bluuebunny/crossref_metadata_2025 huggingface dataset:
On‐line Texture Measurements for the Prediction of the Anisotropy of Magnetic Properties
Authors: Blandford P. , Szpunar J. A.
Published: April 2008

An outline of a system to be used for on‐line determination of texture is presented in this paper;
information is given as to the detection geometry and equipment as well as the method whereby the
orientation distribution function (ODF) will be calculated. Based on coefficients claculated in a
simulation of the on‐line system, a number of correlations, including relative permeability, hysteresis
losses, magnetic torque and others, are carried out.
On‐line Texture Analysis for Magnetic Property Control
Authors: Bunge H. J. , Kopineck H. J. , Wagner F.
Published: April 2008

Magnetic properties of hard and soft magnetic materials are strongly anisotropic, i.e. they depend on
the crystal direction in which they are being considered. Technological materials are usually
polycrystalline. Hence, their properties are orientation mean values of the properties of the
crystallites with the texture of the material as the weight function. Inspection and control of magnetic
properties of materials thus requires inspection and control of the materials texture which can be
carried out off‐line by taking samples from the finished material and investigating them in the
laboratory. If, however, the texture of the material is to be controlled during the production process
then a fast non‐destructive on‐line texture analyser is required the output signal of which can be used
to control the production process.
Estimation of 4th and 6th Order ODF Coefficients From Elastic Properties in Cold Rolled Steel Sheets
Authors: Sakata Kei , Daniel Dominique , Jonas John J.
Published: April 2008

Generally only the 4th order ODF coefficients are deduced from the observed elastic anisotropy of
textured polycrystalline materials with cubic/orthorhombic symmetry. In this study, a method is
described for the prediction of the 4th and 6th order ODF coefficients from the elastic properties of
cold rolled and annealed steel sheets of 5 different types. In order to link these properties with the
texture, the elastic energy method of Bunge (1974) is employed. By estimating the volume fractions of
the principal preferred orientations and their gaussian spreads, ODF coefficients of the 4th (, and ) and 6th (, and ) orders can be successfully obtained. As a result, the planar r‐value distribution can be predicted more accurately than when only the 4th order coefficients are
employed.
Anisotropy of Magnetic Properties in Textured Materials
Authors: Szpunar J. A.
Published: April 2008

A short survey is presented of techniques and methods used to correlate the texture with the magnetic
anisotropy of various properties of soft and hard magnetic materials. Also, examples of magnetic
materials are discussed with emphasis on techniques of processing which optimize the texture.
Development of Cross‐rolling Textures in Armco‐Iron
Authors: Böcker A. , Klein H. , Bunge H. J.
Published: April 2008

ARMCO‐iron was cross‐rolled in two different modes, i.e. with a rotation of the rolling direction
through 90° after each individual pass or after half of the reduction in thickness only. In the first case,
which corresponds to a truly tetragonal straight deformation path, the orientation {001}〈110〉
assumes an extremely high orientation density of 50 × random after 93% reduction. Besides this, the
texture contains a nearly ideal 〈111〉‖ND‐orientation tube, the intensity of which increases to about
10 × random. The texture of the second mode is similar to that of the first one up to about 50%
reduction. After that the density in the orientation {001}〈110〉 decreases and increases again at the
highest deformation degrees. Two minor orientation components {001}〈100〉 and {011}〈100〉 were
found with intensities in the range of 3 to 5 × random at low deformation degrees of about 10%.
Numerical Calculation of Anisotropic Absorption Factors for Lamellar Two‐Phase Structures
Authors: Liu Y. S. , Bunge H. J.
Published: April 2008

X‐ray diffraction in a lamellar two‐phase material is considered. If the lamellae thicknesses are small
compared with the penetration depth of the X‐rays then the absorption factor depends on the whole
path of incident and reflected beam in both phases. Particularly, it depends on a rotation γ about the diffraction vector s additional to the orientation (αβ) of this vector with respect to the sample.
Numerical calculations of the absorption factor A(αβγ) have been carried out for different values of lamellae thicknesses D1D2, absorption coefficients μ1μ2 and lamellae orientations ωρ with respect to the sample surface.
Reduction of Misorientations Between Two Cubic Crystals Into the Base Domain of Axis–Angle Space
Authors: Sztwiertnia K. , Pospiech J. , Haessner F.
Published: April 2008

A misorientation between two cubic crystallites can be described using different orientation
parameters and represented in many symmetrically equivalent ways. It is, however, convenient when
the misorientations between different pairs of crystallites all lie in the same base domain. This paper
presents a computer program which reduces a misorientation given in axis–angle or in Euler′s space
into the base domain of the smallest angle of rotation.
Partial Texture Analysis
Authors: Bunge H. J.
Published: April 2008

The texture is the orientation distribution function of the crystallites of a polycrystalline sample. Being
a continuous function of three variables, it requires a large number of values for its complete
description. The texture can be expressed in terms of a series expansion. It then requires a large
number of coefficients for its complete description. When all functional values or all coefficients are
determined from experimental measurements we speak of complete texture analysis. The most
important methods for complete texture analysis are individual orientation measurements of a large
number of crystals and pole figure measurement followed by pole figure inversion.

