# Highly Isotactic Poly(N-butenyl-carbazole): Synthesis, Characterization, and Optical Properties

Authors: Antonio Botta; Vincenzo Venditto; Alfredo Rubino; Stefania Pragliola
Journal: Journal of Chemistry
 (2016)

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## Abstract

The synthesis of isotactic poly(N-butenyl-carbazole) (i-PBK) by using homogeneous isospecific Ziegler-Natta catalytic system is reported. The achieved polymer is crystalline and shows, to DSC and X-ray analysis, two distinct crystalline phases. i-PBK FTIR spectrum and X-ray diffraction pattern are compared with those of poly(N-vinylcarbazole) (PVK). The observed differences are tentatively associated with higher flexibility of the i-PBK chains due to the alkylene group connecting the carbazole group to the main chain. i-PBK optical properties are also compared with those of PVK and isotactic poly(N-pentenyl-carbazole) (i-PPK), a higher homologue of i-PBK recently used as emitting layer in organic light emitting diodes (OLEDs) showing white light emission. The close similarity of the fluorescence spectra of i-PBK and i-PPK is a promising basis for optical applications of this polymer.


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## Body

## 1. Introduction

The recent growing interest in carbazole containing polymers is due to the discovery of polymeric light emitting diodes [1] and organic photorefractive materials [2], but also to their potential application as components in photovoltaic devices [3].The first and the most widely studied organic polymeric photoconductor is the poly(N-vinylcarbazole) (PVK) [4–6]. This polymer was promptly used by IBM company to develop the PVK-TNF (2,4,7-trinitrofluorenone) system as organic photoconductor for Copier I series [7]. Although PVK-TNF system can be considered nowadays completely obsolete, due to the relatively low photosensitivity, high toxicity of TNF, and poor mechanical strength of the PVK films, the interest in carbazole containing polymers remains high. To find new application fields of PVK derivatives, attempts have been made to modify PVK structure. The aim was to provide the rational design and optimisation of high performance organic photoactive polymeric materials.Polymers with pendant or in chain isolated carbazolyl groups were synthetized by using different polymerization techniques [8–11]. In particular, in literature, a detailed investigation of photophysical properties of polymers with different pendant carbazolyl groups and the comparison with PVK has been reported [9–13]. It was found that the nature and length of spacer linking carbazole moiety to polymer backbone, as well as the stereoregularity of polymer microstructure, modify the photophysical properties and photoconductive behaviour of carbazole containing polymers [10].It is well known that a precise stereocontrol of microstructures for polymers obtained by vinyl monomers can be achieved by coordination Ziegler-Natta polymerization [14]. In particular, the development of homogeneous catalytic systems based on metallocenes and postmetallocenes allowed in the latest two decades reaching an important goal in the realm of specialty polymers [15–18].Recently, we reported the polymerization of a vinyl monomer with a pendant carbazole group (9-(pent-4-en-1-yl)-9H-carbazole). Isotactic poly(N-pentenyl-carbazole) (i-PPK) was obtained with high yield by using the isospecific catalytic systemrac-[(CH3)2Si(indenyl)2]ZrCl2/MAO [19, 20]. For the first time, isotactic microstructure of PPK was unambiguously determined by 13C and 1H NMR analysis [19, 20]. i-PPK optical properties were also investigated and an electroluminescent behaviour of polymer was observed. Innovative organic light emitting diodes (OLEDs) were achieved using this new material as emitting layer, showing white light emission and promising performances [19, 20].In this paper we present the synthesis of isotactic poly(N-butenyl-carbazole) (i-PBK), a polymer homologue to i-PPK but having the linker connecting the carbazole to the main chain one carbon atom shorter.i-PBK was obtained by using the homogeneous isospecific Ziegler-Natta catalytic systemrac-[(CH3)2Si(indenyl)2]ZrCl2/methylallumoxane (MAO).The achieved polymer was structurally analyzed by13C NMR, FTIR, and X-ray analysis; moreover, thermal analysis, UV-Vis, and photoluminescence analysis were also carried out. In addition, the infrared and fluorescence behaviors of i-PBK were compared with those of the largely investigated PVK [4–6, 10] and of the recently achieved i-PPK [19, 20]. On the basis of this comparison, the influence of the flexible alkylene spacer, absent in PVK and longer by one carbon atom in i-PPK, on the structural and optical properties of this class of polymers, was also determined.


## 2. Experimental

All manipulations involving air and moisture sensitive compounds were carried out under an atmosphere of dried and purified nitrogen with standard vacuum-line, Schlenk, or glovebox techniques.


## 3. Materials

All reagents and solvents were purchased from Sigma-Aldrich s.r.l. (Milan, Italy). Toluene was refluxed over sodium for 48 h and distilled before use, methylalumoxane was used as a solid after distillation of solvent (toluene), and other reagents were used without further purification. The catalytic precursorrac-dimethylsilylbis(1-indenyl)zirconium dichloride was purchased from Strem Chemicals, Inc. Poly(9-vinylcarbazole) was purchased from Sigma-Aldrich s.r.l. (Milan, Italy) with an average Mn of 25,000–50,000.


