Processing and characterization of dual phase steel foam

Processing and characterization of dual phase steel foam

A. Gruttadauria^I; Davide Mombelli^I; E. M. Castrodeza^II; C. Mapelli^I

^IDipartimento di Meccanica, Politécnico di Milano. Via G. La Masa 34, 20156 Milano, MI, Italia. e-mail: [e-mail]; [e-mail]; [e-mail] ^IIDepartamento de Eng. Metalúrgica e de Materiais, COPPE-UFRJ, CP 68505, 21941-972 Rio de Janeiro, RJ, Brasil. e-mail: [e-mail]

ABSTRACT

Porous materials featuring cellular structures are known to have many interesting combinations of physical and mechanical properties. Some of them have been extensively used in the transportation field (i.e. balsa wood). Steel foams presented promising theoretical properties for both functional and structural applications in transportation, but processing of such a kind of foams is complex due to their high melting point. Recently a technique for processing Cu-based alloys open-cell foams through the molten metal infiltration of a leachable bed of amorphous SiO₂ particles was proposed. A variation of the proposed technique that uses SiC particles as space holder is now presented and was recently successfully applied for dual phase steel foam processing. Results from a processing of dual phase DP500 steel foams, including some morphological, micro-structural and mechanical characterization, are here presented.

Keywords: Dual phase steel, cellular metals, metal foams, silicon carbide.

1 INTRODUCTION

Based on their particular morphology, cellular metals and alloys offer an interesting mix of physical-chemical and mechanical properties. That makes these materials very attractive both for structural and functional applications [1, 2]. Cellular metals are now produced by several processes, including molten metal infiltration of a leachable bed of solid particles, also known as space holder [3, 4]. A recent work introduced the use of amorphous SiO₂ (silica-gel) beads as space holder for open-cell Cu-based foam processing through molten metal infiltration [5]. Once infiltrated, SiO₂ particles are dissolved by a wet solution of hydrofluoric acid (HF). Unfortunately this technique is not applicable for processing of steel foams, mainly due to the high melting point of steels (~1500 ºC). For overcoming this limitation it is proposed to use beta-SiC as space holder. SiC can withstand the infiltration efforts till 1800 ºC without problems and can be also dissolved by aqueous HF. On the other hand, the chemical stability of SiC at such temperatures diminishes the possibility of interaction among the molten metal and the space holder. Following this route highly homogeneous dual-phase steel foams featuring opened cell structure were processed. The proposed methodology is based on cheap commercial consumables and simple technology, focusing on low cost foams with interesting cost/benefit ratios. Based on the acquired scientific literature the proposed route represents the first attempt for applying SiC as space holder for steel foam processing.

Open-celled metal foams typically show low density, high surface vs. volume ratio, low stiffness and permeability to fluid flow [2, 3]. Based on these features they represent a suitable opportunity for the production of several components, i.e. elements to be inserted in sandwich systems, vibration damping components, filters, substrates for catalytic reactions, electrodes, porous media for biomedical applications, heat exchanging elements, etc [1, 4]. Dual phase steels are much used in the automotive field, for example in seats, bumpers and in reinforced shells. So the dual phase steel foam can found application in this field because of morphology and material properties.

2 EXPERIMENTAL

2.1 Space holder

During the foam processing the space holder was commercial Beta-SiC Vukopor S^® in the form of cylindrical foundry filters. Through EDS examination it was possible to observe that they are composed by approximately 90% in SiC and the other 10% in alumina and silica. The filters were available in three different porosities, being these 10, 20, and 30 pores per inch (ppi). An upper view of the filters is shown in Figure 1. Beta-SiC is virtually inert and has no known adverse and detrimental effects on the environment. The filters are normally used as foundry filters and are commercially available worldwide.

2.2 Wet chemical etching of Beta-SiC

Beta-SiC was dissolved by wet chemical etching in an aqueous solution of HF (25% vol.). In the literature it is possible to find several reactions for HF etching of SiC. The stoichiometric reaction is defined as [6]:

The highly porous morphology of Beta-SiC filters allows improving the dissolution kinetics by aqueous HF. According to our experience, stirring of HF solution also improves the dissolution velocity.

2.3 DP500 steel

Dual phase steels (DP) are high strength steels having a biphasic structure composed by a (soft) ferritic matrix containing a uniform dispersion of (hard) martensitic phase [7]. Ferrite gives to the material a good ductility while martensite ensures good mechanical properties. The mechanical properties of this kind of steel increased with the increasing in martensitic fraction, whereas the total amount of martensite in the alloy depends on the carbon content and on the thermomechanical treatment. The chemical compositions of the processed alloys, obtained by X-ray analysis, are shown in Table 1. Some typical properties of commercial DP500 steel are shown in Table 2, which are completely consistent with the values featuring the alloys applied in the experiments.

2.3.1 Determination of the critical points A_C1 and A_C3 for quenching

The biphasic structure of this kind of steels is obtained through intercritical quenching. During this thermal treatment the specimens are subjected to a temperature defined by the critical points A_C1 and A_C3, and then water-cooled [8]. The temperature A_C1 is the eutectoid temperature while A_C3 is defined as the temperature in which the α-γ phase transformation starts. These points depend on the chemical composition of the alloy and were evaluated through a DSC analysis. The report of this analysis is shown in Figure 2. From the DSC report it is clearly seen that for the analyzed alloy A_C1≅ 741 ºC and A_C3≅ 898 ºC. As a consequence, the temperatures chosen for the beginning of fast cooling were 770 ºC, 800 ºC, and 830 ºC.

