Research Article  Open Access
Thermomechanical Fatigue Behavior of SprayDeposited SiC_{p}/AlSi Composite Applied in the HighSpeed Railway Brake Disc
Abstract
The thermomechanical fatigue (TMF) behaviors of spraydeposited SiC_{p}reinforced AlSi alloy were investigated in terms of the size of Si particles and the Si content. Thermomechanical fatigue experiments were conducted in the temperature range of 150400°C. The cyclic response behavior indicated that the continuous cyclic softening was exhibited for all materials, and the increase in SiC particles size and Si content aggravated the softening degree, which was attributed to dislocation generation due to differential thermal contraction at the Al matrix/Si phase interface or Al matrix/SiC particle interface. Meanwhile, the TMF life and stress amplitude of SiC_{p}/Al7Si composites were greater than those of Al7Si alloy, and increased with the increasing SiC particle size, which was associated with “load sharing” of the direct strengthening mechanism. The stress amplitude of 4.5μmSiC_{p}/AlSi composite increased as the Si content increased; however, the influence of Si content on the TMF life was not so significant. The TMF failure mechanism revealed that the crack mainly initiated at the agglomeration of smallparticulate SiC and the breakage of largeparticulate SiC, and the broken primary Si and the exfoliated eutectic Si accelerated the crack propagation.
1. Introduction
The depletion of natural resources and environmental pollution are major challenges facing humanity today. It is urgent to study new energy sources instead of traditional fossil energy sources. The use of clean energy such as solar energy has been very extensive. For instance, new energy vehicles are using clean energy to save resources and protect the environment [1]. However, the development of new technologies has improved the requirements of materials. For instance, the lightweight, wear resistance, and thermomechanical fatigue properties of composites for automotive brake discs are very important [2–4]. The traditional metal brake discs are easy to crack and cannot ensure the safety of the vehicles due to the high temperature produced by friction between wheel and rail with high driving speed (≥400 km/h). Some new composites like carbon/carbon fiberreinforced carbon matrix composites have excellent hightemperature wear resistance, but oxidation and high manufacturing cost restrict their widespread application. SiC_{p}/AlSi composite, owing to advantages such as highspecific strength, excellent thermal conductivity, and low expansion coefficient, is considered as an ideal metal matrix composite (MMC) for brake disc [5–8]. In the process of actual braking, the residual stress caused by the mismatch in thermalexpansion coefficient (CTE) between SiC particle and AlSi alloy while the composites are subjected to mechanical load leads to thermomechanical fatigue (TMF) collaboratively.
Several methods can be adopted to prepare the SiC_{p}/AlSi composites such as stir casting [9], powder metallurgy [10], and spray deposition [11]. Spray deposition is a rapid prototyping process to gas atomize a stream of molten metal by mean of high velocity gases (i.e., Ar or N_{2}) and to direct the resulting spray into a cold substrate [12]. Not only can this method avoid the oxidation reaction between molten metal and bubbles during stirring process [13] but also make some microstructure improvements such as refining the grains, decreasing the segregated phase, and making the internal SiC particles more evenly distributed in SiC_{p}/AlSi composite [14]. Generally, the material prepared by spray deposition has high strength, good plasticity, and strong wear resistance [15].