### 3.1. Synthesis of 9-(But-3-en-1-yl)-9H-carbazole

In a 100 mL round bottom flask, to a suspension of carbazole (0,0598 mol) and 4-bromo-1-butene (0,598 mol), benzyltriethylammonium bromide (TBEA) (0,00179 mol) and 35 mL of 16 M NaOH solution were added. The mixture was left stirring for 24 h at 60°C. Afterwards the mixture was poured into water and extracted twice with ethyl acetate. The organic layer was dried over anhydrous MgSO4 and filtered and the solvent removed by evaporation to give the crude product. The resulting residue was purified on a silica gel column chromatography in hexane/ethyl acetate (8 : 2) to give a white solid (87% yield). 1H NMR (300 MHz, CDCl3) δ: 2.61–2.68 (2H, m, CH2), 4.40 (2H, t, J=7.2 Hz, NCH2), 5.06–5.12 (2H, dd, J=10.2, 17.1 Hz, CH2=CH), 5.82–5.93 (1H, m, CH), 7.25 (2H, d, J=7.5 Hz, Ar), 7.45 (2H, t, J=8 Hz, Ar), 7.50 (2H, t, J=8 Hz, Ar), 8.12, (2H, d, J=7.8 Hz Ar); 13C NMR (75 MHz, CDCl3) δ: 140.49, 135.11, 125.83, 123.12, 120.58, 119.07, 117.52, 108.88, 42.92, 33.42 [21].


### 3.2. Synthesis of Isotactic PBK (i-PBK)

Isotactic PBK was prepared by introducing 7 mL of dry toluene, 4.52 × 10−3mol (1 g) of monomer, and 8.27 × 10−3mol (480 mg) of MAO into a 50 mL round bottom flask equipped with magnetic stirrer. Polymerization was started by introducing 1.43 × 10−5mol (6.4 mg) ofrac-dimethylsilylbis(1-indenyl)zirconium dichloride. Polymerization was stopped, after 72 hours, by introducing a few milliliters of ethanol. Then, the polymer was coagulated in an excess of acidified ethanol (solution of HCl in ethanol 0.1–0.2 M), washed several times with fresh ethanol, and dried in vacuo at room temperature (yield 0.575 g). The polymer as obtained from the synthesis and was extracted in boiling acetone and two fractions, an insoluble (0.375 g) and a soluble (0.200 g) acetone fractions, were separated. The acetone insoluble fraction was soluble in toluene, chlorobenzene and tetrachloroetane.


## 3.1. Synthesis of 9-(But-3-en-1-yl)-9H-carbazole

In a 100 mL round bottom flask, to a suspension of carbazole (0,0598 mol) and 4-bromo-1-butene (0,598 mol), benzyltriethylammonium bromide (TBEA) (0,00179 mol) and 35 mL of 16 M NaOH solution were added. The mixture was left stirring for 24 h at 60°C. Afterwards the mixture was poured into water and extracted twice with ethyl acetate. The organic layer was dried over anhydrous MgSO4 and filtered and the solvent removed by evaporation to give the crude product. The resulting residue was purified on a silica gel column chromatography in hexane/ethyl acetate (8 : 2) to give a white solid (87% yield). 1H NMR (300 MHz, CDCl3) δ: 2.61–2.68 (2H, m, CH2), 4.40 (2H, t, J=7.2 Hz, NCH2), 5.06–5.12 (2H, dd, J=10.2, 17.1 Hz, CH2=CH), 5.82–5.93 (1H, m, CH), 7.25 (2H, d, J=7.5 Hz, Ar), 7.45 (2H, t, J=8 Hz, Ar), 7.50 (2H, t, J=8 Hz, Ar), 8.12, (2H, d, J=7.8 Hz Ar); 13C NMR (75 MHz, CDCl3) δ: 140.49, 135.11, 125.83, 123.12, 120.58, 119.07, 117.52, 108.88, 42.92, 33.42 [21].


## 3.2. Synthesis of Isotactic PBK (i-PBK)

Isotactic PBK was prepared by introducing 7 mL of dry toluene, 4.52 × 10−3mol (1 g) of monomer, and 8.27 × 10−3mol (480 mg) of MAO into a 50 mL round bottom flask equipped with magnetic stirrer. Polymerization was started by introducing 1.43 × 10−5mol (6.4 mg) ofrac-dimethylsilylbis(1-indenyl)zirconium dichloride. Polymerization was stopped, after 72 hours, by introducing a few milliliters of ethanol. Then, the polymer was coagulated in an excess of acidified ethanol (solution of HCl in ethanol 0.1–0.2 M), washed several times with fresh ethanol, and dried in vacuo at room temperature (yield 0.575 g). The polymer as obtained from the synthesis and was extracted in boiling acetone and two fractions, an insoluble (0.375 g) and a soluble (0.200 g) acetone fractions, were separated. The acetone insoluble fraction was soluble in toluene, chlorobenzene and tetrachloroetane.


