WARM PROCESSING FOR CUBE TEXTURE IN PURE IRON.pptx

CUBE TEXTURE DURING WARM
THERMAL PROCESSING IN PURE
IRON
GERUGANTI SUDHAKAR
PHD(MATERIALS ENGINEERING),H.C.U

DEVELOPMENT OF CUBE TEXTURE DURING WARM
THERMAL PROCESSING IN PURE IRON
A novel warm rolling method is conjectured for controlling orientation of
crystals in body-centred cubic iron. Cube faces of the bcc crystals are aligned
with the rolling surface(RD) of the polycrystalline iron sheet sample. The
magnetizing current required is a function of crystal orientation-being lower
when the flux path coincides with the direction along the cube edge. Such a
texture has been a long-standing aim for research and is advantageous in terms
of good magnetic properties.The technique (aims to)control the favourable
texture orientation as the cube faces are elastically compliant with
minimization of strain energy. The new warm rolling process envisages a
dramatic enhancement in the magnetic ﬂux density and curtailing iron losses.

1.Microstructural and textural development in
an extra low carbon steel during warm rolling
2. Effects of hot and warm rolling on
microstructure, texture and properties of low
carbon steel
3. Development of Through-Thickness Cube
Recrystallization Texture in Non-oriented
Electrical Steels by Optimizing Nucleation
Environment
4. Effect of strain and deformation mode on
cube texture formation in warm bi-axial rolled
low-carbon steel
5. Micro-Structure and Texture of a Warm
Rolled IF Steel
6. Two-stage warm cross rolling and its effect
on the micro-structure,texture and magnetic
properties of an fe-6.5 wt%Si non-oriented
electrical steel
LITERATURE REVIEW:

REFERENCE PAPER : Microstructural and textural development in an extra low carbon steel
during warm rolling
CHEMICAL COMPOSITION
AND
SALIENT FEATURE
WARM ROLING TEMPERATURE,
STRAIN RATE,
DEFORMATION PERCENTAGE,MICRO-
STRUCTURE
TEXTURE
Steel ELC(Extra Low Carbon)
C:0.007%
Mn:0.11%
S:0.010%
P:0.010%
Si:0.003%
Al:0.043%
O2:12ppm
N2:50ppm
CCT(Continous Cooling
Curves)
800°C~500°C Deformation Percentage: 80%

1. completely recrystallized ferrite grains of almost polygonal
shape are obtained after rolling at the high temperature of
800 °C.
2. At 700 °C the microstructure shows recrystallized areas,
pancake shaped grains and dark patches of deformation
bands indicating incomplete recrystallization
3. deformed and elongated ferrite grains with profusion of
deformation bands are obtained at lower rolling temperatures
(600 and 500 °C);
Texture
The most relevant features of the crystallographic texture of the
four samples are displayed in the appropriate ϕ2 = 45◦ sections
of their ODFs. For the 600 and 500 ◦C rolled samples a highly
uniform and strong fibre, as well as a fibre running from
ϕ1=0◦–90◦ in 2 sections are clearly visible. This is also evident
from the fibre plots for these samples . By contrast, the 800
and 700 ◦C rolled samples show only very weak texture
development. The main component of the texture in both the
cases is the rotated cube {001} 110. The above features are also
indicated in the relevant fibre plots of these samples.

REFERENCE PAPER:Effects of Hot and Warm Rolling on Micro-Structure,Texture and Properties of Low Carbon Steel
CHEMICAL
COMPOSITION
WARM
ROLLING
TEMPERATURE
SALIENT
FEATURE
MICRO-STRUCTURE TEXTURE
Grade LC:
C:0.04%
Si:0.02%
Mn:0.02%
S:0.009%
P:0.015%
Al:0.043%
N:0.005%
700-1100°C MEAN FLOW
STRESS
[MFS
VS 1000/T]

