bluuebunny/crossref_metadata_2025 huggingface dataset:
Elastic Properties of Cold‐Rolled and Annealed Sheets of Phosphorus Steel Having High Normal Plastic anisotropy
Authors: Hu Hsun
Published: April 2008

The elastic properties of as‐cold‐rolled and of the
subsequently annealed sheets of a phosphorus steel having high
normal plastic anisotropy and low planar plastic anisotropy have
been calculated according to the averaging procedures of Voigt,
Reuss, and Hill incorporated with texture‐weighting functions.
The calculated values of Young′s modulus in the various directtions
lying in the plane of the sheet were compared with those
determined experimentally by ultrasonic measurements. Results
indicate that the Hill averages are very close to reality, whereas
the Voigt and Reuss averages are somewhat too high and too low,
respectively, in comparison with experimentally measured values.
This paper has been prepared to help familiarize metallurgists,
engineers, and students with the mathematical treatments that
can be used for such studies. The procedures used for the calculations
are described in detail, and examples of calculations
are provided in the Appendix.
Texture and Magnetic Properties
Authors: Morris P. R. , Flowers J. W.
Published: April 2008

Expressions are derived for the dependence of the magnetic
properties of cubic materials on texture. The theoretical
development generally parallels that of Bunge, but employs Roe′s
formalism. The expressions, together with limited experimental
data, enable one to express magnetic property variations in the
plane of the sheet, to obtain property values for comparable
texture‐free specimens, and to separate magnetic properties into
texture‐dependent and texture‐independent components. Core loss,
magnetic permeability and torque or specimens of "nonoriented"
nominal 3% silicon‐iron are fitted to simple fourth‐order equations.
A New Library Program for Generating Augmented Jacobi Polynomials for Texture Calculations
Authors: Ohsugi J. I. , Fujii T.
Published: April 2008

A new library program for generating augmented Jacobi
polynomials for texture analysis is presented. By using this
program, the spatial orientation distribution maps for the
three‐dimensional texture analysis can be produced.
A Method for Obtaining the Complete Pole Figure With a Single Sample Using the Schulz Technique
Authors: Ortiz M. , Hermida J. D.
Published: April 2008

A theoretical expression, which alIows the diffracted
intensities to be corrected for defocusing, is derived from the
convolution over the geometrical defocusing width of a diffraction
peak fitted by a Cauchy function. Alignment errors are taken into
account, and a good agreement between theoretical curves and experimental
points is established.
Geometry of Texture Measurements for Dispersive Methods
Authors: Szpunar Jerzy
Published: April 2008

The application of energy‐dispersive neutron and X‐ray
methods in texture studies is briefly reviewed and discussed. New
geometries of texture measurement using energy‐dispersive methods
with stationary counters and specimen are suggested. Depending
on the number of counters the experimental data can be sufficient
for the orientation distribution function (ODF) or the ideal
orientations determination. Coarse‐grained materials can be
studied not only by neutron diffraction but also by using the
energy‐dispersive X‐ray method. Studies of texture changes under
the influence of temperature, time and external stresses can also
be conducted conveniently. The energy‐dispersive X‐ray method
may readily be adapted to industrial texture control.
Defocusing in the Reflexion Technique for the Determination of Preferred Orientation Using EDXRD
Authors: Kivilä J. , Laine E.
Published: April 2008

The defocusing effect in the reflexion technique for the determination of the preferred orientation using energy‐dispersive x‐ray diffraction (EDXRD) method is studied experimentally. The measurements show that the defocusing effect is dependent on the Bragg angle, the receiving slit width, the reflexion hkl and the metallurgical condition of the specimen. The defocusing correction or at least the optimizing of the measuring geometry is found to be necessary in quantitative texture measurements.
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.
Techniques for the Determination of Complete Polefigures Using Composite Specimens
Authors: Welch P. I.
Published: April 2008

A simple, accurate and flexible method is described
for the preparation of composite samples from metal sheets. The
basic technique can be adapted to conserve material or for the
measurement of thick plate specimens. Any combination of the four
possible quadrants of the polefigure can be determined singly or
combined. In its routine application the technique is ideally
suited to the measurement of three complete polefigures for the
determination of orientation distribution functions. In particular,
the through thickness integration, sheet area sampling and applicability
to large grained materials make it suitable for the measurement
of texture for comparison with bulk physical properties.
Complete instructions are given for the application of the technique
in practice.
Ductile Shear Bands in a Naturally Deformed Quartzite
Authors: Gapais D. , White S. H.
Published: April 2008

