Jie
Chen
a,
Ting
Qiu
c,
Wei
Yan
d and
Charl F. J.
Faul
*b
aCollege of Environment and Resources, Fuzhou University, Fuzhou 350116, P. R. China
bSchool of Chemistry, University of Bristol, Bristol, BS8 1TS, UK. E-mail: charl.faul@bristol.ac.uk
cCollege of Chemical Engineering, Fuzhou University, Fuzhou 350116, P. R. China
dDepartment of Environmental Science and Engineering, Xi'an Jiaotong University, Xi'an 710049, P. R. China
First published on 2nd September 2020
Here we expand our recently reported Bristol–Xi'an Jiaotong (BXJ) approach using simple salts to fine-tune the porosity of conjugated microporous materials synthesized by various reaction approaches, including Buchwald–Hartwig (BH), Sonogashira–Hagihara, oxidative coupling and Suzuki cross-coupling. The surface area and the porosity of the produced conjugated microporous polyanilines (CMPAs) acquired from the non-salt-added BH coupling are optimized by the addition of inorganic salts. BXJ-salt addition provides a facile route to radically improve the BET surface area from 28 to 901 m2 g−1 for PTAPA and from 723 m2 g−1 to 1378 m2 g−1 for PAPA in a controllable manner. In addition, the surface area shows a gradual decrease with an increase in the ionic radius of salts. We furthermore show high compatibility of this approach in the synthesis of typical CMPs, further increasing the surface area from 886 to 1148 m2 g−1, 981 to 1263 m2 g−1, and 35 to 215 m2 g−1 for CMP-1, PTCT and p-PPF, respectively. More importantly, the BXJ approach also allows the broad PSD of the CMPs to be narrowed to the microporous range only, mimicking COFs and MOFs. With the porosity optimized, CO2 uptakes are dramatically improved by >300% from 0.75 mmol g−1 to 2.59 mmol g−1 for PTAPA and from 2.41 mmol g−1 to 2.93 mmol g−1 for PAPA. Careful addressing of Hansen solubility parameters (HSPs) of solvents and resulting polymers through salt addition has the potential to become an important design tool for the preparation of fully tuneable porous materials. We are currently exploring further methods to tune both structure and function in a wide range of organic porous materials.
A wide range of coupling chemistries, such as Sonogashira–Hagihara,12 Yamamoto,18 Suzuki,19 Friedel–Crafts,20 and oxidative coupling,21 have been devoted to construct novel CMPs. Recently, Buchwald–Hartwig (BH) coupling has been applied in CMP design and synthesis, where carbon–nitrogen bonds can be formed in a facile manner using a Pd catalyst and a base.15 A simple route was therefore developed to form N-rich redox-active CMPs, i.e., 3D analogues of the well-known redox-active polymer poly(aniline) (PANi). However, using BH coupling generally resulted in products with low porosity.14,15 Moreover, such materials possessed unexpectedly low micropore volumes and broad pore size distributions (PSDs) when compared, for example, with structurally similar poly(aryleneethynylene)s (PAEs).14,15 To address this unexpected challenge, we have shown in a recent paper22 that the surface area of a model BH-synthesized CMP, polytriphenylamine (PTPA), could be fine-tuned and optimized by the addition of inorganic salts to the reaction mixtures. This approach, termed the Bristol–Xi'an Jiaotong (BXJ) approach, yielded PTPA with a 20 times higher surface area than the standard reaction. The initially broad PSD of PTPA could additionally be tuned by the BXJ approach to a narrow micropore range distribution, closely mimicking that of COFs and MOFs. Our developed approaches therefore present an opportunity to tune surface area and porosity, potentially for a range of amorphous polymers. However, this potentially impactful methodology has only been applied in one specific instance in our first published study,22 and its general applicability to create a design tool for wider application remains to be fully explored.
Thus, we describe here a series of BXJ-assisted conjugated microporous polyanilines (CMPAs) synthesized by BH coupling chemistry.23,24 We explored different linkers with longer length or with more polymerization nodes (i.e., A3 + B3, as depicted in Scheme 1) compared to that used in PTPA to fully confirm the generality of our BXJ approach in the synthesis of amorphous CMPs using BH coupling. Additionally, application of the BXJ approach to other typical coupling reactions, including Sonogashira–Hagihara, Suzuki and oxidative coupling, were studied to further optimize the porosities of these typical model materials (i.e.,CMP-1, p-PPF and PTCT).
