Corresponding parameters for initial packing structures of composite powders before compaction.
Abstract
Uniaxial die compaction of two-dimensional (2D) Al/SiC core/shell (core: SiC; shell: Al) composite powders with different initial packing structures was numerically reproduced using DEM-FEM coupled MPFEM modeling from particulate scale. The effects of external pressure, initial packing structure, and SiC content on the packing densification were systematically presented. Various macro and micro properties such as relative density and distribution, stress and distribution, particle rearrangement (e.g. sliding and rolling), deformation and mass transfer, and interfacial behavior within composite particles were characterized and analyzed. The results show that by properly controlling the initial packing structure, pressure, and SiC content, various anisotropic and isotropic Al/SiC particulate composites with high relative densities and uniform density/stress distributions can be obtained. At early stage of the compaction, the densification mechanism mainly lies in the particle rearrangement driven by the low interparticle forces. In addition to sliding, accompanied particle rolling also plays an important role. With the increase of the compaction pressure, the force network based on SiC cores leads to extrusion on Al shells between two cores, contributing to mass transfer and pore filling. During compaction, the debonding between the core and shell of each composite particle appears and then disappears gradually in the final compact.
Keywords
- Al/SiC composite powders
- compaction
- core/shell structure
- MPFEM modeling
- debonding and rebonding
1. Introduction
Among the advanced particulate reinforced metal matrix composites (PRMMCs), Al/SiC composite is the most commonly studied one due to its potentially high tensile strength and elastic modulus at room or elevated temperatures, low thermal expansion coefficient, high thermal and electrical conductivity, excellent corrosion resistance, good wear resistance, mechanical properties, ductility, low cost and wide range of applications [1, 2, 3]. Normally, two routes (i.e. powder metallurgy (PM) and melt based approach) are used to fabricate PRMMCs with ‘net shape’ or ‘near-net shape’ forming. In the fabrication of Al/SiC composites via a melt process, SiC often reacts with molten Al to degrade the reinforcement strength and the interfacial strength [4], and the uniform distribution of SiC particles especially those with nanosizes are difficult to be realized. This deficiency can be largely avoided by PM process which can offer more control over reinforcement distribution and require less energy input than the conventional foundry route. A common PM process of Al/SiC composite consists of cold compaction in a closed-die or in an isostatic pressing followed by sintering. To fabricate Al/SiC composites with superior performances, large amount of physical and numerical work was carried out using PM method in the past few decades.
Physically, many researchers studied the effects of SiC content and particulate sizes using various forming methods. Ling et al. carried out experiments to study the PM fabrication of Al/SiC composites with SiC content ranging from 0 to 30 vol.% (volume fraction), where four PM methods (such as sintered, cold isostatic pressed (CIPed) and sintered, hot isostatic pressed (HIPed), and sintered plus HIPed in the same HIP cycle) were considered and the results of relative density, mechanical properties, and fractography were characterized and compared [1]. They found that the sintered plus HIPed technique can yield the best bulk composites. When the SiC content is within 10 vol.%, the matrix is more likely suffered to ductile failure. With a higher SiC content, the factors such as the interfacial bond strength, pore structure evolution, and the cracking within particles can all determine the mechanical properties of the composite products. For the Al/SiC composite powder comprising 40 vol.% SiC, Sridhar and Fleck respectively performed isostatic and closed-die compaction [5]. They found that for a given SiC powder content, the compaction pressure to achieve a given relative density increases with the decrease of the SiC particle size. The measured yield surfaces after each compaction indicated that the shape depends on the deformation path, with greatest hardening along the loading direction. Tavakoli et al. [2] studied the consolidation behavior of Al/SiC composite powders (with reinforcement SiC up to 50 vol.