bluuebunny/crossref_metadata_2025_split huggingface dataset:
Evolution of the Texture in Steelcord
Authors: Montesin T. , Heizmann J. J. 
Published: April 2008

Tyre industry wishes always wires with best mechanical performances. This
continuous improvement of the performances needs the knowledge and the understanding
of the deformation process of the wire. To reach this goal, it is useful to know the
cristallographic texture and its evolution during the drawing process.The depth of penetration of X Ray not being very important (about some tens of
micrometers or more in metal, depending on he absorption [1]), the X Ray examination
can be considered as a superficial one for large wires (about a millimeter diameter or
more).On the other hand, if we consider thin wires, it can be said that X‐ray can penetrate
deeply and even reach the core of the wire. In this case the information we get from the
diffracted intensities is a mean orientation factor K(ϕ,ψ) [2] subject to modification
caused by the absorption and the diffracting volume effect. This mean factor will be
closer than that of the surface, especially when the wire becomes larger or the texture
gradient gets lower.To measure with accuracy the texture of steelcord and its change, we have
developed a X‐ray diffraction procedure to obtain the texture evolution across the wire
radius for each important step of the drawing process [2,3]. This evolution is studied
according to some drawing parameters.
Rolled textures and Magnetic Properties of Regular Grain Oriented 3% Silicon Steel With Very Low Thickness
Authors: Han C. H. , Shin J. C. 
Published: April 2008

Regular grain oriented 3 wt.% silicon steel sheets of 0.30mm thick, having
orientations near (110)[001], were cold rolled to 0.050mm thick and their 0.100 and
0.050mm thick foils were annealed in order to study the changes in rolled textures,
recrystallized texture and magnetic properties with decreasing the sheet thickness.
the results are summarized as follows:(110)[001] grains of recrystallized sheets are changed to (111)[112] with cold
rolling and (111)[112] grains of cold rolled sheets are restored to (110)[001]
with annealing.The stronger (111)[112] textures are formed in the cold rolled sheets,
the stronger (110)[001] textures are developed in the recrystallized sheets, when the
cold rolled sheets of 0.100 and 0.050m thick were annealed to and above 600°C for
1 hour, recrystallization occurred to show resoring the magnetic properties to those
of the initially secondary recrystallized 0.30mm thick sheets with forming similary
strong (110)[001] textures.
The Effect of Slips on the Anisotropic Behaviour ofPolycrystalline Aluminium at Elevated Temperature
Authors: Dluzewski Pawel H. 
Published: April 2008

A transition from the field of micro‐heterogeneous strains through the crystal strain orientation
distribution function to the averaging scheme used in slip theory is presented. The conjugate measures
of stress and strain have been derived for slip theory.The theory is utilized here to the modelling of the strongly anisotropic, thermally activated, flow
process observed for untextured aluminium in the plastic strain range from 1*10−6 to 0.5%. The
subsequent yield surfaces are obtained by numerical simulation in time, the whole process
corresponding to the definition of yielding used by Phillips and Tang (1972). It is shown that the
observed athermal stress is closely related to residual stresses and depends strongly on the plastic
strain offset applied. In the present considerations a role of orientation distribution of mobile
dislocation densities in the anisotropic flow of polycrystalline metals is discussed.
Application of Normal Distributions on SO(3) and Sn for Orientation Distribution Function Approximation
Authors: Bucharova T. I. , Savyolova T. I. 
Published: April 2008

The orientation distribution function (ODF) in a polycrystalline sample is of special interest in texture
analysis. Its determination from pole figures leads to an ill‐posed problem, the solution of which is
non‐unique.In the present paper the properties of normal distributions on the rotation group SO(3) proposed by
Parthasarathy (1964), Savyolova (1984) are discussed. A method for ODF determination based on
the superposition of the normal distributions is proposed. The parameters of normal distributions
are determined from the experimental pole figures. The application of this method is demonstrated
for a rolling texture of beryllium.
Evolution of Texture and Yield Locus of AISI 409 FerriticStainless Steel
Authors: Mingolo N. , Pochettino A. , Vial-Edwards C. 
Published: April 2008