SCHEMA FOR HOT ROLLING AND COLD ROLLING
Cooling Rate: 50 deg/hr Cold Rolling reduction: 20%
Heating rate:
250 deg/hr
Skin pass reduction : 2%
Hot Rolling Reduction: 30%
1. 1070 (soaking and homogenization)
790 deg C (Hot Rolling Temperature)
700 deg C (Annealing Temperature)
(Cold Rolling Room Temperature)
(Skin Pass: Room Temperature)
REF:Texture Control During Manufacturing of Non-Oriented
Electrical Steels

Homogenisation 1100 deg C
HotRolling 950 deg C : 60% reduction
Cold Rolling : 72% reduction Cold Rolling : 23% reduction
Annealing 650 deg C : 35 sec
Annealing 900 deg C : 3 min
TEMPERATURE
ALONG Y-AXIS
TIME ALONG X-AXIS
REF:Texture Control During Manufacturing of Non-
Oriented Electrical Steels

INITIAL SIZE OF SPECIMEN: 7mm
SINGLE – STAGE HOT ROLLING:
I) HOT WORKING REDUCTION (60%):
7 * 0.60 = 4.2mm
FINAL SIZE AFTER HOT WORKING REDUCTION :
7 – 4.2=2.8mm
II) TWO – STAGE COLD ROLLING:
i) Ist STAGE COLD WORKING REDUCTION (72%):
2.8 * 0.72 = 2.016mm
FINAL SIZE AFTER Ist STAGE COLD WORKING REDUCTION:
2.8 – 2.016 = 0.784mm
ii) IInd STAGE COLD WORKING REDUCTION (23%):
0.784* 0.23 = 0.18032mm
FINAL SIZE AFTER IInd STAGE COLD WORKING REDUCTION:
0.784 – 0.18032 = 0.603mm
REF:Texture Control During Manufacturing of Non-
Oriented Electrical Steels
SAMPLE SAMPLE
1
SAMPLE 2 SAMPLE 3
WEIGHT(gms) 42.115 48.581 40.198
THICKNESS(mm) 7.01 7.28 6.93
LENGTH(mm) 31.56 32.37 32.28
BREADTH 27.10 30.57 23.66

Effect of Annealing Prior to Cold Rolling
on the Microstructure Evolution and
Energy Losses of Low-Si, Ultra-Low-C
Hot-Rolled Electrical Steel

1100 deg C (soaking and
homogenization:9 hrs)
Heating rate:
900 deg/hr
Cooling rate: 90 deg/hr
A
1032
1020
1000
972
942
928
710
800
Annealing:16.66min Final Annea
10
5
HOT WORKING (AUSTENITE REGION)
HOT WORKING (FERRITE REGION)
-058%
-0.5%
-052%
-0.38%
-0.34%
-0.23%
(4-HIGH REVERSIBLE MILL)
(6 STAND CONTINUOUS MILL)
COLD WORKING:65-92% r
Reference Paper: Effect of Annealing Prior to Cold Rolling
on the Microstructure Evolution and Energy Losses of
Low-Si, Ultra-Low-C Hot-Rolled Electrical Steel

TEMPERATURE °C
TIME hrs
Soaking and Homogenisation (1250°C for 2 min)
Hot Rolling Temperature: 850°C
Hot Rolling Reduction: 20%
20 °C/s 650 °C for 1 h
Cold Rolling Reduction: 70%
AnnealingTemperature: 860°C;3 min
20 °C/s
4-high rolling mill
Air Cooled to Ambient Tempera
2.1 mm-thick NOES (Fe–0.006C–0.71Si–0.21Mn–0.44Al (wt%))
i)Thickness after Hot Rolling Reduction: 1.68mm
Thickness after Cold Rolling Reduction:0.5mm
Hot Rolled Micro-Structure Cold Rolled Micro-Structure
Finally Annealed Cold Rolled Micro
REF:.Effects of hot rolled microstructure after twin-roll casting
on microstructure, texture and magnetic properties of low silicon
non-oriented(electricalsteel).