## 4. Characterizations

### 4.1. NMR Analysis

NMR spectra of monomer were recorded on an AX 300 Bruker spectrometer operating at 298 K. The sample was prepared by dissolving 5 mg of monomer in 0.5 mL of deuterated chloroform (CDCl3). Tetramethylsilane was used as internal chemical shift reference.NMR spectra of polymer were recorded on an AX 300 Bruker spectrometer operating at 75 MHz and 373 K. The samples were prepared by dissolving 40 mg of polymer in 0.5 mL of 1,1,2,2-Tetrachloroethane-d2 (TCDE). Hexamethyldisiloxane was used as internal chemical shift reference.


### 4.2. Gel Permeation Chromatography Measurements

The molecular weight distribution and polydispersity index were estimated by GPC at 140°C using 1,2,4-trichlorobenzene as solvent and narrow molecular weight distribution polystyrene (PS) standard samples as reference. The measurements were performed on PLGPC210 with four PL-Gel Mixed A Columns, a refractive detector, and a DM400 data manager (Viscotek, Malvern Instruments Ltd., Worcestershire, UK).


### 4.3. Calorimetric Measurements

Calorimetric measurements were carried out on a DSC Q20 apparatus manufactured by TA Instruments, in flowing N2. Polymer samples of 5–10 mg were placed in aluminum pans and heated/cooled at a rate of 10°C/min. Measurements were done in the range 30–280°C.


### 4.4. X-Ray Diffraction Patterns

X-ray diffraction patterns of polymer powder sample were obtained by an automatic Bruker D8 Advance diffractometer, in reflection, by using the nickel filtered Cu-Kα radiation (1.5418 Å).


### 4.5. Fourier Transform Infrared Measurements

Infrared spectra were obtained at a resolution of 2.0 cm−1 with a Tensor 27 Bruker spectrometer equipped with deuterated triglycine sulfate (DTGS) detector and a Ge/KBr beam splitter. The frequency scale was internally calibrated to 0.01 cm−1 using a He-Ne laser. Thirty-two scans were signal averaged to reduce the noise. Before infrared analysis, samples were prepared on KBr pellets, at room temperature. The pellets were then dried in vacuum at room temperature.


### 4.6. Optical Characterization

Thin polymer films have been prepared by spin coating on quartz slides substrate. The film thickness and roughness were measured by KLA Tencor P-10 surface profiler. UV-Vis measurement was performed by a Varian Cary 50 spectrophotometer and photoluminescence recorded by a Varian Cary Eclipse spectrophotometer.


## 4.1. NMR Analysis

NMR spectra of monomer were recorded on an AX 300 Bruker spectrometer operating at 298 K. The sample was prepared by dissolving 5 mg of monomer in 0.5 mL of deuterated chloroform (CDCl3). Tetramethylsilane was used as internal chemical shift reference.NMR spectra of polymer were recorded on an AX 300 Bruker spectrometer operating at 75 MHz and 373 K. The samples were prepared by dissolving 40 mg of polymer in 0.5 mL of 1,1,2,2-Tetrachloroethane-d2 (TCDE). Hexamethyldisiloxane was used as internal chemical shift reference.


## 4.2. Gel Permeation Chromatography Measurements

The molecular weight distribution and polydispersity index were estimated by GPC at 140°C using 1,2,4-trichlorobenzene as solvent and narrow molecular weight distribution polystyrene (PS) standard samples as reference. The measurements were performed on PLGPC210 with four PL-Gel Mixed A Columns, a refractive detector, and a DM400 data manager (Viscotek, Malvern Instruments Ltd., Worcestershire, UK).


## 4.3. Calorimetric Measurements

Calorimetric measurements were carried out on a DSC Q20 apparatus manufactured by TA Instruments, in flowing N2. Polymer samples of 5–10 mg were placed in aluminum pans and heated/cooled at a rate of 10°C/min. Measurements were done in the range 30–280°C.


## 4.4. X-Ray Diffraction Patterns

X-ray diffraction patterns of polymer powder sample were obtained by an automatic Bruker D8 Advance diffractometer, in reflection, by using the nickel filtered Cu-Kα radiation (1.5418 Å).


## 4.5. Fourier Transform Infrared Measurements

Infrared spectra were obtained at a resolution of 2.0 cm−1 with a Tensor 27 Bruker spectrometer equipped with deuterated triglycine sulfate (DTGS) detector and a Ge/KBr beam splitter. The frequency scale was internally calibrated to 0.01 cm−1 using a He-Ne laser. Thirty-two scans were signal averaged to reduce the noise. Before infrared analysis, samples were prepared on KBr pellets, at room temperature. The pellets were then dried in vacuum at room temperature.


## 4.6. Optical Characterization

Thin polymer films have been prepared by spin coating on quartz slides substrate. The film thickness and roughness were measured by KLA Tencor P-10 surface profiler. UV-Vis measurement was performed by a Varian Cary 50 spectrophotometer and photoluminescence recorded by a Varian Cary Eclipse spectrophotometer.