The evolution of texture and yield locus of AISI 409 ferritic stainless steel under different deformation
paths was analyzed.Texture evolution with plastic deformation was predicted by two models: Taylor (TPG), assuming
pencil glide in {hkl}〈111〉 slip systems and Viscoplastic under the relaxed constraint assumption
(VRC), considering the following slip systems: {110}〈111〉, {112}〈111〉, and {123}〈111〉, selected
according to a strain rate sensitivity law. TPG model tends to predict some stronger developments of
texture than the VRC model.Predictions of stress–strain curves along different loading paths with TPG and VRC models were
very close to experimental results. Texture evolution did not have a significant effect to modify the
rate and the isotropy of the strain hardening process of AISI 409 ferritic stainless steel.
Numerical Determination of the Variation Width of Feasible ODFs
Authors: Schaeben H. 
Published: April 2008

Within all known methods of calculating a model orientation density (odf) from a given set of pole densities (pdfs) the set of all feasible odfs and in particular its associated variation width remained unaccessible up to now.Here, the variation width is mathematically well defined for the continuous and the discrete setting of the fundamental projection equation of texture goniometry. For the discrete case it is shown that it can be numerically determined by a sequence of optimization problems with extremely simple objective functions.The general solution is exemplified for the SANTA FE model data.
Approximation of the Pole Figures and the Orientation ofDistribution of Grains in Polycrystalline Samples by Means ofCanonical Normal Distributions
Authors: Savyolova T. I. 
Published: April 2008

The orientation distribution function (ODF) as determined from experimental pole figures (PF) in a polycrystalline sample by classical spherical harmonics analysis can have ghost effects and regions of negative values. The regions of negative values and the ghosts are a consequence of the loss of information on the “odd” part of ODF.In the present paper the canonical normal distributions (CND) on the rotation group SO(3) and on the sphere S2 in R3 used in texture analysis are discussed.The examples of CND on SO(3), S2 and their PF calculated for hexagonal lattice symmetry and for a rolling texture of beryllium are demonstrated.
Single Grain Orientation MeasurementsApplied to the Formation and Growth ofRecrystallization Nuclei
Authors: Engler O. , Escher C. , Gottstein G. 
Published: April 2008

Measurements of the crystallographic orientation of individual grains provide information on the spatial
arrangement and distribution of orientations in a crystalline solid, i.e. on the orientation topography,
which can be utilized to establish a basis for a deeper understanding of the microstructural mechanisms
during deformation and recrystallization of metallic materials.Techniques for the convenient measurement of single grain orientations with high accuracy by
evaluation of Kikuchi diagrams in a TEM and SEM (EBSD) are introduced. The principles of Kikuchi
pattern formation as well as the measuring and evaluation procedures are outlined. Particular attention
is focused on the automation of pattern indexing in order to provide fully automated evaluation routines.
The unique potential of these techniques is demonstrated by two examples pertaining to the
microstructural evolution during the formation of recrystallization nuclei and their subsequent growth.
Estimation of the Range of Elastic Interaction Due to Grain Misorientation
Authors: Kiewel H. , Bunge H. J. , Fritsche L. 
Published: April 2008

The discontinuities of the elastic constants across grain boundaries in polycrystalline aggregates can
be considered as sources of “compatibility” strains in the adjacent crystals under the action of an external
stress. This effect was studied theoretically using the cluster model of Kiewel and Fritsche. In order
to distinguish the contributions of individual grains, the orientation of only one grain was changed
whereas all others in the cluster were kept constant. The orientation dependent part of the strain field
thus allows to estimate the range over which the influence of an individual grain reaches. The results
shows that this part decreases faster than 1/r3 with the distance from the centre of the considered grain.
It has virtually vanished at two or three times the grain diameter.The magnitude of the compatibility strains depends on grain shape. It was found higher in a cluster
of cubic grains than in clusters consisting of dodecahedral or cubo‐octahedral grains.The compatibility strains vary systematically when the orientation of the considered grain is changed
continuously. The influence of even small misorientations <5° is distinctly visible.The results show that grain shape and orientation correlation must be taken into consideration
additional to the texture in order to obtain narrower bounds for the effective elastic constants than those
by Voigt and Reuss. They show, however, also that orientation correlations of higher than next‐nearest
neighbours have virtually no influence.
Normal Distribution on the Rotation Group So(3)
Authors: Nikolayev Dmitry I. , Savyolov Tatjana I. 
Published: April 2008