Fig. 1 FTIR spectra of PTAPA: (a and b), before and after tuning by BXJ-Na salts; and PAPA: (c and d), before and after tuning by BXJ-NO3 salts. |
Interestingly, the addition of salts during polymerization did not change the molecular structure (as shown in FTIR and SS 13C CP/MAS NMR), but led to macroscopic gelation of PTAPA during polymerization (rather than the usual precipitation when no salt was added), as was also observed in PTPA synthesis.22 These changes were also reflected in the SEM micrographs of these materials (shown in Fig. S4†), where the normally particulate-like morphology of CMPAs became almost foam-like after the addition of salts. These changes were early indicators of the positive effect the BXJ salts had on the physical properties of CMPAs produced by BH coupling.
We further investigated this influence of salts on the PTPA structures and, potentially, the porosity through detailed BET surface area analysis. PTAPA, with a longer linker than PTPA, showed a very low BET surface area of 28 m2 g−1 under standard BH cross-coupling conditions (as shown Table 1). A remarkable improvement of surface area of more than 30 times to 901 m2 g−1 was obtained with the aid of NaF. The surface area was then systematically decreased to 256 m2 g−1 by increasing the anion size of the employed sodium salts. This tuneable trend was also reflected in the change of total pore volume, with an almost 10 times increase from the initial value of 0.078 cm3 g−1 to 0.81 cm3 g−1 with the use of NaF, and gradual reduction to 0.21 cm3 g−1 (when NaI was applied). This delicate and fine control over the physical properties shows the suitability of the BXJ approach for overall structural design and optimization. General applicability was also confirmed with our BXJ nitrate salts on fine-tuning the surface area of PTAPA as shown in Table 1. A surface area of 652 m2 g−1 was effectively reached by LiNO3, and then tuned to 556 m2 g−1 by adding cations of increasing size. Note that these results were highly reproducible, with selected syntheses repeated three times (see Experimental section). However, unlike the surface area, there was no obvious trend in tuning the pore volume of PTAPA when applying salts with increasing cation radius. This outcome demonstrates the formation and control of pores with different volumes are more complex, especially with nitrate salts, as they could not be as finely controlled by the salt as the surface area. It is noteworthy that similar trends were also observed for the control of PTPA. See Table S1† for full details.
Ion radius (Å) | Surface areaa (m2 g−1) | Total pore volumeb (cm3 g−1) | Micropore volumec (cm3 g−1) | Ultramicropore volumed (cm3 g−1) | CO2 uptake at 273 K, 1 atm (mmol g−1) | Ref. | |
---|---|---|---|---|---|---|---|
a Surface area calculated from the N2 adsorption isotherm using the Brunauer–Emmett–Teller method. b The total pore volume calculated from the desorption branch of the N2 isotherm using the NL-DFT method. c The micropore volume calculated from the desorption branch of the N2 isotherm using the NL-DFT method for micropore (r < 2 nm) volume. d The ultramicropore volume calculated from the desorption branch of the N2 isotherm using the NL-DFT method for ultramicropore (r < 0.7 nm) volume. | |||||||
Control | — | 28 | 0.078 | 0.025 | 0 | 0.75 | This work |
NaF | 1.33 | 901 | 0.81 | 0.44 | 0.21 | 1.89 | This work |
NaCl | 1.84 | 873 | 0.83 | 0.68 | 0.20 | 2.57 | This work |
NaBr | 1.95 | 803 | 0.63 | 0.54 | 0.24 | 2.59 | This work |
NaI | 2.20 | 256 | 0.21 | 0.20 | 0.085 | 0.95 | This work |
LiNO3 | 0.76 | 652 | 0.45 | 0.43 | 0.18 | 2.10 | This work |
NaNO3 | 1.02 | 640 | 0.33 | 0.33 | 0.19 | 1.91 | This work |
KNO3 | 1.33 | 601 | 0.42 | 0.41 | 0.23 | 2.59 | This work |
Ba(NO3)2 | 1.42 | 556 | 0.42 | 0.39 | 0.14 | 1.72 | This work |
0.33 mmol Na2SO4 | 2.35 | 130 | 0.059 | 0.059 | 0.053 | 2.38 | This work |
