For the first time the anionic polymerization of 1,3-butadiene (Bd) is successfully transferred from semi-batch into a continuous microfluidic setup with comparable product properties. The molecular weight distribution described by the polydispersity index (PDI) is commonly used as a key criterion for product quality. The steady state and the local resolution of a continuous setup provide the opportunity to investigate the progress of the PDI during anionic polymerization. In this work, the influence of kinetics (statistics) and fluid dynamics (FD) on the PDI of the product is investigated. Therefore a dedicated setup was designed and erected to keep Bd in the liquid phase and provide a pulsation free constant liquid flow. With optimized parameter settings, a separation of initiation and propagation is obtained and the intrinsic kinetics of propagation are determined. To explain the experimental results, an ideal plug flow and an ideal laminar flow model are applied and compared to computational fluid dynamics (CFD) simulations. Finally, it is concluded which FD and statistical contributions lead to the very low PDI of 1.04 found in the experiments.
Within the framework of the FP7 project CoPIRIDE, funded by the EU, novel process operations have developed in order to enable significant process intensification. High-throughput devices allow a compact, modular process design, so that the whole process can be installed inside a standard container. This concept provides a faster response to the market demands and allows shipping of the containers to places where educts are cheap and available, or the products required .
The often used multipurpose batch reactors allow a high number of different chemical reactions, but they are not optimized for a special chemistry and their handling provokes accidents . Thus, stirred tank reactors are not feasible for fast exothermic reactions . Microfluidic reactors are characterized by their enhanced heat and mass transfer rates, which is useful when researching an exothermic reaction . Several working groups, e.g., Bally et al.  or Commenge et al.  have examined the advantages and the potential of microfluidic devices for highly exothermic polymerization reactions. Due to their nearly isothermal behavior and small inner dimensions, hotspots can be avoided and a fast mixing is assured. In order to control molecular weights and to gain low polydispersities, the devices have to be designed with optimum diameter and length of the channels .
For process intensification, the bottlenecks of conventional processes have to be identified and new types of reactions have to be investigated to make them suitable for novel process windows (NPW) [8–10]. NPW have four chemical intensification paths and two process intensification paths, as given by Hessel et al. . Following the first track, a high-pressure and hightemperature approach is followed, which is best realized by combining a cold micromixer and a hot capillary reactor. Moreover, and contrary to intuition, the absence of radial mixing and thus, an ideal parabolic flow profile with full segregation of the streamlines, leads to very good performance, i.e., low polydispersity index (PDI) of the polymer produced – an effect reported by Cortese et al. for the first time . The immediately high viscosity in the capillary reactor suppresses any radial diffusion and corresponding (monomer) mass transfer. Despite correspondingly very large velocity gradients and thus residence times, each moving segment within such a microreactor has ideal reaction conditions, as there is no interference from the neighboring segment. Such a counterintuitive finding marks an NPW in the sense of process simplification.
Especially the living anionic polymerization (LAP) provides the possibility to design tailor-made polymers [13, 14] with a well-defined molecular weight and more  or less  complex molecule architecture. As monomers, commonly vinylic and aprotic molecules like styrene, isoprene, 1,3butadiene (Bd) and others can be used. Until now, many groups have investigated the LAP and thus the effects of solvent polarity , initiators , ligands , and temperature  are well known. In the anionic polymerization of Bd as a monomer, the first addition of one monomer unit to the initiator, here n-butyllithium (BuLi), is the initial step, see Figure 1. It is usually much faster than the following addition of further monomers (propagation) due to the slightly higher stability of the 1,3-π-allylic complex [21, 22].
Bd can be inserted in the 1,2- or 1,4-position. The product specification of the polybutadiene often requires a certain amount of vinyl groups, because they influence the properties of the polymer, e.g., the viscosity. The fraction of m/(m+n) within the whole chain quantifies the vinyl content. LAPs of Bd in pure tetrahydrofuran (THF) lead to a very high fraction of vinyl groups, because THF acts as a ligand which coordinates on the cation and thus influences the degree of delocalization of the negative charge. Thus, the ratio of ligand to initiator (L/I) strongly influences the charge distribution of the 1,3-π-allylic complex and whether the consecutive addition of the next monomer occurs on C1 (1,4-addition) or on C3 (1,2-addition) . With cyclohexane (CHx) as the solvent and a certain amount of the ligand THF, the vinyl content can be adjusted.
