CHAPTER -1 INTRODUCTION 1.1 Basics of Heat treatment 1.1.1 Hardening processes The general purpose of heat treatment process is to vary the hardness of the metal or to produce a structure or a surface that facilitates the progress of subsequent manufacturing operations (Payson, P., 1943) or the proper fimctioning of the product. Hardening Hardening consists of heating of metallic materials to hardening temperature, holding at that temperature, followed by rapid cooling such as quenching in water, oil or salt baths. The high hardness developed by this process is due to the phase transformation accompanying rapid cooling. The term rapid cooling simply does not mean that cooling rate is higher than that adopted in annealing and normalizing. What it really means is that cooling rate is equal to or more than the critical cooling rate of the given material. Rapid cooling results in the transformation of austenite at considerably low temperatures transformation into non-equilibrium products. The product of low temperature transformation of austenite is martensite, which is hard microconstituent of steel (Schimizu, N. and Tamura, I., 1978). Brayans, R.G., et al., (1969) analyzed the mechanism of phase transformation in crystalline solids and observed that the hardening temperature depends on chemical composition. For plain carbon steels, it depends on carbon content alone. Hypoeutectoid steels are heated to about 30-50°C above the upper critical temperature, whereas eutectoid and hypereutectoid steels are heated to about 30-50°C above the lower critical temperature. The phases, Ferrite and pearlite transform into austenite at hardening temperature for hypoeutectoid steels. This austenite transforms to marteniste on rapid quenching from hardening temperature. The presence of martensite accounts for high hardness of quenched steel. If hypoeutectoid steel is heated to a hardening temperature equivalent to that for hypereutectoid steel, the structure will consist of ferrite and
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CHAPTER -1 INTRODUCTION
1.1 Basics of Heat treatment
1.1.1 Hardening processes
The general purpose of heat treatment process is to vary the hardness of the metal
or to produce a structure or a surface that facilitates the progress of subsequent
manufacturing operations (Payson, P., 1943) or the proper fimctioning of the product.
Hardening
Hardening consists of heating of metallic materials to hardening temperature,
holding at that temperature, followed by rapid cooling such as quenching in water, oil or
salt baths. The high hardness developed by this process is due to the phase
transformation accompanying rapid cooling. The term rapid cooling simply does not
mean that cooling rate is higher than that adopted in annealing and normalizing. What it
really means is that cooling rate is equal to or more than the critical cooling rate of the
given material. Rapid cooling results in the transformation of austenite at considerably
low temperatures transformation into non-equilibrium products. The product of low
temperature transformation of austenite is martensite, which is hard microconstituent of
steel (Schimizu, N. and Tamura, I., 1978).
Brayans, R.G., et al., (1969) analyzed the mechanism of phase transformation in
crystalline solids and observed that the hardening temperature depends on chemical
composition. For plain carbon steels, it depends on carbon content alone. Hypoeutectoid
steels are heated to about 30-50°C above the upper critical temperature, whereas
eutectoid and hypereutectoid steels are heated to about 30-50°C above the lower critical
temperature. The phases, Ferrite and pearlite transform into austenite at hardening
temperature for hypoeutectoid steels. This austenite transforms to marteniste on rapid
quenching from hardening temperature. The presence of martensite accounts for high
hardness of quenched steel. If hypoeutectoid steel is heated to a hardening temperature
equivalent to that for hypereutectoid steel, the structure will consist of ferrite and
austenite. This will transform to femte and martensite on quenching. Femte, a very soft
phase, lowers the hardness of hardened steel considerably. Thus, the very purpose of
hardening, i.e. attainment of improved mechanical properties is lost. This is also known
as incomplete hardening, and is not usually employed in practice. The preferred
hardening temperature for hypereutectoid steel lies between the lower critical temperature
(A,) and the upper critical temperature (Lm). The advantage gained from hardening
temperature in this range is two-fold. The first is related to the presence of cementite in
hardened steel. The cementite in a martensitic matrix accounts for several desirable
properties. Wear resistance is one of them. The fact that both martensite and cementite
are hard constituents their presence is responsible for high wear resistance of the resulting
microstructure. Cementite is harder than martensite and so wear resistance of the two-
phase microstructure is better than what is achieved by martensite alone. The second
advantage of this hardening temperature is the attainment of fme martensite in the final
structure. In fact, heating of hypereutectoid steel above the upper critical temperature
(km) for hardening is detrimental because such a high temperature will result in
coarsening of austenitic grains and decarburization at the surface. Coarse austenite will
transform to coarse acicular marteniste (microstructure) which has poor mechanical
properties. Decarburized surface responds poorly to hardening treatment. In addition to
these factors, quenching from such a high temperature will introduce severe internal
stresses in the hardened steel.
