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Polymers 2014, 6(2), 565-582; doi:10.3390/polym6020565
Published: 21 February 2014
Abstract: One hundred ninety three-nanometer candidate photoresist materials were synthesized by nitroxide-mediated polymerization (NMP). Statistical copolymerizations of 5-methacryloyloxy-2,6-norboranecarbolactone (NLAM) with 5–10 mol% of controlling co-monomers (which are necessary for controlled polymerizations of methacrylates by NMP with the initiator used) in the feed, such as styrene (ST), p-acetoxystyrene (AcOST), 2-vinyl naphthalene (VN) and pentafluorostyrene (PFS), using the unimolecular BlocBuilder® initiator in 35 wt% dioxane solution at 90 °C were performed. As little as 5 mol% controlling comonomer in the feed was demonstrated to be sufficient to lead to linear evolution of number average molecular weight Mn with respect to conversion up to 50%, and the resulting copolymers had dispersities Mw/Mn of ~1.3 in most cases, an attractive feature for reducing line width roughness (LWR) in photoresists. The copolymers generally showed relatively low absorbance at 193 nm, comparable to other 193-nm candidate photoresists reported previously, despite the inclusion of a small amount of the styrenic co-monomers in the copolymer.
Nitroxide-mediated polymerization (NMP), a type of controlled radical polymerization (CRP), combines the practicality of conventional free radical polymerization with the good microstructural control usually associated with living polymerizations, like ionic polymerization [1,2]. Traditionally, NMP mediated by TEMPO (2,2,6,6-tetramethylpiperidine-N-oxyl) was limited to the polymerization of styrenics only [3,4]. The development of the TIPNO (2,2,5-trimethyl-4-phenyl-3-azahexane nitroxide) and the SG1 (N-tert-butyl-N-(1-diethylphosphono-2,2-dimethylpropyl) nitroxide) families of nitroxides subsequently extended the ability of NMP to polymerize acrylic monomers [5,6,7] and acrylamides [8,9,10]. The successful control of methacrylates with SG1 was not achieved until Nicolas et al. demonstrated that with a small amount of styrene or acrylonitrile as the controlling co-monomer, the polymerization of methyl methacrylate (MMA) could be effectively controlled with relatively low dispersity and the ability to re-initiate a second batch of monomer [11,12,13]. Following this, NMP has been shown to be an effective and robust method for the synthesis of a variety of poly(methacrylate)s with a small amount of controlling co-monomers, such as styrene [14,15], 9-(4-vinylbenzyl)-9H-carbazole (VBK) , sodium 4-styrene sulfonate  and 2-vinylpyridine (2VP)  using the SG1-based BlocBuilder unimolecular initiator. Furthermore, NMP is able to provide tight control over the molecular weight distribution and excellent retention of chain end fidelity in bulk [9,19], aqueous (mini)emulsion [20,21,22] and ionic liquids [23,24]. In addition, the general applicability of NMP to design polymers with complex molecular architectures has also been demonstrated by the synthesis of hyperbranched polymers [25,26], star-shaped polymers [27,28,29], amphiphilic block copolymers [30,31] and graft copolymers [32,33,34]. It should also be noted here that the thermally-induced NMP was the route chosen for the materials. Photo-NMP is another route towards homo poly(methacrylates) that is advantageous in terms of energy (lower polymerization temperatures are possible) and for absorption properties (with no styrenic required, absorption problems could potentially be avoided) .