Furthermore a small amount of THF is activating the initiator BuLi during the initiation step. Even a small amount of THF (L/I of at least 1) avoids oligomerization and accelerates the initiation, where BuLi is tended to oligomerization in nonpolar solvents e.g., pure CHx . By using THF not only the accessibility of the monomers to the active center is increased. It avoids dimerization or higherfold oligomerization  of at least two living ends that are insulating the active centers  (Figure 2). In pure CHx, propagation is slow, but by addition of THF to the reaction solution the polymerization is finished within a few min . Due to the high heat removal rates microstructured or millistructured devices are suitable for handling this fast and exothermic reaction .
An important indicator for product quality is the PDI that is a calculated factor given by the ratio of weight and number average molar mass of a polymer sample. The PDI is a degree of conformity of the molecular weights within a polymer sample, see Eq. (1), where Mw is the mass average molar weight and Mn the number average molar weight. Mi is the molar weight of the ith species, Ni is the number of molecules of species Mi in the sample. This means that in a sample, where all chains have the same molecular weight, the PDI is theoretically 1.0 .
And depending on the molar fraction
In reality, propagation underlies a statistical addition of monomers to the chain ends. Hence, product distribution for polymerization degree P [see Eq. (9)] follows the Poisson distribution (PD) according to Eq. (3), where
LAP-made polybutadienes should have a PDI below 1.1 to fulfill the demand of high quality and to be suitable for specialty applications .
Wilms et al. , Wurm et al. , and Ziegenbalg et al.  showed that a very fast anionic polymerization of styrene in pure THF can be performed in a micromixing device with molecular weights up to 70 kg mol-1 and polydispersities lower than 1.1. Furthermore, Nagaki et al.  reported on a flow rate dependency on the molecular weight distribution and that too low flow rates will lead to a broadening. Iida et al.  described that every kind of disruption of the flow regime in the propagation channel has to be avoided to obtain a low-PDI polystyrene or isoprene. In best cases, they obtained polystyrenes with PDI of 1.09  and 1.07 , respectively.
In a former publication of Cortese et al. , computational fluid dynamics (CFD) calculations explained the dependency of PDI on microfluidics in a microchannel, with styrene as the monomer. Based on several assumptions it should be possible to obtain polystyrenes with a molar mass of up to 30,000 g mol-1 and a PDI of 1.03, if the mean residence time is high enough.
In this work, experimental results for an anionic polymerization of Bd in capillaries are compared with ideal reactor models and the CFD model of Cortese et al. .
2 Materials and methods
The setups described in literature for performing an LAP with styrene or isoprene as the monomer [29–33] are not feasible for Bd, which is gaseous at atmospheric pressure and room temperature. Figure 3 shows the flow scheme of the setup that allows a pulsation-free liquid phase polymerization. The combination of a pressurized reservoir and a mass flow controller (MFC, Bronckhorst CoriFlow mini, Wagner Mess- und Regeltechnik GmbH Offenbach/Main, Germany) has the advantage to keep and feed Bd in the liquid phase without any pulsation compared to a mechanical pump. Also, there is no possibility that cavitation occurs during the intake step.
The initiator solution and monomer solution are combined and mixed in a T-junction, with an inner diameter of 1.2 mm. In comparison to special micromixing devices like slit-interdigital or caterpillar micromixers, the T-junction proved to be less prone to clogging. The mixing device is tempered to avoid hotspots in the early state of polymerization. It is assumed that an engulfment mixing  is fast enough for an ideally premixed feed entering into the propagation capillary. Through a transfer pipe (di=0.7 mm), the reaction solution flows in the tempered propagation capillary whose dimensions (length, diameter) can be varied. An attached backpressure regulator (BPR, 7 or 17 bar) minimizes outgassing inside the propagation capillary and keeps the educts in a liquid phase. At the outlet of the capillary, the polymer is quenched with methanol and collected under methanol in a vial.
For determining the mixing quality, a setup without a propagation capillary was chosen. The BPR is directly attached to the tempered T-junction and its outlet leads immediately into a vial under methanol.