There are many factors affecting the TMF properties of MMCs, involving complex mechanism. The inphase (IP) and outofphase (OP) experiments are conducted to simulate the temperature, strain, and phase relationship generally [16]; therefore, previous work about TMF of MMCs has been investigated mainly on the influence of phase, the volume fraction of reinforcement, and stress level on the fracture mechanism. Qian et al. [17–19] researched the TMF behavior of SiC_{W}/6061Al composites with SiC_{W} volume fraction of 15% and 28% and found that cyclic softening occurred in both composites during IP and OPTMF, and the cyclic stress range of highvolumefraction composites was greater than that of lowvolumefraction composites at an equivalent strain range. In addition, the 15% SiC_{W} composite revealed a longer life than 28% SiC_{W} composite in the case of IPTMF, but the fatigue life curves of the two composites passed across each other in the case of OPTMF, and the damage mechanism consists of initiation, growth, and coalescence of voids in the matrix around whiskers. Eun [20] reported that the IPTMF life of Ti48Al2V alloy and TiB_{2} particles reinforced Ti48Al2V composites became longer as the maximum temperature and the stress range decreased, and the TMF mechanism was nucleation and growth of voids on interlamellar plate, twin, and grain boundaries; their interlamellar, translamellar, and intergranular linkage; intergranular separation and disintegration of lamellar structure. The IP and OPTMF behavior of SiC_{p}/Al 2xxxT4 between 100°C and 300°C composites has been investigated by Karayaka and Sehitoglu [16]. They found that the failure mechanism was creepfatigue damage in shortlife areas and oxidation damage in longlife areas. Sehitoglu [21] found that the TMF life of Al/SiC composites became longer with smaller SiC particle size. It was investigated by Wang et al. that the TMF damage behavior of AlSi piston alloy was affected by temperature ranges; the cracks mainly initiated from the broken primary silicon in the temperature range of 120~350°C and nucleated from the interface between matrix and primary Si in the temperature range of 120~425°C [22]. However, the effect of particle size and Si contents on the TMF behavior of spraydeposited SiC particles reinforced AlSi alloy has rarely been investigated.
Thus, the cyclic stress behavior, particulate strengthening mechanism, and thermomechanical fatigue fracture of SiC_{p}/AlSi composites in terms of different SiC particle sizes and Si contents were investigated.
2. Experimental Materials and Procedures
The AlSi alloy and composites reinforced with 15 vol.% SiC particles were prepared by multilayer spray deposition technology; the details of which have been shown in the previous studies [23]. The nominal composition of investigated samples is given in Table 1. The sprayed ingots were extruded at the ratio of 17.3, and T6 heat treatment was performed at 535°C for 2.5 h followed by quenching in roomtemperature water and natural aging more than 12 h, finally artificial aging at 160°C for 7 h. All of samples were treated by the abovementioned process.

The machined specimens had a rectangular section of and a gauge length of 25 mm, according to ASMT standard E8. TMF tests were examined on a computercontrolled servo hydraulic test machine. As can be seen in Figure 1, the temperature was controlled by triangle wave and detected by thermocouple. Mechanical strain was controlled by cosine waves and measured with 25 mm hightemperature extensometer. The total strain amplitude is 0.3% and of stress ratio is 0.1. Considering that the disc surface temperature is generally 150400°C, sometimes up to 450°C [24], specimens were heated using induction heater from minimum temperature of 150°C to a maximum temperature of 400°C. The cycle period (total heating and cooling times) was 100 s for the TMF experiments. After TMF experiments, the fracture morphology was observed by the Quanta 2000 environment scanning electron microscope (SEM).
3. Results
3.1. Microstructure
Some typical phases of Al7Si alloy and SiC_{p}/AlSi composites are identified and marked briefly in the optical micrographs (Figure 2). The Al7Si alloy is mainly consisted of αAl matrix and Si particles with white color, which cluster together forming the eutectic Si phase marked in Figure 2(a). SiC particles with an average size of 4.5 μm were distributed evenly in the 4.5μmSiC_{p}/Al7Si composite (Figure 2(b)). In Figure 3(c), the SiC particles with grey color and a mean particle size of 20 μm were irregular shaped, and interparticle spacing is smaller than 4.5μmSiC_{p}/Al7Si obviously. The morphology of Si phase changed with an increase in Si content; it can be seen a few blocklike primary Si phase with an average of 5.85 μm and many round eutectic Si phase with an average of 2.51 μm in the 4.5μmSiC_{p}/Al13Si composite (Figure 2(d)). While for 4.5μmSiC_{p}/Al20Si composite, the average size of primary Si phase is 7.85 μm and the shape is more random. More details about microstructure have been reported in previous investigations [25, 26].
