Unit2 - Equilibrium Diagram
Unit2 - Equilibrium Diagram
Unit2 - Equilibrium Diagram
Metallurgy
Chapter 2
Equilibrium Diagrams
By
Prof. A. H. Kamble
M.E. (Mech.- Prod. Engg.) – Govt. College of Engg. Karad
PhD (Pursuing)
Prof. S. K. Khillare
M.Tech (CAD/CAM) – SGGS, Nanded
PhD (Pursuing)
Equilibrium Diagrams
2.1 Introduction
Equilibrium diagrams are also called phase diagrams.
Equilibrium diagrams are the diagrams which indicate the phases existing in the
system at any temperature and composition.
The coordinate system of binary phase diagrams uses temperature as the ordinate Y-
axis) and weight percent of second element (i.e. solute) as abscissa (X-axis).
These diagrams are used to find out the amounts of phases existing in a given alloy
with their compositions at any temperature.
From the amounts of phases at room temperature, in certain cases, it is possible to
estimate the approximate properties of the alloy.
These diagrams also help in understanding the phenomena that occur during heating
and cooling of the alloys.
Before studying the equilibrium diagrams, the meanings of terms used here are defined
in the next section.
2.4 Solution
Solution is a homogeneous mixture composed of two or more substances.
When an alloy is in a liquid state the atoms of the constituent are distributed
randomly through the liquid.
When solidification takes place, there appears number of possibilities.
A number of different types of solutions may form, which are given below;
Examples
Sterling silver (92.5% silver and the remainder copper) is a solid solution of silver
and copper. In this case silver atoms are solvent atoms whereas copper atoms are
solute atoms.
Brass is a solid solution of copper (64%) and zinc (36 %). In this case copper atoms
are solvent atoms whereas zinc atoms are solute atoms.
2.5.2 Difference between Substitutional solid solution and interstitial solid solutions
Interstitial Solid Solution Substitutional Solid Solution
1. In this solid solution the solute atom 1. In this solid solution the solute atom
occupies position in between the replaces the position of solvent atom.
interstitial sites or vacant places of
solvent atoms.
2. The atomic size of solute is smaller 2. The atomic size of solute and solvent
than solvent atom atoms are almost equal.
3. It is not governed by Hume Rothery 3. It is governed by Hume Rothery rules.
rules.
4. It produces more strong and hard 4. It produces less strong and hard
alloys. alloys.
5. e.g. Steel 5. e.g. Au-Cu solution.
2 = It represents any two variables out of the above three i.e. temperature, pressure and
concentration.
Most of the studies are done at constant pressure i.e. one atmospheric pressure and hence
pressure is no more variable. For such cases, Gibb’s phase rule becomes;
F C P 1
In the above rule, 1 represents any one variable out of the remaining two i.e. temperature
and concentration.
Hence, at lower temperatures nuclei become progressively smaller in size but the
number increases in greater amount.
Hence, some degree of undercooling is necessary to start solidification i.e.
nucleation.
At point E, solidification completes, and the solid pure metal cools from point E to
room temperature.
3. Note down the liquidus and solidus temperatures of these materials. Liquidus
temperatures are marked as L1, L2, L3, L4 ... L9, L10, L11, and solidus temperatures
are marked as S1, S2, S3, S4 ... S9, S10, S11; respectively.
4. Since materials 1 and 11 are pure metals, they solidify at constant temperature
and hence their liquidus and solidus temperatures are same i.e. L1 =S1 and L11 =
S11.
5. Transfer these liquidus and solidus temperatures to a temperature Vs
composition graph as shown in Fig 2-6.
6. Corresponding to materials 1 and 11 i.e. for pure Cu and Ni, we get only one
point and for others we get two points because solid solution alloys solidify over
a range of temperature.
7. Draw smooth curves through the points L1 to L11; and S1, to S11, which represent
liquidus and solidus of the diagram.
8. Above liquidus temperatures, all the materials are in the liquid state and below
the solidus temperatures they are in the solid state. Between the liquidus and
solidus temperatures, the alloys are in the liquid as well as solid state.
9. The resulting loop type of curve is called as the phase or equilibrium diagram.
Steps for
plotting of equilibrium diagram of any other system are similar to that
explained above.
Let us consider an isomorphous system of two metals A and B (Fig 2-7). Let Z be
the composition of the alloy under consideration and T be the temperature at which
the amounts of phases are to be determined.
At this temperature, the phases are solid and liquid. Let the amount of solid be S and
hence the amount of liquid (L) will be (1 − 𝑆), if the total amount is assumed to be
1.
We know that,
Now, the amount of B in the liquid or solid phase is equal to the amount of phase
multiplied by its composition in terms of B.
Here, at temperature T, the composition of solid is D and the composition of liquid
is C. Therefore,
The rule also holds good for other phases such as α +β or β + γ and is not restricted
to only solid and liquid phases.
2.11.1 Iron- Iron Carbide Equilibrium Diagram Fe-C or Fe-Fe3c Equilibrium Diagram
or Fe-C or Fe-Fe3c Phase Diagram
Iron- Iron Carbide Equilibrium Diagram is shown in Fig 2-9.