Bd (Westfalen AG, Münster, Germany, 2.5, stabilized with 1,4-tert-butylcatechol) is destabilized and dried by a column of BASF (Ludwigshafen, Germany) activated alumina F-200 and a molecular sieve 4 Å. The monomer reservoir is charged with 33.9 wt% of Bd in cyclohexane (Acros Organics, Thermo Fisher Scientific, Geel, Belgium, 99.5%, extra dry, over a molecular sieve 4 Å, AcroSeal), chilled to -10°C and pressurized by 40 bar of nitrogen (Westfalen AG, 5.0). The initiator solution is prepared in a second reservoir with a 2:1 mixture of THF (Acros Organics, 99.8%, extra dry) and BuLi (Acros Organics, 1.6 m solution in n-hexane) and was consumed within 2 h, due to its high decomposition rates [36, 37]. Within 2 h, no significant decomposition of BuLi was observed, since a steady state operation also related to product specification was found. Solvents and BuLi are used without further purification. THF and CHx are checked for traces of water by Karl-Fischer-Coulometry (Metrohm 831 KF Coulometer with diaphragm, Deutsche METROHM GmbH & Co. KG, Filderstadt, Germany) and are allowed to have a maximum of 15 ppm water.
The polymer samples are analyzed by gel permeation chromatography (GPC). As GPC-device, an Agilent 1260 (Agilent Technologies, Böblingen, Germany) Infinity Series with degasser, isocratic pump, autosampler, tempered column department, and refraction index (RI) detector is used. THF (Fisher Scientific, high pressure liquid chromatography grade) is used as an eluent, and the column is one single PLgel mixed-D, with a particle size of 5 µm. The GPC is calibrated by PSSbdfkit [1,4-polybutadienes molar mass (Mw)=861–169,000 g mol1, by PSS Polymer Standards Service GmbH, Mainz, Germany]. With the help of the WinGPC-PlugIn for Agilent ChemStation, Mw and PDIs are determined.
By head-space gas chromatography (GC), the mixing quality was determined with an HP 5860 Series II, equipped with a 50 m PONA column, hydrogen as a carrier gas, and a split of 1:400. The initial temperature is 35°C held for 3 min, with an additional heating up to 60°C during the following 8 min. The signal areas are calculated by the ChemStation software. The ratios of the integrals of Bd to CHx signals and butane to n-hexane signals are manually calculated.
2.4 Experimental procedure
2.4.1 Investigation of mixing quality
For investigation of the mixing quality, the setup without a propagation capillary is used. The temperature of the mixing device is set to Tmix=-10°C, 0°C, and 25°C, with the mass flow rates
2.4.2 Variation of capillary length
For polymerization, the temperature of the mixing device is Tmix=25°C and the capillary temperature is Tcap=45°C. Mass flow rates of
|Monomer solution||Initiator solution|
|Content||33.9 wt% Bd in CHx||10 ml n-BuLi 1.6 M in 20 ml THF|
|Mass flow rates||60 g h-1||15 g h-1|
|Density ρ||725 kg m-3||810 kg m-3|
Bd, 1,3-butadiene; BuLi, n-butyllithium; CHx, cyclohexane; THF, tetrahydrofuran.
2.4.3 Variation of reaction temperature
Generally the same procedure was performed as for the variation of capillary length, but only the 4 ml capillary was used and the temperature Tcap is varied in steps of 15°C, from 30°C to 90°C. To keep the Bd in the liquid phase, the outlet pressure was increased to pBPR=17 bar. The work-up of the polymer followed the steps described above.
2.5.1 Kinetic modeling
LAP is a strictly linear addition of the monomers. Chain transfer reactions and untimely terminations of the propagation do not occur. Eq. (4) describes the propagation, where Pi is the i-th polymer species and M the monomer. The reaction rate r obeys a first order kinetics, both related to the monomer and the polymer chain and is calculated according to Eq. (5), where cM is the concentration of the monomer, cPi the concentration of the growing polymer chain with chain lengths of i monomers and kP the propagation rate constant.
Thus, the concentration of active sites cΣP- is constant and equates to the starting concentration of the initiator cI,0 under inert conditions [Eq. (6)]. Furthermore, the initiation step (kI) is much faster than the following propagation (kP) [Eq. (7)], and it is assumed that initiation only takes place in the mixing device. Thus, the initiation step is negligible in the polymerization kinetics. In most cases, the consumption of the monomer can be described with a pseudo-first order kinetics following Eq. (8), where cM,t is the time-related concentration of residual monomer, cM,0 the starting concentration, and τ the residence time.
Due to the difficulty of determining the residual Bd, cM,t can be calculated from the polymer formed. cM,0 is known, the average molar mass Mw of the polymer sample is a result of the GPC analysis, so the percentage of the consumed monomer is calculated with the help of the mean P, that gives the number of the monomer units in a polymer chain:
The ratio of the P of the sample, Psample, and the theoretical polymerization degree Pmax corresponding to full conversion of the monomer, gives the conversion of the monomer XM [Eq. (10)].
