bluuebunny/crossref_metadata_2025_split huggingface dataset:
Orientation Selection During Static Recrystallization of Cross Rolled Non‐Oriented Electrical Steels
Authors: Kestens L. , Jonas J. J. , van Houtte P. , Aernoudt E. 
Published: April 2008

Very sharp deformation textures, with single maxima of more than 50x random centred on the rotated
cube component ({001}<110>), were produced by submitting a non‐oriented electrical steel sheet to various sequences of cross‐rolling. The cold rolled sheets were subsequently annealed at 730ºC for 3 min. The resulting recrystallization textures were much weaker than the cold rolling textures, displaying
maxima of about 5x random at locations some distance away from the {001}<110> cross rolling
component.Due to the very sharp character of the rolling texture, the conventional low and high stored energy
nucleation mechanisms were effectively prevented from operating. Thus orientation selection could only
take place by the selective growth of nuclei external to the dominant rolling component. Quantitative
analysis of the experimental ODFs revealed that the rolling and recrystallization components are related
by Σ27 (31.6º<110>) and Σ7c (38.2º<111>) coincidence site lattice (CSL) orientation relations.
Simulations of the annealing texture on the basis of random nucleation and combined Σ27‐Σ7c selective
growth produced reasonable agreement between the predictions and the experimental results.
Preferential Growth of Secondary Recrystallized Goss Grains During Secondary Recrystallization Annealing in Grain Oriented Silicon Steel Sheet
Authors: Inokuti Yukio 
Published: April 2008

Computer color mapping of the primary and secondary recrystallized Goss grains which formed during
secondary recrystallization annealing was performed with an image analyzer, using crystallographic
orientation data measured by a Kossel examination.The preferential growth of secondary recrystallized Goss grains took place in a defined zone at the
1/10 depth beneath the surface of the as‐decarburized and primary recrystallized steel sheet.With short‐time secondary recrystallization annealing, a secondary recrystallized Goss grain with an
80 × 50 μm elliptical form grew preferentially in its defined zone.With further secondary recrystallization annealing, four secondary recrystallized Goss grains coalesced
to sizes of 100‐350 μm, and exhibited a zigag morphology due to a difference in the degree of
consumption of primary recrystallized grains by the secondary recrystallized Goss grains. Primary
recrystallized grains with {100}<001>, {100}<0kl>, and {100}<011> orientations were resistant to comsumption by secondary recrystallized Goss grains, but those with {110}<001> and {111}<112> orientations were easily consumed by secondary recrystallized Goss grains.With long‐time secondary recrystallized annealing, the full thickness of the silicon steel sheet was
occupied by giant secondary recrystallized Goss grains, which ultimately extended to lengths of several
millimeters. The orientation of the secondary recrystallized Goss grains is highly aligned to the [001]
axis rather than the (110) crystallographic plane.It is considered that the nuclei for preferentially developing secondary recrystallized grains are
inherited by the structure memory from highly oriented (110)[001] areas at the 1/10 depth beneath the
surface of hot‐rolled silicon steel sheet.
Mapping the Grain‐Boundary Character‐(Free) Energy Linkage in Polycrystalline Materials
Authors: Adams Brent L. 
Published: April 2008

Relationships between structure‐sensitive macroscopic properties and the grain boundary network are known to depend upon the intrinsic variability of the local physico‐chemical properties of the boundaries and upon how these are distributed and connected in the network. Progress towards acquiring a data base linking the local properties of grain boundaries with their geometrical character (lattice misorientation and inclination) has been hampered by the rate at which grain boundary structure can be experimentally determined, by the opacity of polycrystalline materials, and by the very large number of physically distinctive (geometrical) characteristics of grain boundaries which occur in nature.Described in this paper is a perspective on modern opportunities to solve the comprehensive inverse problem relating the thermodynamic properties of grain boundaries to their geometrical type over the full (five‐parameter) fundamental zone. The advent of rapid, automated measurements of local lattice orientation (orientation imaging microscopy), when coupled with precision serial sectioning, makes it feasible now to characterize the local crystallographic and geometrical features of very large numbers of grain boundaries and triple junctions. Such data can be analyzed within a classical framework in order to extract the thermodynamic properties mapping. This paper examines the opportunities and challenges associated with the requisite measurements and analysis.This paper is dedicated to the memory of Professor Hsun Hu, whose kind encouragement and penetrating insight has inspired and lifted a generation of young scientists.
Texture Effect in X‐Ray Analysis of Retained Austenite in Steels
Authors: Järvinen Matti 
Published: April 2008