If only a limited number of values of the texture function or a few of its coefficients are being
determined we speak of “partial texture analysis”. The most important methods of partial texture
analysis are the fixed angle texture analyzer and the measurement of the anisotropy of physical
properties such as Young′s modulus magnetic properties, thermal expansion and others.
An Evaluation of the Single Orientation Method for Texture Determination in Materials of Moderate Texture Strength
Authors: Wright Stuart I. , Adams Brent L.
Published: April 2008

New microscopy technology has made it feasible to consider using single orientation measurements to
obtain Orientation Distribution Functions (ODF). Single orientations are preferred over pole figure
data in ODF calculations because the odd terms of the series expansion are not directly accessible
when pole figures are used. However, the number of single orientation measurements required to
calculate a statistically reliable ODF has generally been considered too large to practically obtain.
This study found that the location of the major features of the ODF in rolled aluminum sheet were
identifiable after only 100 measurements. However, the heights of the peaks and the secondary
features required many more measurements to stabilize. Unless the orientation measurements can be
automated or orientation correlation data is needed the pole figure method remains a more efficient
means of obtaining the data necessary to measure texture.
Toughness and Fatigue Crack Growth Rate of Textured Metals
Authors: Sevillano J. Gil
Published: April 2008

The influence of anisotropy of crystallographic origin on both fracture toughness and the rate of
stage‐II ductile fatigue crack growth in textured metals is discussed in terms of a plane‐strain small
geometry change solution for plastic non‐hardening materials (a Prandtl‐type slip‐line field solution
accounting for anisotropy). Results corresponding to FCC or BCC metals sliding, respectively, on
{111} 〈110〉 or {110} 〈111〉 systems are presented. Remarkable effects of both texture toughening and
fatigue crack growth rate anisotropy are predicted. Stronger effects are anticipated in more
anisotropic metals (HCP).
Measurement of Local Textures With Transmission and Scanning Electron Microscopes
Authors: Schwarzer R. A.
Published: April 2008

Transmission and scanning electron microscopy methods are discussed for the determination of grain
orientations. For the study of local textures with a TEM electron‐transparent thin samples are
required. The standard techniques of orientation determination grain by grain are the interpretation
of selected area electron spot and microbeam Kikuchi diffraction patterns. Specimen areas smaller
than 500 nm or 50 nm in diameter can be selected. More recently selected area pole‐figures can be
measured directly with a TEM technique similar to the conventional transmission X‐ray method.

The orientation of grains in a bulk sample can be obtained with a scanning electron microscope
from reflection Kikuchi (i.e. electron backscattering) and channeling patterns. Local resolution is
approximately 1 μm or 5 μm, respectively.

Since the interpretation of electron diffraction patterns is tedious, techniques have been developed
to perform measurements on‐line by interfacing the electron microscope to a computer. An
outstanding advantage of texture measurements by electron diffraction is the high local resolution and
the ability of imaging the microstructure of the sampled region. Experimental results of individual
grain‐orientation measurements may be represented statistically by inverse pole‐figures, orientation
distribution functions and misorientation distribution functions.
An ODF Study of the Deformation andRecrystallization Textures of Rolledand Channel‐die CompressedHigh Purity Copper
Authors: Hammelrath H. , Butler J. F. , Juul-Jensen D. , Leffers T. , Hu Hsun , Lücke K.
Published: April 2008

The rolling deformation has widely been considered equivalent to plane strain compression. The
validity of this presumption, particularly at high strains, was tested by comparing the deformation and
recrystallization textures in rolled and channel‐die compressed copper using the ODF techniques.
Noticeable differences were observed in both the deformation and recrystallization (cube) textures of
the strips produced by these two deformation methods. For the deformation texture, the rolled strip
shows stronger “copper” and “S”, but weaker “brass” components, in comparison with the
channel‐die compressed strip. For the recrystallized specimens, the cube texture is stronger in the
rolled than in the channel‐die compressed specimens, and their microstructures are also noticeably
different. These observed differences are all more prominent at higher reductions. The causes of these
differences will be discussed.
Anisotropic Finite‐Element Analysis of Plastic Metalforming Processes
Authors: van Bael A. , van Houtte P. , Aernoudt E. , Hall F. R. , Pillinger I. , Hartley P. , Sturgess C. E. N.
Published: April 2008

This paper describes some aspects of the incorporation of plastic anisotropy of textured materials into an elastic‐plastic finite‐element program in order to simulate the deformation of such materials.
Plastic Deformation of B.C.C. Polycrystals: ComparisonBetween Experimental Datas and Results of Several Modelling Codes
Authors: Royer F. , Nadari A. , Yala F. , Lipinski P. , Ceccaldi D. , Berveiller N. , Penelle P.
Published: April 2008

This contribution complete a previous one (1) in that the
specific problems of the elastoplastic behaviour of body‐centered
polycrystals are analyzed. The experimental results (yield stress,
Lankford′s ratio, textures, …) are compared with those of self‐consistent
and Taylor modelling codes. A particular attention is
put on the influence of the selection of glide systems in the
framework of crystallographic or non‐crystallographic assumptions.
Modeling of Deformation Textures Evolution in Semi‐Crystalline Polymers
Authors: Ahzi S. , Parks D. M. , Argon A. S.
Published: April 2008

A composite model for plastic deformations of semi‐crystalline polymers
is used to simulate deformation textures evolution in these two‐phase materials.
Three types of textures are simulated: crystallographic texture,
morphological texture, and molecular alignment within the amorphous domains.
Predictions of these textures in deformed high density polyethylene
(HDPE) are shown for a uniaxial tension test.
Rolling Texture of Al‐Mg Alloys
Authors: Kohara S. , Inagaki H.
Published: April 2008

The development and the transition of texture in rolled
Al‐Mg alloys have been followed by determining pole
figures for the alloys with various Mg contents and with
various degrees of rolling reduction.

