Influence of the Rate and Degree of Deformation on the Texture , Structure and Mechanical Properties of Steel

The tests of uniaxial tensile by 10, 20, and 30% at strain rates of 0.1, 1, 60, 120, and 300mm/min in rolling direction and transverse direction of recrystallized cold-rolled low-carbon steel sheets were carried out. The effect of rate and degree of deformation on the texture, structure, and mechanical properties were studied. The texture transformations and the growth of the anisotropy of mechanical properties with increasing strain rate up to 120mm/min are explained by the effect of crystallographic intragranular slip and twinning of deformation mechanism. The further increase of deformation rate leads to texture scattering and decreasing of properties anisotropy, which are bound to the difficulty of intragranular sliding and activation of grain boundary sliding.


Introduction
The deformation of polycrystalline metal forms the preferential crystal orientation or texture.Type of texture depends on many factors, namely, circuit deformation, crystal structure of the metal, temperature, strain rate, and all.The deformation ratio and temperature are generally studied in connection with their effects on the deformation resistance of the metal during processing pressure [1,2].The nature of the texture that formed at different strain rates and temperatures of deformation during the mechanical tests remains often unclear.However, the study of the crystallographic texture of deformed polycrystals allows determining the mechanisms operating during plastic deformation of the metal and determining the nature of change of its physical-mechanical properties [3].In [4] studied the effect of strain rate during the uniaxial tensile tests on the formation of the texture, but influence of the deformation degree in this case was not investigated.
The aim of the present work is to study the texture, microstructure, mechanisms of plastic deformation, and the change of the mechanical properties under different rates of deformation and its degree of uniaxial tensile of low-carbon steel sheets.

Materials and Methods
The low-carbon cold-rolled steel sheets 0.95 mm in thickness after recrystallization annealing were studied.The chemical composition of steel was 0.06% C, 0.35% Mn, 0.40% Si, and ∼0.025% S and P, the masses in %.Specimens for mechanical tests of initial length of the working part 50 mm and a width of 12.5 mm were cut from the sheets in the rolling direction (RD) and transverse direction (TD).Mechanical testing was carried out by uniaxial tension at room temperature by means of tensile machine 250N5A WN 143331 with force sensor ID 0 WN 805506 20 kN.The strain rates of 0.1 mm/min, 1 mm/min, 60 mm/min, 120 mm/min, and 300 mm/min were applied.
Crystallographic texture was studied after uniaxial tensile tests of 10, 20, and 30% by means of electron backscatter diffraction (Method EBSD) [5] from the RD.After deformation, surface of deformed sample (perpendicular to tensile 2 Journal of Metallurgy axis) was prepared for EBSD study by conventional mechanical grinding and polishing, followed by final vibratory polishing.Data on the microstructure and texture obtained electron microscope LEO 1455 VP at accelerating voltage of 20 kV.The step size was 0.17 m.To describe the texture were using inverse pole figures (IPF) of rolling direction (RD), normal direction (ND), and transverse direction (TD).

