Damiano
Cattaneo
a,
Stewart J.
Warrender
*a,
Morven J.
Duncan
a,
Richard
Castledine
b,
Nigel
Parkinson
b,
Ian
Haley
c and
Russell E.
Morris
a
aSchool of Chemistry, University of St Andrews, North Haugh, St Andrews KY16 9ST, UK. E-mail: sjw9@st-andrews.ac.uk
bFine Industries Ltd, Seal Sands, Middlesbrough, TS2 1UB, UK
cMettler-Toledo Ltd, 64 Boston Rd, Beaumont Leys, Leicester, LE4 1AW, UK
First published on 11th November 2015
The applicability of water-based reflux and room temperature synthesis processes for the production of CPO-27 MOFs, suitable for NO delivery applications, is investigated. NO adsorption, storage and release performance of products obtained under reflux conditions are comparable to those of equivalent samples synthesised from traditional solvothermal methods at small scale. Products obtained from room temperature processes show lower NO release capability, although the quantities that are released are still more than adequate for biomedical applications. Results also reveal differences for the first time in NO uptake, storage and release depending on whether Zn, Ni or Mg is employed. The results indicate that while the crystallinity of CPO-27(Zn) and CPO-27(Mg) is not affected by moving to lower temperature methods, the crystallinity of CPO-27(Ni) is reduced. Particle morphology and size is also affected. The low temperature processes are successfully demonstrated at 20 L and 100 L scale and the main problems encountered during scale-up are outlined. The 100 L scale is in itself an appropriate production scale for some niche biomedical products. Indeed, results indicate that this synthesis approach is suitable for commercial production of MOFs for this application field. We also confirm that BET surface area from nitrogen adsorption at 77 K is not a good indicator for successful adsorption of NO.
NO is an important messenger molecule in our body; it controls blood platelet adhesion, blood pressure and cell proliferation.7 This colourless free radical gas has been studied for in vitro and in vivo antibacterial, wound healing and antithrombotic applications,8,9 for which the ability to deliver precise and controlled doses is highly desirable. We are therefore interested in developing MOFs for use in biological and biomedical applications firstly because of their ability to release safe yet biologically active levels of NO, and secondly because of their potential to help deliver the gas exactly where and when it is required. The biologically active amount of nitric oxide required depends on the targeted application. For example, anti-thrombosis applications require only very small amounts (pmol s−1 cm−2 flux),9 while antibacterial applications may require an order of magnitude more flux.
CPO-27(Ni) has shown great promise as an NO delivery agent.6 Due to its porous nature and coordinatively unsaturated metal sites (CUS), this material exhibits high capacity and stable storage coupled with controllable and reversible release. Traditional procedures for the synthesis of CPO-27(Ni) and its compositional analogues (including CPO-27(Mg) and CPO-27(Zn)) are based on solvothermal methods employing solvents such as dimethylformamide and tetrahydrofuran, at high temperatures over extended time periods (up to 3 days). Table 1 summarises typical conditions used in these solvothermal preparations. Lower temperature procedures have been developed, but still with a dependence on organic solvents such as dimethylformamide.10
Metal | Solvents | Reaction temperature and duration | Solvent exchange method | Activation conditions | N2 adsorption 77 K (m2 g−1) | Ref. |
---|---|---|---|---|---|---|
a Not reported. | ||||||
Ni | DMF/ethanol/H2O | 373 K/24 h | MeOH (2 days × 4) | 523 K 5 h | 1070 | 11 |
THF/H2O | 383 K/3 days | — | 473 K 19 h | 1218 | 12 and 13 | |
383 K 1 h | ||||||
Mg | DMF/ethanol/H2O | 398 K/20 h | MeOH (2 days × 4) | 523 K 5 h | 1495 | 11 |
N-Methylpyrrolidone/H2O | 393 K/24 h | MeOH (7 days × 7) | 513 K 48 h | 1542 | 12 | |
393 K 1 h | ||||||
THF/NaOH/H2O | 383 K/3 days | MeOH (14 days) | 523 K 17 h | 877 | 14 | |
H2O (4 days) | ||||||
Zn | DMF/propanol/H2O | 373 K/20 h | MeOH (2 days × 2) | 543 K 16 h | 816 | 15 |
DMF/H2O | 373 K/20 h | MeOH (6 days × 3) | 543 K | 783 | 16 | |
THF/NaOH/H2O | 383 K/3 days | 17 |
In order to permit storage of gases and other guest species, solvent molecules must be removed from the MOF in a process known as activation. This process, which renders the high surface area and pore volume accessible, and generates CUSs, is typically achieved through heat treatment. However, the pores of products from traditional synthesis methods can be occupied by solvent molecules that cannot be easily removed by this method. Furthermore, some solvents form very strong adducts with metal sites within the framework making it difficult to create CUSs by heating at temperatures below the thermal decomposition of the MOF. In these circumstances solvent exchange processes are required to introduce lower boiling and less strongly coordinating solvent molecules to permit activation at lower temperatures.11,12,18 For example, the MOFs prepared by Caskey et al. (see Table 1) are synthesised in DMF and are then solvent exchanged four times over two days in methanol to attain high gas adsorption capacities.11 Similarly, magnesium CPO-27 MOF prepared using a mixture of THF and water requires solvent exchange in methanol over numerous days.14 Currently the only structure reported that does not require solvent exchange is CPO-27(Ni) prepared using a mixture of THF and water.12,13 It is noted that the activation conditions for each material reported in Table 1 involve temperatures (after solvent exchange) higher than 473 K, under dynamic vacuum.
