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Journal of Nanomaterials
Volume 2015 (2015), Article ID 275705, 17 pages
http://dx.doi.org/10.1155/2015/275705
Research Article

Preparation of Nanostructured Microporous Metal Foams through Flow Induced Electroless Deposition

1School of Chemical Engineering and Advanced Materials, Newcastle University, Newcastle upon Tyne NE1 7RU, UK
2Canik Başarı University, Canik, 55080 Samsun, Turkey
3GAP Technologies, 1 Grosvenor Place, 8th Floor, London SW1X 7HU, UK
4Optimum, Domodedovskiy Rayon, Starosyanova Village, Sadovaya Street No. 4, Moscow 142030, Russia

Received 15 May 2015; Revised 20 June 2015; Accepted 12 July 2015

Academic Editor: Ovidiu Ersen

Copyright © 2015 Galip Akay and Burak Calkan. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

Abstract

Monolithic nanostructured metallic porous structures with a hierarchy of pore size ranging from ca. 10 μm to 1 nm are processed for use as microreactors. The technique is based on flow induced electroless deposition of metals on a porous template known as PolyHIPE Polymer. The process is conducted in a purpose built flow reactor using a processing protocol to allow uniform and efficient metal deposition under flow. Nickel chloride and sodium hypophosphite were used as the metal and reducing agent, respectively. Electroless deposition occurs in the form of grains with a composition of in which the grain size range was ca. 20–0.2 μm depending on the composition of the metal deposition solution. Structure formation in the monoliths starts with heat treatment above 600°C resulting in the formation of a 3-dimensional network of capillary-like porous structures which form the walls of large arterial pores. These monoliths have a dense but porous surface providing mechanical strength for the monolith. The porous capillary-like arterial pore walls provide a large surface area for any catalytic activity. The mechanisms of metal deposition and nanostructure formation are evaluated using scanning electron microscopy, energy dispersive X-ray analysis, XRD, BET-surface area, and mercury intrusion porosimetry.

1. Introduction

1.1. Structured Catalysts

Although catalysis accelerates reaction rates and chemical conversions, accessibility of the reactants to and removal of products from the catalytic sites are important to realize the full potential of catalysts. Supported catalyst systems are intended for these provisions. Catalysts are either deposited as a thin film on the walls of reactors or deposited on high surface area porous support particles and subsequently palletized for use in particulate form in packed/fluidized bed reactors or stirred tanks. These two techniques have certain drawbacks: in coated systems, catalyst adhesion can be nonuniform and weak while the accessibility of the active sites within the interior of the catalyst pallets is hindered due to low porosity, small pore size, and connectivity. Therefore, when the reactions are transport-limited, even such systems cannot provide adequate accessibility of the catalytic sites since the high surface area support materials themselves restrict transport processes.

In recent years, the so-called “structured catalysts” became available in order to address these problems. The catalyst supports are often in the form of macroporous foams or monoliths which actually form the reactor, acting as a static mixer at the same time. In order to increase the surface area of the monolithic catalyst supports without excessive pressure drop, macrochannel systems are utilized in industry such as those in catalytic converters. In these systems, not only the local hydrodynamic conditions but also the catalyst coating thickness can be controlled to obtain well-defined catalytic reactors and they invariably outperform reactors with catalyst particles in packed bed or stirred tank configuration [13]. Monolithic reactors combine the advantages of fixed bed (ease of handling) and turbulent stirred tank reactors (intense contacting) while providing a narrow residence time distribution, avoiding mal-distribution and scale-up problems.

1.2. Monolithic Reactors with Hierarchic Pore Structure

Monolithic catalyst systems with nonporous/low porosity walls also suffer from certain disadvantages, such as cost, low catalyst loading, integrity of the catalyst coating on the monolith channel walls, and the presence of two independently controlled length scales which only provide partial accessibility of the catalytic sites. The accessibility of the nanosized catalytic sites is achieved most effectively by a hierarchical channel or pore network structures which are ubiquitous in nature [46]. In these systems, the main chemical processes are principally controlled at the molecular/nanoscale as many of these processes are transport-limited, while the continuous supply/removal of reactants/products is achieved through capillaries/pores of ever increasing diameter. Such a system provides an optimum architecture incorporating micro-/nanoscale with chemically functional features within the macrosystem at an optimum surface area for catalytic applications. Such hierarchically structured catalyst systems with fractal-like meso- to macropore size distribution can be expected to be more efficient and robust due to the enhanced surface area and accessibility leading to the intensification of chemical processes [6].

1.3. Production of Porous Metallic Structures

There are several important applications of metallic foams as both structural/engineering and specialized materials. Excellent periodical reviews are available describing the manufacture, characterization, properties, and application of these materials [79]. One particular metallic foam is produced through electrochemical metal deposition on polyurethane foam followed by heat treatment when the template polymer is burnt off [10, 11]. These materials are commonly used for catalyst support to obtain supported catalyst systems as well as electrode in fuel cells. These materials are marketed as Metapore, Celnet, Retimet, and Recemet. Their macrostructure is very similar to some of the materials produced by the current technique except that these materials do not have a hierarchy of pores, while their surface area density (surface area per unit volume) is some 100-fold smaller and pore size is some 50 times smaller than those produced in this work.

1.4. PolyHIPE Polymers as Monolithic Microreactors and as Templates for Electroless Metal Deposition

In the design of novel monoliths with hierarchical porous catalytic reactors having a pore size range of ca. 100 μm to a few nanometers, the first step is to obtain structures with controlled pore size and porosity and functionalize them to impart both nanostructure and catalytic activities. One such highly versatile monolithic (or indeed particulate) system is known as PolyHIPE Polymer (PHP) which was developed at Unilever Research Laboratory at Port Sunlight (UK) during the 1980s by a team including one of the present authors (Galip Akay) who also developed the processing of the basic material and advanced its use in both small and large scale applications [12, 13]. A summary of PolyHIPE Polymer chemistry can be found in [14].