Results and Discussions
Experimental IPF of steel after tensile at different strain rates on different strain degrees are represented in Figures 1-3.The corresponding microstructures are shown in Figure 4.The initial average grain size measured in two mutually perpendicular directions (TD × ND) was 14 × 7 m (Figure 4(a)).The interpretation of the texture data was carried out on the basis of following (conceptions) regularities.The activation of the known crystallographic mechanisms of slip and twinning along certain crystallographic planes and directions develops textures of a particular type.Activation of grain boundary sliding is not associated with the formation of crystallographic texture and leads to weakening and scattering texture that already exists in the material [6].
On the IPF (ND) of the initial specimen (Figure 1(a)) the absolute maximum of pole density of ∼10 0 displaces on ∼10 from the pole ⟨111⟩ along the diagonal ⟨111⟩-⟨100⟩ stereographic triangle.There is wide scatter of the pole density.In addition there are two other pole density maxima at ∼7 near the ⟨113⟩ (with a scatter up to ⟨321⟩) and ⟨320⟩.
On the IPF (RD) a maximum of ∼14 displaces from the pole ⟨110⟩ to ⟨320⟩.On the IPF (TD) of the initial specimen two intense ∼14 maximum pole densities are observed.One coincides with the ⟨111⟩ direction, and the second is shifted from the ⟨111⟩ to ∼100 along the diagonal ⟨111⟩-⟨100⟩ stereographic triangle.This indicates the presence of a partial axial texture in the texture plane deformation.The origin of one of them is related to the rotation of orientations of the type {ℎ} ⟨110⟩ in a constrained deformation around the RD [7].The second axial orientation is caused by rotation around the ⟨111⟩ [7].Thus, texture of original sheet is characterized by superposition round {113} (110) and {111} ⟨110⟩ recrystallization texture of mild steel [8].
When the tensile strain is 10-30% at a strain rate of 0.1 mm/min, the grains in the sample rotate so that crystallographic ⟨110⟩ axes coincide with the RD.The limited axial texture with axis almost coinciding with the ⟨110⟩ direction is formed in the samples.The pole density of ⟨110⟩ is ∼14 in the IPF (RD) (Figures 1(b)-3(b)).When takes rotation around the indicated axes, the normal direction coincides with different probability with normals to crystallographic planes {111}, {113}, {112}, {335}, {221}, and {355}, as seen from IPF (ND).The pole density of 8 observed on the IPF (ND) near ∼ ⟨113⟩ may be caused by twinning in the conjugate plane {112} of the main tensile texture component ⟨110⟩ or by compression along the ND during deformation by tensile along the RD in the test [7].Area of high pole density of value ∼10 near pole ⟨335⟩ scattered up to ⟨111⟩ observed on the IPF (TD).Activation of the crystallographic slip on the systems {110} ⟨111⟩ may result in the formation of such textures [7].Thus, the axial texture with axis ⟨110⟩ parallel to the RD begins to form in the sheet after tensile on 10% at strain rate of 0.1 mm/min.
The intense maximum ∼12 near pole {111} on IPF (TD) is observed (Figure 2(b)) if tensile degree is 20% at a strain rate of 0.1 mm/min.This indicates the formation of the planar texture of the type {112} ⟨111⟩.
The abovementioned planar texture weakens since the intensity maximum at about {111} pole on IPF (TD) reduces to 8 and the area of high pole density becomes wider after uniaxial tensile strain by 30% at a rate of 0.1 mm/min (Figure 3(b)).
Tensile strain by 10% at a strain rate of 1 mm/min leads to improvement of axial texture ⟨110⟩ along RD with a maximum density of about 14 (Figure 1(c)) due to the action of the abovementioned crystallographic deformation mechanisms.During the tensile of the sample along the RD the compression in the ND takes place.Thus the maxima of pole density value of ∼11 and ∼7 about {553} and {533}, respectively, on IPF (ND) are formed.The maxima of this type {ℎℎ} and {ℎ} with high values of ℎ and  (ℎ > l) are formed by compression, if the primary and cross slip are carried out [7].The limited axial texture with the axis of ∼ ⟨533⟩ parallel to the TD is formed in this case, as seen in the OPF (TD), where the maximal pole density ∼12 is observed to be about {533}.
Similar texture is formed at the tensile strain of 20% at the strain rate of 1 mm/min (Figure 3