Microscale shear bands are features that often occur oblique to the mylonitic foliation in
mylonites. This paper is concerned with such structures within a quartz‐mylonite. Geometrical
features, microstructures and fabrics associated with shear bands are described. Both optical
and transmission electron microscopy have been used. It was observed that the development
of shear bands is closely related to (i) the onset of dynamic recrystallisation during deformation,
(ii) a change of bulk deformation within the mylonites from relatively homogeneous to inhomogeneous
and (iii) a marked softening of the mylonite. Across shear bands, dominant deformation
mechanisms change from a dislocation creep type to grain boundary sliding. This induces strong
modification of quartz lattice preferred orientations. The asymmetry of quartz fabrics due to
shear should generally be favoured by the development of shear band structures. Our results
indicate that the production of ductile shear band structures helps to accommodate large strain
deformations at low temperatures. Results also indicate that grain and sub‐grain sizes are not
affected by variations in strain rate.
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.
Effects of Terms With Odd l on the Surface Texture of Primary‐Recrystallized Silicon‐Iron Sheet
Authors: Morris Peter R.
Published: April 2008

A procedure is described for determining the linearly independent coefficients of the generalized spherical harmonic expansion (GSHE) of the crystallite orientation distribution (COD) for idealized textures with Gaussian spread functions. An attempt was made to synthesize an experimentally determined COD from such functions. Coefficients with l even and l odd were then determined from the aggregate of such functions, and the resultant GSHE of the COD was calculated. The approach used is similar to that employed by Pospiech and his co‐workers.
Volume Fractions of Texture Components of Cubic Materials
Authors: Flowers J. W.
Published: April 2008

A method for obtaining volume fractions in regions about ideal texture components of cubic materials by integration of the orientation distribution function is described. Illustrative examples of the application of the method are given for the primary‐recrystallized textures of a 3.15% Si‐Fe alloy and several low‐carbon steels.
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.
Fault Rocks of the Moine Thrust Zone: Microstructures and Textures of Selected Mylonites
Authors: White S. H. , Evans D. J. , Zhong D.-L.
Published: April 2008

In this paper, the microstructures typifying the common mylonites found in the Moine
Thrust Zone at Eriboll are presented along with c‐axis quartz textures.
Typical cataclasite microstructures are also depicted. The study revealed that the deformation and
softening mechanisms in fault rocks can change with increasing shear strain. It also revealed that strain
can be extremely inhomogeneous on the microscale at high shear strains. There is evidence for episodic
pulses of brittle behaviour which has been associated with possible seismic behaviour within the zone. The contribution concludes by outlining the microstructural and textural features that can be used to determine the direction of shearing in a mylonite zone.
Determination of the Orientation Distribution Function From One Pole‐figure
Authors: Imhof János
Published: April 2008

The values of the orientation distribution function and the data of the pole‐figure are correlated
by products of particular conditional probabilities. One of the possible approximations of these
products are obtained and demonstrated with the help of an example showing how the orientation
distribution function can thus be obtained.
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.
Introducing a Conditional Ghost Correction Into the Vector Method
Authors: Schaeben H.
Published: April 2008

The concept of conditional ghost correction is introduced into the vector method of
quantitative texture analysis. The mathematical model actually chosen here reduces the
texture problem to one of quadratic programming. Thus, a well defined optimization
problem has to be solved, the singular system of linear equations governing the correspondence
between pole and orientation distribution being reduced to a set of equality
constraints of the restated texture problem. This new mathematical approach in terms
of the vector method reveals the modeling character of the solution of the texture problem
provided by the vector method completely.
A New Method for the Determination of Texture Functions From Incomplete Pole Figures—Comparison With Older Methods
Authors: Van Houtte P.
Published: April 2008

Three series expansion methods for texture analysis from incomplete pole figures have
been compared. Method I is the presently most used method, method II is a variant
of it and method III is entirely new. Computer programs have been written for the three
methods.