PolyHIPE Polymers are prepared through a high internal phase emulsion (HIPE) polymerization route and hence the acronymic name, PolyHIPE, which reflects the processing history. Depending on the composition of the HIPE, processing, and polymerization history, PHPs can have hierarchical pore and interconnects over a size range ca. 100 μm to nanometre, while the pore volume can reach as high as 97% for practical applications. Chemical/biochemical functionalization processes of PHPs are relatively easy [15] and, coupled with their easy manufacture in monolithic form with well-defined macro-, meso-, and nanostructures providing a hierarchy of pores, they are ideally suited for process intensification [6] in agricultural, biological, and chemical processes, in both small scale or large scale applications. Further acceleration, efficiency and selectivity in processing are obtained when PHPs are used as monoliths.

PolyHIPE Polymers can be chemically and biologically functionalized [1620] in order to achieve mimicking of nature’s processing strategy and applied to tissue engineering, bioprocess intensification, and agroprocess intensification. Furthermore, nonbiological functionalization processes were used for specific applications such as separation processes [21], fast response ion-exchange resins [22], and environmental and energy conversion processes [23].

Monolithic chemical or biochemical reactors have several advantages over packed bed/fluidised bed or stirred tank reactors even when hierarchic catalysts are used in particulate form. In monolithic flow-through reactors, there is no channeling and the distribution of flow across the cross-section of the monolithic reactor is more uniform and the catalytic sites are only micrometers away from the reactants. Furthermore, in some reactions when the rate is limited by product concentration, flow through the monolith allows the removal of the product from the catalytic sites into the bulk/convective flow. These characteristics result in process intensification, and direct comparison of packed bed and monolithic reactor performance is available when PolyHIPE Polymer was used in particulate form (packed bed) [17] and in monolithic form [18].

As reviewed above, PolyHIPE Polymer monoliths have been used successfully for intensifying processes in agriculture, biology, chemical/physical-chemical, and energy conversion processes due to their unique hierarchic pore structure in which large arterial pores with large interconnecting holes (windows) facilitate convective mass transfer, while walls of the arterial pores provide the catalytic sites which are connected to the arterial pores via mesoscale (typically 100 nm) pores [15]. However, to the best of our knowledge, there is no metallic equivalent form of such monolithic structures. Therefore, the manufacture of such metallic monoliths will increase the temperature and pressure range of chemical/physical-chemical processes and catalyst, reactant, and product ranges of these reactors.

1.5. Electroless Deposition

There are different mechanisms in the literature suggested for the chemical reduction of nickel salts by hypophosphites. Probably the most widely accepted mechanism is the one suggested by Brenner and Riddell [24] as also reported in [25, 26]. They stated that atomic hydrogen is the real nickel reductant. With sufficient energy and a catalytic surface, hypophosphite ions react with water and they are oxidized to orthophosphite. The hydrogen generated by this reaction is absorbed onto the catalytic surface:Nickel ions at the catalytic surface are reduced by the absorbed active hydrogen:The liberation of hydrogen gas in the catalytic nickel reduction is the result of recombination of the hydrogen atoms:The mechanism of atomic hydrogen being the real nickel reductant has found support from many researchers. But still it has failed to explain certain issues like the simultaneous reduction of nickel and hydrogen. Also there is no clarification of why stoichiometric consumption of hypophosphite never exceeds 50%. Usually 5 kg of sodium hypophosphite is required to reduce 1 kg of nickel for an average efficiency of 37%. In another source [27], this problem was explained by the catalytic oxidation of most of the hypophosphite present to orthophosphate and gaseous hydrogen evolution according to the reaction which occurs independently of the deposition of nickel and phosphorus, hence causing the low efficiency of electroless nickel solutions:The most important application of electroless deposition is the coating of plastic surfaces with metal or indeed metal coating of surfaces. In these applications, coating thickness is small (a few tens of microns) and then the removal of hydrogen is simple. In the present case, metal deposition is extensive and confined to micron size pore walls. Furthermore, the walls of the porous template polymer surface were not catalyzed to achieve metal deposition and polymer/metal integration was not necessary. Nevertheless, the above chemical reactions indicate that the removal of hydrogen is of paramount importance in order to sustain metal deposition.

1.6. Novelty of the Current Process

The characteristics of flow-through monolithic reactors have been used in this research (most importantly, the removal of reaction products) in order to obtain electroless deposition. In this study, we use PolyHIPE Polymers to electrolessly deposit metals and subsequently heat-treat the resulting constructs to obtain monoliths which can be used as gas separation and reaction media at high temperatures. Previous attempts to produce monolithic porous metal systems through electroless deposition using PolyHIPE Polymer as template failed because the processing setup did not allow the continuous removal of reaction products during deposition. Hence, only small, weak porous metallic particles could be obtained [28].

As we aim to demonstrate that catalytic microreactors with hierarchic pore structure can be produced through this method, we need to choose the composition of the metal deposition solution carefully. In this case, the introduction of phosphorous in the reactor should be avoided as phosphorus is a well-known catalyst poison [29]. Instead, a dimethylamine borane system was chosen in order to obtain monoliths with catalyst activity in which the presence of boron enhances resistance of nickel catalyst against poisoning [30]. The results with dimethylamine borane will be reported separately.