Al‐Mg alloys containing 0.5, 1.0 and 2.0 % Mg were
prepared by melting in an argon atmosphere and rolled into
sheets of 1 mm thickness. The rolling reductions were
70, 82.5, 90 and 95 %. Pole figures were determined with
111, 200 and 220 difractions. The results were analyzed
using the orientation distribution function.

For low reduction of rolling, pole figures for all Al‐Mg
alloys were almost the same as that for pure aluminium,
that is, the copper type. For high reduction of rolling,
pole figures for the alloys containing up to 1% Mg were
the copper type. However, the alloy containing 2 % Mg
showed the pole figure of different type. The main
component of this texture was represented as {001}<110>.
Texture Manipulation by Ion Implantation
Authors: Helming K. , Rauschenbach B.
Published: April 2008

High fluence nitrogen ion implantation into titanium at room temperature
results in the formation of titanium nitride precipitation. Electron
diffraction measurements reveal an implantation‐induced texture of
titanium nitride precipitations. The experiments demonstrate a strong
coupling effect between the implantation‐induced fibre texture and the
direction of implantation. The results of this investigation support the
assumption that the effect of implantation‐induced texture is caused by
the process of seed selection by ion channeling.
Texture Evolution in Zr‐2.5 Nb Deformed in Uniaxial Compression
Authors: Rodriguez A. Salinas , Root J. H.
Published: April 2008

The evolution of texture in Zr‐2.5 Nb during uniaxial
compression was studied in annealed specimens with α grain
sizes of 5 and 10 μm. It is shown that texture development is
determined by the mechanism controlling ‐axis deformation.
In fine grained material  and  slip are found to be
responsible for texture evolution. Tensile twinning controls
the formation of a sharp [0001] compression texture in coarse
grained material. It is suggested that the mode of ‐axis
deformation is determined by the α grain size.
Determination of the Orientation Distribution Function FromArbitrary Diffraction Data
Authors: Szpunar J. A.
Published: April 2008

A method proposed by Bunge in which we assume a fit between the theoretical ODF and the isolated
expetal points was used to calculate the ODF from experimental data chosen in an arbitrary way in a pole
figure and an inverse pale figure space. In particular, this technique was used to obtain the ODF from the
measurements of three, two and one pole figures, from the data obtained using the reflection technique only or
transmission technique only, from inverse pole figures and from the photo showing the Debye‐Scherrer rings.
Various tests described in this paper allows us to suggest an empirical rule indicating that the number of
experimental data points should be three times higher than the number of required series expansion coefficients
of the ODF. In addition, other factors, for instance, the strength of texture and the distribution of experimental
points are also important.
Simultaneous Measurement of Pole Figures by X‐Ray DiffractionUsing a 2Ɵ‐Position Sensitive Detector
Authors: Wcislak L. , Bunge H. J.
Published: April 2008

Pole figure measurement is usually carried out with texture goniometers equipped with
a single detector. Thereby defocalization due to the sample tilt is taken into account by
using broad enough receiving slits possibly with a defocalization correction. This method
does not work in line‐rich diffraction spectra with profuse peak overlap, particularly at high
tilt angles. In this case the whole diffraction spectrum is needed for each pole figure point
{α/β}. The integrated intensities are then to be obtained by a deconvolution procedure.
Because of the necessary measuring time this is virtually impossible with a single detector.
Using a position sensitive detector complete diffraction spectra can, however, be obtained
for each pole figure point in reasonable times. In the present case, a 7º linear position
sensitive detector was used. The line broadening as a function of the tilt angle was measured,
coordinate transformation formulae for the back‐reflexion case are given and it was shown
that the so obtained results exhibit smaller experimental errors than the conventional single
dctector measurements.
Automated Lattice Orientation Determination From ElectronBackscatter Kikuchi Diffraction Patterns
Authors: Wright S. I. , Adams B. L.
Published: April 2008

The ability to measure individual orientations from crystallites enables a more
complete characterization of the microstructure. A primary obstacle to the use of
single orientation measurements is the large investment of direct operator time
necessary to obtain a statistically reliable data set. The most viable technique for
obtaining individual orientation measurements is electron backscatter Kikuchi
diffraction (BKD). Current technology requires an operator to identify a zone axis
pair in a BKD pattern. This paper describes research in progress to automate the
identification of lattice orientation from BKD patterns by identifying the planes
associated with the bands that appear in the patterns. This work considered FCC crystal
symmetry.
Textures in Non‐Metallic Materials
Authors: Bunge H. J.
Published: April 2008

The texture of a polycrystalline material is defined by the
orientation distribution function (ODF) of its crystallites. Besides
this, the misorientation distribution MODF of neighbouring
crystals may be important. Although this applies equally
to all crystalline materials, texture studies have extensively
been done in metals and not so much in ceramics and polymers.
This is partly due to experimental difficulties of texture
measurement in these materials which have only recently been
overcome. Besides this, two deviating definitions of the term
”texture” are being used. These are the ”shape texture” in
ceramics and the ”chain texture” in polymers.

