Reactively Synthesized Porous Ti₃SiC₂ Compound and Its Mechanical Properties with Different Apertures

Abstract

Reactively synthesized porous Ti₃SiC₂ with different pore sizes was prepared using TiH₂, Si and graphite powders as starting materials. The effect of pore size on the flexural stress–strain relationship, bending strength and flexural elastic modulus were investigated. The results show that the synthesized porous Ti₃SiC₂ intermetallic compounds have a characteristic of a high-purity MAX phase with typical laminate microstructure. When the average pore size decreases from 21.8 to 2.1 μm, the volume content of Ti₃SiC₂ phase ranges from 96.9% to 99.6%, and the porosity is in the range of 49.9% to 54.1%. The flexural stress–strain curves of porous Ti₃SiC₂ show a characteristic of two stages of elastic deformation and fracture. The flexural modulus is in the range of 13 to 70 GPa, which increases rapidly with further decrease of the pore size. A relation similar to the Hall–Petch equation between the mechanical property and the pore size was investigated for the porous material.

1. Introduction

Porous Ti₃SiC₂ [1,2,3,4,5], as a new type of porous intermetallic compound with MAX phase, has the performance advantages of porous metals and ceramics, such as excellent environmental corrosion resistivity [1], high temperature stability [2] as well as good thermal shock resistance and machining performance [3]. In addition, porous Ti₃SiC₂ prepared by reactive synthesis of elemental powders [6,7,8] also shows a good open-pore structure and pore-structure stability [1,2].

Compared with dense material, the mechanical strength of porous material decreases significantly [9,10,11]. The mechanical model [8,12], microstructure [8] and the effect of porosity on mechanical properties [12,13] of porous Ti₃SiC₂ have been investigated, which is classified as a kinking nonlinear elastic solid [14,15]. The strength and stiffness of porous Ti₃SiC₂ decrease with increasing the porosity [12]. In the case of porous MAX phases prepared with space holder with the size of several hundred microns [4,5,13], it was found that the porosity and the pore type were the main factors influencing the elastic properties [13]. On the other hand, porous Ti₃SiC₂, due to its unique pore structure and material properties, can be well applied in biological separation [16], chemical filtration and hydrometallurgy [1], etc., where the mechanical properties of porous materials should meet the requirements of the working conditions [3]. The pore size is an important pore structure parameter determining the filtration accuracy, and its influence on mechanical properties is an important design basis for porous materials in the filtration application. To the best of our knowledge, investigations on the effect of pore size of porous Ti₃SiC₂ on its strength and stiffness have not been reported so far.

Currently, the relationship between porosity and strength of porous materials can be simulated by the Barsen equation [17]. The Hall–Petch equation can be used to reveal the relation between the strength or hardness and the grain size of single phase material [18,19,20] or composite material [21,22,23]. In this work, a series of porous Ti₃SiC₂ compounds with different pore sizes and approximately the same porosities and phase purities were prepared by the reactive synthesis of elemental powders through a pressure less sintering process. The Hall–Petch relationship between the pore size and the bending strength was studied, and the effect of pore size on the flexural modulus of porous Ti₃SiC₂ was discussed.

2. Experimental Procedure

Porous Ti₃SiC₂ compounds were prepared using commercially available TiH₂, Si and graphite powders as the starting materials by a pressure less sintering process [1]. TiH₂ powder can be prepared by hydrogenation of titanium sponge and subsequent mechanical pulverization process [24]. The median diameter of TiH₂ powder is in the range of 10 to 180 μm, which was utilized to fabricate porous material with different pore sizes. The median diameters of Si and graphite powders are in the ranges of 10–15 μm and 5–10 μm, respectively. The purities of all the used powders were above 99.0 wt.%, and were mixed according to the atomic ratio of Ti, Si, and C of 3:1.2:2. An excess of 20% Si was added to compensate for its high temperature volatilization loss [1,3]. Analytically pure stearic acid was used as forming agent and lubricant. Cold forming procedure was carried out by means of uniaxial die pressing with the pressure of 100 MPa. The prepared compacts are cuboids with dimensions of length, width and thickness of 30 mm, 6–7 mm and 2–3 mm, respectively. A multi-stage heating process under vacuum was utilized for the sintering of compacts [3]. The sintering procedure diagram is shown in Figure 1. The low-temperature sintering process at 350 °C is designed to decompose and remove the organic additives from the compacts, which is followed by a heating stage at 650 °C to dehydrogenate TiH₂. At the intermediate sintering stage at 1000 °C, the binary intermediate phases including TiC and Ti₅Si₃ are gradually formed through the solid phase diffusion [3,6], which is conducive to the subsequent synthesis of Ti₃SiC₂ [3]. The final sintering temperature is 1350 °C for 3 h with the vacuum pressure of 10⁻¹–10⁻³ Pa. The heating rate is controlled at 5–10 °C/min. After the pressure less sintering, the compacts are cooled with the furnace.

