Journal of Crystallization Process and Technology, 2013, 3, 163-169
http://dx.doi.org/10.4236/jcpt.2013.34025 Published Online October 2013 (http://www.scirp.org/journal/jcpt)
163
Recrystallization Kin etics and Microstructure Evolution of
Annealed Cold-Drawn Low-Carbon Steel
Nurudeen A. Raji, Oluleke O. Oluwole
Department of Mechanical Engineering, University of Ibadan, Ibadan, Nigeria.
Received July 23rd, 2013; revised August 23rd, 2013; accepted August 30th, 2013
Copyright © 2013 Nurudeen A. Raji, Oluleke O. Oluwole. This is an open access article distributed under the Creative Commons
Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is
properly cited.
ABSTRACT
The recrystallization behavior of cold-drawn 0.12 wt% C steel during annealing at temperatures 600˚C and 650˚C was
investigated. Hardness tests were used to characterize the recrystallization kinetics. The micrographs of the steel were
obtained using optical microscopy (OM) to characterize the grain microstructure of the non-treated and the annealed
steel samples. Annihilation of dislocation defects occur within the soaking time of 5 - 10 minutes for all the deformed
steel after annealing at 650˚C. Specifically at 5 minutes soaking time the grains elongation is still observed indicating
that reformation of grains is not taking place but recovery of the deformed grains. At the 10 minutes annealing time,
new grains are observed to begin and full recrystallization is achieved at 15 minutes annealing time. At annealing time
between 20 - 25 minutes, grains coarsening are observed indicating the onset of grain growth. The hardness of the ma-
terial reduces with increasing annealing temperature for all the degree of cold drawn deformation. On the basis of the
experimentally obtained hardness values, recrystallization increases with increasing degree of cold drawn deformation
for the annealed steel. Recovery process was found to prolong in the 20% cold drawn steel as compared to the 55% cold
drawn steel. The prolong recovery process is due to reduction in the driving force. Full recrystallization of the annealed
steel is achieved at different soaking time depending on the degree of the cold drawn steel.
Keywords: Drawn Steel; Recovery; Recrystallization; Microstructure; Hardness; Soaking Time
1. Introduction
Drawn steel is products of metal drawing process which
include bar or rod drawing, tube drawing and wire draw-
ing. This drawing process has been widely used to ma-
nufacture fine wires, tension loaded structural compo-
nents, springs, paper clips, spokes for wheels and plain
nails [1,2]. The wire drawing process reduces the cross-
section of a wire by pulling it through series of drawing
dies of decreasing diameter to produce wires of desired
diameters. It is mostly performed at room temperature
and thus is classified as cold-work process. The original
metal usually consists of strain-free crystal grains [3].
When the metal is deformed by cold drawing, dislocation
and other imperfections such as vacancies are introduced
into the crystal structure generating microstructure het-
erogeneities that exhibit large orientation gradient [4].
The grains then acquire a preferred orientation or texture.
The structural changes which occur include the gradual
stretching of the grains in the direction of principal de-
formation and accumulation of dislocation and some
other defects [5]. The accumulation and migration of the
dislocation due to the cold drawing process results in
strain hardening of the steel allowing for increase in its
tensile strength with reduced ductility [6]. The degree of
cold-drawn deformation determines whether the steel
will attain a brittle nature or remains ductile [7]. The
strain hardening also known as work hardening is an in-
crement in internal energy associated with an increase in
the dislocation density as well as density in point defects,
such as vacancies and interstitials [8,9]. Some other ef-
fects of such cold work on the properties of polycrystal-
line structures have been studied extensively [10-20].
The individual grain of a polycrystalline material chang-
es relative to the direction of applied stress during the
deformation which is distributed heterogeneously among
the individual grains [21]. A typical feature of such de-
formed structure is anisotropy of mechanical properties.
An initially isotropic material responds by developing
anisotropy when subjected to inelastic deformation. The