Quenching media
When hardening tools and machine components, the heat treater generally aims at
obtaining a martensitic structure, at least in the surface layers of the steel. Hence, the rate
of cooling must be controlled so that the formation of femte, pearlite or bainite is
avoided. For cooling the hot metals, the various quenchants used are water, oil, air, salt
baths, mixtures of water and oil (emulsions) and polymer quenching media.
During the quenching of steel in liquid media, the whole operation may be split
up into three stages, viz. the vapour-blanket stage, the boiling stage, and the convection
stage, as shown in Figure 1. l(Christian, J.W., 1975).
CONVECTION I
Figure 1.1 Three stages of the cooling curve
During the vapour-blanket, stage a thin vapour film form, which is, heat
insulating and thus prevents heat abstraction. Therefore, the curve has rather flat
appearance in this range.
During the boiling stage, there is high rate of heat abstracting which in part is due
to the energy consumed by the vapour formation and in part to the vigorous agitation.
During the convection stage, the heat abstraction takes place more slowly and the
curve is flat once again.
Tempering
Jaffe, L.D. and Buffurn, D.C., (1965) investigated the Upper Temper
Embrittlement of Ni-Cr-Steel and found that, when steel is hardened to a martensitic
structure the toughness is rather low. On tempering, i.e. heating it to some temperature
between 160°C and 650°C, the toughness increases considerably.
Austempering is special heat treatment process in which austenite is transformed
into bainite. Similar to austempering, Martempering involves heating the steel to the
austenitizing temperature, followed by quenching in a constant temperature bath
maintained above M, point. The usual temperature of the bath lies between 180°C and
250°C. Steel is held in the bath till the temperature throughout the section becomes
uniform and is equal to the bath temperature. As soon as this temperature is attained,
steel is withdrawn and cooled in air. The cooling rate should be sufficiently high and
holding time considerably short to prevent transformation of austenite to pearlite or to
bainite. Martensite is formed in the second stage, namely during cooling in air.
Sub-zero treatment
The resultant microstructure of klly hardened steel should consist of martensite.
In practice, it is very difficult to have a completely martensitic structure by hardening
treatment. Some amount of austenite is generally present in the hardened steel. This
austenite existing along with the marteniste is referred to as retained austenite.
Conventional metallography does not reveal the presence of retained austenite till it
exceeds 20 percent. The presence of retained austenite greatly reduces mechanical
properties and such steels do not develop maximum hardness even after cooling at rates
higher than the critical cooling rate. The amount of retained austenite depends largely on
the chemical composition of steel. For plain carbon steels, the amount of retained
austenite increases with the rise in carbon contents (Suryanarayana, A.V.K., 1979). The
problem of retained austenite is more complex in alloy steels. Most of the alloying
elements increase the content of retained austenite.
Hardness can be improved in hardened steels containing retained austenite by a
process known as sub-zero treatment or cold treatment. Retained austenite is converted
into martensite by this treatment. This conversion of retained austenite into martensite
results in increased hardness, wear resistance and dimensional stability of steel. When
hardened steel is left with retained austenite, it is likely to get transformed into martensite
during subsequent thermal cycling. Such transformation leads to unpredictable
dimensional changes. Hence, for dimensional stability, it is necessary to eliminate
retained austenite as far as possible. This can be done through sub-zero treatment. The
process consists of cooling steel to sub-zero temperature, which should be lower than the
Mf temperature of the steel. Mf temperature for most steels lies between -30°C and -
70°C. During the process, considerable amount of internal stresses are developed in the
steel, and hence tempering is done immediately after the sub-zero treatment. This
treatment also helps to temper martensite, which is formed by decomposition of retained
austenite during sub-zero treatment. This treatment has been found to be less effective if
performed on steels, which have been kept at room temperature for several hours or
mildly heated, say up to 100 or 150°C, after the hardening treatment. The reason for this
is that the stability of austenite is increased considerably by these two processes. The
austenite so stabilized does not transform to marteniste completely. Therefore, sub-zero
treatment must be performed just after the hardening treatment. Mechanical refrigeration
units, dry ice, and some liquefied gases such as liquid nitrogen can be used for cooling
steels to sub-zero temperatures (Rajan, T.V., et al., 1998).
