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Drying of Supported Catalysts: A Comparison of Model Predictions and
Experimental Measurements of Metal Profiles
Xue Liu, Johannes G. Khinast, and Benjamin J. Glasser*,
Department of Chemical and Biochemical Engineering, Rutgers UniVersity, 98 Brett Road, Piscataway,New Jersey 08854, and Institute for Process Engineering, Graz UniVersity of Technology, Inffeldg. 21A,
A-8010 Graz, Austria
Supported metal catalysts are used in many industrial applications. Experiments have shown that drying maysignificantly impact the metal distribution within the support. Therefore we need to have a fundamentalunderstanding of drying. In this work, a theoretical model is established to predict the drying process, and themodel predictions are compared with experimental measurements of a nickel/alumina system. It is found thategg-shell profiles can be enhanced by increasing the drying temperature or the initial metal concentration ifthe metal loading is low. For high metal loadings, nearly uniform profiles are observed after drying. We havealso investigated how breakage of the liquid film inside the pores of the support can affect the metal distributionduring drying. It was found that film-breakage has a significant impact on the metal distribution, and it isimportant to correctly capture film-breakage in the model in order to get good experimental agreement.
1. Introduction
Supported catalysts are used in a variety of industrial
processes, ranging from catalytic converters and the production
of petroleum to the production of new drugs. These catalysts
consist of a porous support, one or more active catalytic
materials deposited on the support, and in some cases a
modifier.1 With respect to the distribution of the active
component in the support, four main categories of metal profiles
can be distinguished, that is, uniform, egg-yolk, egg-shell, and
egg-white profiles.2,3 The choice of the desired metal profile is
determined by the required activity and selectivity, and can be
tailored for specific reactions and/or processes. Although the
development and preparation of supported catalysts have been
investigated for many years, many aspects of the various catalyst
manufacturing steps are still not fully understood, and in industrythe design of catalysts is predominated by trial and error
experiments, which are expensive and time-consuming, and do
not always offer assurances on the final manufacturing results.
The preparation of supported catalysts usually involves three
steps: impregnation, drying, and reduction and calcination.
Experimental work has shown that the metal distribution within
the support is mainly determined by the impregnation and drying
steps.4-9 Therefore, to achieve an optimum metal profile a
fundamental understanding of both impregnation and drying is
crucial. However, most studies on controlling the metal profiles
in catalysts have focused on the impact of the impregnation
step. There are still many questions regarding the impact of
drying that remain unanswered.The effect of drying on the metal distribution and catalyst
properties has been studied experimentally by Wu et al.10,11 who
investigated the impact of various preparation procedures on
the mechanical strength of solid catalysts and showed that drying
has a significant effect on the catalysts mechanical properties.
Santhanam et al.12 examined the nature of the Pd precursors
and the adsorption of Pd complexes during and after drying
with different adsorption strengths. They showed that for strong
adsorption there is no migration of the metal through the pellets
during drying, while for weak adsorption migration does occur,leading to a modified final profile. Li et al.9 studied the Ni
distribution during the preparation of Ni/alumina catalyst pellets
and compared the experiments with simulations. They showed
that the simulation fitted the experimental data well, if the metal
redistribution during drying was considered. Other work has
focused on the characterizations of the physicochemical pro-
cesses that occur during the preparation of supported catalysts
using nuclear magnetic resonance,13-17 and spatially resolved
Raman and UV-visible-NIR spectroscopy.18-20
Computer simulations have also been used to predict the
impregnation and drying of supported catalysts. Theoretical
models describing the impregnation step have been reported in
a number of papers.