It is evident from these representative examples that traditional synthesis procedures for these potentially industrially important materials are not particularly environmentally friendly or favourable for larger scale production, given the length of time involved, multiple steps, harmful solvents and high temperature (energy) requirements.
In recent years, we and other groups have shown that CPO-27(Zn) and (Ni) can be obtained from simple water-based reactions operated at room temperature or under reflux.19–21 The development that enabled the move away from organic solvents was the conversion of the organic linker (in this case dihydroxyterephthalic acid) from its protonated (and water insoluble) form to its Na salt – either by first isolating the salt prior to use in the MOF synthesis19 or in a single step process in which the linker is dissolved in aqueous NaOH19–21 and used as a solution (but without the additional use of organic solvents employed in previous literature reported methods14). It has been claimed that this move away from solvothermal processes will facilitate the larger scale production of MOFs due to the simplicity of the reaction and required equipment, as well as the more environmentally friendly and less energy intensive nature of the new process. We also speculate that the use of a water-rich synthesis medium will generate products that do not require solvent exchange prior to activation in order to permit gas adsorption and storage.
In this contribution, we investigate the applicability of this approach in producing CPO-27 MOFs for NO storage and release – namely CPO-27(Zn), (Ni) and (Mg), and compare for the first time the NO adsorption, storage and delivery performance of these three isotypes. We also show that such methods do indeed lend themselves well to larger scale production and herein report the development process undertaken to enable scaling up of the method to 20 L and 100 L scales.
Throughout the following text, products are identified and named based on their synthesis method using the following nomenclature – Solv = prepared solvothermally, RF = prepared under reflux, RT = prepared at room temperature, 2S = prepared in a two-step process, 1S = prepared in a one step process. For example, 2SRF = material prepared under reflux conditions using a two-step procedure.
The release of NO was measured using a Sievers NOA 280i chemiluminescence nitric oxide analyser. Samples were transferred to a chamber that is connected to the analyser and through which flows humid nitrogen gas (humidity controlled at 11% RH). The humid gas triggers the release of NO and carries it to the analyser. The amount of nitric oxide released is measured using the chemiluminescence reaction between nitric oxide and ozone (O3):
The emission from the excited nitrogen dioxide (hν) is detected using a red-sensitive photomultiplier detector. The level of NO present in the carrier gas is recorded (in ppm or ppb) each second until data collection is stopped. Measurements were stopped once NO levels had dropped to an arbitrary value of 20 ppb (a value nearing the limit of the instrument resolution). Data were transformed from ppb and ppm to mmol g−1 and finally molecules per unit cell. Summation of the data produced a plot of total NO release over time. Note that the time taken to reach 20 ppb can vary between samples and is a further performance metric.