The propagation rate constant kP can be calculated according to Eq. (11):
with Eq. (12).
2.5.2 Reactor modeling
In the first two simulations, an ideal plug flow reactor (PFR) and an ideal laminar flow reactor (LFR) are assumed. It sets the focus on a simple PDI modeling for anionic polymerization in tubular reactors. The most simplified model is to assume the tubular reactor as a single PFR. There is no interaction between wall and fluid, thus, there is no difference in individual residence times. The molar mass distribution of a polymerization in a PFR must be equal to the PD.
In the second simulation, the LFR with a parabolic flow profile is assumed, which causes a broad residence time distribution. With the simplification that a mean flow velocity can be attributed to every shell, each shell is modeled by a PFR.
These two simulations are calculated with some simplifying general assumptions: during the polymerization density, diffusivity, and viscosity will not change and the reaction rate constant kP is independent from the degree of conversion or chain length. Furthermore, initiation is completed and the propagation starts homogeneously at the inlet of the capillary (z=0). Finally, the polymerization solution behaves as a Newtonian fluid. Influence of discretization is step size tested.
The third simulation based on CFD examines the fluid dynamic (FD) impact on the PDI. It sets its focus on the properties of the reaction solution that are changing with the chain length of the polybutadienes. At the outlet, the PDI is calculated from the sum of all obtained molecular weights Mw.
126.96.36.199 Ideal PFR model
A single ideal PFR provides a simplified model of the polymerization in a capillary and supplies information on statistical PDI development, excluding FD effects, but including a full cross-mixing. Therefore, a first order kinetic is assumed following the reaction scheme described by Eq. (4). The reaction rate rP is calculated by Eq. (5), with kP being the rate constant.
Eq. (13) is the mass balance of the ideal PFR which describes the formation and consumption of the polymer with chain length i along the capillary. The mass balance is solved with the help of MATLAB ODE-solver (MathWorks, Ismaning, Germany). The concentrations of the species Pi give the molecular weight distribution at the corresponding position along the axis and the mean P. The PDI is calculated by Eq. (1).
This simulation is compared to the PD that is given by Eq. (3) for the molar fraction
188.8.131.52 Ideal LFR model
For the ideal LFR, the parabolic flow profile is divided into shells. Each shell is modeled as a single PFR, assuming that there is no mass transport by diffusion between the streamlines (full segregation), see Figure 4. At the outlet of the capillary, all polymers obtained in each shell are summed up and give the average PDI.
The flow velocities v(rcap) of the parabolic profile are calculated by Eq. (14), where vavg is the average flow velocity, rcap the radial position in the capillary, and Rcap the entire radius of the capillary.
The tube is divided into N shells having a width Δrcap according to Eq. (15).
The local mean flow velocity in the shell, v(rx), is calculated as follows:
Each shell is modeled as an ideal PFR. At axial reactor position z, the mass balance according to Eq. (13) is solved for each shell. The flow rates of each polymer species Pi, the local mean molar masses, and the PDI are calculated with Eqs. (17)–(20). This finally leads to the mean PDI of all shells by summing over the cross section to get the total flow rate of each species [Eq. (20)].
184.108.40.206 CFD model
In contrast to the simplified PFR models, the CFD model includes changes in fluid properties, like viscosity, diffusivity, thermal conductivity, and heat capacity correlating to the molecular weight Mw of the polymer chain. The dependences of the viscosity and the diffusivity of the reaction solution on the molecular weights of polybutadienes in CHx as the solvent are shown in Figure 5. The intrinsic viscosity is calculated by the Han equation  as a function of molecular weight of the polymer with the dataset of Mello et al. . The diffusion coefficient is correlated to the solution viscosity by means of the Hayduck-Cheng equation  using as a starting data-set the values reported by Chalykh et al. .
The methodology for the calculations is described in more detail by Cortese et al. . Like the other simulations, the CFD calculations presume an ideally premixed feed at the inlet and an isothermal reaction. To avoid a virtual clogging in the capillary, a slip flow at the wall is introduced. It is assumed that the polymer is not diffusing. The calculations are performed with COMSOL (Comsol Inc., Los Angeles, CA, USA), 220.127.116.11. Due to the high computing effort, the capillary was scaled to a shorter one, but checked for comparability to the capillary with a length of 3.28 m.
