annealing heat treatment.pdf
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austenite again causes a certain volume increase, and in the third tempering stage the
progressive decomposition of martensite leads to the volume decrease.
For high-alloy tool steels (e.g., 210CrW46, curve 3 of Figure 6.49), a stabilization of
austenite is evident, so that the effect of the volume increase (due to austenitebainite or
austenitemartensite transformation) takes place only at higher temperatures. In most cases,
as can be seen from Figure 6.49, a reduction in length, i.e., a volume decrease, can be found
after tempering.
It should be noted that the changes in length shown in Figure 6.49 represent only the order
of magnitude of the expected changes, because the actual value depends in each case on the
specific heat treatment conditions. The austenitizing temperature, which determines the
amount of carbon dissolved and the amount of retained austenite, has a strong influence
on expected volume changes.
6.2 ANNEALING PROCESSES
6.2.1 STRESS-RELIEF ANNEALING
Stress-relief annealing is an annealing process below the transformation temperature Ac1,with subsequent slow cooling, the aim of which is to reduce the internal residual stresses in a
workpiece without intentionally changing its structure and mechanical properties.
Residual stresses in a workpiece may be caused by
1. Thermal factors (e.g., thermal stresses caused by temperature gradients within the
workpiece during heating or cooling)
2. Mechanical factors (e.g., cold-working)
3. Metallurgical factors (e.g., transformation of the microstructure)
In processes that involve heat, residual stresses are usually caused by the simultaneous
existence of thermal and transformational stresses (e.g., during the solidification of liquid
metals, hot forming, hardening, or welding). Thermal stresses are always directly propor-
tional to the existing temperature gradient, which further depends on the cross-sectional size
and on the heating or cooling rate.In workpieces made of steel, for the above reasons, local residual stresses may amount to
between about 10 N/mm2 and values close to the yield strength at room temperature. The
consequences of residual stresses may include
1. Dimensional changes and warpage of the workpiece
2. Formation of macroscopic and microscopic cracks
3. Asymmetric rotation of shafts
4. Impairment of the fatigue strength of engineering components
2
3
4651
Tempering temperature, C
Change
inlength,%
0
1: DIN 105WCr6
2: DIN 40CrMOV21.14
3: DIN 210CrW46
4: DIN X100CrMoV5.15: DIN 50NiCr13
6: DIN 165CrMoV460.15
0.100.05
0
0.05
0.10
0.15
100 200 300 400 500 600
FIGURE 6.49 Change in length of different steels during tempering as a function of tempering tem-
perature. (Designation of steels according to DIN.) (From H.J. Eckstein (Ed.), Technologie der Warme-
behandlung von Stahl, 2nd ed., VEB Deutscher Verlag fur Grundstoffindustrie, Leipzig, 1987.)
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Residual stresses in a workpiece can be reduced only by a plastic deformation in the
microstructure. This requires that the yield strength of the material be lowered below the
value of the residual stresses. The more the yield strength is lowered, the greater the plastic
deformation and correspondingly the greater the possibility or reducing the residual stresses.
The yield strength and the ultimate tensile strength of the steel both decrease with increasing
temperature, as shown in Figure 6.50 for a low-carbon unalloyed steel. Because of this, stress-
relief annealing means a through-heating process at a correspondingly high temperature. For
plain carbon and low-alloy steels this temperature is usually between 450 and 6508C (842 and
12008F), whereas for hot-working tool steels and high-speed steels it is between 600 and
7508C (1112 and 13828F). This treatment will not cause any phase changes, but recrystalliza-
tion may take place. Tools and machine components that are to be subjected to stress-relief
annealing should be left with a machining allowance sufficient to compensate for any warping
resulting from stress relief.
When dealing with hardened and tempered steel, the temperature of stress-relief annealing
should be about 258C (778F) below that used for tempering. If the tempering temperature was
quite low, after stress-relief annealing quite a high level of residual stresses will remain. In
some other cases, for instance with a gray iron, the maximum temperature of the stress-reliefannealing should be limited because of possible strength loss. Therefore gray iron must not be
stress-relief annealed above 5508C (10228F).
