Elastic constants and internal friction of martensitic steel, ferritic-pearlitic steel, and α-iron

Kim, Sudook A.; Johnson, Ward L.

doi:10.1016/j.msea.2006.11.147

Cited by 171 publications

(42 citation statements)

References 24 publications

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“…More recently, single-crystal elastic constants of the martensite phase in ferrite-martensite two-phase mixtures were determined, together with those of the ferrite phase, by resonant ultrasound spectroscopy. 15) The elastic moduli of polycrystals derived from them are lower than those of iron, in accordance with the conclusion of Speich and Leslie.…”

Section: Introductionsupporting

confidence: 86%

“…[5][6][7][8][9][10] The elastic moduli of iron-carbon martensite were reported by several researchers. [11][12][13][14][15] Schmidtmann et al 11) measured Young's modulus of quenched carbon steels by the resonance vibration method and found that it decreases with increasing the C content. Speich et al 13) obtained similar results for both Young's modulus and shear modulus of quenched Fe-C alloys.…”

Section: Introductionmentioning

confidence: 99%

“…It is the purpose of this work to theoretically evaluate the singlecrystal elastic constants of iron-carbon and iron-nitrogen martensites by means of ab initio calculations. As mentioned above, the single-crystal elastic constants of Fe-C martensite were evaluated by sophisticated measurements and analysis of ferrite-martensite two-phase mixtures, 15) but only at a single C content. A difficulty in experiment is, either of single-phase or in two-phase mixtures, martensites always involve high density of crystal defects and are accompanied with internal stresses arising from the structural transformation; experimentally determined values of elastic modulus may be influenced by these defects and stresses.…”

Section: Introductionmentioning

confidence: 99%

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Elastic Properties of Fe–C and Fe–N Martensites

Souissi

Numakura

2015

ISIJ International

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Single-crystal elastic constants of bcc iron and bct Fe-C and Fe-N alloys (martensites) have been evaluated by ab initio calculations based on the density-functional theory. The energy of a strained crystal has been computed using the supercell method at several values of the strain intensity, and the stiffness coefficient has been determined from the slope of the energy versus square-of-strain relation. Some of the third-order elastic constants have also been evaluated. The absolute magnitudes of the calculated values for bcc iron are in fair agreement with experiment, including the third-order constants, although the computed elastic anisotropy is much weaker than measured. The tetragonally distorted dilute Fe-C and Fe-N alloys exhibit lower stiffness than bcc iron, particularly in the tensor component C 33 , while the elastic anisotropy is virtually the same. Average values of elastic moduli for polycrystalline aggregates are also computed. Young's modulus and the rigidity modulus, as well as the bulk modulus, are decreased by about 10% by the addition of C or N to 3.7 atomic per cent, which agrees with the experimental data for Fe-C martensite.

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Section: Introductionsupporting

confidence: 86%

Section: Introductionmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

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Elastic Properties of Fe–C and Fe–N Martensites

Souissi

Numakura

2015

ISIJ International

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“…A detailed modern summary and review of various values is offered in Hess et al [46]. It should be recognised that there are great technical difficulties in reliably measuring the elastic modulus because it is dependent on the strain path, the chemical composition, the orientation of the crystal lattice within the specimen and the heat treatment, whilst the stiffness of the measuring rig and minor errors in loading alignment may also introduce experimental scatter [46][47][48].…”

Section: Processing Of Measured Stress-strain Curvesmentioning

confidence: 99%

Statistical analysis of the material properties of selected structural carbon steels

et al. 2015

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Modern design procedures for steel structures increasingly employ more realistic representations of the stress-strain behaviour of steel rather than a simple ideal elasticplastic. In particular, for buckling failure modes in the plastic range, stresses in excess of the yield stress are always involved, together with a finite post-yield stiffness.Moreover, the 'plastic plateau' in buckling curves for stocky structural members cannot be predicted computationally without a significant strain hardening representation. If a good match is to be sought between experiments and computational predictions in the elastic-plastic zone, strain hardening must be included. Most studies have either used individual laboratory measured stress-strain curves or educated guesswork to achieve such a match, but it is not at all clear that such calculations can reliably be used for safe design since the same hardening properties may not exist in the next constructed structure, or even within a different batch of the same steel grade.A statistical exploration is presented here to assess the reliable magnitudes of postyield properties in common structural grade steels. For simplicity, only two critically important parameters are sought: the length of the yield plateau and the initial strain hardening tangent modulus. These two are selected because they both affect the elastic-plastic buckling of stockier structural elements. The statistical analyses exploit proprietary data acquired over many years of third-party auditing at the Karlsruhe Institute of Technology to explore possible regressed relationships between the postyield properties. Safe lower bounds for the selected properties are determined.

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“…XRD analysis has been done on Cu 3-7 , ferritic-pearlitic steel 8 , Aluminium 9-10 martensitic steel [11][12] , pearlitic steel [13][14][15] , nickle 16 ,FeN 17 , 10Cr-5W heat resistant steels 18 . The elaborate study on elastic constants 19 for hypereutectoid steel and dislocations contrast factors [20][21][22] of cubic crystals is available in literature. The present study is carried out to correlate the mechanical properties, microstructural changes as well as detailed X-ray diffraction line profile analysis for better understanding of cold drawing process of hypereutectoid steel wires.…”

Section: Introductionmentioning

confidence: 99%

X-ray Diffraction Analysis of Severely Cold Deformed Hypereutectoid Steel Wire

Bargujer¹,

Suri

Belokar

2015

DSJ

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Hypereutectoid steel wire rod of diameter 6.40 mm is lead patented in lead bath of an electric powered furnace and then it is cold drawn through converging conical dies in a die sequence up to 2.50 mm diameter. The drawn wires subjected to different true strain are analysed using line profile X-ray diffraction methods. The classical Williamson-Hall plot as well as modified Williamson-Hall plot of drawn wire specimens of different true strain is plotted. The theoretical as well as experimental value of q is evaluated. The q is a parameter which depends up on elastic constant of the crystal and type of dislocations. The changes in nature of dislocations from edge dislocations to screw dislocations are calculated against true strain and are verified by scanned electron microscopy's micrograph of drawn wire.keywords: Hypereutectoid steel wire, Williamson-Hall plot, spring, true strain, x-ray diffraction, elastic constant and full width half maximum, FWHM

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Elastic constants and internal friction of martensitic steel, ferritic-pearlitic steel, and α-iron

Cited by 171 publications

References 24 publications

Elastic Properties of Fe–C and Fe–N Martensites

Elastic Properties of Fe–C and Fe–N Martensites

Statistical analysis of the material properties of selected structural carbon steels

X-ray Diffraction Analysis of Severely Cold Deformed Hypereutectoid Steel Wire

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