%) during pressure cycling (ranging from 90 to 360 MPa with 1 Hz) at room temperature in uniaxial compaction experiments to address the effects of compaction mode and SiC content on the densification, microstructure and mechanical properties of Al/SiC composites. And corresponding comparisons were made with monotonic compaction. The results showed that the pressure cycling can enhance the densification of Al/SiC composite powder, and the densification rate increases with the SiC content. Using HIP, Tang et al. [6, 7] studied the consolidation of Al/SiC composite powder with 6.5 vol.% nano-sized SiC particles (25 nm in size) synthesized via cryomilling and followed by hot rolling. Microstructural investigation indicated that the nano-sized SiC particles had been dispersed homogeneously in the reinforced regions in the composites and the tensile strength of the composite was improved greatly. However, coarse-grained SiCp-free regions were observed to be formed during HIPing, which improved the ductility but to a certain degree decreased the strength. In short, SiC nanoparticles located at grain boundaries can contribute to limiting grain growth, but it is difficult to achieve the complete uniform distribution of nano SiC particles. Jamaati et al. [8] investigated the effects of SiC particle size (2 and 40 μm, respectively) on microstructure and mechanical properties (tensile strength and elongation) of Al/SiC (with 10 vol.% SiC) composite fabricated by accumulative roll bonding. It was found that the composite strip with 40 μm particle size became uniform with high bonding quality and without any porosity sooner than the strip of 2 μm particle size. For both sizes, different cycles could lead to different tensile strength and tensile elongation.
To determine the compressibility behavior of Al-Cu/SiC composite powder mixtures which include 4 wt.% (weight fraction) Cu and 5–20 wt.% SiC, a double action die compaction with the pressure ranging from 50 to 450 MPa was performed by Ghiţă and Popescu [9]. And empirical equations were proposed to describe densification mechanism of the composite powders and predict the optimal pressure applied. Li et al. [10] carried out physical experiments to study the distributions of SiC particles in different positions of the Al/SiC composite samples (with 35 vol.% SiC) formed by equal channel angular pressing and torsion (ECAPT) and found that the shear strain could create significant influences. And from the compaction stage to the angular pressing stage during ECAPT, the distribution homogeneity of SiC particles increases greatly, implying that this forming method can realize relatively homogeneous SiC distribution. With the addition of nanosized SiC particles (0–7 wt.%), Moazami-Goudariz and Akhlaghi [11] conducted physical experiments on the compaction of Al/SiC composites. In their work, the effects of morphology, microstructure, size, apparent density, flowability, and hardness of the produced powder mixtures on their compaction behavior were investigated. The results showed that the chemical composition and the nano SiC content created effects on the compaction behavior as well as properties of the compact. Al/SiC composites with different contents (up to 15 vol.%) and sizes (3, 6, and 11 μm) of SiC particles were fabricated using conventional PM route [12], where the effects of the size and content of SiC particulates on the microstructural and corrosion behavior of the composite were studied. Meanwhile, El-Kady and Fathy [13] also studied the effects of SiC particle size (70 nm, 10, and 40 μm) and content (5 and 10 wt.%) on both physical and mechanical properties of Al/SiC nanocomposites produced with PM followed by hot extrusion. Majzoobi et al. [14] investigated the tribological properties of Al/SiC nanocomposite prepared by hot dynamic compaction (with the strain rate of 103 s−1), where the content of SiC nanoparticles was respectively 0, 5, and 10 vol.%. After compaction, the relative density of the composite compact can be up to 98%.