TEMPERATURE °C
TIME hrs
(Sieq=Si%+2[Al%]−0.50[Mn%]+2.92[P%])
Thickness after 2 mm
Initial thickness of 30 mm
AnnealingTemperature: 860°C;3 min
Air Cooled to Ambient Temperature
Cold Rolling Reduction: 70%
Final Thickness 0.6mm
REF:Texture evolution of experimental silicon steel grades.
Part I: Hot rolling

REFERENCE PAPER :Development of Through-Thickness Cube
Recrystallization Texture in Non- oriented Electrical Steels by
Optimizing Nucleation Environment
CHEMICAL
COMPOSITION
WARM ROLLING
TEMPERATURE
MICRO-STRUCTURE TEXTURE
0.01 wt pct C,
2.1 wt pct Si,
0.2 wt pct Mn,
0.002 wt pct Al,
0.004 wt pct S,
0.017 wt pct P,
and balance Fe
400 to 600 °C

REFERENCE PAPER: Effect of strain and deformation mode on cube texture formation in warm bi-axial rolled low-carbon steel
CHEMICAL
COMPOSITION
WARM
ROLLING
TEMPERATURE
WITH
NUMBER OF
PASSES WITH
REDUCTION
SCHEMATIC BI-AXIAL ROLLING
PROCESS,CROSS-SECTIONAL SHAPE
INITIAL AND 24 PASS ROLL
BARS,ORIENTAL MAPS ALONG ROLLING
DIRECTION AND NORMAL DIRECTION
TEXTURE[ ORIENTAL DISTRIBUTION FUNCTION
AT Ø =45; [001] POLE FIGURES AT THE
CENTRE,QUARTER,SURFACE IN 24 PASS ROLL
BARS]
(0.15C-0.3Si-
1.5Mn)
823 K
24-pass warm
bi-axial rolling
(WBR)
approximately
88% reduction
(40mm-13mm)

REFERENCE: Micro-Structure and Texture of a Warm Rolled IF Steel
CHEMICAL
COMPOSITION
OF INTERSTIAL
FREE(IF) STEEL
% OF SHEAR
BANDS AS A
FUNTION OF
ROLLING
REDUCTION
AND
DEFORMATIO
N
TEMPERATURE
MICRO-STRUCTURE
(SPECIMENS ROLLED AT
400C and 600C)
TEXTURE
[0DF of the 40% REDUCED SAMPLES AT:
(a) 400C, (b) 600C;
CONTOUR VALUES UNDER FIGURES]
C:0.003
Al:0.052
TI:0.075
Mn:0.18
Ni:0.006
P:0.017

REFERENCE PAPER:TEXTURE DEVELOPMENT IN EXTRA LOW CARBON (ELC) AND INTERSTITIAL FREE (IF) STEELS
DURING WARM ROLLING
CHEMICAL COMPOSITION WARM
ROLLING
TEMPERATURE
SALIENT
FEATURE AND
MICRO-
STRUCTURE
TEXTURE COMPARION OF
THREE STEELS AFTER
SINGLE PASS
RROLLING
ELC Steel Nb-IF Ti-IF
C 0.007 0.003 0.003
Mn 0.011 0.10 0.11
S 0.010 0.010 0.009
P 0.010 0.012 0.012
Si 0.003 0.008 0.008
Al 0.043 0.044 0.050
Ti --- 0.020 0.054
Nb --- 0.037 0.014
500-800°C Dislocation
Bands and
Dislocation
densities

REFERENCE PAPER:Secondary Recrystallization of Grains with Cube Orientation for Pure Iron Tape
CHEMICAL COMPOSITION COLD ROLLING
REDUCTIONS
AND
ANNEALING
TEMPERATURES
SALIENT
FEATURE
AND MICRO-
STRUCTURE
TEXTURE COPARI
ON OF
THREE
STEELS
AFTER
SINGLE
PASS
RROLLI
NG
Pure iron:
C <0.0020
P <0.0005
S <0.0005
Si <0.0005
Mn <0.0005
Cu <0.0005
O <0.0005
N <0.0010
H <0.0005
15% for first
rolling, 75%
for second
rolling and
92% for third
rolling, which
was final
rolling. The
annealings
The grain with
cube
orientation for
secondary
recrystallizatio
n grows in a
vacuum
atmosphere
according to
the following
the growth

MICROSTRUCTURAL DEVELOPMENT DURING WARM
ROLLING OF AN IF STEEL
warm working in the temperature range 500~800°C. Mean
flow stress-strain curves calculated from load-time data of
rolling tests reasonably correspond to work hardening and
dynamic recovery behaviour.
Microbands in directions of + 35” with respect to the rolling
direction, independent of strain, temperature and initial grain
orientations are the most noticeable features in the
microstructural observations.