3 Results and discussion
3.1 Premixing and initiation
In all the reactor models used in this work, an ideally premixed feed with completed initiation entering the propagation capillary is assumed. Therefore, the setup without the propagation capillary is used to gain insight into the state of the polymerization before entering the propagation capillary. The amount of unconverted BuLi cannot be analyzed directly, but the protonated product n-butane is separable from to Bd on a nonpolar PONA column by GC. However, it is difficult to get a concrete quantitative conclusion from an analysis of a pressurized gas/liquid product system, due to the complex gas/liquid equilibria after expansion. Furthermore, the untimely decomposed BuLi also forms butane, which is carried through the setup (ABu,x). For a semi-quantitative investigation, the relative head-space GC method, where the ratios of signal-areas of butane to hexane and butadiene to CHx, respectively, are examined, is sufficient. The conversion of BuLi XBuLi is given by Eq. (21), with
For Bd, the conversion is calculated by Eq. (22), with the signal areas ABd,tot of Bd in the headspace of the feed reservoir and ABd,t after reaction with BuLi in the mixer.
The conversion for three different residence times is measured at three temperatures (Tmix=-10°C, 0°C, and 25°C). Figure 6 shows no further increase of conversion exceeding 0°C. Even a residence time of τ=18 s is not leading to significantly higher conversion of BuLi. Thus, it can be assured that initiation is completed when entering the capillary. The deviations of the expected full conversions at high temperatures and residence times are caused by the semi-quantitative approach due to the headspace measurements.
For the conversion of XBd, it is shown in Figure 7 that up to a residence time of τ=12 s at Tmix=25°C, only a small amount of XBd<10% is converted, or has been added to the initiator. With a higher residence time (τ=18 s), a higher amount of Bd is converted.
It can be concluded that a mixing temperature of 25°C and mass flow rates of
3.2 Intrinsic kinetics
For the anionic polymerization of Bd initiated by BuLi in a solvent mixture of CHx and THF, the activation energy EA and the pre-exponential factor kP,inf can be determined by variation of the temperature. The experiments are carried out in the described setup, with a capillary of Vcap=4 ml (lcap=1.66 m, di=1.75 mm) and a BPR with pBPR=17 bar. With a total mass flow rate of
|pBPR=7 bar Mw(g mol-1)||pBPR=17 bar Mw(g mol-1)|
Mw, weight average molar mass; pBPR, pressure at the outlet of the capillary; Tcap, wall temperature of the capillary.
Figure 8 shows the obtained molar masses Mw of the samples for each reaction temperature. For the calculation of every particular propagation rate kP, an ideal PFR is assumed and Eq. (11) is applied. The average molar mass of each run is taken.
|Tcap(°C)||Mw,av(g mol-1)||P (-)||XBd(-)||kP(l mol min-1)|
kP, propagation rate constant; Mw,av, weight average molar mass; P, polymerization degree; Tcap, wall temperature of the capillary; XBd, conversion of Bd.
According to the Arrhenius equation [Eq. (23)], the activation energy is EA=22.0 kJ mol-1 and the pre-exponential factor is kP,inf=94,100 l mol min-1.
In the following, kP=25 l mol-1 min-1 corresponding to 45°C is used for the simulations.
3.3 Determining the PDI
3.3.1 Ideal PFR model
Figure 9 shows the distributions of molar fractions of polymers with the mean polymerization degrees P=5, 20, 40, and 80, the so-called PD following Eq. (3) and the simulation based on Eqs. (5) and (13), with the rate constant determined beforehand. The resulting curves are matching exactly. Thus, under ideal and simplified conditions, the PDI in a PFR is calculable only by the molar fraction combining Eqs. (2) and (3).
Usually PDIs at lower polymerization degrees are higher, due to the fact that one more or less monomer unit effects are more noticeable at lower than at higher polymerization degrees. With Eq. (13) and with the determined rate constant, the resulting molar weights of the i-th polybutadiene species are calculated. The PDIs are determined according to Eq. (2) and are plotted versus the normalized reactor length, see Figure 10. The normalization is necessary for model comparison, because the simulation uses the capillary geometry and reaction parameters of the experiments. It is shown that the lowest obtainable PDI is about 1.015 for a polymerization degree of about 250 at the outlet and falls below 1.02 after about 15% of the reactor length.
