovoltaic with a protective KG1 filter calibrated by the National renewable Energy Laboratory.
Devices data: FIG. 22 illustrates the characteristics of the two devices, and the detailed comparisons are summarized in Table 12. Using the regioregular copolymers, the short circuit current density (JSC) of device II increases as much as four times (from 2.41 to 9.03 mA/cm2) compared with that of device I using the regionrandom copolymers. As is known, the JSC is not only determined by the number of absorbed photons, but also heavily influenced by the component morphology in the active layer. Therefore, a remarkable increase in JSC for the device II implies that the morphology of the active layer has been substantially improved. Moreover, the open circuit voltage (VOC) and Fill Factor (FF) increased slightly, and the power conversion efficiency (PCE) of device II is up to 1.96%.







TABLE 12







Summary of solar cell device performance based on


PSDTPTR-EH and PSDTPT2-EH copolymers














Voc
Jsc
FF
PCE



Devices
(V)
(mA/cm2)
(%)
(%)







PSDTPTR-
0.56
2.41
35.9
0.48



EH



PSDTPT2-EH
0.58
9.03
37.3
1.96










EXAMPLE 5
High mobility lies in the heart of practical applications for organic electronics. High mobility enables low operating voltage and less energy consumption in organic thin film transistors (OTFTs). Recently, narrow bandgap donor-acceptor (DA) copolymers are attracting researchers' attention. The combination of DA moieties on polymer chain can induce preferred charge transfer between DA units with different electron affinities. Therefore, delocalization, improved transport and higher mobility are expected.
An outstanding class of polymers composed of cyclopenta[2,1-b:3,4-b′]dithiophene (CDT) and 2,1,3-benzothiadiazole (BT) has been reported [14-18]. After replacing BT unit by pyridal[2,1,3]thiadiazole (PT) with larger electron affinity difference to CDT, higher mobility was demonstrated on regioregular-PCDTPT1 (rr-P1) (see FIG. 23) and regioregular-PCDTPT2 (rr-P2) but not in regiorandom-PCDTPTR (ra-P3). Ra-P3 only gave μ=5×10−3 cm2/Vs while μ=0.6 and 0.4 cm2/Vs, respectively, were obtained by rr-P2 and rr-P1 [19]. Molecular structures of the three polymers, device architecture, and work functions are shown in FIG. 23. In order to further increase the mobility, larger molecular weight and films with improved structural order are required. However, to precisely characterize the performance from the different mass distribution of the synthesized polymers, low polydispersity index (PDI) is important as well as molecular weight.
Using gel permeation chromatography (GPC), it is possible to fraction different partitions of molecular weight with low PDI from rr-P2. By controlling collecting time of permeated polymer solution, high molecular weight 300 kDa with PDI≈1.6 was collected and high mobility, μ=2.5 cm2/Vs, was demonstrated after annealing. Improved alky stacking with annealing temperature was confirmed by a growing peak in X-ray diffraction (XRD) spectra. Obvious fiber structure was observed after the film was annealed over 300° C. Thus, the high mobility, over 2 cm2/Vs, after annealing could be correlated to the higher degree of structural order in films of high molecular weight rr-P2. To push mobility even higher than 2.5 cm2/Vs, inducing higher molecular weight and more ordering in polymer film are promising. However, to further increase the molecular weight by GPC is impractical because of the required collecting time and the quantity of the fractionated solution.
The transfer and output characteristics of the OTFTs made of rr-P2 are shown in FIGS. 24(a) and 24(b). The polymer film was drop cast on a prepatterned substrate with bottom contact (BC) architecture made of gold. The SiO2 gate dielectric was passivated by decyl(trichloro)silane (DTS). FIG. 24(a) shows clear transistor behavior with linear and saturation regimes and on-off ration 6×106. The positive shift of threshold voltage from negative VG to VG=20 V elucidates the existence of hole traps on the interface of gold and polymer.
Table 13 is a mobility table showing drop casted films prepared from different concentration solutions after different annealing temperatures. The highest mobility value 2.5 cm2/Vs, was achieved from the film prepared by 0.025 wt % solution and annealed at 350° C. Even though the mobility values continuously increase with annealing temperature, the numbers saturate after 200° C., mainly varying from 1.8 to 2.3 cm2/Vs.