The miniaturization of electronic devices using lithography requires the design of functional polymers with well-defined molecular properties. For example, polymers are often used as photoresists to imprint desired patterns onto a substrate. Two CRP techniques, such as atom transfer radical polymerization (ATRP) [36,37,38,39] and reversible addition fragmentation chain transfer (RAFT) [40,41,42], have been used in the past to synthesize well-defined statistical copolymers with narrow molecular weight distribution for photoresists. Parameters that characterize pattern resolution, such as the line edge roughness (LER) and line width roughness (LWR), are influenced by physical/chemical properties, such as molecular weight, dispersity, composition and microstructure [41,43,44,45,46]. However, one drawback that makes ATRP and RAFT undesirable for photoresist materials is the requirement of metal catalysts and the chain transfer agents, respectively [42,45], which cause undesirable coloration, pungent odor and have to be removed through additional purification steps in order to meet the high purity standards used in the microelectronic industry. Indeed, the electronic/optical materials generally demand the metallic catalyst concentration to be below 1 ppm to avoid unfavorable photochemical effects [47,48]. Many studies have investigated the adverse effect of metallic contamination in photoresists on the lithography process and developed methods to limit the concentration to levels as low as 10 ppm [49,50,51,52].
In general, there are three basic requirements that all 193-nm (the current standard wavelength in the photolithography industry) resists have to satisfy: high optical transparency at 193 nm, good etch resistance and thermal stability to withstand high temperature processing conditions that are used in manufacturing [53,54]. Due to their high carbon contents, polymers with alicyclic units, such as the adamantyl and isobornyl groups, have been shown to have high etching durability [55,56]. Hydrophilic substituents, such as the hydroxyl, ester, acetate or gamma-butyrolactone groups, were also introduced to enhance the adhesion and solubility properties of the resists . To further improve the etch resistance ability of the lactone structure, the addition of norbornene lactone, oxatricyclodecanone and adamantyl lactone structures have proven to be highly effective [57,58,59]. One representative of this class of monomers is 5-methacryloyloxy-2,6-norboranecarbolactone (NLAM). Recently, Miyazaki et al. studied the synthesis of poly(NLAM) by ATRP . To the best of our knowledge, there have been no reports on the polymerization of NLAM by NMP. Thus, in this study, we report the first preparation of well-defined NLAM-rich random copolymers by NMP using BlocBuilder® as the initiator (Scheme 1). Specifically, the copolymerization kinetics of NLAM with different controlling comonomers, i.e., p-acetoxystyrene (AcOST), styrene (ST), 2-vinyl naphthalene (VN) and pentafluorostyrene (PFS), was investigated, and the absorption properties of the NLAM-rich copolymers were studied. This latter part is essential, as the methacrylate requires a controlling co-monomer for BlocBuilder-mediated NMP, which is often a styrenic, which can absorb at wavelengths near 193 nm. The absorption tests will show which co-monomer absorbs the least and/or show what kind of co-monomer content can be tolerated. Thus, this study will suggest the feasibility of NMP-synthesized materials as potential candidates for 193-nm photoresists.
2. Experimental Section
Calcium hydride (90%–95% reagent) and basic alumina (Brockmann, Type 1, 150 mesh) were obtained from Sigma-Aldrich and used as received. Chloroform (99.9% HPLC grade), N,N-dimethylformamide (DMF, 99.9% HPLC grade), dioxane (99%) and methanol (99%) were received from Fisher Scientific and used as received. Pentafluorostyrene (PFS, 99%) was purchased from Oakwood Chemicals, and 2-vinyl naphthalene (VN, 97%) was received from VWR International. N-(2-Methylpropyl)-N-(1-diethylphosphono-2,2-dimethylpropyl)-O-(2-carboxylprop-2-yl) hydroxylamine (99%, BlocBuilder®) and tert-butyl[1-(diethoxyphosphoryl)-2,2-dimethylpropyl]amino} nitroxide (SG1, > 85%) was received from Arkema. 5-methacryloyloxy-2,6-norboranecarbolactone (NLAM) was received from Kuraray and used as received. Styrene (ST, 99%) and p-acetoxystyrene (AcOST, 99%) were both received from Sigma-Aldrich and were purified to remove the inhibitor by passing through a column of basic alumina mixed with 5 wt% calcium hydride and then stored in a sealed flask under a head of nitrogen in a refrigerator until needed. 2,2′-Azoisobutyronitrile (AIBN, 98%) was received from Sigma-Aldrich and was purified by re-crystallization from methanol. The deuterated chloroform (CDCl3, 99%) used as a solvent for nuclear magnetic resonance (NMR) was obtained from Cambridge Isotopes Laboratory.