3.3.2 Ideal LFR model
This model gives a slower decrease of the PDI along the propagation capillary compared to the single PFR, where the reactor length is normalized on the length of the capillary (3.28 m) (Figure 11). The PDI course falls below 1.02 after 60% of the entire capillary length and the PDI decreases consecutively to 1.015 at the outlet.
3.3.3 CFD model
The results of the 3D CFD simulations using the overall kinetics r=kP cI,0 cM are shown in Figure 12. Due to the very time-consuming calculations, only two 3D results were created. For the CFD results, PDIs are higher than in the ideal PFR or LFR models. It shows that PDI is dependent on FD as well as statistical effects (PD). The statistics influence the most to the final PDI, while FD alone contributes, adding 0.015 to the total PDI in a continuous set-up (Table 4).
|τ (s)||kP(l mol-1min-1)||XBd (%)||Mw (g mol-1)||PDICFD||PDICFD+PD|
CFD, computational fluid dynamics; kP, propagation rate constant; Mw, weight average molar mass; PD, Poisson distribution; PDI, polydispersity index; τ, residence time; XBd, conversion of Bd.
In the calculations it is shown that a segregated flow regime is prevailing. The diffusion coefficient DAB is in the order of 10-11m2 s-1 in the blue area in Figure 13; the Fourier number (Fo) suggests with values of about Fo=0.01, that the streamlines are segregated. According to Einstein’s equation, see Eq. (24), the mean diffusion length for Bd <Δl> is about 10 µm at the outlet of the capillary. Compared to the inner diameter of the propagation capillary with 1.75 mm the diffusion is negligible low. Thus the streamlines are practically independent.
However, the high diffusion fluxes at the walls, described by the red area in Figure 14, should give the reason for increased PDIs of the CFD results. Although the streamlines can be assumed as almost segregated in consideration of diffusion constants, the monomer concentration gradients increase towards the wall. This effect is not described by the ideal segregated flow in the LFR model. Elevated monomer diffusion fluxes from the center to the wall affect a change on the ratio of the monomer to the living polymer chain ends or rather initiator [M/I, with Eq. (6)] in the ideally premixed volume units. The consecutive fading into blue describes the slow-down of the diffusion and diffusion fluxes and therefore the ratios of the monomer to the polymer anion are frozen on the streamlines. This leads to deviations in the polymerization degrees and a higher PDI.
3.4 Comparison with experimental results
For investigation of the development of PDI during the polymerization, the results of the experimental variation of the capillary length are shown in Figure 15. Only the two lowest PDIs of obtained polybutadienes of each capillary length are chosen. They mark the lower limit. Other values are neglected, due to the high sensitivity of PDI on every deviation from the steady state.
Obviously, there is an experimental limit with at a PDI of about 1.04 for molecular weights up to 16,500 g mol-1. Compared to the results in the ideal PFR or the ideal LFR, the experimental PDIs are still too high. As expected, the PFR describes the PD. The LFR model gives PDIs which are slightly closer to the experimental data, but nevertheless still significantly lower by an absolute value of about 0.02. Compared to the PFR model, the LFR model gives higher PDI values due to the segregated flow. For very high residence times, the courses of the ideal PFR and LFR models approach to the same boundary value, the PD, which also confirms the work of Cortese et al. , where segregated flow and a high residence time lead to very low PDI. The PFR and the LFR approaches give the right tendency, but do not reflect the real behavior. Considering only the statistical effects, the lower limit of PDI is about 1.02. The experimental results must contain an additional influencing value due to a not fully segregated flow. Moreover, CFD simulations suggest that a further value of 0.015 has to be added to the statistical PDI, due to the described effects of higher monomer concentration gradients towards the wall and the consecutive freezing of the disarranged monomer to initiator ratios. As boundary conditions neither full cross-diffusion (PFR) nor fully segregated flow (LFR) are fulfilled. Thus, the sum of FD effects and the statistics lead to realistic PDI values that can be observed in experimental results in a continuous microfluidic setup.
The comparison of the obtained polymers and PDIs with the results of other groups shows that there are advantages of the used setup. Avoiding pulsation and the combination of a chilled mixing device and a heated capillary outperforms the hitherto existing setups (Table 5). A separation of mixing and further propagation in a segregated flow causes a decrease of the PDI.
|Ref.||Setup/mixer||Monomer||Solvent||VM/I(ml min-1)||TR(°C)||Mw(g mol-1)||Lowest PDI|
CHx, cyclohexane; Mw, weight average molar mass; PDI, polydispersity index; TR, reaction temperature; THF, tetrahydrofuran; SIMM: Slit Interdigital Micromixer (IMM Mainz GmbH, Mainz, Germany); Cap., Capillary; T-junc., T-junction.