TABLE 13







Polymer films were drop casted from various solution


concentrations. Hole mobility values after annealed at


different temperatures were collected.








Sol.



Concen-
Annealing Temp














tration
RT
100° C.
150° C.
200° C.
250° C.
300° C.
350° C.





 0.1%
0.9
1.1
1.6
1.8
1.9
2.2
2.2


0.075%
1.4
1.2
1.8
2.1
2.2
2.3
2.3


 0.05%
0.8
1.2
1.2
1.9
2.1
1.9
2.3


0.025%
0.8
1.4
1.6
1.8
2.0
2.1
2.5









Height and phase images shown in FIGS. 25(a) and 25(b) were obtained by atomic force microscopy, showing fiber structure with length 100 to 200 nm after annealing at 350° C. XRD spectra with temperature dependence shown in FIGS. 26(a) and 26(b) confirms the ordered structure increasing with annealing temperature. The peak at 2θ=3.3° can be correlated to 2.7 nm alkyl packing. As demonstrated in Table 13, because mobility values obviously increase with annealing temperature, the increasing mobility can be associated with the increasing ordered alkyl packing.
The dark spots in the image are actually holes in the film.
To further optimize device performance, contact resistance (Rc) was also studied. Rc shown in FIG. 27 demonstrates a largest Rc=21.5 kΩ at RT, decreases to 5.4 kΩ after 250° C. annealing, and increases to 14.7 kΩ after annealed at 350° C. Rc was significantly reduced by factor 4 after annealed at 250° C. The increase of Rc after 350° C. annealing could come from possible thermal decomposition of the polymer films that degrades the interface between polymer and metal contact.
Through comparing the temperature dependence among Table 13, AFM images in FIG. 25, and XRD spectra in FIG. 26, we concluded the high mobility over 2 cm2/Vs was from the ordered packing of the high molecular weight rr-P2 after annealing. In order to advance the performance of this polymer system, higher molecular weight and more ordering in polymer film are both important.
Experimental
PCDTPT2 (P2) was originally synthesized with 55 kDa and PDI>4. To collect high molecular weight P2 by gel permeated chromatography (GPC), 75 mg P2 was dissolved in chloroform (0.25% triethylamine) with 1 mg/ml concentration. Permeated solution was collected within 6 sec and produced P2 with 300 kDa and PDI=1.6. After drying, then, the high molecular weight P2 was dissolved in chlorobenzene with 0.1, 0.075, 0.05, and 0.025 wt % for drop casting on bottom contact substrates passivated by decyl(trichloro)silane. The casted substrates were kept in a glovebox with oxygen level less than 2 ppm, drying for 6 hours. All devices were tested in a nitrogen environment and data were collected by Keithley 4200.
REFERENCES
The following publications are incorporated by reference herein in their entireties:

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Although the present invention has been described in connection with the preferred embodiments, it is to be understood that modifications and variations may be utilized without departing from the principles and scope of the invention, as those skilled in the art will readily understand. Accordingly, such modifications may be practiced within the scope of the invention and the following claims.

## Claims

1. A regioregular donor-acceptor copolymer comprising a regioregular conjugated main chain section, said regioregular conjugated main chain section having a repeat unit that comprises a pyridine of the structure



wherein:
Ar is a substituted or non-substituted aromatic functional group;
the pyridine is regioregularly arranged along the conjugated main chain section; and
the repeat unit further comprises a dithiophene of the structure





wherein each Ar is independently a substituted or non-substituted aromatic functional group, or each Ar is independently nothing and the valence of its respective thiophene ring is completed with hydrogen,
each R is independently hydrogen or a substituted or non-substituted alkyl, aryl or alkoxy chain;
X is C, Si, Ge, N or P; and
the charge carrier mobility of the regioregular donor-acceptor copolymer is greater than the charge carrier mobility of a regiorandom donor-acceptor copolymer of similar composition.

