heat_treatment.pdf
TRANSCRIPT
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Bulk and Surface Treatments
Annealing, Normalizing, Hardening, Tempering
Hardenability
HEAT TREATMENT
With focus on Steels
Principles of Heat Treatment of Steels
Romesh C Sharma
New Age International (P) Ltd., Publishers, New Delhi, 1993.
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We have noted that how TTT and CCT diagrams can help us design heat treatments to
design the microstructure of steels and hence engineer the properties. In some cases a
gradation in properties may be desired (usually from the surface to the interior- a hard
surface with a ductile/tough interior/bulk).
The general classes of possibilities of treatment are: (i) Thermal (heat treatment), (ii)
Mechanical (working), (iii) Chemical (alteration of composition). A combination of these
treatments are also possible (e.g. thermo-mechanical treatments, thermo-chemical
treatments).
The treatment may affect the whole sample or only the bulk.
A typical industrial treatment cycle may be complicated with many steps (i.e. a
combination of the simple step which are outlined in the chapter).
Heat Treatment of Steels
Thermal (heat treatment)
Chemical
Treatments MechanicalOr a combination
(Thermo-mechanical, thermo-chemical)
Bulk
Surface
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HEAT TREATMENT
BULK SURFACE
ANNEALING
Full Annealing
Recrystallization Annealing
Stress Relief Annealing
Spheroidization Annealing
AUSTEMPERING
THERMAL THERMO-
CHEMICAL
Flame
Induction
LASER
Electron Beam
Carburizing
Nitriding
Carbo-nitriding
NORMALIZING HARDENING &
TEMPERING
MARTEMPERING
An overview of important heat treatments
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A1
A3
Acm
T
Wt% C
0.8 %
723C
910C
Spheroidization
Recrystallization Annealing
Stress Relief Annealing
Full Annealing
Ranges of temperature where Annealing, Normalizing and Spheroidization treatment are
carried out for hypo- and hyper-eutectoid steels.
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Full Annealing
The steel is heated above A3 (for hypo-eutectoid steels) | A1 (for hyper-eutectoid steels) → (hold) → then the
steel is furnace cooled to obtain Coarse Pearlite
Coarse Pearlite has ↓ Hardness, ↑ Ductility
Not above Acm → to avoid a continuous network of proeutectoid cementite along grain
boundaries (→ path for crack propagation)
A1
A3
Acm
T
Wt% C
0.8 %
723C
910C
Spheroidization
Recrystallization Annealing
Stress Relief Annealing
Full Annealing
Full Annealing
Normali
zatio
nNormalization
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Recrystallization Annealing
Cold worked grains → New stress free grains
Used in between processing steps (e.g. sheet rolling)
Heat below A1 → Sufficient time → Recrystallization
A1
A3
Acm
T
Wt% C0.8 %
723oC
910oC
Spheroidization
Recrystallization Annealing
Stress Relief Annealing
Full Annealing
Full Annealing Normali
zatio
nNormalization
A1
A3
Acm
T
Wt% C0.8 %
723oC
910oC
Spheroidization
Recrystallization Annealing
Stress Relief Annealing
Full Annealing
Full Annealing Normali
zatio
nNormalization
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Stress Relief AnnealingAnnihilation of dislocations,
polygonization
Welding
Differential cooling Machining and cold working Martensite formation
Residual stresses → Heat below A1 → Recovery
A1
A3
Acm
T
Wt% C0.8 %
723oC
910oC
Spheroidization
Recrystallization Annealing
Stress Relief Annealing
Full Annealing
Full Annealing Normali
zatio
nNormalization
A1
A3
Acm
T
Wt% C0.8 %
723oC
910oC
Spheroidization
Recrystallization Annealing
Stress Relief Annealing
Full Annealing
Full Annealing Normali
zatio
nNormalization
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Spheroidization Annealing
Heat below/above A1 (long time)
Cementite plates → Cementite spheroids → ↑ Ductility
• Used in high carbon steel requiring extensive machining prior to final hardening & tempering
• Driving force is the reduction in interfacial energy
A1
A3
Acm
T
Wt% C0.8 %
723oC
910oC
Spheroidization
Recrystallization Annealing
Stress Relief Annealing
Full Annealing
Full Annealing Normali
zatio
nNormalization
A1
A3
Acm
T
Wt% C0.8 %
723oC
910oC
Spheroidization
Recrystallization Annealing
Stress Relief Annealing
Full Annealing
Full Annealing Normali
zatio
nNormalization
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NORMALIZING