6,7,21-23
Because of the complexity of thedrying step, only a few theoretical models have been reported
for drying. However, experiments and simulations have shown
that the drying procedure can significantly affect the metal
profile established during impregnation, if adsorption of the
metal component on the support surface is weak or mode-
rate.12,24-27 Neimark et al.5,28 were among the first to theoreti-
cally study the metal redistribution during drying. They used a
dimensionless number to characterize slow drying and fast
drying regimes, and their theory is in agreement with the
experiments of Komiyama et al.,8 who showed that a very high
drying rate can result in a uniform profile, while a relatively
low drying rate favors an egg-shell profile. More detailed drying
models were formulated by Uemura et al.,29 Lee and Aris,6 and
Lekhal et al.24-26 They considered the effects of the capillaryflow and metal diffusion and simulated the metal migration
during drying. Recently, the sensitivity of the metal distribution
during impregnation and drying with respect to the physical
and processing parameters was examined by Liu et al.27 They
also considered the effect of crystallization in their model, and
showed that metal crystallization has a significant effect on the
generation of egg-shell profiles for relatively high metal
concentrations.
It is of particular interest to compare simulation results and
experimental measurements to validate the theory and determine
the key parameters used to predict the metal distribution during
the preparation of supported catalysts. Most previous studies
* To whom correspondence should be addressed. Tel.: 732- 445-4243. Fax: 732-445-2581. E-mail: bglasser@ rutgers.edu.
Rutgers University. Graz University of Technology.
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only focused on a comparison of theory and experiments for
the impregnation step. A systematic comparison for the drying
step has not been reported as of yet. Thus, the objective of this
paper is to predict the metal distribution during drying and to
compare the simulation results with experimental measurements.
Furthermore, it is of interest to investigate the fundamental
mechanisms occurring during drying, and to study the impact
of the processing parameters and material properties on the final
metal distribution.
2. Model and Experiment Setup
2.1. Model Equations.In the present work, we studied the
drying of a Ni/alumina system, which is widely used in
processes like hydrogenation, hydrodesulfurization, and steam
reforming of hydrocarbons.30,31 During the drying process,
several phenomena are taking place simultaneously: heat transfer
from the hot gas to the wet support, solvent evaporation near
the external surface, solvent convective flow toward the external
surface, and metal diffusion and adsorption inside the support.
An accurate drying model must include all these phenomena.
In this work, we extend the model proposed by Lekhal et
al.24 by considering a cylindrical geometry and the impact of
breakage of the liquid film inside the pores of the support (film-breakage). In our model the following parameters have an
impact on the drying process: the metal diffusion coefficient,
the equilibrium constant of adsorption and desorption, the
intrinsic permeability, the initial metal concentration in the
solvent, the drying temperature, the humidity of the drying air,
and the film-breakage parameters. It is important to note that
although the results presented are chosen for a Ni/alumina
system, the methodology is entirely general. It is not limited to
specific active components and supports.
There are two main assumptions in our model: (1) During
drying the metal concentration in the solution is below its
solubility; therefore, crystallization is not considered. (2) The
equilibrium adsorption constant can be assumed to be a constantduring the drying process. These assumptions have been made
in order to arrive at a model that can simply yet accurately
describe the important physical processes taking place during
drying. Our model can capture convective flow in the gas and
liquid phases, metal convection, diffusion, and adsorption on
the porous support as well as heat transport.
The following equations describe the drying process:
Equations 1 and 2 represent the mass balances of the drying
medium (air) and the solvent (water). Equations 3 and 4represent the mass balances of the metal dissolved in the liquid
and deposited on the support. Equation 5 is the energy balance.
gand lare the volume fractions of the gas and liquid phases,Cg,a (mol/m
3) and Cl,s (mol/m3) are the concentrations of the
drying air and the liquid solvent, respectively.Cl,i(mol/m3) and
Cs,i (mol/kg) are the concentrations of the metal dissolved in
the solvent and adsorbed on the support. Ng,a (mol/(m2 s)) and
Ng,v (mol/(m2 s)) are the fluxes of the air and solvent vapor.
Nl,s (mol/(m2 s)) and Nl,i (mol/(m
2 s)) are the fluxes of the
solvent and the dissolved metal. Fs (kg/m3) is the apparent
density of the porous support.Ri(mol/kg/s) represents the rateof metal adsorption, which is described using a Langmuir
model.32-34
where kads (m3/mol/s) and kdes (s
-1) are the adsorption and
desorption constants of the metal component. Csat (mol/kg)
denotes the metal saturation concentration. In this model we
assume adsorption is not the limiting step. Consequently, the
adsorbed metal is in equilibrium with its dissolved precursor,
and the equilibrium adsorption constant can be calculated as
Keq ) kads/kdes. Although the value of the equilibrium adsorption
constant may change during drying,26
in this work we assumeit to be a constant.hg,i(J/mol) represents the enthalpy of the air
or solvent vapor.hl(J/mol) andhs(J/kg) denote the enthalpy of
the liquid and solid. (J/(m s K)) is the effective thermalconductivity.
