Production, Characterization, and Applications of Porous MaterialsView this Special Issue
Research Article | Open Access
Alexander Martin Matz, Bettina Stefanie Mocker, Daniel Wyn Müller, Norbert Jost, Gunther Eggeler, "Mesostructural Design and Manufacturing of Open-Pore Metal Foams by Investment Casting", Advances in Materials Science and Engineering, vol. 2014, Article ID 421729, 9 pages, 2014. https://doi.org/10.1155/2014/421729
Mesostructural Design and Manufacturing of Open-Pore Metal Foams by Investment Casting
The present paper describes the manufacturing process of open-pore metal foams by investment casting and the mesostructural/morphological evolution resulting from a new technique of modifying the precursor. By this technique, the precursor is coated with a polymer layer whereby a thickening of the struts occurs. Relative densities in the range of of open-pore metal foams can be achieved with high accuracy. The samples investigated have pore densities of ppi, 10 ppi, and 13 ppi. The relevant processing parameters needed for a homogenous formation of the polymer layer are determined for two different coating materials and the resulting open-pore foam’s mesostructure is characterized qualitatively and quantitatively. The alloy used for investment casting open-pore metal foamsis AlZn11. The microstructural evolution of these foams is evaluated as a function of the mesostructure. Differences in the microstructure are observed for foams with low and high relative densities and discussed in terms of cooling subsequent to investment casting.
Open-pore metal foams possess attractive properties due to their highly porous and light weight structure in combination with their base material. Hence, this group of materials is of great interest for different fields of application, such as in the sectors of heat engineering [1, 2], biomedical engineering [3, 4], electrical energy storage [5, 6], or lightweight design [7, 8].
Common processing techniques for manufacturing open-pore metal foams are based on sintering or casting [9, 10]. The method used in this investigation is a modified investment casting process which offers great advantages due to a targeted adaptation/tailoring of the relative density , structure of the cells, geometry, and alloy composition for any specific application. The open-pore metal foam also acts as an exact copy of the precursor—whereby also highly complex component geometries are possible—, and regular structures and pore-size distributions can be achieved [11–13]. Typically, a reticulated polymer foam  is used as a precursor. In many investigations (cf. [15–17]) these polymer foams are used for the metal foam production in as-received conditions leading to a relative density of for samples in a range of pore densities of 10 ppi ≤ ≤ 40 ppi. However, for some applications such a low metallic portion is not adequate and hence the relative density needs to be enhanced. One common method of doing this is by thickening the struts of the polymer foam by dunking it into liquid wax [16, 18–20]. However, this method requires a high level of experience to achieve a homogenous structure in a repetitive accuracy and to avoid blocking of the pores [18, 19]. Furthermore, thickening the struts can just be conducted within narrow confines.
For these reasons an alternative method for a mesostructural design of open-pore metal foams is developed. Using this method any required relative density can be achieved through a homogenous thickening of the struts. The thickening is a thermal-additive process where the struts of the samples are firstly coated with an adhesive layer, followed secondly by powdering them with polymer granules and thirdly treating the samples above the melting temperature of the polymer granules. In the present study the basics of the modified investment casting process for open-pore metal foams are described briefly. Furthermore, the influence of treatment time , treatment temperature , diameter of polymer granules , and quantity of treatment runs on the open-pore metal foam’s mesostructure and its relative density is investigated. The microstructural evolution resulting in the investment casted open-pore metal foams is identified.
2.1. Strut Thickening
The precursors for the modified investment casting process used in this investigation are commercial reticulated open-pore polymer foams (brand name “Regicell”) with different pore densities of ppi, 10 ppi, and 13 ppi, obtained from Foampartner Reisgies Schaumstoffe GmbH in Leverkusen, GER. These as-received samples have a relative density of representing the reference condition for this study. The thickening of the open-pore polymer foam’s struts as a three-step process is achieved via the following:(1)spray coating with a synthetic elastomer based aerosol glue with the brand name “Scotch-Weld Spray 77” from 3 M Deutschland GmbH in Neuss, GER as an adhesive layer in an apparatus with a rotating sample holder at standard conditions, resulting in a homogenous distribution of the adhesive on the polymer foam’s surface,(2)powdering with polymer granules in diameters of μm (PG1) of the type Abcite X1060 from DuPont Polymer Powders Switzerland Sàrl in Bulle, CH and μm (PG2) of the type FA-7035-SG412 from Ganzlin Beschichtungspulver GmbH in Ganzlin, GER in the abovementioned apparatus at standard conditions, resulting in a homogenous distribution of the polymer granule on the polymer foam’s spray coated surface, and(3)thermal treatment of the coated samples in a batch furnace at °C for min (PG1) or min (PG2), respectively, followed by cooling at standard conditions.