0.50 mmol Na2SO4 | 2.35 | 180 | 0.038 | 0.038 | 0.0095 | 2.61 | This work |
0.75 mmol Na2SO4 | 2.35 | 249 | 0.15 | 0.14 | 0.088 | 2.75 | This work |
1.00 mmol Na2SO4 | 2.35 | 371 | 0.23 | 0.23 | 0.14 | 2.10 | This work |
1.50 mmol Na2SO4 | 2.35 | 150 | 0.18 | 0.18 | 0.11 | 1.87 | This work |
2.00 mmol Na2SO4 | 2.35 | 131 | 0.11 | 0.11 | 0.065 | 0.81 | This work |
Toluene/0.75 mmol Na2SO4 | 2.35 | 162 | 0.13 | 0.10 | 0.075 | 0.74 | This work |
THF/0.75 mmol Na2SO4 | 2.35 | 249 | 0.23 | 0.23 | 0.14 | 2.75 | This work |
Dioxane/0.75 mmol Na2SO4 | 2.35 | 418 | 0.22 | 0.22 | 0.16 | 2.65 | This work |
CMP-1 | — | 834 | 0.53 | 0.33 | N.A. | N.A. | 25 |
COF-1 | — | 711 | 0.32 | N.A. | N.A. | N.A. | 26 |
CTF-1 | — | 791 | 0.40 | N.A. | N.A. | N.A. | 27 |
MOF-1 | — | 516 | 0.29 | N.A. | N.A. | 0.86 | 28 |
In an effort to continue to further validate the applicability of our BXJ approach, we investigated the influence of the BXJ method on the BET surface area of another CMPA: PAPA, with one additional polymerization node in the linker than PTPA (see Scheme 1). Again, the addition of salts during polymerization did not change the molecular structure (as shown in FTIR and SS 13C CP/MAS NMR, Fig. 1 and 2, respectively), but led to macroscopic gelation (as found for the other systems).
Interestingly, an unexpected high surface area of 723 m2 g−1, as shown in Table 2, was acquired before salt tuning, indicating that the chosen reaction conditions were already a very good starting point for our investigations. In addition, earlier studies showed that higher connectivity in monomers often lead to higher surface area.29,30 In order to explore whether these already high values could be tuned, and further control exerted over other physical characteristics, we varied the salts using our BXJ approach. Here a very well-defined trend in the surface area was observed when sodium salts with varying anion radius were applied: the surface area was almost doubled to 1378 m2 g−1 by NaF, and then decreased with increasing anionic radius of the salts. This obtained surface is, to the best of our knowledge, one of the highest surface areas reached for BH-synthesized polymers. Nitrate salts (where the cation radius was varied) also showed regular influence on the surface area of PAPA as shown in Table 2. The initial surface area was increased slightly to 818 m2 g−1 with the decrease of cation radius. However, this influence was much less pronounced for PAPA (compared with that of PTPA and PTAPA).
Ion radius (Å) | Surface areaa (m2 g−1) | Total pore volumeb (cm3 g−1) | Micropore volumec (cm3 g−1) | Ultramicropore volumed (cm3 g−1) | CO2 uptake at 273 K, 1 atm (mmol g−1) | Ref. | |
---|---|---|---|---|---|---|---|
a Surface area calculated from the N2 adsorption isotherm using the Brunauer–Emmett–Teller method. b The total pore volume calculated from the desorption branch of the N2 isotherm using the NL-DFT method. c The micropore volume calculated from the desorption branch of the N2 isotherm using the NL-DFT method for micropore (r < 2 nm) volume. d The ultramicropore volume calculated from the desorption branch of the N2 isotherm using the NL-DFT method for ultramicropore (r < 0.7 nm) volume. | |||||||
Control | — | 723 | 0.58 | 0.47 | 0.23 | 2.41 | This work |
NaF | 1.33 | 1378 | 0.88 | 0.47 | 0.47 | 2.51 | This work |
NaCl | 1.84 | 777 | 0.45 | 0.21 | 0.21 | 2.28 | This work |
NaBr | 1.95 | 742 | 0.45 | 0.27 | 0.27 | 2.29 | This work |
NaI | 2.20 | 741 | 0.47 | 0.22 | 0.22 | 1.82 | This work |
LiNO3 | 0.76 | 818 | 0.49 | 0.29 | 0.29 | 2.88 | This work |
NaNO3 | 1.02 | 783 | 0.43 | 0.25 | 0.25 | 2.45 | This work |
KNO3 | 1.33 | 765 | 0.40 | 0.20 | 0.20 | 1.63 | This work |
Ba(NO3)2 | 1.42 | 724 | 0.36 | 0.20 | 0.20 | 2.07 | This work |
0.33 mmol Na2SO4 | 2.35 | 817 | 0.57 | 0.50 | 0.24 | 2.77 | This work |
0.50 mmol Na2SO4 | 2.35 | 830 | 0.47 | 0.46 | 0.26 | 2.58 | This work |
0.75 mmol Na2SO4 | 2.35 | 780 | 0.61 | 0.53 | 0.26 | 2.83 | This work |
