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Crystalline CO2-based polycarbonates prepared from racemic catalyst through intramolecularly interlocked assembly

The crystalline stereocomplexed polycarbonates can be prepared by mixing enantiopure polymers with opposite configuration, which derived from the asymmetric copolymerization with CO2 using enantiopure catalyst or/and chiral epoxides. Herein, we develop a powerful strategy for producing crystalline intramolecular stereocomplexed polycarbonates from racemic catalysts, which possess similar thermal stability and crystalline behaviour in comparison with the stereocomplexes by mixing opposite enantiopure polymers. Living polymer chains shuttle between catalyst molecules with different configurations to produce diastereomeric active species which is suggested to be responsible for the formation of isotactic multiblock polycarbonates in racemic bimetallic cobalt catalyst-mediated stereoselective copolymerization of CO2 and meso-epoxides. Solid-state NMR spectroscopy study suggests that the interaction in the carbonyl and methine regions is responsible for the strong crystallization capacity and compact package structure in the crystalline polycarbonates.

It is generally known that the physical properties of a polymer are determined not only by the monomer structure, its molecular weight and polydispersity, but also by the relative stereochemistry (the spatial arrangement of atoms or groups in a polymeric unit) of adjacent locations in the polymeric chains. A representative example is the widely studied polypropylene. The isotactic polypropylene is a typical semicrystalline material, possessing a melting temperature (T m ) of 130 À 175°C, dependent on the isotacticity, while the amorphous polypropylene is a viscous polymer at ambient temperature with a T g of B0°C (ref. 22). For CO 2 -based polycarbonates, in comparison with their amorphous structure, the crystalline forms should show improved thermal and mechanical properties, due to the high stereoregularity. In the recent contributions, some crystalline polycarbonates were prepared by stereospecific copolymerization of CO 2 and epoxides using enantiopure metal-complex catalysts [23][24][25] . Notably, isotactic polycarbonates from meso-epoxides showed high levels of crystallinity, possessing T m s of 179 À 273°C, dependent on the structure of the epoxides [26][27][28][29][30] . Interestingly, the cocrystallinzation of amorphous isotactic polycarbonates having opposite configurations and identical structures was observed to form crystalline stereocomplexes 31,32 , which show enhanced thermal stability and new crystalline behaviour, significantly distinct from the component enantiomers. These discoveries open up a new way to prepare various semicrystalline materials having a wide variety of physical properties. Nevertheless, these crystalline materials all originate from chiral isotactic polycarbonates prepared by the enantiopure metalcomplex-mediated CO 2 /epoxides copolymerization. As a consequence, these processes are far away from practical applications, due to the high cost of chiral catalysts. Therefore, the exploration of the synthesis of crystalline CO 2 -based polycarbonates from racemic catalyst and rac-or meso-epoxides is highly desirable.
Herein, we report an approach for the synthesis of intramolecular stereocomplexed polycarbonates by stereoselective copolymerization CO 2 with meso-epoxides using racemic dinuclear Co(III) complex as catalyst (Fig. 1), which possess similar thermal stability and crystalline behaviour in comparison with the stereocomplexes by mixing opposite enantiopure polymers.

Results
Synthesis of crystalline polycarbonates from 3,5-dioxaepoxide. For the alternating copolymerization of CO 2 with meso-epoxides mediated by racemic isotactic catalyst systems, three possible microstructures might be observed in the resultant copolymers, dependent on the copolymerization chain growth rate (R g ) and polymer chain-transfer rate (R t ) (Fig. 2). Only when R g is significantly higher than R t , the racemic isotactic catalystmediated copolymerization reaction provides isotactic polycarbonates or isotactic multiblock polymers. The racemic-(SalBinap)-AlO i Pr complex has been demonstrated to be very effective for the ring-opening polymerization of racemic lactide, affording the crystalline, stereoblock polymers 33 . Coates and coworkers presented the first report for synthesizing a broad range of highly isotactic polyethers via the enantioselective polymerization of racemic epoxides using racemic catalyst 34-36 . In this system, (S)-binaphthol linked dinuclear cobalt complex predominantly catalysed the ring-opening polymerization of (S)-epoxides to afford (S)-polyethers, while the polymerization of (R)-epoxides only concerned (R)-binaphthol linked catalyst to provide (R)-polyethers. The resultant mixture of (S)-and (R)-polyethers are highly isotactic, and most of them display high T m values. Nevertheless, no cocrystallization occurs in the resultant mixture, in comparison with (S)-or (R)-polyethers.