Reference Paper: Cube Texture Formed in Biaxially Rolled Low-Carbon Steel
Cube texture could be obtained in low-carbon steels by
annealing the warm-rolled samples, where
the intensified α-fiber and γ-fiber warm-rolling texture is
changed to the {100}<uvw> orientations.
In order to obtain a developed cube texture in low-
carbon steels biaxial warm-rolling, i.e. on the
normal direction (ND) and transverse direction (TD) of a
bar-shaped sample alternatively, is tried in
the present work. It is considered that the biaxial rolling
will cause an orientation equivalence
between ND and TD directions, the {100}<011>
component in the warm-rolled and annealed
{100}<uvw> texture may become unstable due to the
alternative rolling on the {100} and {110}
planes in ND and TD directions, respectively. In contrast,
the cube texture should be stabilized since
its orientation equivalence in both ND and TD.

REFERENCE PAPER: Cube Texture Formed in Biaxially Rolled Low-Carbon Steel
CHEMICAL
COMPOSITION
WARM ROLLING
TEMPERATURE;
ROLLINGSPEED,
REDUCTION,
PERCENTAGE
DEFORMATION,
ROLLING PASSES
SALIENT
FEATURE
MICRO-STRUCTURE AND TALYOR FACTOR TEXTURE
low-carbon
steel :
0.16 C
0.37 Si
1.39 Mn
723K and 923K
90.5%
30
the biaxial
rolling will
cause an
orientation
equivalence
between
ND and TD
directions,
the
{100}<011>
component
in the
warm-
rolled and
annealed

REFERENCE: Regulating the recrystallized grain to induce strong cube texture in
oriented silicon steel
CHEMICAL
COMPOSITION
SALIENT
FEATURE
CROSS COLD ROLLING
PROCESS
TEXTURE
[Ø2 450 0DF SECTION SHOWING
TEXTURES]
0.055% C,
3.28%
Si, 0.104% Mn,
0.027% P,
0.0071% S,
0.0284% Al,
0.0078% N.
The strong
cube texture
with ODF
density of
50.73 mrd was
obtained by
cross-rolling
and pulsed
electric current
treatment.

1) 23.849 2) 23.642 3) 22.453 4) 21.52 5) 25.835 gms
The Samples are melted using Vaccum Arc Melting.
Intially first three samples were melted and solidified. Later next two
samples were melted with former solidified product to
form final product.
SAMPLE ‘S with corresponding weights:
Experimental Procedure:
Pure Iron buttons are Melted by Vaccum Induction Melting in protective atmosphere of Argon gas. The resultant Iron conglomerate
is characterized for MicroStructure,XRD,Hardness respectively.

SAMPLE SAMPLE
1
SAMPLE 2 SAMPLE 3
WEIGHT(gms) 42.115 48.581 40.198
THICKNESS(mm) 7.01 7.28 6.93
LENGTH(mm) 31.56 32.37 32.28
BREADTH 27.10 30.57 23.66

1. Sample 1 --- 23.849 gms
2. Sample 2 --- 23.642 gms
3. Sample 3 --- 22.453 gms
4. Sample 4 --- 21.523 gms
5. Sample 5 --- 25.835 gms
______________
Total Wt: 117.302 gms
______________
Measured Target Weight : 115.722 gms
Difference Between Original Raw Material
Weight – Measured Final Weight = 117.302
– 115.722 =1.58 gms.
Thickness of FINAL IRON CONGLOMERATE :
6mm