2. The regioregular donor-acceptor copolymer of claim 1, wherein each substituted or non-substituted aromatic functional group of the pyridine and the dithiophene independently comprises one or more alkyl or aryl chains.

3. The regioregular donor-acceptor copolymer of claim 2, wherein the one or more alkyl or aryl chains are each independently a C6-C30 substituted or non-substituted alkyl chain, —(CH2CH2O)n wherein n is an integer from 2 to 20, C6H5, —CnF(2n+1) wherein n is an integer from 2 to 20, —(CH2)nN(CH3)3Br wherein n is an integer from 2 to 20, —(CH2)nN(C2H5)2 wherein n is an integer from 2 to 20,2-ethylhexyl, PhCmH2m+1 wherein m is an integer from 1 to 20, —(CH2)nSi(CmH2m+1)3 wherein m and n are each individually an integer from 1 to 20, or —(CH2)nSi(OSi(CmH2m+1)3)x(CpH2p+1)y wherein m, n, and p are each individually an integer from 1 to 20 and x+y is 3.

4. The regioregular donor-acceptor copolymer of claim 1, wherein the substituted or non-substituted alkyl, aryl or alkoxy chain is a C6-C30 substituted or non-substituted alkyl, aryl or alkoxy chain, —(CH2CH2O)n wherein n is an integer from 2 to 20, C6H5, —CnF(2n+1) wherein n is an integer from 2 to 20, —(CH2)nN(CH3)3Br wherein n is an integer from 2 to 20, —(CH2)nN(C2H5)2 wherein n is an integer from 2 to 20,2-ethylhexyl, PhCmH2m+1 wherein m is an integer from 1 to 20, —(CH2)nSi(CmH2m+1)3 wherein m and n are each individually an integer from 1 to 20, or —(CH2)nSi(OSi(CmH2m+1)3)x(CpH2p+1)y wherein m, n, and p are each individually an integer from 1 to 20 and x+y is 3.

5. The regioregular donor-acceptor copolymer of claim 1, wherein X is C or Si.

6. The regioregular donor-acceptor copolymer of claim 1, wherein the pyridine is a pyridine unit selected from the group consisting of:










wherein each R is independently a substituted or non-substituted alkyl, aryl or alkoxy chain, —(CH2CH2O)n wherein n is an integer from 2 to 20, C6H5, —CnF(2n+1) wherein n is an integer from 2 to 20, —(CH2)nN(CH3)3Br wherein n is an integer from 2 to 20, —(CH2)nN(C2H5)2 wherein n is an integer from 2 to 20, 2-ethylhexyl, PhCmH2m+1 wherein m is an integer from 1 to 20, —(CH2)nSi(CmH2m+1)3 wherein m and n are each individually an integer from 1 to 20, or —(CH2)nSi(OSi(CmH2m+1)3)x(CpH2p+1)y wherein m, n, and p are each individually an integer from 1 to 20 and x+y is 3.

7. The regioregular donor-acceptor copolymer of claim 1, wherein the repeat unit further comprises the dithiophene unit selected from the group consisting of:







wherein each R is independently a substituted or non-substituted alkyl, aryl or alkoxy chain, —(CH2CH2O)n wherein n is an integer from 2 to 20, C6H5, —CnF(2n+1) wherein n is an integer from 2 to 20, —(CH2)nN(CH3)3Br wherein n is an integer from 2 to 20, —(CH2)nN(C2H5)2 wherein n is an integer from 2 to 20,2-ethylhexyl, PhCmH2m+1 wherein m is an integer from 1 to 20, —(CH2)nSi(CmH2m+1)3 wherein m and n are each individually an integer from 1 to 20, or —(CH2)nSi(OSi(CmH2m+1)3)x(CpH2p+1)y wherein m, n, and p are each individually an integer from 1 to 20 and x+y is 3.