Textures in ceramics were studied quantitatively mainly in
hard magnetic materials. They are, however, also most important
in HTc‐superconductors, in ferroelectrics, in transformation
toughened ceramics, in ceramic surface layers, copperbonded
Al2O3 substrates and probably in many others. Textures
in the crystalline part of polymers have been studied
quantitatively using ODF‐methods. ”Momenta” of the orientation
distribution function of the crystalline as well as the
non‐crystalline part can, however, be obtained more easily by
physical methods. This is sufficient if the correlation between
preferred orientation and anisotropic properties is considered.
Texture formation by deformation is, however, related to the
complete orientation distribution function.
Textures and Barrier Properties of Ethylene‐Vinylalcohol CopolymerFilms
Authors: Ishida Takashi , Soutome Takayuki , Sekine Kazuyoshi
Published: April 2008

The effect of textures produced by various types
of deformation processing on gas barrier property of
copolymer film has been studied in the case of
ethylene‐vinylalcohol (EVOH) resin which is known as
a semicrystalline polymer with low gas permeability.

The heavily cold rolling and cold stretching give
rise to highly oriented molecular structures and
strong crystallographic textures, which reduce gas
permeability of the film at high humidity. It was
found, in particular, that the increased tri‐axial
orientation type texture and resulting molecular
structure changes due to the plane strain compression
type deformation, such as rolling, improved greatly
the barrier property of the EVOH film.
The Effect of Nucleation Sites for Recrystallisation on AnnealingTexture and Earing in Aluminium
Authors: Oscarsson A.
Published: April 2008

It is important to control the recrystallised texture in the aluminium
alloy used for beverage cans. A model has previously been proposed
which explains the recrystallised texture of the hot bands as a competition
between grains nucleated either in transition bands or around coarse
particles. Present work confirms that most recrystallised grains are nucleated
around coarse particles and that these do not have any preferred
orientation. Possibly the smaller of the coarse particles have a weak tendency
to nucleate grains in a retained rolling orientation. Other recrystallised
grains not associated with particles are preferably oriented on
the (100)‐fibre parallel to the rolling direction including the important
cube and Goss orientations.

A light cold rolling of the hot bands prior to annealing can increase
the final cube texture, but only if the hot band is slightly recrystallised.
This is explained by a destruction of most small recrystallised
grains while a few selected grains are conserved. Recrystallised grains in
the vicinity of coarse particles are prone to destruction while grains
oriented in the actual cube position for the applied cold rolling reduction
are especially apt for conservation.
Transformation Textures in a Controlled Rolled Nb‐V Steel
Authors: Ray R. K. , Butrón-Guillén M. P. , Jonas J. J.
Published: April 2008

The transformation textures produced by the controlled rolling of a
Nb‐V steel are compared with bcc textures predicted analytically from those
of a cold rolled fcc Ni30Co alloy of comparable stacking fault energy. The
calculated textures show very good agreement with experimental ferrite
textures produced from the steel rolled 75% in the γ no‐recrystallization
range before transformation, and there does not seem to be any variant
selection in this case. However, variant selection is likely when ferrite
transformation takes place from more heavily deformed austenite (90%
reduction) and also during martensite formation. In addition to the Cu and
Bs components of the γ rolling texture, the S component also contributes
significantly to the formation of the main components of the transformation
texture.
Texture in Nd‐Fe‐B Alloys Produced by Rapid Solidification
Authors: Szpunar J. A. , Blandford P. , Altounian Z. , Stromolsen J. , Zaluska A.
Published: April 2008

The texture and microstructure of melt‐spun ribbons was studied
using X‐ray diffraction, pole figures and SEM. At constant wheel speed, the
nozzle diameter affects the quenching conditions. The observed changes
were responsible for a drastic variation of the strength of texture through
the thickness of the specimens, and also for significant differences in the
microstructure. We have demonstrated that the observed differences in the
texture are related to the grain size and indicate that there is a relationship
between the growth rate of a grain and its orientation.
Texture Development in Thin Metallic Films
Authors: Knorr D. B. , Tracy D. P. , Lu T.-M.
Published: April 2008

Aluminum films 1μm in thickness are deposited on SiO2/Si(100) by the self‐ion
assisted PIB technique and by sputtering. Texture analysis of the four deposition
conditions reveals an {111} texture component superimposed on a random grain distribution.
The relative fraction of the two components depends strongly on deposition conditions.
Annealing at 400°C for 0.5 hr sharpens the {111} texture component at the expense
of the random while inducing substantial grain growth where mean grain size increases by a
factor of 3.5 to 5. One condition is truly a fiber texture, and the other three have
textures with some deviation from axial symmetry.
Using the Mean Field Model to Analyze the Influence ofTexture on the Hysteresis Behaviour of Silicon Steels
Authors: Kozina T. , Szpunar J. A.
Published: April 2008

A critical study of the Jiles and Atherton Mean Field Model was done. to determine the validity of the
modal, a tool in describing and understanding the magnetization process in textured silicon steels.

