Interfacial shear strength of Ti/SiC fibre composites measured by synchrotron strain measurement

A single fibre Ti/SiC_f composite sample was loaded incrementally and unloaded in-situ on a beam line at the European Synchrotron Research Facility (ESRF) in Grenoble. It was possible to measure the strain along the fibre with a high spatial resolution (50 μm) within the titanium matrix. The interfacial frictional shear strength inferred from the longitudinal strain profile of the broken fibre was calculated to be around 200 MPa. The result is compared to the interfacial shear stress derived from other methods developed to evaluate the matrix/reinforcement interface in this system. An axisymmetric finite element model gave good agreement between the numerical and experimental results.     

Initial-stage hot-pressing of SiC fibre/ Ti monotapes

The initial compaction under uniaxial hot-pressing conditions of titanium monotapes containing silicon carbide fibres is studied for variable matrix/fibre volume ratio, temperature (800–950°C) and compaction stress (10–40 MPa). The matrix compaction rate is predominantly affected by the latter two variables, less by temperature. The sample pore structure is strongly influenced by the preform packing characteristics including fibre-to-matrix volume ratio and irregularities in fibre arrangements.     

Micro-area Auger analysis of a SiC/Ti fibre composite

The reaction zone of an annealed W-SiC/Ti fibre composite was studied by means of micro-area Auger spectroscopy. The Auger peaks and the respective concentrations of the reaction products across the fibre-matrix reaction zone were analysed using smallspot line scans. In spite of surface topographical limitations it was possible to semiquantitatively determine elemental concentrations with spatial resolutions much higher than are possible using X-ray micro-analysis and to speculate on the formation of different compounds as reaction products.     

Processing, microstructure and mechanical properties of hot-pressed SiC continuous fibre/SiC composites

SiC (SCS-6TM) continuous fibre/SiC composites were fabricated by hot-pressing at 1700°C in vacuum using an Al sintering additive. Analytical transmission electron microscopy was used to investigate the microstructure of the composites. The room-temperature mechanical and high-temperature creep properties of the composites were investigated by four-point bending. The SiC powders used were sintered at a relatively low sintering temperature to high density (97% of theoretical density) with the addition of the Al sintering additive. It is believed that the Al additive is very efficient for the densification of SiC. The SiC fibres maintained their original form and microstructure during fabrication. The SiC matrix reacted with the outermost carbon sublayer in the fibre, forming a thin (1.8–4.8m) interfacial layer, which was composed of Al4C3, Si–Al–C, and Si–Al–O phases. The incorporation of SiC fibre into a dense SiC matrix significantly increased the room-temperature failure strain and improved the high-temperature creep properties. In addition, the incorporation of SiC fibre into a porous SiC matrix increased the room-temperature failure strain, but did not contribute to the high-temperature creep properties.     

Microstructural analysis of isothermally exposed Ti/SiC metal matrix composites

Specimens of diffusion-bonded titanium metal matrix composites have been subjected to thermal exposure treatments and examined principally by transmission electron microscopy. The fibres investigated were SCS-6 and Sigma. The fibre/matrix reaction layers have been shown to consist of titanium carbide and two titanium silicides. The reaction proceeds by the initial formation of a layer of TiC followed by a layer of mixed silicides, Ti₅Si₄ and Ti₅Si₃. Extensive porosity is generated during the reaction and this prevents the formation of a completely protective interfacial layer.     

反应热压烧结法制备SiC/Ti3SiC2复合材料及其性能

采用反应热压烧结法制备了SiC/Ti3SiC2复合材料,研究了热压温度、SiC含量及粒度对SiC/Ti3SiC2复合材料相组成、力学性能以及应力-应变行为的影响.结果表明:热压温度影响SiC/Ti3SiC2复合材料相组成;随着热压温度的提高,复合材料的弯曲强度和断裂韧性提高;随SiC含量的增加,SiC/Ti3SiC2复...     

铜钛硅碳石墨合金材料摩擦磨损性能研究

为研究铜钛硅碳石墨合金材料摩擦磨损性能,通过常规的粉末冶金方法制备了铜钛硅碳石墨材料。对样品硬度等性能的测试,选择出87%Cu的最优配方。再用无流磨损和载流磨损实验测试其摩擦磨损性能,进而通过扫描电镜对磨损表面进行观察,探讨摩擦磨损机理。结果表明,无流磨损过程中,磨损量呈线性增长,磨损的主要形式为梨削;载流磨损过程中,磨损量呈非线性增长,随着行程的增加,磨损率降低,磨损的主要形式有梨削和电弧烧损,磨损率降低可能是杂质Al相弥散强化铜基体所致,其微观机理是一个复杂的各种机理的组合。     

An experimental study on the in situ strength of SiC fibre in unidirectional SiC/Al composites