Film-breakage is an important phenomenon during drying.
At the beginning of drying, the water phase is continuously
distributed in the support. As evaporation proceeds, isolated
domains are gradually formed in the liquid phase. Finally, the
liquid is only found in the isolated domains. To consider
the effect of film-breakage in our model, a factor R is added to
the flux terms in eqs 2, 3, and 5. Neimark et al.5 showed that
film-breakage is related to the support pore structure and the
water content in the support. Therefore, for a given solid carrier,we assume that the film-breakage factor, R, is a function of the
water volume fraction.
where R1 represents the water volume fraction when film-
breakage starts, and R2 represents the water volume fraction
when the solvent only exists in the isolated domains and the
water flux completely stops. We assume that when the value of
the water volume fraction is between R1 and R2, R linearly
decreases with a decrease in the water volume fraction indicating
that the flux in the liquid phase linearly decreases with a decrease
in the water content.
The gas-phase fluxes Ng,aand Ng,vare assumed to follow the
dusty gas model (DGM),35 which considers the effect of
molecular diffusion, Knudsen diffusion, and viscous flow.
In eq 8Pg(Pa) is the total gas pressure, R (8.314 J/(mol K))is the gas constant, T(K) is the temperature, xg,irepresents the
t(gCg,a) ) -
1
r
r(rNg,a) (1)
t(lCl,s) ) -
1
r
r(RrNl,s + rNg,v) (2)
t(lCl,i) ) -
1
r
r(RrNl,i) - FsRi (3)
t(Cs,i) ) Ri, i ) metal component (4)
t(
i)1
2
gCg,ihg,i + lCl,shl + Fshs) )
- 1
r
r(i)1
2
rNg,ihg,i + RrNl,shl - rT
r) (5)
Ri ) kadsCl,i(Csat - Cs,i) - kdesCs,i, i ) metal component
(6)
R ) 1 when fg R1
R )(R1 - f)
(R1 - R2) when R1 > f> R2
R ) 0 when fe R2
(7)
-Pg
RTxg,i -
xg,i
RT(1 -KKg,effPg
gDKnud)Pg )
j)1j*i
2 xg,jNg,i - xg,iNg,j
Dg,ij+
Ng,i
DKnud(8)
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vapor or air mole fraction in the gas phase, Dg,ij(m2/s) and DKnud
(m2/s) are the effective binary and Knudsen diffusion coefficients
estimated from the kinetic gas theory,36 andKg,effis the intrinsic
permeability of the gas phase, which has the form
Jones37 has shown that eq 9 can describe experimental data
very well. In this work, the water vapor pressure is calculated
using the Antoine equation38 and the Hailwood-Horrobin
equation39 with parameters fitted by Simpson.40 We assume that
the convective flow in the liquid phase follows Darcys law,41
where Kl,eff is the relative permeability of the liquid phase, l(Pa s) is the viscosity of the liquid phase, K (m2) represents
the intrinsic permeability, and Pl (Pa) is the liquid phase
pressure, which is equal to the local gas pressure less the
capillary pressurePc(Pa).41 In the present workPcis described
using the form proposed by Perre et al.,42
where (N/m) represents the surface tension, and Ml,s is themolecular weight of the liquid solvent. The flux of the dissolved
metal is described by the Nernst-Planck equation,43 which takes
into account the effect of convective flow of the solvent
(capillary flow), diffusion due to the metal concentration
gradient, and migration caused by electrical charges. It takes
the form
where Dl,i (m2/s) is the effective diffusion coefficient of the
dissolved metal, Zi is the charge of the metal component, F
(96500 C/mol) is the Faraday constant, and (V) represents
the electrostatic potential. In this work we assume there is no
external current and the electroneutrality condition is satisfied
in the support. The gradient of the electrostatic potential, which
is a function of the number of charges and the concentration
gradient of the charged components, is determined by the no-
current equation:44
wheren is the total number of ionic species in the liquid phase.