The phase compositions of the compacts after sintering at 1350 °C for 3 h were analyzed by X-ray diffraction (XRD: Dmax 2500VB, Tokyo, Japan) with a Cu Kα source at room temperature. The corresponding XRD data processing and analysis was carried out by Jade5 software (MDI, California, USA). The mechanical properties and the relation between flexural stress and strain of porous Ti₃SiC₂ were measured according to the three point flexural test by an electric servo-hydraulic material test system (Instron3369, Instron Ltd., High Wycombe, UK). The sintered compacts with the rectangular section mentioned above were used as the samples for the bending strength test, in which the span and the displacement rate are 25 mm and 0.02 mm/min, respectively. The mechanical strengths are the average of the three replicates used. The pore size was determined by the bubble point method (FBP-III) [6]. The open and overall porosities were calculated through the pycnometry method.

3. Results and Discussion

The XRD patterns of porous Ti₃SiC₂ with three different average pore sizes are shown in Figure 2. The phases of these porous materials are composed of Ti₃SiC₂ phase (a = 3.062 Å and c = 17.637 Å, Space Group P63/mmc, PDF 40-1132) and a small amount of TiC impurity phase (a = 4.327 Å, Space Group Fm-3m, PDF 65-0242). According to the standard additive method [25], the Ti₃SiC₂ phase volume contents of the porous compounds with average pore sizes of 2.1, 12.9 and 21.8 μm have been calculated to be 99.6%, 98.8% and 96.9%, respectively, showing a high-purity characteristic. The MAX phase content of porous Ti₃SiC₂ increases to a certain extent as the pore size reduces. The phase composition of porous Ti₃SiC₂ compounds prepared by reactive synthesis has been investigated to be influenced by the raw material type [1], the synthesis parameters [3], the material composition and alloying elements [7] and the material granularity [16]. The addition of TiH₂ was proved to improve the phase purity of the synthesized Ti₃SiC₂ MAX phase, which was attributed to the low oxygen content and high reactivity of elemental Ti generated from the dehydrogenation of TiH₂ [1,3].

In the preparation process of porous Ti₃SiC₂ by the reactive synthesis of TiH₂, Si and graphite, the pore size of the resultant porous material has a strict linear relation with the powder particle size of TiH₂, and the porosity is kept essentially constant when the pore size changes [6]. Therefore, the pore size of porous Ti₃SiC₂ can be adjusted by changing the powder size of TiH₂. In fact, the synthesized porous Ti₃SiC₂ in this work has the average pore size in the range of 2.1–21.8 μm with the open and overall porosities in the ranges of 44.6%–48.5% and 49.9%–54.1%, respectively. The decrease of pore size means the increase of specific surface area of the reactant under the condition that porosity is basically constant, which helps to enhance the surface diffusion during the synthesis process.

Figure 3 reveals the pore structure morphology and the lamellar microstructure of porous Ti₃SiC₂. The synthesized Ti₃SiC₂ compound has the characteristics of rich porous structure and high specific surface area, as shown in Figure 3a and b with the average apertures of 6.2 μm and 3.0 μm, respectively. A large number of interconnected pores are generated in the sintered compact with the aperture at the micron level. A few coarse pores exist locally, which is related to the original particle clearance in the compacts [7]. The prepared Ti₃SiC₂ phase skeleton generally has a smooth surface, which is conducive to the permeability of the porous material. Further observations reveal that the Ti₃SiC₂ grains exhibit obvious lamellar characteristic with the grain size in the range of several microns (Figure 3c), which is a typical microstructure feature of the reactively synthesized MAX phase [1,2,3].

Figure 4 shows the relation between the flexural stress and strain for porous Ti₃SiC₂ with different average pore sizes. The variation rate of flexural stress with strain increases with decreasing the pore size. All the stress–strain curves show a typical elastic deformation stage directly followed by a fracture stage. However, the flexural stress increases nonlinearly with increasing strain, which is mainly attributed to the deformation of the MAX phase as a kinking nonlinear elastic solid through the formation of regular and incipient kink bands [12].