2.2. Mold Preparation
The precursor in its dimensions of mm3 is mounted on a gate with a feeding system made of wax which represents the pattern in its final state (Figure 1). Thereupon this pattern is placed in a steel cuvette. The molding material is a sulfate-bonded investment, supplied by SRS Ltd. in Riddings, GB, which is mixed with water and stirred to form a ceramic slurry which gets evacuated until reaching a residual pressure of mbar to minimize trapped air. After drying for h at standard conditions, the mold is heated in an incineration furnace in a multistep cycle, shown in Figure 2. The first step at a temperature of °C is conduced to counteract the hygroscopicity. In a second step at °C the gating system is dewaxed and in a third step at °C the polymeric precursor is pyrolyzed. The final drying and hardening of the mold is achieved at °C in a last step followed by furnace cooling. Due to phase transitions and volume changes, these temperatures are kept for at least h and a heating rate of max. K/min is chosen to prevent crack formation.
The alloy used for all castings in this study is AlZn11. The starting materials are Al granules with a purity of and Zn pieces with a purity of from Chempur Feinchemikalien und Forschungsbedarf GmbH in Karlsruhe, GER. The metallurgical processing of the open-pore metal foam is carried out by centrifugal casting. Both, Al and Zn in the mass ratio , are placed in a preheated crucible and inductively melted under vacuum. At a temperature of °C, the casting is induced and the mold, which was preheated at °C for h, is infiltrated by the melt. After min, the mold is removed from the casting machine whereupon it is quenched in water (°C). In a last step the samples are cleaned by water jet and Tetranatriumethylendiamintetraacetate (C10H12N2Na4O8).
2.4. Mesostructural Characterization
The mesostructure of open-pore foams includes the geometric parameters of the foam-like structure such as strut width and cell diameter and general foam parameters including pore density and relative density . To determine the effects of strut thickening on the foam’s mesostructure, the digital microscope “VHX-500FD” from Keyence NV/SA in Mechelen, BEL, is used. The conducted investigations are focused on the degree of wetting of the struts by the polymer layer and the interaction of successively added polymer granules, which is analyzed qualitatively. Furthermore, quantitative correlations of polymer granules diameter, strut width , and relative density are deduced. The relative density, which is defined as the ratio of the foam’s mass and the mass of a solid body with the same base material in identical outer dimensions, is governed by weighing the open-pore AlZn11 foam sample with a microbalance (type “AB104” from Mettler-Toledo GmbH in Gießen, GER).
2.5. Microstructural Characterization
To evaluate the influence of the relative density on the microstructural evolution of the open-pore AlZn11 foams, microscopical studies are carried out. Therefore, the metal foam samples are partitioned at a distance of mm to the deadhead by a wet disc grinder. The single sample pieces are embedded in a cold polymerizing plastic (Scandiplex in addition to Varioplex from Scan-Dia Hans-P. Tempelmann GmbH & Co.KG in Hagen, GER) for further mechanical sample preparation. This is carried out by an automatic grinding/polishing machine (TegraPol-21 from Struers GmbH, GER) in two main steps, namely, wet grinding and diamond polishing as well as chemic-mechanical polishing, as described in  in detail. Subsequent to these preliminary steps, electrolytic etching according to Barker is applied (cf. ). The microscopical studies of the prepared samples are obtained by a light-optical microscope (DMI 500 M from Leica GmbH, GER) at amplifications of in polarized light for evaluating the microstructural morphology.
3. Results and Discussion
In the following, the results of the experimental investigations are pointed out. The processing quality is examined to determine the optimum processing parameters for strut thickening and the mesostructural evolution is characterized by quantifying mesostructural parameters. Moreover, the microstructural evolution in consequence of the varied mesostructure is evaluated for the investment casted foam samples.
3.1. Processing Quality
The key factors for the mesostructural design of open-pore metal foams are the processing parameters of the thermal-additive method for thickening the struts. Particularly temperature and time of thermal treatment affect the quality of the precursor considerably.