A method is described that can be used for determining the retained austenite concentration in steel samples that have texture. The method is based on symmetrized harmonics expansion for the representation of the orientation distribution of the crystallites in the sample and it presumes the use of specimen spinner on the data collection.For demonstrating the application of this method integrated intensities of seven reflections from three steel samples with different degree of texture is measured using CuKα radiation and the retained austenite concentration is determined.
Influence of Initial Texture, Temperature and Total Strain on the Texture Development of Polycrystalline Pyrrhotite Ores in Deformation Experiments
Authors: Niederschlag Elke , Siemes Heinrich 
Published: April 2008

The development of the crystallographic preferred orientation (texture) of polycrystalline pyrrhotite from
Sullivan mine, Canada, and Cerro de Pasco, Peru was determined by neutron texture analyses before
and after experimental deformation. The pyrrhotite ore from Sullivan has an initial texture with a distinct
c‐axis maximum perpendicular to the foliation whereas the ore from Cerro de Pasco shows a weak
and moreover inhomogeneous texture within the specimen.The deformation texture and deformation behaviour of samples from Sullivan were investigated as
a function of temperature, total strain and the angle between the compression axis and the initial c‐axis
maximum. The deformation textures show the influence of different activated glide modes as a
function of the compression direction and temperature. Investigations of the deformation texture and
deformation behaviour of samples from Cerro de Pasco were carried out as a function of temperature,
total strain and strain rate. The inhomogeneous texture of the starting material did not allow to draw
conclusions about the texture development as a function of strain rate and temperature. Nevertheless
the preferred orientation of the c‐axes parallel to the compression axis becomes more evident with
increasing total strain.
2 Dimensional Dislocation Dynamics – A New Technique for the Simulation of Deformation Microtextures
Authors: Roters F. , Raabe D. 
Published: April 2008

A new technique for the simulation of microtexture evolution during cold deformation which is based
on 2 dimensional (2D) dislocation dynamics is presented. In the simulation all involved dislocations
are regarded as infinite straight line detects which are embedded in an otherwise isotropic linear elastic
medium. As the model is 2D only edge dislocations are considered.In the first simulation step the net local stresses are derived and used to calculate the resulting
dislocation motion. Dislocation multiplication, annihilation and reactions are taken into account. Thermal
activation is included. In the second step the local misorientations arising from the dislocation
distribution are calculated.This method shows in microscopic detail how misorientations are generated and distributed within
grains during plastic deformation.
Application of Anisotropic Texture Components
Authors: Eschner Th. , Fundenberger J.-J. 
Published: April 2008

The description of textures in terms of texture components is an established conception in quantitative
texture analysis. Recent developments lead to the representation of orientation distribution functions
as a weighted sum of model functions, each corresponding to one anisotropic texture component. As
was shown previously, an adequate texture description is possible with only a very small number of
anisotropic texture components. As a result, textures and texture changes can be described by a small
number of vivid parameters and their variations, namely by volume parts, half widths and ideal
orientations.The texture of a tensile tested commercial aluminum alloy was investigated by decomposition into
anisotropic components. The texture evolution during tensile testing is represented by the corresponding
changes of the component parameters and compared with results from an iterative series expansion
analysis.
Model Calculations of the Accuracy of Structure Factor Determination From Textured Powder Samples
Authors: Hedel R. , Bunge H. J. , Reck G. 
Published: April 2008