(c)).
A planar deformation texture near to the {112} ⟨111⟩ is formed in the sample at a tensile strain of 30% at a strain rate of 1 mm/min (Figure 3(c)).
For the sample deformed with the tensile strain by 10% at the strain rate of 60 mm/min the displacement of the axis ⟨110⟩ to ⟨320⟩ (pole density is ∼10) on the IPF (RD) and also the scattering texture on IPF (ND) are observed (Figure 1(d)).The peak of high intensity (with pole density ∼14) is formed in pole ⟨111⟩ on the IPF (TD) at the same time.
This testifies to the rotation of the crystals around the TD under tensile.Thus, the limited axial texture between ≈ {112} ⟨110⟩ and {123} ⟨320⟩ with the axis ⟨111⟩ parallel to the TD is formed when tensile strain rate increases to 60 mm/min.
When tensile strain is 20% at a strain rate of 60 mm/min (Figure 2(d)), the texture formed is similar to the texture that was formed by means of tensile strain of 10% at strain rate of 0.1 mm/min (Figure 1(b)).This testifies to similar deformation mechanisms that operate at appropriate deformation modes.
Tensile strain in the RD by 30% at strain rate of 60 mm/min (Figure 3(d)) promotes the formation of texture with the axes ⟨210⟩, ⟨320⟩, and ⟨331⟩ parallel to the tensile direction.The similar orientations may be caused by twinning on the twinning plane (1 12).The twinning dislocation is (1/6) [111] for crystals adjacent to the [001].Slip system,     which supplies the twinning dislocations during deformation via coplanar slip, is (101) [111] [7,9].As can be seen in Figure 4(j), the boundaries of the matrix ferrite are straight comparatively.But a series of notches is presented in some cases.These notches are due likely to either faults or to detwinning by slip, but their exact cause and nature have not been established [10].
Tensile strain in the RD at the same time is accompanied by the compression in the ND that leads to the formation of compression texture near {533}, as it showed on IPF ND (Figure 3(d)).Formation of this texture during the compression may be realized due to the primary and cross slip of dislocations on systems {110} ⟨110⟩ [7].
The tensile strain by 10% at the strain rate of 120 mm/min concentrates the pole density on the IPF (RD) mainly near the poles ⟨320⟩ and ⟨110⟩ (Figure 1(e)).The areas of increased pole density are concentrated near the ⟨211⟩ and ⟨321⟩ on the IPF (ND) also.An area of high pole density (∼13) is formed near the ⟨111⟩ direction with scattering to ⟨221⟩ on the OPF (TD) in this case.Comparing the pole density distribution on IPF (Figure 1(e)) can conclude that in sheets the limited axial texture of between ≈ {112} ⟨110⟩ and {123} ⟨210⟩is formed with axis ⟨111⟩ parallel to the TD when a tensile rate is 120 mm/min.Similar texture may be formed in the bcc metals during the tensile due to the activation of the primary slip system {110} ⟨111⟩ with followed slip in coplanar planes [7] and due to sliding on the primary systems during the compression of sample in the ND [7] or in the process of tensile in the RD.
The tensile strain of 20% at the strain rate 120 mm/min (Figure 2(e)) forms the texture similar to that which is formed by means of tensile strain of 10% at strain rate 1 mm/min (Figure 1(c)).
The texture formed at the elongation of 30% at the rate of 120 mm/min (Figure 3(e)) is similar to the texture at the elongation rate of 20% with 0.1 mm/min (Figure 2(b)).
The further increasing of the strain rate up to 300 mm/min by means of tensile to 10% results in a certain weakening of the texture (Figure 1(f)).The maximal pole density ⟨110⟩ on the IPF (RD) decreases to ∼12.A maximum near pole of ⟨210⟩ decreases to 10. IPF (ND) is characterized by a wide scatter of increased pole density.There are peaks of ∼6 near ⟨332⟩ and ⟨110⟩, as well as the maxima of ∼5 near the poles ⟨112⟩, ⟨321⟩, and ⟨135⟩.There is also scatter of pole density from the maximal value of 14 in the pole ⟨111⟩ to the level of ∼10 close to ⟨533⟩ pole on the IPF (TD).This argues that grains rotate around TD during the tensile.Thus, the texture that is formed at a tensile rate of 300 mm/min by 10% may be described as a set of orientations {011} ⟨110⟩, {332} ⟨110⟩, {321} ⟨121⟩, {112} ⟨110⟩, and {135} ⟨211⟩.A similar trend with a tensile speed of 300 mm/min by 20 and 30% (Figures 2(f) and 3(f)) is observed.
Texture scattering in the wide range of orientations may testify to the realization of noncrystallographic mechanisms of plastic deformation by means of slipping of disordered intergrain boundaries due to difficulty of intragrain slip processes.The effect of texture scattering with increasing strain rate was observed in [6] after tensile tests of aluminum alloy.
Thus, the texture analysis demonstrates that increasing the rate of deformation by uniaxial tensile to the 120 mm/min changes the initial texture.There are formed limited axial textures by activating crystallographic deformation mechanisms.At the same time there is observed certain regularity of influence of degree and strain rate on the texture formation.Particularly, the texture that formed during the tensile by 10% at a rate of 0.1 mm/min (Figure 1(b)) is being formed again, but at an elongation of 20% at a rate of 60 mm/min (Figure 2(d)).The texture, which is produced during the tensile strain by 30% at a strain rate of 120 mm/min (Figure 3(e)), is similar to texture at an elongation by 20% at the strain rate 0.1 mm/min (Figure 2(b)), as is described above.In other words, the small tensile strains at a low strain rate are more favorable to the formation of one or another texture.
The further increasing of strain rate activates the noncrystallographic mechanisms of plastic deformation associated with the intergranular slipping due to the difficulty of crystallographic slip processes.
The above described texture transformations naturally are associated with changes of the mechanical properties, which are presented in Table 1.The anisotropy of the yield strength is observed.Meaning of yield strength in TD ( 0.2 TD) exceeds its value in the RD ( 0.2 RD).This behavior of the yield stress is caused by crystallographic texture of specimens.
The crystal axes ⟨111⟩ and ⟨110⟩ are orientated in the TD and the RD, accordingly (Figure 1).The crystals with the orientations of ⟨111⟩ are more resistant to the strain than crystals with the orientations ⟨110⟩ [11].
It is usually assumed that the greater effect of hardening fits to the higher strain rate [1,2].In the first approximation, we can estimate the hardening using the hardening coefficient , which is the ratio of metal yield strength after hardening to the yield point before hardening [11].The hardening coefficient in RD ( RD ) and in TD ( TD ) does not change monotonically (see Table 1).
With increasing of deformation rate the values of  increase and reach a maximum at the tensile rate of 120 mm/min.At this stage, the textures that are represented by means of limited axial orientations of the axes ⟨110⟩ and ⟨210⟩ parallel to the RD and limited axial texture with the axis ⟨111⟩ parallel to the TD (Figure 1(e)) are getting the most sharp.
The increasing strain rate up to 300 mm/min decreases the hardening coefficient, as well as texture sharpness (Figure 1(f)).
The anisotropy of the tensile strength ( ts ) is expressed considerably weaker than of yield strength ( 0.2 ) and shows the opposite character: tensile strength in the TD ( ts TD) greater than tensile strength in the RD ( ts RD), likely, due to the structural texture, which is characterized by elongation of the grains predominantly in the RD (Figure 2).
The ability of a steel sheet to the deep drawing is expressed by the ratio of yield strength to the tensile strength ( 0.2 / ts ) (recommended 0.55-0.66[12,13]).The values of  0.2 / ts in Table 1 are beyond the scope of that at deformation rates of 60 and 120 mm/min.It indicates that after these deformation rates the ability of studied sheets to the deep drawing deteriorates.Elongation at break shows a trend opposite to the strength properties (see Table 1).
The coefficient of normal plastic anisotropy  10% has a value greater than 1.25 (see Table 1) that is recommended for deep drawing, when undesirable thinning of the sheet takes place [14].
At the same time,  10% changes in a complicated manner depending on the deformation rate (see Table 1).At a minimum tensile rate in the RD of 0.1 mm/min  10% RD is greater than its value at tension in the TD ( 10% TD).There is a maximum of  10% RD and minimum of  10% TD if a tensile rate is equal to 60 mm/min.If the strain rate is equal to 120 mm/min  10% RD and  10% TD are of minimum and maximum values, respectively.
There is the significant linear correlation between the averaged arithmetic values of the coefficient of normal plastic anisotropy (in last column of Table 1) on the one hand and the averaged values of maximal pole density in the IPF (RD) and IPF (TD) on the other hand.The corresponding regression equation is of the form  = 0.41 − 3.23, where a value of  denotes the averaged arithmetic magnitude of the coefficient of normal plastic anisotropy  10% av. and  denotes the arithmetic mean of the maximal pole density in the IPF (RD) and IPF (TD).The reliability coefficient of approximation  2 is 0.81.