Adsorption, storage and release data are presented below as molecules of NO per MOF unit cell (instead of the more commonly used mmol g−1) to enable fair comparison between materials of different composition. The data are presented in the more conventional units of mmol g−1 of MOF in ESI.†
The research data supporting this publication can be accessed at http://dx.doi.org/10.17630/85aa840e-aaf0-4c57-90b7-cb30df6076e7
PXRD analysis of the products (Fig. 2) confirms that each possesses the CPO-27 structure and that they are of single phase, however CPO-27(Ni) prepared at low temperature is of significantly lower crystallinity compared to its reflux and solvothermal counterparts. The use of room temperature conditions did not, however, adversely affect CPO-27(Zn), which exhibits very good crystallinity when synthesised under these conditions.
![]() | ||
Fig. 2 PXRD patterns of (a) reference CPO-27(Mg),14 (b) Solv-CPO-27(Mg), (c) 2SRF-CPO-27(Mg), (d) Solv-CPO-27(Zn), (e) 2SRF-CPO-27(Zn), (f) 2SRT-CPO-27(Zn), (g) Solv-CPO-27(Ni), (h) 2SRF CPO-27(Ni) and (i) 2SRT-CPO-27(Ni). |
Examination of the products from two-step processes by SEM (Fig. 3) reveals notable differences in crystal size and morphology depending on the metal employed and whether room temperature, reflux or solvothermal conditions are used. When prepared solvothermally, CPO-27(Mg) exhibits blocky rod-shaped crystals that appear to grow together in floret-like arrangements; however when prepared under reflux conditions the material exhibits discrete crystals of uniform size. CPO-27(Zn) forms needle-shaped crystals and exhibits a reduction in crystal size when moving to lower temperature, and a tendency to form as floret-like intergrowths under room temperature conditions. In contrast, CPO-27(Ni) presents particles of much smaller granulation and no discernable morphology, regardless of synthesis temperature, in line with previously reported observations.22 Further alterations in the morphology and surface quality of CPO-27(Zn) crystals are observed when moving to a one-step process and when conducting the synthesis at different scales. This behaviour and its potential consequence are discussed later.
A notable difference between materials produced via the different methods is the variation in BET-measured surface areas (ESI Table 1†). The measured surface areas are generally lower than those reported in the literature for similar materials, although wide variation was reported by Dietzel et al. depending on the way in which the MOFs are treated.14 The lower values reported herein may be due to the fact that the samples were not handled and stored under inert conditions. This has been reported to be important particularly for CPO-27(Mg),23 although we note that a measurement of over 1000 m2 g−1 was still recorded for 2SRF-CPO-27(Mg). The lower and variable measurements may therefore be due to the synthesis method. However, as will be discussed later, lower BET surface area values do not necessarily correlate with poorer NO adsorption and release.
It is widely accepted that in order to achieve optimum gas adsorption in MOFs they must be activated (often by heating) to remove adsorbed solvent and guest species. It is common practice to exchange the adsorbed solvent, where appropriate, with a lower boiling or more labile one prior to attempting activation. Gravimetric analyses showing NO uptake and storage for activated Solv-CPO-27(Zn) and (Mg) with and without solvent exchange treatment are shown in Fig. 4 (ESI Fig. 1†) (solvent exchange is not necessary for Solv-CPO-27(Ni)).
It can be observed from the data that solvent exchange prior to activation does indeed result in higher NO uptake and storage by solvothermally prepared CPO-27(Zn) and (Mg), confirming the need for this step in order to maximise performance for these materials. Therefore, to set the most stringent benchmark for the reflux- and room temperature-prepared materials, NO adsorption and release data for these samples are compared in subsequent charts to data from the equivalent solvent exchanged solvothermal products. We postulated that materials synthesised via water-based reflux and lower temperature methods would not require solvent exchange and would only require activation. These products were therefore not solvent exchanged prior to activation and NO analysis. Neither were they exhaustively washed, for example in methanol as reported elsewhere,20 prior to use. If successful without such post treatment, the manufacturing time would be significantly reduced.
The temperature of activation was identified by TGA (ESI Fig. 2†), which, although suggests differences in stability at high temperature, indicates a temperature window ranging from 393 K to 523 K for all samples where the frameworks are dehydrated and stable. The temperature of activation was set at 423 K (under vacuum) – much lower than the previously reported activation temperature for these materials, see Table 1. On dehydration, there was a change in colour from yellow to pale yellow for CPO-27(Mg) and (Zn), and mustard colour for CPO-27(Ni) as a result of changing metal coordination and the formation of the CUSs. Exposure to NO gas resulted in an immediate further colour change to darker yellow-green (which is more evident in CPO-27(Mg) and (Zn) samples) indicating the formation of a metal-NO adduct. It is the strength of this adduct that partly determines the storage and release properties of NO from these types of materials.6 The NO is released by exposure to a moist atmosphere at room temperature, i.e. exchange of NO for water with regeneration of the starting material.