Recrystallization Kinetics and Microstructure Evolution of Annealed Cold-Drawn Low-Carbon Steel
164
inelastic induced anisotropy includes directional anisot-
ropy in cold worked metals [22]. These changes in the
mechanical properties of the steel due to the deformation
often influence the performance of the resulting product
of the process in service. In the case of wire drawing pro-
cess for plain nail manufacture, the steel is cold-drawn to
sizes at 20%, 25%, 40%, and 55% for the manufacture of
4 inches, 3 inches, 2.5 inches and 2 inches respectively.
During the drawing operation the carbon steel experi-
ences microstructure changes which affect the mechani-
cal properties of the steel and consequently the perform-
ance of the resulting product in service [23]. The associ-
ated problems include high strain hardening of the steel
due to the degree of plastic deformation which causes
nail brittleness or poor ductility resulting in buckling of
the nail in service. The large amount of internal strain in
the form dislocation as a result of the strain hardening
means that energy is stored in the metal. This energy can
be released through heat treatment, where energy in the
form of heat is introduced into the material allowing the
release of stored energy in the process of recrystallization
[24]. Recrystallization is the reconstruction of the grain
structure during annealing of deformed metals. It causes
a change in the grain structure of the material that has
been previously cold-worked or plastically deformed.
The recrystallization process tends to eliminate the dis-
locations by means of migration of high-angle grain
boundaries driven by the stored energy of deformation
and a new grain structure in the deformed material
evolved. [25,26]. Thus, new dislocation-free grains are
formed within the recovered structure. The new grains
then grow at the expense of the old deformed grains,
leaving a new structure with low dislocation. The new
structure consumes the old grains, resulting in a new
grain structure with a very or no low dislocation density
[27].
Recrystallization is a function of the amount of strain
induced during deformation as well as the time and tem-
perature of annealing [28]. In this study, the recrystalli-
zation kinetics and the corresponding microstructure evo-
lution in annealed cold-drawn low carbon steel is inves-
tigated according to annealing time by mechanical test
and microstructure characterization. The kinetics of re-
crystallization involves determining the fraction of re-
crystallized grains with annealing time which is used to
describe the evolution of the recrystallized grains with
increasing time of annealing at a particular temperature
[29]. The studies of the recrystallization kinetics have
shown that the mechanical properties of metallic materi-
als could be controlled by the microstructure of the mate-
rial [28,30,31]. The control of the microstructure of the
steel could therefore be used to obtain desired mechanic-
cal properties for the steel. The idea of control of me-
chanical properties in materials through these processing
techniques has been studied [32].
Recrystallization is a thermally activated process, con-
sisting of the generation of strain-free grains and their
growth at the expense of the deformed grains until the
deform grain is entirely consumed [28]. And the driving
force for recrystallization is the energy stored in the ma-
terial during deformation [33]. The purpose of recrystal-
lization is to refine the grains for improved properties
and important mechanical properties can be restored after
annealing of cold deformed steel allowing for further de-
formation.
The generally accepted empirical model used to de-
scribe recrystallization kinetics is the Johnson-Mehl-Avra-
mi-Kolmogorov (JMAK) expressed [28,30,33] as:
1exp n
v
X
kt

 

where v
X
the volume recrystallized, k is the JMAK
variable which is temperature dependent and n is the
JMAK exponent and t is the annealing time.
The model was developed on the assumption that the
recrystallized nuclei form randomly in the cold-worked
microstructure and that the growth of the nuclei is iso-
tropic but real materials do not exhibit this behavior be-
cause of the non-uniform distribution of the stored en-
ergy, non-random distribution of the nuclei and anisot-
ropic growth of recrystallized nuclei [34]. It is therefore
of importance to consider real situation of the recrystal-
lization process through experimentation as input for a
realistic model.
This paper considered the use of the micro hardness
property of the annealed cold drawn low carbon steel at
different temperature and soaking time to investigate the
recrystallization process for desired mechanical proper-
ties.
2. Materials and Methods
The low carbon steel used for this study is obtained from
Nigeria Wire Industry Ltd, Ikeja, Nigeria. The average
chemical composition for the steel is as given in Table 1.
Samples of wire cold-drawn by 25% and 40% degree of
deformation were obtained. A Muffle furnace, Gallen-
komp® model SVL-1009 with voltage regulation of 220
V, 50 Hz of temperature range 300˚C ~ 1000˚C obtained
in the materials test laboratory of Igbinedion University,
Okada was used to annealed the steel at 650˚C and
700˚C for time interval ranging from 5 minutes to 60
minutes.
Table 1. Chemical composition of the as-received steel wire
material (wt%).
C Si Mn P Fe
0.12 0.18 0.14 0.7 98.86