This treatment is employed for high carbon and high alloy steels used for making
tools, bearings, measuring gauges and components requiring high impact and fatigue
strength coupled with dimensional stability. Case hardened steels, which have a tendency
to retain austenite, are also subjected to such treatment.
1.1.2 Surface heat treatment
There are situations in which the requirement is such that the outer surface should
be hard and wear resistant and the inner core more ductile and tougher. Such a
combination of properties ensures that the component has sufficient wear resistance to
give long service life and at the same time has sufficient toughness to withstand shock
loads. Such combination can basically achieved by case hardening process (Child, H.C.,
1980).
Case hardening treatments are basically classified into two groups. The first
group is known as thennochemical treatment because the surface composition of the steel
is changed by difhsion of carbon and some times by other elements.
Examples: Carburizing-Pack carburizing, Liquid Carburizing and Gas Carburizing
Vacuum carburizing, Post-Carburizing, Cyaniding and carbonirtriding, Nitriding, Plasma
Nitriding, Salt bath nitrocarburizing, Boronizing, Chromizing and Toyota Diffusion
Process
The second one is called thermo-mechanical treatment, which involves phase
transformation, by rapid heating and cooling of the outer surface.
Examples: Flame hardening, Induction hardening Electron beam hardening and laser
hardening
Thermo-chemical surface hardening
Carburizing
Carburizing is the most widely used process for surface hardening of steels. In
this process carbon is difhsed into steel by heating above the transformation temperature
and holding the steel in contact with a carbonaceous material which may be a solid
medium, liquid or a gas. Under such condition, carbon is absorbed in solid solution in
austenite. As the solubility of carbon is more in the austenitic state than in fenitic state,
fully austenitic steel is essential for carburizing (Colegate, G.T., 1951). Carburizing can
be divided into Pack carburizing, Liquid Carburizing and Gas Carburizing. Among them
Gas Carburizing is the most widely used industrial heat treatment process.
Gas carburizing is a process in which the surface of the component is saturated
with carbon in a gaseous atmosphere containing carbon. To accomplish this, first the
components are heated in a gas tight furnace in a neutral atmosphere to a predetermined
temperature in the range of 870 to 940 OC. Then the furnace is flooded with a suitable
gas such as Propane, Butane, Kerosene etc. Finally, the components are held at this
temperature to allow diffusion of carbon into the case. After the carburizing treatment is
over the components are quenched to get the required hardness, wear resistance and
fatigue resistance on the surface, supported by a tougher core. A striking feature of gas
carburizing process is that in this process the original toughness and the ductility
remains unaffected even after the heat treatment.
Cyaniding
In cyaniding, the surface layer of steel is hardened by addition of both carbon and
nitrogen. Cyaniding is carried out in a liquid bath of NaCN. In this process, parts to be
heat treated are immersed in a liquid bath (800 - 960 OC) of NaCN with the concentration
varying between 25% and 90%. Measured amount of air is passed through the molten
bath. NaCN reacts with the oxygen in the air and is oxidized. Carbon and Nitrogen so
formed in atomic form diffuse into the steel and give thin wear resistance layer. Usually
this process requires 30-gominutes for completion. Case depth ranging from 0.5 to 2mm
can be achieved. This process is not suitable for hardening those parts, which are
subjected to shock, fatigue and impact because nitrogen addition has adverse effects on
such properties of steels (Waterfall, F.D., 1949).
Carbo-nitriding
Carbo-nitriding is carried at lower temperatures (800 - 870 OC) in a gas mixture
consisting of a carburizing gas and Ammonia. A typical gas mixture contains about 15%
NH3 5% CH4, and 80% neutral carrier gas. Carbon and nitrogen are diffused at the same
time into the surface of the steel in the austenitic ferritic conditions and gives case
thickness of the order of 0.05 to 0.75mm. After Carbo-nitriding, quenching is done in oil
to a avoid cracking.
