E. Ilkhani

P. Paulitsch

Experimental Deformation of Epidotes

In M&#xF6;ssbauer spectroscopy it is desirable to work with single crystals or with polycrystalline material of random orientation. The actual, most occuring, case of preferred orientation (texture) and its influence on the relative line intensities of hyperfine split M&#xF6;ssbauer spectra is analysed. Texture information which can be obtained from such an analysis is demonstrated with variously prepared barium ferrite (Ba Fe12 O19) samples.

E. Kreber

U. Gonser

The Problem of Texture in M&#xF6;ssbauer Spectroscopy

A condensed review of casting, deformation, and annealing textures of polycrystalline metals and alloys is presented. It is intended to provide an informative but simplified reference for researchers, engineers, and students who are seeking quick information on the development of textures in various metal objects, and for those who are primarily interested in the textures of non-metallic materials, but wish to acquire a general background knowledge on the texture formation in metals.

Hsun Hu

Texture of Metals

The three-dimensional orientation distribution was calculated from neutron diffraction pole figures for a copper 27.2&#x25; zinc alloy cold rolled to different degrees of deformation. The results agree qualitatively with those of other authors. There are however differences in the quantitative respect which influence the conclusions to be
drawn. For rolling degrees lower than about 70&#x25; the texture exhibits an orientation tube similar to that of the
copper type, but with a significantly different distribution along the tube axis. For rolling degrees larger than 70&#x25;
the texture can be described by the orientation <mml:math id="E1" xmlns:mml="http://www.w3.org/1998/Math/MathML"><mml:mrow><mml:mrow><mml:mo>{</mml:mo><mml:mrow><mml:mn>110</mml:mn></mml:mrow><mml:mo>}</mml:mo></mml:mrow><mml:mrow><mml:mo>&#x2329;</mml:mo><mml:mrow><mml:mn>112</mml:mn></mml:mrow><mml:mo>&#x0232A;</mml:mo></mml:mrow></mml:mrow></mml:math>. The deformation is assumed to occur according to the Wassermann model and the Hu model respectively in these two ranges.

J. Tobisch

A. M&#xFC;cklichf

The Development of Rolling Texture in &#x3B1;-Brass Determined by Neutron Diffraction

Johanna Grewen

Les Textures Dan Les M&#xE9;taux de R&#xE9;seau Cubique

E. Doering

Determination of the Orientation of Olivine Using the Electron-Microscope-Universal-Stage

U. Schl&#xE4;fer

H. J. Bunge

Authors&#x27; Reply to Comments on the Determination of Wire Textures

Jaakko Kajamaa

Comments on the Determination of Wire Textures

A system of FORTRAN programmes is being described which allows most of the standard problems of three-dimensional texture analysis to be easily carried out. It requires about 25 K memory space and it may easily be enlarged by incorporating further subroutines.

J. Jura

J. Pospiech

A System of FORTRAN for Three-Dimensional Texture Analysis

The present paper describes a computer program for the automatic tracing of new stereographic nets aimed at the description of pole figures.

A. Vadon

D. Ruer

R. B&#xE4;ro

Automatic Drawing of Stereographic Nets

The preferred orientations in hot-rolled, cold-rolled (70 &#x25; reduction), and annealed low-carbon steels (capped and aluminium-killed grades) have been investigated. Particular attention has been paid to the factors that control texture formation during annealing.The elastic energy stored in the cold-rolled steels is orientation dependent and the sequence, estimated from a Fourier analysis of X-ray line broadening, is <mml:math id="E1" xmlns:mml="http://www.w3.org/1998/Math/MathML"><mml:mrow><mml:msub><mml:mi>V</mml:mi><mml:mrow><mml:mn>110</mml:mn></mml:mrow></mml:msub><mml:mo>&#x003E;</mml:mo><mml:msub><mml:mi>V</mml:mi><mml:mrow><mml:mn>111</mml:mn></mml:mrow></mml:msub><mml:mo>&#x003E;</mml:mo><mml:msub><mml:mi>V</mml:mi><mml:mrow><mml:mn>211</mml:mn></mml:mrow></mml:msub><mml:mo>&#x003E;</mml:mo><mml:msub><mml:mi>V</mml:mi><mml:mrow><mml:mn>100</mml:mn></mml:mrow></mml:msub></mml:mrow></mml:math>; the values range from 3.51 to 1.14 cal/g atom. The high energy components (&#x7B;110&#x7D;, &#x7B;111&#x7D;) have elongated cell structures but those of lower energy are equiaxed. In capped steels the high energy components recover and recrystallize most rapidly. In aluminium-killed
steels both recovery and recrystallization are inhibited at low temperatures &#x2264; 500&#x2103; and recrystallization begins first in the &#x7B;111&#x7D; components. It is shown that these effects are associated with precipitation and/or segregation of AlN during recovery. The recrystallization texture is determined primarily by oriented nucleation.

R. L. Every

M. Hatherly

Oriented Nucleation in Low-Carbon Steels

The variations of the fourth-order coefficients of the crystallite orientation distribution function, with rolling reduction have been determined after cold-rolling and annealing for a deep-drawing quality rimming steel and an aluminium-killed steel. These coefficients influence drawability and earing behaviour and by the manipulation of
the coefficients in the distribution function of a 60&#x25; cold-rolled and annealed rimming steel, a hypothetical non-earing sheet texture has been derived. By comparison with the actual sheet texture those textural components which most affect earing behaviour are identified.

