Abstract:Silver-copper-titanium (Ag-Cu-Ti) ternary alloys are often used as active braze alloys for joining ceramics to metals at temperatures ranging from 780°C (the melting point of the Ag-Cu eutectic) up to 900°C. When Ti/Ag-Cu joints are brazed at low temperature (near 800°C), the intermetallic compound Ti 2 Cu 3 (tetragonal, P4/nmm, a = 0.313 nm, c = 1.395 nm) is systematically missing from the interface reaction layer sequence. An experimental investigation based on isothermal diffusion experiments in the Ag-Cu-T… Show more
“…After corrections for atomic number, absorption and fluorescence, the atomic contents of Ag, Cu and Ti were obtained with an accuracy better than ± 0.5 at%. It had been previously verified by X-ray powder diffraction [7] that the crystalline phases for which each interface reaction layer or crystal analysed were effectively obtained under the same heat-treatment conditions.…”
Section: Methodsmentioning
confidence: 84%
“…For these reasons, it was decided to further investigate the chemical interaction between titanium and the eutectic Ag-Cu alloy at temperatures down to 780 °C, the temperature of the eutectic transformation. In the first approach at investigating the kinetics of compound formation in the Ag-Cu-Ti system, cold-pressed mixtures of Ag, Cu and Ti powders were heated at 700-860 °C and characterized [7]. In the present work, additional experiments have been carried out at 780-800 °C on Ti/Ag-Cu semi infinite couples and Ti/Ag-Cu/Ti sandwiches in order to determine the extent and constitution of the interface reaction zone formed between solid Ti and liquid Ag-Cu eutectic alloy.…”
Reaction zones formed at 790 °C between solid titanium and liquid Ag-Cu eutectic alloys (pure and Ti-saturated) have been characterized. When pure Ag-Cu eutectic alloy with 40 at.% Cu is used, the interface reaction layer sequence is: αTi / Ti 2 Cu / TiCu / Ti 3 Cu 4 / TiCu 4 / L. Because of the fast dissolution rate of Ti in the alloy, the reaction zone remains very thin (3-6 µm) whatever the reaction time. When the Ag-Cu eutectic alloy is saturated in titanium, dissolution no longer proceeds and a thicker reaction zone with a more complex layer sequence grows as the reaction time increases. Four elementary chemical interaction processes have been identified in addition to Ti dissolution in the liquid alloy. These are growth of reaction layers on Ti by solid state diffusion, nucleation and growth from the liquid of TiCu 4 , isothermal solidification of silver and, finally, chemical conversion of the Cu-Ti compounds by reaction-diffusion in the solid state. A mechanism combining these processes is proposed to account for the constitution of Ti/ Ag-Cu/ Ti joints brazed at 780-800 °C.
“…After corrections for atomic number, absorption and fluorescence, the atomic contents of Ag, Cu and Ti were obtained with an accuracy better than ± 0.5 at%. It had been previously verified by X-ray powder diffraction [7] that the crystalline phases for which each interface reaction layer or crystal analysed were effectively obtained under the same heat-treatment conditions.…”
Section: Methodsmentioning
confidence: 84%
“…For these reasons, it was decided to further investigate the chemical interaction between titanium and the eutectic Ag-Cu alloy at temperatures down to 780 °C, the temperature of the eutectic transformation. In the first approach at investigating the kinetics of compound formation in the Ag-Cu-Ti system, cold-pressed mixtures of Ag, Cu and Ti powders were heated at 700-860 °C and characterized [7]. In the present work, additional experiments have been carried out at 780-800 °C on Ti/Ag-Cu semi infinite couples and Ti/Ag-Cu/Ti sandwiches in order to determine the extent and constitution of the interface reaction zone formed between solid Ti and liquid Ag-Cu eutectic alloy.…”
Reaction zones formed at 790 °C between solid titanium and liquid Ag-Cu eutectic alloys (pure and Ti-saturated) have been characterized. When pure Ag-Cu eutectic alloy with 40 at.% Cu is used, the interface reaction layer sequence is: αTi / Ti 2 Cu / TiCu / Ti 3 Cu 4 / TiCu 4 / L. Because of the fast dissolution rate of Ti in the alloy, the reaction zone remains very thin (3-6 µm) whatever the reaction time. When the Ag-Cu eutectic alloy is saturated in titanium, dissolution no longer proceeds and a thicker reaction zone with a more complex layer sequence grows as the reaction time increases. Four elementary chemical interaction processes have been identified in addition to Ti dissolution in the liquid alloy. These are growth of reaction layers on Ti by solid state diffusion, nucleation and growth from the liquid of TiCu 4 , isothermal solidification of silver and, finally, chemical conversion of the Cu-Ti compounds by reaction-diffusion in the solid state. A mechanism combining these processes is proposed to account for the constitution of Ti/ Ag-Cu/ Ti joints brazed at 780-800 °C.