With the help of experiments and simulations, it can be shown that the resulting PDI of a polymer made by LAP consists of FD and a statistical part. The FD contribution increases the PDI only by a value of about 0.015. More dominating is the statistical effect that obeys the PD and limits the PDI to 1.02 for anionic polymerizations up to a molar weight of 16,500 g mol-1 in a microfluidic system with the investigated chemistry and setup. With the help of CFD modeling, it is shown that neither an infinite dispersion across the cross section (ideal PFR model) nor a fully segregated flow regime (ideal LFR model) exists. High diffusion fluxes near the wall at the inlet of the propagation capillary effect changes in the ratio of monomer to initiator. This leads to inhomogeneous polymerization degrees and therefore a broader distribution of the molecular weights of the polymer. Nevertheless, in summary, a PDI of 1.035 marks a realistic value that can definitely be achieved. Thus, a continuous microfluidic flow reactor can provide a low-PDI polymer that is comparable to polymers that are made in a batch reactor.
The combination of a pulsation free dosing and the use of a chilled mixing device and a heated capillary can provide low-PDI polybutadienes and outperforms the existing setups. This gives the opportunity for process intensification by a transfer from a semi-batch operation into a continuous microfluidic reactor, while maintaining the product quality.
Integrated signal area at GC measurements
- C, mol l -1
- D AB,m 2 s -1
- d, m
Fourier number (Fo=DABτ l-2)
Counter variable, regarded species
- k I,l mol -1 min -1
Initiation rate constant
- k P ,l mol -1 min -1
Propagation rate constant
- k P,inf, l mol -1 min -1
- l, M
Ligand to initiator ratio (THF/BuLi)
- m, G
Mass flow rate
- M, g mol -1
- Mn, g mol -1
Number average molar mass
- Mw, g mol -1
Weight average molar mass
Monomer to initiator ratio (Bd/BuLi=Bd/P-)
- n, Mol
Molar amount of matter
Molar flow rate
Discretization step in axial direction
- N i
Number amount of species i
- pBPR, Bar
Pressure at the outlet of the capillary
Poly dispersion index (Mn/Mw)
- r, m
- r, mol l -1 min -1
- R, J mol -1 K -1
Gas constant (8.3141 J mol-1 K-1)
- Tcap, °C
Wall temperature of the capillary
- Tmix, °C
Temperature of the mixing device
- T R, °C
- t, S
- v, m s -1
Volume flow rate
- V R, cm 3
Coordinate in radial direction
SymbolsSymbol, Unit Description
- η, Pa s
- [ η], Pa s
- ρ, kg m 3
- τ, s
Greek symbolsSymbol, Unit Description
computational fluid dynamics
gel permeation chromatography
high pressure liquid chromatography
living anionic polymerization
laminar flow reactor
- P -
plug flow reactor
The research leading to these results has received funding from the European Community’s Seventh Framework Programme [FP7/2007–2013] under grant agreement no. CP-IP 228853-2.
 Schnyder A. „Chemische Prozesse in Mehrproduktanlagen sicher fahren“, Jubiläumspublikation 15 Jahre Schnyder Sicherheit in der Chemie AG, 2002, 1–50. Search in Google Scholar
 Hugo P, Lopez F. Chem. Ing. Tech. 2009, 81, 145–152. Search in Google Scholar
 Jähnisch K, Hessel V, Löwe H, Baerns M. Angew. Chem. Int. Ed. 2004, 43, 406–446. Search in Google Scholar
 Bally F, Serra CA, Hessel V, Hadziioannou G. Chem. Eng. Sci. 2011, 66, 1449–1462. Search in Google Scholar
 Commenge JM, Falk L, Corriou JP, Matlosz M. Chem. Eng. Technol. 2005, 28, 446–458. Search in Google Scholar