G. J. Davies

D. J. Goodwill

J. S. Kallend

Earing in Deep-Drawing Steels

The development of the rolling texture of a low carbon steel was investigated by neutron diffraction calculating three-dimensional orientation distribution functions. The textures consist of two limited fibre axis components A and B centered about <mml:math id="E1" xmlns:mml="http://www.w3.org/1998/Math/MathML"><mml:mrow><mml:mrow><mml:mo>(</mml:mo><mml:mrow><mml:mover accent="true"><mml:mn>1</mml:mn><mml:mo>&#x00AF;</mml:mo></mml:mover><mml:mover accent="true"><mml:mn>1</mml:mn><mml:mo>&#x00AF;</mml:mo></mml:mover><mml:mn>1</mml:mn></mml:mrow><mml:mo>)</mml:mo></mml:mrow><mml:mrow><mml:mo>[</mml:mo><mml:mrow><mml:mover accent="true"><mml:mn>1</mml:mn><mml:mo>&#x00AF;</mml:mo></mml:mover><mml:mn>21</mml:mn></mml:mrow><mml:mo>]</mml:mo></mml:mrow><mml:mo>+</mml:mo><mml:msup><mml:mn>5</mml:mn><mml:mo>&#x2218;</mml:mo></mml:msup></mml:mrow></mml:math>
 and <mml:math id="E2" xmlns:mml="http://www.w3.org/1998/Math/MathML"><mml:mrow><mml:mrow><mml:mo>(</mml:mo><mml:mrow><mml:mn>001</mml:mn></mml:mrow><mml:mo>)</mml:mo></mml:mrow><mml:mrow><mml:mo>[</mml:mo><mml:mrow><mml:mover accent="true"><mml:mn>1</mml:mn><mml:mo>&#x00AF;</mml:mo></mml:mover><mml:mn>10</mml:mn></mml:mrow><mml:mo>]</mml:mo></mml:mrow></mml:mrow></mml:math> respectively with an angle of rotation of about <mml:math id="E3" xmlns:mml="http://www.w3.org/1998/Math/MathML"><mml:mrow><mml:msup><mml:mrow><mml:mn>70</mml:mn></mml:mrow><mml:mo>&#x2218;</mml:mo></mml:msup></mml:mrow></mml:math>. For rolling degrees larger than 50&#x25; the intensity of the fibre axis component A is being modulated so as to favour the orientation <mml:math id="E4" xmlns:mml="http://www.w3.org/1998/Math/MathML"><mml:mrow><mml:mrow><mml:mo>(</mml:mo><mml:mrow><mml:mover accent="true"><mml:mn>1</mml:mn><mml:mo>&#x00AF;</mml:mo></mml:mover><mml:mover accent="true"><mml:mn>1</mml:mn><mml:mo>&#x00AF;</mml:mo></mml:mover><mml:mn>2</mml:mn></mml:mrow><mml:mo>)</mml:mo></mml:mrow><mml:mrow><mml:mo>[</mml:mo><mml:mrow><mml:mover accent="true"><mml:mn>1</mml:mn><mml:mo>&#x00AF;</mml:mo></mml:mover><mml:mn>10</mml:mn></mml:mrow><mml:mo>]</mml:mo></mml:mrow></mml:mrow></mml:math>. The texture may be considered as inverse to the low concentration brass texture in the sense of interchanging rolling and normal directions. It may be understood in terms of <mml:math id="E5" xmlns:mml="http://www.w3.org/1998/Math/MathML"><mml:mrow><mml:mrow><mml:mo>{</mml:mo><mml:mrow><mml:mn>110</mml:mn></mml:mrow><mml:mo>}</mml:mo></mml:mrow><mml:mrow><mml:mo>&#x2329;</mml:mo><mml:mrow><mml:mn>111</mml:mn></mml:mrow><mml:mo>&#x0232A;</mml:mo></mml:mrow></mml:mrow></mml:math>&#x2014;glide and <mml:math id="E6" xmlns:mml="http://www.w3.org/1998/Math/MathML"><mml:mrow><mml:mrow><mml:mo>{</mml:mo><mml:mrow><mml:mn>112</mml:mn></mml:mrow><mml:mo>}</mml:mo></mml:mrow><mml:mrow><mml:mo>&#x2329;</mml:mo><mml:mrow><mml:mn>111</mml:mn></mml:mrow><mml:mo>&#x0232A;</mml:mo></mml:mrow></mml:mrow></mml:math>&#x2014;twinning.

D. Schl&#xE4;fer

The Development of the Rolling Texture of Iron Determined by Neutron-Diffraction

Quantitative studies of textures developed in compressed iron&#x2013;0.02&#x25;C and iron&#x2013;0.14&#x25;C alloys before and after annealing have allowed theoretical predictions based on homogeneous plasticity theory to be assessed. It is concluded that qualitatively the theory is very good but predicts rates of texture development rather higher than those observed. The prediction of the theory that orientations on a line joining [110] and [411] should have a tendency to split into two components on deformation and form transition bands, which may be important in nucleating recrystallisation, has been confirmed by the results of the annealing experiments.

I.  L. Dillamore

H. Katoh

K. Haslam

The Nucleation of Recrystallisation and the Development of Textures in Heavily Compressed Iron-Carbon Alloys

The rolling texture of Cu3Au has been investigated by X-ray diffraction. At room temperature, independently of the degree of long-range order, Cu3Au developed a mixed or &#x201C;hybrid&#x201D; texture; it consisted of elements of each of the prototype face-centered cubic textures characterized by pure copper and 70/30 brass. However, on rolling at 77 K the alloy in the disordered state was significantly more &#x201C;brass-like&#x201D; than when it was fully ordered. This result may be explained by a stacking fault energy texture reversal analogous to that observed in wire drawing at low SFE. The lack of twinning (or other deformation mechanism such as slip by partial dislocations) in the ordered alloy could be responsible for this reversal.

R. A. Vandermeer

J. C. Ogle

The Rolling Texture of Cu3Au

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Texture, Stress, and Microstructure