The constitutive relations proposed by Jones37 are adopted for
the relative permeability Kl,eff.
The boundary conditions are the zero-flux conditions at the
support center and the Neumann conditions at the support
surface.24,25 The resulting system of nonlinear partial differential
equations is spatially discretized by a finite volume method.45
Then the resulting set of ordinary differential equations is solved
by LIMEX, which is efficient for solving highly stiff differential-algebraic equations.46
2.2. Experiment Setup and Parameter Measurement.The
system studied in this work is a nickel/alumina system. Nickel
nitrate powders (Sigma-Aldrich) were used as metal precursors
and cylindrical-alumina pellets provided by Saint-Gobain wereused as solid carriers. The pellets are 3 mm in diameter and
around 10 mm in length with a void volume fraction of 0.3
cm3/g and a surface area of 200.7 m2/g. The basic experimental
protocol includes the following steps: (1) The solid support is
preheated in an oven at 120 C for 12 h. (2) The dry alumina
supports are immersed in nickel nitrate solutions for impregna-tion. The pH of the solutions is adjusted by adding nitric acid
or NH4OH. To investigate the effect of the metal concentration,
we changed the concentration of the nickel nitrate solutions from
0.01 to 4 M. Usually we hold the impregnation time sufficiently
long such that a uniform profile can be obtained after impregna-
tion, representing an equilibrium state. (3) The catalyst samples
are dried in an oven at a constant temperature. The drying
temperature is varied between 22 and 180 C. (4) Calcination
is carried out at 500C for 2 h. During impregnation and drying,
nickel nitrate gives the catalyst a green color. During calcination,
nickel nitrate becomes nickel oxide, and thus, the catalyst color
changes. The gray or black color of the samples after calcination
is most likely due to some deviation from ideal 1:1 stoichiometry
of the NiO.47
The nickel concentration in the solution is measured using a
UV-visible spectrophotometer at a wavelength of 190 nm. To
obtain the standard curve, seven samples were prepared with
the Ni(NO3)2concentration equaling 0.001, 0.005, 0.01, 0.025,
0.05, 0.075, and 0.1 M. Then the absorbance value of each
sample was measured by the UV-visible apparatus. From
experiments we found that there is a linear relation between
the nickel concentration, CNi and the absorbance value, Auv.
Using a linear regression, we can obtain the equation:
This equation can be used to calculate the nickel concentrationin the solution during impregnation. To investigate the metal
profiles after drying or calcination, we cut the catalyst samples
in half in the radial direction and measured the radial nickel
profile using micro-X-ray fluorescence spectroscopy (micro-
XRF).
To solve our drying model, we need to measure several
parameters.9,32 In our work, a Langmuir equation is used to
describe the adsorption and desorption processes (see eq 6).
Under equilibrium conditions, the rate of the metal adsorption
is equal to the rate of the metal desorption (RM ) 0). Therefore,
eq 6 can be rewritten as
From eq 16 it can be seen that a straight line is obtained
when plotting 1/Ceq versus 1/Cs. Then the values of Csat and
Keqcan be calculated from the line intercept and the slope. Six
samples with Ni(NO3)2concentration equal to 0.01 M, 0.02 M,
0.04 M, 0.06 M, 0.08 M, and 0.1 M were prepared. Each sample
contained 100 mL of Ni(NO3)2 solution and 1 g of alumina
support with the pH equal to 6.5. The value of Cs can be
calculated based on the Ni mass balance in the system, since
the amount of the metal in the solution before impregnation
minus the amount of the metal in the solution after impregnation
equals the amount of the metal adsorbed on the support. From
Figure 1, it can be seen that the amount of metal deposited onthe supports increases rapidly at the beginning of impregnation.