Gravimetric analyses of NO adsorption and desorption (storage) by products prepared under reflux are compared to those of equivalent solvent exchanged, solvothermally prepared products in Fig. 5 (ESI Fig. 3†). Data are currently unavailable for products prepared at room temperature. The data clearly illustrate that CPO-27(Zn) and (Mg) prepared from reflux methods, and not solvent exchanged prior to activation, show equal performance to their solvent exchanged, solvothermally prepared counterparts. This is despite the noticeable differences in surface area observed between these samples (ESI Table 1†), perhaps indicating that surface area measured by nitrogen adsorption is not necessarily a reliable indicator of good NO adsorption and storage capacity. Apparent low surface area measured by nitrogen adsorption may be due to incomplete removal of tightly bound solvent molecules from the internal surface. However, it may also be a result of surface effects blocking access to nitrogen. It is possible that such effects are overcome when using a more strongly coordinating gas (i.e. NO) and by conducting the adsorption at higher temperature.
The data also confirm our view that a solvent exchange step would be unnecessary for these products. Differences in performance are, however, observed between the different compositions suggesting a metal-dependent response. Such a phenomenon has been reported in other adsorption studies, for example the adsorption of CO211 and H2
24 by CPO-27 MOFs of different compositions.
Activated Solv-CPO-27(Ni) adsorbs ∼20 molecules of NO per unit cell (Fig. 5, ESI Fig. 3†). The desorption isotherm indicates a loss of ∼3 molecules per unit cell of physisorbed gas from the porous network resulting in a stored capacity of ∼17 molecules per unit cell (maximum theoretical value is 18 molecules per unit cell). In contrast, after activation, both Solv- and 2SRF-CPO-27(Mg) adsorb a total of only ∼5 molecules of NO per unit cell (Fig. 5, ESI Fig. 3†). However, during the reapplication of vacuum, the NO level remains constant, indicating that the quantity of NO adsorbed is equal to that stored. Analysis of activated Solv- and 2SRF-CPO-27(Zn) reveals uptake and storage levels intermediate between those of CPO-27(Mg) and CPO-27(Ni). As observed with CPO-27(Ni), the desorption isotherms for these Zn analogues illustrate loss of NO, giving a storage capacity of ∼10 molecules per unit cell.
From these results alone, it may be concluded that the synthesis method has no effect on the performance of the material. However, differences are revealed when comparing the quantity of stored NO that can be released on exposure to moist atmosphere. Of course it is this property that is most important for biomedical applications requiring controlled NO delivery.
The total NO released over time from Solv-CPO-27(Ni) when exposed to moist atmosphere reaches up to 17 molecules per unit cell over 20 hours (Fig. 6, ESI Fig. 4†), highlighting an almost completely reversible release of the chemisorbed nitric oxide. These data are in good agreement with previously reported values.6 Similar performance is observed from the reflux product although perhaps slightly less of the stored NO is released. In contrast, when the synthesis is conducted at room temperature, the quantity of NO released and the time scale in which it takes place is dramatically reduced. Possible causes of this are discussed later. On exposing Solv- and 2SRF-CPO-27(Mg) to humidity (Fig. 6, ESI Fig. 4†) only ∼0.07 of the 4 molecules of NO stored per unit cell are liberated, suggesting that the stored NO is tightly bound within the framework. Since both CPO-27(Mg) products exhibit the same result, it is probable that the method of synthesis is not responsible for these effects. Rather, we suggest that this material is more difficult to fully dehydrate (in accord with observations published previously by Dietzel et al.14) and that the metal used (magnesium) has a high, non-reversible affinity for NO. We are presently conducting further analysis to ascertain the heats of adsorption and desorption of NO in CPO-27 MOFs. CPO-27(Zn) exhibits intermediate NO release performance between those of its Ni and Mg counterparts. When prepared under reflux (using Na2(dhtp)·2H2O and water) the total level of NO that is released is comparable to that from the solvothermally prepared product, which is approximately 5% of the stored capacity. However, the dose period is much shorter from the reflux product. As observed for CPO-27(Ni) there is a significant reduction in total NO release when the material is prepared at room temperature, although the level released may still be adequate for many biomedical applications (where often only ppb levels of NO are required9,25). Possible causes for these variations are discussed later.