2.2. Synthesis of NLAM Random Copolymers
The syntheses were done in a 25-mL three-necked round bottom glass flask equipped with a reflux condenser, a thermal well and a magnetic stir bar. The flask was placed inside a heating mantle and the whole set-up mounted on top of a magnetic stirrer. Table 1 lists the formulations studied for the NLAM/X (X = controlling co-monomer) copolymerizations (Scheme 2). For example, for the experiment NLAM-AcOST-5, BlocBuilder (0.0498 g, 0.13 mmol), SG1 (0.0036 g, 0.013 mmol), NLAM (3.15 g, 14.2 mmol), purified AcOST (0.125 g, 0.77 mmol) and 1,4 dioxane (6.08 g, 69 mmol) were added to the reactor, and then, the reactor was sealed with a rubber septa. The thermocouple connected to a temperature controller was placed inside a thermal well and connected through one of the necks. A mixture of glycol/water (90/10 vol%) at a temperature of 5 °C was circulated (NesLab RTE 740 refrigerating circulator) through the condenser connected to one of the necks of the reactor to prevent any evaporation loss of the monomers and/or solvent. A purge of ultra-pure nitrogen was then introduced to the reactor for 30 min (while maintaining the reactor temperature at 40 °C to facilitate dissolution) to deoxygenate the reactants prior to polymerization. The purge was vented through the reflux condenser.
After purging at 40 °C for 30 min, the reactor was heated at a rate of about 10 °C min−1 to 90 °C with continuous nitrogen purge. The time at which the reactor temperature reached 90 °C was taken arbitrarily as the start of the reaction. Samples were then taken from the reactor periodically by a syringe until the samples became too viscous to withdraw. Then, reactions were stopped by removing the reactor from the heating mantle and letting the contents cool down to room temperature, while under continuous nitrogen purge. For each sample withdrawn during the polymerization, the polymer was precipitated twice with excess methanol. After filtration and recovery, the precipitated polymer was dried at 40 °C under vacuum in the oven overnight to remove any solvent and unreacted monomers. Gel permeation chromatography (GPC) was performed using narrow distribution, linear poly(methyl methacrylate) (PMMA, Agilent Technologies, molecular weight range 875 g mol−1 to 1,677,000 g mol−1) as standards with HPLC grade DMF with 0.1 wt% LiBr as the eluent at 50 °C, with the exception of NLAM/AcOST, copolymers for which HPLC grade chloroform was used as the eluent. Specifications of the GPC are described more fully in the Characterization section.
|Table 1. Formulations for 5-methacryloyloxy-2,6-norboranecarbolactone (NLAM)/X (X = controlling co-monomer) random copolymerizations initiated by BlocBuilder at 90 °C in 35 wt% 1,4 dioxane solution.|
|Sample ID#||[BlocBuilder]0 (mol L−1)||[NLAM]0 (mol L−1)||[X]0 (mol L−1)||[SG1]0 (mol L−1)||fX,0||[Dioxane]0 (mol L−1)|
[X]0 is the initial concentration of controlling co-monomer in the formulation (X = p-acetoxystyrene (AcOST), styrene (ST), vinylnaphthalene (VN), pentafluorostyrene (PFS)), and fX,0 is the initial molar fraction of the controlling co-monomer.
1H NMR (400 MHz, CDCl3, TMS) for poly(NLAM-ran-AcOST): (ppm) 4.3–4.75 (m, 2H, OCHCHO of the norbornene-lactone ring of NLAM, 3.15–3.3 (m, 1H, CHCOO of NLAM), 2.30–2.70 (m, 4H, 2 × CH2CHCOO of the norbornene-lactone ring of NLAM), 6.9–7.1 (s, 4Haromatic in AcOST).
