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Abstract
In the present study, a Cu–6Ni–6Sn–0.6Si alloy is fabricated through frequency induction melting, then subjected to solution treatment, rolling, and annealing. The phase composition, microstructure evolution, and transition mechanism of the Cu–6Ni–6Sn–0.6Si alloy are researched systematically through simulation calculation and experimental characterization. The ultimate as-annealed sample simultaneously performs with high strength and good ductility according to the uniaxial tensile test results at room temperature. There are amounts of precipitates generated, which are identified as belonging to the DO22 and L12 phases through the transmission electron microscope (TEM) analysis. The DO22 and L12 phase precipitates have a significant strengthening effect. Meanwhile, the generation of the common discontinuous precipitation of the γ phase, which is harmful to the mechanical properties of the copper–nickel–tin alloy, is inhibited mightily during the annealing process, possibly due to the existence of the Ni5Si2 primary phase. Therefore, the as-annealed sample of the Cu–6Ni–6Sn–0.6Si alloy possesses high tensile strength and elongation, which are 967 MPa and 12%, respectively.
Highlights
Published: 10 September 2021The copper–nickel–tin alloy is one of the important copper alloys that is widely used in modern industries such as aerospace, rail transit, heavy-duty machinery, marine engineering, etc. [1–7] In recent years, many researchers have been attracted to the study of how to improve the mechanical properties and conductivity of copper–nickel–tin alloys such asCu–15Ni–8Sn [8–10] and Cu–9Ni–6Sn, with high contents of Ni and Sn elements [11,12].It is well known that the mechanical properties depend on the microstructures; the microstructure evolution and influencing factors should be researched systematically
Alloying elements added into the copper–nickel–tin alloys can affect the microstructures of the alloys, causing the mechanical properties of the alloys to vary [13–21]
A lot of research shows that the segregation suppression of Sn during the solidification process and the inhibition of the discontinuous precipitation of the γ phase during the heat treatment process are two difficulties which can directly influence their comprehensive performance and application in copper–nickel–tin alloys with high Ni and Sn contents [22–26]
Summary
The copper–nickel–tin alloy is one of the important copper alloys that is widely used in modern industries such as aerospace, rail transit, heavy-duty machinery, marine engineering, etc. [1–7] In recent years, many researchers have been attracted to the study of how to improve the mechanical properties and conductivity of copper–nickel–tin alloys such as. A lot of research shows that the segregation suppression of Sn during the solidification process and the inhibition of the discontinuous precipitation of the γ phase during the heat treatment process are two difficulties which can directly influence their comprehensive performance and application in copper–nickel–tin alloys with high Ni and Sn contents [22–26]. Publisher’s Note: MDPI stays neutral with regard to jurisdictional claims in published maps and institutional affiliations Sn added, such as Cu–6Ni–6Sn, such as Cu–6Ni–6Sn, alloys shouldwith low be studied, but seldom been researched so far. Avoiding numerous generations of the discontinuous precipitation of theAt γ phase in the Cu–6Ni–6Sn alloy would significantly improve its mechanical properties. The phase composition, microstructure evolution, mechanical properties the Cu–6Ni–6Sn–0.6Si alloy during the whole process areand observed and properties of the. 0.6Si, which can simultaneously perform with high strength and good ductility This may may even provide important references for the preparation of copper–nickel–tin alloys.
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