Crystal structure analysis is based on absolute values of structure factors |Fhkl|. These values can be measured by powder diffraction. In random powder diffraction many superpositions occur in the
diffraction diagram over the Bragg angle θ. If non‐random (textured) samples are used and intensity measurements are done in the three‐dimensional reciprocal space, i.e. over θ and the sample rotation angles αβ then these superpositions can be deconvoluted to a good deal. In order to perform this deconvolution a two‐step procedure was developed and was implemented in a computer code. In the first step the texture is determined from a low number of reflections having no or only two‐fold overlap. In the second step the deconvolution is done for all reflections. This includes the deconvolution of “systematically” overlapped reflections, e.g. those with the same h2 + k2 + l2 in cubic symmetry.Model calculations were performed in order to test the reliability and resulting accuracy of the deconvolution procedure depending on various experimental as well as modelling parameters. It is concluded that good resolution for superposed |Fhkl| can be reached up to reasonably high lattice parameters.The decisive accuracy limiting factor is texture determination in the first step of the procedure. It is concluded that it is necessary to employ texture analysis methods with higher angular resolving power and higher statistical accuracy than in conventional routine texture analysis. This is, however, possible with the existing modern texture diffractometers.
Influence of Sample‐Movement on Particle‐Randomization of Powder Samples in the Parallel‐Beam Geometry
Authors: Burger K. , Ihringer J. 
Published: April 2008

Today, from powder X‐ray diffraction the scientists want to obtain high resolution diffraction patterns with reliable Bragg‐reflection intensities. Two well‐known and closely connected obstacles on the way are texture and particle randomization of the sample, which strongly influence the measured intensities. In the work presented here, we examine the second problem.Especially with high resolution diffractometers, for well crystallized or highly absorbing samples the number of contributing crystals in the powder is too small, thus introducing significant errors in the profiles and measured intensities of Bragg‐reflections. This may be the major source of inaccuracy in data used for structure determination. Calculations of the error of the integrated intensities are presented, for the high resolution, parallel beam geometry at a synchrotron X‐ray source. Results exhibit errors of 40 % in the range of highest resolution for a sample of 3 μm crystals of corundum, with the sample at rest. To enhance randomization, several methods of sample‐movement are considered. A new effective method is proposed, where the rotation axis of the flat sample‐disk is slightly inclined out of the diffraction plane.
Generalization of the Orientation Distribution Function: Determination of Crystalline Orientations in any Section of the Specimen
Authors: Gaspard C. , Messien P. , Mignon J. 
Published: April 2008

A generalization of the O.D.F. representation has been proposed in such a way that its calculation is possible in any axes system of a material provided that is known in one particular system. Using an appropriate rotation matrix T(a,b,c) it is possible to compute crystallographic orientations (hkℓ)
[uvw] in any macroscopic plane of the material. This calculation method leads also to a direction distribution function which gives the angular distribution of the crystallographic direction [u1v1w1] in a macroscopic plane of the material.This analysis has been applied to the representation of texture and of slip directions in planes at 45 degrees from the directions RD, ND and TD of a mild steel deformed in equi‐biaxial expansion.
Plastic Deformation and Crystalline Texture in Equibiaxial Expansion
Authors: Gaspard C. , Messien P. , Mignon J. , Greday T. 
Published: April 2008

The classical three‐dimensional analysis (O.D.F.) has been extended in such a manner as to obtain the representation of the texture, and, more precisely, the distribution of the slip systems <111> {hkℓ} in the planes where shear stresses induced in equibiaxial expansion are maximum.Quantification of the slip systems configuration allows the development of a deformation model which takes into account the factors influencing the degree of stretchability of the steels. From this model it is possible to define true hardening rates and equibiaxiality coefficients characterizing the ability of the steel to distribute the deformation in the macroscopic shear planes.In association with the resistance to thinning defined by the configuration of the slip systems, the theoretical treatment makes it possible to grade different steels according to their experimental behavior.
Effect of Dynamic Strain Aging on the Plastic Anisotropy and Mechanical Properties of Low‐Carbon Phosphorus Steels
Authors: Spitzig W. A. , Hu Hsun , Sober R. J. 
Published: April 2008