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3.2. StressMechanical Strain Hysteresis Loop
Figure 3 shows the hysteresis loop for the first and halflife time of SiC_{p}/Al7Si composites with different particle sizes during TMF loading. During the heating period of the first cycle, the stress increases with increasing temperature and strain value. When the temperature and strain value first reach the maximum and then both decrease to minimum value, the stress amplitude first reaches the maximum positive value and then decreases to the maximum negative value, correspondingly. In addition, the maximum tensile stress is greater than the maximum compressive stress for the all materials. It can be seen from the Figures 3(a)–3(c) that the stress amplitude of the first cycle life is greater than that of the halflife cycle for all samples, which means that softening occurs once the first cycle begins. Comparison of Figures 2(a)–2(c) shows that the softening degree of Al7Si alloy is more obvious than other two composites. Especially, the 4.5μmSiC_{p}/Al7Si composites have the lowest softening degree.
Typical first and halflife hysteresis of 4.5μmSiC_{p}/AlSi composites with different Si contents for TMF are given in Figure 4. The stress amplitude of the halflife cycle is lower than that of the first cycle life and softening occurs after the first cycle loading for all specimens. It can be also observed that the cyclic softening degree increases with an increase in Si content. The maximum tensile stress is greater than the maximum compressive stress for the same materials during TMF loading process.
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3.3. Cyclic Stress Response
Figure 5 shows the cyclic stress response of the studied SiC_{p}/AlSi composites at the total mechanical strain amplitude of 0.3%. It can be observed that the cyclic response stress of Al7Si alloy has the similar trend to those of SiC_{p}/Al7Si composites from Figures 5(a) and 5(b), i.e., cyclic softening. While there are a few differences between the details, for Al7Si alloy, the onset of slight cyclic softening stage occurs from 1 to 10 cycles, and then the softening degree becomes more significant, and finally rapid softening occurred from about 300 cycles to rupture time. For 4.5μmSiC_{p}/Al7Si composite, rapid cyclic softening occurs during the first 20 cycles, nearly followed by saturation around 700 cycles and rapid softening till failure. The 20μmSiC_{p}/Al7Si composites show rapid cyclic softening during the first 30 cycles, followed by slight softening till about 800 cycles and then failure. In addition, the stress ranges are the largest in the first cycle and then decrease rapidly in the following cycles for all samples. It can be found that the stress amplitude of Al7Si alloy is obviously lower than that of SiC particlereinforced Al7Si composites, of which the stress amplitude of 20μmSiC_{p}/Al7Si composite is the highest. Thereafter, it is worth noting that an increase in SiC particle size leads to an increase in the TMF life. The 4.5μmSiC_{p}/AlSi composites with different Si content also exhibit softening tendency from initial cycles to final rupture, and an increase in Si content results in a more pronounced cycle softening (Figure 5(b)). In terms of stress amplitude, a similar trend also appears. The higher the Si content, the greater the stress amplitude. However, there is no significant difference in the TMF life of these composites; the TMF life of 4.5μmSiC_{p}/Al7Si composite is slightly longer than the other two composites, while the TMF life of 4.5μmSiC_{p}/Al13Si composites and 4.5μmSiC_{p}/Al20Si composites is similar.