In the heat treatment of metals, quenching or rapid cooling is the cause of the greatest
residual stresses. A high level of residual stress is generally to be expected with workpieces that
have a large cross section, are quenched at a high cooling rate, and are made of a steel of low
hardenability. In such a case high-temperature gradients will arise on the one side, and on the
other side structural transformations will occur at different points of the cross section at
different temperatures and different times. In contrast to heat treatment processes with con-
tinuous cooling, processes with IT (e.g., austempering) result in a low level of residual stresses.
To activate plastic deformations, the local residual stresses must be above the yield
strength of the material. Because of this fact, steels that have a high yield strength at elevated
temperatures can withstand higher levels of residual stress than those that have a low yield
strength at elevated temperatures.
A
1000
Yieldstrengthandultimatetensile
strength,
MPa
Elongation,
%
Temperature, C
800
600
400
200
200 100 100 200 300 400 500 600
Rm
sso
ssu
0
0
10
20
30
40
50
0
FIGURE 6.50 Change in some mechanical properties of low-carbon unalloyed steel with increasing
temperature, according to Christen. A, Elongation; Rm, ultimate tensile strength; sso, upper yield
strength; ssu, lower yield strength. (From H.J. Eckstein (Ed.), Technologie der Warmebehandlung von
Stahl, 2nd ed., VEB Deutscher Verlag fur Grundstoffindustrie, Leipzig, 1987.)
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The level of yield strength at elevated temperatures depends on the alloying elements in
the steel. Figure 6.51 shows the increase in yield strength at temperatures of 3005508C (572
10228F) when 0.5% of each element was added to an unalloyed steel. It can be seen from this
diagram that additions of Mo and V are most effective in increasing the yield strength at
elevated temperatures.
To reduce residual stresses in a workpiece by stress-relief annealing, a temperature must
be reached above the temperature corresponding to the yield strength that is adequate to the
maximum of the residual stresses present. In other words, every level of residual stress in a
workpiece corresponds to a yield strength that in turn depends on temperature. In addition to
temperature, soaking time also has an influence on the effect of stress-relief annealing, i.e., onthe reduction of residual stresses, as shown in Figure 6.52.
The relation between temperature and soaking time during stress-relief annealing can be
described by Hollomons parameter:
P T(C log t) (6:33)
where Pis Hollomons parameter (heat treatment processes with the same Hollomon para-
meter value have the same effect), Cis the HollomonJaffe constant, Tis temperature (K),
and t is time (h).
The HollomonJaffe constant can be calculated as
C 21:3 (5:8% carbon) (6:34)
Figure 6.53 shows (according to LarsonMiller method) calculated values of the yield strength
at elevated temperatures (for 0.2% strain) for three grades of alloyed structural steels for
hardening and tempering (designations according to DIN). Using this diagram, the abscissa
ofwhichrepresents theactualHollomonparameterP, knowing thetemperature andtimeof the
stress-relief annealing, one can read off the level of residual stresses that will remain in the
workpiece after this annealing process, i.e., the level up to which the residual stresses will be
reduced by this stress-relief annealing. If, for instance, for DIN 24CrMoV5.5 steel, a
Mo
V
Ti
Cu
Mn
Cr
Ni0
20
40
60
80
100
300 350 400 450 500 550
Temperature, C
120
Increaseoftheyieldstrength
,N/mm2
FIGURE 6.51 Increase in yield strength at elevated temperatures when 0.5% of each alloying element
indicated is added to an unalloyed steel. (From G. Spur and T. Stoferle (Eds.), Handbuch der Fertigung-stechnik, Vol. 4/2, Warmebehandeln, Carl Hanser, Munich, 1987.)
2006 by Taylor & Francis Group, LLC.