Hysteresis loops were generated using an Epstein apparatus in various directions with respect to rolling and
for various external magnetic fields. Various techniques of generating the loops from the model and analyzing
the experimental results were proposed. These techniques were then used to obtain the model parameters.

An analysis of the experimental data using this modal lets us conclude that the modal gives a close
description of texture influence on hysteresis behaviour and predicts the variation of the pinning parameter k
which agrees with our understanding of the role of texture in changing the parameter. We have observed that
the highest value of this parameter coincides with the angles at which it is most difficult to magnetize the speciment.
Quantitative Measurement of the Development of Recrystallization Texture in OFE Copper
Authors: Necker C. T. , Doherty R. D. , Rollett A. D.
Published: April 2008

High purity OFE copper samples, cold rolled 58, 73 and 90%, were studied at different
fractions recrystallized to follow the change of texture, the associated kinetics, release of stored
energy, growth rates and microstructures. Higher strains led to a stronger copper deformation
component and a stronger cube recrystallization component. The strength of the cube texture
correlated strongly with the frequency of cube nuclei at the early stage of recrystallization for the
73 and 90% reductions. The kinetics had low Avrami exponents of 1.1, 1.2 and 1.8 respectively
for the 3 rolling reductions. Average growth rates, G, decreased linearly with fraction
recrystallized. However, unlike the study by Hutchinson et al., here the rate of stored energy
release was constant with fraction recrystallized.
Microstructure and Local Texture in Hot Rolled Aluminum
Authors: Weiland H. , Hirsch J. R.
Published: April 2008

Local textures have been determined in the deformed and partially recrystallized
substructure of a hot rolled commercial aluminum alloy by measuring individual grain
orientations in a TEM. These local textures were compared to the global textures of the
bulk material obtained by conventional X‐ray diffraction techniques. Cube oriented nuclei
were analyzed and two mechanisms for the development of strong cube textures of hot
rolled and subsequently cold rolled and recryslallized aluminum sheet are discussed. These
mechanisms are the uniform stability of cube oriented grains during rolling and the
generation of cube oriented nuclei by shear strains.
Neutron Diffraction Texture Analysis of Multiphase andLow‐Symmetry Materials Using the Position‐Sensitive DetectorJulios and Peak Deconvolution Methods
Authors: Schäfer W. , Merz P. , Jansen E. , Will G.
Published: April 2008

Diffraction patterns of multiphase and low‐symmetry materials
are characterized by a manifold of reflections with high peak overlap, hindering
individual pole figure measurements by conventional X‐ray technique. These
difficulties can be overcome by using neutron diffraction with its advanced
position‐sensitive detector technology and by separating overlapping peaks by
means of profile fitting methods. The paper describes appropriate instrumental
equipment and a semi‐automatic procedure for individual pole figure data analysis
to be performed interactively on a PC. Pole figure results of a two‐phase
chalcopyrite ore are given.
Modelling of Texture Development During Nucleation and Grain Growth
Authors: Tavernier Ph. , Szpunar J. A.
Published: April 2008

A model of development of recrystallization texture has been proposed based on physical processes observed
during nucleation and growth of grains. In this model the nucleation is driven by energies stored in various
texture components. The assumption is made that there exists a specific relationship between the place the
nucleation starts and the orientation of the nuclei. The grain growth modelling is determined by the grain
boundary energy and is related to assumptions that certain orientations of grain are favoured during the grain
growth.

The model is used to simulate the texture development in low‐carbon steel and offers in addition to textural
information the prediction of the kinetics of nucleation and grain growth illustrating the fundamental aspects of
grain topology in the deformed and annealed metals which at the same time are general enough to allow to
introduce in the future more realistic assumptions for nucleations and grain growth processes.
The Effect of Particles on Texture Evolution in Commercial AlMn
Authors: Rickert Theo , Guldberg Sigrid , Furu Trond , Nes Eric , Lücke Kurt
Published: April 2008

Two commercial Aluminium alloys with high Mn content were investigated in three
different precipitation states. The rolling textures possess a portion of random orientations
that is proportional to the volume fraction of larger particles. It is therefore identified with
their deformation zones having about double the diameter of the particles. The recrystallization
textures are weak for high annealing temperatures and show the more retained rolling
texture the more the temperature is lowered. This is interpreted as a matter of nucleation site.
But also growth mechanisms influence the texture evolution. Minor texture components are
characteristic for the different conditions.
X‐Ray Measurement of Residual Stresses in Textured Thin Coatings
Authors: de Buyser L. , van Houtte P. , Aernoudt E.
Published: April 2008

The X‐ray diffraction technique is a well known non‐destructive
method to determine the residual stress level in a material. The most
commonly used method is the ′d‐sin2Ψ′ method. However for textured
materials and very thin coatings (0.1 .. 2 μm), this method can no
longer be applied as will be shown. Therefore, a new measurement
method, based on the ’glance angle’ technique has been developed.
Origins of Misorientation Texture (Mesotexture)
Authors: Randle Valerie
Published: April 2008