2. Experimental Section

2.1. Preparation of Template PolyHIPE Polymer (PHP) for Metal Deposition

PHP is conveniently prepared through the polymerization of a polymerizable continuous phase of a high internal phase water-in-oil emulsion (HIPE) using the equipment in Figure 1. The effects of temperature and the non-Newtonian fluid mechanics aspects of the HIPE formation and dispersed phase (water) droplet size reduction without phase inversion to oil-in-water have been described in [31]. The techniques used in this study ensure the preparation of macroporous polymers with well-controlled internal architecture, pore and interconnect sizes, and their distributions. The continuous (oil) phase of HIPE consisted of styrene, 78 wt% (monomer); divinylbenzene, 8 wt% (cross-linking agent); and sorbitan monooleate (Span80), 14 wt% (surfactant), all obtained in reagent grade from Aldrich and used without any further treatment. The dispersed (aqueous) phase is comprised of double distilled water containing 1 wt% potassium persulfate as initiator for polymerization.

Figure 1: Schematic representation of PHP preparation adopted from [15].

The total volume of the aqueous phase and oil phase combined was 225 mL, which was the optimum amount for this particular mixing vessel (internal diameter was 12 cm) (Figure 1). Mixing was conducted using two flat paddles (diameter 9 cm) that were stacked 1 cm apart from each other at right angles. The bottom impeller was 0.5 cm above the bottom of the vessel. Rotational speed of the impellers was 300 rpm. The phase volume of the aqueous phase was 95% in order to obtain highly open pore polymer (pore sizes ca. 50–60 μm). Agitation of aqueous phase and oil phase was performed in the mixing vessel, which was heated by a water jacket that circulated hot water at 60°C by using a water bath. Prior to the mixing of the constituents, the hot water circulation was started to ensure that the reactor reached the required temperature. The aqueous phase was also preheated to 60°C on a hot plate. When the aqueous phase and the mixing vessel temperatures were set, all the oil phase (11.3 mL) was poured into the vessel at once. The mixing was conducted in a closed environment to prevent monomer/cross-linker loss through evaporation. Emulsification at relatively high temperatures results in large pores at a given mixer speed of 220 rpm and 3 minutes mixing time.

Feeding of the aqueous phase (214 mL) was performed by four tubes connected to two peristaltic pumps. The rate of pumping was adjusted at such a speed that all the aqueous phase was dosed into the vessel in 2 minutes. The impeller was started at the same time as the dosing of the aqueous phase into the vessel. After dosing all the aqueous phase into the oil phase, the mixture was stirred for another minute for homogenization. The emulsion was then put into 50 mL plastic containers with internal diameters of 26 mm (Figure 1). The plastic containers were then placed in a preheated (60°C) oven, where polymerization took place in about 8 hours. After the HIPE polymerized, the solidified PHP blocks were removed from the containers and cut into 4 mm thick disks with sharp razors. Drying of the disks did not require any specific equipment, as the disks were left to dry overnight on tissues in a fume cupboard. In order to remove the surfactant and residual monomer, the disks were washed in a Soxhlet extractor. First, they were washed with isopropanol for 3 hours, followed by another 3 hours of washing with double distilled water to clean any remaining residues in the pores and interconnecting walls. The pore size of the disks was evaluated by scanning electron microscopy.

2.2. Electroless Deposition Solution

The electroless deposition was conducted under flow conditions. Therefore, some of the common electroless deposition problems, such as constant change in pH (caused by hydrogen liberation during deposition) and difficulty to control reduction of free nickel, were not encountered. Hence, employment of buffering agents, inhibitors, or complexing agents was not required. The electroless deposition solution (plating bath) was composed of nickel source, reducing agent, and ammonium hydroxide to adjust the pH. Sodium hypophosphite hydrate was used as a reducing agent. Accordingly, the plating bath compositions were very simple compared with the well-established plating bath compositions often used in commercial applications such as metal coating of plastic parts [25].

Metal Deposition Solutions (Plating Bath). Nickel chloride was used as the metal source. The main study is focused on the use of sodium hypophosphite as the reducing agent. However, in order to demonstrate the effect of reducing agent on the characteristics of metal deposition, we also used dimethylamine borane as the reducing agent.

Plating Bath-1. Consider the following:(i)Metal source is nickel chloride, with fixed concentration at [Ni] = 0.13 M.(ii)Reducing Agent-1 is sodium hypophosphite hydrate (NaH2PO2·H2O) with variable concentration at [P] = 0.13 M; 1.26 M; 2.52 M. Here, we represent the reducing agent concentration through the molar concentration of phosphorous.(iii)pH regulator is ammonium hydroxide (35% concentration) to set pH = 11.5.

Plating Bath-2. Consider the following:(i)Metal source is nickel chloride, with fixed concentration at [Ni] = 0.13 M.(ii)Reducing Agent-2 is dimethylamine borane [(CH3)2NHBH3] at a fixed concentration of [B] = 0.26 M.(iii)Solution stabilizers are 0.27 M sodium acetate and 3.88 × 10−4 M sodium lauryl sulphate.(iv)pH regulator is ammonium hydroxide (35% concentration) to set pH = 7.5.

2.3. Metal Deposition Process

The metal deposition setup used through this study is shown in Figure 2. The flow diagram of the metal deposition setup is shown in Figure 2(a). A metal deposition cell was constructed as illustrated in Figure 2(b). The deposition cell housed the template PHP in the form of a disk (4 mm thick and 26 mm in diameter). Referring to Figure 2(b), PHP template sample (S) was sandwiched between two PTFE flow distributors (D) at the end of the PTFE flow channel (C) bored into the holders (A) which also acted as support for PHP. The whole assembly was then placed between two circular brass blocks (B) which was electrically heated using a band heater (E). Note that the PHP template was in direct contact with the brass holder to provide direct heating. Temperature of the PHP template was monitored using a thermocouple (T) in contact with the polymer. All parts of the flow cell which were in direct contact with the plating bath were made of PTFE in order to prevent metal deposition in the flow channels.