We study the normal distribution on the rotation group SO(3). If we take as the normal
distribution on the rotation group the distribution defined by the central limit theorem in
Parthasarathy (1964) rather than the distribution with density analogous to the normal
distribution in Eucledian space, then its density will be different from the usual ()
exp⁡(−(x − m) 2/2σ2) one. Nevertheless, many properties of this distribution will be
analogous to the normal distribution in the Eucledian space. It is possible to obtain
explicit expressions for density of normal distribution only for special cases. One of these
cases is the circular normal distribution.The connection of the circular normal distribution SO(3) group with the fundamental
solution of the corresponding diffusion equation is shown. It is proved that convolution
of two circular normal distributions is again a distribution of the same type. Some projections
of the normal distribution are obtained. These projections coincide with a
wrapped normal distribution on the unit circle and with the Perrin distribution on the
two‐dimensional sphere. In the general case, the normal distribution on SO(3) can
be found numerically. Some algorithms for numerical computations are given. These
investigations were motivated by the orientation distribution function reproduction
problem described in the Appendix.
Calculation of the Effective Absorption Coefficient in Multi‐Phase Powders
Authors: Reefman D. 
Published: April 2008

A calculation of the effective absorption coefficient μeff in multi‐phase powders is presented. Characteristic in
the calculation is, that the distribution function of the grains
is similar to the correlation function for fluids. It is shown,
that for average grain diameters comparable to the inverse of the
absorption coefficients, the commonly used formulae for μeff (either a linear combination of the contituting μ′s or simply μ for a single component) do not hold.The analytical expressions derived for μeff are compared with numerical simulations, which show that, within certain limits, the former give reasonable estimates of μeff. The simulations also show, however, that shape effects can have influence on μeff which are not included (yet) in the formulae.Also shown is that surface roughness can give effects comparable to those of microabsorption, but can be much more sensitive to particle statistics.
X‐Ray Scanning Apparatus for Mapping Texture and Element Distributions
Authors: Schwarzer R. A. , Wehrhahn M. 
Published: April 2008

The past decade has seen some remarkable progress in spatially resolved texture analysis due to new computer‐aided techniques of electron diffraction with the SEM and TEM. To avoid, however, some limitations specific for electron microscopy, an x‐ray scanning apparatus has been developed for the mapping of texture and element distributions on bulk samples. The set‐up consists of a “white” x‐ray source, a collimator system to produce a fine primary beam spot, an x‐y sample stage operated by stepper motors, and an EDX detecting system for peak separation.Energy dispersive x‐ray diffraction and x‐ray fluorescence analysis are used for data acquisition. The density distributions of selected crystallographic directions or of element concentrations in the sample surface are acquired spot by spot, and represented by pseudocolour or grey shade maps. Several texture distribution as well as element composition maps can be obtained simultaneously. Spatial resolution is presently limited to 50 μm by the low level of primary beam intensity.
Silicon in Fe‐Si Alloys: Correction of X‐Ray Intensities for Preferred Orientation
Authors: Figueiredo M. O. , Margarido F. 
Published: April 2008

A texture effect in the silicon phase of industrial Fe‐Si alloys was noticed in the X‐ray diffraction patterns through the reinforcement of the 111 reflection. A similar effect was also apparent in a commercial silicon standard pellet used as reference material and supposed to be texture‐free.A quick correction procedure to account for preferred orientation effects was developed, based on a previous algorithm currently applied for the automatic profile fitting of powder diffractometer data. “Modified Wilson plots” are established for visualizing the efficiency of texture correction according to the proposed method.
An Analytical Method for the Quantitative Determination of the Volume Fractions in Fiber Textures
Authors: Tomov Ivan , Bunge H. J. 
Published: April 2008