Characteristics of the misorientations between grains ‐ "mesotexture" ‐ are discussed. It is shown that
a computer simulation approach is a useful way to probe both the relationship between microtexture and mesotexture
and the form of the mesotexture.
Dynamic Recrystallization of a Quartz Porphyroclast
Authors: Lloyd G. E. , Freeman B.
Published: April 2008

Dynamic recrystallization occurs to minimize strain energy via either grain boundary migration
or subgrain rotation1,2. Both result in similar microstructures, but whereas in the former new
grains have their crystallographic orientation controlled by neighbouring grains, in the latter
new grains are derived from the parent grain. We have used the scanning electron microscope (SEM)
electron channelling (EC) technique3-7 and the program CHANNEL8 to distinguish the contribution
of these processes in a 50% recrystallized quartz porphyroclast (Crinan Grits, Dalradian, SW
Highlands, Scotland; 370‐400℃)9,10. This grain exhibits a core region of subgrains and a mantle
region of neoblast grains (Fig. 1).
Two‐Dimensional Computer Modelling of Polycrystalline Film Growth
Authors: Dammers A. J. , Radelaar S.
Published: April 2008

Polycrystalline thin films, deposited from a vapour
phase, often show a columnar morphology. We present
computer simulations of a 2D model of the polycrystalline
growth process. The model consists of randomly oriented
squares, growing from a line. We find, that the characteristic
length scale <Δx> of the growing surface (average edge length
projected on the substrate) diverges as a function of time
according to a power law  ∼tp, with p ≈ 0.52.
Development of an X‐Ray Technique for Measuring Grain Size as aFunction of Orientation in Polycrystalline Materials
Authors: Abbruzzese G. , Di Nunzio P. E.
Published: April 2008

A new application of the X‐ray technique developed by B.E. Warren [1], is
presented here. The method, based on statistical fluctuation of counts recorded
by a properly modified X‐ray diffractometer, has been used to estimate
the average grain diameter of different textural classes in metallic
polycrystalline materials; it has been tested to evaluate its reproducibility
and precision limits. The method appears to be promising for current
applications in industrial research laboratories and for quality control
routines since specimen preparation is easy and measurement is automated.
The Influence of Temperature on the Rolling Textures of Al Alloys in the Absence of Recrystallization
Authors: Bacroix B. , Brun O. , Chauveau Th.
Published: April 2008

Textures measured on 2 Al alloys after hot and cold rolling are analyzed in detail. It is
shown that the texture strength and the intensity of the brass component increase with
increasing temperature. This is in good agreement with some texture predictions.
The Effect of Measurement Geometry for on‐Line Texture Analyzing Systems
Authors: Blandford P. , Szpunar J. A.
Published: April 2008

A laboratory prototype of a system for the measurement of texture on‐line
in the manufacturing process of steel or aluminum is being built at
McGill University. In order to test the effect that the different measurement
geometry, i.e an angular dispersive reflection or an energy dispersive
transmission geometry, has on the calculation of the coefficients of the
orientation distribution function (ODF), a number of simulated texture
measurements were done for both geometries. The effect of the measured
texture on the prediction of magnetic torque was also studied.

In general, there is good agreement between the textures calculated
by simulating the two measurement geometries and the original texture
used to recalculate the pole figures from which the simulation data was
extracted. The results also showed that, for the slightly inhomogeneous
steel, the bulk magnetic torque predicted from the texture measurements
simulating the energy dispersive, transmission geometry was only slightly
better than that predicted from the angular dispersive, reflection geometry.
In the case of the inhomogeneous steel, the prediction from the transmission
geometry was significantly better than that of the reflection geometry. It
has been shown that measurement geometry for on‐line texture analyzing
systems has a significant impact on the accuracy of the texture information
obtained and the prediction of certain property anisotropies, especially for
those sheet materials exhibiting significant through‐thickness
inhomogeneity.
Effect of Whiskers and Small Particles on the Deformation and Recrystallization Texture of Aluminium
Authors: Hansen N. , Jensen D. Juul , Liu Y. L.
Published: April 2008

The effect of small Al2O3 particles (d < 0.1 μm) and of a mixture of Al2O3
particles and SiC‐whiskers on the cold‐rolling and on the recrystallization texture of
aluminium has been studied by neutron diffraction. It has been observed that the
strength and the relative intensity of the main rolling components in the deformation
texture are affected both by small particles and by introduction of SiC whiskers. In the
recrystallized state very different textures have been found ranging from a weak cube
texture to a strong {100} <013> (N‐texture). The measured textures are related to the
size of the recrystallized grains in a discussion of the effect of small particles and
whiskers on deformation microstructures and nucleation and growth processes.
Effects of iron and Silicon on Recrystallization Textures of Drawn Aluminium
Authors: Inakazu N. , Kaneno Y. , Inoue H.
Published: April 2008

