Dislocation–Substructure–Strengthening and Mechanical–Thermal Treatment of Metals

McElroy, R.J.; Szkopiak, Z. C.

doi:10.1179/095066072790137684

Cited by 144 publications

(21 citation statements)

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“…Equation (2) has been shown 34) to hold for a wide variety of materials. Further, an additional approximate relationship between stored energy (E Stor ) and the dislocation density can be used 3) : In Eq.…”

Section: Resultsmentioning

confidence: 99%

Separation of Static Recrystallization and Reverse Transformation of Deformation-induced Martensite in an Austenitic Stainless Steel by Calorimetric Measurements

2003

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Section: Resultsmentioning

confidence: 99%

Separation of Static Recrystallization and Reverse Transformation of Deformation-induced Martensite in an Austenitic Stainless Steel by Calorimetric Measurements

2003

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“…The internal energy change across the shock front is calculated from Eq. [8] assuming an adiabatic process. The work done on the solid during rarefaction is calculated by assuming the relief process is isentropic (11).…”

Section: A Production Of Shock Waves: Determination Of the Shock Wavmentioning

confidence: 99%

Residual Microstructure - Mechanical Property Relationships in Shock-Loaded Metals and Alloys

Murr

1981

Shock Waves and High-Strain-Rate Phenomena in Metals

111

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“…17) Much lower SFE was reported in the solution-treated specimen of Inconel X-750 alloy (0.09 J/m 2 ), 18) while the SFE of the SUS304 steel was estimated to be 0.011 J/m 2 according to Breedis. 19) Temperature measurements of chips were not made in this study.…”

Section: Generation Of Equiaxed Submicron Grain Structurementioning

confidence: 95%

Microstructures of Machined Chips in Pure Titanium, Pure Iron and 0.83%C Steel

Tanaka

Fujita

2013

ISIJ Int.

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Microstructures were examined on the chip specimen of pure titanium with close-packed hexagonal (cph) structure (α-Ti, the shear strain, γ, is ~22), and those of pure iron (α-Fe, γ ≈ 7.5) and 0.83%C steel which had originally pearlite structure (γ ≈ 7.5) with body-centered cubic (bcc) structure by the FE-SEM/ EBSP method and optical microscopy. The hardness of the chip specimens was also measured and compared to that of the original materials. UFGed materials could be produced at relatively small shear strain (~7.5) in pure iron and 0.83%C steel. The average grain diameter of the chip specimen was slightly larger in the 0.83%C, because lamellar cementite phase in original pearlite structure hindered the formation of submicron grains. The hardness of the chip specimens increased with increasing shear strain, and the hardness of the chip specimen with γ ≈ 7.5 (391 Hv) was ~4 times as much as that of the original material (93.9 Hv) in pure iron. However, it was impossible to produce the ultra-fine grained materials by machining of α-Ti even at γ ≈ 22. According to the experimental results obtained so far, the number of slip systems (crystal structure) as well as shear strain seems to be one of the important factors controlling the generation of equiaxed submicron grain structure. Higher stacking fault energy is favorable for cross-slip or climb of dislocations in dynamic recovery which probably governs the generation of submicron grains.

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Dislocation–Substructure–Strengthening and Mechanical–Thermal Treatment of Metals

Cited by 144 publications

References 0 publications

Separation of Static Recrystallization and Reverse Transformation of Deformation-induced Martensite in an Austenitic Stainless Steel by Calorimetric Measurements

Separation of Static Recrystallization and Reverse Transformation of Deformation-induced Martensite in an Austenitic Stainless Steel by Calorimetric Measurements

Residual Microstructure - Mechanical Property Relationships in Shock-Loaded Metals and Alloys

Microstructures of Machined Chips in Pure Titanium, Pure Iron and 0.83%C Steel

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