Previously, we have demonstrated that isotactic (R)-PCXC or (S)-PCXC were easily dissolved in various organic solvent, such as dimethylsulphoxide and tetrahydrofuran (THF), while stereocomplexed PCXC prepared from mixing equivalent (R)-and (S)-PCXC had no solubility in these solvents. It was found that the copolymer formed from the racemic catalyst system also had no solubility in both dimethylsulphoxide and THF, suggesting the formation of the stereocomplex. Furthermore, methanol was added as a chain-transfer reagent to the copolymerization mediated by rac-1/PPN-DNP catalyst system at the identical reaction conditions. We discovered that the resultant polymers were also crystallizable, although the melting temperature was decreased to a certain extent ( Table 1, entries 1-4). For example, a T m of 221°C was found in the copolymer produced from rac-1/PPN-DNP catalyst system in the presence of 100 equivalents of MeOH, which is 119°C lower than the PCXC resulted from the same catalyst in the absence of MeOH ( Supplementary Fig. 1). The addition of methanol also resulted in the significant decrease in the copolymerization rate. In addition, a decrease in M n is very obvious, and thereby causing Isotactic multi block polycarbonates n n m n n R g = polymer chain growth rate R t = polymer chain transfer rate Figure 2 | Effects of polymer chain growth and transfer rate on the polymer structure. Three possible microstructures produced from the alternating copolymerization of CO 2 with meso-epoxides using racemic isotactic catalyst. Table 1 | Enantiopure Co(III)-complex-mediated asymmetric CO 2 /meso-epoxides copolymerization*. ARTICLE their dissolvable in THF and dimethylsulphoxide. 13 C NMR analysis show that the peaks corresponding to carbonyl and methine region were found to be splitted when the reaction was carried out in the presence of methanol ( Supplementary Fig. 2), suggesting a decrease in stereoregularity. It is worth noting that the intensities of various diffraction peaks in the copolymer sample from racemic catalyst are obviously lower than the stereocomplexed PCXC obtained from the 1:1 mixture of the opposite enantiomers (Fig. 3, bottom, plots B and C). In addition, the melting endothermic peak is also slightly lower than that of the stereocomplexed PCXC with a T m of 347°C (Fig. 3, top, plots B and C). These results suggest that the crystallinity of the resultant PCXC from racemic-1 catalyst system is significantly lower than that of the stereocomplexed PCXC consisted of the mixed opposite enantiomers. We tentatively assume that the copolymer from racemic-1 catalyst system is an isotactic multiblock polymer. The reduced isotacticity originates from the stereoerrors in the copolymer caused by the polymer growth-chain transfer between (R,R,R,R)-1 and (S,S,S,S)-1 during the copolymerization. As a result, the intramolecular cocrystallization of the isotactic multiblock-PCXC from racemic-1 catalyst system predominantly contributes the formation of intramolecular stereocomplexed polycarbonates.