The recrystallization textures of cold drawn aluminium alloys
were determined by means of the orientation distribution functions
(ODFs). The changes in texture with annealing temperature were
interpreted by examining the interrelation between recrystallization
and precipitation. The drawing textures of all the specimens
are mainly composed of the <111> fiber component. In the case of
Al‐Si, silicon exists in the solid solution at high and medium
temperatures (623‐723K), therefore, the <111> component is
sharpened and the recrystallization textures are composed of the
strong <111> component and the weak <100> one. On the other hand,
precipitation of silicon participates in recovery and recrystallization
at low temperatures (523‐573K) so that the <100> component
nearly equals to the <111> one in intensity. Al‐Fe shows the
strong <111> + weak <100> fiber texture in the all ranges of
annealing temperatures, though the <111> component is stronger at
a high temperature (723K), where precipitation occurs after
recrystallization, than at low and medium temperatures (573‐673K),
where it does before recrystallization. For Al‐Fe‐Si, the recrystallization
textures are almost the same as Al‐Fe except for
weakening in orientation density.
Experimental Aspects of the Use of Electron Back Scattering for Characterisation of Microtextureand Mesotextures
Authors: Randle V. , Furley J.
Published: April 2008

The aim of this paper is to explain the experimental techniques required for the operation
of the EBS system. Also, by use of suitable examples, its potential as a tool for the rapid
analysis of the microtexture and mesotexture of materials is demonstrated.
Rolling and Recrystallization Textures of a Ni‐40Co Alloy
Authors: Ray R. K. , Lücke K.
Published: April 2008

The deformation texture of a Ni‐40 wt. percent Co alloy
has been found to be of neither the pure metal nor the alloy
type. On annealing, an almost random texture is produced in this
alloy in the fullyrecrystallized condition. During the grain
growth stage, a weak cube component develops which does not show
much of a variation even after prolonged annealing.
Influence of Texture and Microstructure Inhomogeneities on theOrigin of Goss Texture in Silicon Steel
Authors: Seidel L. , Lücke K.
Published: April 2008

Development of texture and microstructure of commercial high
permeability silicon steel during rolling and recrystallization were studied by
Orientation Distribution Functions (ODFs) and optical and electron
microscopy. The present results confirm former single crystal results that
large {111}<112>‐oriented cold rolled grains containing shear bands are the
origin of the Goss texture after primary and secondary recrystallization. The
formation of {111}<112>‐oriented grains during intermediate cold‐rolling
can be explained by relaxed constraint models. In the case of iron‐silicon
their orientation density is still enhanced by the transformation of the shear
texture in the hot band subsurface during cold rolling. Formation of Goss
nuclei in shear bands together with growth preference of the Goss nuclei in
these grains leads to a primary recrystallization texture containing Goss
grains.
The Relation Between Texture and Microstructure in Rolled FCC Materials
Authors: Leffers T. , Jensen D. Juul
Published: April 2008

The relations between texture and microstrueture in rolled fcc metals and alloys are described. In materials with low stacking fault energy texture and microstructure together provide a consistent empirical description of the deformation process. In materials with intermediate and high stacking fault energy things are more complicated.
There are a number of textural and microstructural features which are not understood and which probably require a combination of texture and microstructure to be understood. A substantial effort is needed in order to establish this connection.
Plastic Instability in Copper and Brass and its Relation to Microstructure and Texture
Authors: Leffers T. , Ananthan V. S.
Published: April 2008

Second‐generation microbands in copper and bundles in brass reflect plastic instabilities. The possible crystallographic rules for the selection of grains with such instabilities are investigated. In copper the existence of simple crystallographic rules is questionable. In brass there seems to be a set of crystallographic rules which is in reasonable agreement with theoretical considerations.
Analysis of Grain Boundary Cavitation Damage in Copper
Authors: Field David P. , Adams Brent L. , Zhao Junwu
Published: April 2008

The interface damage function (IDF) defining the fraction of damage on crystallite
interfaces in a polycrystalline material1 is extended to include functional dependence
upon individual crystallite lattice orientation of grains composing a boundary. The
material studied was OFHC copper crept at 10 MPa and 0.6 Tm. Major peaks in the
IDF were found through a series of projections of the eight‐dimensional domain of the
function. A maximum value of 0.95 was found for the IDF.
Texture Control and the Drawability of α‐Brass
Authors: Rellick J. R. , Lawley A.
Published: April 2008

Texture strengthening analyses for cubic
metals predict enhanced deep drawing performance
with {110} and/or {111} components in the plane of
the sheet. Since {110}<112> is the primary texture
in heavily cold rolled α‐brass, an attempt was made
to retain this texture through recovery of the cold
rolled material at low temperatures. A second approach
is suggested by the observation of the {110}
texture in α‐brass on annealing ≳600°C (873°K), and
involves short time exposures to limit grain size.
It is found that low temperature recovery treatments,
while partially retaining the rolling texture, produce
a hard condition of low drawability. High
temperature annealing produces appreciable {110}
textural components only at grain sizes too large
for many commercial applications. A potentially
more tractable approach is discussed.
Microbands in 80% Drawn Copper Single Crystals With <111> and <100> Starting Orientations
Authors: Horiuchi S. , Asakura K. , Wassermann G. , Grewen J.
Published: April 2008

Copper single crystals with the starting
orientations <111> and <100> were drawn 80%. In the
core region of the rods the orientations and the
microstructures were investigated. The stable <111>
crystal had a structure consisting of equiaxed cells
and microbands which were formed parallel to the
{111} planes with the exception of the {111} plane
in the cross section of the rod. The <100> orientation
was not entirely stable; the beginning of
some orientational changes was observed at a high
degree of deformation. In the parts with stable
orientation a cylindrical cell structure was found
with the long axes parallel to the drawing direction.
Single microbands formed locally. Dislocation
tangles around them finally developed, which
lead to a change of the <100> orientation.
On Orientation Changes Accompanying Slip and Twinning
Authors: Hosford W. F.
Published: April 2008