The effects of a dynamic‐strain‐aging treatment,
as compared with a static‐strain‐aging treatment,
on plastic anisotropy and mechanical properties has been
determined for vacuum‐melted low‐carbon phosphorus steels
containing various amounts of silicon. It was found
that prestraining at 185°C, as compared with straining
at 22°C followed by aging for four hours at 100°C, resulted
in about twice the increase in yield strength
(90 versus 48 MPa) on subsequent tension testing at 22°C
and an improvement in rm values from about 1.8 to 2.0.Analyses of the textures and dislocation structures
of the steels after the two strain‐aging treatments and
after subsequent deformation at 22°C showed that a greater
dislocation density gives rise to the greater strengthening
of dynamic‐strain‐aged specimens, and a finer polyhedral
network of dislocation tangles is believed to be
the reason for their higher rm values.
Texture and Microstructure Evolution During Superplasticity of theMetal Matrix Composite PM 2014 Al–20% Al2O3
Authors: Kaibyshev R. , Kazyhanov V. 
Published: April 2008

The effects of superplastic deformation (SPD) on grain structure and texture evolution of
the Al 2014–20%Al2O3 composite produced via powder metallurgical method were
investigated in conjunction with surface relief observations. Samples were deformed in
tension at different strains in the range of true strain rates 10-4–100 S-1 at temperature
500C. It was found that SPD strains have a large effect on both texture and grain size. At
the initial stage of superplastic flow, deformation bands are formed in the aluminum
matrix along the tension direction. Simultaneously, the initial 〈111〉 fiber texture is broken and formation of 〈110〉 fiber texture takes place. Further strain up to
50% leads to grain structure change from banded structure to
nearly equiaxed. The 〈111〉 fiber
texture is restored and texture intensity decreases with increasing strain. Strain rate
dependence of texture developments showed evidence for dislocation activity in examined
strain range.The relation between microstructure evolution and texture development during
superplastic deformation of the PM 2014–20% Al2O3 composite is explained from the
viewpoint of cooperative grain boundary sliding (CGBS).
Fault Rocks of the Moine Thrust Zone: A Guide to Their Nomenclature
Authors: White S. 
Published: April 2008

The aim of this article is to extract from the existing literature a consistent nomenclature that can be used in the description of coherent fault rocks. The nomenclature is dealt with in this paper. Typical microstructures illustrating each is presented in a later paper (White et al ., 1982). It will be shown that a simple set of nomenclature can be extracted from the literature, so long as genetic connotations are kept to a minimum. The sequence, with increasing shear strain is country rock–protomylonite–blastomylonite–mylonite–ultramylonite if the rock has a well developed foliation; country rock–protocataclasite–cataclasite–ultracataclasite if it is without a foliation.It is emphasized that a mylonite is basically a fine‐grained schist that has formed within fault zones. It is the association with faulting that distinguishes a mylonite from a fine grain schist.
The Fabric of Polycrystalline Ice Deformed in Simple Shear: Experiments in Torsion, Natural Deformation and Geometrical Interpretation
Authors: Bouchez J. L. , Duval P. 
Published: April 2008