In order to evaluate pole‐figure measurements quantitatively, one
needs the normalization factor which reduces measured intensity
values to multiples of the random density. This factor may be
determined experimentally by measuring the intensities of a random
sample or it may be calculated by integrating over the whole
pole‐figure or its asymmetric unit. If pole‐figure values are not
available in the whole angular range 0 ≤ φ ≤ 90° (incomplete pole‐figures), then the calculation is in
general much more difficult and it usually presumes the knowledge
of several pole‐figures.In the case of fiber textures (axial symmetry), consisting of only
a few strongly preferred orientations with the crystal directions
〈uvw〉i parallel to the axis of symmetry, the normalization factor and hence the volume fractions of the components i may be calculated in a rather simple way requiring only one, possibly incomplete, pole figure.
Influence of Grain Refinement of Hot Band and Cold Rolling Reduction on the Formation of Textures and R‐Value of Cold RolledPlain Extralow‐Carbon Steel Sheets
Authors: Senuma Takehide , Hashimoto Natsuko 
Published: April 2008

A textural analysis was carried out to explain the cause of the planar anisotropy of r‐value
of cold rolled plain extralow‐carbon steel sheets. For a detailed analysis, a model for
calculating r‐values from ODF‐data of texture was applied and the influence of each or a
group of crystal orientations of the recrystallization texture on the planar anisotropy of
r‐values was studied. The following results were obtained:A development of {111}〈110〉 − {443}〈110〉 − {332}〈110〉 − {221}〈110〉 enhanced the V‐type
planar anisotropy of r‐values. A decrease in the intensity of these orientations by
increasing the cold rolling reduction or the refinement of the hot band microstructure
reduced the r‐values in L and C directions and hardly affected the r‐value in D direction,
and as a result, the V‐type planar anisotropy of r‐values was improved. On the other
hand, an increase in the intensity of {111}, {334} orientation by increasing the cold rolling
reduction or the refinement of the hot band microstructure raised r‐values in sequence of
L < D < C
directions and contributed to the reduction of V‐type planar anisotropy of r‐values as a whole.
New Parameter Model for TextureDescription in Steel Sheets
Authors: Delannay L. , Van Houtte P. , Van Bael A. 
Published: April 2008

A new model is proposed for the characterisation of steel sheet textures. This model relies
on the identification of 25 relevant parameters in the Orientation Distribution Function
(ODF). Textures consisting of alpha‐ and gamma‐fibres and/or cube and Goss components
can be generated. The model is mathematically formulated and an automatic parameter
identification technique is presented.It was found that the model can quantitatively reproduce almost any industrial steel
sheet texture. Based on this parameter model, a method is presented to systematically study
the sensitivity of material properties on texture.
Investigation of Inhomogeneous Surface Textures With Constant Information Depth: Part 1: Fundamentals
Authors: Bonarski J. T. , Bunge H. J. , Wcislak L. , Pawlik K. 
Published: April 2008

A method is described which allows to measure pole figures under
the condition of constant information depth. This is achieved by
using ω‐ and χ‐tilt simultaneously. In order to obtain satisfactory
integrated intensities the use of a position sensitive detector is
nearly indispensable. The functional relationship between
ω and χ for constant information depth and the transformation
of Euler angles {ϕ1, φ, ϕ2} to pole figure angles {α β} are given as well as the necessary intensity
correction. The use of ω‐tilt leads to blind areas in the centre of pole
figures which can, however, be compensated by increasing the
number of pole figures and using appropriate ODF programs.The method was tested with composite samples obtained by stacking
aluminium foils with known textures but with exchanging rolling
and transverse direction of the uppermost foil. The results will
be shown in the second part of the paper.
Influence of the Secondary Recrystallization Temperature on theSharpness of Goss Secondary Recrystallization Texture
Authors: Woo Jong Soo , Han Chan-Hee , Hong Byung-Deug , Harase Jirou 
Published: April 2008