Interestingly, the total amount of NO released from products prepared under reflux conditions was adversely affected when using this one-step approach – reduced from approximately 14 to 11 molecules per unit cell for CPO-27(Ni) and from approximately 0.4 to 0.2 molecules per unit cell for CPO-27(Zn) (Fig. 8, ESI Fig. 5†). However, the performance of Ni-based products prepared at low temperature was actually improved compared to equivalent materials prepared via the two-step process – releasing ∼8 molecules per unit cell. Zn-based products prepared at room temperature performed as well as equivalent materials prepared via the two-step approach, releasing approximately 0.1 molecules per unit cell. These results suggest that the NO release performance may be influenced by different factors depending on the MOF composition. This is discussed in more detail below.
Addition time (h) | Stir out time (h) | Filtration time (min) |
---|---|---|
1.25 | 3.5 | 4 |
1.75 | 3.5 | 3 |
2.25 | 3.5 | 10 |
0.50 | 5.0 | 70 |
By tuning the addition rate and stir-out time it is therefore possible to reduce filtration times and facilitate larger scale production without recourse to more specialised recovery methods. Nevertheless, a compromise must be sought between allowing the reaction to proceed far enough to maximise yield, and preventing it from progressing so far that the population of fine particles becomes too high and prevents efficient recovery. PXRD patterns for products obtained from mid and large-scale syntheses indicate consistent purity and crystallinity (Fig. 7). Approximately 1 kg of material was recovered from the 20 L vessel, operated at three quarters capacity. The entire process from loading the vessel to drying the filter cake was conducted in a single day shift with a resultant yield of 85% ± 5. The total amount of NO released from products obtained at 1 L and 20 L scales are comparable to and possibly slightly higher than that of the small-scale product (Fig. 8, ESI Fig. 5†) with the release period being slightly longer.
However, unlike CPO-27(Ni), the variation in NO release properties observed between CPO-27(Zn) materials prepared under different conditions and scales shows no correlation with BET surface area (ESI Fig. 6†), which is reasonably consistent across all samples. Nor can it be attributed to crystallinity since this appears to be constant across all samples (Fig. 7). It is also unlikely to be linked to particle size and morphology, despite large variations in these properties being observed between products prepared in different ways (ESI Fig. 7†). It is possible that residual sodium acetate present in the products may partially block access to the MOF pores and CUSs; however this effect would be present in all samples and is not expected therefore to cause such a wide variation in performance. Closer inspection of the SEM images of each product suggests that higher NO release performance is obtained from samples with clean and evenly formed surfaces, suggesting that the NO release performance is partly governed by a surface effect, and that controlling the surface characteristics of this product during synthesis may be crucial. These findings perhaps indicate that internal surface area alone (measured by BET) may not always necessarily be a reliable indicator of good NO storage/release performance. Dietzel et al. reported a wide range in surface areas measured by nitrogen adsorption depending on how the MOF was pre-treated.14 In this present study, Solv-CPO-27(Mg) and 2SRF-CPO-27(Mg) show very different BET surface area measurements (despite being treated equally), yet their NO release (and adsorption) performance are very similar.
At present, gravimetric adsorption/storage data is unavailable for one-step and low temperature samples therefore it is unclear whether the reduction in NO release associated with poorer crystallinity/surface area in the case of CPO-27(Ni) and poorer surface quality in the case of CPO-27(Zn) is due to lower adsorption and/or storage, or whether less of the stored NO is releasable. The current limited gravimetric data for Solv- and 2SRF-CPO-27(Zn) and (Ni), combined with their release data, suggest that the latter case cannot be ruled out. Work is on-going to examine these issues.
An interesting conclusion that can also be taken from this research is that the BET surface areas calculated form nitrogen adsorption at 77 K are not good predictors for the adsorption of gases like NO at room temperature. As such BET surface areas are often used as the standard measurement of porosity, but clearly the situation may not be so simple.
Footnote |
† Electronic supplementary information (ESI) available. See DOI: 10.1039/c5dt03955j |
This journal is © The Royal Society of Chemistry 2016 |