The purpose of this note is to make a few observations on several analyses of lattice
rotation by slip and by twinning in deformation.
Program for Calculation of Augmented Jacobi Polynomials
Authors: Morris Peter R.
Published: April 2008

The augmented Jacobi polynomials, designated
Zℓmn by Roe, or the closely related generalized
Legendre functions, of Bunge, are required
for series expansions of the crystallite
orientation distribution. The problem of publishing
extensive tabular information has limited compilation
of these functions to certain crystal and physical
symmetries. This paper gives a brief description
and listing of a computer program which permits calculation
of Fourier sine (m–n odd) or cosine (m–n
even) series expansions of Zℓmn(ξ) for ℓ = 0, 1, …, 32; m = 0, 1, …, ℓ; n = 0, 1, …, ℓ.
Local Textures in Deformed and Recrystallized Aluminium Crystal
Authors: Akef A. , Driver J. H.
Published: April 2008

The recrystallization mechanisms in deformed aluminium single crystals have been investigated by
SEM microdiffraction techniques (ECP and EBSP). Aluminium crystals of (001)(uv0) and (001)[01]
orientations were deformed in plane strain compression to a true strain of ~1 to develop different
deformation microstructures. Transition bands separating deformation bands were formed by
orientation splitting in the (001)(uv0) crystals, but were not observed in the (001)[01] crystal.

During annealing at 250°C and 400°C, recrystallization nuclei are developed in both the deformed
matrix and along transition bands. Matrix nucleation appears to occur by a subgrain coalescence
mechanism according to which the new grains are misoriented 15‐30° from the average as‐deformed
material. Transition band nucleation gives an orientation spread 20‐30° around the original,
undeformed crystal orientation. A well‐defined cube recrystallization texture is obtained at 400°C
after complete recrystallization of the initial cube crystal.
Microtexture Characterization by EBSP in Iron and Titanium Alloys
Authors: Penelle R. , Baudin T.
Published: April 2008

The Orientation Distribution Function (O.D.F.) calculation is usually performed using pole figures
measured by X‐ray or neutron diffraction. However, this kind of experimental technique does not
allow to determine a total ODF since the odd terms of the series expansion are not directly accessible
from pole figures. The individual orientation measurement technique can be used but it is necessary to
estimate the right orientation number necessary to calculate a statistically reliable ODF. For samples
at the surface, at the fifth of the thickness from the surface and at the centre of a Fe 3% Si sheet, the
present study shows that only 100 orientations are sufficient to find the main components of the
texture but this number must be increased by a factor 10 to evaluate with a rather good accuracy the
height of the peaks. In the case of a titanium alloy so called TA6V 350 orientations appear to be
sufficient.
Microstructure and Microtexture Evolution During High Temperature Low Cycle Fatigue of Nickel
Authors: Brodesser S. , Gottstein G.
Published: April 2008

The development of microstructure, texture, misorientation and grain boundary character during
cyclic deformation of Nickel at elevated temperatures was investigated. At high numbers of cycles
grain boundaries align with the maximum shear stress. Texture and microstructure change significantly
and low ∑CSL boundaries with (111) rotation axes emerge. The Schmid factor increases with
progressing deformation but Sachs‐ and Taylor‐type deformation modelling fail to predict the actual
texture change. It is proposed to attribute the observed texture and microstructure development to an
interaction of deformation mechanisms with grain boundary motion.
Grain Boundary Design for Advanced Materials on the Basis of theRelationship Between Texture and Grain Boundary Character Distribution (GBCD)
Authors: Watanabe Tadao
Published: April 2008

On the basis of recent knowledge of structure‐dependent boundary properties, the design and control
of boundary‐related bulk properties and performance of advanced polycrystalline materials are
discussed. The grain boundary character distribution (GBCD) which has been recently introduced as a
new microstructural factor is shown to be a powerful tool for designing and controlling the bulk
properties in polycrystalline materials. The relationship between texture and GBCD has been
discussed in connection with other microstructural factors associated with grain boundaries. It has been
shown that the relationship between texture and GBCD can provide an important clue to the grain
boundary design and control for polycrystalline materials with desirable properties and performance.
The present paper shows recent successful achievement of toughening of brittle materials by
controlling texture and GBCD. The potential and prospective of the grain boundary design and
control for functional materials are also discussed.
EBSP, Progress in Technique and Applications
Authors: Hjelen J. , Ørsund R. , Hoel E. , Runde P. , Furu T. , Nes E.
Published: April 2008

To measure grain orientation in SEM with high accuracy a new EBSP calibration software is
developed. Grain orientation determination is simply based on marking three zone axes in the live
EBSP. The EBSP‐technique has been applied to study misorientation between subgrains in high
purity and commercially pure aluminium. The lattice curvatures, which develop during deformation,
increase with the amount of deformation. During annealing the subgrains grow, resulting in an
increased average neighbouring misorientation due to misorientation accumulation.