1.00 mmol Na2SO4 | 2.35 | 690 | 0.39 | 0.39 | 0.22 | 1.70 | This work |
1.50 mmol Na2SO4 | 2.35 | 595 | 0.35 | 0.35 | 0.26 | 2.93 | This work |
THF/0.5 mmol Na2SO4 | 2.35 | 830 | 0.47 | 0.46 | 0.26 | 2.58 | This work |
Toluene/0.5 mmol Na2SO4 | 2.35 | 108 | 0.24 | 0.042 | 0.036 | 1.16 | This work |
Dioxane without salts | — | 838 | 0.53 | 0.50 | 0.27 | 2.90 | This work |
Dioxane/0.5 mmol Na2SO4 | 2.35 | 614 | 0.46 | 0.39 | 0.18 | 1.56 | This work |
CMP-1 | — | 834 | 0.53 | 0.33 | N.A. | N.A. | 25 |
COF-1 | — | 711 | 0.32 | N.A. | N.A. | N.A. | 26 |
CTF-1 | — | 791 | 0.40 | N.A. | N.A. | N.A. | 27 |
MOF-1 | — | 516 | 0.29 | N.A. | N.A. | 0.86 | 28 |
To gain insight into the influence of BXJ salts on the microporosity of these CMPAs, optimized dosages, as determined from the study of salt dosage influence on the porosity as shown in Tables 1, 2 and Fig. S6,† of various sodium salts (NaF, NaCl, NaBr, NaI) and nitrate salts (LiNO3, NaNO3, KNO3, Ba(NO3)2) were now employed in the BXJ synthesis of PTAPA and PAPA. Specifically, salt concentrations of 0.75 mmol (for PTAPA) or 0.5 mmol (for PAPA) were used and the porosities of polymers acquired were investigated by N2 adsorption and desorption isotherms, as shown in Fig. 3. For PTAPA a typical Type II isotherm was observed, as shown in Fig. 3(a) and (c), while a very broad PSD was obtained when using the standard reaction without salt as control (as shown in Fig. 3(b) and (d)). Such a broad PSD most likely results from interparticular voids or interparticulate porosity rather than from the intrinsic porosity.13,15 Type I isotherms were acquired for BXJ-PTAPA after adding both types of salt (Fig. 3(a) and (c)), with the resulting PSD becoming very narrow, showing only micropores. This result indicates that large numbers of micropores of defined size were produced by adding salts to the reaction mixture.12,31 As for PAPA, even though its isotherm showed intrinsic Type-I shape before salt tuning, the PSD was significantly narrowed after salt addition. As such, tuning the pores of amorphous CMPAs to resemble COF- or MOF-like distributions is therefore within reach with our BXJ approach (see the relevant XRD diffractograms in Fig. S7,† and transmission electron microscope (TEM) images in Fig. S8 and S9†).
To obtain a fundamental understanding of the influences of our BXJ approach on these CMPAs, we further explored the theory of Hansen solubility parameters (HSPs)32 in the context of our synthetic approach. According to the HSP theory (see detailed guide in Section S2 in ESI†), solvents are designated as “good solvents” for a polymer when the difference in their total solubility parameter |δT| < 1 (where |δT| = |δT, solvent − δT, polymer|). Solvents with a δT difference of 1 < |δT| < 3 would be classified as “intermediate solvent”, and would still be able to perform well during a polymerization. When the |δT| > 3, solvents are indicated as “poor solvents” for the resulting polymer and is not suitable for polymer synthesis.33,34 As a general guide, the early phase separation of our polymer networks (and the resulting large average diameter pores and low BET surface areas) could result from weak matching of δT, solvent with that of the growing polymer. Solvents with matching HSPs and good compatibilities (difference in |δT| < 1) with the (growing) polymer networks would, in contrast, contribute to a much later-stage phase separation, yielding polymers with uniform PSD and rich micropores (see our recent publication and the ESI† for detailed discussion).22,33,34 With this background in mind, we calculated35 the HSPs of PAPA and PTAPA, with a detailed step-by-step methodology and results presented in the ESI† (Section S3, results shown in Fig. S10, Tables S2 and S3†). The estimated total solubility parameter (δT) of PTAPA and PAPA, listed alongside that of PTPA and literature values of solvents, are summarized in Table 3.