Recently, the mechanical properties and corrosion behavior of Al/SiC (comprising 20 vol.% SiC) composites fabricated by vacuum hot pressing sintering at 700°C under a pressure of 20 MPa were studied by Zhang et al. [15], in their work the high relative density of 99.65 ± 0.08% for the Al/SiC composite can be obtained. Cold isostatic compaction of Al/SiC composite powders with different content of nano SiC particulates as the reinforcement was experimentally performed by Bajpai et al. [16], where various properties such as hardness, density, porosity, compressive strength, indirect tensile strength and the microstructure of the samples were measured and characterized. The micrograph shows the uniform distribution of nano SiC particles in the aluminum matrix. With micro wave sintering and hot extrusion, Penchal Reddy et al. [17] fabricated nano-sized SiC (0, 0.3, 0.5, 1.0 and 1.5 vol.%) reinforced Al metal matrix composites and studied the structural, mechanical and thermal properties of the developed Al/SiC nanocomposites. Results indicated that hot extruded Al/SiC nanocomposites (with 1.5 vol.% SiC) exhibited the best mechanical and thermal performance as compared to the other developed Al/SiC nanocomposites.
Aforementioned researches in physical experiments indicate that most of the previous work was mainly focusing on the sintering stage or the forming stage, comprehensive studies on the compaction of Al/SiC composite powders are less conducted. Actually, most of the densification takes place in the compaction stage by rate-independent plasticity [1]. And the relative density (defined as the volume of the powder divided by the volume occupied by the die) and corresponding packing structure of the compact can determine the subsequent sintering process as well as the final properties of the sintered component. Therefore, the researches on the compaction of Al/SiC composite powders when subjected to external energy have increasingly attracted the materials scientists and engineers’ interests in the past few years. Nevertheless, even though physical experiments can reproduce the relationship between relative density and compaction pressure and/or temperature, they are unable to quantitatively characterize the local density distribution, stress distribution, and particle motion behavior for pore (or void) filling in situ, especially the nonlinearity features in geometry, materials, and contact during compaction all increase the difficulties of physical experiments [18, 19, 20, 21, 22]. Most importantly, it’s really hard for researchers to accurately control the uniform distribution (ordered or disordered) of reinforcement (SiC) in the metal (Al) matrix, these disadvantages in physical experiments can be conquered by the so called numerical simulations.
Numerically, various models or methods were proposed or used to simulate powder compaction densification in PM process. For example, a traditional macro continuous FEM (finite element method) simulation model, in which the powder mass is regarded as a continuum with uniform void distribution, was proposed to solve the problems arising from physical experiments. In addition to the relationship between overall relative density and compaction pressure, this method can also be used to analyze local relative density and distribution, stress distribution, and powder displacement in the compact upon compaction from macro continuous scale. Therefore, as reported in the authors’ previous researches, the single-action die compaction of pure metal powders [23, 24] and composite powders [25] has been systematically investigated by this method. Even though the traditional FEM can to some extent solve the problems in physical experiments, it is really hard to deal with the important issues like dynamics and contact mechanics from particulate scale based on the aforementioned continuum assumptions. However, this will be overcome by molecular dynamics based DEM (discrete element method) simulation. DEM has been widely applied to generate various packing structures of spherical and non-spherical particles [26, 27, 28, 29], but its effectiveness in modeling the compaction of powders is restricted to limited relative density (e.g.
In this chapter, uniaxial die compaction of Al/SiC composite core/shell powders with different initial packing structures was numerically reproduced using DEM-FEM coupled MPFEM modeling from particulate scale. The effects of external pressure, initial packing structure, and SiC content (composition) on the packing densification were systematically presented. Various macro and micro properties such as relative density and distribution, stress and distribution, particle rearrangement (e.g. sliding and rolling), deformation and mass transfer, and interface behavior between particles were characterized and analyzed. Some interesting results have been obtained, which can provide the materials scientists and engineers with valuable references to the realization of fully dense and high performance Al/SiC composite compacts in PM production.