1H NMR (400 MHz, CDCl3, TMS) for poly(NLAM-ran-ST): (ppm) 4.3–4.75 (m, 2H, OCHCHO of the norbornene-lactone ring of NLAM, 3.15–3.3 (m, 1H, CHCOO of NLAM), 2.30–2.70 (m, 4H, 2 × CH2CHCOO of the norbornene-lactone ring of NLAM), 6.9–7.1 (m, 5Haromatic in ST).
1H NMR (400 MHz, CDCl3, TMS) for poly(NLAM-ran-VN): (ppm) 4.3–4.75 (m, 2H, OCHCHO of the norbornene-lactone ring of NLAM, 3.15–3.3 (m, 1H, CHCOO of NLAM), 2.30–2.70 (m, 4H, 2 × CH2CHCOO of the norbornene-lactone ring of NLAM), 7.25–7.8 (m, 7Haromatic in VN).
13C NMR (500 MHz, CDCl3, TMS) for poly(NLAM-ran-PFS): (ppm) 168.5–180 (O–C=O), 136.5–147 (C–F), 114.5–118 (Caromatic in PFS), 76–85.5 (–CH– in norbornene-lactone ring of NLAM), 31.5–46 (–CH2– in NLAM, –CH2– in PFS), 18.5–21 (–CH2– in norbornene-lactone ring of NLAM).
2.3. Synthesis of Poly(NLAM) by Free Radical Polymerization
Poly(NLAM) was also synthesized by conventional free radical polymerization using 2,2′-azoisobutyronitrile (AIBN) as the initiator at 80 °C in 30 wt% dioxane solution. Zero-point-zero-six-two grams (0.38 mmol) of AIBN, 6.19 g (27.9 mmol) NLAM and 20.5 g (232 mmol) dioxane were added to a 50-mL reactor. The setup and procedures followed were the same as described above. The reaction was stopped after 50 min, and the resulting polymer was precipitated in methanol and dried at 40 °C under vacuum. The final polymer (Mn = 22,900 g mol−1, Mw/Mn = 1.73) was characterized by GPC relative to poly(methyl methacrylate) (PMMA) standards at 40 °C. This homopolymer was to be used as a comparison against the copolymers for the UV absorption experiments.
2.4. Chain Extension Experiments
Statistical copolymers NLAM/PFS-5 and NLAM/VN-10 were chain extended with PFS and VN, respectively, at 110 °C in 35 wt% dioxane solution. Copolymers containing PFS or VN are chosen because there has been little study done on their controlling abilities in NMP [60,61]. The experimental setup and procedures were the same as the syntheses for the statistical copolymers, NLAM/X, described earlier. For the chain extension of NLAM/PFS-5 with PFS, 0.60 g (2.7 mmol) macroinitiator, 1.1 g (5.6 mmol) PFS and 3.2 g (36 mmol) 1,4 dioxane were added to the reactor. Similarly, for the chain extension of NLAM/VN-10 with VN, 0.6 g (2.8 mmol) macroinitiator, 0.9 g (5.8 mmol) VN and 2.8 g (32 mmol) 1,4 dioxane were used. The reactions were stopped after about 3.5 h, and the polymer was then precipitated in methanol and dried in a vacuum oven at 40 °C overnight. The chain-extended products were characterized by GPC calibrated with poly(methyl methacrylate) standards (see the Characterization section for more details).