Primary recrystallized Fe–3%Si specimens containing AI and nitrided were annealed
intermittently with the heating rate of 15℃/h in 100% N2 atmosphere. The magnetic
induction B8 was measured after each annealing. The onset of secondary recrystallization
was detected by the rapid rise of B8. The maximum B8 obtained was about 1.94 T when the
onset temperature of the secondary recrystallization was around 1075℃ regardless of the
initial grain size or nitrogen content.The same primary specimens were coated with MgO and annealed with the same heating
rate in 5% H2–N2. The maximum B8 obtained was nearly same as with the above annealing
condition, however, the initial grain size and nitrogen content was quite contrary in this
annealing. The difference in the optimum grain size and nitrogen content for obtaining the
highest B8 between both annealings was explained on the assumption that ∑9 boundaries
become most mobile at 1075℃ regardless of the annealing methods. Based on this finding,
the possibility of producing grain oriented silicon steel without hot band annealing and
nitriding treatment was shown.
Mechanism of Orientation Selectivity During Grain Growth ofSecondary Recrystallization in Fe‐3%Si Alloy
Authors: Ushigami Y. , Kubota T. , Takahashi N. 
Published: April 2008

Selective growth of {110}〈001〉 grains in the temperature gradient annealing has been
studied in Fe–3%Si alloy. As grains grow, the average
deviation angle from the ideal {110}〈001〉 orientation becomes smaller and orientation
distribution changes corresponding to that of coincidence grains
in the matrix. Secondary recrystallization temperature depends on
the orientation of secondary recrystallized grain and sharper
{110} 〈001〉 grains grow preferentially at lower temperatures.These phenomena are explained by modified Hillert′s model of grain growth. Interfacial
energy of coincidence boundary is lower than that of general
boundary. Therefore, sharper {110}〈001〉 grains, which have higher frequency of coincidence grains in the
primary recrystallized matrix, suffer lower pinning effect from the second phase particles
and thus grow preferentially at lower temperatures.
The Deformation and Shear Bands in the Fe–3%Si Alloy
Authors: Sokolov B. K. , Gubernatorov V. V. , Gervasyeva I. V. , Sbitnev A. K. , Vladimirov L. R. 
Published: April 2008

This paper deals with a metallographic study of shear and deformation bands, which are
formed and developed during rolling and fatigue tests of single crystals and polycrystals
of Fe–3% Si. The effect of the initial orientation of the single crystals, dimensions of
grains in polycrystals, thickness of the samples and certain rolling factors on the formation
of banded structures was analyzed. The effect of these structures on the structure
and the texture, which appear in the deformed alloy subject to annealing, was studied too.
The obtained data provided a better account of the banded structures and permitted
directing ways to control their formation and evolution.
Texture and Microstructure Control in Zinc Coated Steel Sheets.Effect on Formability of the Coatings
Authors: Gaignard S. , Lazik S. , Lietzau J. , Wegria J. , Dubois M. , Philippe M. J. , Esling C. 
Published: April 2008

Many commercial galvanised steel sheets have been characterised before deformation
(grain size, grain distribution in the coatings, pre‐cracking, individual orientations, misorientations
between neighbouring grains, local and global textures) in connection with
the zinc alloy which was used and the process parameters.The samples were bent by a biaxial expansion and examined afterwards. All the coatings
were pre‐cracked before deformation.The extent of the pre‐cracking depends on the intensity and the sharpness of the basal
planes texture of the coating and also on the misorientations across the grain boundaries.
In the same way, zinc primary dendrites and recrystallised grains can hinder the crack
propagation, limiting their extent.We can establish a correlation between the texture, the microstructure of the coatings
(using a concept that corresponds to the mean free path of the crack) and the formability.
As we know the process parameters, it is now conceivable that the texture of the coatings
could be controlled.
Initial and RecrystallizationTextures of Nickel Electrodeposits
Authors: Kim Insoo , Lee Sae Gwang 
Published: April 2008

The texture of electrodeposits vary with deposition conditions. Electrodeposits texture is
also related to microstructure, surface morphology and mechanical properties. When the
electrodeposits annealed, the recrystallization texture may be different from the original
deposition texture. The surface morphology, the microstructure and the initial and
recrystallization textures of nickel electrodeposits vary with deposition conditions.The 〈100〉 and 〈110〉 textures of nickel electrodeposits can be obtained from nickel sulfate,
nickel chloride and boric acid baths. The size of surface asperities decreases with increasing
current density and decreasing temperature. The 〈100〉 and 〈110〉 textures of nickel electrodeposits
changed to the 〈100〉 and texture, when recrystallized, respectively.