Figure 2: (a) Diagrammatic illustration of the metal deposition setup. (b) Details of the metal deposition cell.

The metal deposition solution was kept at room temperature and was pumped into the deposition cell using a syringe driver at a rate of 2 mL/min. In order to cause metal deposition within the pores of the template polymer, the temperature of the solution was raised to °C in the polymer. In order to achieve this, the deposition cell was heated to 90°C by using the band heater and charged with dematerialized water at 97°C for 4 minutes at a rate of 40 mL/min. This was followed by the syringe pumping of the metal bath solution. After pumping 50 mL solution, the deposition was stopped and hot water washing was renewed and the cycle was repeated. Throughout the experiment, the band heater and hot water washing kept the polymer constantly at 90°C. After using 340 mL metal bath solution, the direction of flow was reversed until a sufficient amount of metal was deposited. It is possible to reverse the flow direction after each 50 mL deposition and washing, in order to obtain more uniform deposition.

2.4. Heat Treatment

After the completion of the metal deposition and final washing, the samples were put into a high temperature oven and the temperature of the oven is increased from room temperature to the heat treatment temperature () which was dominantly 600°C. The heating rate () was such that total heating period was 1 hour. After reaching this heat treatment temperature, the samples were annealed at this temperature for a period of . In the majority of cases,  min.

2.5. Scanning Electron Microscopy (SEM) and Energy Dispersive X-Ray (EDX) Analysis

The scanning electron microscope used in the present work was an environmental scanning electron microscopy (XL30 ESEM-FEG) fitted with a Rontec Quantax system for energy dispersive X-ray (EDX) analysis to obtain local atomic concentration of various elements in metallic samples after heat treatment. Since the metallic samples were conductive, they were not coated although the nonconductive polymeric samples could also be examined in their natural state without significant sample modification or preparation. However, polymeric samples were coated with gold for SEM imaging.

2.6. X-Ray Diffraction (XRD)

The X-ray diffraction (XRD) equipment was a PANalytical X’Pert Pro diffractometer, fitted with an X’Celerator. The X’Celerator is a relatively new attachment to the X’Pert and has the effect of giving a good quality pattern in a fraction of the time of the traditional diffractometer.

2.7. BET Surface Area Analysis

A Beckman-Coulter SA 3100 analyzer was used. This instrument uses the gas sorption technique to obtain the surface area and pore size distributions at room temperature using helium. Specific surface area of the metallized monoliths was calculated after measuring bulk density of the samples in order to compare these materials with the commercially available porous metals.

2.8. Mercury Porosimetry

In this study, the mercury intrusion porosimetry technique was used to measure the porosity and pore size distribution of the metal foams. The equipment (Autopore II 9220) was manufactured by Micromeritics Ltd.

3. Results and Discussion

Our aim is to demonstrate the feasibility of obtaining monolithic metal foams which can also be used as catalytic reactors or as supported membranes. Therefore, in the first instance, we aim to establish the method of production which can be scaled up, evaluate the mechanism of electroless deposition as well as nanostructure formation through heat treatment, and evaluate the characteristics of the metallic monoliths with a hierarchic pore structure in which the pore size ranges from nanometers to micrometers. For this purpose, we used a nickel chloride/hypophosphite system in a very simple deposition solution which did not contain any stabilizers and surface sensitization (by palladium) of the template deposition medium (i.e., PHP) to promote deposition and reduction reactions.

3.1. PolyHIPE Polymer Templates

Throughout this study, we used one type of PolyHIPE Polymer (PHP) template with phase volume 95%, pore size μm. A scanning electron micrograph of the PHP template is shown in Figure 3. We have chosen this material because smaller pore size or phase volume PHP requires pressurization to pump the metal deposition solution and it does not allow the deposition of sufficient metal to provide mechanical strength.

Figure 3: Pore morphology of the PHP disks, with porosity of 95% and average pore size of μm that were used in the metallization experiments: (a) general appearance (scale bar = 500 μm); (b) details (scale bar = 100 μm).
3.2. Metal Deposition Characteristics

The deposition of metal within the pores is in the form of metal grains. Figures 4(a) and 4(b) illustrate the metal deposition behavior, in which the metallic grains as well as the polymer structure can be identified clearly as the deposition is at the early stages of the experiments (340 mL solution passed). The deposition was carried out until all the strands of the polymer were totally covered with metal grains which required 600 mL solution in this example illustrated in Figure 4(b). The weight of a typical construct (template polymer and nickel deposit) was 3.2 g when the deposition was stopped. An example of a fully deposited polymer disk is shown in Figure 4(b) which indicates the autocatalytic nature of the deposition kinetics. Initial deposition rate was low since the template polymer was not sensitized and the size of the metal grains was some 70% larger compared with the average size of the grains deposited at the later stages as shown in Figure 4(a).

Figure 4: Nickel deposition from NiCl2 [Ni] = 0.13 M solution with sodium hypophosphite as reducing agent [P] = 2.52 M. (a) Inner structure at the early stages of deposition, after passing 300 mL solution through the template when the dry weight of the resulting construct (PolyHIPE Polymer and metal deposit) was 0.87 g (scale bar = 20 μm). (b) Inner structure after passing 600 mL solution when the weight of the resulting construct was 3.2 g (scale bar = 10 μm).

X-ray diffraction patterns of the electroless Ni-P grains in the as-deposited condition are given in Figure 5 which exhibited a single broad peak indicative of the amorphous nature of the metal deposits. It also indicates the presence of small amounts of NaCl generated during the reduction of NiCl2 by NaH2PO3.

Figure 5: XRD pattern of the as-deposited Ni-P grains before heat treatment of the construct obtained through nickel deposition using a plating bath with 0.13 M NiCl2 and 1.26 M sodium hypophosphite after using 600 mL solution.