In order to investigate the effect of strain rate and high temperature exposure on the mechanical properties of the fibre in the unidirectional fibre reinforced metal-matrix composite, in situ SiC fibre bundles are extracted from two kinds of SiC/Al composite wires, which are heat-treated at two different temperatures (exposed in the air at 400 and 600 °C for 40 min after composition). Tensile tests for these two fibre bundles are performed at different strain rates (quasi-static test: 0.001 s⁻¹, dynamic test: 200, 700, and 1200 s⁻¹) and the stress–strain curves are obtained. The experimental results show that their mechanical properties are rate-dependent, the modulus E, strength σ_b and unstable strain _b (the strain corresponding to σ_b) all increase with increasing strain rate. Compared with the mechanical properties of the original SiC fibre, those of the two in situ fibres degrade to some extent, the degradation of the in situ fibre extracted from the composite wire exposed at 600 °C (hereafter referred to as in situ fibre 2) is more serious than that of the in situ fibre extracted from the composite wire exposed at 400 °C (hereafter referred to as in situ fibre 1). The mechanism of the degradation is investigated. A bi-modal Weibull statistical constitutive equation is established to describe the stress–strain relationship of the two in situ fibre bundles. The simulated stress–strain curves agree well with the experimental results.     

Critical factors on manufacturing processes of natural fibre composites

Elevated environmental awareness of the general public in reducing carbon footprints and the use non-naturally decomposed solid wastes has resulted in an increasing use of natural materials, biodegradable and recyclable polymers and their composites for a wide range of engineering applications. The properties of natural fibre reinforced polymer composites are generally governed by the pre-treated process of fibre and the manufacturing process of the composites. These properties can be tailored for various types of applications by properly selecting suitable fibres, matrices, additives and production methods. Besides, due to the complexity of fibre structures, different mechanical performances of the composites are obtained even with the use of the same fibre types with different matrices. Some critical issues like poor wettability, poor bonding and degradation at the fibre/matrix interface (a hydrophilic and hydrophobic effect) and damage of the fibre during the manufacturing process are the main causes of the reduction of the composites’ strength. In this paper, different manufacturing processes and their suitability for natural fibre composites, based on the materials, mechanical and thermal properties of the fibres and matrices are discussed in detail.     

Critical factors on manufacturing processes of natural fibre composites

Elevated environmental awareness of the general public in reducing carbon footprints and the use non-naturally decomposed solid wastes has resulted in an increasing use of natural materials, biodegradable and recyclable polymers and their composites for a wide range of engineering applications. The properties of natural fibre reinforced polymer composites are generally governed by the pre-treated process of fibre and the manufacturing process of the composites. These properties can be tailored for various types of applications by properly selecting suitable fibres, matrices, additives and production methods. Besides, due to the complexity of fibre structures, different mechanical performances of the composites are obtained even with the use of the same fibre types with different matrices. Some critical issues like poor wettability, poor bonding and degradation at the fibre/matrix interface (a hydrophilic and hydrophobic effect) and damage of the fibre during the manufacturing process are the main causes of the reduction of the composites’ strength. In this paper, different manufacturing processes and their suitability for natural fibre composites, based on the materials, mechanical and thermal properties of the fibres and matrices are discussed in detail.     

The properties of carbon fibre/SiC composites fabricated through impregnation and pyrolysis of polycarbosilane

Unidirectional carbon fibre reinforced SiC composites were prepared from four types of carbon fibres, PAN-based HSCF, pitch-based HMCF, CF50 and CF70, through nine cycles or twelve cycles of impregnation of polycarbosilane and subsequent pyrolysis at 1200°C. The polycarbosilane-derived matrix was found to be -SiC with a crystallite size of 1.95 nm. The mechanical properties of the composites were evaluated by four-point bending tests. The fracture behavior of each composite was investigated based on load-displacement curves and scanning electron microscope (SEM) observation of fracture surfaces of the specimens after tests. It was found that CF50/SiC and CF70/SiC exhibited high strength and non-brittle fracture mode with multiple matrix cracking and extensive fibre pullout, whereas HSCF/SiC and HMCF/SiC exhibited low strength and brittle fracture mode with almost no fibre pullout. The differences in the fracture modes of these carbon fibre/SiC composites were thought to be due to differences in interfacial bonding between carbon fibres and matrix. Values of flexural strengths of CF70/SiC and CF50/SiC were 967 MPa and 624 MPa, respectively, which were approximately 75% and 38% of the predicted values. The relatively lower strength of CF50/SiC, compared with CF70/SiC, was mainly attributed to the shear failure of CF50/SiC during bending tests.     

A new criterion for determining the failure of Ti/SiC metal-matrix composites

The failure of titanium metal-matrix composites (MMCs) strengthened with monofilament carbon-coated sigma SiC fibres has been studied following exposure at a temperature of 900C. Statistical analysis of the data shows that the time to penetration of the carbon layer on the as-received carbon-coated sigma monofilament (SiC+C) can be used as a failure criterion for these composites. The same technique can also be used as a measure of the effectiveness of different diffusion barrier coatings.     