The temperature at which the allotropic changes take place in iron is influenced by
alloying elements, the most important of which is carbon.
The portion of the iron-carbon alloy system is shown in Error! Reference source
not found.. This is the part between pure iron and an interstitial or intermetallic
compound iron carbide Fe3C containing 6.67% carbon by weight.
The properties of iron carbon-alloy system can be understood with the help of Fe-C
equilibrium diagram. Therefore, it is highly essential to study the Fe-C equilibrium
diagram.
Fe-Fe3C equilibrium diagram consists of four distinct phases which are α –Ferrite,
γ- Austenite, δ- Ferrite, 4 Cementite. These phases are described as below;
1 α –Ferrite
α- Ferrite is almost a pure iron.
It is an essential solid solution of carbon in low temperature B.C.C. α-iron.
The solubility of carbon in α- iron at room temperature is 0.008% and increases with
increase in temperature to about 0.025% at 727oC.
It is relatively soft and ductile phase having hardness about 80 BHN.
It can be extensively cold worked without cracking.
It is strongly ferromagnetic up to 768oC and becomes paramagnetic at 768oC during
heating.
The temperature (768oC) at which α- ferrite becomes paramagnetic is called Curie
temperature.
2 γ- Austenite
γ- Austenite is an interstitial solid solution of carbon in FCC γ-iron.
The phase is called Austenite in honour of Sir Austin, who was one of the first
metallographer to study its properties.
It can dissolve up to 2.0% carbon at 1147oC.
Austenite phase is stable only above 727oC.
It is soft, ductile, malleable, and paramagnetic phase.
It can be extensively worked at the temperatures of its existence.
3 δ- Ferrite
It is an interstitial solid solution of carbon in high temperature BCC δ- iron.
It is similar to α- Ferrite except its occurrence at high temperature.
1 Peritectic Transformation
In general, Peritectic transformation is;
𝐶𝑜𝑛𝑠𝑡𝑎𝑛𝑡 𝑇𝑒𝑚𝑝𝑒𝑟𝑎𝑡𝑢𝑟𝑒
𝑆1 + 𝐿 → 𝑆2
In above reaction, δ of 0.1% carbon is added with liquid of 0.55% carbon at the
temperature 14930C to get γ of 0.18% carbon.
The peritectic reaction in iron-iron carbide system is as shown in Fig 2-10.
For hypoeutectic steels (< 0.18% carbon), the reaction may be as follows;
For hypereutectic steels (> 0.18% carbon), the reaction may be as follows;
All steels contain carbon in the range of 0.10 to 0.55% as shown in peritectic reaction in
Error! Reference source not found.. When cooled from the liquid state, the
commercial heat treatment is not done in δ- region, we will not refer this region while
study of steels, so no use of changes in properties of steels.
2 Eutectoid Transformation
The eutectoid transformation reaction occurs as follows;
𝐶𝑜𝑛𝑠𝑡𝑎𝑛𝑡 𝑇𝑒𝑚𝑝𝑒𝑟𝑎𝑡𝑢𝑟𝑒
𝑆𝑜𝑙𝑖𝑑 1 → 𝑆𝑜𝑙𝑖𝑑2 + 𝑆𝑜𝑙𝑖𝑑3
Where Solid 1, Solid 2, and Solid 3 are various solid phases.
The eutectoid reaction in iron-carbon system is as shown in Figure 2-1.
The properties of pearlite depends upon its interlamellar distance. Similar the distance
higher will be the mechanical properties. The interlamellar distance depends upon the
cooling rate and not on the limit. The distance becomes less as the cooling rate increases.
The hardness of pearlite will be 225BHN to 275 BHN.
3 Eutectic Transformation
The eutectic transformation reaction in general as follows;
In iron carbon system, the reaction occurs at 11470C and carbon at 4.3%.
The transformations are as follows;
The liquid transforms to eutectic mixture of austenite (2% carbon) and cementite (6.67%
carbon) is called Ledeburite. The eutectic reaction in iron carbon system as shown in
Figure 2-2 as below;
Austenite from the Ledeburite is not stable at low temperature and gets transformed to
pearlite with slow rates of cooling at 727oC; and hence at room temperature, structure
consists of pearlite and cementite. The mixture of perlite and cementite at room
temperature is called Transformed Ledeburite.
The amount of pearlite and cementite in transformed Ledeburite at room temperature
according to lever rule are as below;
The cementite phase having carbon content 6.67% due to which cementite is hard and
brittle and pearlite is slightly hard and therefore, transformed Ledeburite is hard and
brittle.
Iron carbon equilibrium diagram showing the transformation and occurrence
region of pearlite and Ledeburite is shown in Figure 2-3.
The critical temperatures are shown on Fe-Fe3C phase diagram in Fig 2-11.
In Fig 2-12, it shows that, solidification starts at or just below liquidus temperature
i.e. line PQR.
Below liquidus line PQR, separation of δ-ferrite for a steels of less than 0.55%
carbon and γ-austenite for a steel of carbon between 0.55 to 2.0% take place.
As the temperature decreases, more and more liquid solidifies and the solidification
completes at the solidus temperature (line PSUV).