Recrystallization Kinetics and Microstructure Evolution of Annealed Cold-Drawn Low-Carbon Steel
165
The samples for evaluation of the microstructures by
optical microscopy (OM) were cut from the annealed
wire, and taken through a grinding process on silicon
carbide paper, 240, 320, 400, and 600 grit. The samples
were then polished initially at 1μm and finally at 0.5 μm
using emery cloth and silicon carbide solution, etched
with 2% nital and the metallography was carried out us-
ing the optical microscope (OM) with image capturing
device. The hardness test was done on a Brinnel tester. In
preparation for hardness measurements, scaling on the
surface of each of the annealed specimens was removed
in the area where the test was to be conducted. A wire
brush was used to remove the surface scaling. Each speci-
men for the hardness test was filed to create flat surface
on the nail shank. The flat surface was then polished with
emery paper to obtain very smooth surface required of
the test. The Brinnell test for this experiment employed a
1-mm diameter carbide ball which was pressed onto the
specimen by a 1750-g load that was maintained for 10
seconds. The diameter of the indenter impression was
measured with the Brinnel reading microscope of magni-
fication 20× and the measurement converted to the Bri-
nell-Hardness Number on the Brinnel tester conversion
table.
The recrystallization fraction is determined based on
the hardness measurement using Expression (1) [33].

initial
initial final
BHNBHN t
BHN BHN
v
X  (1)
where initial BHN the hardness of the deformed sample,
final
BHN is the hardness of the fully recrystallized sam-
ple and

BHN t is the hardness after a given soaking
time.
3. Results and Discussion
3.1. Microstructure Evolution
Figures 1(a)-(f) show the microstructure evolution of the
25% cold-drawn low-carbon steel and as annealed at
650˚C for annealing time range of 5 - 20 minutes. The
microstructure of the cold-drawn steel shown in Figure
1(a) non-treated is inhomogeneous with accumulating
dislocation density concentrated at the grain boundaries
as indicated by the large area of dark patterns of the
structure. After annealing the drawn steel at 650˚C for a
soaking time of 5 - 10 minutes, annihilation of the dislo-
cation is observed with most of the dark patterns clearing
off the structure. Specifically at 5 minutes soaking time
as shown in Figure 1(b), the grains elongation is still
observed indicating that reformation of grains is not tak-
ing place but recovery of the deformed grains which in-
volves movement of low-angle grain boundaries. At the
10 minutes annealing time, new grains are observed to
begin to form as shown in Figure 1(c) and full recrystal-
lization is achieved at 15 minutes annealing time as
shown in Figure 1(d). At annealing time between 20 - 25
minutes, grains coarsening are observed indicating the
onset of grain growth. This is usually avoided in-order to
keep the required strength of the material.
3.2. Material Hardness
Figures 2-5 show the steel hardness measured from the
Brinnel hardness test as a function of the soaking time at
different annealing temperature for the 20%, 25%, 40%
and 55% cold drawn steel respectively. It is observed that
recrystallization could be said to start after 600 seconds
at all the applied annealing temperatures. The hardness of
(a) (b) (c)
(d) (e) (f)
Figure 1. (a) As-received cold-drawn at 25%; (b) annealing time of 5 min; (c) annealing time of 10 min; (d) annealing time of
15 min; (e) annealing time of 20 min; (f) annealing time of 25 min.

Recrystallization Kinetics and Microstructure Evolution of Annealed Cold-Drawn Low-Carbon Steel
166
190
195
200
205
210
215
220
225
230
235
01000 2000 3000 4000
BHN
Soakingtime(sec.)
Annealed20%col ddrawn
500deg.C
550deg.C
600deg.C
650deg.C
700deg.C
Figure 2. Influence of soaking time on hardness of annealed 20% cold drawn 0.12 wt% C steel.
180
200
220
240
260
280
300
01000 2000 3000 4000
BHN
Soakingtime(sec.)
Annealed25%colddrawn
500de g.C
550de g.C
600de g.C
650de g.C
700de g.C
Figure 3. Influence of soaking time on hardness of annealed 25% cold drawn 0.12 wt% C steel.
200
220
240
260
280
300
320
340
01000 2000 3000 4000
BHN
Soakingtime9sec.)
Annealed40%colddrawn
500deg.C
550deg.C
600deg.C
650deg.C
700deg.C
Figure 4. Influence of soaking time on hardness of annealed 40% cold drawn 0.12 wt% C steel.
200
220
240
260
280
300
320
340
360
01000 2000 3000 4000
BHN
Soakingtime(sec. )
Annealed55% col d drawn
500deg.C
550deg.C
600deg.C
650deg.C
700deg.C
Figure 5. Influence of soaking time on hardness of annealed 55% cold drawn 0.12 wt% C steel.