8. The regioregular donor-acceptor copolymer of claim 1, wherein
the pyridine unit is




and the dithiophene unit is





wherein each R is independently hydrogen or a substituted or non-substituted alkyl, aryl or alkoxy chain.

9. The regioregular donor-acceptor copolymer of claim 1, wherein the repeat unit comprises:




wherein each R is independently hydrogen or a substituted or non-substituted alkyl, aryl or alkoxy chain, and X is C, Si, Ge, N or P.

10. The regioregular donor-acceptor copolymer of claim 9, wherein the substituted or non-substituted alkyl, aryl or alkoxy chain is a C6-C30 substituted or non-substituted alkyl, aryl or alkoxy chain, —(CH2CH2O)n wherein n is an integer from 2 to 20, C6H5, —CnF(2n+1) wherein n is an integer from 2 to 20, —(CH2)nN(CH3)3Br wherein n is an integer from 2 to 20, —(CH2)nN(C2H5)2 wherein n is an integer from 2 to 20,2-ethylhexyl, PhCmH2m+1 wherein m is an integer from 1 to 20, —(CH2)nSi(CmH2m+1)3 wherein m and n are each individually an integer from 1 to 20, or —(CH2)nSi(OSi(CmH2m+1)3)x(CpH2p+1)y wherein m, n, and p are each individually an integer from 1 to 20 and x+y is 3.

11. The regioregular donor-acceptor copolymer of claim 9, wherein X is C or Si.

12. The regioregular donor-acceptor copolymer of claim 11, wherein each R is C12H25, each R is C16H33, each R is 2-ethylhexyl, or each R is PhC6H13.

13. An electronic device comprising the regioregular donor-acceptor copolymer of claim 1, wherein the regioregular donor-acceptor copolymer forms an active semiconducting layer.

14. The device of claim 13, wherein the device is a field effect transistor, organic photovoltaic device, polymer light emitting diode, organic light emitting diode, organic photodetector, or biosensor.

15. An field-effect transistor (FET) device including a regioregular donor-acceptor copolymer comprising a regioregular conjugated main chain section, said regioregular conjugated main chain section having a repeat unit that comprises a pyridine of the structure



wherein:
Ar is a substituted or non-substituted aromatic functional group;
the pyridine is regioregularly arranged along the conjugated main chain section;
the repeat unit further comprises a dithiophene of the structure





wherein each Ar is independently a substituted or non-substituted aromatic functional group, or each Ar is independently nothing and the valence of its respective thiophene ring is completed with hydrogen,
each R is independently hydrogen or a substituted or non-substituted alkyl, aryl or alkoxy chain; and
X is C, Si, Ge, N or P;
the regioregular donor-acceptor copolymer forms an active semiconducting layer in the field-effect transistor device; and
the charge carrier mobility of the regioregular donor-acceptor copolymer is greater than the charge carrier mobility of a regiorandom donor-acceptor copolymer of similar composition.

16. A regioregular donor-acceptor copolymer comprising a regioregular conjugated main chain section, said regioregular conjugated main chain section having a repeat unit that comprises a pyridine of the structure




wherein:
Ar is a substituted or non-substituted aromatic functional group;
the pyridine is regioregularly arranged along the conjugated main chain section; and
the repeat unit further comprises a dithiophene of the structure




wherein:
R is independently hydrogen or a substituted or non-substituted alkyl, aryl or alkoxy chain; and X is C, Si, Ge, N or P; and

the charge carrier mobility of the regioregular donor-acceptor copolymer is greater than the charge carrier mobility of a regiorandom donor-acceptor copolymer of similar composition.