Kg,eff) 1 - 1.11(l ) (9)
Nl,s ) -Cl,sKKl,eff
lPl (10)
Pc ) 1.364 105(
lcl,sMl,s
Fs)
-0.63
(11)
Nl,i ) -Cl,iKKl,eff
l
P - lDl,icl,i - lCl,iZiDl,iF
RTl,
i ) metal component (12)
i)1
n
zi
Nl,i
) 0 (13)
Kl,eff)(l )3
(14)
CNi ) 0.0878Auv (15)
1
Ceq)
1
CsatKeq
1
Cs+
1
Csat(16)
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Then, the adsorption rate decreases due to the increase in the
surface coverage of the active sites. After approximately 3 days
a plateau is reached indicating an equilibrium state, from which
we can obtain the equilibrium metal concentration in the solution
Ceq and the corresponding metal load on the supportCs. Using
eq 16, we obtained Csat ) 0.3 mol/kg and Keq ) 0.2 m3/mol
when plotting 1/Ceq versus 1/Cs.
At the beginning of impregnation, the effect of desorption
can be neglected. Thus, the decrease in the metal concentration
in the solution is mainly due to the accumulation of the metal
adsorbed on the support. Therefore,
where C0 represents the initial metal concentration in the
solution.9,32 When plotting dC0/dtversusC0, a straight line can
be obtained and the value of the kinetic adsorption constant
kadscan be calculated from the slope. To obtainkads, we prepared
five samples with Ni(NO3)2 concentrations equal to 0.01, 0.02,
0.03, 0.04 and 0.05 M, at a pH equal to 6.5. To reduce diffusion
effects during impregnation we ground the pellet supports into
powders. The particle size was between 150 and 250 m. We
used a sieve to remove large particles, and then used water towash out fine particles. The powder supports were dried in the
oven at 120 C for 12 h before being used. For each sample,
the value of the Ni concentration was measured at 10 min
intervals after impregnation started. Then the value of dC0/dt
was calculated. By plotting dC0/dt versus C0, we obtained kads) 6.5 10-5 m3/(mol/s).
The diffusion coefficient of nickel nitrate in water was taken
from the work of Takahashi et al.48 as D ) 6 10-10 m2/s.
The permeability is based on the support pore size distribution.
The pore size distribution was measured by Saint-Gobain using
a mercury volume test. The porosity of the support is around
0.67 with 80% small pores (average 7 nm) and 20% large pores
(average 500 nm). Then the permeability of the support can becalculated using the modified Ergun equation.49
Using eq 18, we obtained a permeability ofK) 5 10-16 m2.
In general, the base case conditions used in our simulations
are pH ) 6.5,Csat ) 0.3 mol/kg, Keq ) 0.2 m3/mol, kads ) 6.5
10-5 m3/(mol/s), D ) 6 10-10 m2/s, K) 5 10-16 m2,
and 30% relative humidity. The initial metal concentration in
the solution C0 was varied from 0.04 to 4 M, and the drying
temperature Tbulkwas varied from 22 to 180 C. A uniform initial
metal distribution was utilized indicating that impregnationreached an equilibrium state.
3. Results and Discussion
3.1. Experimental Results. Typical experimental drying
results are shown in Figure 2 for Tbulk) 60 C. In Figure 2a
the water volume fraction can be seen to decrease with timeuntil a plateau is reached. In Figure 2b the drying rate is equal
to the weight of the water evaporated from the support per
kilogram dry support per minute. At the beginning of the process
the drying rate is constant. After about 40 min the drying rate
decreases and finally the water content in the support is reduced
to 1% after 75 min (see Figure 2a) indicating the end point of
drying. Similar results have been reported in previous studies.25
During drying the metal concentration in the liquid phase
increases due to evaporation of water. This may greatly affect
the solution properties, the drying rate, and the metal distribu-
tion. Figure 3 shows experimental measurements of the evolu-
tion of the drying rate for different initial metal concentrations
at a drying temperature of 60 C. The lines here are included
as a guide for the eye. By comparing the curves for C0 ) 0 M(water only) and C0 ) 0.1 M, we find that for a low initial
Figure 1. The variation of the concentration of the metal deposited on thesupport with the impregnation time.
dC0
dt ) -kadsFCsatC0 (17)
K) i
3idci2
200 (18)
Figure 2. Variation of (a) the water volume fraction and (b) drying ratewith the drying time at Tbulk) 60 C and C0 ) 100 mol/m
3.
