MME 345, Lecture 36
Cast Iron Foundry Practices3. Metallurgy of grey irons
Ref: Heine, Loper and Rosenthal. Principles of Metal Casting, Tata McGraw-Hill, 19670
Topics to discuss today …
1. Graphite morphology
2. Metastable nature of iron – iron carbide system
3. Solidification of Fe-C-Si alloy
4. Chemical composition effects
5. Properties of grey iron
6. Heat treatment of grey iron
Graphite Morphology
Shape
Size
Distribution
ASTM A247
ISO R-945
classification of graphite flake size and shape
The properties of grey iron castings are influenced by the shape
and distribution of the graphite flakes.
The standard method of defining graphite forms is based on the
system proposed by the American Society for the Testing of Metals,
ASTM Specification A247, which classifies the form, distribution
and size of the graphite.
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Summary and description of ASTM and equivalent
ISO classification of graphite shapes
ASTM
Type(a)
Equivalent
ISO Form(b) Description
I VI Nodular (spheroidal) graphite
II VI Nodular (spheroidal) graphite, imperfectly formed
III IV Aggregate, or temper carbon
IV III Quasi-flake graphite
V II Crab-form graphite
VI(c) I Flake graphite
(a) As defined in ASTM A 247;
(b) As defined in ISO/R 945-1969 (E);
(c) Divided into five subtypes base on graphite distribution; uniform flakes; rosette grouping;
superimposed flake size; interdendritic, random orientation; and interdendritic, preferred orientation.
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reference diagrams for different graphite form / shape as specified in ISO/R 945
Six forms:
I flake graphite
II crab-form graphite
III quasi-flake graphite
IV aggregate or tempered carbon
V nodular graphite, imperfectly formed
VI nodular graphite
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longest flakes 4 in.
or more in lengthlongest flakes 1 to 2 in.
in length
longest flakes 2 to 4 in.
in length
longest flakes 1/2 to 1 in.
in length
longest flakes 1/4 to 1/2 in.
in length
longest flakes 1/16 to 1/8 in.
in length
longest flakes 1/8 to 1/4 in.
in length
longest flakes 1/16 in.
or less in length
graphite flake sizes as specified in ASTM A247
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reference diagrams for the distribution of graphite (Form 1) as specified in ASTM A247
Type A: Random orientation, uniform distribution
The preferred type for engineering applications. This type of
graphite structure forms when a high degree of nucleation
exists in the liquid iron, promoting solidification close to the
equilibrium graphite eutectic.
Type B: Rosette grouping
The eutectic cell size is large because of the low degree of
nucleation. Fine flakes form at the centre of the rosette
because of undercooling, these coarsen as the structure
grows.
Type C: Superimposed flake sizes, random orientation
Structures occur in hypereutectic irons, where the first
graphite to form is primary kish graphite. It may reduce tensile
properties and cause pitting on machined surfaces.
Type D: Interdendritic segregation, random orientation
Type E: Interdendritic segregation, preferred orientation
Both are fine, undercooled graphites which form in rapidly
cooled irons having insufficient graphite nuclei. Although the
fine flakes increase the strength of the eutectic, this
morphology is undesirable because it prevents the formation
of a fully pearlitic matrix. Occurs in hypoeutectic alloys.
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chemical composition, structure and properties of grey iron vary over broad limits
range of alloy composition and properties produced are better understood by
considering grey iron metallurgy, particularly the metastable nature of iron carbide
The Metastable Nature of Fe-Fe3C System
iron carbide becomes unstable
1. in contact with graphite at elevated temperature
2. at prolonged exposure to high temperature
3. in presence of certain elements in the alloy
under normal conditions,
• a hypoeutectic Fe-C alloy (>4.3%C) freezes with austenite dendrite and ladeburite (austenite-carbide
eutectic), which at room temperature transform into pearlite dendrite and transformed ladebutite
(pearlite-carbide mixture)
• a eutectic Fe-C alloy consists only the transformed eutectic
conversely, nucleation of graphite is prevented and metastable carbide persisted if
1. the cooling is rapid
2. the alloy contains certain elements8/26
Solidification of Fe-C-Si Alloy
• presence of Si in the alloy is the single most
important composition factor that promote
graphitisation in grey iron
• Three important stages of graphitisation:
1. During solidification
2. By carbon precipitation from austenite (solid state)
3. During eutectoid transformation (solid state)
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Graphitisation During Solidification
• Size, shape and distribution of graphite flakes developed.