Influence of microstructure of fibre/matrix interface on mechanical properties of Al/SiC composites

Abstract

The relationship between microstructure and mechanical properties of composites of squeeze cast Al–Cu and Al–Cu–Mg reinforced with 25 vol.-%SiC whiskers was investigated. Tensile test results were compared with values calculated using a modified rule of mixtures (ROM). The results were found to be in good agreement for the Al–Cu matrix composite, whereas a relatively large discrepancy was observed for the Al–Cu–Mg matrix composite. It was concluded from microstructural observations that this difference resulted from a reduction of the whisker strength due to more pronounced decoration of the interfaces by oxides and spinels. For the Al–Cu–Mg composite, the effect of interfacial phases on the composite strength must betaken into account when the modified ROM is applied.

MST/1242     

Brazing of SiC and SiCf/SiC composites performed with 84Si-16Ti eutectic alloy: microstructure and strength

The microstructure and strength of brazed joints for monolithic SiC and SiC_f/SiC composites are presented and discussed; the brazing technique is based on the use of the 84Si-16Ti (at%) eutectic alloy. The rather low melting point of the used alloy allows to avoid a degradation of the fibre/matrix-interfaces in the composite materials. All the joints did not show any discontinuities and defects at the interface and revealed a fine eutectic structure. Moreover, in the case of composites, the joint layer appeared well adherent both to the matrix and the fibre interphase, and the brazing alloy infiltration looked sufficiently controlled. High resolving electron microscopic investigations of the microstructure and of the nanochemistry (HREM, EELS, esp. ELNES) revealed atomically sharp interfaces without interdiffusion or phase formation at the interlayer leading to the conclusion that direct chemical bonds are responsible for the adhesion. The joints of SiC_f/SiC composites showed 71 ± 10 MPa shear strength at RT and nearly the same values at 600°C.     

Low temperature synthesis of Ti3 SiC2 from Ti/SiC/C powders

Abstract

Ternary carbide Ti₃ SiC₂ was first synthesised through a pulse discharge sintering (PDS) technique from mixtures of Ti, SiC, and C with different molar ratios. Sintering processes were conducted at 1200 – 1400°C for 15 – 60 min at a pressure of 50 MPa. The phase constituents and microstructures of the synthesised samples were analysed by X-ray diffraction (XRD) technique and observed by scanning electron microscopy (SEM). The results showed that, for samples sintered from 3Ti/SiC/C powder at 1200 – 1400°C, TiC is always the main phase and only little Ti₃ SiC₂ phase is formed. When the molar ratios Ti : SiC : C were adjusted to 3 : 1.1 : 2 and 5 : 2 : 1, the purity of Ti₃ SiC₂ in the synthesised samples was improved to about 93 wt-%. The optimum sintering temperature for Ti₃ SiC₂ samples was found to be in the range 1250 – 1300°C and all the synthesised samples contain platelike grains. The relative density of Ti₃ SiC₂ samples was measured to be higher than 99% at sintering temperatures above 1300?C. It is suggested that the PDS technique can rapidly synthesise ternary carbide Ti₃ SiC₂ with good densification at lower sintering temperature.     

Microstructure and mechanical properties of short carbon fibre/SiC multilayer composites prepared by tape casting

Silicon carbide multilayer composites containing short carbon fibres (C_sf/SiC) were prepared by tape casting and pressureless sintering. The C fibres were dispersed in solvents with dispersant (Triton X-100) firstly and then mixed with the SiC slurry to make green C_sf/SiC tapes. Fibres were homogeneously distributed in the tape and tended to align fairly well along the tape casting direction. The addition of short C fibre hindered the shrinkage in the plane containing the fibres as well as the grain growth of SiC during sintering. The weight loss occurring during oxidation tests of C_sf/SiC multilayer composites increased with fibre amount and material porosity. Elastic modulus of C_sf/SiC multilayer composites decreased linearly with fibre amount. Bending strength presented clear relationship with the relative density, that is with the total porosity.     

High-temperature dielectric and electromagnetic interference shielding properties of SiCf/SiC composites using Ti3SiC2 as inert filler

Ti₃SiC₂ filler has been introduced into SiC_f/SiC composites by precursor infiltration and pyrolysis (PIP) process to optimize the dielectric properties for electromagnetic interference (EMI) shielding applications in the temperatures of 25–600 °C at 8.2–12.4 GHz. Results indicate that the flexural strength of SiC_f/SiC composites is improved from 217 MPa to 295 MPa after incorporating the filler. Both the complex permittivity and tan δ of the composites show obvious temperature-dependent behavior and increase with the increasing temperatures. The absorption, reflection and total shielding effectiveness of the composites with Ti₃SiC₂ filler are enhanced from 13 dB, 7 dB and 20 dB to 24 dB, 21 dB and 45 dB respectively with the temperatures increase from 25 °C to 600 °C. The mechanisms for the corresponding enhancements are also proposed. The superior absorption shielding effectiveness is the dominant EMI shielding mechanism. The optimized EMI shielding properties suggest their potentials for the future shielding applications at temperatures from 25 °C to 600 °C.