Figure 3. Effect of the initial metal concentration on the drying rate atTbulk) 60 C for (a) catalyst samples and (b) solution samples. The lineshere are included as a guide for the eye.
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metal concentration (C0 < 0.1 M), the effect of the metal
concentration on the drying rate is not significant (see Figure
3a). For C0 > 2 M, however, the drying rate is significantly
reduced. In Figure 3a, the drying time for C0 ) 0.1 M is around
50 min. In contrast, the drying time required for C0 ) 4 M is
more than 75 min. We believe that this is due to the decrease
in the vapor pressure and the increase in the solvent viscosity
with an increase in the metal concentration.50 Therefore, drying
is much slower for high metal concentrations, and the drying
time required for high metal concentrations is much longer than
for low metal concentrations. To eliminate the effect of thesupport pore size distribution and pore network on the drying
rate and only focus on the contribution of the initial metal
concentration, 1 mL of solution (no support) with a certain
amount of Ni(NO3)2 was dried in the oven at 60 C. In Figure
3b, we show results for five samples with Ni(NO3)2concentra-
tion equal to 0 M (only water), 0.1, 0.5, 2, and 4 M. It is clear
that for a low initial metal concentration (C0< 0.1 M), after an
initial increase the drying rate reaches a plateau and then reduces
rapidly at the end of drying. For a high initial metal concentra-
tion (C0 > 2 M), however, the drying rate is much lower and
the drying rate evolution becomes quite different. The plateau
region observed in the low initial metal concentration conditions
disappears and the drying rate gradually reduces with time. Thisis because for high metal concentration conditions, the amount
of the metal precursor is comparable to the amount of water so
the increase in the molar ratio of the metal precursor in the
liquid phase during drying becomes significant leading to a
gradual decrease in the water vapor pressure.50 In contrast, for
low metal concentration conditions the amount of water is much
higher than the amount of the metal precursor. Therefore,
although the molar ratio of the metal precursor keeps increasing
during drying its effect on the change of the water vapor pressure
is negligible. If we compare the drying rate evolution curves
shown in Figure 3 panels a and b, we find that the curve shapes
and the extent of the decrease in the drying rate with the initial
metal concentration look quite similar for the two cases. This
indicates that the effect of the initial metal concentration onthe drying procedure during preparation of supported catalysts
is important. For moderate or high metal loading, an accurate
drying model must be capable of capturing the change of the
solvent properties due to the increase in the metal precursor
concentration during drying.
After impregnation, the metal inside the support has two
forms: metal dissolved in the solvent or metal adsorbed on the
support. From past studies we know that drying can change the
distribution of the metal dissolved in the solvent, while its effect
on the metal already adsorbed on the support is much smaller.12
After impregnation, the ratio of the amount of the metal
dissolved in the solvent to that adsorbed on the support isdetermined by the adsorption strength and the initial metal
concentration in the solvent. The effect of adsorption strength
on the metal profiles during drying has been reported in previous
work.25,27 It was found that drying can modify the metal profiles
only for weak adsorption, while its effect is not significant for
strong adsorption.
The impact of the initial metal concentration on the final metal
distribution after drying is shown in Figure 4a-c. Clearly, the
total metal left in the support after drying increases with an
increase in the initial metal concentration. From Figure 4a,b,
we can see that for a uniform initial condition, an egg-shell
profile is obtained if the metal load in the system is low or
moderate. This is due to the effect of convection which drivesthe metal to move toward the support surface. If the initial metal
concentration is sufficiently high (C0 > 3 M), nearly uniform
profiles can be observed after drying (see Figure 4c). This may
be related to three mechanisms. (1) For C0 > 3 M, the drying
rate is greatly reduced (see Figure 3a), which favors a final
uniform distribution. (2) If the metal concentration is sufficiently
high, during drying the support pores can be blocked by the
accumulation of metal crystals due to adsorption and crystal-
lization. This pore-blockage mechanism can greatly reduce the
water transport and the metal redistribution during drying.