The effect of reducing agent concentration [P] in the metal deposition solution on the size of the nickel-phosphorous grains is illustrated in Figure 6. The grain size decreased with increasing reducing agent concentration. Regarding the sizes of the deposits, Ni-P grain diameters ranged from 7 to 18 μm, from 2.5 to 10.5 μm, and from 0.75 to 2 μm when the reducing agent concentration increased from 0.63 to 1.26 and then to 2.52 M.

Figure 6: Size of the spherical grain deposits varied depending on the concentration of the plating bath. Amount of the reducing agent sodium hypophosphite and volume of solution used were (a) 0.63 M and 200 mL, (b) 1.26 M and 200 mL, and (c) 2.52 M and 600 mL. (d) In this example, we also used 0.26 M dimethylamine borane as the reducing agent and 600 mL solution was used. Regarding the size of the deposits, (a) Ni-P grain diameters ranged from 5 to 20 μm, (scale bar = 50 μm); (b) Ni-P grain diameters ranged from 2 to 12 μm, (scale bar = 20 μm); (c) Ni-P grain diameters ranged from 0.5 to 2 μm (scale bar = 5 μm); (d) Ni-B grain diameters were in the order of a few hundred nanometers (scale bar = 2 μm).

As seen in these micrographs, the concentration of deposited grains increases with increasing reducing agent concentration. In order to illustrate the effect of the type of reducing agent on grain size, we also used 0.63 M borane dimethylamine instead of sodium hypophosphite. As seen in Figure 6(d), the grain size for borane dimethylamine is ca. 200 nm.

3.3. Heat Treatment and Skin-Core Structure Development

In order to understand the mechanism of structure formation in these constructs (i.e., template PolyHIPE Polymer and metal deposit) after passing 600 mL plating bath solution through the template PolyHIPE Polymer, the resulting samples were heat-treated. In these experiments, we used 0.13 M nickel chloride and 1.26 M reducing agent and sodium hypophosphite. After full deposition was achieved (weight of the washed and dried constructs was typically 3.2 g), the resulting constructs were washed in water and then heat-treated.

Starting from room temperature, the sample already in the oven, temperature was increased to a prescribed temperature at a variable rate so that the heating period was 60 minutes. After reaching the target temperature (i.e., 500, 600, and 800°C), samples were either removed immediately (so that annealing time ) and subsequently cooled to the room temperature in air or alternatively kept at the target temperature for a fixed period of time (usually 60 min) and then removed from the oven and allowed to cool down in air. Final heat treatment procedure involved a prolonged annealing. After reaching the heat treatment temperature and remaining at this temperature for 60 minutes ( min), the heating was switched off and the samples were gradually cooled in the oven over a period of 12 hours.

The reason for this heat treatment protocol was to understand the structure formation as a result of the solid-state reaction that took place during heat treatment. The fracture surface of these heat treated samples was examined under scanning electron microscopy (SEM). The location of the examination was typically at the center of the samples in all cases. The reason for this is that these monoliths form a skin/core structure in which the skin has reduced porosity but provides strength to the monolith. These results are illustrated in Figures 7(a)7(f) which reveal the mechanism of structure formation through a solid state reaction.

Figure 7: Development of hierarchic pore structure during heat treatment of the Ni-P metal deposits. Sample characteristics: [Ni] = 0.13 M; [P] = 1.26 M. Amount of deposition solution used was 600 mL. (a) First stage of the formation of grain surface skin after temperature reached °C during heating at °C/min; . (scale bar = 1 μm). (b) Skin formation after temperature reaches °C during heating at °C/min; . (scale bar = 1 μm). (c) Skin formation after temperature reaches °C during heating at °C/min;  min (scale bar = 2 μm). (d) Full grain skin formation after heat treatment at °C when °C/min;  min followed by cooling in the closed oven until reaching room temperature over a period of 12 hours (scale bar = 2 μm). (e) Details of the skin at high magnification (sample as in Figure 7(d)) showing the existence of the pores with size ca. 200 nm (scale bar = 1 μm). (f) The inner structure of the grains revealed by the fractured grains showing a porous skin and a dense inner core. Sample same as in Figure 7(d) (scale bar = 10 μm).

The transformation of the Ni-P grains began on the surface of the grains. As the reaction proceeded, dense metallic strands appeared which eventually covered the inner part of the grains (Figures 7(a)7(d)). These strands also fused but formed a porous skin (Figure 7(e)) with pore size of ca. 200 nm and thickness ca. 1 μm. Further SEM examination of the fracture surface of the grains indicated that core of the grains is phase separated from the porous skin (Figure 7(e)). During heat treatment, the original discrete spherical grains now merged to form a continuous undulating capillary with porous walls forming the walls of the micron sized large pores which are connected to each other through micron size arterial interconnecting windows.

Figures 7(a)7(f) show that, during heat treatment, the fused grains forming the walls of the porous monolith undergo a solid-state reaction which also causes a phase separation, resulting in a porous skin and a detached core. However, as these grains are all connected, the resulting wall structure is in the form of undulating porous capillaries filled with nickel-phosphorus compound as revealed by XRD and energy dispersive X-ray analysis.

When the core material was removed from the broken grain skin, the remaining structure looked like an empty shell. Extensive SEM examination indicated that these grains fuse together to form undulating partially filled capillaries. These structures can be termed as “capillary-like, or capillaric” and indeed they are also formed in nature as part of angiogenesis [32, 33]. The materials within these capillaries are the unreacted Ni-P compounds Ni2P, Ni12P5, and Ni3P, with the latter being the most stable of these Ni-P compounds as shown later using XRD. The inner part of the grain skin (shell) can be seen in Figure 8(a). As this structure was examined in more detail, it was observed that the inner part of grain skin was composed of nanosized pores as shown in Figure 8(b).