Incomplete pole figures have then been prepared from known textures of f.c.c. metals.
In some cases, artificial experimental errors have been simulated. These pole figures were
analyzed by the three computer programs, after which the resulting texture functions
were compared to the original texture functions.

No significant differences were found for weak textures. On the other hand, the results
of method I are much poorer than those of the two other methods for sharp textures,
because it underestimates the normalisation factors.

The best results were obtained by method III.
Texture and Cleavage in Molybdenum
Authors: Welch P. I. , Davies G. J.
Published: April 2008

It is of considerable technological importance to establish how far textures introduced
into controlled‐rolled steels by finish rolling at low temperatures may affect the fracture
strength. The purely textural effect is difficult to isolate in such steels because of anisotropy
associated with grain shape, inclusions and pearlite banding. Consequently, an investigation
was carried out using molybdenum, a b.c.c. single phase material showing good
structural homogeneity, as a model. Texture development was studied using crystallite
orientation distribution function analysis to identify a suitable processing route leading
to a sharp texture with a suitable distribution of {100} cleavage planes. The behaviour
of a sharply textured specimen was analysed by taking fracture specimens from various
orientations in the plate. The energy absorbed in impact showed a positive correlation
with the density of 100 planes in the crack direction, but the extent of the variation was
less than would have been expected had crack propagation been the controlling step in
the fracture process.
Cubic Invariant Spherical Surface Harmonics in Conjunction With Diffraction Strain Pole‐Figures
Authors: Brakman C. M.
Published: April 2008

Four kinds of cubic invariant spherical surface harmonics are introduced. It has been
shown previously that these harmonics occur in the equations relating measured diffraction
(line‐shift) elastic strain and macro‐stresses generating these strains for the case of
textured cubic materials. As a consequence, these harmonics are important for the
determination of unknown macro‐stress tensor components if the o.d.f. expansion
coefficients are known. On the other hand, they play a role in the determination of
unknown o.d.f. expansion coefficients if the macro‐stresses are known using for instance,
a tensile test device on the diffractometer. Then, even the odd‐order o.d.f. expansion
coefficients can be obtained. In this paper, special attention is given to the mathematical
construction of the cubic harmonics, the physical symmetry requirements they are subject
to and some examples are given exhibiting both even and odd order harmonics.
Evaluation of the Effect of Initial Texture on the Development of Deformation Texture
Authors: Leffers T. , Jensen D. Juul
Published: April 2008

We describe a computer procedure which allows us to introduce experimental initial
textures as starting conditions for texture simulation (instead of a theoretical random
texture). We apply the procedure on two batches of copper with weak initial textures
and on fine‐grained and coarse‐grained aluminium with moderately strong initial
textures. In copper the initial texture turns out to be too weak to have any significant
effect. In aluminium the initial texture has a very significant effect on the simulated
textures—similar to the effect it has on the experimental textures. However, there
are differences between the simulated and the experimental aluminium textures that
can only be explained as a grain‐size effect. Possible future applications of the
procedure are discussed.
Determination of the Complete Orientation Distribution Function by the Zero‐Range Method
Authors: Lee H. P. , Bunge H. J. , Esling C.
Published: April 2008

Because of the superposition of pole figures corresponding to symmetrically
equivalent crystal directions, only the reduced orientation distribution function
can be obtained directly by pole figure inversion. The additional information
contained in the positivity condition of the ODF allows, however, the determination
of an approximation to the “indeterminable” part and hence of the complete ODF
f(g), if the texture has sufficiently large zero‐ranges. The application of the method
and the accuracy of the results was tested using two theoretical and one experimental
textures. The accuracy of the complete ODF depends on the size of the zero‐range,
the errors in its determination, and on the errors, experimental and truncational, of
the reduced ODF. The “physical zero” used in order to determine the zero‐range is
defined according to the statistical error of the pole figure measurement.
Normalizing Incomplete Experimental Pole Figures by Means of the Vector Method
Authors: Schaeben H. , Vadon A.
Published: April 2008