Similar results have been observed in previous work. Sietsma
et al.47 investigated the preparation of Ni/SiO2catalysts via the
impregnation and drying method. They found that with 4.2 M
initial metal concentration, the average crystal size after dryingwas 9 nm which was around the same size as the mesopore
Figure 4.Effect of the metal concentration on the metal profiles after drying atTbulk ) 60C: (a) low metal concentrations; (b) moderate metal concentrations;(c) high metal concentrations. Effect of the metal concentration on the metal profiles after calcination: (d) low metal concentrations; (e) moderate metalconcentrations; (f) high metal concentrations.
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diameter of the SBA-15 support they used. (3) Since the melting
point of Ni(NO3)2is 56C, part of the nickel nitrate could be
melted when the samples were dried at 60 C. For high metal
loading conditions (C0> 3 M), the liquid Ni(NO3)2may lead to
the liquid phase remaining continuous during drying, and thus
film-breakage would not occur. This will favor a final uniform
distribution. The effect of film-breakage on the metal distribution
during drying will be further discussed in the following section.
For practical use of the catalyst it is of interest to study the
effect of calcination on the distribution of the metal in the
support. Figure 4 panels d-f show the metal distribution after
calcination with the variation of the metal concentration from
0.05 to 4 M. It is clear that for all cases studied in this work
the metal distribution after drying and after calcination is similar,
indicating that the effect of calcination on the metal redistribu-
tion is not significant. Therefore, it is reasonable to assume that
for our specific systems the metal profile obtained after drying
can be used to predict the final metal distribution of the catalysts.
3.2. Comparison of Experiments and Simulations.In this
section we focus on low metal loads where the initial metal
concentration is less than or equal to 0.1 M. For these cases,
the effect of the metal ions on the solvent properties during
drying is small, and pore-blockage and crystallization arenegligible. Therefore, the final metal distribution is determined
by the initial metal concentration (C0), adsorption strength (Keq,
kads,Csat), drying conditions (Tbulk), transport properties (Dl,i,K)
and film-breakage conditions (R1, R2). Given a specific
metal-support system, the parameters for adsorption, transport,
and film-breakage are fixed and cannot be adjusted in a
straightforward manner. Thus, the final metal profile can be
controlled mainly by changing the initial metal concentration
and the drying temperature.
The variation of the water volume fraction in the support
during drying for different drying temperatures is shown in
Figure 5, where the symbols represent the experimental data
and the lines represent the simulation results. To investigatethe effect of film-breakage, two sets of simulation results are
presentedsone including and one excluding the effects of film
breakage. In the simulations with film-breakage, we assumeR1)0.53 representing the situation where film-breakage starts as
the water evaporation transits from the large pores to the small
pores (R1 ) voidage volume fractionxpercentage of small pores
in the void ) 0.67 0.8), and R2 ) 0.013 below which the
liquid phase is completely discontinuous (solvent flux ) 0). The
value of R2 was chosen on the basis of the regression of
experimental data forC0) 0.04 M, and thereafter we held this
value a constant for other cases. R2) 0.013 corresponds to the
mass ratio of water in the support equal to 2%. In general the
value of R2 is related to the hydrophilic or hydrophobic
properties of the solvent on the support, the size of the smallpores, and the pore network in the support.51 The structure of
the pore network has a significant effect on the transport of the
solvent during drying. Neimark et al. proposed that the pointwhere the liquid phase becomes completely discontinuous (i.e.,
R2) can be calculated on the basis of a coordination number for
the support if the porous space can be represented as a system
of intersecting channels and the coordination number is the
average number of channels meeting at a lattice site.28
In Figure 5, it is clear that drying is much faster at higher
drying temperatures. When drying is carried out at room
temperature (Tbulk ) 22 C), drying is very slow and an
unacceptable amount of water remains in the support at the end.