Results in Table 3 clearly shows the reason for the BXJ tuning performance on different CMPAs. For PTAPA, the |δT| between THF and PTAPA was 3.9, indicating THF is a poor solvent for PTAPA synthesis. This explains why a low surface area of 28 m2 g−1 was acquired in THF without any salt addition. However, salts contribute to the permanent dipole interactions (δP) and the hydrogen-bonding interactions (δH) of the solvent, resulting in a decrease of |δT| and increase of compatibility of the solvent for polymer during the polymerization. A high surface area was therefore acquired for PTAPA after exploiting the BXJ approach. Additionally, the electronegativity of the ions decreases with the increase of salt ionic radius. As such, ions with larger radii should have less influence on the δP and δH components of the solvent (by adjusting the hydrogen bonding and polarity of the solvents), thus resulting in a less effective adjustment (and therefore matching) of the HSPs. The surface area of PTAPA could be therefore fine-tuned by the radii of the salts, as shown in Table 1. However, for PAPA, an intrinsic low δT was estimated, and the |δT| between THF and PAPA was only 1.4, suggesting that THF was an intermediate solvent suitable for PAPA to polymerize. This observation is consistent with the surface area data shown in Table 2, in that no or much less salts were needed to tune the solvent to be compatible for PAPA polymerization; a high surface area of 723 m2 g−1 could be reached by simply using THF, but then increased dramatically to almost double (1378 m2 g−1) by salt tuning.
For the case of PTAPA, a much larger δT of 23.4 was obtained, compared with the values of 22.6 and 20.9 for PTPA and PAPA, respectively. This obtained value validated the observations that significantly higher salt concentrations (1.00 mmol) were needed to acquire matching solvent quality for PTAPA, as observed in dosage-dependent results shown in Tables 1 and 2. These observations also explain the fact that it was easier to overtune the solvent for PAPA (with the lowest δT) compared with PTPA and PTAPA. These results further support the applicability of our BXJ approach and HSP mechanism for fine-tuning the surface area of CMPAs in a quantitative manner.
With this principle fully established, we expanded our investigations and switched solvents to dioxane to prepare PAPA (δT, dioxane = 20.5, and thus a very close match of (|δT| = 0.4) to the calculated value for PAPA). As shown in Fig. S11(d–f),†Tables 1 and 2, an increased surface area of 838 m2 g−1 was achieved by dioxane even when using the standard BH reaction without salts (compared with a value of 723 m2 g−1 acquired with THF as solvent under such conditions). Exploring properties with salt additions of 0.5 mmol Na2SO4 led to overtuning the HSPs of dioxane, and consequently to a decrease in the surface area of PAPA from 838 m2 g−1 to 614 m2 g−1.
We further expanded our BXJ approach to other typical CMP-forming reactions, including Sonogashira–Hagihara,12 oxidative,21 and Suzuki36 couplings, to attempt tuning and improving the surface area of the prototypical examples from such reactions. As a starting point we added 0.5 mmol of NaF (based on our experience for CMPA optimization as outlined above) to these reaction mixtures. Results, and comparisons to published data are shown in Fig. 4 and Table 4, clearly demonstrating the successful application of the BXJ approach in these reactions too. The surface area of poly(aryleneethynylene)s (CMP-1) acquired from Sonogashira–Hagihara reaction was increased from 886 to 1148 m2 g−1. In the case of PTCT, produced by oxidative coupling, the surface area increased from 981 to 1263 m2 g−1, while for p-PPF, synthesized by Suzuki coupling, a significant increase in surface area from 35 m2 g−1 to 215 m2 g−1 was observed, despite the fact that inorganic salts, such as CuI, FeCl3 and K2CO3 were already utilized as catalysts or bases in the original reactions. More interestingly, the PSDs of these products were generally narrowed, as shown in Fig. 4(b), (e) and (h). Improved values for micropore volumes were also observed: 0.58 to 0.80 cm3 g−1 (CMP-1), from 0.60 to 0.86 cm3 g−1 (PTCPT), and from 0.081 to 0.14 cm3 g−1 (p-PPF), respectively.