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3.4. Fractographical Observation
The TMF fractography of Al7Si alloy and SiC_{p}/AlSi composites is shown in Figure 6. The rough fracture surface consists of many micropores with 35 μm in size uniformly distributed in the region of stable fatigue crack propagation (Figure 6(a)). Figure 6(b) is the magnified view of the region of fatigue crack propagation, and there are many small eutectic Si particles scattering around the micropores, which is probably associated with debonding during TMF loading. Crack tip factor increases as the cycles increases, which results in the sharp rising amount of micropores and dimples. Fatigue striation and micropores distributed alternatively on the rough fracture surface of 4.5μmSiC_{p}/Al7Si composite can be presented in Figure 6(c), and the direction of fatigue crack propagation is perpendicular to fatigue striation. Plenty of complete SiC particles and several Si particles can be observed at transient fracture zone (Figure 6(d)), which indicates that SiC particles debond from AlSi matrix and form aggregation accelerating fatigue crack initiation and propagation during TMF loading. Figure 6(e) shows rougher fracture surface of 20μmSiC_{p}/Al7Si composites in the region of crack propagation than that of Al7Si alloy and 4.5μmSiC_{p}/Al7Si composite, and the propagation paths are more tortuous. There are some broken primary SiC particles distributing on the fracture plane, where the decohesion of SiC particles and Si particles also occurs peripherally. Besides, many voids form around the particles, and cavities and pits accumulate together with the increase in TMF cycles. The contiguous holes interlink with each other due to the tearing of different phases in the monolithic alloy, thus forming many microcracks (Figure 6(f)).
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Similar to 4.5μmSiC_{p}/Al7Si composite, typical fatigue striation should have been observed in the region of crack propagation for the 4.5μmSiC_{p}/Al13Si composite; however, there is no such characterization probably because some free SiC particles and Si phases concealed the fatigue striation, but plenty of homogeneous cavities and dimples also can be seen in the fracture surface. These SiC particles agglomerate together more tightly to form a large cluster, like a big particle, which results in the crack initiation more easily (Figure 6(g)). In addition, the fracture of some free primary Si possibly takes place at crack growth stage (Figure 6(h)). The striations and cavities appear alternatively in the TMF fractographs of 4.5μmSiC_{p}/Al20Si composites (Figure 6(i)), and the reason for the formation of cavities may be related to SiC particles and Si particles debonding from AlSi matrix. The size of primary Si particles increases as Si content increases, and cracks nucleate primary Si particles with larger size, which results in many microcracks in Figure 6(j).
4. Discussion
4.1. The Effect of Thermal Expansion Coefficient on Fatigue Life
Karayaka and Sehitoglu [16] investigated the thermomechanical fatigue of metal matrix composite and found that temperature and mechanical strain always changed momentarily in the TMF process. Lloyd [27] also pointed out that the total strain was the sum of thermal and mechanical strain components: where is the total strain, is the thermal strain, is the mechanical strain, is the initial temperature at the beginning of experiment, is the realtime temperature of experiment, and is the thermal expansion coefficient of composites.
SiC_{p}/AlSi composites are composed of the Al matrix, Si phases, and SiC particles. The difference in Si content and SiC particle size will lead to a great difference in thermal expansion coefficient of materials, which will directly affect the dislocation and residual internal stress of materials. Elomari et al. [28] indicated that the addition of SiC reinforced particles could effectively reduce the thermal expansion coefficient of the material. When the volume fraction of reinforced particles was constant, the thermal expansion coefficient of composites decreased with the decrease of SiC particle size. Thus, it can be concluded that the thermal expansion coefficient of Al7Si alloy in this paper is the highest, followed by composite with 20 μm SiC particles and composite reinforced with 4.5 μm SiC particles. When the cyclic loading temperature is applied between 150 and 400°C, the Al7Si alloy exhibited the most obvious thermoplastic deformation, which is attributed to the highest thermal strain and residual thermal stress, leading to the lowest fatigue life.
4.2. The Effect of SiC Particle Size
The stress amplitude and TMF life of SiC_{p}/Al7Si composite are both greater than that of Al7Si alloy, which is closely related to the strengthening mechanism of reinforced particles. Generally, there are two kinds of strengthening mechanisms, direct strengthening and indirect strengthening. The load transmission between matrix and reinforced particles is taken into account for direct strengthening, and the effect of reinforcement on microstructure and deformation mode of matrix is concerned about indirect strengthening [29]. From the perspective of direct strengthening, elastic modulus of matrix is lower than that of SiC particles; thus, SiC particles can undertake the loading partly from matrix, which improves the strength of materials. According to the shear lag model proposed by Nardone and Prewo [30], where is the yield strength of composites, is the yield strength of alloys, is the lengthtodiameter aspect ratio of reinforced particles, and and are the volume fraction of reinforced particles and matrix, respectively.