• Segregation, undercooling and rapid cooling promotes type D/E-type graphites.
• Suppression of eutectic freezing (by chilling for example) form white iron.
• Factors to consider: Section size, Superheat, Inoculation.
Section Size
• Large, randomly nucleated flakes (type A/B) low nucleation rate, slow cooling rate, rapid graphitization
• Small flakes moderate undercooling, moderate nucleation with still time for diffusion and graphitization
• No flakes (chilled / white iron) severe undercooling (prevents graphitization)
Superheating (heating liquid above 1510 C)
• Undercooling would most likely to occur
• Produce type D/E flakes
• Chill / mottled iron would also occur if not inoculate properly.
Inoculation (additions to molten iron)
• Produce marked change in graphite type by preventing undercooling
• The effect is the most pronounced when added to superheated liquid
• Only 0.05 – 0.25% FeSi or other graphitizing agent addition produces type A graphite10/26
Graphitisation in the Solid State
• On slow cooling, graphite precipitates on previously existing flakes.
• On very slow cooling, austenite completely transforms into ferrite and graphite.
• Fine graphite flakes (formed during freezing) promote solid-state graphitisation.
• The commercial practice is to retain 100% or some portion of pearlite
• Proper balance between Mn and S assists to obtain pearlitic structure even when
cooled in sand moulds
• Rapid solid-state cooling and presence of carbide-forming elements increase
retention of combined carbon
• Fine graphite flakes (developed during solidification), regardless of type,
promotes solid-state graphitisation
• The flakes serve as the precipitation centre for carbon
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Grade (BS 1452: 1990) 150 200 250 300 350
Total carbon, % 3.1 – 3.4 3.2 – 3.4 3.0 – 3.2 2.9 – 3.1 3.1 max.
Silicon, % 2.5 – 2.8 2.0 – 2.5 1.6 – 1.9 1.8 – 2.0 1.4 – 1.6
Manganese, % 0.5 – 0.7 0.6 – 0.8 0.5 – 0.7 0.5 – 0.7 0.6 – 0.75
Sulphur, % 0.15 0.15 0.15 max. 0.12 max. 0.12 max.
Phosphorous, % 0.9 – 1.2 0.1 – 0.5 0.3 max. 0.01 max. 0.10 max.
Molybdenum, % – – – 0.4 – 0.6 0.3 – 0.5
Copper or Nickel, % – – – – 1.0 – 1.5
cast iron compositions
Chemical Composition Effects
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• Mechanical-property specifications are usually considered far more important
than chemical specifications
• So, composition and foundry practice must be adjusted to obtained the desired
strength class of grey iron
Element Effect
Carbon • Reported as total carbon: % TC = % Graphitic C + % Combined C
• For graphitisation, TC must have a minimum value (2.2% , value depends on Si content)
Silicon • Shifts eutectic and eutectoid points to the left.