CHARACTERISATION BY XRD : X-RAY DIFFRACTION TECHNIQUE

VICKER’S
HARDNESS(2
00gms)
HARDNESS
OBSERVED
AVERAGE STANDA
RD
DEVIATI
ON
1 207.3 111.8 50.4
2 77.1
3 164.5
4 69.9
5 152.2
6 41.6
7 74.6
8 113.8
9 1.5.2
10 101.9
INDENTATION
POINTS
(EIGHT)
VICKERS
HARDNESS
(LOAD
:200)
AVERAGE :
VH VALUE
STANDARD
DEVIATION
1 130.4 109.3 18.9
2 118.9
3 99.4
4 78.4
5 139.3
6 91.8
7 114.4
8 101.3
CHARACTERISATION OF HARDNESS:
VICKERS HARDNESS TECHNIQUE

Grain Size Distribution
CHARACTERISATION OF MICRO-STRUCTURE :
OPTICAL MICROSCOPY

EXPERIMENTAL PLAN
Iron samples were warm rolled using both single pass and
multipass rolling.
1. Single pass rolling was carried out with wedge shaped
samples. These were soaked at both 830oC and 1150oC for
45 min and then rolled in one pass at the desired FRT of
800, 700, 600, and 500oC. The total amount of rolling
reduction given at each temperature was ,80%.
2. In multipass rolling, the relative amounts of deformation
in the gamma and alpha temperature ranges were varied
according to the following schedules:
(1) ,71% rolling reduction was given in the gamma region
and the resulting material was subjected to a further
,33% reduction in the alpha region;
(2) ,42% in the gamma region and a further ,66.6% in the
alpha region;
(3) 0% rolling reduction in the gamma region and ,80%
reduction in the alpha region.
The bar samples for multipass rolling were soaked at
1150C for 45 min and the FRT used were 800 and 500C.
3. All the warm rolled samples of the three iron samples
were recrystallization annealed in a salt bath furnace at a
temperature of 775C for 25 min. Textures were measured at
mid-thicknesses of samples using the orientation distribution
function (ODF) technique. Finally fiber plots were prepared
from the ODF data.

Warm rolling is often carried out such that the microstructure during the
final finishing passes is composed of more than 90% ferrite. the maximum
warm rolling finishing exit temperature falls around 780˚C

CONCLUSIONS:
After conventional rolling and annealing, it
is rarely able to develop a cube texture in the pure iron
sheets. This is partially because all the thermomechanical
processing steps utilized to produce the final thin sheets,
e.g. hot rolling, warm rolling,cold rolling and annealing, will
ALTER the initial crystallographic texture formed
during the solidification process, and METALLURGICAL
mechanisms that govern the formation of
texture during these processes tend to favor a gamma-
fibre (<111>//ND) and an alpha-fibre (<110>//RD) rolling
direction), not the cube texture, in the final sheets .
FUTURE WORK:
The formation mechanisms of specific textures during
thermomechanical processing are still not completely
understood, especially those during recrystallization and
grain growth. It is thus imperative to
control the operational parameters during material
processing to obtain the desired final texture which should
be future goal.

REFERENCES:-
1. Texture formation in metal alloys with cubic
crystal structures
2.Texture Control During Manufacturing of
Non-Oriented Electrical Steels
3. Effect of strain and deformation mode on
cube texture formation in warm bi-axial rolled
low-carbon steel
4.Effect of Strain Rate on Mechanical
Properties of Pure Iron
5. Cube Texture Formed in Biaxially Rolled
Low-Carbon Steel
6. Distinctive Aspects of the Physical Metallurgy of WarmRolling
7. Effects of Process Parameters on Ferrite Grain Size of
Commercially PureIron
8. Effect of Heating Rate on the Development of AnnealingTexture
in Nonoriented Electrical Steels
9.Efficient Generation of Cube-on-Face Crystallographic Texture
in Iron and its Alloys
10.Production and Properties of Grain-Oriented Commercially
Pure Iron