Figure 8: Details of the porous undulating capillaries forming the walls of the large arterial pores. Sample characteristics: [Ni]  =  0.13 M; [P] = 1.26 M. Amount of deposition solution used was 600 mL. Heat treatment conditions: °C during heating at °C/min;  min. (a) Inner structure of an empty capillary wall (Scale bar 2 μm). (b) Details of the inner structure of the capillary walls of the arterial pores (scale bar = 500 nm).
3.4. Structure of the Grains and Capillaric Walls of the Arterial Pores

After heat treatment, the formation of a grain skin around the core was not the only change in the solid deposits. The core material itself was also subjected to reaction and a second skin appeared in the grains. The presence of multiple skins was only observed when the reducing agent concentration was high ([P] = 1.26 or 2.52 M). This feature can be best explained by the expression “Russian doll” structure as shown in Figure 9. The sample in Figure 9 had a grain size of ca. 12 μm. The first skin had a thickness of ca. 2 μm while the thickness of the second skin was ca. 1 μm. These skins were separated from each other although the second skin was connected in part to the inner unreacted core which had a diameter of ca. 6 μm. The erosion of the core can be observed in the SEM image at high magnification in Figure 9. As the grains got smaller in size, they became more difficult to find broken cores to be examined. Innermost cores as small as 0.5 μm were observed in other samples as seen in Figure 10 which also indicates that the capillary-like (capillaric) walls of the arterial pores have large porosity.

Figure 9: Russian doll structures after heat treatment when [Ni]  =  0.13 M, [P] = 1.26 M, Heat treatment temperature °C (heating rate °C/min), and annealing time  min followed by cooling in air. Scale bar = 2 μm and 200 nm (scale bar of inset).
Figure 10: Formation of capillaric walls of the arterial pores after heat treatment following the solid state oxidation of compounds in the grains. Sample characteristics: [Ni] = 0.13 M, [P]  =  2.52 M, heat treatment temperature °C (heating rate °C/min), and annealing time  min followed by cooling in air. Scale bar = 1 μm.

Inward oxygen diffusion and oxygen gas transport through the voids and microchannels in the NiO scale resulted in the formation of a duplex NiO structure [3437]. Further inward oxygen diffusion and oxygen transport can also cause triplex or quadruplex oxide scale formation. The balance between oxygen supply (activity) and phosphorus content determines exactly which structures form at which time during oxidation. Formation of a complete layer between Ni-P and NiO layers must be validated by further investigation with TEM.

The summary of the effect of reducing agent concentration on the grain structure is given in Table 1.

Table 1: The properties of three samples prepared by using [Ni] = 0.13 M and sodium hypophosphite as reducing agent at concentrations [P] = 0.63 M, 1.26 M, and 2.52 M. Heat treatment was conducted with gradual heating from room temperature to 600°C at a rate of 10°C/min followed by annealing at 600°C for 60 minutes and cooling in air.

Although it can be clearly seen that the grain sizes decrease with increasing sodium hypophosphite molarity, there is not a uniform distribution of grain sizes before or after the heat treatment. However, after heat treatment, the sample produced by using 0.63 M sodium hypophosphite had the most regular size and shape of grains. When 2.52 M sodium hypophosphite was used as a reducing agent, a very high degree of sintering/agglomeration of the grains was observed. Grain surface pore size was similar in the first two samples. The high concentration of sodium hypophosphate decreased the size of the surface pores drastically although these pores were not well defined.

3.5. Chemical Distribution within Grains: XRD and EDX Analysis

In order to obtain the overall chemical composition of the porous monoliths after heat treatment, the XRD patterns are taken. These patterns change with plating bath composition and heat treatment. A typical XRD pattern of the whole sample is shown in Figure 11. The sharp XRD peaks indicate crystalline structure formed by various compounds which were identified as Ni; NiO; Ni12P5; Ni3P; and Ni2P. Although XRD study is useful in the identification of the compounds and their crystal structure, the distribution of nickel, oxygen, and phosphorous across the grains and indeed in different locations was studied using energy dispersive X-ray (EDX) analysis.

Figure 11: XRD pattern of the Ni-P structure (same sample in Figure 10) after heat treatment at 600°C. Sample details: plating bath composition: [Ni] = 0.13 M, [P] = 1.26 M and heat treatment conditions: °C, heating rate = 10°C, and curing/annealing time  min followed by cooling in air.

For EDX analysis, we used 3 different samples produced under different conditions and an additional sample was tested as a duplicate to test the reproducibility of the method. A grain in the sample chosen and its center was located under SEM. Several EDX measurements were performed at various distances from the center of the grain. This scheme is illustrated in Figure 12.

Figure 12: Typical example of the EDX analysis on a fractured grain using spot measurements starting from the center of the grain (Point 0) as a function of distance from the center. Sample characteristics: [Ni] = 0.13 M, [P] = 1.26 M, heat treatment temperature °C, heating rate °C/min, and annealing time min followed by cooling in air. Scale bar = 2 μm.

From the EDX spectrum, atomic fractions of nickel, oxygen, and hosphorous were calculated. The results are shown in Figure 13 where the atomic weight percent of phosphorous is plotted as a function of distance from the center of the grain. The range of overall phosphorous concentration in the samples before heat treatment ranged from 10.5 to 15.4 atomic percent (at%) when the phosphorous concentration in the plating bath ranged from 0.63 to 2.52 M. As seen in Figure 13, the maximum phosphorous concentration is ca. 16 at% although phosphorous concentration in the plating bath was 0.63 M and 1.52 M. As discussed earlier, not all of the reducing agents are utilized in the reduction of sodium hypophosphite to Ni [26] and it therefore appears that the effect of the reducing agent is to change the morphology of the grains (and hence the structure of the monolith) rather than change the chemical composition of compounds. In commercial applications for nickel coating of plastic surfaces, the phosphorous content also ranges from ca. 4.6 to 23.1 at%.