 Tonhauser C, Natalello A, Löwe H, Frey H. Macromolecules 2012, 45, 9551–9570. Search in Google Scholar
 Hessel V, Cortese B, de Croon MHJM. Chem. Eng. Sci. 2011, 66, 1426–1448. Search in Google Scholar
 Hessel V, Chem. Eng. Technol. 2009, 32, 1655–1681. Search in Google Scholar
 Lomel S, Falk L, Commenge JM, Houzelot L. Chem. Eng. Res. Des. 2006, 84, 363–369. Search in Google Scholar
 Hessel V, Kralisch D, Kockmann N, Noël T, Wang Q. ChemSusChem 2013, 6, 746–791. Search in Google Scholar
 Cortese B, Noël T, de Croon MHJM, Schulze S, Klemm E, Hessel V. Macromol. React. Eng. 2012, 6, 507–515. Search in Google Scholar
 Szwarc M. Nature 1956, 178, 1168–1169. Search in Google Scholar
 Quirk, RP. In Encyclopedia of Polymer Science and Technology, John Wiley & Sons, Inc.: New York, 2002. Search in Google Scholar
 Hajichristidis N, Pitsikalis M, Pispas S, Iatrou H. Chem. Rev. 2001, 101, 3747–3792. Search in Google Scholar
 Halasa AF, Lohr DF, Hall JE. J. Polym. Sci., PCE Ed. 1981, 19, 1357–1360 Search in Google Scholar
 Essel A, Salle R, Golé J, Pham QT. J. Polym. Sci. PCE 1975, 13, 1847–1853. Search in Google Scholar
 Hsieh HL. J. Polym Sci, Pt. A 1966, 3, 163–172. Search in Google Scholar
 Antkowiak TA, Oberster AE, Halasa AF, Tate DP. J. Polym. Sci. Pt. A Vol. 1972, 10, 1319–1334. Search in Google Scholar
 Uraneck CA. J. Polym. Sci. Pt. A 1971, 9, 2273–2281. Search in Google Scholar
 Morton M, Sanderson RD, Sakata R. Polym. Lett. 1971, 9, 61–70. Search in Google Scholar
 Morton M, Fetters LJ. Rubber Chem. Technol. 1975, 48, 359–409. Search in Google Scholar
 Halasa AF, Schulz DN, Tate DP, Mochel VD. Adv. Organomet. Chem. 1980, 18, 55–97. Search in Google Scholar
 Bywater S, Worsfold DJ. J. Organomet. Chem. 1967, 10, 1–5. Search in Google Scholar
 Worsfold DJ, Bywater S, Macromol. 1972, 4, 393–397. Search in Google Scholar
 Bywater S, Worsfold DJ, Hollingsworth G. Macromol. 1972, 4, 389–393. Search in Google Scholar
 Chang CC, Miller Jr. JW, Schorr GR. J. Appl. Polym. Sci. 1990, 39, 2395–2417. Search in Google Scholar
 Young RJ, Lovell PA, Introduction to Polymers, 3rd ed., CRC Press, Taylor and Francis Group: Boca Raton, 2011. Search in Google Scholar
 Baskaran D, Müller A. Prog. Polym. Sci. 2007, 32, 173–219. Search in Google Scholar
 Wilms D, Klos J, Frey H. Macromol. Chem. Phys. 2008, 209, 343–356. Search in Google Scholar
 Wurm F, Wilms D, Klos J, Löwe H, Frey H. Macromol. Chem. Phys. 2008, 209, 1106–1114. Search in Google Scholar
 Ziegenbalg D, Kompter C, Schönfeld F, Kralisch D. Green Proc. Synth. 2012, 1, 211–241. Search in Google Scholar
 Nagaki A, Tomida Y, Yoshida J. Macromol. 2008, 17, 6322–6330. Search in Google Scholar
 Iida K, Chastek TQ, Beers KL, Cavicchi KA, Chun J, Fasolka MJ. Lab Chip 2009, 9, 339–350. Search in Google Scholar
 Engler M, Kockmann N, Kiefer T, Woias P. Chem. Eng. J. 2004, 101, 315–322. Search in Google Scholar
 Gilman H, Gaj BJ. J. Org. Chem. 1957, 22, 1165–1168. Search in Google Scholar
 Stanetty P, Koller H, Mihovilovic M. J. Org. Chem. 1992, 57, 6833–6837. Search in Google Scholar
 McCrackin FH. Polymer 1987, 28, 1874–1850. Search in Google Scholar
 Mello IL, Delpech MC, Coutinho FMB, Albino FFM. J. Braz. Chem. Soc. 2006, 17, 194–199. Search in Google Scholar
 Hayduk W, Cheng SC. Chem. Eng. Sci. 1971, 26, 635–646. Search in Google Scholar
 Chalykh AY, Titkova LV, Malkin AY, Dreval VY, Pronin IS. Polym. Sci. USSR 1974, 16, 2134–2144. Search in Google Scholar
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