The vector method of quantitative texture analysis provides a new solution of the problem
of normalizing incomplete experimental pole figures. It basically makes use of the fact
that the matrix σ*(hkl) to which the corresponding matrix σ(hkl) reduces in case of:
(1) axial symmetry in terms of pole figures; or (2) fiber textures in terms of orientations,
is full range. In this case σ*(hkl) actually establishes the correspondence between the axial
symmetrical direct pole figure and the corresponding inverse pole figure with respect to
the normal ON of the sample.
On the Representation of Texture Functions of Cubic Metals in Euler Space
Authors: Houtte P. Van
Published: April 2008

Cubic‐orthorhombic texture functions (e.g., of rolling textures) are conventionally
represented by Euler diagrams with a range of 0° to 90° for φ1, Φ and φ2. Some drawbacks of this method are discussed. By means of inverse pole figure representations,
it is explained how this range can be subdivided into three completely equivalent “unit zones”. In order to overcome the drawbacks mentioned above, without adding yet a new type of O.D.F. representation to the list of those that already exist, it is proposed to continue using the same type of representation but to consider only unit zone 3, which is much less distorted than the two other unit zones. It is recommended to show the limits between the unit zones in the Euler diagrams.
Evaluation of the Integral
Authors: Brakman C. M.
Published: April 2008

Integrals of the type indicated can be evaluated using the Fourier‐series development of the Jacobi‐polynomials. An alternative procedure is given yielding an analytical expression in terms of l, m and n.
Orientation Correlation in Grain and Phase Boundaries
Authors: Bunge H. J. , Weiland H.
Published: April 2008

The properties of grain and phase boundaries depend on five angular coordinates, i.e. three parameters specifying the orientation difference across the boundary and two parameters specifying the orientation of the boundary normal direction in space or with respect to the crystal lattice. Hence, five‐dimensional boundary distribution functions have to be considered. If one considers only misorientation a three‐dimensional
misorientation distribution function is obtained. The deviation of this function from the #8220;uncorrelated” misorientation distribution yields the orientation correlation function. The most economical representation of these functions is the one using series expansions in terms of symmetrized harmonic functions. With the present state of experimental technique it seems to be impossible to determine the complete boundary distribution functions. However, two‐dimensional analoga of these functions can be obtained from electron diffraction measurements.
Role of Twinning in Texture Development and in Plastic Deformation of Hexagonal Materials
Authors: Philippe M. J. , Esling C. , Hocheid B.
Published: April 2008

This paper presents an extensive study of the conditions of appearance of mechanical twinning and its role in the texture development during uniaxial tension, biaxial expansion and rolling of Ti and Zr alloys.

With the help of literature, the analyses are extended to alloys of Mg, Zn and Be.

Finally, the influence of twinning on the shape of the forming limit diagrams and on formability is discussed for hexagonal metals.
Calculation of the Yield Locus of Textured Polycrystals Using the Taylor and the Relaxed Taylor Theory
Authors: Houtte P. Van
Published: April 2008

Several authors have proposed methods which use the Taylor–Bishop–Hill theory in order to calculate the yield surface of textured samples of which the O.D.F. is known.

The purpose of this paper is to show how these methods can be generalized while keeping the computational effort within reasonable limits. It must be emphasized that the new method produces “true” plane sections of the yield locus instead of so‐called “principle strain yield loci.”

A theorem that permits the exploitation of the sample symmetry is demonstrated. After a general description of the method, it is explained how the theorem can be used in order to restrict the number of deformation modes that must be considered.

The next section discusses how a data bank of Taylor factors can be constructed. The full‐constraint Taylor theory as well as the relaxed Taylor theory are considered.

In the next section, it is explained how the plane sections through the multidimensional yield locus are generated. A few applications are finally discussed, including a study of the elongation of a torsion sample of which the O.D.F. has been measured.
Piezoelectric Pole Figure of a Vein Quartz Sample
Authors: Ghomshei M. M. , Narod B. B. , Templeton T. L. , Arrott A. S. , Russell R. D.
Published: April 2008