2.4 Foam Preparation

The infiltration process was performed in a 10 kW centrifugal induction casting machine having a cylindrical alumina crucible. The infiltration temperature was controlled by a thermocouple placed into the molten metal. The SiC filters as space holder were placed into a graphite mold. Before reaching approximately 100 ºC above the melting temperature in the molten metal, the thermocouple was withdrawn, the induction main power is switched off, and the centrifuge is switched on. At this point the molten metal was forced into the mold by the centrifugal force, infiltrating into the space holder. After complete solidification and cooling the obtained solid (steel and space holder) was submerged in an aqueous HF bath (25% vol.) till complete SiC dissolution. The three processed foams having different porosities are shown in Figure 3.

2.5 Relative Density Calculation

The relative density of the final foam, that is the foam density to bulk density ratio, was calculated based on measurements of physical dimensions of the final (post-machined) cellular solid and on weight measurements. The same calculation could be also done through quantitative metallography by image processing. In this case some images were taken from the steel foam surfaces and analyzed through ImageProPlus software (Figure 4). The results from these two techniques were then compared. It is interesting to note that through image analysis it is also possible to calculate the surface to volume ratio, or specific surface density. Results of both calculations are shown in Table 3.

2.6 Microstructure

For microstructural analysis the samples were polished and immersed in Nital (5%) to reveal the boundary grains, and in Sodium Metabisulfite to reveal the martensitic islands. Micrographs from different quenched specimens showing different amounts of martensite were taken, similar to the presented in Figure 5.

In Figure 5 it is possible to see the alloy micro-structure after thermal treatment. The structural components are martensite (M), ferrite (F) and bainite (B). This kind of structure is predicted by Bain's curves [8].

In Figure 6 it is possible to see the different amounts of martensite (darker areas) due to different thermal treatments.

2.7 Compression Testing

A basic mechanical characterization of the DP500 foams was performed through uniaxial compression testing on prismatic specimens (12 by 12 mm in cross section and 18 mm in height). The specimens were tested in an electro-mechanical universal testing machine under displacement control at constant crosshead velocity (1 mm/min). For the Young's modulus evaluation some unloading-reloading cycles were performed during the tests. Figure 7 shows stress-strain records from the three different space holders (quenching temperature = 830 ºC)

As can be seen, all the specimens showed typical cellular metal stress-strain behavior. The records are comparable to results from metallic foams having similar relative densities [9, 10]. In all the cases the elastic modulus measured from the unloading-reloading cycle was close to 50 GPa, which is in the expected range according to theoretical models in literature [1]. Comparing the curves in Figure 7 and the results of relative density calculations from Table 3 it is also possible to see that, even for steel foams having the same relative density, the increasing on the porosity of the filters used as space holders promoted and increasing in the mechanical resistance of the foam. Based on the literature and from the point of view of the relative density, this behavior is unexpected and need to be further investigated.

3 CONCLUSIONS

Based on the experimental results it is possible to conclude:

1. The production of open-celled metal foams of DP500 steel by molten metal infiltration of SiC filters then leached by aqueous HF has been experimentally demonstrated.

2. The space holder (beta-SiC filters) remained stable in shape and dimensions during liquid steel infiltration (processing temperature ~ 1650 ºC). Because of the high chemical stability of SiC no interaction with the metallic system during liquid infiltration has been found.

3. The resulting metal foams had a relative density of 0.65 and all the observed cells are open and interconnected.

4. The compression tests demonstrate that the steel foam specimens show the typical stress-strain behavior of cellular metals.

5. Different degrees of porosity of the SiC filters used as space holders permitted to obtain different mechanical properties and different surface-volume ratio, even with the same final relative density.

4 REFERENCES

Data de envio: 25/03/2010

Data de aceite: 02/07/2010

Autor Responsável: Andrea Gruttadauria

• [1] ASHBY, M.F., EVANS, A., FLECK, N.A., GIBSON, L., HUTCHINSON, J.W., WADLEY, H., "Metal foams: a design guide", Butterworth-Heinemann, 2000.
• [2] BANHART, J., "Manufacture, characterization and application of cellular metals and metal foams", Progress in Materials Science, v. 46, pp. 559-632. 2001.
• [3] DEGISCHER, H.P., KRISZT B., (Eds), Handbook of Cellular Metals: Production, Processing, Applications, Wiley-VCH, 2002.
• [4] WADLEY, H.N.G., "Cellular metals manufacturing", Advanced Engineering Materials, v. 4, pp. 726-733, 2002.
• [5] CASTRODEZA, E.M., MAPELLI, C. Processing of brass open-cell foam by silica-gel beads replication Journal of Materials Processing Technology, v. 209, n. 11, pp. 4958-4962, 2009.
• [6] VILLAVECCHIA, V. EIGENMANN, G., "Nuovo dizionario di merceologia e chimica applicata", v. 6. Hoepli, 1996.
• [7] NICODEMI, W., Acciai e leghe non ferrose, Zanichelli, 2004.
• [8] NICODEMI, W., Metallurgia: principi generali, Zanichelli, 2004.
• [9] POLLIEN, A., CONDE, Y., PAMBAGUIAN, L., MORTENSEN, A., "Graded open-cell aluminum foam core sandwich beams", Materials Science and Engineering A, v. 404, pp. 9-18, 2005.
• [10] GAILLARD, C., DESPOIS, J.F., MORTENSEN, A., "Processing of NaCl powders of controlled size and shape for the microstructural tailoring of aluminium foams", Materials Science and Engineering A, v. 374, pp. 250-262, 2004.

Publication Dates

• Publication in this collection
  27 Aug 2010
• Date of issue
  2010

History

• Accepted
  02 July 2010
• Received
  25 Mar 2010