Below line XUV, all the steels have austenitic structure.
Further decrease in temperature results in solid to solid phase transformation at upper
and lower critical temperatures.
As the carbon increases, the amount of proeutectoid ferrite decreases and pearlite
increases.
For 0.8% carbon, the amount of ferrite becomes 0% and pearlite becomes 100%.
There is linear relation in amount of carbon content of the steel and the amount of
pearlite & ferrite.
For 0.008% C, the amount of α-ferrite is 100% and for 0.8%C, the amount of pearlite
is 100%.
The variation of ferrite and pearlite with carbon is shown in Fig 2-14.
Fig 2-14 variation of pearlite and ferrite with carbon for hypoeutectoid steels
Ferrite appears white and pearlite appears dark or lamellar under the microscope
with most common etching reagents such as nital and picral.
Typical microstructures of some of the hypoeutectoid steels are shown in Fig 2-15
to Fig 2-17.
Fig 2-15 Microstructure of ≈ 0.1% Carbon steel light phase being the ferrite and the dark phase being pearlite.
Fig 2-16 Microstructure of ≈ 0.2% Carbon steel light phase being the ferrite and the dark phase being pearlite.
Fig 2-17 Microstructure of ≈ 0.4% Carbon steel light phase being the ferrite and the dark phase being pearlite.
When this steel is cooled from point 1, structural changes are occurred.
At point 1, cementite starts separating out on the grain boundaries of austenite.
As the temperature decreases amount of cementite increases.
The composition of austenite varies along line EJ while composition of cementite
does not change as it is an intermetallic compound.
This continues up to point2.
The cementite which is separated before eutectoid transformation is called primary
or proeutectoid cementite.
At point 2, the existing amount of γ-austenite starts to transform into peralite.
Cooling from point 2 to 3 does not result in significant change in microstructure and
hence the same structure is observed at room temperature.
The amount of cementite and pearlite can be calculated as;
As the carbon increases, the amount of Fe3C increases and for a steel containing
maximum amount of carbon i.e. 2.0%, the amount of Fe3C is;
Free cementite is 0% for 0.8%C steel and increases linearly with increasing carbon
reaching to 20.4% for 2.0% carbon steel.
The variation of Fe3C and pearlite with carbon is shown in Fig 2-20.
Fig 2-19 Variation of pearlite and cementite with carbon for hypereutectoid steels.
Cementite appears white at the grain boundaries of pearlite and pearlite appears dark
or lamellar under the microscope with the general etching reagents such as nital and
picral
Fig 2-20 Microstructure of 1.0%C steel slowly cooled from austenitic region showing cementite (white) at the grain
boundaries (Etchant 5% Nital, 100X)
They are good for fabrication work by welding, pressing or machining; however,
they cannot be hardened by heat treatment.
They are used for wires, nails, rivets, screws, panels, welding rods, ship plates, boiler
plates and tubes, fan blades, gears, valves, camshafts, crank shafts, connecting rods,
railway axles, fish plates, cross-heads, tubes for bicycles and automobiles and small
forgings.
Steels with 0.15 to 0.3% carbon are widely used as structural steels and finds
applications as building bars, grills, beams, angles, channels etc.
They are used for forging dies, punches, hammers, springs, clips, clutch discs, car
bumpers, chisels, vice jaws, shear blades, drills, leaf springs, music wires, knives,
razor blades, balls and races for ball bearings, mandrels, cutters, files, wire drawing
dies, reamers and metal cutting saws.
a. Rimmed Steels
In rimmed steels, oxygen is not removed by any deoxidation process.
During solidification, the dissolved oxygen combines with carbon to form CO.
This CO gas forms blow holes and gets collected at the centre of the ingot i.e. given
steel.
The outer thin layer of the solid iron thus contains less carbon, more purity and free
from blow holes.
These blow holes get eliminated during cold working.
Rimmed steels are not used for forging operation.
b. Killed Steels
In killed steels, the oxygen is completely removed by addition of deoxidizing agents
such as Al, Si, Mn etc.
These deoxidants remove free oxygen but form oxide inclusions.
Killed steel is free from blow holes throughout the cross-section of the ingot.
These steels can be used for forgings, rolling etc.
c. Semi-killed steels
In theses steels, part of the dissolved oxygen is removed by addition of de-oxydiseres
and the rest combines with carbon.
These steels contain oxygen in the form of CO and oxide inclusions.
Fewer blowholes are observed as compared to rimmed steels.
a. Non-hardenable steels
Contains less carbon and almost no alloying elements.
f) Tool steels
g) Free cutting steels
h) Sprig steels
i) Structural steels
j) Die steels
Additional letters added between the second and third digits include B when boron
is added (between 0.0005 and 0.003%) for enhanced hardenability, and L when lead
is added (between 0.15 and 0.35%) for enhanced machinability.
The prefix M is used to designate merchant quality steel (the least restrictive quality
descriptor for hot-rolled steel bars used in noncritical parts of structures and
machinery).
The prefix E (electric-furnace steel) and the suffix H (hardenability requirements)
are mainly applicable to alloy steels.