Longitudinal piezoelectric coefficients have been measured on cubic samples and from 150 different orientations on a spherical sample of coarse‐grained vein quartz. The results are consistent with the presence of a piezoelectric fabric. The piezoelectric pole figure of the studied spherical sample demonstrates three distinct
patterns of alternatively positive and negative signs defining one strong and two weak electric dipoles in the fabric. The magnitude of the piezoelectric effect along the major maximum is as large as 7% of the theoretical effect in a single crystal and is considerably higher than the expected statistical effect. Preferred orientation of the
a‐axes, was independently confirmed by subjecting the same spherical sample to neutron diffraction analysis. The location of nonpolar a‐axes maximum determined by neutron diffraction analysis agrees with the piezoelectric maximum which is theoretically related to the polar preferred orientation of a‐axes. The piezoelectric effect and neutron diffraction are both volume events and ensure reliable statistics for analysis of coarse‐grained quartz aggregates where surface events (such as X‐ray diffraction) may suffer poor statistics.
Development of the Rolling Texture in Titanium
Authors: Lee H. P. , Esling C. , Bunge H. J.
Published: April 2008

The complete ODF of titanium, cold rolled up to 80% deformation, was calculated using the series expansion method, including the zero range method. The rolling texture obtained after 80% deformation is mainly characterized by the well‐known orientation {0001} ± 40°TD but with distinct spread ranges about it. At about 40% deformation several other texture components are found of which the component {0001} must be mentioned. Further features of the obtained textures are a minor component as well as characteristic zero ranges. Texture development as function of the rolling degree can be divided into three ranges
judged by increase or decrease of various texture components. In the early stages twinning in two different types of twinning systems is assumed whereas at higher deformation degrees the formation of the rolling texture is ascribed to glide deformation only.
Orientations of the Cubic Unit Cell and Tetrahedron
Authors: Casato J. C. , Fricke W. G.
Published: April 2008

Charts are presented showing the cubic unit cell and tetrahedron for various simple orientations relative to the rolling plane and direction.
Description and PresentationMethods for Textures
Authors: Hirsch Jürgen , Lücke Kurt
Published: April 2008

Different methods to describe and analyze the peak and/or fibre characteristics of
textures are discussed. In metallic materials the main features of a certain type of
texture can clearly and comprehensively be described by using adequate extractions
from the three‐dimensional orientation distribution function (ODF), which is usually
calculated from two‐dimensional X‐ray pole figures. The ODF has a higher resolving
power, but the abstract form of orientation density data plotted in a three‐dimensional
orientation space is not always the most suitable way for presentation
and further interpretation. Methods to describe the textures with the help of ideal
orientations and/or fibres, their quantitative analysis with the help of Gauss‐type
scattering components, the selective projection and plot of characteristic orientation
fibres are discussed and compared. As an example the development of rolling
textures of fcc metals is described and analyzed. Using these evaluation methods it
can be demonstrated how their characteristic features are related to theoretical
predictions and to microstructural effects.
Effect of Ti on the Developmentof Rolling Textures in HighPurity Iron
Authors: Inagaki Hirosuke
Published: April 2008

With the method of the crystallite orientation distribution function analysis, the
development of the rolling texture was studied in detail on a Fe‐0.004%C‐0.20%Ti
alloy cold rolled up to 90% reduction in thickness. It was found that the effect of Ti
was widely different among various rolling texture components. The addition of Ti
enhanced the development of the 〈110〉‖RD fiber rolling texture component by
promoting the rotation about the 〈110〉‖RD axis. This resulted in the development
of the strong {112}〈110〉 texture component. As to the 〈110〉‖TD fiber texture
component, it was found that, although the addition of Ti did not affect the rotation
about the 〈110〉‖TD axis in the range {110}〈001〉 to {554}〈225〉, it strongly
suppressed the rotation of {554}〈225〉 into {111}〈112〉. As a result, strong
{554}〈225〉 rolling texture component was developed below 70% rolling reduction.
This component seems to provide origins of the {554}〈225〉 recrystallization texture
commonly observed in the Ti‐stabilized steel. Such changes in the rolling texture
would be expected, since slip modes are strongly affected by scavenging of C atom by
Ti, or by the presence of very fine TiC precipitate particles.
Texture Changes in Pass‐Rolling of Steel Rods
Authors: Schubert A. , Klimanek P. , Hensger K.-E.
Published: April 2008