In accordance with the microstructure of SiC_{p}/Al7Si composites, the aspect ratio can be measured to be 1.38 and 1.94 for 4.5 μm SiC particle and 20 μm SiC particles, respectively. It can be calculated from formula (2) that composite with 20 μm SiC reinforcement exhibits the highest yield strength, which is consistent with the mechanical properties measured experimentally in literature [23], leading to a higher cyclic stress response.
In this study, the indirect strengthening mainly caused by the geometric dislocation resulted from the mismatch of the thermal expansion coefficient between the refractoryphase reinforced particles SiC and the deformablephase Al7Si alloy. Especially, the thermal expansion coefficient induced by smaller particles results in higher geometrically dislocation density, discussed in Ref. [21]. Consequently, the geometrically dislocation density of 4.5μmSiC_{p}/Al7Si composite is greater than that of 20μmSiC_{p}/Al7Si composite. Based on the constitutive relationship between shear flow stress and dislocation proposed by Fleck et al. [31], where is the elastic modulus of Al7Si alloy, GPa; is the scalar coefficient; is the Burgers vector. Thus, the increase in dislocation density results in an increase in flow stress, namely, the yield strength of 4.5μmSiC_{p}/Al7Si composite is greater than that of 20μmSiC_{p}/Al7Si composite; in ordinary, the TMF behaviors have the same rule as yield strength. Similar results are also reported in Ref. [21]. However, the observations in cyclic stress response are different from the above accepted point, which could be predominantly correlated to the lower yield strength resulted from the formation of fine particle clusters [23]. Load transfers from the matrix to the SiC particles in the TMF process, but when the aggregated SiC particles form loose microstructure, crack initiation and propagation occur more easily, which accelerates the failure of the material. While SiC particles are distributed uniformly in the 20μmSiC_{p}/Al7Si composite, cracks initiate the defects of particles. Reference [24] indicates that the SiC particles with small size result in void nucleation, increasing the lowcycle fatigue life at the high strain amplitude (>0.3%). In summary, the direct strengthening mechanism is dominant in Al7Si alloy and SiC_{p}/Al7Si composites.
4.3. The Effect of Si Content
Generally, the Si species, including primary Si phase and eutectic Si phase, differ from Si contents in composites, which results in different TMF properties. The microstructure of 4.5μmSiC_{p}/AlSi composites shows that the volume fraction and average size of Si phase increase with an increase in Si content. The SEM images of the fracture surface on the TMF samples indicate two distinctly crack growth mechanisms of primary Si particle and eutectic Si, which are summarized in Figure 7. It can be described that the TMF cracks will propagate through the primary Si particles and along the interface between eutectic Si and αAl matrix, which is related to the cracktip driving forces [32]. Besides, continuous thermal cycle will result in expansion of Si particles and local microplasticity around the αAl/Si interface accelerating the deformation of composites, the concept has also been reported in Ref. [22]. Therefore, in this study, the fracture modes of 4.5μmSiC_{p}/Al7Si composite are debonding and aggregation of SiC particles, along with the detachment of eutectic Si phase, while for 4.5μmSiC_{p}/Al13Si composite, the detachment of eutectic Si phase is the main fracture mode; meanwhile, the broken primary Si phases are very rare. The fracture tendency of primary Si increases with increasing Si content; thus, plenty broken primary Si phases can be seen for 4.5μmSiC_{p}/Al20Si composite. In addition, the loading distribution between particles and matrix is largely decided by the Si interparticle distance, and the interparticle distance of 4.5μmSiC_{p}/Al20Si composite is the smallest. Once the plastic deformation occurs in the local matrix, Si phase can impede the dislocation sliding movement due to more difficult deformation than αAl matrix, which can slow down the overall plastic deformation of composite. Therefore, 4.5μmSiC_{p}/Al20Si composite possesses the best performance to resist the plastic deformation. Moreover, the stress amplitude of composite, which meets the movable dislocation amount bypassing the obstacles, increases with increasing Si content; therefore, the stress amplitude of 4.5μmSiC_{p}/Al20Si composites is the highest.