As basic conditions for identifying the optimum thermal treatment temperature , the chosen temperature needs to exceed the melting temperature of the polymer granules or coating material, respectively, and needs to be below the temperature where the skeletal structure of the polymer foam collapses, . According to manufacturer’s data and DSC measurements the relevant temperatures for both polymer granules and the polymer foam are determined. The melting temperature is °C for PG1 and °C for PG2. The foam proves to be inherently stable until reaching a temperature of °C.
In a series of experiments, thermal treatment in a temperature range of 120°C ≤ ≤ 200°C was conducted. The results show at °C that the desired effect of strut thickening can be achieved. However, the process needs up to half an hour to be finished. At °C, the process can be accelerated which is yet coupled with the negative side effect of mass stratification of the polymer layer due to gravitation and a nonhomogenous relative density within the foam, respectively. The best results are determined to be at °C for PG1 and PG2.
The required duration of the thermal treatment is investigated in another series of experiments. For this purpose several polymer foam samples are prepared using the first and second process step mentioned in Section 2.1 and thermal treatment at °C in a time range of 4 min ≤ ≤ 14 min is applied, whereby all minute samples are taken and qualitatively analyzed by the digital microscope. The evolution of strut thickening is shown in Figure 3 which demonstrates the formation of a polymer layer by agglomeration of the single powder granules as a function of time leading to the result of a homogenous layer after min for PG1. Using PG2, a homogenous layer is formed after min.
3.2. Mesostructural Evolution
To quantify the mesostructural evolution aroused by the thermal-additive process for strut thickening, all the polymer foam samples are characterized in consideration of the overall mesostructural key parameter: the relative density . It can be observed that is in a linear relationship as a function of the quantity of thermal treatment runs , as shown in Figure 4. By comparing the pore densities of the foam samples, it can be seen that the increase in relative density with each treatment run rises by a higher pore density or a smaller cell diameter , respectively. An increase of pore density by ppi leads to an approx. higher relative density per treatment .
This can be explained by considering the specific surface area of the foam which is available for coating by the polymer powder. Using the example of a simple expression for the specific surface area (see [23, 24]) with as a constant and as the cell diameter and the relation between the relative density and cell diameter with as another constant and inserting (2) in (3) leads to the relation between the specific surface area and pore density with the consequence of a higher relative density by increasing the pore density.
As another mesostructural parameter, the strut width is characterized by measuring the distance between the outer edges of a single strut, as the example depicted by Inayat et al. . In each sample batch with identical pore density and identical quantity of thermal treatment runs , at least 150 single struts are measured to achieve a representative mean value, since the mesostructural parameters, such as the strut width, are normally distributed . For a sample batch with ppi, which was treated by runs with PG1 (resulting in a relative density of ), the strut width distribution is shown in Figure 5. The mean value of the strut width is mm and the standard deviation amounts to mm for this foam. The corresponding strut widths resulting for the other samples coated by PG1 are listed in Table 1 and the ones coated by PG2 are listed in Table 2.
The increase in strut width shows, similarly to the relative density , that it is in a linear conjunction with the quantity of thermal treatment runs and can be expressed by in which the strut width resulting for any thermal treatment run increases by the product of the polymer granule’s particle diameter and the quantity of thermal treatment runs . However, this expression is, in this investigation, only valid for the polymer granule PG1. For the other polymer granule, PG2, the function results. This can be justified by the small particle diameter of PG2 (compared to PG1) which forms just a thin polymer layer on the foam’s surface in conjunction with the fact that the polymer foam in reference conditions or untreated conditions (), respectively, exhibits a strut cross section which can be described by a concaved equilateral triangle (Plateau border). Treating the polymer foam by , its strut cross sections result in an equilateral triangle (Figure 6(a)) and by the strut cross sections become shaped as a convex equilateral triangle (Figure 6(b)). In all three conditions, , 1, and 2, the outer tips of the plateau border remain as the outer edges by applying the above named method for measuring, resulting in an identical strut width . In comparison, a strut of a polymer foam treated by is shown in Figure 6(c) at which the strut cross section emerges in a circular-like shape.
Furthermore, it can be deduced from Table 1 that a lower pore density leads to a higher strut width for each treatment run. This fact results due to the already higher strut width of low-pore density foams in untreated or as-received conditions as the consequence of a lower amount of struts in total by an approx. identical relative density .
3.3. Microstructural Evolution
The evaluation of the microstructural evolution as a result of the varied mesostructural parameters is investigated for the open-pore AlZn11 foams with a pore density of ppi. The sample illustrated in Figure 7(a) represents the reference conditions and is hence not strut thickened (). The ones shown in Figures 7(b) and 7(c) are strut thickened by a quantity of thermal treatment runs and with PG1. The increase in strut width with each treatment run can be seen clearly through these macroscopic photographs.