The overall monomer conversion was determined by 1H nuclear magnetic resonance (NMR) for all the copolymerizations, except the NLAM/PFS systems, for which gravimetry was used, due to the lack of protons in the PFS aromatic ring. The 1H NMR measurements were done with a 400 MHz Varian VNMRS spectrometer using CDCl3 solvent with 16 scans. 13C nuclear magnetic resonance (NMR) was used to estimate the copolymer compositions of NLAM/PFS copolymers. The 13C NMR measurements were done with a 500 MHz Varian VNMRS spectrometer using CDCl3 solvent with 5000 scans. The molecular weight distributions were measured using gel permeation chromatography (GPC, Water Breeze) with HPLC grade chloroform or DMF with 0.1 wt% LiBr as the mobile phase. A mobile phase flow rate of 0.3 mL min−1 was applied, and the GPC was equipped with 3 Waters Styragel® HR columns (HR1 with a molecular weight measurement range of 102–103 g mol−1, HR2 with a molecular weight measurement range of 5 × 102–5 × 104 g mol−1 and HR4 with a molecular weight measurement range 5 × 103–6 × 105 g mol−1); and, a guard column was used. The columns were heated to 50 °C during the analysis. The molecular weights were determined by calibration with linear narrow molecular weight distribution poly(methyl methacrylate) (PMMA) standards, and the GPC was equipped with a differential refractive index (RI 2410) detector. The differential scanning calorimetry (DSC) was carried out on a Q2000 (TA instruments, New Castle, DE, USA) at a heating rate of 10 °C min−1. Calibrations for temperature and heat flow were done using indium and benzoic acid standards, respectively, and the resulting glass transition temperatures (Tg) were calculated using the inflection method from the change in slope observed in the DSC traces. Resist polymers were dissolved in cyclopentanone/DMF (80/20 vol/vol) at 20–30 wt% relative to the solvents and spin coated at 2000 rpm on 1-inch quartz slides and then baked at 110 °C for 90 s. After baking, the absorption spectra of the polymers were measured by a Cary 5000 UV-Vis-NIR Spectrophotometer. Film thickness was determined using an Ambios XP-200 profilometer.
3. Results and Discussion
3.1. Kinetics of NLAM/X Random Copolymerizations (X = Controlling Comonomer)
The random copolymerizations of NLAM with small amounts of different controlling co-monomer X (X = AcOST, ST, VN or PFS) were done by NMP using BlocBuilder® as the initiator in 35 wt% 1,4 dioxane solution at 90 °C. The semi-logarithmic kinetic plots of ln[(1−x)−1] (x = monomer conversion) versus time are illustrated in Figure 1. The slopes of these plots were typically obtained from the linear fit of about five to seven sample points. The slope represents the apparent rate constant, 〈kp〉 [P•] (Table 2), where 〈kp〉 is the average propagation rate constant and [P•] is the concentration of the propagating macro-radicals. For the systems studied here, the 〈kp〉 [P•] reported were all obtained during the early stage of the polymerization, where the number average molecular weight increased linearly with conversion. From these values, 〈kp〉 〈K〉 can be estimated from Equation (1), where 〈kp〉 is the average propagation rate constant for the copolymerization, [P-SG1] is the concentration of the macroalkoxyamine, which is assumed to be equal to [BlocBuilder]0, and r is the ratio of the initial concentration of free nitroxide to BlocBuilder: [SG1]0/[BlocBuilder]0.