Plasma-nitriding
Plasma nitriding is also known as an Ion nitriding process. In this process the
steel components to be heat treated is kept at 450 OC in vacuum at a negative potential of
the order of 1000 ohms with respect to chamber. Then an appropriate mixture of nitrogen
and Hydrogen is passed at a pressure of 0.22 to 8m bar. As a result, plasma formation of
these gases takes place. Korotchenko, V., and Bell, T., 1978, showed that in Plasma
Nitriding the time required for achieving the case depth of 4pm is about 20 hours at
450°C.
Boronizing
Boronizing is the one of the recent methods of surface hardening. Both pack and
gaseous techniques can be applied using Boronizing. In the case of pack Boronizing, The
Components are packed in heat resistant boxes with mixtures of granules or paste of
boron carbide with addition of activators at 900 - 1000 OC. Boron diffuses inwards and
iron borides layers are formed. On the outer surface FeB phase forms, while in the
interior Fe2B phase is formed. FeB phase is more brittle and it is not desirable. Higher
temperatures, longer treatment times and high alloy steels favours the formation of FeB
Phase. The treatment time requires for a case depth of 0.15mm is 6hours at about 900
"C. The significance of this process is the treatment temperature, which is very high and
hence hardening of components before Boronizing is not required (Graf Von
Matuschka, A,, 1975).
Chromizing
Chromizing is used for surface hardening of both carbon and tool steels. The
components to be chromized are packed with fine chromium powder and additives. A
typical Chromizing mixture consists of 60% Cr, 0.2%Ammoium Iodide and 39% Kaolin
powder. Diffusion of chromium takes place at 900-1020 OC and chromium carbide is
formed at the outer surface of the steel. The treatment time needed for achieving a case
depth of 0.02 - 0.04mm is 12 hours. Hardness of chromium carbide layer is about
1500VHN (Raghavan, V., 1984).
Toyota Diffusion process
In this surface hardening process, which produces the hardest surface, the
hardness achieved is of the order of 3000 - 4000VHN. In Toyota Diffusion process, the
component is kept in salt bath of proprietary composition based on borax. The carbide
forming elements are added in the form of Ferro alloys. The process is carried out at
about 1050°C. After salt bath treatment, the components are quenched and tempered.
This process of surface hardening is very appropriate for die and tool steels (Rajan, T.V.,
et al., 1998).
Thermo mechanical surface hardening
Flame hardening
Flame hardening is the simplest form of surface hardening heat treatment. This
process consists of heating the large work piece, such as crankshaft, axles, large gear,
cam or any other complicated cross section by an oxy-acetylene or oxy-fuel blowpipe
followed by spraying of jet of water as coolant. Hardness in flame-hardened steel is due
to martenisitic and lower bianitic structure. The carbon content required for flame
hardening steels varies from 0.3% -0.6%. High carbon steels can also be hardened by
this process, but greater care is required to avoid cracking. This process can achieve
normally, a case depth of upto 3mm. There are four different methods, which are used in
general for flame hardening: i) Stationary, ii) Progressive iii) Spinning iv) Progressive-
Spinning.
There is a little scaling, decarburization or distortion in flame hardening. Since
the heating and cooling are very fast, the core remains unaffected (Davies, D.E., 1966).
Induction hardening Process
Generally this process is used to surface harden crankshaft, camshaft, gears, crank
pins and axles. In this process, heating of the components is achieved by electromagnetic
induction. A conductor (coil) carries an alternating current of high frequency, which is
then induced in the enclosed steel part within the magnetic field of the coil. As a result,
induction heating takes place. The heat so generated affects only the outer surface of the
steel components due to skin effect. The component is heated usually for a few seconds
only, and then it is quenched immediately by the jet of cold water. Due to quenching
martensitic structure is formed which makes the outer surface hard and wear resistance.
The hardening temperature ranges from 760 to 930°C. According to the Carbon content
and alloy addition, the temperature is fixed (Lakhtin, Yu.M., 1979).
Electron beam hardening
Electron beam hardening is a short surface hardening procedure for
martenisitically hardeneable ferrous materials. So this process is used for hardening
those components, which cannot be induction, hardened because of associated distortion.