Figure 5 shows the relation between the bending strength and the average pore size of porous Ti₃SiC₂. The bending strength increases in a nonlinear manner with decreasing the average pore size (Figure 5a). As the aperture decreases from 21.8 to 2.1 μm, the bending strength increases from 22 to 89 MPa. Through data fitting, the relationship between them is as follows:

$$\mathsf{\sigma }=\mathrm{k}·{\mathrm{d}}^{-\mathsf{\lambda }}$$

(1)

where σ and d are the bending strength (MPa) and the average pore size (μm) of the porous material, respectively. k and λ are the constants with the values of 154.04 and 0.56, respectively. The determination coefficient R² of the fitting relation equation is 0.92. Given λ is close to 0.5, further relationship between σ and d^−0.5 is investigated, as shown in Figure 5b. It is observed that σ increases linearly with d^−0.5. Through data fitting, the relationship between them is as follows:

$$\mathsf{\sigma }={\mathsf{\sigma }}_0+\mathrm{k}·{\mathrm{d}}^{-\frac{1}{2}}$$

(2)

where σ₀ and k are the constants with the values of 1.60 MPa and 135.48 MPa·μm^1/2, respectively.

The determination coefficient R² of the fitting relation equation is 0.94, which shows a higher fitting degree than Equation (1). Equation (2) is the Hall–Petch equation reflecting the relationship between the microstructure parameter and the mechanical property [20,21]. The result indicates that the influence of the pore size on the strength of the reactively synthesized porous Ti₃SiC₂ compound can be described by the Hall–Petch equation under the condition of approximately the same porosities and phase purities. In fact, a similar linear relationship between strength and reciprocal square root of the pore size was also found in porous alumina ceramics [26]. As the main component of the porous material, the pore can be approximately regarded as a phase in composite material. The decrease of pore size weakens the size factor that causes stress concentration [27], which is conducive to the improvement of material strength. On the other hand, the content of MAX phase in the sintered compacts increases with decreasing the pore size (Figure 2). Compared with Ti₃SiC₂ phase, TiC impurity phase has higher hardness and brittleness. Under the action of external load, this kind of hard and brittle impurity phase can often cause the stress concentration, which results in the decrease of the strength of the material. Therefore, the synthesis of Ti₃SiC₂ phase with high purity has always been the focus of researchers [1,3,25].

In this work, the pore size of porous Ti₃SiC₂ compounds has been adjusted by changing the particle size of TiH₂ powder. In the reactive synthesis process, there is a strict linear relationship between the powder size of TiH₂ and the pore size [6]:

$${\mathrm{d}}_{\mathrm{m}}=\mathrm{g}·{\mathrm{d}}_{\mathrm{p}}$$

(3)

where d_m and d_p are the maximum pore size (μm) of porous Ti₃SiC₂ and the powder particle size (μm) of TiH₂, respectively, and g is the proportionality coefficient. Under the same synthetic process conditions, the reduction of powder size is beneficial to obtain the resultant material with smaller pores [6].

Figure 6 shows the relationship between the flexural elastic modulus and the pore size. When the pore size decreases from 21.8 to 2.1 μm, the flexural modulus increases from 13 to 70 GPa, which increases rapidly with the further decrease of the pore size to several microns. For comparison, the Young’s and the shear moduli of porous Ti₃SiC₂ with the porosity fraction of ca. 0.5 prepared by space holder were investigated to be about 50 GPa and 20 GPa, respectively [13]. Through data fitting, the relationship between them is as follows:

$$\mathrm{E}=\mathrm{h}·{\mathrm{d}}^j$$

(4)

where E and d are the flexural modulus (GPa) and the average pore size (μm) of porous Ti₃SiC₂, respectively. h and j are the constants with the values of 97.42 and −0.61, respectively.

The determination coefficient R² of Equation (4) is 0.95, indicating that the flexural modulus of porous Ti₃SiC₂ has a relatively good power function relation with the pore size. In the investigations on the relation of pore size and elastic modulus for porous materials, there are two kinds of research results for different material types. On the one hand, it has been revealed that the elastic modulus increases slightly with the increase of the pore size for a porous alumina ceramic [26]. On the other hand, it has been found that the elastic modulus increases with the decrease of the pore size for a porous nickel metal [28]. In this study, the change behavior of Ti₃SiC₂ MAX phase is similar to that of the latter, which indicates that porous Ti₃SiC₂ exhibits similar characteristics to porous metals under the action of bending stress.

4. Conclusions

Reactively synthesized porous Ti₃SiC₂ compounds with different pore sizes have the characteristics of high purity of MAX phase and laminar microstructure. The flexural stress–strain curves of porous Ti₃SiC₂ compounds exhibit two stages of elastic deformation and fracture, and the elastic deformation behavior shows a characteristic of kinking nonlinear elastic solid. The bending strength increases with decreasing the pore size for the synthesized porous Ti₃SiC₂ with approximately the same porosities and phase purities, and the change law between them follows the Hall–Petch equation. The flexural modulus of porous Ti₃SiC₂ has a power function relationship with the pore size. The reduction of the pore size of porous Ti₃SiC₂ improves the phase purity, strength and stiffness while increasing its filtration accuracy.