## 5. Results and Discussion

### 5.1. Synthesis and13C-NMR Characterization

Monomer, 9-(but-3-en-1-yl)-9H-carbazole, was synthesized following a synthetic procedure accurately described in the experimental part.Polymerization of monomer was performed at 20°C in toluene solution by using therac-[(CH3)2Si(indenyl)2]ZrCl2/methylallumoxane (MAO) catalytic system (see Scheme 1). The catalytic precursorrac-[(CH3)2Si(indenyl)2]ZrCl2, activated by MAO, is well known to promote the isospecific polymerization of α-olefins [15, 22, 23]. Recently, its high performances in the isospecific 9-(pent-4-en-1-yl)-9H-carbazole polymerization was also reported [19, 20].Scheme 1The obtained polymer (PBK) was fractionated by exhaustive extraction with boiling acetone and two different fractions, an acetone insoluble (65% of whole starting material) and a soluble (35% of whole starting material), were obtained.Both PBK fractions, analyzed by GPC, showed monomodal curves and narrow molecular weight distributions. The molecular weight of the acetone insoluble fraction (Mn=3000 Dalton, PDI = 1.6) becomes higher than the acetone soluble fraction (Mn=1922 Dalton, PDI = 1.10).The microstructure of PBK fractions was fully determined by13C NMR analysis, utilizing the carbon attributions in similar environments, reported in literature [19, 20, 24–27]. In Figure 1(a), the 13C NMR spectrum of the acetone insoluble PBK fraction sample is reported. As expected, this spectrum is fully consistent with both regio- and stereoregular polymer microstructure and, in particular, from the chemical shifts related to carbons 1 and 2, an isotactic microstructure of polymer (i-PBK) is assumed [24–26].Figure 1
13C NMR spectra of PBK fractions, (a) acetone insoluble, (b) acetone soluble (solvent: tetrachlorodideteuroethane; scale: hexamethyldisiloxane).The acetone soluble PBK fraction13C NMR spectrum (Figure 1(b)) is instead indicative of a less stereoregular polymer microstructure. Regioerrors are also recognized in this fraction.