Automatic transmission clutch cams (SAE 5060 Steels) are hardened by this process.
The work piece is kept in vacuum at 0.06m bar pressure. Electron beam is focused on the
work piece to heat the surface. In the beginning, energy input is kept high. With time,
power input is reduced as the component gets heated up. This is done to avoid melting.
Normally case depth upto 1.5mm can be achieved by this method (Brooks, C.R., 1996).
Laser surface hardening
Laser surface hardening of ferrous materials is an established process used to
enhance the mechanical properties of highly stressed machine parts such as gears and
bearings. Laser beams are used since these have very high intensity, but they may melt
the work piece when they are used at such a high intensity. Therefore, a lens is used to
reduce the intensity by producing a defocused spot from 1 to 25 mm wide. Ashby and
Easterling, (1984) demonstrated that a laser beam of 1kW produces a circular spot
whose diameter may vary from 0.5- to 0.25mm. Industrial lasers upto 20kW are now
available. Case depth of about 1.3mm is obtained by self quenching. The microstructure
of laser heated steel consists of bianite and ferrite at the surface of the heated spot and
pearlite and fenite in the interior.
Salt bath hardening
Salt bath heat treating methods are uniform, quick, efficient, economical and
environmentally responsible. Salt bath are used in a wide variety of commercial heat
treating operations. Parts that are heated in molten salt bath are heated by conduction.
The molten salt bath provides a ready source of heat as required. Although materials
being heated come in contact with heat through their surfaces, the core of a part rises in
temperature at approximately the same rate as its surface. Heat is quickly drawn to the
core fiom the surface and salt bath provide heat at an equal rate over the total part. Salt
bath hardening consists of four stages namely Preheating, Austenitizing, Quenching and
Drawing (Grossmann, A,, and Bain, E.C., 1964).
1.1.3 Gas carburizing
During the last few decades, carburizing by means of gas has become the most
popular method of case hardening. The furnaces are very dependable and relatively
simple to operate. Since hydrocarbons enter into the process, several reactions take place
simultaneously. In addition to the reaction
2com C+ C02 ...l.l
there is also the methane reaction
-2%
CH4 - C+ 2H2 ... 1.2
and the water-gas reaction a
CO+H2 '- C+H20 ... 1.3
The composition of the furnace gas can be determined by analysis and hence the
carbon potential may be determined. The moisture content of the gas has a great
influence on the carbon potential as indicated by reaction (eq. 1.3) and may be measured
by simply determining the dew point of the gas. The dew point is that temperature at
which the water droplets (dew) are deposited from the gas (saturation).
Harris, F.E., (1943) described a method of calculating the carbon potential from
the composition of the gas. There are a number of methods in existence for the
continuous measurement and control of the carbon potential. One such method is based
on infrared rays, which are used to register the concentration of C02 in the gas. This
value gives a measure of the CO concentration, which, in turn, relates to the carbon
potential. By means of a special measuring unit, the resulting impulse can be converted
direct to a numerical value of the carbon potential. The control may also be carried out
my measuring the resistance of a steel wire, which is calibrated for different carbon
concentrations. The resistance measured is proportional to the carbon concentration.
Indirect measurement of the carbon content can take place by means of an oxygen probe.
When gas carburizing is being employed, a primary requirement is the availability
of furnaces sufficiently gas tight to prevent air ingress, since this would interfere with the
process.
In principle, there are four different ways of producing the gas, viz.:
Dripping carburizing liquid into the furnace. This liquid generally contains ethyl
alcohol and white spirit or only isopropyl alcohol. It drops on to a plate inside the
hrnace where it is dispersed and vaporized. By this method, it is possible to
employ a liquid that produces a carrier gas having a relatively low carbon
potential. This potential can then be adjusted by dripping a more active liquid
into the furnace. In practice, however, only one liquid is used and the carbon
potential is adjusted by varying the volume of liquid added.
Admission of gas from a gas-producing unit. The gas is produced by endothermic
combustion. The raw gas, usually propane, is mixed with air in carefully
balanced proportions and burnt in the gas-producing unit to produce a carrier gas
with a carbon potential of 0.35% - 0.50%. Before it enters the furnace, the carrier
gas is given an extra addition of propane, thereby adjusting the carbon potential to
the required level, which is usually around 0.8%.
