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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.

    Ind. Eng. Chem. Res. 2010, 49,26492657 2649

    10.1021/ie9014606 2010 American Chemical SocietyPublished on Web 02/15/2010

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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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