Sample preparation and metallographic analysis are applied as mentioned in Section 2.5 whereby the investigated sections of the foam represent a strut orientated parallel to the sample plane. The micrograph illustrated in Figure 8(a) shows a strut in untreated conditions () with two comparatively large grains. In contrast, in the investigated sections of the samples strut thickened with PG1 by (Figure 8(c)), a dominant dendritic microstructure with small grains is visible. The samples treated by (Figure 8(b)) partly exhibit a distinctive dendritic microstructure and there are partial zones at which no casting structure is evident.
These differences in microstructure can be explained by the fact that after solidification in the mold, the cooling rate is higher in foam samples with a higher relative density since a higher volume fraction of AlZn11 is existent and more heat can be dissipated due to the high thermal conductivity of an Al alloy. In contrast, the thermal conductivity of the plaster is much smaller but its heat capacity is much higher which leads to a lower heat dissipation in foams with small relative densities .
4. Summary and Conclusion
In the present study, a new method of thickening the struts is proposed to achieve defined relative densities of investment-cast open-pore metal foams in the range of . This method is a three-step process, where the open-pore polymer foams need to get spray coated by an adhesive layer, afterwards powdered with polymer granules, and thermally treated to achieve a precursor in its required relative density with homogenous struts. Subsequently, the common procedure of investment casting has to be applied.
For evaluating the processing quality of the strut thickening process, two polymer powders with different particle diameters μm (PG1) and μm (PG2) are investigated. By varying temperature and time of thermal treatment, the optimum parameters for a homogenous mesostructure of the foam and for a uniform formation of the polymer layer are identified. The processing temperature is determined to be at °C for both powder types. The formation of the polymer layer occurring by agglomeration of the powder granules is achieved after min for PG1 and min for PG2.
With respect to the mesostructural parameters resulting from this method, the relative density and strut widths as a function of the quantity of thermal treatment runs are determined for open-pore foams with pore densities of ppi, 10 ppi, and 13 ppi. A linear relationship between and is observed whereby the increase of with each treatment run is more dominant as the pore density is higher which is a consequence of the foam’s specific surface area . Furthermore, the strut widths also show a linear dependency on the quantity of thermal treatment runs in compliance with the requirement of a circular-like shaped strut cross section which can be ascribed by the product of the polymer powder’s particle diameters and quantity of thermal treatment runs in addition to the strut width of the foam in untreated conditions .
The microstructural evaluation indicates differences in the microstructure of the open-pore AlZn11 foams as a function of the mesostructural parameters. A dominant dendritic structure in foams with high relative densities is observed whereas no indications for that are evident in foams with low relative densities. The reason might be a higher cooling rate resulting from the higher metal portion with its high thermal conductivity in foams with high relative densities.
Conflict of Interests
The authors declare that there is no conflict of interests regarding the publication of this paper.
The authors gratefully acknowledge the European Union/European Fund for Regional Development and the federal state Baden-Württemberg for financial support. Moreover, they wish to thank Foampartner Reisgies Kunststoffe GmbH, especially H.-J. Stolz, DuPont Polymer Powders Switzerland Sàrl, and Ganzlin Beschichtungspulver GmbH for material support. The authors would also like to express their gratitude to E. Drotleff, R. Burkart, and J. Aktas for assistance concerning experimental tasks.
- X.-H. Han, Q. Wang, Y.-G. Park, C. T'Joen, A. Sommers, and A. Jacobi, “A review of metal foam and metal matrix composites for heat exchangers and heat sinks,” Heat Transfer Engineering, vol. 33, no. 12, pp. 1–20, 2012.
- C. Y. Zhao, “Review on thermal transport in high porosity cellular metal foams with open cells,” International Journal of Heat and Mass Transfer, vol. 55, no. 13-14, pp. 3618–3632, 2012.
- Y. Er and E. Unsaldi, “The production of nickel-chromium-molybdenum alloy with open pore structure as an implant and the investigation of its biocompatibility in vivo,” Advances in Materials Science and Engineering, vol. 2013, Article ID 568479, 7 pages, 2013.
- D. W. Müller, A. M. Matz, and N. Jost, “Casting open porous Ti foam suitable for medical applications,” Bioinspired, Biomimetic and Nanobiomaterials, vol. 2, no. 2, pp. 76–83, 2013.