Figure 13: Distribution of phosphorus in grains as a function of distance from the center of the grain. Identification of the samples: Sample 31A: [P] = 0.63 M, °C, and  min; Sample 38A: [P] = 1.26 M and °C; Samples G3 and P5: [P] = 1.26 M and °C. In all cases, time to reach the heat treatment temperature is 60 minutes and curing/annealing time  min followed by cooling in air.

It is clear from Figure 13 that, within the core of the grains, phosphorous concentration remains constant but it is reduced sharply outside the core when the skin is reached where it is typically less than 1 at%, within the accuracy of the experiments.

3.6. Overall Structure of the Monoliths: Crust Formation

The foregoing analysis of the foam structure was performed near the center of the monolith in order to illustrate the mechanism of structure formation. However, for practical purposes, the mechanical strength of the monoliths is important and hence the full structure evaluation is necessary.

It was found that, even at the initial stages of metal deposition, a dense layer is formed on the surface of the template PolyHIPE Polymer. This dense layer is described as “crust” as it can be separated from the inner bulk of the monolith although both regions are connected. Crust is formed on both sides of the template when the flow direction is reversed as well as around the perimeter of the circular monoliths as plating bath solution leaks through the sides of the template disk. When these polymer/metal constructs are heat-treated, the resulting porosity of the dense layer (crust) is considerably smaller than that of the inner structure. Figure 14 illustrates the structure of crust after heat treatment at 600°C of a typical monolith with crust.

Figure 14: Structure of the skin produced on the top and bottom surface of the monoliths after heat treatment. Sample characteristics: [Ni]  =  0.13 M; [P] = 1.26 M; °C, °C/min;  min followed by cooling in air. (a) General appearances of top surfaces of metal disks after heat treatment. (b) Cross-section of the crust. (c) Large pore was formed by the fusion of numerous grains. All the core material in these grains was fused to form one extended core surrounding the large pores. (d) Details of how the core material and grain skin were shared. As a result, the core can be obtained in tubular form with very high porosity.

The thickness (crust) is dependent on the plating bath composition as well as on the deposition conditions. Furthermore, by using another nickel source (such as NiSO4), the dense crust layer can be completely eliminated.

It is possible to isolate the crust from the bulk and examine its structure separately. Figure 14(a) illustrates the surface appearance of the crust indicating the reduced porosity of the surface. The cross-section of the crust is shown in Figure 14(b) which shows that the porosity of the crust increases with distance from the surface. This is further illustrated in Figure 14(c) at larger magnification. Further investigation of the crust structure indicates that the pore walls are formed by the fusion of the grains which subsequently became hollow during heat treatment as seen in Figure 14(d). From Figure 14(d), it can also be observed that the pore walls (which can be described as capillaric) are also porous similar to those observed for the inner core structure.

EDX analysis of the crust shows that, within the crust, phosphorous level is very low and the surface of the crust is oxidized which explains the formation of hollow walls within the crust. The results are shown in Table 2.

Table 2: Energy dispersive X-ray analysis of the crust. Variation of Ni, O, and P concentration as a function of distance from the top surface of the crust. ([Ni] = 0.13 M; [P] = 1.26 M; = 600°C, = 10°C/min; = 60 min).
3.7. Inner Structure of Monoliths

The inner structures of the monoliths are examined by using SEM and they are illustrated in Figure 15 which shows the presence of large arterial pores and arterial interconnecting holes/windows (Figures 15(a) and 15(b)). The walls of the arterial pores are made from porous grains. The grain size decreases with increasing reducing agent concentration (compare Figures 15(b), 15(c), and 15(d)). The effect of reducing agent concentration on the pore size of the grains is illustrated in Figures 16(a)16(c). As seen from these SEM images, when the reducing agent concentration is [P] = 0.63 M or 1.26 M, grain surface porosity is similar but when [P] = 2.52 M, the grain surface porosity is smaller but less well defined.

Figure 15: Inner bulk structures of the monoliths showing the effect of reducing agent concentration. Experimental conditions: [Ni] = 0.13 M; °C, °C/min;  min followed by cooling in air. (a) General appearance of the bulk structure showing the presence of pore hierarchy with large arterial pores (interconnects/windows) with size range 10–30 μm and pore walls made from the porous capillaric structures of ca. 10 μm size. Reducing agent concentration [P] = 0.63 M, scale bar = 50 μm. (b) Sample as in Figure 15(a) at larger magnification. Scale bar = 10 μm. (c) Reducing agent concentration [P] = 1.26 M. Scale bar = 10 μm. (d) Reducing agent concentration [P] = 2.52 M. Scale bar = 10 μm.
Figure 16: Effect of reducing agent concentration on the surface pore structure of the arterial walls (in the form of porous undulating interconnecting capillaries). Experimental conditions: [Ni] =0.13 M; °C, °C/min;  min followed by cooling in air. Scale bar = 500 nm. (a) Reducing agent concentration, [P] = 0.63 M. (b) Reducing agent concentration, [P] = 1.26 M. (c) Reducing agent concentration, [P] = 2.52 M.
3.8. Overall Chemical Structure of Crust and Bulk

The chemical composition of the crust and the bulk were evaluated by XRD studies. In the first instance, the crust and the bulk of the monoliths were separated out and each part was subjected to XRD analysis. These results are shown in Figure 17 which indicates that Ni, NiO, and Ni3P are present in both the inner structure and crust but Ni2P and Ni12P5 are only present in the inner structure. See Figure 11 for the identification of the XRD peaks.