Direct admission of gas and air into the furnace. The gas actually doing the
carburization is produced in the furnace chamber by the reaction between the gas
and air, which are admitted in balanced amounts.
Carburizing in a vacuum furnace. Only hydrocarbons are admitted into the
furnace fi-om which air is evacuated. Since no oxygen takes part into the reaction,
there is no internal oxidation. The process can take place at a temperature higher
than that normally used, thus allowing the carburization to proceed more quickly
(Western, H.W., 1972 and Grosch, et al., 1981).
Depth of hardnesspenetration (Case depth)
The depth of hardness penetration depends on the carbon content of the
carburized layer. Provided only martensite is formed in the case on quenching, the depth
of case hardening would be equivalent to a depth of carbon penetration down to 0.40% C.
This would agree well for small parts but as the section dimensions increase, the rate of
cooling decreases and hence the conditions necessary for the formation of martensite are
changed. This implies that steel components of different sizes but which have the same
depth of carbon penetration obtain a casehardening depth that is dependent on the
dimensions of the piece (Beurnelburg, W., 1964).
Surface hardness
The carbon dissolved in the austenite is the decisive factor determining surface
hardness. When the carbon concentration at the surface of conventional alloy case-
hardening steels exceeds 0.70%, the M, temperature falls steeply, the amount of retained
austenite after quenching increases and the hardness decreases. If the surface layer of the
steel contains the appropriate concentration of carbon for maximum hardness, the
quenching temperature is of minor importance to the hardness provided that the grain size
is not altered. By varying the quenching temperature of an 'over-carburized' steel it is
possible to control the amount of carbon going into solution and hence the amount of
retained austenite which, in turn, affects the hardness (Robinson, G.H., 1957).
Fatigue strength of case-hardened steel
By and large, the increase in fatigue strength brought about by case hardening is
proportional to the hardness increase in the surface zone. It is also dependent on the
compressive stresses in this zone. The maximum fatigue strength value is obtained when
the carbon is about 0.6%. Most fatigue strength investigations of case-hardening steels
show that optimum properties are obtained when the surface carbon content is 0.6-0.8%
and the surface hardness at least 700HV (Diesburg, D.E., et a1.,1978).
ASM (Metals Handbook: Heat Treating, 1981) suggested the following general
heat-treatment recommendations for casehardening steels. The treatment is designed to
give a surface hardness of atleast 60 HRC or 7 10 HV after quenching.
Carburizing in solid compound (pack carburizing) - Temperature: 900-925OC
When direct quenching is employed, a carburizing temperature of 900°C is
recommended. If a casehardening depth of more than 1.25 mm is aimed at, it might be a
good practice to perform the traditional practice of a double quench, i.e. a first quench
from about 880°C and then a final quench. During the first heating for quenching, the
carbon concentration is reduced by diffusion. In addition, it breaks up and dissolves the
carbide network that usually forms when pack carburizing is used to give a deep carbon
penetration.
Depth of Case hardening in mm < 0.50 0.50 - 1.25 < 1.25
Method of hardening Direct Quench Single quench from 800 to 820°C Double quench
Carburidcing in a salt bath (liquid bath carburizing)-Temperature: 850-900°C
Depth of Case hardening in mrn Method of hardening I Direct - Quench I
For direct quenching, a carburizing temperature of 8 50-870°C is recommended; for
0.50 - 1.00
double quenching, 900°C may be used.
Requench fAm 800 to 820°C (Double quench)
Carburizing in gas (Gas carb urizing)-Temperature: 900-940°C
The carburization is carried out to the required depth of case hardening and to a
surface carbon concentration of 0.70-0.80%. When the process is completed, the
temperature in the h a c e is lowered to 83Q°C and the part is quenched in a suitable
medium.
Case-hardened steels are tempered at temperatures generally around 1 60-220°C.
Temperatures below 160°C should not be used, particularly if a grinding operation is to
follow, since grinding cracks develop very easily. The hardness falls quite rapidly when
the steel is tempered between 160°C and 200°C. If a hardness of 60HRC is required, the
tempering temperature should not be higher than 1 80°C (TheIning, 1984).