Solid state NMR spectroscopy is a powerful tool for studying the polymer segment, structure and dynamics. Macromolecular motions covering a wide range of time scales have long been considered to affect the physical and mechanical properties [37][38][39][40] . Usually, polymers in amorphous state show high-amplitude motions, especially for the temperature above the T g s. As previously mentioned, there are huge differences in physical properties for the amorphous, enantiopure and stereocomplexed-PCXCs in solid state, such as solubility, melting and crystalline behaviour. In the present study, solid state NMR spectroscopy was also employed for studying the difference in microstructure of various PCXCs (Fig. 5). Spin-lattice relaxation time (T 1 ) was measured for each carbon atom in four representative PCXC samples under the cross-polarisation condition by application of the saturation recovery-based sequence ( Table 2). We discovered that the T 1 value of carbonyl region for the enantiopure PCXC was longer than the amorphous state. Especially, the T 1 value of carbonyl region for the stereocomplexed PCXC is up to 223 s, which is 175 s longer than the amorphous state and 131 s longer than enantiopure-PCXCs, in accordance with its much stronger crystallization capacity and compact package structure. Notably, it was demonstrated that PCXC resulted from racemic-1 (multiblock-PCXC) possessed a similar structure with the stereocomplexed PCXC, because its T 1 value in carbonyl region also reached to 156 s. There is an interesting information for methine region, which was found to be splitted to three peaks for multiblock-PCXCs, and two peaks for stereocomplexed-PCXCs. The T 1 values are 165 and 150 s for stereocomplexed-PCXCs, in agreement with 110 and 116 s for multiblock-PCXCs. However, no split was observed in the methine region for amorphous or enantiopure-PCXCs, in which T 1 values are 38 and 36 s, respectively. Interestingly, T 1 value for the middle peak in the methine region for multiblock-PCXCs is 50 s, corresponding to the methine region for amorphous or enantiopure-PCXCs. We tentatively ascribe it to the minor glassy state in the crystalline domains, which originated from the stereoerrors in the copolymer caused by the polymer growth-chain transfer  between (R,R,R,R)-1 and (S,S,S,S)-1 during the copolymerization. Nevertheless, T 1 values of quaternary and primary carbon for amorphous PCXCs were very similar to those measured for stereocomplexed-and multiblock-PCXCs, indicating that they are more inclined to motion and the energy can be released more easily.
Indeed, 13 C NMR spectra of carbonyl and methine regions in Fig. 4 did not give the accurate isotacticity of the multiblock-PCXCs originated from the racemic catalyst system. In order to confirm the formation of the isotactic multiblock structure, cyclohexene oxide (CHO) was chosen as a model monomer of meso-epoxides for testing the stereoregularity of its CO 2 copolymer produced by racemic Co(III) complexes, since the microstructure of poly(cyclohexene carbonate) (PCHC) was wellcharacterized [41][42][43] . Indeed, CHO also has relatively high reactivity in copolymerizing with CO 2 catalysed by both mono-and di-nuclear Co(III) complexes in the presence of a nucleophilic cocatalyst. In previous study, we have demonstrated that for the mono-nuclear Co(III) complex-mediated CO 2 /epoxide copolymerization, the dissociation of the propagating carboxylate from the metal centre is a much faster process than propagation, and the free propagating carboxylate can also act as a nucleophile for attack at a cobalt-coordinated epoxide, so the binary catalyst system of racemic mono-nuclear Co(III)-Salen complex and PPN-DNP for CHO/CO 2 copolymerization provided atactic PCHC 18 . On the contrary, the racemic dinuclear Co(III) complex 1 gave isotactic-enriched PCHC, based on the 13 C NMR analysis. However, the isotacticity is obviously lower than that obtained from enantiopure dinuclear Co(III) complex. This means the occurrence of the copolymerchain transfer between two kinds of catalyst molecules with different configurations. Previously, various stereoregular PCHCs tetrad and triad sequences have been assigned in the 13 C NMR spectrum 42,43 . In keeping with the previously established conventions in this field, it is important to note that [m] and [r] assignments used herein represent the relative stereochemistry of the carbons of the cyclohexene carbonate units (Supplementary Fig. 3). By synthesizing model poly(cyclohexene carbonate) oligomers or using Bernoullian statistical methods, all [mmm] and [mmr] tetrads were correlated to one central resonance at 153.7 p.p.m. and