2. Simulation method and conditions
2.1. Simulation method
The simulation method used in current work is MPFEM. In this method, the initial random powder packing is firstly generated by DEM and then imported into FEM model, where each particle is fully discretized into finite element meshes. Figure 1 respectively gives the schematic diagram of an individual composite particle with core/shell structure and corresponding mesh division as well as the numerically generated initial packing structure in the closed die before compaction when the SiC content is 25 vol.%, where each core (SiC)/shell (Al) composite particle includes respectively 200/1700 nodes and 173/1552 elements. After all the parameters and conditions are determined, the program will be complied and run in the commercialized MSC.Marc software. For simplicity, the details of DEM model are not given here, interested readers can refer to [26, 27, 28, 29, 45] for more information. In comparison, each initial ordered binary packing is generated by the intrinsic function in MSC.Marc software based on geometry. The initial random or ordered packing structure was then imported into MPFEM model as the input. Figure 2 shows the packing morphologies of Al/SiC composite powders before compaction. Here three initial ordered packings, i.e. simple cubic (SC), hexagonal close packed (HCP) and honeycomb structures are considered. The composition of the composite powder can be adjusted by the thickness of Al shell, which is represented by
Initial packing structure | Size ratio ( | SiC content, vol.% | Packing density |
---|---|---|---|
SC | 1/2 | 25 | 0.7841 |
SC | 2/3 | 44.4 | 0.7842 |
HCP | 1/2 | 25 | 0.8782 |
HCP | 2/3 | 44.4 | 0.8783 |
Honeycomb | 1/2 | 25 | 0.6045 |
Random | 1/√10 | 10 | 0.7516 |
Random | √15/10 | 15 | 0.7526 |
Random | 1/√5 | 20 | 0.7544 |
Random | 1/2 | 25 | 0.7424 |
Random | √3/√10 | 30 | 0.7515 |
2.2. Simulation conditions
After the generated binary initial packing structure was imported into the MPFEM model in MSC.Marc software, the simulation conditions including material properties, definition of contact, mesh adaptability, and loading cases etc. were then set. In the simulation, the power law model is used to describe the properties of aluminum materials and the yield stress is given by:
where A, B, m, n are material constants;
where
where
Materials | Young’s modulus, | Poisson’s ratio, ν | Strength coefficient, A/MPa | Work hardening index, m |
---|---|---|---|---|
Al | 70.00 | 0.33 | 225.90 | 0.05 |
SiC | 470.00 | 0.142 | Elastic-perfectly |
Contact definition | Loading setup | Operation conditions |
---|---|---|
Particles: deformable | Iteration method: full Newton-Raphson algorithm | Friction: modified Coulomb friction model |
Die and punches: rigid | Convergence criteria: displacement or residual stress control | Large deformation: updated Lagrange function |
Friction coefficient between particles: | Global mesh self-adaptive division: for Al part | Contact method: segment to segment method |
Upper punch: velocity control ( |
3. Results and discussion
3.1. Compaction process and property characterization
In PM production, the relationship between the relative density
In comparison with ordered initial packings, the initial random packings of Al/SiC composite powders are frequently encountered in actual PM production. Figure 4 gives the compaction curves of five initial random packings with different SiC contents and relative densities as well as corresponding model validation. As indicated in Figure 4(a), the compaction curves are quite different from those in Figure 3(a), which can be ascribed to the difference of initial packing structures. For each
where
3.2. Initial packing structure effects
Previous results have illustrated that the initial packing structure of the composite powder or the SiC content can create effects on the compaction behavior and property of the compact. To further identify their important role in the densification process, the compaction on SC and HCP ordered initial packings with different SiC contents is shown in Figure 5, where Figure 5(a) gives the compaction curves and Figure 5(b) indicates the morphologies of the compacts under the pressure of 200 MPa and the stress distributions therein. Here, the equivalent Von Mises stress is given by:
where
In addition to the compaction on ordered initial packing structures, the evolutions of morphologies and stresses in the compacts formed by random initial packings with five SiC contents at different compaction stages are also systematically studied. Here, the compaction on the random initial packing with 25% SiC is taken as an example for detailed analysis. Figure 6 gives the morphology evolution of the compact and corresponding stress transmission/distribution at each compaction stage. As indicated, during compaction both translational motion (including the sliding as indicated by the arrow in the third snapshot of Figure 6(a)) and rotational motion are observed, which are mainly occurred in early stage of compaction when the pressure is low. In this case, the densification is mainly due to the rearrangement of the Al/SiC composite particles, and the force chain is formed as a skeleton or network. With the increase of the incremental modeling steps