Recrystallization Kinetics and Microstructure Evolution of Annealed Cold-Drawn Low-Carbon Steel
167
the material reduces with increasing annealing tempera-
ture for all the degree of cold deformation. This implies
that rate of recrystallization increases with increasing
annealing temperature.
3.3. Recrystallization Kinetics
The evolution of the recrystallization was measured by
the Brinnel hardness during the annealing at 600˚C and
650˚C. Table 2 shows the hardness values of the steel.
The maximum and minimum hardness values were
measured from the hardness test such that the maximum
hardness correspond to the hardness of the material at
time of zero seconds which is the hardness of the de-
formed material without annealing and the minimum
hardness correspond to the hardness of the fully recrys-
tallized grain.
The relationship between the recrystallization kinetics
and soaking time showing the influence of the degree of
cold drawn deformation are shown in Figures 6 and 7 for
the 20%, 25%, 40% and 55% degree of cold drawing
annealed at temperatures of 600˚C and 650˚C. The fig-
ures show truncated sigmoidal shape lacking the small
slope region which usually describe the nucleation period
of recrystallization. This could be explain that the lack of
the clear nucleation region of the curves is as a result of
prolonging recovery process which tends to reduce the
driving force required for nucleation at lower soaking
time. The extent of recovery decreases with increasing
degree of cold drawn deformation. The prolonged recov-
ery process in the 20% and 25% cold drawn steel could
be as a result of reduction in the driving force required
for nucleation at lower soaking time. It is also observed
that the rate of recrystallization increases with increasing
degree of cold drawn deformation. This means that re-
covery process is faster in the highly cold drawn steel.
The influence of recovery is to cause the recrystallizing
grain growth rate to decrease continuously during recrys-
tallization. The figures show that full recrystallization of
the grains commenced at different soaking time for the
cold drawn steel depending on the degree of cold drawn
deformation.
4. Conclusion
The microstructure evolution of cold drawn 0.12 wt% C
steel has been analyzed. The accumulated dislocation due
to cold drawing deformation of the steel annihilate after
annealing the drawn steel at 650˚C for a soaking time of
5 - 10 minutes, annihilation of the dislocation is observed
with most of the dark patterns clearing off the structure.
At lower soaking time, recovery of the deformed grains
is pronounced. Recrystallization of the grains com-
menced after annealing for soaking time of 10 minutes.
At annealing time between 20 - 25 minutes, grains coars-
ening are observed indicating the onset of grain growth.
The hardness of the material reduces with increasing
annealing temperature for all the degree of cold deforma-
tion indicating increasing recrystallization with increase-
ing annealing temperature. The kinetics of recrystalliza-
tion has been described with the hardness test values for
cold drawn 0.12 wt% C steel annealed at 600˚C and
Table 2. Initial and recrystallized values for hardness of
cold drawn 0.12 wt% C steel.
%
Deformation BHNinitial
BHNfinal
(annealed at 600˚C)
BHNfinal
(annealed at 650˚C)
20 230 201.2 197.91
25 281.65248.3 221
40 315.67257.7 234.6
55 336 296 248
0.7
0.75
0.8
0.85
0.9
0.95
1
1.05
01000 2000 3000 4000
Fr actionr ecrystallized
soakingtime,sec.
20%colddrawn
25%colddrawn
40%colddrawn
55%colddrawn
Figure 6. Recrystallization kinetics of cold drawn 0.12 wt% C steel annealed at 600 deg. C.

Recrystallization Kinetics and Microstructure Evolution of Annealed Cold-Drawn Low-Carbon Steel
168
0.7
0.75
0.8
0.85
0.9
0.95
1
1.05
01000 2000 3000 4000
Fractionr ecrystallized
soakingtime,sec.
20%colddrawn
25%colddrawn
40%colddrawn
55%colddrawn
Figure 7. Recrystallization kinetics of cold drawn 0.12 wt% C steel annealed at 650 deg. C.
650˚C. The recrystallization kinetic is characterized by
prolonged recovery at lower soaking time and rate of
recrystallization increases with increasing degree of cold
drawn deformation. Full recrystallization is achieved faster
in the highly deformed steel.
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