REFERENCES:-
11.Effect of deformation route and intermediate annealing on
magnetic anisotropy and magnetic properties of a 1 wt% Si
non-oriented elec-trical steel
Ali Sonboli a,b,n, Mohammad Reza Toroghinejad a, Hossein
Edris a, Jerzy A. Szpunar
12. Texture Control During theManufacturing of
Nonoriented Electrical Steels
Leo Kestens1 and Sigrid Jacobs2
13. Effect of Annealing Prior to Cold Rolling on
the Microstructure Evolution and Energy Losses of
Low-Si, Ultra-Low-C Hot-Rolled Electrical Steels
Héctor Ortiz Rangel 1,*, Armando Salinas Rodríguez 1 and
Omar García Rincón 2

ADDITIONAL INFORMATION:
Mostly polycrystalline crystals are not randomly
oriented in space, but rather, their axes are
approximately aligned with the macroscopic
shape of the sample. The non-random
distribution arises because of ori-ented
processing, heat-treatment or phase
transformation. The sample is then said to be
crystallographically textured and exhibits
macroscopically anisotropic properties, which
reflect the orientation distribution. Such
anisotropy can be advantageous.
In ferritic iron, the magnetic flux density rises
most easily along <100>directions, in contrast to
<111>directions which are said to be magnetically
hard.Iron used for electrical transformer core
applications involves rapid changes in magnetic
field therefore iron perform better in terms of
energy loss, permeability as well as magnetic flux
den-sity when the crystals are aligned with
<100>directions par-allel to the sheet normal.
The {100} planes which contain two
perpendicular <001>directions
and no <111>direction are naturally the
planes of easy magnetisation, so a texture
in which these planes are aligned to the
sheet surface with the cube edges parallel
to the sample axes is known as the cube
texture, {100}<001>.
Typi-cal efficiency of motors ranges from 83
to 92%, and their operating efficiency is far
below, 62% The only way to improve motor
efficiency is to reduce motor losses. Loss
components in an induction motor include
core loss in iron cores, the copper loss in
rotors and stators, the stray load loss, and
the friction and windage loss.Among
them,the copper loss and the core loss,
which cover at least 75 %of the overall
losses, can be reduced significantly by
improving magnetic flux density along with
reducing iron loss through the texture
control of core materials.

A texture parameter quantifies the density of
〈100〉 easy magnetic directions in the sheet
planes. An extensive correlation study revealed
relation of this parameter with the hysteresis
losses, determined at an induction of 1.5 T, and
with the induction measured at anapplied
external field of 25 A/cm .
Conventional continuous annealing is applied
on warm-rolled material with a rolling strain
of 70% reduction ata temperature between
700 and 850◦C and with a heatingrate of 2 to
10◦C/s. These large rolling reductions are
neces-sary to obtain the relatively thin gauges
of 0.60 mm orless which are generally
required for the production of softiron core
lamella.
All the factors viz. texture factor,Annealing time and
Temperature,Heating rate,Warm rolling process
parameters can be integrated to evolve the desired micro-
structure and texture. After Warm rolling is carried out,
the following parameters are measured to ascertain the
variation in hysteresis losses and Magnetic Inducation. A
parameter in hexadecimal degree, will help to identify the
cube texture formation. A parameter is lowest for cube
texture
Theoretically lowest value of the A parameter is 22.5 deg.

2. iron has been found useful for magnetic cores where there is
a need for good permeability at high-flux densities
3. The magnetizing current required is a function of crystal
orientation-being lower when the flux path coincides with the
direction along the cube edge
4. A high degree of cube orientation produces an iron material
having unusually low exciting current, high permeability, and
low core loss.
Reference Paper :Production and Properties of Grain-Oriented
Commercially Pure Iron
1. The development of a process for grain orientation in
commercially pure iron could be expected to substantially
improve the magnetic properties, making possible new
applications.
5.Effective inhibition of normal grain growth has been
accomplished by diffusing extra manganese sulfide irihibitors
into the primary grain boundary in a very early stage of the
final anneal
6. dispersed second phase is the result of melting with a proper
amount of secondphase material present and then solution
treating the material in the slab or ingot-heating operation
followed by precipitation during hot rolling
7. Under these conditions, the fine-grained primary structure in
the sheet at final thickness can be consumed by rapidly
growing crystals having the cube-on-edge orientation

WARM PROCESSING FOR CUBE TEXTURE IN PURE IRON.pptx

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