1.1.4 Induction hardening
When electric current passes through a conductor, a magnetic field is created
round it. If the conductor consists of a coil, a magnetic field is established inside the coil.
This field persists even if a metal ba is inserted into the coil, as shown in Figure 1.2. If
the magnetic flux is created by a high-frequency alternating current, it gives rise to eddy
currents in the surface of the metal bar, which consequently becomes heated (Figurel.3).
In iron, hysteresis losses also contribute to some extent to the temperature rise upto to the
Curie point (768'C), above which iron is non-magnetic (Semiatin S.L., and Stutz, D .E.,
1986)
The depth of penetration of the heat is governed mainly by the power and
frequency employed. The normal power input is 0.1 - 2kw/cm2 of the heated surface.
The relationship between depth of penetration and frequency can be calculated
approximately by using the following simplified expressions, which are valid for the
temperature rise in steel upto the hardening temperature:
= 20/ f cold state (20°C)
dh= 5001 fhot state (800°C)
Where, d, and dh = depth of penetration in mm, suffices, c and h represents the
cold and hot state conditions.
f- frequency in cycles per sec (Hz)
Owing to heat conduction in the material during heating, the overall depth of
penetration is larger. It is possible to calculate the additional penetration due to heat
conduction from the following expression.
dl = 0.2 t
where dl = depth of penetration in mm
t = time in seconds
Figure 1.2 Path of magnetic flux through a metal bar inserted in a coil
through which an electric current is flowing
1 0
Figure 1.3 Path of the electrical current in the coil and metal bar during
Induction hardening
The total depth of penetration is obviously c& ordh+ dl, It should be stressed that
these expressions give only a rough estimate of the depth of penetration and they have
been included here only to show the fbndamental effects of frequency and time
(Osborn, H.B., 1955).
Working coils and fixtures
The coils, also known as inductors, also got heated by the electric current and by
thermal radiation fiom the heated steel. The coils are often made from copper tubing and
are cooled during operation by internal water flow. Figure 1.4 shows three basic types of
working coils designed for external and internal heating, and for heating of a flat surface.
The internal diameter of the copper tube is matched to suit generator power
output. For the power output normally required, around 50kW, tubing with an internal
diameter of around 5mm is used. The coils are usually wound with a distance of 2-5mm
between turns and with roughly the same spacing between the coil and the workpiece.
By varying this distance, it is possible to influence the rate of heating to a very large
extent.
Parts that are to be hardened must be held in a fixture of some sort so that they are
correctly located in the inductor. Small components must be f m l y held so that they are
not displaced by the magnetic filed. A metallic fixture that comes near the coil may
become heated by the induced current. To avoid this fixture and centre washers are
normally made from an insulating and heat-resistant material such as 'sindango' or a
heat-resistant plastic (KatsuyuM Matsui, et al., 1998).
External Internal Surface
Figure 1.4 Types of coil used for Induction hardening
The influence of various factors on hardness and depth of hardening
The carbon content has a decisive influence on hardness after hardening. As the
carbon content increases, upto to about 0.80% the hardenability also increases,
particularly when in combination with other alloying elements. Both the hardening
temperature and holding time are decisive factors that govern the hardness and depth of
hardening. For induction hardening with conditions otherwise remaining, the same the
depth of hardening i s governed by the fkquency of the inductive current. Since the
hardening temperature, heating time and holding time can be controlled relatively easily
dwing induction hardening, it is possible with this method to determine in advance the
required hardness depth with a relatively high degree of certainty by using calculated and
empirical values (Rudnev.V., and Demidovich, V., 1997).
The hardening temperatures employed for induction hardening are normally some
50°C higher than those used for conventional hardening. The holding times are
extremely short. In many cases, there is no holding time, i.e. cooling starts directly when
the desired temperature has been reached. Temperatures are normally controlled by
means of optical pyrometers (Siedel, W., and Netz, W., 1982).
The pressure of the cooling medium and the angle of incidence of the jet as well
as its width are o f paramount importance to the intensity o f cooling. Hence, these factors
influence the depth of hardening and the hardening itself. Kegel and Pennekamp (1974)
arrived at the following recommendations based on experiments and theoretical
calculations of the coefficient of heat transfer through the vapour film:
Pressure 1-3 bas
Angle o f incidence 20-30'
Width of slit 0.8 -1.2 mm, preferably 0.9 -1.0 mm
Usually the spray nozzle contains a number of holes, the diameters of which are
taken as equivalent to the slit width of the above recommendations.