### 5.2. X-Ray, DSC and Infrared Characterization

In Figure2(a), the X-ray diffraction pattern of the as polymerized i-PBK is reported.Figure 2
X-ray diffraction patterns of (a) as polymerized sample, (b) acetone-soluble fraction, (c) acetone-insoluble fraction, and (d) crystalline fraction after annealing atT = 200°C for 20 min.The X-ray pattern shows a small but well-defined reflection at 2θ ≈ 7° and other less defined reflections in the 2θ range of 10°–15° overlapped to a large amorphous halo centered at 2θ ≈ 20°. Such X-ray pattern indicates that a limited amount of crystalline phase is present in the as polymerized sample.X-ray spectra of acetone soluble and insoluble fractions ofi-PBK are shown in Figures 2(b) and 2(c), respectively.The pattern of the acetone-soluble fraction, Figure2(b), presents only a broad amorphous halo with two well defined humps at 2θ ≈ 12° and 20°, while the pattern of the acetone-insoluble fraction, Figure 2(c), shows many well-defined crystal reflections.The results of WAXD analysis of the amorphous and crystalline fractions of thei-PBK are in agreement with the NMR analysis, which shows that the acetone-insoluble fraction (crystalline fraction) is more stereoregular of the acetone-soluble fraction (amorphous fraction).It is worth noting that the two humps in the X-ray pattern of the amorphous fraction correspond to those observed in the spectrum of the as polymerized sample, and the few indistinct crystal reflections observed in the X-ray pattern of the as polymerized sample correspond to peaks of the crystalline fraction pattern.In Figure3, the second DSC heating run of the unfractionated polymer (Figure 3(a)) and that of its amorphous fraction (Figure 3(b)) are compared. The observed difference in glass transition (Tg) value can be rationalized on the basis of the fact that the molecular weight of the amorphous fraction, evaluated by GPC analysis, is smaller (Mn ≈ 2000 Da) compared to that of the unfractionated polymer (Mn ≈ 3000 Da).Figure 3
Second heating of DSC runs of (a) as polymerized (unfractionated) sample, (b) acetone-soluble fraction, and (c) first heating of DSC run of acetone-insoluble fraction.The first DSC heating run of the polymer crystalline fraction, is also shown in Figure3. Two separate and well-defined endothermic peaks, at T≈174°C and T=216°C, associable with distinct crystalline phases, are observed.Between the two endothermic peaks a weak exothermic peak atT ≈ 200°C, is also present. This peak can be tentatively interpreted as a crystallization phenomenon associated with the solid-solid transition between the two crystal forms which melt at T ≈ 174 and 216°C, respectively.In Figure2(d), the X-ray pattern of the i-PBK crystalline fraction after annealing at T = 200°C for 20 minutes is shown. Only some of narrow peaks of the pattern (c) of Figure 2 are still present, although slightly shifted. On the contrary, many reflections of the two patterns do not match each other.These differences can be rationalized by assuming that the two patterns correspond to two different crystalline phases, which are probably very similar.Both of these two crystalline forms cannot be obtained by crystallization from the melt, so that in the second DSC heating run (not showed in Figure3) of the i-PBK crystalline fraction, only a glass transition at T = 97°C is observed. This Tg value, which is very similar to that of the as polymerized i-PBK sample (see Figure 3(a)), appears to be intermediate between that reported for PVK (Tg = 211°C) (obtained from the second DSC heating run of poly(9-vinylcarbazole) purchased from Sigma-Aldrich s.r.l. (Milan, Italy) with an average Mn of 25,000–50,000) and i-PPK (Tg = 90°C) [20]. The observed differences between Tg of these polymers accord well with the widely accepted hypothesis that rigidity of polymer chains, on which Tg value depends, is affected by the side branches length of polymer chain.In detail, as for the PVK, the carbazole units directly connected to the main chain make the polymer chain extremely rigid [28], while, for PBK and PPK, the alkylene linkers, which connect the carbazole unit with the main chain spacing the polymer chains each other, increases the free volume and reduces Tg.The differentTg values of i-PBK and i-PPK, on the basis of this hypothesis, can be justified by the different length of the alkylene linker which is 2 and 3 C atoms for i-PBK and i-PPK, respectively.As for the infrared characterization of thei-PBK, particularly informative is the comparison with the PVK. The FTIR spectra of amorphous samples of PVK and i-PBK are very similar to each other. The most important difference is in the region of C-H stretching (Figure 4(a)) where the intensity ratio of the aliphatic to aromatic C-H stretching (at 2848–2918 cm−1 and 3021–3048 cm−1, resp.) increases in the i-PBK spectra, due to the (CH2)2 alkylene linker connecting the carbazole moiety to the main chain.Figure 4
FTIR spectra of PVK (line (A)); crystalline (line (B)); and amorphous (line (C)) fractions ofi-PBK.
(a)
(b)The same phenomenon has already been reported fori-PPK [20], a polymer homologue to i-PBK but having the linker connecting the carbazole to the main chain one carbon atom longer.In addition to the C-H stretching region, the region in which there are more differences between the PVK infrared spectrum and those of the amorphous and crystalline fractions ofi-PBK is in the wavelength range 1070–1260 cm−1 (Figure 4(b)).In Figure4(b), the absorption bands of carbazole ring vibrational modes, at 1121, 1132, and 1151 cm−1 as valued in the spectrum of PVK, assigned to C-H in-plane bending and ring deformation [29], remain substantially unchanged in the i-PBK spectra, although slightly shifted.On the contrary, the PVK absorption bands at 1224 and 1236 cm−1, assigned, respectively, to Ccarbazole-N and Caliphatic-N stretching [29–31], change position and intensity in the spectra of i-PBK fractions, and they are blue shifted at 1128 and 1241 cm−1, respectively. In addition a new band at 1180 cm−1 appears in both amorphous and crystalline i-PBK fractions.These differences are probably due to the influence that the alkylene linker has oni-PBK vibrational modes and in particular on vibrational modes involving the nitrogen of the carbazole group.Finally, it should be noted that additional bands at 1195 and 1224 cm−1 are present only in the spectrum of i-PBK crystalline fraction. These bands are possibly associated with the vibrational modes influenced by polymer chains packing in the i-PBK crystalline structure.


### 5.3. Optical Characterization

The good solubility ofi-PBK in chlorobenzene allowed the preparation of uniform and homogenous films of 100 nm thick.Figure5 shows the absorption spectrum of a i-PBK film sample. It presents several peaks maxima at around 230, 262, 295, 330, and 345 nm, where the two longest wavelengths are due to the carbazole group [32].Figure 5
Absorption spectrum ofi-PBK film.i-PBK fluorescence spectrum of the acetone insoluble fraction film sample measured under an excitation wavelength of 298 nm at room temperature is reported in Figure 6 (bottom curve). In Figure 6, for comparison, the fluorescence spectra of an i-PPK film sample [19, 20] (medium curve) and a commercial PVK sample (trade sample purchased from Sigma Aldrich Company presenting a partially isotactic microstructure) (curve on the top) are also shown. It is worth nothing that both i-PBK and i-PPK fluorescence spectra present very similar curve shape.Figure 6
Fluorescence spectra ofi-PBK, i-PPK, and PVK films.Thei-PBK spectrum exhibits two emission bands in the high energy region presenting peaks at 357 nm and 374 nm, respectively, which correspond to those from isolate monomer units [33, 34]. The same bands are also present in the i-PPK spectrum, but not in the PVK spectrum. This result can be related to the presence of the flexible spacer (-(CH2)3- for PPK and -(CH2)2- for PBK), absent in PVK, between the main chain and the carbazole pendant. It was found that other vinyl polymers with pendant carbazole groups connected to the skeleton chain by a flexible spacer like -O-(CH2)2- (poly[2-N-carbazolyl]ethyl vinyl ether) also show the typical monomer emission bands in their fluorescence film spectra [35, 36].As ini-PPK sample, other two strong, broad, and partially overlapping fluorescence bands, centred at 394 and 421 nm, respectively, are also detected in the i-PBK spectrum. As already reported in our previous papers on i-PPK [19, 20], these bands can be attributed to two different excimers formed by close carbazole groups. In particular, the band at 421 nm was attributed to a fully overlapping conformation of two carbazole groups (sandwich-like excimer fluorescence), while the band at 394 nm was attributed from a partially overlapping conformation of two carbazole groups (second excimer fluorescence) (see Scheme 2).Scheme 2The formation of these two excimers was previously detected in PVK films and was also described in literature [35, 37–41]. Nevertheless, it is worth noting that the fluorescence due to “sandwich-like” excimers that is also common to all vinyl aromatic polymers is always observed in PVK. Instead, the fluorescence due to the high energy “partially overlapping” excimers, which is peculiar of vinyl polymers with pendant carbazole groups [39], is only associated with PVK syndiotactic sequences [39]. It was also reported that the polymer conformation allowing the formation of the high energy “partially overlapping” excimer state has to exist prior to initial excitation step [37, 41].Partially isotactic PVK commercial sample, used for comparison in this work, shows an emission spectrum where the fluorescence generated by the “sandwich-like” excimer state is predominant. Instead,i-PBK spectrum, as in the case of i-PPK, presents, in addition to the characteristic monomer emission bands, both the fluorescence bands attributable to two different excimers, “sandwich-like” and “partially overlapping,” having comparable intensity.


