Primary Recrystallization Texture Research Articles

ニッケル圧延板において2次再結晶により出現する立方体集合組織

In a high-purity electrolytic nickel cold rolled to 72.5% reduction, the cube texture developes as the secondary recrystallization texture. The major part of the primary recrystallization texture is nearly random except a weak preferred orientation of (100)[001]. The results can be rationally interpreted on the basis of the ‘oriented growth’ theory. It is concluded that the nearly random texture after primary recrystallization is due to the ‘random nucleation’ and that the cube texture developes by the ‘selective growth’ of large primaries with (100)[001] orientation.

Croissance, par recristallisation secondaire, de gros cristaux exempts de macles dans le cuivre purifié par fusion de zone

Only zone refined copper, rolled 91%, at −196 °C, and annealed at 1050 °C under high vaccum (10−7Corr) yields large twin-free crystals by secondary recrystallization. The textures of the crystals are of the pes: (110) [114] and (751) [12 7 49]. In the case of high purity copper (99.999%), small grains are obtained, while with OFHC copper (99.99%), the crystals show a lot of large twins. Each type of secondary grain is related to two principal components of the primary recrystallization texture by two rotations about two common <111> poles. The observed relationships are high angle boundaries with coincidence lattice sites (Kronberg-Wilson boundaries).

Development of primary recrystallization textures in metastable austenitic steels

The cold-rolling and annealing textures of 18%Cr–10%Ni, 18%Cr–12%Ni and 18%Cr–14%Ni steels have been examined with particular reference to the role of the martensite transformation in developing primary recrystallization textures. The amount of martensite formed after 90–95% cold rolling increases from ~5% for 18%Cr–14%Ni steel to ~86% for 18%Cr–10%Ni steel, and textures of both α′ martensite and the remaining austenite are the same for each steel. Principal components of the martensite texture are {112} 〈\bar 110〉 and {111} 〈\bar 1\bar 12〉, with a minor component {001} 〈\bar 110). The austenite exhibits a normal f.c.c. alloy type texture, {110} 〈\bar 112〉+ a minor {110} 〈001〉 component. Both 18%Cr–12%Ni and 18%Cr–14%Ni steels recrystallize to a {225} 〈\bar 5\bar 33〉 texture, whereas the 18%Cr–10%Ni steel recrystallizes to mainly {230} 〈3′\bar 2′14〉 and {6′10′1} 〈5\bar 31〉 orientations with considerable spread remaining in the region of {6′8′17}〈\bar 5\bar 75〉, which is close to {225} 〈\bar 5\bar 33〉. Factors influencing development of the annealing textures are the relative amounts of α′ and γ formed by cold rolling, recovery in both phases, α′ → γ shear transformation, variant selectivity during the transformation and, finally, competitive growth of favourably oriented nuclei.

Fe-A1-N 合金の一次再結晶集合組織におよぼす炭素量の効果

Fe-Al-N alloys investigated contained<0.005%, -0.06% Al, <0.002%-0.02% N and 0.001%-0.04%C. Effects of C content on primary recrystallization texture, A1N precipitation, grain size and drawability in these alloys were studied.With increasing C content, the amount of grains with {111} lattice plane parallel to the sheet plane decreases, the main component of primary recrystallization texture changes from {111}‹110› to {554}‹225›, grain size decreases, grain shape changes from the “pancake” to the equiaxial type, and thedrawability markedly decreases.These effects of C content on various properties of Fe-Al-N alloys are rather inconspicuous for the C content up to 0.01%but become extremely remarkable when it exceeds 0.01%and are explained by the effect of C content on AIN precipitation during precipitation treatment prior to cold rolling and during heating to (and at) the annealing temperature.

The effects of AIN on secondary recrystallization textures in cross rolled and annealed (001) (hkl) oriented single crystals of 3 Pct Si-Fe

A study was made of the effects of A1N on the recrystallization textures in cross rolled and annealed (001)[hkl] oriented single crystals of 3 pct Si-Fe and A1N was found to have a great effect on secondary recrystallization textures. Cross rolled and annealed (001)[hkl] oriented crystals containing fine needle-like A1N about 1 µ or less in length develop (001)[hkl] oriented secondary recrystallization textures at the expense of the primary recrystallized matrix. Furthermore, very fine needles of A1N contained in (001)[110] oriented single crystals control the orientation of primary recrystallization textures.