the remaining r-centred tetrads resided in the 153.3-153.0 p.p.m. range. The carbonyl region of the 13 C NMR spectra of various PCHCs resulted from different catalysts or conditions is shown in Fig. 6 (The relationship between the tetrad sequences and the polymer microstructures was described in Supplementary Fig. 3). On the basis of the peaks assigned to the appropriate tetrads in accordance with the literature, the PCHC with a P m of 0.84 obtained from (S,S,S,S)-1/PPN-DNP catalyst system revealed a 13 C NMR spectrum with two distinct resonances at 153.70 and 153.04 p.p.m. assigning to [mmm þ mmr] and [mrr] tetrads, respectively (Fig. 6, plot B). Especially, the peak at 153.04 p.p.m. for PCHC with a P m of 0.96 decreased significantly (Fig. 6, plot A). The r-centred [mrr] tetrad was produced by the errors in the chain growth (mismatched monomer was incorporated) and then corrected by the chiral environment that is constructed by the ligand around the metal centre through an enantiomorphic site control. However, for polycarbonates resulted from racemic-1 (Fig. 6, plot C), a peak at 153.22 p.p.m. was discovered, corresponding to [mrm] tetrad, significantly distinct from PCHC resulted from (S,S,S,S)-1 with the same P m s (Fig. 6, plot B). Moreover, because of the formation of [mmr] tetrads, the peak corresponding to m-centred tetrads of polycarbonates resulted from racemic-1 become broaden in comparison with the PCHC with the identical stereoregularity.  The 13 C NMR spectra of methylene region also confirmed the results (Supplementary Fig. 4). The presence of a small [mrr] peak also suggests that a minimal amount of the unpreferred enantiomer is incorporated into the chain at a level, consistent with the PCHCs described in plots A and B.
On the basis of [mrm] tetrad in 13 C NMR analysis, we can conclude that the polymer should have -RRRRRRSSSSSS-or -SSSSSSRRRRRR-sequences in the main chain. In fact, the polycarbonates produced from racemic-1 has a stereo multiblock structure with alternating blocks of (R)-and (S)-polymer segments, rather than a stereocomplex of two highly enantiomerically enriched chains. A statistical model was used to simulate the spectrum of the PCHC with stereochemical defects formed in the polymer growth-chain transfer between (R,R,R,R)-1 and (S,S,S,S)-1, suggesting that a block in the stereo multiblock PCHC contain an average of five enantiomerically pure carbonate units.
In the recent contributions, we demonstrated that the enantiopure biphenol-linked dinuclear Co(III) complex 1 was a privileged chiral catalysts for asymmetric copolymerization of CO 2 with various meso-epoxides, showing high activity and excellent enantioselectivity [27][28][29] . The mechanistic study revealed that chain-growth step predominantly involves an intramolecular bimetallic cooperation mechanism, wherein alternating chain growth and dissociation of propagating carboxylate species takes turn between two Co(III) ions from the inside cleft of dinuclear Co(III) catalysts by the nucleophilic attack of the growing carboxylate species at one metal centre towards the activated epoxide at the other 44 . It was also found that the propagating polymer chain transfer could be caused by protic solvents such as water and methanol, rather than the excess cocatalyst. Although every effort has been made to keep the copolymerization reaction anhydrous, we were concerned that trace quantities of water might be present, and thereby cause the growing polymer-chain transfer. Furthermore, it was found that the addition of 10 equiv. of methanol resulted in the significant decrease in copolymer molecular weight from 32.0 to 10.1 kg mol À 1 , and a slight loss in P m from 0.82 to 0.79 (Table 1, entry 8).
On the basis of the evidence and analysis mentioned above, the possible formation process for isotactic multiblock PCHC is proposed in the Fig. 7. Since the insertion of CO 2 into the growing polymer chain is a fast process, the predominant ringopening event is the reactions of (S)-1 with (R)-C À O and (R)-1 with (S)-C À O bond of CHO, affording (S)-PCHC and (R)-PCHC, respectively (enantiomeric active species A and B). However, the adventours water or the addition of protic solvent probably results in polymer-chain exchange between the (R)-PCHC anchored on (R)-1 and the (S)-PCHC anchored on (S)-1, affording the (S)-PCHC anchored on (R)-1 and the (R)-PCHC anchored on (S)-1 (diastereomeric active species C and D). At this point, polymer chain propagation resumes with the favoured stereoisomer, creating a diblock structure. The polymer chain exchange and propagation take place repeatedly to provide the isotactic multiblock polycarbonates.