## 5.1. Synthesis and13C-NMR Characterization

Monomer, 9-(but-3-en-1-yl)-9H-carbazole, was synthesized following a synthetic procedure accurately described in the experimental part.Polymerization of monomer was performed at 20°C in toluene solution by using therac-[(CH3)2Si(indenyl)2]ZrCl2/methylallumoxane (MAO) catalytic system (see Scheme 1). The catalytic precursorrac-[(CH3)2Si(indenyl)2]ZrCl2, activated by MAO, is well known to promote the isospecific polymerization of α-olefins [15, 22, 23]. Recently, its high performances in the isospecific 9-(pent-4-en-1-yl)-9H-carbazole polymerization was also reported [19, 20].Scheme 1The obtained polymer (PBK) was fractionated by exhaustive extraction with boiling acetone and two different fractions, an acetone insoluble (65% of whole starting material) and a soluble (35% of whole starting material), were obtained.Both PBK fractions, analyzed by GPC, showed monomodal curves and narrow molecular weight distributions. The molecular weight of the acetone insoluble fraction (Mn=3000 Dalton, PDI = 1.6) becomes higher than the acetone soluble fraction (Mn=1922 Dalton, PDI = 1.10).The microstructure of PBK fractions was fully determined by13C NMR analysis, utilizing the carbon attributions in similar environments, reported in literature [19, 20, 24–27]. In Figure 1(a), the 13C NMR spectrum of the acetone insoluble PBK fraction sample is reported. As expected, this spectrum is fully consistent with both regio- and stereoregular polymer microstructure and, in particular, from the chemical shifts related to carbons 1 and 2, an isotactic microstructure of polymer (i-PBK) is assumed [24–26].Figure 1
13C NMR spectra of PBK fractions, (a) acetone insoluble, (b) acetone soluble (solvent: tetrachlorodideteuroethane; scale: hexamethyldisiloxane).The acetone soluble PBK fraction13C NMR spectrum (Figure 1(b)) is instead indicative of a less stereoregular polymer microstructure. Regioerrors are also recognized in this fraction.