When the drying temperature is above 60 C, the mass fraction
of the water in the support can be reduced to 1% within a
reasonable amount of time. From Figure 5 it can be seen that
for low to moderate drying rates (Tbulk0.53) we find that the
metal distribution changes only slightly when further increasing
this number. This is because two mechanisms occur with the
variation ofR1. For a high R1 value, film-breakage occurs at thebeginning of drying, which reduces the water flux toward
the surface, and thus suppresses the accumulation of the metal
at the surface. With continued drying, metal starts to move back
to the support center due to the gradient of the metal concentration
in the solvent. Film-breakage can reduce this back diffusion, and
this reduction effect increases with an increase in R1. Therefore,
for a highR1value film-breakage suppresses the egg-shell profile
at the earlier stages of drying and favors the egg-shell profile at
the later stages of drying. Consequently, the effect ofR1 on the
final metal profiles is due to the compensation of these two
contributions. To enhance the egg-shell profile, an optimumR1is
required. The egg-shell profile can be greatly enhanced with
increasing the value ofR2(not shown). This is because the variationof the value ofR2 has only a slight effect on the early stage of
drying, while its effect on the final stage of drying is significant.
Therefore, for a high value ofR2(R2 ) 0.13), the pronounced egg-
shell profile formed in the early stage of drying may be still
observed at the end of drying.
The sensitivity analysis was also carried out for other
parameters based on our nickel/alumina system (not shown).
In general, the egg-shell profiles can be enhanced by increasing
the permeability and uniform profiles can be obtained by
increasing the diffusion coefficient. This is in agreement with
our previous work.25,27 In our specific case the adsorption
process is much faster than the transport process; we found that
the metal redistribution is not sensitive to the variation of thekinetic adsorption constant.
4. Conclusions
We established a theoretical model to predict the metal
distribution during drying and compared the simulation results
with experimental measurements for a nickel/alumina system.
The adsorption and transport parameters used in the simulations
are obtained from separate experiments/calculations.
From the experiments, several interesting phenomena were
observed. (1) We found that egg-shell profiles can be enhanced
by increasing the drying temperature and the initial metal
concentrations, if the metal load in the system is low or
moderate. For high metal loadings, nearly uniform metal profiles
are observed from the experiments. (2) We compared the metal
profiles after drying and after calcination and showed that for
our specific situation the effect of calcination on the metal
distribution is not significant. Thus, the metal profiles obtained
after drying can be used to predict the final metal distribution
of the catalysts. (3) By plotting the variation of the water content
and the drying rate with the drying time for different initial
metal concentrations, we found that if the initial metal concen-
tration is high the solvent properties may change dramatically
during drying because of water evaporation and high metal
concentration in the liquid phase.
We also compared the simulations with experiments tovalidate our theory. Since the effect of crystallization and pore-
blockage is not considered in our model, our comparison only
focused on low metal load conditions. To investigate the effect
of film-breakage on the metal redistribution during drying, we
assume that once film-breakage occurs the solvent flux linearly
decreases with the decrease in the water volume faction until
the water volume fraction reaches a certain point, at which the
liquid flux completely stops and the metal is enclosed in isolated
liquid domains. We found that film-breakage is crucial to capture
the metal profiles observed in the experiments and the simula-
tions show an excellent agreement with experiments if the effect
of film-breakage is considered.
In summary, the goal of this study is to better understandthe fundamental mechanisms during drying, and to determine
the key parameters used to generate a desired metal profile, using
theoretical simulations and experiments. We have compared
experiments and simulations for low metal concentration
conditions (C0 < 0.1 M). For moderate and high metal
concentrations, crystallization may become important and the
change of the solvent properties during drying due to the
increase in the metal concentration in the solvent may greatly
affect the drying process. Pore-blockage may also become
important at high metal concentrations. It remains to be seen
what is the relative importance of these additional phenomena
that occur at moderate and high metal concentrations, and future
work should investigate how these phenomena interact to impact
drying.
Acknowledgment
We wish to acknowledge partial financial support for this
work from the National Science Foundation and the Rutgers
Catalyst Manufacturing Science and Engineering Consortium.
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ReceiVed for reView September 16, 2009ReVised manuscript receiVed February 1, 2010
Accepted February 2, 2010
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