When the composite is cooled from high temperature or processing, the αAl matrix near the Si phase and SiC particles is easily deformed; thus, dislocations are generated, moved, and stored. The main reason of dislocation generation is differential thermal contraction at the AlSiSiC_{p} interface due to the CTE mismatch among αAl matrix, Si phase, and SiC particles [33, 34]. If the size and volume fraction of SiC particles is constant, the effect of Si content on the dislocation should be considered carefully. Figure 8 is the schematic of geometrically necessary dislocation model. Assuming that (1) the AlSiSiC interface is wellbonded and (2) Si particles and SiC particles are simplified as sphere, the strain gradient is produced in the transition area from the Siphase interface to the region far away the interface in the matrix; thus, the geometrically necessary dislocation decreases with the increasing interparticle spacing, namely, the in Figure 8. It can be examined that the interparticle distance () of Si phase increases with Si content in Figure 2. In addition, the presence of strain gradient results in geometrically necessary dislocation to adapt to lattice distortion for composites, and the relationship can be expressed as formula (4) proposed by Arsenlis and Parks [35]: where is the geometrically necessary dislocation, is the Nye factor, and usually for polycrystalline materials, is the strain gradient, and is the Burgers vector. Therefore, the geometrically necessary dislocation increases as the strain gradient increases, the same to Si contents. Therefore, the dislocation density of 4.5μmSiC_{p}/Al20Si composite is the greatest, which is the dominant reason of highdegree softening.
5. Conclusion
The thermomechanical fatigue behaviors of spraydeposited SiC_{p}/AlSi composites were investigated in terms of the size of SiC particles and the Si content in the temperature range of 150400°C. The main findings are listed below: (1)Hysteresis loop reveals that the stress amplitude of the first cycle life is greater than that of the halflife cycle for all samples, which means that softening occurs since the first cycle begins. And the maximum compressive stress is generally lower than the maximum tensile stress for the same materials during TMF loading process(2)There exists a continuous cyclic softening in Al7Si alloy and SiC_{p}/AlSi composite. Both the increase in SiC particle size and Si content can aggravate the softening degree obviously, which is correlated with the dislocation generation in differential thermal contraction at the Al matrix/Si phase and Al matrix/SiC particles. Besides, the stress amplitude of SiC_{p}/Al7Si composites increases with increasing SiC particle size or Si content, which is attributed to the abilities to meet the movable dislocation amount bypassing the obstacles(3)The TMF life is remarkably enhanced by an increase in SiC particle size, which is associated with “load sharing” of the direct strengthening mechanism. Nevertheless, little or no influence on the TMF life is found through increasing Si content(4)Compared to Al7Si alloy and 4.5μmSiC_{p}/Al7Si composite, 20μmSiC_{p}/Al7Si composite presents a rougher fracture surface in the region of crack propagation. As Si content increases, the fracture tendency of primary Si increases, resulting in an increase in microcrack nucleation. The failure mechanism of SiC_{p}/Al7Si composites reveals that the agglomeration of smallparticulate SiC and the breakage of largeparticulate SiC are the main crack initiation sites. The broken primary Si and the exfoliated eutectic Si accelerate the crack propagation
Data Availability
All data used to sustain the findings of this study are included in the article.
Conflicts of Interest
The authors declare that they have no conflicts of interest.
Acknowledgments
The authors received financial support from the National Natural Science Foundation of China (No. 51675058), the Key Scientific Research Project of the Education Department of Hunan Province (No. 16A002), the Science and Technology Innovation Project of Hunan Province (No. 2018RS3073) and the Natural Science Foundation of Hunan Province (No. 2018JJ3531), and the Double FirstClass Scientific Research International Cooperation Project of Changsha University of Science and Technology (2019IC15).
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