As shown in Figure 1, the kinetic plots are fairly linear with respect to the copolymerization time. Table 2 summarizes the experimental 〈kp〉〈K〉 values for the various copolymerizations studied. The apparent rate generally increased with decreasing concentration of controlling co-monomers in the feed, with the exception of the NLAM/ST system. We initially surmised that the excess free nitroxide added was slightly higher for NLAM/ST-5 compared to NLAM/ST-10, which would stabilize the system with the lower concentration of the controlling co-monomer. Even after adjusting for the concentration in the free nitroxide used, the difference in 〈kp〉〈K〉 was not significantly different between the two compositions. Thus, only a detailed copolymerization study of the NLAM/ST system over a wider composition range could help determine when the apparent rate constant would sharply increase with decreasing ST content. Lessard et al. examined the random copolymerizations of different methacrylates with styrene as the controlling co-monomer under similar condition to ours and reported the 〈kp〉〈K〉 value of (9.8 ± 0.3) × 10−6 s−1 for the copolymerization of butyl methacrylate with 8.0 mol% styrene in the feed . This is comparable to the 〈kp〉〈K〉 values obtained in the NLAM/ST system investigated in this study, which were (1.0 ± 0.1) × 10−5 s−1 and (8.4 ± 0.6) × 10−6 s−1 for 5 mol% and 10 mol% styrene in the feed, respectively. Furthermore, Miyazaki et al. studied the synthesis of NLAM via ATRP in DMF and o-dichlorobenzene (ODCB) solution with a target Mn of 22.3 kg mol−1 at 70 °C using 1 M equivalent of EtBrP (ethyl 2-bromopropionate) as the initiator, 1 M equivalent of CuBr as the catalyst and 4 M equivalent of PMDETA (pentamethyltriethylenetetramine) as the ligand ([M]:[I]:[Cu]:[L] = 100:1:1:4) and obtained an apparent rate constant, 〈kp〉 [P•], of 8.2 × 10−5 s−1 , which is not too dissimilar to the apparent rate constants observed in this study (i.e., (1.2 ± 0.1) × 10−4 s−1 for NLAM/AcOST-5, (9.2 ± 0.8) × 10−5 s−1 for NLAM/ST-5, (7.3 ± 0.6) × 10−5 s−1 for NLAM/VN-5 and (5.3 ± 0.4) × 10−5 s−1 for NLAM/PFS-5). Furthermore, there seem to be insignificant differences in the apparent rate constants for copolymerizations done with the various co-monomers studied, which can be due to the similarities in the chemical structure of the co-monomer and the low co-monomer initial feed concentration used.
|Table 2. The summary of copolymerization kinetic data of 5-methacryloyloxy-2,6-norboranecarbolactone (NLAM)/X (X = controlling co-monomer) controlled by BlocBuilder® at 90 °C in 35 wt% 1,4 dioxane solution.|
|Experimental ID||fX,0||r||〈kp〉〈K〉 (s−1)||〈kp〉[P•] (s−1)|
|NLAM/AcOST-5||0.05||0.10||(1.2 ± 0.1) × 10−5||(1.2 ± 0.1) × 10−4|
|NLAM/AcOST-10||0.11||0.10||(6.3 ± 0.5) × 10−6||(6.3 ± 0.5) × 10−5|
|NLAM/ST-5||0.05||0.11||(1.0 ± 0.1) × 10−5||(9.2 ± 0.8) × 10−5|
|NLAM/ST-10||0.10||0.09||(8.4 ± 0.6) × 10−6||(9.3 ± 0.7) × 10−5|
|NLAM/VN-5||0.05||0.10||(7.3 ± 0.6) × 10−6||(7.3 ± 0.6) × 10−5|
|NLAM/VN-10||0.11||0.08||(3.8 ± 0.4) × 10−6||(4.7 ± 0.5) × 10−5|
|NLAM/PFS-5||0.05||0.09||(4.8 ± 0.4) × 10−6||(5.3 ± 0.4) × 10−5|
|NLAM/PFS-10||0.10||0.10||(3.8 ± 0.3) × 10−6||(3.8 ± 0.4) × 10−5|
fX,0 is the initial molar fraction of the controlling co-monomer in the formulation (X = p-acetoxystyrene (AcOST), styrene (ST), vinylnaphthalene (VN), pentafluorostyrene (PFS)).