〈110〉 軸が圧延方向に平行なフェライト鋼単結晶での {011}〈100〉 一次再結晶集合組織の形成

Single crystals of 3% silicon iron and 17% chromium iron alloys with a common [110] axis parallel to the rolling direction and with a rolling plane rotated about this axis from (001) plane through angles, θ, equal to 35, 43, 45, and 55 degrees were cold rolled by 60, 70 and 80% and annealed at 600, 700, 800, and 1 100°C.After cold rolling, initial orientations are macroscopically maintained. In the substructures of cold rolled matrixes, the small abnormal regions in which deformation proceeds by single slipping on the particular one of the slip systems having high Schmid factors are observed. The frequency of the formation of these abnormal regions is higher as θ of crystals and/or the reduction of cold rolling are increased.The primary recrystallization textures of the crystals are approximately {011}‹100› or {011}‹211›, and the sharpness of {011}‹100› texture becomes maximum in the 3 % silicon iron crystals of θ equal to about 45°, cold rolled 60% and annealed at 600°C. In the very early period of annealing, recrystallization embryos are observed in the abnormal regions mentioned above.

Magnetic domain observations on 0.014-inch 50-percent Ni-Fe strip

The Kerr effect was used to observe and photograph surface domain patterns in the 0.014-inch 50-percent Ni-Fe strip after high temperature vacuum annealing treatments on commercial cold rolled material. The type of domain pattern observed depended on the recrystallization texture and also on the duration of the annealing treatment. The domain structure in primary recrystallization textures,

A Study of Recrystallization Texture Formation in Cold Rolled Iron Sheets with X-Ray Diffraction Techniques

AbstractThe possibility that primary recrystallization textures are influenced by local inhomogeneities of deformation induced in the regions of grain boundaries has been confirmed by comparing the cold rolling and the annealing textures of polycrystalline pure irons which were different in the grain size prior to cold rolling. Analyses were made for the effects of deformation on crystals, namely storage of lattice strain and orientation spread, with application of X-ray diffraction techniques, in order to elucidate the role of in homogeneities of deformation on recrystallization texture formation. Apparent correspondence was found between the orientation dependence of stored strain energy and the textural change on recrystallization. This is a scribed to oriented nucleation in high energy blocks, in the case of originally large-grain material in which the effects of inhomogeneities of deformation are small. But discrepancies arise on this basis in originally small - grain material in which the effects of inhomogeneities of deformation are thought to be considerable. The discrepancy is inferred to arise as an effect of local inhomogeneities of deformation, from the change in the trend of rotational orientation spreads from, a stable orientation and the extent of development of potential nuclei of recrystallization at high energy blocks in the orientation spreads. The change is considered to give rise to the variation in amount of microstrain distribution, which is expressed in recovery characteristics of lattice strains and in the dependence of microstrains on the column length as analyzed by following the procedure of Warren-Averbach.

Effects of AlN on the Primary Recrystallization Textures in Cold-Rolled-(110)[001]-Oriented Single Crystals of 3% Silicon Iron

Cold-rolled-(110)[001]-oriented single crystals of 3% silicon iron containing AlN in solution develop a doublet {111} 〈110〉−oriented primary recrystallization texture consisting of grains with diameter of 0.5 to 1 mm after anneal at 550°C for 40 h followed by anneal at 1200°C. At the first anneal, very fine needle-like AlN precipitates, while (110)[001]-oriented primaries begin to originate at the surface of the sheet. At the heating process of the subsequent anneal, doublet {111} 〈110〉−oriented primaries originate at the middle of the sheet, and then grow at the expense of (110)[001]-oriented primaries. It is proved that very fine needle-like AlN precipitated after cold rolling is found to have a great effect on these primary recrystallization phenomena.

Coalescence of Sulfides during Secondary Growth in 3% Silicon—Iron

The behavior of manganese sulfide inclusions in the development of the cube-on-edge texture in 3% silicon—iron was investigated. Primary-recrystallized specimens of two commercial alloys were heated from 590°C to 760°, 870°, 980°, 1090°, and 1200°C in dry hydrogen. The sulfide-particle sizes were measured as a function of annealing temperature by electron microscopy. The measurements showed that a marked coalescence of the particles occurred between 870° and 980°C. In one of the alloys studied, vigorous secondary grain growth took place concurrently with the coalescence of the inclusions. The secondary growth was complete before any sulfur was removed from the specimens by diffusion. In the second alloy, which had a weaker cube-on-edge component in the primary recrystallization texture, normal grain growth occurred despite a similar coalescence of the sulfide particles.