## 5.2. X-Ray, DSC and Infrared Characterization

In Figure2(a), the X-ray diffraction pattern of the as polymerized i-PBK is reported.Figure 2
X-ray diffraction patterns of (a) as polymerized sample, (b) acetone-soluble fraction, (c) acetone-insoluble fraction, and (d) crystalline fraction after annealing atT = 200°C for 20 min.The X-ray pattern shows a small but well-defined reflection at 2θ ≈ 7° and other less defined reflections in the 2θ range of 10°–15° overlapped to a large amorphous halo centered at 2θ ≈ 20°. Such X-ray pattern indicates that a limited amount of crystalline phase is present in the as polymerized sample.X-ray spectra of acetone soluble and insoluble fractions ofi-PBK are shown in Figures 2(b) and 2(c), respectively.The pattern of the acetone-soluble fraction, Figure2(b), presents only a broad amorphous halo with two well defined humps at 2θ ≈ 12° and 20°, while the pattern of the acetone-insoluble fraction, Figure 2(c), shows many well-defined crystal reflections.The results of WAXD analysis of the amorphous and crystalline fractions of thei-PBK are in agreement with the NMR analysis, which shows that the acetone-insoluble fraction (crystalline fraction) is more stereoregular of the acetone-soluble fraction (amorphous fraction).It is worth noting that the two humps in the X-ray pattern of the amorphous fraction correspond to those observed in the spectrum of the as polymerized sample, and the few indistinct crystal reflections observed in the X-ray pattern of the as polymerized sample correspond to peaks of the crystalline fraction pattern.In Figure3, the second DSC heating run of the unfractionated polymer (Figure 3(a)) and that of its amorphous fraction (Figure 3(b)) are compared. The observed difference in glass transition (Tg) value can be rationalized on the basis of the fact that the molecular weight of the amorphous fraction, evaluated by GPC analysis, is smaller (Mn ≈ 2000 Da) compared to that of the unfractionated polymer (Mn ≈ 3000 Da).Figure 3
Second heating of DSC runs of (a) as polymerized (unfractionated) sample, (b) acetone-soluble fraction, and (c) first heating of DSC run of acetone-insoluble fraction.The first DSC heating run of the polymer crystalline fraction, is also shown in Figure3. Two separate and well-defined endothermic peaks, at T≈174°C and T=216°C, associable with distinct crystalline phases, are observed.Between the two endothermic peaks a weak exothermic peak atT ≈ 200°C, is also present. This peak can be tentatively interpreted as a crystallization phenomenon associated with the solid-solid transition between the two crystal forms which melt at T ≈ 174 and 216°C, respectively.In Figure2(d), the X-ray pattern of the i-PBK crystalline fraction after annealing at T = 200°C for 20 minutes is shown. Only some of narrow peaks of the pattern (c) of Figure 2 are still present, although slightly shifted. On the contrary, many reflections of the two patterns do not match each other.These differences can be rationalized by assuming that the two patterns correspond to two different crystalline phases, which are probably very similar.Both of these two crystalline forms cannot be obtained by crystallization from the melt, so that in the second DSC heating run (not showed in Figure3) of the i-PBK crystalline fraction, only a glass transition at T = 97°C is observed. This Tg value, which is very similar to that of the as polymerized i-PBK sample (see Figure 3(a)), appears to be intermediate between that reported for PVK (Tg = 211°C) (obtained from the second DSC heating run of poly(9-vinylcarbazole) purchased from Sigma-Aldrich s.r.l. (Milan, Italy) with an average Mn of 25,000–50,000) and i-PPK (Tg = 90°C) [20]. The observed differences between Tg of these polymers accord well with the widely accepted hypothesis that rigidity of polymer chains, on which Tg value depends, is affected by the side branches length of polymer chain.In detail, as for the PVK, the carbazole units directly connected to the main chain make the polymer chain extremely rigid [28], while, for PBK and PPK, the alkylene linkers, which connect the carbazole unit with the main chain spacing the polymer chains each other, increases the free volume and reduces Tg.The differentTg values of i-PBK and i-PPK, on the basis of this hypothesis, can be justified by the different length of the alkylene linker which is 2 and 3 C atoms for i-PBK and i-PPK, respectively.As for the infrared characterization of thei-PBK, particularly informative is the comparison with the PVK. The FTIR spectra of amorphous samples of PVK and i-PBK are very similar to each other. The most important difference is in the region of C-H stretching (Figure 4(a)) where the intensity ratio of the aliphatic to aromatic C-H stretching (at 2848–2918 cm−1 and 3021–3048 cm−1, resp.) increases in the i-PBK spectra, due to the (CH2)2 alkylene linker connecting the carbazole moiety to the main chain.Figure 4
FTIR spectra of PVK (line (A)); crystalline (line (B)); and amorphous (line (C)) fractions ofi-PBK.
(a)
(b)The same phenomenon has already been reported fori-PPK [20], a polymer homologue to i-PBK but having the linker connecting the carbazole to the main chain one carbon atom longer.In addition to the C-H stretching region, the region in which there are more differences between the PVK infrared spectrum and those of the amorphous and crystalline fractions ofi-PBK is in the wavelength range 1070–1260 cm−1 (Figure 4(b)).In Figure4(b), the absorption bands of carbazole ring vibrational modes, at 1121, 1132, and 1151 cm−1 as valued in the spectrum of PVK, assigned to C-H in-plane bending and ring deformation [29], remain substantially unchanged in the i-PBK spectra, although slightly shifted.On the contrary, the PVK absorption bands at 1224 and 1236 cm−1, assigned, respectively, to Ccarbazole-N and Caliphatic-N stretching [29–31], change position and intensity in the spectra of i-PBK fractions, and they are blue shifted at 1128 and 1241 cm−1, respectively. In addition a new band at 1180 cm−1 appears in both amorphous and crystalline i-PBK fractions.These differences are probably due to the influence that the alkylene linker has oni-PBK vibrational modes and in particular on vibrational modes involving the nitrogen of the carbazole group.Finally, it should be noted that additional bands at 1195 and 1224 cm−1 are present only in the spectrum of i-PBK crystalline fraction. These bands are possibly associated with the vibrational modes influenced by polymer chains packing in the i-PBK crystalline structure.