3.3. Quantitative analysis on particle rearrangement during compaction
It is known that the densification of composite powders during early stage of compaction is mainly due to the rearrangement of particles through translational motion and rotational motion, while systematic analysis on the particle rotation in the compaction process is less studied because this behavior is difficult to be quantitatively characterized. To achieve this, an algorithm is proposed to calculate the rotation of particles during compaction. Figure 7(a) schematically illustrates the particle (here two nodes adjacent to SiC core in Al is selected as the research target) relative position before (e.g. ΔOAB) and after (e.g. ΔOA′B′) rotation, here the coordinates of (
where:
and
To further study the effects of initial packing structures, three packings with the similar relative densities (≈ 0.74) and SiC (25%) but different structures as shown in Figure 7(b) were chosen for analysis. The results are shown in Figure 8, where Figure 8(a) gives the evolution of average rational angle with the relative density of each initial packing structure during compaction and Figure 8(b) indicates the quantitative statistics on the distribution of rotational angles. As can be seen from Figure 8(a) that with each case, the average rotational angle increases with the relative density but the increasing rate decreases. And different initial packing structures can result in different rotation behavior even the relative density and the composition of the composite powder are similar. Meanwhile, one can also find that the fast increasing region of rational angle is mainly located in the region where the relative density is lower than about 0.82. Previous researches [48] have demonstrated that 0.82 is the relative density of random close packing state with stable structure for 2D disks, beyond which both the translational motion and rotational motion during compaction become difficult. This variation has similar trend with previous results from other packing systems [31]. Besides, the distribution of average rotation angle in Figure 8(b) indicate that during compaction most particles rotate with the angle of 1–5°. Large scale particle rotation is mainly formed at the initial rearrangement stage of the compaction when the pressure is low. Because after deformation under high pressure the contact between neighboring particles changes from point to face, which restrains the further rotation of composite particles. From Figure 8(b) one can also find that different initial packing structures can lead to different rotation behavior, which will further determine the densification process as well as the resultant properties of the final compacts.
3.4. Debonding and rebonding phenomena
During compaction on composite powders with core/shell structures, a common phenomenon, i.e. debonding can be occurred, which has also been observed at the Al/SiC interface in current MPFEM simulation. Interestingly, after debonding, the separated Al and SiC in a composite particle can rebond again to form a good cohesion and combination at the interface. It needs to clarify that in current simulation only physical interaction at the interface is considered, chemical reactions are not included. Previous results in this chapter have shown that some composite particles are debonded during compaction. Especially for those particles that are close to the punches or close to the large voids, the debonding is more probable. Those composite particles that form local ordered dense packing structure are not likely to debond unless the SiC content is very large. In order to explain the mechanisms of debonding and rebonding phenomena, a single Al/SiC composite particle in initial random packing is selected for analysis. The evolution of normal stresses and shear stresses in this particle at different stages of compaction is shown in Figure 9. As can be imagined from the figure that at the early stage of compaction, composite particles are fully rearranged with the help of relatively low pressure from the upper punch. In this case, no matter the tangential forces or the normal forces between particles or between Al and SiC at the interface are all very small. With the increase of the compaction pressure, the contact forces between composite particles increase. The large extrusion deformation or the shear due to relative sliding induces large tangential stresses at the interface between Al shell and SiC core, when the normal contact forces or stresses are very small at this region, the debonding occurs. While with the further increase of the compaction pressure, the bulk density of the compact increases. The normal contact forces or stresses at the debonding region increase due to the extrusion from neighboring particles, leading to the rebonding at the interface. Through comparison, one can conclude that the occurrence of debonding phenomenon, which has also been identified in others’ work [49], is mainly caused by sufficient tangential forces but insufficient normal forces at the interface. Therefore, the interface should have a certain shear strength and relatively large normal strength, which can not only effectively avoid the possible debonding, but also make the distribution of equivalent strain in the matrix more uniform.