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1 h
10 h
10
20
30
40
50
60
70
80
90
100
Reductionofresidualstresses,%
Temperature, C
200 300 400 500 600 700
24 h
48 h
FIGURE 6.52 Effect of soaking time (at different temperatures) of stress-relief annealing on the
reduction of residual stresses for hardening and tempering steels. (From G. Spur and T. Stoferle
(Eds.), Handbuch der Fertigungstechnik, Vol. 4/2, Warmebehandeln, Carl Hanser, Munich, 1987.)
P=T(20+log t)103
Temperature T, C
Hollomon's parameter P
Holdingtime,
t
30CrMoN
iV5.11
a
b
400
200
80
6050
40
30
20
10(a) h
(b)
15
0.1
5
10
20
16 17 18 19 20 21 22 23
100
700650550 600
700650550 600
700650550 600
700650550 600
Yieldstrengthorminimum
residualstress
afterstress-reliefannea
ling,
N/mm2
24C
rMoV
5.5
28NiCrM
o7.4
FIGURE 6.53 Yield strength at elevated temperatures (for 0.2% strain) calculated according to the
LarsonMiller method for three grades of alloyed structural steels for hardening and tempering
(designations according to DIN). (a) Calculated values and (b) experimentally obtained values. (From
G. Spur and T. Stoferle (Eds.), Handbuch der Fertigungstechnik, Vol. 4/2, Warmebehandeln, Carl Hanser,
Munich, 1987.)
2006 by Taylor & Francis Group, LLC.
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temperature of 6008C (11128F)and a soaking timeof 10h arechosen for stress-reliefannealing,
the residual stresses will, after this annealing, be reduced to a maximum of 70 N/mm2. Higher
temperatures and longer times of annealing may reduce residual stresses to lower levels, as can
be seen from Figure 6.53.
As in all heat treatment processes where Hollomons parameter is involved, selection of a
higher temperature may dramatically shorten the soaking time and contribute substantially to
the economy of the annealing process.
Dealing with structural steels for hardening and tempering, the stress-relief process and the
tempering process can be performed simultaneously as one operation, because Hollomons
parameter is also applicable to tempering. In such a case the stress-relief diagram may be used
in combination with the tempering diagram to optimize both the hardness and the level of
reduced residual stresses.
The residual stress level after stress-relief annealing will be maintained only if the cool-
down from the annealing temperature is controlled and slow enough that no new internal
stresses arise. New stresses that may be induced during cooling depend on the cooling rate, on
the cross-sectional size of the workpiece, and on the composition of the steel. Figure 6.54
shows the effect of cooling rate and cross-sectional diameter of forgings made of a CrMoNiVsteel on the level of tangential residual stresses after stress-relief annealing.
A general conclusion about stress-relief annealing is the following: In the temperature
range 4506508C (84212008F), the yield strength of unalloyed and low-alloyed steels is
lowered so much that a great deal of residual stress may be reduced by plastic deformation.
The influence of the steel composition on the level of residual stresses after annealing can be
considerable. While unalloyed and low-alloy steels with Ni, Mn, and Cr after stress-relief
annealing above 5008C (9328F) may get the residual stresses reduced to a low level, steels
alloyed with Mo or Mo V will retain a much higher level of the residual stresses after stress-
relief annealing at the same temperature because of their much higher yield strength at
elevated temperature.
6.2.2 NORMALIZING
Normalizing or normalizing annealing is a heat treatment process consisting of austenitizing
at temperatures of 30808C (861768F) above the Ac3 transformation temperature (for
00
20
40
60
80
100
120
10 20 30 40 50 60 80Tangentia
lresidualstresses,
N/mm2
Average cooling rate to 400, C/h
Dia
m.=
1000
mm
800
mm
600
mm
400mm
200m
m
FIGURE 6.54 Tangential residual stresses in a CrMoNiV alloy steel depending on the cooling rate and
cross-section diameter. (From G. Spur and T. Stoferle (Eds.), Handbuch der Fertigungstechnik, Vol. 4/2,
Warmebehandeln, Carl Hanser, Munich, 1987.)
2006 by Taylor & Francis Group, LLC.