Neutron‐diffraction was used to study the texture development during pass‐rolling of
rods of an austenitic (f.c.c.) steel X8CrNiTi18.10 and a ferritic (b.c.c.) material
X8CrTi17 in a round→oval→round→oval→round groove sequence. The orientation
distributions occurring in the core of the pass‐rolled rods can be described in a
good approximation in terms of orthorhombic sample symmetry and qualitatively
interpreted either as press textures on conditions of anisotropic material flow in the
plane perpendicular to the press direction or as rolling textures on condition of large
spreading. However, though they must be characterized by components {hkl}〈uvw〉 the pass‐rolling textures are not rolling textures in the usual sense.
Texture Changes in an Al–LiAlloy Sheet SuperplasticallyDeformed to High Strains
Authors: Bowen A. W.
Published: April 2008

Changes in the texture and grain shape of an Al–Li alloy sheet superplastically
deformed into the shape of a cone have been measured as a function of strain. The
starting microstructure was characterised by strong {110}〈112〉 and {123}〈634〉
orientations, together with a number of minor orientations, and an elongated grain
shape. Increases and decreases in the intensities of the individual orientations
occurred at low values of strain (<0.5) as the elongated grains became equiaxed.
Once all the grains were equiaxed, however, there was a continuous decrease in the
intensities of all orientations, except for those of some minor orientations which
remained essentially constant. The results are explained in terms of slip occurring in
the early stages of deformation, because elongated grains will experience difficulty in
sliding and rotating, but becoming negligible when grains are equiaxed and are free
to slide and rotate. There was some evidence of dynamic recrystallisation but only
whilst slip occurred.
An X‐ray Study on Texture Caused by Rolling Contact
Authors: Nagashima Shin-Ichi , Ohtsubo Toshinori
Published: April 2008

Rolling contact loading causes a remarkable plastic flow at the contact surface of rail
and wheel or the surface of a pair of disks rotating under normal force. It is supposed
that significant residual stress, work hardening and preferred orientation will be
introduced as well as the plastic flow, and the combination of all of those factors may
cause the fatigue damage to the specimen. In the present study, the mode of plastic
flow and the preferred orientation with respect to the tangential force, or slip at the
contact region were measured. The experimental results were nearly the same for
both laboratory tested disk specimen and a used rail. The distribution of degree of
plastic flow showed good agreement with the work hardening of the flowed region,
besides the mode of plastic flow is nearly the same as the calculated result. The
major texture component at the flowed region was near (111) [] and near
(111) [] which are the major components of cold rolling texture being formed by
the combination of compressive stress and weak shear stress.
The Influence of Non‐Octahedral Slip on Texture Development in FCC Metals
Authors: Bacroix B. , Jonas J. J.
Published: April 2008

In order to account for the differences observed between low and high temperature
deformation textures, the influence of slip or cross‐slip on planes other than the
{111} is considered in FCC metals. The first set of possible new slip systems treated
is the {100}〈110〉. The dual single crystal yield surface is constructed using a novel
technique, and deformation textures are predicted for rolling and torsion using the
FC‐RC model usually employed at room temperature. The {112} and {110}〈110〉
cross‐slip systems are also considered. The rolling textures obtained when slip and
cross‐slip or only cross‐slip occur are presented. These two cases are first treated on
the assumption of a constant CRSS on all systems and then with the aid of a linear
latent hardening law, which only takes into account the interactions between colinear
systems.

It is shown that the concurrent activation of both slip and cross‐slip systems leads
to the presence of three main rolling components: i.e. the Cu, S and brass
orientations, in proportions that vary with the CRSS ratios of the different systems.
These results are in good agreement with experimental observations for high SFE
metals such as aluminum. Some torsion textures are also presented for the case when
both slip and cross‐slip systems are activated. The trends observed in this case are
not as clear as in the case of rolling. However, the orientation, which is the only
component found at high temperatures and high strains in aluminum, is present in
higher proportions than with the classical FC‐RC model, but some other texture
components are also present.
Recrystallization Experiments in Tensile Deformed 〈100〉‐ and 〈111〉‐Oriented Copper Single Crystals
Authors: Klement U. , Ernst F. , Wilbrandt P.-J.
Published: April 2008