It is a pity that the isotactic multiblock PCHC with a P m of 0.82 was amorphous material with a T g of 125°C, slightly higher than the atactic PCHC. Indeed, no crystallizability of the isotacticityenriched PCHC is not strange. In previous contribution, we have demonstrated that only PCHCs with more than 90% isotacticity were crystallizable 26 . However, we expect with great passion the formation of the intramolecular stereocomplexed PCHC, since a stereocomplex formed by the polymer assembly of optically active PCHCs with opposite configurations was previously confirmed 30 . In order to validate our supposition, solid state NMR spectroscopy was also employed for studying the difference of the microstructure of various PCHCs. (Supplementary Fig. 5 and Supplementary Table 1). As anticipated, the T 1 value of carbonyl region for the stereocomplexed PCHC is up to 271 s, which is 223 s longer than that for the amorphous PCHC. Similarly, the T 1 values of methine (250 and 195 s) and methylene carbons (146 and 110 s) for the stereocomplexed PCHC are significantly longer than that for the amorphous PCHC (35 s for methine region, and 23 and 21 s for methylene carbons). However, for the isotactic multiblock PCHC, the T 1 values of carbonyl region and methine carbons are 56 and 39 s, respectively, while that of methylene carbons are 26 and 24 s. These values are slightly higher than that for the amorphous state, but significantly lower than that for the stereocomplexed PCHC.

Discussion
In conclusion, novel intramolecular stereocomplexed polycarbonates were synthesized by the stereoselective copolymerization of CO 2 and meso-epoxides using racemic bimetallic cobalt catalyst system. Highly enantioselective chain growth in an enantiopure catalyst molecule and the copolymer-chain transfer between different configuration catalyst molecules results in the formation of the isotactic multiblock polycarbonates. Solid state NMR spectroscopy study suggests that the interaction in the carbonyl region is responsible for the strong crystallization capacity and compact package structure in the crystalline polycarbonates. This is the only example for the synthesis of crystalline CO 2 polymers from racemic catalyst. Due to the use of the inexpensive racemic or achiral ligand, the present synthesis strategy is of great importance for preparing various intramolecular stereocomplexed polycarbonates with enhanced thermal stability.

Methods
General. All manipulations involving air-and/or water-sensitive compounds were carried out in a glove box or with the standard Schlenk techniques under dry nitrogen. CO 2 (99.995%) was purchased from Dalian Institute of Special Gases and used as received. Methylene chloride and chloroform were distilled from calcium hydride under nitrogen. Tetrahydrofuran and toluene were distilled from sodium/  benzophenone under nitrogen. Epoxides were purchased from Acros and distilled over calcium hydride.
Fast-scan chip calorimeter. Fast-scan chip calorimetry (FSC) was performed with the commercialized FSC (Flash DSC1, Mettler-Toledo, Switzerland). The empty chip-sensor was calibrated according to the standard procedure before the experiment. The ready temperature of test module for all measurements was set as 30°C. Purge nitrogen gas was used as the protection atmosphere with the constant flow rate 50 ml min À 1 . First cycle: from 20°C to 280°C at a heating rate of 3,000 K s À 1 , and holding at 280°C for 5 min, and from 280 to 20°C at a cooling rate of 3,000 K s À 1 . Second cycle: from 20°C to 400°C at a heating rate of 3,000 K s À 1 . For all FSC analysis, the result was given based on second cycle.
Solid state NMR experiments. Solid state NMR experiments were performed using an Agilent DD2-500 MHz NMR spectrometer in 4-mm ZrO 2 rotors at MAS frequencies ranging from 12 to 14 kHz. 13 C cross-polarisation MAS NMR spectra were collected at 125 MHz with a B1( 13 C) field nutation frequency of 100 kHz, a contact time of 3 ms and a recycle delay of 4 s. 13 C spin-lattice relaxation experiments were carried out under CPMAS conditions using the saturation recoverybased sequence. The chemical shifts were referenced to the adamantane with the upfield methine peak at 29.