## 5.3. Optical Characterization

The good solubility ofi-PBK in chlorobenzene allowed the preparation of uniform and homogenous films of 100 nm thick.Figure5 shows the absorption spectrum of a i-PBK film sample. It presents several peaks maxima at around 230, 262, 295, 330, and 345 nm, where the two longest wavelengths are due to the carbazole group [32].Figure 5
Absorption spectrum ofi-PBK film.i-PBK fluorescence spectrum of the acetone insoluble fraction film sample measured under an excitation wavelength of 298 nm at room temperature is reported in Figure 6 (bottom curve). In Figure 6, for comparison, the fluorescence spectra of an i-PPK film sample [19, 20] (medium curve) and a commercial PVK sample (trade sample purchased from Sigma Aldrich Company presenting a partially isotactic microstructure) (curve on the top) are also shown. It is worth nothing that both i-PBK and i-PPK fluorescence spectra present very similar curve shape.Figure 6
Fluorescence spectra ofi-PBK, i-PPK, and PVK films.Thei-PBK spectrum exhibits two emission bands in the high energy region presenting peaks at 357 nm and 374 nm, respectively, which correspond to those from isolate monomer units [33, 34]. The same bands are also present in the i-PPK spectrum, but not in the PVK spectrum. This result can be related to the presence of the flexible spacer (-(CH2)3- for PPK and -(CH2)2- for PBK), absent in PVK, between the main chain and the carbazole pendant. It was found that other vinyl polymers with pendant carbazole groups connected to the skeleton chain by a flexible spacer like -O-(CH2)2- (poly[2-N-carbazolyl]ethyl vinyl ether) also show the typical monomer emission bands in their fluorescence film spectra [35, 36].As ini-PPK sample, other two strong, broad, and partially overlapping fluorescence bands, centred at 394 and 421 nm, respectively, are also detected in the i-PBK spectrum. As already reported in our previous papers on i-PPK [19, 20], these bands can be attributed to two different excimers formed by close carbazole groups. In particular, the band at 421 nm was attributed to a fully overlapping conformation of two carbazole groups (sandwich-like excimer fluorescence), while the band at 394 nm was attributed from a partially overlapping conformation of two carbazole groups (second excimer fluorescence) (see Scheme 2).Scheme 2The formation of these two excimers was previously detected in PVK films and was also described in literature [35, 37–41]. Nevertheless, it is worth noting that the fluorescence due to “sandwich-like” excimers that is also common to all vinyl aromatic polymers is always observed in PVK. Instead, the fluorescence due to the high energy “partially overlapping” excimers, which is peculiar of vinyl polymers with pendant carbazole groups [39], is only associated with PVK syndiotactic sequences [39]. It was also reported that the polymer conformation allowing the formation of the high energy “partially overlapping” excimer state has to exist prior to initial excitation step [37, 41].Partially isotactic PVK commercial sample, used for comparison in this work, shows an emission spectrum where the fluorescence generated by the “sandwich-like” excimer state is predominant. Instead,i-PBK spectrum, as in the case of i-PPK, presents, in addition to the characteristic monomer emission bands, both the fluorescence bands attributable to two different excimers, “sandwich-like” and “partially overlapping,” having comparable intensity.


## 6. Conclusions

Isotactic poly(N-butenyl-carbazole) (i-PBK) was synthesized by using the homogeneous isospecific Ziegler-Natta catalytic systemrac-[(CH3)2Si(indenyl)2]ZrCl2/methylallumoxane (MAO) and 9-(but-3-en-1-yl)-9H-carbazole monomer.The microstructures of PBK fractions were fully determined by13C NMR analysis and, for the first time, the isotactic microstructure of PBK (i-PBK) was unambiguously determined.WAXD analysis showed thati-PBK insoluble acetone fraction is crystalline, while i-PBK soluble acetone fraction is amorphous.DSC analysis ofi-PBK crystalline fraction showed two separate and well-defined endothermic peaks, at T ≈ 174°C and T = 216°C, associable with two distinct crystalline phases. The solid-solid transition between these two crystal forms was also observed as an exothermic peak at 200°C.i-PBK Tg value (96.8°C) became intermediate between that previously reported for PVK (Tg = 211°C) and i-PPK (Tg = 90°C).As for the infrared analysis,i-PBK showed FTIR spectra similar to that of PVK as regards the bands related to the carbazole group, but it presented a number of differences tentatively associated to the (CH2)2 alkylene group connecting the carbazole group to the main chain. In fact, this group, distancing the main chains, increases the flexibility of polymer chains and modifies the intra- and interchain interactions and therefore the normal vibrational modes of polymer.To optical analysis,i-PBK (crystalline fraction), similarly to i-PPK, showed a fluorescence film spectrum presenting both bands relative to isolate monomer units and other two, broad and partially overlapping bands due to different excimer states, “sandwich-like” and “partially overlapping,” respectively.It is worth noting that OLEDs showing white light emission, although of low efficiency, were obtained by usingi-PPK as emitting layer. The similar optical behavior of i-PBK with respect to that of i-PPK makes this material very promising for optical applications and deserving greater attention.The development of OLED devices based oni-PBK is in progress.



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*Source: 1656459-2016-03-07.xml*