3.2. Characterization of NLAM/X Statistical Copolymers
The evolution of the number average molecular weight (Mn) versus conversion is plotted in Figure 2. A linear increase of Mn with conversion is one of the key features of a living polymerization. All the NLAM/X copolymerizations, although not true living systems, exhibited superficially living characteristics and showed a linear trend of Mn versus conversion up to about 50% conversion, except the NLAM/ST system, which remained fairly linear up to 60 mol% conversion. At higher conversions, the plots tend to plateau. The reason for the plateau could be attributed to the chain transfer side reactions to the solvent and monomers, which become more prevalent at higher conversions . However, it should be noted that the styrenic comonomer tended to be incorporated preferentially into each of the copolymers, and the preferential incorporation could have led to irreversible termination reactions at a higher conversion, as the controlling co-monomer concentration would be steadily depleted or removed completely. The polymerization control could be lost in such cases. This would result in lower apparent average molecular weight and higher dispersities (Mw/Mn), since new chains were created when the radicals transfer to monomer or solvent molecules. The newly created chains are probably still able to polymerize in a controlled manner, but with a significant fraction of new chains at low molecular weight, this would result in a lower than expected Mn and a broader molecular weight distribution. Greszta et al. demonstrated that the combination of chain transfer to monomer and alkoxyamine decomposition were the main reasons for lower Mn and higher Mw/Mn at high conversions in the polymerization of styrene with TEMPO nitroxide .
All GPC characterizations of NLAM/X copolymers were initially done using chloroform as the eluent. However, it was observed that except for the NLAM/AcOST copolymers, the other copolymers showed undesired absorption issues with the columns, such as abnormally long low-molecular weight tailing. Consequently, the molecular weights for the NLAM/ST, NLAM/VN and NLAM/PFS copolymers were measured again using DMF with 0.1 wt% of LiBr as the eluent. It should be noted that the experimentally measured Mns (Figure 2b–d) are slightly above the theoretical lines. This could be ascribed to the polymer-column, polymer-solvent interactions induced by the addition of LiBr in the DMF eluent, which was used to avoid the adsorption problems observed in the GPC chromatograms [64,65]. As a side effect, the retention volumes of GPC measurements could be higher or lower than those in pure DMF, depending on the polymers and columns used [64,65,66,67]. In this case, the Styragel columns, being negatively charged, repel the weakly negatively charged polymer coils and, thus, resulted in a slightly lower retention time or higher apparent molecular weight than would be expected . Furthermore, it should be noted that the GPC measurements were based on calibration by PMMA, which may lead to a discrepancy, due to its structural difference from NLAM copolymers.
The characterization of all copolymers synthesized is summarized in Table 3. All the final copolymers are fairly NLAM-rich and had Mw/Mn s of around 1.3, except that of the NLAM/PFS-5 copolymer, which had Mw/Mn of 1.47. P-acetoxystyrene (AcOST), which has been employed in the past as a key component in 248-nm photoresists , exhibited the best controlling ability based on the lowest dispersity (Mw/Mn ~ 1.29) at a concentration as low as 5 mol% in the feed. Pentafluorostyrene (PFS), also offering relatively good control (Mw/Mn ~ 1.47 and 1.31 for 5 and 10 mol% in the feed, respectively), is of interest, because fluorinated polymers have been shown to be good candidates for both 157-nm and 193-nm photoresists, due to their low absorption, good etch resistance properties [69,70,71,72,73] and high hydrophobicity [74,75], which is especially important in immersion lithography. 2-vinyl naphthalene (VN) was also an effective co-monomer in being able to produce copolymers with low dispersities (Mw/Mn ~ 1.3) with as low as 5 mol% in the feed. The naphthalene unit also showed relatively low absorption at 193 nm (Figure 3), and its derivatives have been used as chain transfer agents in the syntheses of well-defined 193-nm photoresists by RAFT [40,45]. The absorption spectra (at wavelengths from 185–350 nm) of NLAM-rich copolymers synthesized by NMP and poly(NLAM) (= 22,900 g mol−1, Mw/Mn = 1.73) made by conventional free radical polymerization are presented in Figure 3. All polymers exhibited absorbances below 0.8 μm−1. NLAM/PFS-5 showed a very low absorbance of around 0.2 μm−1 at 193 nm, while NLAM-VN-5 and NLAM-ST-5 had relatively higher absorbances of about 0.5–1.0 μm−1 at 193 nm, and this could be partially due to the higher mole fractions of VN and ST present in the respective final copolymers. Overall, the small amount of the controlling co-monomers added did not significantly affect the optical transparency of the poly(NLAM)-rich copolymers at 193 nm compared to pure poly(NLAM), and all the copolymers exhibited absorbance levels comparable to other 193-nm candidate photoresist materials previously reported in the literature [76,77,78,79].
