scholarly journals Effect of annealing on recrystallization of GAP particles of Fe-Nd-B system alloy

Author(s):  
V Chaika ◽  
V Savin ◽  
M Sorokovikov ◽  
A Marukhin ◽  
A Martyushev
Keyword(s):  
Author(s):  
N.N. Zagirov ◽  
Yu.N. Loginov ◽  
E.V. Ivanov ◽  
V.G. Kuz’min

The problem of chip processing of aluminum alloy containing scandium is considered. The difficulty of remelting due to easy oxidation of the alloy components is noted. It is proposed to dispose of the shavings without transferring the metal to liquid state. The aim of the work is to construct technological scheme for the processing of waste chips of the Al—Mg—Sc alloy formed as result of machining cast billets by cutting. Results of experiments including cold briquetting, hot extrusion and drawing are presented. The mechanical properties of the product obtained according to several variants of the technological scheme are measured. The possibility of continuous drawing of semi-finished product is shown. The conclusion is made about the possibility of using the scheme in the production process.


2020 ◽  
Vol 989 ◽  
pp. 577-582
Author(s):  
I.E. Illarionov ◽  
T.R. Gilmanshina ◽  
A.A. Kovaleva

The purpose of this work is to study the structure and mechanical properties of an aluminum – magnesium system alloy after various types of heat treatment (quenching and ageing). The microstructure of an alloy has been studied by means of Zeiss OBSERVER.D1m microscope combined with a camera and image display on a monitor screen. Micro X-ray spectral analysis was performed by means of Carl Zeiss EVO 50 scanning electron microscope. The micro-hardness of the samples has been measured on prepared metallographic sections by means of DM8 micro-hardness meter. In the course of the process it has been found that quenching the Al-12,78% Mg alloy from temperatures of 430–440 ° C does not lead to the formation of a single-phase solid solution. Ageing at 100 ° C enables the formation of secondary phases. It was noted that with an increase in the quenching temperature, the micro-hardness increases slightly. An increase in the exposure time doesn’t influence greatly the micro-hardness of the alloy, while the structure remains practically unchanged.


2019 ◽  
Author(s):  
E. N. Stepanova ◽  
G. P. Grabovetskaya ◽  
I. P. Mishin ◽  
O. N. Lykova ◽  
A. D. Teresov

Author(s):  
E A Sarkeeva ◽  
V D Sitdikov ◽  
G I Raab ◽  
W Wei ◽  
I V Alexandrov

2019 ◽  
Vol 105 (3) ◽  
pp. 358-362
Author(s):  
Hidekazu Todoroki
Keyword(s):  

1997 ◽  
Vol 46 (6) ◽  
pp. 665-670
Author(s):  
Hideaki MATSUOKA ◽  
Yukio HIROSE ◽  
Yoichi KISHI ◽  
Kenji HIGASHI

1977 ◽  
Vol 39 (1) ◽  
pp. K21-K23 ◽  
Author(s):  
V. S. Postnikov ◽  
V. V. Postnikov ◽  
V. S. Zheleznyi

2017 ◽  
Vol 2017 ◽  
pp. 1-12 ◽  
Author(s):  
José G. Miranda-Hernández ◽  
Héctor Herrera-Hernández ◽  
Carlos O. González-Morán ◽  
Jesús Noé Rivera Olvera ◽  
Ivanovich Estrada-Guel ◽  
...  

Mechanical ball milling assisted by sintering in the solid state was used in this research to produce the Zn-Nix system alloy. The derivative powder compositions of Zn-Nix (x = 0, 5, 10, 15, and 20 wt.%) were obtained to study the Ni effects on the microstructural and mechanical properties. It is worth remarking that conventional methods are not appropriate for the manufacture of the Zn-Nix system alloy. The morphological structure and phases were examined by optical microscopy, X-ray diffraction, and SEM/EDS elemental mapping, whereas the mechanical behavior was accomplished by means of a diamond indentation print (Hardness Vickers). The results showed that the intermetallic γ-ZnNi phase did not form during milling time (<4 h); it appears after the sintering process, which is associated with atomic diffusion mechanism through grain boundary at the minimum interfacial energy (ΔG256°C = −13.83 kJ·mol−1). The powder Zn-Ni10 was found to have better properties. Semispherical coarser particles were seen into the metal matrix (Zn δ-hcp structure) as segregates; however, each particle contains an intermetallic compound Zn-Ni that encloses the Ni (α-fcc structure) pure phase. The Ni-α phase was then transformed into a γ-ZnNi intermetallic compound which shifts to higher values of mechanical hardness from about 60 HV to 400 HV units.


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