4. Conclusions
DEM-FEM coupled MPFEM modeling on the single action die compaction of Al/SiC core/shell (core: SiC; shell: Al) composite powders with different initial packing structures was conducted from particulate scale in 2D. The effects of compaction pressure, initial packing structure, and SiC content (composition) on the packing densification were systematically presented. Various macro and micro properties such as relative density and distribution, stress and distribution, particle rearrangement through translational motion and rotational motion, deformation and mass transfer, and interfacial behavior between composite particles were characterized and analyzed. Following conclusions can be drawn:
MPFEM simulation can effectively reproduce the compaction densification of Al/SiC composite particles with core (SiC)/shell (Al) structures from particulate scale.
Beyond a certain Al content, the compaction on both ordered and random initial packings of the composite particles all can realize the full densification, however, the micro properties in these compacts are initial structure sensitive. And the densification rate is also different.
The compaction on Al/SiC core/shell composite powders can obtain more uniform relative density and stress distributions than other Al/SiC composite systems.
During compaction on random initial packings of Al/SiC composite powders, obvious particle rotations can be observed with the relative density of the compact between 0.74–0.82, and the value of average rotational angles is also affected by the initial packing structure.
The debonding between SiC core and Al shell during compaction on random initial packings mainly occurs at the area close to the large pore, where the normal stress is small and the shear stress is relatively large. To avoid it, sufficient normal stress at the core/shell contact area should be satisfied. For the compaction on ordered initial packing such as SC and HCP structures, debonding mainly appears close to the punches when the SiC content is relatively high, and it will be disappeared in the final stage of compaction.
The researches can not only enhance people’s understanding on the compaction densification of Al/SiC composite powders with core/shell structures and various initial packing states, but also provide the materials scientists and engineers with valuable references for the realization of high performance Al/SiC compact in future PM production.
Acknowledgments
The authors are grateful to National Natural Science Foundation of China (No. 51374070) and Fundamental Research Funds for the Central Universities of China (No. N162505001) for the financial support of current work.
Nomenclature
Scalars | |
A | strength coefficient |
B | material constant |
E | Young’s modulus |
m | work hardening index |
N | incremental modeling step |
n | material constant |
O | center of a circle |
P | compaction pressure |
r | radius of SiC particle |
R | radius of Al/SiC composite particle |
R2 | relative coefficient |
U | constant |
v | velocity |
x | coordinate on X axis |
y | coordinate on Y axis |
Z | constant |
Greek letters | |
α | angle |
β | angle |
Δ | triangle |
ε | strain |
εij | strain tensor |
ε¯· | equivalent strain rate |
ε¯ | equivalent strain |
θ | angle |
μ | frictional coefficient |
ν | Poisson’s ratio |
ρ | relative density |
ρc | relative density of the compact |
σ | stress |
Subscripts | |
0 | initial time |
1 | spatial direction |
2 | spatial direction |
3 | spatial direction |
A | spatial point |
A′ | spatial point |
B | spatial point |
B′ | spatial point |
c | compact |
i | integer, ranging from 1 to 3 |
j | integer, ranging from 1 to 3 |
p | particulate |
y | yield |
Acronyms | |
2D | two-dimensional |
CIPed | cold isostatic pressed |
DEM | discrete element method |
ECAPT | equal channel angular pressing and torsion |
FEM | finite element method |
HIPed | hot isostatic pressed |
MPFEM | multi-particle finite element method |
PM | powder metallurgy |
PRMMCs | particulate reinforced metal matrix composites |
vol. | volume |
wt. | weight |
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