7-3黄銅強圧延板の再結晶の電顕観察

The recrystallization process in 7-3 brass cold rolled by 93% was examined by using an electron microscope. The orientation of the recrystallized grains 1 to 3 μ in diameter, formed at the initial stage of recrystallization, was statistically at random. It can be said, therefore, that the primary recrystallization texture whose major component is {225}〈734〉 is formed due to the oriented growth mechanism.

Secondary Recrystallization and Its Relation to Magnetic Properties in Thin Grain-Oriented 3% Silicon-Iron

Polycrystalline 3% silicon-iron with (110)[001] texture forms a primary recrystallization texture near the original texture after cold reduction of about 70% followed by primary recrystallization. If rapid heating is used for primary recrystallization, vigorous secondary recrystallization by grain boundary energy takes place after subsequent annealing at 775°C. The secondaries grow to about 5-mm diam with a texture deviating from the primary texture. Annealing twins also form during secondary growth. The activation energy for this growth was found to be much lower than for growth processes dependent on impurities for inhibitors. Such secondary growth must be avoided in commercial applications. If primary recrystallized material is annealed at 1200°C under conditions favorable for growth of (100) by surface energy, (100)[001] secondaries will grow depending on the amount of prior cold reduction.

Metallurgy of Oriented Silicon Steels

For the past twenty-five years, a single oriented silicon steel containing 3% silicon has been commercially produced. The crystallographic description of this material is usually given as (110)[001]. It is now generally agreed that this texture occurs because of a preferred type of secondary recrystallization occurring at temperatures above 950°C. The primary recrystallization texture contains only a small fraction of the (110)[001] component which forms from a (111)[112] deformation texture. In order to complete the orientation process by secondary recrystallization, various impurities have been suggested. These impurities are in the form of a second phase. However, manganese sulphide has been found to be the most effective for providing conditions for selective growth of the (110)[001] component. Furthermore, at the desirable annealing temperatures, sulfur is rapidly lost by diffusion, thus, the final product is highly oriented and has excellent properties because of the low impurity level. More recently, a cube texture (001)[100] has also been made by at least two techniques. By controlled columnar freezing of the ingot, a type of 〈001〉 fiber texture can be produced. If this structure is carefully cold rolled and annealed, eventually a primary recrystallization (100)[001] texture will result. Alternately the cube texture can also be achieved by a controlled surface energy reaction causing a secondary recrystallization. The primary recrystallization texture necessary for the production of a highly oriented product is obtained by rolling and annealing a (110)[001] type of orientation. The secondary growth of the (100)[001] grain is controlled by surface and grain boundary energies. A critical amount of sulfur is required in the steel to initiate the cube grains. However, an excess of either sulfur or oxygen will prevent the growth process. Elimination of oxygen to the lowest possible levels will favor cube growth providing that the sulfur content is in a critical concentration range. If the sulfur content drops to too low a level, cube grain growth will also cease. The range of sulfur required for cube growth is orders of magnitude below the reported level of solid solubility.

Recristallisation secondaire et recristallisation apres ecrouissage critique de l'uranium de haute purete

The growth of large grains, either by secondary recrystallization after deformation by heavy rolling and prolonged annealing at high temperatures in the α phase, or by critical straining and annealing applied to a primary recrystallization texture, has been observed in electrolytic uranium of high-purity. Only uranium of high purity undergoes these two types of exaggerated grain growth. Thus, these two methods of growth provide then a very secure qualitative criterion of the purity of the uranium. Secondary recrystallization gives rise to crystals of smaller dimensions than growth after critical strain, because there are always whatever may be the length and temperature of anneal, some remnants of the fine grains of the primary recrystallization texture. By critical strain, however, it is possible to obtain very large and very perfect grains (of 1—3 cm 2 surface area) together with the complete disappearance of the primary recrystallization texture. The crystalline orientation of a very large number of grains formed by the two methods of growth have been determined by Laue back-reflection diagram. The crystals of secondary recrystallization possess a texture very much more pronounced than that displayed by the crystals produced by critical straining. However, in the two cases, it is remarkable that the b axis of all the crystals seems to play an important role in the growth since it is always oriented essentially parallel to the direction of rolling. It is only when a deformation is applied to the primary recrystallization texture, considerably in excess of the critical deformation that one observes growth during further annealing of crystals having some very diverse orientations. An attempt has been made to explain these two modes of growth, by secondary recrystallization or by critical strain, by relating the deformation texture obtained on heavy deformation to the textures either of secondary recrystallization or of recrystallization after critical strain.