“…[12,13,20,[34][35][36] However, contrary to the present observations, Shiue et al [19] and Shafiei et al [20] reported the formation of the Cu 4 Ti phase in the BZ, whereas they did not report the formation of Cu 3 Ti 2 phase which formed conspicuously in the present study. Andrieux et al [40] in an experimental investigation on the phase stability study on the Cu-Ti system showed that the Cu 3 Ti 2 phase is stable and can form by solid state reaction in a temperature range of 1063 K to 1133 K (790 C to 860 C). The presence of Cu-Ti-based amorphous phase in the BZ, as shown earlier, signifies that the entire melt did not transform into crystalline phases upon solidification.…”
Section: B Phase Formation In the Braze Zonementioning
Microstructural evolution and interfacial reactions during vacuum brazing of grade-2 Ti and 304L-type stainless steel (SS) using eutectic alloy Ag-28 wt pct Cu were investigated. A thin Ni-depleted zone of a-Fe(Cr, Ni) solid solution formed on the SS-side of the braze zone (BZ). Cu from the braze alloy, in combination with the dissolved Fe and Ti from the base materials, formed a layer of ternary compound s 2 , adjacent to Ti in the BZ. In addition, four binary intermetallic compounds, Cu 3 Ti 2 , Cu 4 Ti 3 , CuTi and CuTi 2 formed as parallel contiguous layers in the BZ. The unreacted Ag solidified as islands within the layers of Cu 3 Ti 2 and Cu 4 Ti 3 . Formation of an amorphous phase at certain locations in the BZ could be revealed. The b-Ti(Cu) layer, formed due to diffusion of Cu into Ti-based material, transformed to an a-Ti + CuTi 2 eutectoid with lamellar morphology. Tensile test showed that the brazed joints had strength of 112 MPa and failed at the BZ. The possible sequence of events that led to the final microstructure and the mode of failure of these joints were delineated.
“…In Mg-(Ti + Cu) BM , in addition to Mg, Ti, Cu and Mg 2 Cu phases, low intensity peaks corresponding to Ti-Cu intermetallic phase can be seen; in contrast, in the un-ball milled, directly added Mg-Ti-Cu these peaks are not prominent. Considering that the formation enthalpies of various Ti-Cu intermetallics phases such as TiCu, TiCu 4 , TiCu 2 , Ti 2 Cu 3 , Ti 3 Cu 4 , Ti 2 Cu, Ti 3 Cu and TiCu 3 are close to each other, the reaction between Ti and Cu can result in any of these intermetallics phases [24][25][26][27][28]. On comparing the experimental diffraction peaks with the standard powder diffraction data, it can be associated to either Ti 2 Cu 3 or Ti 3 Cu phase.…”
Section: X-ray Diffractionmentioning
confidence: 99%
“…On comparing the experimental diffraction peaks with the standard powder diffraction data, it can be associated to either Ti 2 Cu 3 or Ti 3 Cu phase. However, as the Ti 2 Cu 3 intermetallic phase formation occurs only at ~780 °C to 860 °C and also at a much slower cooling rate, the observed Ti-Cu intermetallics peaks can hence be identified as Ti 3 Cu [25]. …”
Abstract:In this study, metallic elements that have limited/negligible solubility in pure magnesium (Mg) were incorporated in Mg using the disintegrated melt deposition technique. The metallic elements added include: (i) micron sized titanium (Ti) particulates with negligible solubility; (ii) nano sized copper (Cu) particulates with limited solubility; and (iii) the combination of micro-Ti and nano-Cu. The combined metallic addition (Ti + Cu) was carried out with and without preprocessing by ball-milling. The microstructure and mechanical properties of the developed Mg-materials were investigated. Microstructure observation revealed grain refinement due to the individual and combined presence of hard metallic particulates. The mechanical properties evaluation revealed a significant improvement in microhardness, tensile and compressive strengths. Individual additions of Ti and Cu resulted in Mg-Ti composite and Mg-Cu alloy respectively, and their mechanical properties were influenced by the inherent properties of the particulates and the resulting second phases, if any. In the case of combined addition, the significant improvement in properties were observed in Mg-(Ti + Cu) BM composite containing ball milled (Ti + Cu) particulates, when compared to direct addition of Ti and Cu particulates. The change in particle morphology, formation of Ti 3 Cu intermetallic and good interfacial bonding with the matrix achieved due to preprocessing, contributed to its superior strength
OPEN ACCESSMetals 2012, 2 275 and ductility, in case of Mg-(Ti + Cu) BM composite. The best combination of hardness, tensile and compressive behavior was exhibited by Mg-(Ti + Cu) BM composite formulation.
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