Conclusion
The tests of uniaxial tensile by 10, 20, and 30% at strain rates of 0.1, 1, 60, 120, and 300 mm/min in the rolling direction and the transverse direction of recrystallized cold-rolled specimens of low-carbon steel were carried out.
Texture of initial sheet is mainly represented via superposition of residues rolling texture {112} ⟨110⟩ and recrystallization texture of mild steel that is close to the {111} ⟨110⟩.
Tensile strain by 10 and 20% at the strain rates of 0.1 mm/min and 60 mm/min leads to the formation in a steel sheet of axial texture with the axis ⟨110⟩ parallel to the rolling direction.Increase of the tensile strain at such conditions promotes the production of a planar texture of type {112} ⟨111⟩.
The tensile strain by 10 and 20% at the strain rate of 1 mm/min in a sheet leads to the formation of limited axial texture between ≈ {335} ⟨110⟩ and {355} ⟨110⟩ with axis ⟨110⟩ parallel to the rolling direction.Tensile strain by 30% at the strain rate of 1 mm/min promotes to the formation of the planar texture.
Tensile strain by 10% at the strain rate of 60 mm/min leads to formation in the steel sheet of limited axial texture between ≈ {112} ⟨110⟩ and {123} ⟨320⟩ with the axis of ⟨111⟩ being parallel to the transverse direction.Increasing of the degree strain during this helps to activate twinning.
If the tensile strain is 20% at strain rate 120 mm/min, a texture is formed similar to texture that was formed via tensile strain by 10% at the strain rate of 1 mm/min.Texture of tensile by 30% at rate of 120 mm/min is similar to the texture of tensile by 20% at a rate of 0.1 mm/min.
It is observed that the small tensile strains at a low rate are more favorable to the formation of one or another texture.
The plastic deformation occurs as a result of activation of intragranular crystallographic slip on the systems {110} ⟨111⟩ and by twinning on the conjugate planes {112} at the strain rates up to 120 mm/min inclusive.
Intragranular slip becomes difficult and grain boundary sliding is activated, when a strain rate is of 300 mm/min.
The increase of the strain rate from 0.1 to 120 mm/min promotes to the increasing of hardening coefficient, yield stress, tensile strength, and their anisotropy.Percentage elongation at this shows the opposite trend.
If the strain rate is 300 mm/min, then is observed a blur of texture, reduction of coefficient hardening and anisotropy of echanical properties.At the same time tensile strength continues to increase and its value in the rolling direction is getting greater than its value in the transverse direction.
The significant linear correlation between the arithmetic mean of values coefficient of normal plastic anisotropy on the one hand and of the averaged maximal values of the pole density in the IPF (RD) and IPF (TD) on the other hand is found.The reliability coefficient of approximation has the value of 0.81.

Table 1 :
Mechanical properties of the steel at various tensile rates.