Figure 17: Superimposed XRD patterns of the crust and the inner bulk structure of the monolith. Processing conditions: [Ni] = 0.63 M; [P] = 1.26 M; °C, °C/min;  min followed by cooling in air. Ni, NiO, and Ni3P are present in both the crust and inner structure while Ni2P and Ni12P5 are only present in the inner structure.
3.9. Surface Area and Porosity

The surface area of the crust and the internal structure of the monoliths were measured using BET surface area analysis. After measuring the density of the these two parts (crust and bulk) of the monoliths, the specific surface area was calculated. Mercury intrusion technique was used to calculate the porosity. The results of the mercury intrusion technique for the inner structure and crust are shown in Figures 18(a) and 18(b), respectively.

Figure 18: Variation of the cumulative and incremental pore radius with pore size of the crust and bulk. Processing conditions: [Ni] = 0.63 M; [P] = 1.26 M; °C, °C/min;  min followed by cooling in air. (a) Crust. (b) Bulk of the monolith.

Figure 18 indicates that the porosity of the crust was 63.5% while the inner bulk structure had a porosity of 75.6%. From Figure 18, it can be seen that both the crust and the bulk of the monolith have bimodal pore size distribution. The arterial pores in the range 5–30 μm are in a majority while the second set of pores were in the range of 2–6 nm. Nanopores were more dominant in the bulk of the monolith. These results were further validated by measuring the BET surface area which also provides the range of pore sizes. The surface area of the crust and bulk of the monoliths described in Figure 18 and Table 3 were 0.238 m2/g and 0.626 m2/g, respectively. The pore size distribution obtained by BET surface area analysis was confined to the range of 2 to 160 nm (Table 3). Within this range, 17.7% of all the pores were between 2 to 6 nm, which verified the peak in Figure 18(b), obtained by the mercury porosimeter. These results for the crust and the bulk are shown in Table 3.

Table 3: Pore size distribution by surface area analysis. Processing conditions: [Ni] = 0.63 M; [P] = 1.26 M, = 600°C, = 10°C/min = 60 min followed by cooling in air.

4. Conclusions

Unlike the previous attempts to produce strong microporous monolithic metal foams from PolyHIPE Polymer template, a simple metal deposition solution was successfully used in a flow-enhanced deposition process which resulted in grain formation and faster deposition. The important element of this technique is the electroless deposition under flow while preventing deposition outside the template. This is achieved by the cyclic charge of deposition solution and washing solution, coupled with the reversal of the flow direction to obtain uniform distribution of metal deposition. The effects of flow can be summarized as follows:(a)Flow removes hydrogen generated during electroless deposition. Failure to remove hydrogen stops electroless deposition.(b)The deposition template is heated locally to accelerate the electroless deposition. However, the deposition solution is charged into the template at room temperature to prevent premature deposition in the flow path.(c)After deposition for a certain length of time, deionized water at high temperature (97°C) was passed through the deposition template in order to remove reduction products from the electroless deposition as well as heating the deposition template which is also heated externally to prevent heat losses.(d)As the deposition proceeds, the deposition cycle time can be increased due to the increase in the heat capacity of the monolith which allows faster deposition.(e)Combination of washing and heating at 90°C allows the removal of reaction products such as sodium chloride, thus removing such impurities from the final monolith.(f)Depending on the metal and reducing agent source, a dense layer is also formed on both sides of the monolith.Metal deposition from NiCl2 solution with NaH2PO2 as the reducing agent takes place in the form of grains. Depending on the composition of the metal deposition solution and the type of the reducing agent, metal grain size ranges from ca. 20 μm to 0.2 μm. These grains also form the walls of the large arterial pores. During heat treatment, these discrete grains undergo a solid state chemical reaction which results in the following:(a)Formation of a porous metallic Ni skin covers the unreacted inner core which contains mainly NiO and compounds.(b)These grains also undergo sintering, thus forming a continuous porous capillary-like (capillaric) structure constituting the walls of the arterial pores.(c)With further increase in the heat treatment, the solid state reaction continues and the inner structure of the capillaric walls becomes void thus increasing the overall porosity of the monoliths.(d)The dense layers on the surfaces of the monolith are transformed into a strong metal crust with reduced porosity compared with the bulk of the monolith which is sandwiched between the crusts. The pores of the crust have the same capillaric walls except the size of the arterial pores which are now reduced and the thickness of the walls is increased.These structures are also encountered in the human body where capillary-like conduits are formed. In the present case, the monoliths have a hierarchy of pores. Convective mass transfer is provided by the arterial pores which have porous capillaric walls, providing catalytic sites for reactions where the diffusional resistance to mass transfer is significantly reduced due to the presence of mesoscale pores between the convective and conductive mass transfer regions.

The mechanisms of electroless metal deposition and subsequent structure development during heat treatment are evaluated. The chemical and physical structures of the monoliths were evaluated. The formation of a strong top surface with reduced porosity (crust) in the monoliths can be desirable as it imparts mechanical strength as well as providing a self-filtering system in gaseous reactions due to the formation of a reduced porosity. The pore volumes of the crust and the bulk are large, 63.5% and 75.6%, respectively.

Conflict of Interests

The authors declare that there is no conflict of interests regarding this publication.

Acknowledgments

The authors acknowledge with thanks that this research was initially supported by Engineering and Physical Sciences Research Council (EPSRC) and Department of Trade and Industry of the UK (Grant no. GR/R59212) through a LINK project with additional grant provided by Intensified Technologies Incorporated (ITI) Ltd. through a Ph.D. support to Dr. Burak Calkan. Further research was funded by an EU FP7 Project (COPIRIDE CP-IP 228853-2), carried out at Newcastle University directed by Prof. G. Akay.

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