Refine grain structure prior to hardening
To harden the steel slightly
To reduce segregation in casting or forgings
Heat above A3 | Acm → Austenization → Air cooling → Fine Pearlite (Higher hardness)
• In hypo-eutectoid steels normalizing is done 50oC above the annealing temperature
• In hyper-eutectoid steels normalizing done above Acm → due to faster cooling
cementite does not form a continuous film along GB
Purposes
A1
A3
Acm
T
Wt% C0.8 %
723oC
910oC
Spheroidization
Recrystallization Annealing
Stress Relief Annealing
Full Annealing
Full Annealing Normali
zatio
nNormalization
A1
A3
Acm
T
Wt% C0.8 %
723oC
910oC
Spheroidization
Recrystallization Annealing
Stress Relief Annealing
Full Annealing
Full Annealing Normali
zatio
nNormalization
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HARDENING
Heat above A3 | Acm → Austenization → Quench (higher than critical cooling rate)
• Quench produces residual strains
• Transformation to Martensite is usually not complete (will have retained Austenite)
• Martensite is hard and brittle
• Tempering operation usually follows hardening; to give a good combination of
strength and toughness
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Typical hardness test survey made along a
diameter of a quenched cylinder
Schematic showing variation in cooling
rate from surface to interior leading to
different microstructures
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Severity of quench values of some typical quenching conditions
Process Variable H Value
Air No agitation 0.02
Oil quench No agitation 0.2
" Slight agitation 0.35
" Good agitation 0.5
" Vigorous agitation 0.7
Water quench No agitation 1.0
" Vigorous agitation 1.5
Brine quench
(saturated Salt water)No agitation 2.0
" Vigorous agitation 5.0
Ideal quench
Note that apart from the nature of the quenching medium, the vigorousness of the shake
determines the severity of the quench. When a hot solid is put into a liquid medium, gas bubbles
form on the surface of the solid (interface with medium). As gas has a poor conductivity the
quenching rate is reduced. Providing agitation (shaking the solid in the liquid) helps in bringing
the liquid medium in direct contact with the solid; thus improving the heat transfer (and the
cooling rate). The H value/index compares the relative ability of various media (gases and
liquids) to cool a hot solid. Ideal quench is a conceptual idea with a heat transfer factor of (
H = )
1[ ]f
H mK
Severity of Quench as indicated by the heat
transfer equivalent H
f → heat transfer factor
K → Thermal conductivity
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Jominy hardenability test Variation of hardness along a Jominy bar
(schematic for eutectoid steel)
Schematic of Jominy End Quench Test
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Tempering
Heat below Eutectoid temperature → wait→ slow cooling
The microstructural changes which take place during tempering are very complex
Time temperature cycle chosen to optimize strength and toughness
Tool steel: As quenched (Rc 65) → Tempered (Rc 45-55)
Cementite
ORF
Ferrite
BCC
Martensite
BCTTemper
)( Ce)( )( ' 3
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AustenitePearlite
Pearlite + Bainite
Bainite
Martensite100
200
300
400
600
500
800
723
0.1 1 10 102 103 104 105
Eutectoid temperature
Ms
Mf
t (s) →
T
→
+ Fe3C
MARTEMPERING
AUSTEMPERING
To avoid residual stresses generated during quenching
Austenized steel is quenched above Ms for homogenization of temperature across the
sample
The steel is then quenched and the entire sample transforms simultaneously
Tempering follows
To avoid residual stresses generated during quenching
Austenized steel is quenched above Ms
Held long enough for transformation to Bainite
Martempering
Austempering
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Various elements like Cr, Mn, Ni, W, Mo etc are added to plain carbon steels to create
alloy steels
The alloys elements move the nose of the TTT diagram to the right
→ this implies that a slower cooling rate can be employed to obtain martensite
→ increased HARDENABILITY
The ‘C’ curves for pearlite and bainite transformations overlap in the case of plain carbon
steels → in alloy steels pearlite and bainite transformations can be represented by separate
‘C’ curves
ALLOY STEELS
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