〈100〉‐ and 〈111〉‐oriented copper single crystals were tensile deformed to a final
strain of 20% and 4%, respectively. Specimens prepared from these crystals were
abraded at one end. During the subsequent annealing treatment (750 K, 2 h for the
〈100〉‐oriented crystals and 750 K, 90 min for the 〈111〉‐oriented crystals) the
recrystallization process started on this side. In both cases the orientation relationships
between the largest recrystallized grains and the uniformly oriented deformed
microstructure can be characterized by the following relations: 22.6° 〈100〉, 21.8°
〈111〉, 46.8° 〈111〉 and 129.8° 〈540〉. Additionally, in the 〈111〉 crystals other
orientation relationships were found. This is caused by the different dislocation
densities in the specimens. The 〈111〉‐oriented crystals represent the early stage of
recrystallization whereas the 〈100〉‐oriented crystals show the orientations of the late
recrystallization stage. Between these stages a further selection of orientations occur.
Texture and Microstructure of Meltspun Shape Memory Alloys
Authors: Eucken S. , Hirsch J. , Hornbogen E.
Published: April 2008

Shape memory effects are based on the shear stress sensitivity of the orientation of
lattice variant and invariant shear which is associated with reversible martensitic
phase transformation. The effect of texture and microstructure of the high
temperature phase was investigated with copper based shape memory alloys. Rapid
solidification can produce either a columnar grain structure with a pronounced 〈100〉
fibre texture, or an equiaxal structure with a grain orientation close to random. It
could be shown that the columnar and textured grain structure produces the
maximum shape memory effect in β‐Cu alloys if the ribbon shaped specimen is
exposed to tensile stress parallel to the length of the ribbons. These effects are
explained by the influence of primary texture of the high temperature phase on the
texture which originates in the martensitic low temperature phase if the transformation
occurs under an external load.
Neutron Diffraction Texture Analysis in Extruded Al‐Pb Composites
Authors: Brokmeier H. G. , Böcker W. , Bunge H. J.
Published: April 2008

The textures of the two phases of Al–Pb composite samples of various compositions
extruded 96% at room temperature were determined by neutron diffraction. In both
phases the degree of texture decreases with an increase in amount of the other
phase. In the case of the harder Al‐phase, this is due to the decreasing internal
deformation degree of the hard Al‐particles in the soft Pb‐matrix. In the case of the
softer Pb‐phase, the decrease must be related to increasing turbulence of flow in the
soft phase. Furthermore, this phase was recrystallized after extrusion.
Applications of Neutron Diffraction Pole Figure Measurements on Polycrystalline and Monocrystalline Metallic Samples. Examples From the Four‐Circle Neutron Diffractometer InJülich
Authors: Schäfer W. , Höfler S. , Will G.
Published: April 2008

Four different examples of neutron diffraction pole figure measurements are
presented showing the variety of applications in metallic texture and microstructure
analysis. Two examples are concerned with the study of texture effects on cold rolled
titanium and warm bended α‐iron sheets. Two further examples are connected with
the study of twinning laws and special orientation relationships in hexahedritic and
octahedritic iron meteorites. Nishiyama–Wassermann orientations between α‐ and γ‐iron phases are experimentally confirmed.
The Early Stages of the Development of Rolling Texture in Copper and Brass
Authors: Leffers T. , Jensen D. Juul
Published: April 2008

The texture development in copper and brass (15% zinc) is followed by neutron‐diffraction
measurements from the early stage. The texture development is found to
be different in the two materials from the very beginning (largely towards the
respective final textures of copper and brass). As demonstrated by texture simulation
starting with the experimental orientation distributions of the undeformed materials,
the early difference in texture development is not a result of the differences in initial
texture. The conclusion of the texture measurements—and of earlier microstructural
observations confirmed in the present work—is that the development of the
brass‐type texture cannot be explained by any of the proposed twinning theories.
The only existing model capable of reproducing the development of the brass texture
at moderate strains without disagreement with experimental observations appears to
be the Sachs model, or rather a modified Sachs model.
Fifty Years Textures in Research and Practice
Authors: Bunge H. J.
Published: April 2008