Three cylinders of artificial ice have been deformed in torsion at about –10℃ up to finite shear strains γ of 0.6, 0.95 and 2. The initial random lattice orientation rapidly evolves into a bimodal distribution of the basal slip planes as already observed by Kamb (1972) and Duval (1981) for low‐strains experiments near the melting point. For the γ = 0.6 and 0.95 experiments, one family of grains (> 50%) corresponds to basal planes tending to parallel the imposed shear plane; the basal planes of the other family make a broader maximum at about 60° from the shear plane. The direction of minimum concentration between the two populations approximately corresponds to the flattening plane or to the elongation direction of the strain ellipsoid. With increasing strain (γ = 2) the second submaximum vanishes and only the principal maximum parallel to the shear plane remains. This evolution is conformable with the data of Hudleston (1977) in a natural shear zone in glacial ice; it also compares remarkably well with Etchecopar′s (1977) geometrical computer model of simple shear in the same range of γ values. Single slip on the basal plane with no preferential slip direction in that plane can explain the analogy between fabrics in ice deformed in plane strain and fabrics obtained from the two‐dimensional computer model.The bimodal distribution reflects predominant slip on the basal plane; the progressively
increasing heterogeneous strain enhances internal distorsion, rigid body rotation and recrystallization of grains unfavorably oriented for further slip, leading to the unimodal distribution. The adequacy of fabric analyses to infer the strain regime and the sense of shear in plastically deformed rocks is strengthened.
Dynamic Recrystallization in a Naturally Deformed Albite
Authors: Gerald J. D. Fitz , Etheridge M. A. , Vernon R. H. 
Published: April 2008

Coarse‐grained, deformed albite occurs in veins within a blueschist from the Cazadero region, California. In some grains, deformation and recrystallization are concentrated in narrow shear zones less than 50 μm wide. We have examined the substructural progression across these zones by transmission electron microscopy (TEM), in an attempt to determine the details of the dynamic recrystallization mechanism. The misorientation across subgrain and recrystallized grain boundaries has been determined by analysis of electron diffraction patterns.Dynamic recrystallization apparently proceeded by the following stages: 1) the formation of a well‐ordered substructure from a more tangled, cell‐like array, 2) increasing misorientation between subgrains, 3) rapid growth of subgrains at a misorientation between 3° and 5° to produce new “grains” with straighter grain boundaries and lower internal dislocation densities and 4) continued deformation and rotation of the recrystallized grains with local grain‐boundary migration to maintain relatively equiaxed shapes. The ultimate recrystallized structure in the narrow deformation zones consists of grains misoriented by between 5° and at least 30°, most of them containing a well‐developed substructure.The combination of subgrain growth and rotation explains a number of features common to dynamically recrystallized minerals. The smaller subgrains present prior to growth and also within recrystallized grains form a population distinct from the larger subgrains and recrystallized grains of approximately equal size, which are those observed in an optical microscope. The smaller subgrains are visible only in TEM. Individual recrystallized grains may remain through substantial straining, rotating in response to dislocation and sub‐boundary motion within them, thus preserving and even enhancing the crystallographic fabric (texture). The retention of an initial recrystallized grain population throughout significant continuing deformation may explain the absence of strain softening in some recent experimental studies.
Three‐Dimensional Texture Analysis After Bunge and Roe: Correspondence Between the Respective Mathematical Techniques
Authors: Esling C. , Bechler-Ferry E. , Bunge H. J. 
Published: April 2008

Bunge′s and Roe′s three‐dimensional texture analysis methods, although both founded on
harmonic analysis, show some differences between the various mathematical techniques used.This paper establishes the correspondence relation between the respective mathematical techniques
allowing one to compare works done in either variant. Taking the latest developments in
three dimensional texture analysis into account, the correspondence relations hold for the odd
degrees l as well as for the even ones.Finally numerical tables give the extension of the symmetry coefficients (after Bunge)
and (after Roe) to all the degrees l of the series expansion, even and odd, including l = 34.
The Use of a Quadratic Form for the Determination of Non‐negative Texture Functions
Authors: Van Houtte P. 
Published: April 2008

The classical analysis of measured pole figures of textured polycrystals by the series
expansion method does not necessarily produce a non‐negative texture function. The
main reason for this is, that the method is unable to find the terms of odd rank l of the
series expansion.A new method is proposed, which introduces the non‐negativity condition into the
series expansion method by the use of quadratic forms. The method is found to be
successful when treating sharp textures, which have a considerable zero range in Euler
space. The preliminary determination of this zero range by experimental methods is
however not necessary.