Surface areaa (m2 g−1) | Total pore volumeb (cm3 g−1) | Micropore volumec (cm3 g−1) | Ultramicropore volumed (cm3 g−1) | CO2 uptake at 273 K, 1 atm (mmol g−1) | Ref. | |
---|---|---|---|---|---|---|
a Porosity data calculated from N2 adsorption and desorption were unavailable from the original paper published by authors.35 The authors acquired surface area from CO2 sorption isotherm due to the low porosity, and the data was not suitable for comparison. b The total pore volume calculated from the desorption branch of the N2 isotherm using the NL-DFT method. c The micropore volume calculated from the desorption branch of the N2 isotherm using the NL-DFT method for micropore (r < 2 nm) volume. d The ultramicropore volume calculated from the desorption branch of the N2 isotherm using the NL-DFT method for ultramicropore (r < 0.7 nm) volume. b c d | ||||||
CMP-1 (published) | 834 | 0.47 | 0.33 | N. A. | 2.05 | 12 |
CMA-1 (replication, without BXJ-NaF) | 886 | 0.58 | 0.44 | 0.31 | 1.10 | This work |
CMA-1 (with BXJ-NaF) | 1148 | 0.80 | 0.56 | 0.38 | 1.62 | This work |
PTCT (published) | 895 | 1.17 | 1.04 | N. A. | N. A. | 21 |
PTCT (replication, without BXJ-NaF) | 981 | 0.60 | 0.52 | 0.32 | 1.94 | This work |
PTCT (with BXJ-NaF) | 1263 | 0.86 | 0.73 | 0.46 | 2.53 | This work |
p-PPF (published) | N. A. | N. A. | N. A. | N. A. | N. A. | 36 |
p-PPF (replication, without BXJ-NaF) | 35 | 0.081 | 0.014 | 0 | 0.55 | This work |
p-PPF (with BXJ-NaF) | 215 | 0.14 | 0.065 | 0 | 0.79 | This work |
These results further reinforced the adaptability of our BXJ approach to facilitate the creation of well-defined micropores and high surface area for polymers acquired by non-BH reaction routes. It is noteworthy that the porosity was enhanced by BXJ salts in a similar way as for CMPAs by influencing the phase separation and the polymerization degrees, as evidenced in the very different SEM morphologies obtained for these model networks (Fig. S12†) as well as the enhanced thermal stability (Fig. S13†) before and after salt addition. As shown for CMPAs, the molecular structures of these samples were not changed by our BXJ method either, and confirmed by FTIR study (Fig. 1, S14 and S15†).39
As the materials synthesized through the BXJ approach showed very promising microporosity, the influence on the functionality (i.e., these materials' ability to adsorb CO2 at 273 K) was investigated. Data are shown in Fig. 5, with the capacity at 1 atm summarized in Tables 1 and 2. Significant increases in CO2 sequestration capacities were acquired with our BXJ approach. CO2 uptake was dramatically improved by >300% for PTAPA from 0.75 mmol g−1 to 2.59 mmol g−1; a small enhancement from 2.41 mmol g−1 to 2.93 mmol g−1 was observed for PAPA. The influence was also clearly observed for the polymers produced by non-BH reactions, as shown in Table 4, where a maximum improvement of 47% in CO2 capacity was achieved for CMP-1.
Fig. 5 CO2 adsorption isotherm at 273 K of PTAPA (a and b), PAPA (c and d), and CMP-1, PTCT & p-PPF (e) before and after tuning by BXJ salts. |
However, unlike the surface area, there was no obvious trend for the CO2 uptake ability when increasing the ionic radius of anions or cations in the applied salts. The CO2 uptake shown above for PTAPA and PAPA samples seems to be unrelated to other porosity parameters such as total pore volume, micropore volume and ultramicropore volume. These observations further support the conclusion that the CO2 adsorption of such porous systems is related to a number of factors, not only surface area.37,38 By comparing the CO2 uptake ability with other polymers in Table S4,† our CMPAs, powered by the BXJ approach, exhibit very attractive CO2 sequestration capabilities, owing to the combination of their rich micropores, high surface area and significant N content.
Footnote |
† Electronic supplementary information (ESI) available. See DOI: 10.1039/d0ta05563h |
This journal is © The Royal Society of Chemistry 2020 |