The orientation distribution or texture of the crystallites is one of the most important
structural parameters of polycrystalline materials. Texture studies were carried out
for more than fifty years. This branch of materials science, first established by G.
Wassermann in 1939 by his monograph “Texturen metallischer Werkstoffe,” has now
developed into a quantitative science based mainly on measurements by X‐ray,
neutron and electron diffraction. A mathematical theory of textures has evolved
mainly in the last twenty years. The extension of interest from basic metals to all
kinds of crystalline materials is one of the present features. Concludingly, the future
development in the field of textures may be extrapolated.
SAECP Combined WithQuantitative Image Analysis—an Improved Tool for TextureAnalysis
Authors: Lorenz W. , Hougardy H.
Published: April 2008

A selected area electron channelling pattern (SAECP), which allows the determination
of the orientation of individual grains in polished steel specimens, can be
obtained with a scanning electron microscope. The different methods to determine
the orientation of the grains from the measured pattern are summarized. A minimum
grain diameter of about 7μm is required for orientation determination and the
maximum error for the determination of (hkl) is about 2°, and about 4° for [uvw].
The total time needed for the determination of the orientation of 400 grains is in the
range of 60 hours. Different representations of results are discussed. An example
shows that the measurement of single orientations can give more information on the
mechanisms of recrystallization than an investigation by x‐rays only.
Texture and Lattice Deformation Pole Figures of Machined Surfaces
Authors: Maurer G. , Neff H. , Scholtes B. , Macherauch E.
Published: April 2008

A short review of the current knowledge about machining induced texture states is
given. The applied methods for the determination of texture and residual stress
states are outlined. The surface textures and residual stress states present after
grinding, milling and shot peening of initially residual stress‐ and texture‐free as well
as of 78% cold‐rolled plain carbon steel are presented. Texture and residual stress
states are represented by texture and lattice deformation pole figures. In the initially
texture‐free specimens, machining by grinding and milling gives rise to weak, but
typical asymmetric textures. The appertaining principal residual stress systems do
not coincide with the specimen system. Shot peening causes a centrosymmetric
texture and residal stress state. The cold‐rolling texture and residual stress state is
significantly changed due to machining. Milling and grinding introduce an asymmetry
into the symmetric rolling texture and residual stress state. After shot peening of
cold‐rolled specimens, a centrosymmetric residual stress state is found.
Natural and Simulated (10.4) Pole Figures of Polycrystalline Hematite
Authors: Quade H.
Published: April 2008

Qualitative (10.4) pole figures of hematite have been generated by simulating the
rotative arrangement of c axes on planes of preferred simple shear. The procedure of
simulation is described which consists in geometric operations varying the degree of
texture anisotropy and homogeneity. Comparisons are made between predicted
orientation diagrams and natural textures of high‐grade hematite ores from Precam‐brian
deposits of North and South America, Africa, and Australia. The mechanisms
of preferred orientation of hematite in ores are explained in terms of changing
metamorphic conditions and variations in amount of simple rotational shear.
Nest of Origin Predicts Adult Neuron Addition Rates in the Vocal Control System of the Zebra Finch
Authors: Hurley Patrick , Pytte Carolyn , Kirn John R.
Published: April 2008

Neurogenesis and neuronal replacement in adulthood represent dramatic forms of plasticity that might serve as a substrate for behavioral flexibility. In songbirds, neurons are continually replaced in HVC (used as a proper name), a pre-motor region necessary for the production of learned vocalizations. There are large individual differences in HVC neuron addition. Some of this variation is probably due to individual differences in adult experience; however, it is also possible that heritability or experience early in development constrains the levels of adult neuron addition. As a step toward addressing the latter two possibilities, we explored the extent to which nest of origin predicts rates of HVC neuron addition in adult male zebra finches. One month after injections of [3H]-thymidine to mark dividing cells, neuron addition in HVC was found to co-vary among birds that had been nest mates, even when they were housed in different cages as adults. We also tested whether nest mate co-variation might be due to shared adult auditory experience by measuring neuron addition in nest mate pairs after one member was deafened. There were significant differences in neuron addition between hearing and deaf birds but nest mate relationships persisted. These results suggest that variation in genotype and/or early pre- or postnatal experience can account for a large fraction of adult variation in rates of neuron addition. These results also suggest that a major constraint on neurogenesis and the capacity to adjust rates of neuron addition in response to adult auditory experience is established early in development.