方向性珪素鋼帯の2次再結晶に及ぼす微量添加元素の影響

Effects of minor elements on secondary recrystallization in cold rolled 3.25 wt%Si-steel were studied.It was found that the presence of impurity elements such as Pb, Sb, Nb, Ag, Te, Se, or S is necessary in order to develop the strong (110)[001] texture by secondary recrystallization. To obtain complete secondary recrytallization, the primary matrix grains must be stabilized so that they remain small as compared with the secondaries which eventually consume them.The activation energy for nucleation of secondary recrystallization was obtained to be 57∼135 kcal/mol.The free energy of activation for secondary grain boundary migration at 900°C was calculated to be 30 kcal/mol. This value is much smaller than that for primary grain boundary migration. This result indicates that primary grains in orientations deviating markedly from the primary recrystallization texture grow into secondary grains having specific preferred orientations.

On a Complex Recrystallization Texture in 3% Silicon Iron

Components in a complex primary recrystallization texture, which is a matrix texture for secondary recrystallization to the Goss texture in 3% silicon-iron strip, have been determined by the axis-chart method of Jetter, McHargue, and Williams. The results obtained are compared with former pole-figure results and found to include components not previously resolved or noted. It is found also that the components of the texture explain reasonably well the observed magnetic torque curve of the material.

(110) [001] Secondary Recrystallization Texture in Three Percent Silicon-Iron

The secondary recrystallization texture has been related to the structure developed during prior processing. The (110) [001] component of the primary recrystallization texture, from which secondary grains grow, develops from the (111) 〈112〉 doublet component in the prior recrystallization texture. If the material undergoes two rather than one prior recrystallization heat treatments (each separated by a cold reduction), the amount of the (110) [001] component in the primary recrystallization texture is in general increased, and as a consequence, the completeness of secondary recrystallization is promoted.

Development of Preferred Orientations in Silicon Iron

The (110) [001] texture in silicon iron arises by a process of secondary recrystallization after cold reduction of the strip in two stages separated by an anneal. It is possible to produce the same texture by a one-stage or a three-stage reduction process. The rolling textures and primary recrystallization textures for each of these processes have been experimentally determined and are all different. In spite of this, the (110) [001] secondary orientation develops in each case. It is tentatively suggested that impurities in the steel, already known to be important in controlling grain growth in silicon iron, also supply the directional forces leading to the (110) [001] texture.

Simple orientation relationships for secondary recrystallization in Si-Fe

Reorientation due to primary recrystallization in (111) [112] oriented single crystals after 70 pct reduction in thickness was found to occur by rotations of approximately 25° to 30° and in such a way as to produce one strong component and several weak components. The strong component had the (110) [001] orientation. Upon further annealing secondary recrystallization occurred, but without the formation of new components. The (110) [001] orientation disappeared and some of the weak components of the primary recrystallization texture failed to produce identically oriented components in the secondary recrystallization texture, but other weak components developed into components of the secondary recrystallization texture. As a result the latter were related to the cold rolled orientation by rotations of approximately 25° to 30°. The results obtained could be explained rather simply in terms of the oriented nucleation growth selectivity theory wherein large grains (primaries) from weak components of the primary recrystallization texture grew into secondary recrystallization grains (secondaries) having the 25° to 30° rotation relationship with the cold rolled orientation.

Primary Recrystallization Textures in Cold Rolled Si-Fe Crystals

The primary recrystallization textures of 11 single crystals cold rolled 70 pet were determined. The effect of crystal orientation on recrystallization behavior was investigated also and found to be large. Ah exception was found to the relationship that strong components of the recrystallization texture are rotated from the cold rolled texture by 30° about axes, but generally this relationship was found to hold quite well. Evidence supporting oriented nucleation was found and discussed in terms of probable active slip systems and edge dislocations.