|Table 3. Molecular characterization of NLAM/X (X = controlling co-monomer) random copolymers synthesized at 90 °C in 35 wt% 1,4 dioxane solution with BlocBuilder® and additional SG1 free nitroxide.|
|Sample ID#||fcomonomer,0||Conversion x||FNLAM a||Mn (g mol−1)||Mw/Mn||tpolymerization (min)||Tg (°C)|
a FNLAM is the molar fraction of NLAM in the final copolymer as determined by 13C NMR for NLAM-PFS copolymers or 1H NMR for the other copolymers.
3.3. Chain Extensions of Selected Copolymers
The statistical copolymers, NLAM/PFS-5 and NLAM/VN-10, were chain extended by VN and PFS, respectively, to examine their reinitiation ability. Copolymers controlled by PFS and VN were chosen, because PFS showed very low absorbance and VN has never been tested as a controlling co-monomer in NMP [60,61]. The GPC chromatograms of the chain extension are shown in Figure 4. The chain-extended block copolymers (shown as dotted lines) all shifted to lower elution times compared to their macroinitiators (shown as solid lines). The Mns of the block copolymers were slightly higher compared to those of their respective macroinitators. Indeed, the chain-extended block copolymer, NLAM-PFS-5-PFS, resulted in Mw/Mn of 1.56, while NLAM-VN-10-VN showed Mw/Mn of 1.48 (Table 4). These results confirmed the ability of the macroinitiators to reinitiate a new batch of monomer and polymerize in a controlled way, which superficially resembles the features expected of truly living polymers.
|Table 4. Molecular characterizations for NLAM/PFS-5 and NLAM/VN-10 chain extensions with PFS and VN, respectively.|
|Sample ID||Macroinitiator||Chain-Extended Polymer|
|Mn (g mol−1)||Mw/Mn||FNLAM a||Mn (g mol−1)||Mw/Mn||FNLAM b|
a FNLAM is the molar fraction of NLAM in the macroinitiator as determined by 13C NMR or 1H NMR; b FNLAM is the molar fraction of NLAM in the final chain-extended polymer as determined by 13C NMR or 1H NMR.
Well-defined random candidate copolymers rich in NLAM for 193 nm photoresists were synthesized for the first time by NMP at 90 °C in 1,4 dioxane solution with BlocBuilder® as the unimolecular initiator. The polymerization kinetics were examined for four different types of controlling co-monomers for NLAM (i.e., AcOST, ST, VN and PFS). In all cases, as little as 5 mol% controlling co-monomer in the feed was demonstrated to be sufficient in producing the linear evolution of the number average molecular weight against conversion in the range studied (up to 50% conversion), suggesting that the polymerizations were relatively well controlled. Further, the resulting copolymers were characterized by GPC and showed relatively narrow molecular weight distributions (~1.3 in most cases) and relatively low absorbance, which ensured high optical transparency. Selected copolymers NLAM/PFS-5 and NLAM/VN-10 were used as macroinitiators and successfully chain-extended with new batches of PFS and VN monomers, respectively, at 110 °C in 35 wt% dioxane solution.
This work was supported by NanoQuébec College Technology Transfer Center (CCTT) grant, and Z.-J.W. was partially supported by the Eugenie Lamothe Scholarship. The authors thank Motonari Nakamura and Hideki Matsuda of Kuraray Co. Ltd. (Tokyo, Japan) for the kind donation of NLAM, and Scott Schmidt and Noah Mary of Arkema, Inc. (King of Prussia, PA, USA), for their help in obtaining the BlocBuilder® alkoxyamine initiator used in this work.
Conflicts of Interest
The authors declare no conflict of interest.
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