Diffraction study of spinodal decomposition in Cu-10 w/o Ni-6 w/o SN

Ditchek, B. M.; Schwartz, L. H.

doi:10.1016/0001-6160(80)90157-1

Cited by 74 publications

(17 citation statements)

References 17 publications

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“…Additionally, in the early stage of spinodal decomposition, the composition fluctuation profile exhibited a sinusoidal wave. 6,14) Therefore, a conclusive description of the interfacial energy between the 0 phase and ordered k 0 particles cannot be given in the present study.…”

Section: Resultsmentioning

confidence: 83%

Effect of Carbon on Spinodal Decomposition in Fe-26Mn-20Al-C Alloys

et al. 2011

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The supersaturated austenite () phase decomposed into fine C-rich ordered k 0 particles and C-depleted 0 phase during quenching in alloys with 5:5 C 8:0 at%. The misfit between k 0 particles and 0 phase decreased with increasing carbon content. The strain energy increased dramatically as carbon content approached slightly below 5.5 at%. Undercooling may be insufficient to overcome the strain energy effects, thus leading to the absence of spinodal decomposition and k 0 particles in the present and prior austenitic FeMnAlC alloys with 3:1 C 5:2 at% under the as-quenched condition. Additionally, both the amount of ordered k 0 particles and the carbon concentration in the k 0 particles increased with increasing carbon content of the alloy. These results revealed that a higher degree of carbon supersaturation in the initial phase might promote a tendency toward C-rich k 0 particle formation during quenching.

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Section: Resultsmentioning

confidence: 83%

Effect of Carbon on Spinodal Decomposition in Fe-26Mn-20Al-C Alloys

et al. 2011

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“…1 that all sidebands are asymmetric and in all alloys the sidebands on the low-angle side are of higher intensity. Although this asymmetry in the sidebands may in principle be explained by the effects of strain on the diffraction pattern, there is no satisfactory theory for this effect [1]. Similar asymmetric sidebands were observed in Cu-Ni-based alloys [7][8][9][10][11][12].…”

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confidence: 88%

“…Nevertheless, the modulation in lattice spacing leads to contributions to the satellite intensity which depend on the amplitude and wavelength of the composition. Therefore, when both effects occur the satellites are complex diffuse phenomena [1]. Decomposition of supersaturated solid solutions within the spinodal region of the equilibrium diagram produces fluctuations in the elastically soft directions in the crystal.…”

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confidence: 99%

Sidebands in spinodal Cu-Ni-Cr alloys and lattice parameters inquiries

Fındık

1993

J Mater Sci Lett

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Spinodal decomposition causes a modulation in the lattice spacing and lattice chemistry, and hence in the scattering factor. The intensity and position of the satellites about the Bragg peaks is influenced by these effects. Depending on the composition only, the modulation in the scattering factor provides a contribution to the satellite intensity. Nevertheless, the modulation in lattice spacing leads to contributions to the satellite intensity which depend on the amplitude and wavelength of the composition. Therefore, when both effects occur the satellites are complex diffuse phenomena [1]. Decomposition of supersaturated solid solutions within the spinodal region of the equilibrium diagram produces fluctuations in the elastically soft directions in the crystal. Sidebands are produced in spinodal alloys with contributions from both the scattering factor variation [2] and the lattice parameter variation [3,4]. In this study sidebands in spinodal Cu-Ni-Cr alloys and lattice parameters inquiries were investigated and compared with values from previous studies.In order to obtain all nominal compositions, pure copper (99.999%), nickel (99.9%) and chromium (99.9%) were melted in a vacuum arc-furnace. Chemical analysis of the alloys by X-ray energydispersive analysis showed the actual compositions to be (wt%): . After casting and checking the composition, the cast buttons were solution-treated and rapidly quenched as defined in [5,6].Heat treatments were carried out in a vertical tube furnace. The temperature within the hot zone of the furnace was controlled to an accuracy of +5 °C. Ageing times from 5 min to 3 weeks were employed and after the ageing all specimens were rapidly quenched into iced water. After the heat-treatments the specimens were examined by electron microscopy and X-ray diffraction as described in [5,6].In the early stages of ageing, the characteristics of spinodal decomposition observed in the X-ray diffraction and in the electron microscope were sidebands in the X-ray diffraction, a periodic structure in the electron micrographs and a constant wavelength (z).In order to carry out sideband analysis in X-ray diffraction, step-scans were made from 47 to 54 ° of 20. The scanning speed was 0.25 ° min -1 . This region of 20-space covered both the sidebands and the 2 0 0 Bragg peak. The 200 peak was used because it supplied the best combination of intensity and 338 sideband resolution. To obtain sidebands under these conditions, all alloys were scanned and sidebands were observed in all alloys. Sidebands were observed in the range 300-600 °C in the 2.5Cr and 5Cr asymmetrical alloys, and at 300-800 °C in the 10Cr and 15Cr symmetrical alloys (Fig. 1). However, sidebands were not very clear at 500-600 °C in the 5Cr alloy, at 800 °C in 10Cr and at 600 and 800 °C in 15Cr alloy. The reason for this might be due to no fitness of the combination of intensity and sideband resolution in the (200) peak for these alloys for particular temperatures. Similar sideband analyses were carried out by Rao et al. [7][8][9] fo...

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“…[1][2][3][4][5][6][7][8][9][10][11][12] Among the high-strength Cu alloys, Cu-Ni-Sn alloys have gathered strong attention as possible low-cost substitutes for Cu-Be alloys. [1][2][3][4][5][6][7][8][9][10][11][12] The Cu-Ni-Sn alloys contain a relatively high amount of expensive Ni and Sn, which acts as a barrier for the wide spread use of the alloys. The low hot workability further limits the application.…”

Section: Introductionmentioning

confidence: 99%

Tensile anisotropy in Cu-Ni-Mn-Sn-Al alloys

Han,

Sohn,

Kim

et al. 2004

Metall Mater Trans A

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In the present study, the tensile anisotropy of age-hardened Cu-6Ni-2Mn-2Sn-2Al, Cu-6Ni-2Mn-2Sn-2Al, and Cu-6Ni-2Mn-5Al alloy sheets, either perpendicular or parallel to the rolling direction, was examined. It was found that age-hardened Cu-Ni-Mn-Sn-Al alloys have higher tensile strength along the T orientation than L orientation at high rolling ratios. Such a trend was most notable in the high Al containing Cu-6Ni-2Mn-5Al alloy among the alloys studied. At high rolling ratios, well-developed deformation bandlike structures were observed to be mostly aligned perpendicular to the rolling direction for each alloy. These deformation bandlike structures appeared to be responsible for the higher tensile strength along the T orientation. The transmission electron microscopy (TEM) examination demonstrated that the deformation bandlike structures consisted of tangled dislocation networks, which were further thickened with the addition of Al or the reduction of Sn. The stacking fault energy (SFE) of Al and Sn, as related to the ease of cross-slip, is believed to be responsible for the present observation.

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Diffraction study of spinodal decomposition in Cu-10 w/o Ni-6 w/o SN

Cited by 74 publications

References 17 publications

Effect of Carbon on Spinodal Decomposition in Fe-26Mn-20Al-C Alloys

Effect of Carbon on Spinodal Decomposition in Fe-26Mn-20Al-C Alloys

Sidebands in spinodal Cu-Ni-Cr alloys and lattice parameters inquiries

Tensile anisotropy in Cu-Ni-Mn-Sn-Al alloys

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