- P. S. Liu, T. F. Li, and C. Fu, “Relationship between electrical resistivity and porosity for porous metals,” Materials Science and Engineering A, vol. 268, no. 1-2, pp. 208–215, 1999.
- Q.-X. Low, W. Huang, X.-Z. Fu et al., “Copper coated nickel foam as current collector for H2S-containing syngas solid oxide fuel cells,” Applied Surface Science, vol. 258, no. 3, pp. 1014–1020, 2011.
- M. F. Ashby, “The mechanical properties of cellular solids,” Metallurgical Transactions A, vol. 14, no. 9, pp. 1755–1769, 1983.
- H. Kanahashi, T. Mukai, Y. Yamada et al., “Experimental study for the improvement of crashworthiness in AZ91 magnesium foam controlling its microstructure,” Materials Science and Engineering A, vol. 308, no. 1-2, pp. 283–287, 2001.
- G. J. Davies and S. Zhen, “Metallic foams: their production, properties and applications,” Journal of Materials Science, vol. 18, no. 7, pp. 1899–1911, 1983.
- H. N. G. Wadley, “Cellular metals manufacturing,” Advanced Engineering Materials, vol. 4, no. 10, pp. 726–733, 2002.
- S. F. Fischer, M. Thielen, R. R. Loprang et al., “Pummelos as concept generators for biomimetically inspired low weight structures with excellent damping properties,” Advanced Engineering Materials, vol. 12, no. 12, pp. B658–B663, 2010.
- A. Jung, Offenporige, nanobeschichtete hybrid-metallschäume: herstellung und mechanische eigenschaften [Ph.D. dissertation], Saarland University, Saarbrücken, Germany, 2011, (German).
- U. Krupp, A. Ohmdorf, T. Guillén et al., “Isothermal and thermomechanical fatigue behavior of open-cell metal sponges,” Advanced Engineering Materials, vol. 8, no. 9, pp. 821–827, 2006.
- R. A. Volz, “Reticulated polyurethane foams and process for their production,” US3171820, 1965.
- S. F. Fischer, P. Schüler, C. Fleck, and A. Bühring-Polaczek, “Influence of the casting and mould temperatures on the (micro)structure and compression behaviour of investment-cast open-pore aluminium foams,” Acta Materialia, vol. 61, no. 14, pp. 5152–5161, 2013.
- L. C. Wang and F. Wang, “Preparation of the open pore aluminum foams using investment casting process,” Acta Metallurgica Sinica (English Letters), vol. 14, no. 1, pp. 27–32, 2001.
- Y. Yamada, K. Shimojima, Y. Sakaguchi et al., “Processing of an open-cellular AZ91 magnesium alloy with a low density of 0.05 g/cm3,” Journal of Materials Science Letters, vol. 18, no. 18, pp. 1477–1480, 1999.
- M. Grohn, Feingegossene metallschwämme als preform zur schmelzflüssigen infiltration [Ph.D. dissertation], Shaker, Aachen, Germany, 2005, (German).
- C. A. Hintz, Präzisionsgegossene metallische schwammstrukturen [Ph.D. dissertation], Shaker, Aachen, Germany, 2003, (German).
- L. Wang, H. Li, F. Wang, and J. Ren, “Preparation of open-cell metal foams by investment cast,” China Foundry, vol. 2, no. 1, pp. 56–59, 2005.
- B. S. Mocker, U. Christian, A. M. Matz, N. Jost, and C. Siegle, “Mikrostrukturelle charakterisierung im feingussverfahren hergestellter offenporiger metallschäume aus aluminium-silizium-legierungen,” Fortschritte in der Metallographie, vol. 45, pp. 279–284, 2013 (German).
- G. Petzow, Metallographic Etching: Techniques for Metallography, Ceramography, Plastography, ASM International, Materials Park, Ohio, USA, 2nd edition, 2001.
- A. Inayat, H. Freund, T. Zeiser, and W. Schwieger, “Determining the specific surface area of ceramic foams: the tetrakaidecahedra model revisited,” Chemical Engineering Science, vol. 66, no. 6, pp. 1179–1188, 2011.
- J. Vicente, F. Topin, and J.-V. Daurelle, “Open celled material structural properties measurement: from morphology to transport properties,” Materials Transactions, vol. 47, no. 9, pp. 2195–2202, 2006.
Copyright © 2014 Alexander Martin Matz et al. 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.