1.1.5 Material Testing and Inspection
Testing of material is one o f the important and essential steps for judging
suitability for engineering applications after heat treatment. Most of the properties of
interest are mechanical properties since heat treatment essentially alters mechanical
properties. This section i s confined to the testing o f mechanical properties; non-
destructive methods of testing materials have also been included, as they constitute an
important aspect of testing heat treated components (Testing of Materials ASTM, 1970:
Raval, B.M., 1995). Many tests and testing methods are in use now-a-days.
Vickers Hardness Test
Vickers hardness test is also referred to as Vickers Diamond Pyramid test. The
indenter used in this test is a square base diamond pyramid. The included angle between
opposite faces of the pyramid is 136". The loads generally employed in this test vary
fiom ikg to 120kg, depending on the hardness of the material under test. Therefore, at
varying loads, the same indenter can be used for the measurement of hardness of a
number of metals and alloys. Due to the accuracy associated with this test, it is generally
used for research and high precision work.
Microhardness testing can be defined as indentation hardness testing it involves
forcing a diamond indenter of specific geometry into the surface o f the test material at
loads ranging from 1 to 1000kgf (Andrew, et al., 1995).
In Vickers microhardness testing, the hardness value is determined by measuring
the size of the resulting indentation by using a microscope and established formula.
The microhardness test uses preciously shaped diamond indenter and various load
ranges to determine the hardness variety of the material. The specific application for
microhardness includes.
1 Measuring hardness of precision work-pieces that are too small to be
measured by conventional macroscopic hardness testing methods.
2 Monitoring of carburizing or nitriding operations, this i s usually accomplished
by hardness surveys taken on cross sections of test pieces that accompanied
the work-pieces through production operations.
3 Measuring hardness of individual micro constituents and hardness close to
edges, thus detecting undesirable surface conditions such as grinding bum and
decarburization.
Figure 1.5 Diamond pyramid indenter used for the Vickers Hardness
test and resulting indentation in the work- piece
The Vickers indenter is a highly polished, pointed, square-b ased pyramidal
diamond with face angles of 136' C (Figure 1.5). With the Vickers indenter, the depth of
indentation is about one seventh of the diagonal length. The Vickers hardness number
(VHN) is the ratio of the load applied to the indenter to the surface area of the
indentation;
VHN=2Psin ( 0 / 2 ) l ~ *
Where,
P - Applied load, (kg9
D - Mean diagonal o f the indentation, (mm) and
0 - Angle between opposite faces of the diamond, 136'
Rockwell hardness test
This test differs from both the Brine11 and Vickers tests in the sense that here the
depth of penetration, and not the surface area, is used as the parameter for arriving at the
hardness value. It works on the principle that the depth of penetration varies with the
hardness o f material. The higher the hardness, smaller will be depth of penetration and
vice versa. In this depth of penetration is not measured. Instead of that, the hardness
values can be read directly on a dial attached to the tester. Accuracy that can be
achieved by this test is not comparable to either Brine11 or Vickers hardness test.
However, the test is very popular in day-today industrial practice. There are two basic
reasons for this: Firstly, it is a fast process and, secondly, very small indentation is made
on the surface. Therefore, even finished parts can be subjected to this test.
Non-destructive Testing methods
A number of situations are encountered in day-to-day industrial practice where it
becomes necessary to study the flaws in metallic components without destroying them.
Under such circumstances, recourse is taken to non-destructive testing (NDT) technique.
This technique makes the use of the component more reliable, safe and economical,
Non-destructive testing has two important roles to play: (i) From these investigations, the
presence o f defects is established; (ii) it is also useful in estimating the nature and extent
of defects and amving at a conclusion about accepting or rejecting the product for service
(Dieter, G.E., 1986). Non-destructive tests also help in measuring the defect size and
distribution, which plays a crucial role in taking the final decision on accepting or
rejecting the component. A number of non-destructive tests are available now a days to
detect the flaws in metallic components. Some of these tests are Magnetic Particle