Eutectic %C = 4.3 - %Si / 3
CE = %C + %Si / 3
• Promote graphitisation after carbon; a certain minimum level of Si is necessary to cause
sufficient graphitisation during solidification and develop a satisfactory grey iron
• Low Si is not sufficient to causes graphitisation during solidification, but promote nucleation
and graphitisation at high temperature in the solid state (malleableisation treatment)
Sulphur and
Manganese
• Both act as carbide stabiliser; presence in low level will cause complete graphitisation
• S alone form FeS and segregates along grain boundary, but with Mn, form MnS and
precipitated throughout the matrix; the effect as carbide stabiliser is lost
• Relationship between S and Mn:
%Mn = 1.7 %S form MnS
%Mn = 1.7 %S + 0.15; Highest limit of Mn to promote ferrite & graphite
%Mn = 3.0 %S + 0.35; Lowest limit of Mn to develop 100% pearlite
Phosphorous • Forms steadite and segregated along grain boundary
• Forms iron – iron phosphide eutectic, thereby promoting eutectic formation
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Properties of Grey Irons
foundry properties
for several reasons, grey irons are among the most easily cast of all alloys
1. Pouring Temperature
• wide working temperature (1200 – 1700 °C)
• permits easy manipulation, re-ladling, adequate time for pouring
• typical pouring temperature: 1250 – 1550 °C
2. Shrinkage and Feeding
• favourable freezing mechanism and low shrinkage characteristics
• higher yield (60 – 70% or even higher)
• feeding is not always easy; some casting designs are easily cast
with commercially acceptable soundness with low CE value
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3. Fluidity
• most fluid of ferrous alloys;
intricate and thin sections can
be produced
• the eutectic composition has
the most fluidity
• the hypereutectic composition
suffers extreme loss of fluidity
due to graphite precipitation
Composition Factor (CF)
= %C + %Si / 4 + %P / 2
(for highest fluidity, CF = 4.55)
Fluidity (inch)
= 14.9 x CF + 0.05 T - 155
(T = pouring temperature in °F)
Fluidity related to pouring temperature and composition
of grey and malleable cast iron
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engineering properties
Country SpecificationDesig-
nation
Minimum Tensile Strength (MPa)
100 150 180 200 220 250 260 300 350 400
France NFA 32-101-1987 FGL 150 200 250 300 350 400
Germany DIN 1691 -1985 GC 10 15 20 25 30 35
India IS 210 -1978 FG 150 200 250 300 350 400
Italy UNI 5007 -1969 G 10 15 20 25 30 35
Japan JIS G5501-1989FC 100 150 200 250 300 350
Class 1 2 3 4 5 6
Netherlands GOST 1412 -1979 Sch 10 15 18 20 25 30 35 40
UK BS 1452 1990 Grade 100 150 180 200 220 250 300 350
USA ANS/ASTM A48-83 Grade 20A 25A 30A 35A 40A 45A 50A 60A
International ISO 185 -1988 Grade 100 150 200 250 300 350
Equivalent Tonf/in2 6.5 9.7 12.9 16.2 19.4 22.7
Specification of grey irons
Grade 150 200 250 300 350 400
BHN (10/3000) 136 – 167 159 – 194 180 – 222 202 – 247 227 – 278 251 – 307
Hardness ranges for grades of grey iron
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from metallurgical standpoint, grey irons are viewed as
microstructurally-sensitive alloys
microstructure, chemical composition and mechanical properties
are intimately related
the processing parameters that influence structure, chemical
composition variations and cooling rate also influence properties
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relationship between tensile strength and
carbon equivalent value for various bar diameters
composition and structure effect
tensile strength of 1.20-in.-diameter gray-iron
bars as affected by carbon equivalent.
• C and Si are the most important composition factors
affecting mechanical properties
• maximum strength obtained with a pearlitic matrix
• maximum limit of strength by decreasing CE value is about
45000 psi; higher strength requires special alloy additions
• type A graphite produces maximum strength
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• Addition of alloying elements has two effects:
1. effect on microstructure, metal matrix, and graphitisation process
2. effect on properties (increased strength, resistances to wear, corrosion, oxidation/scaling and abrasion)
relationship between section size, CE value and structure
cooling rate (section size)
• effect of cooling rate on
properties is profound because
of its influence on microstructure
• rapid cooling increased
hardness and tensile strength
(as long as no white or chilled
iron or D-type graphite is
produced)
• slow cooling coarsening of
graphite flakes and lamellar
pearlite and appearance of ferrite,
causing softening and weakening
of grey iron with reduced wear
resistance
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variation of tensile strength with section thickness for several grades of iron
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dependence of grey iron properties on section thickness
• thin section casting has the possibility of
misruns and chilled iron surface or hard spot
• so, certain minimum section thicknesses are
desirable in grey iron castings
ASTM
Class Iron
Suggested Wall Thickness,
min. (inch)
20 1/8
25 1/4
30 3/8
35 3/8
40 5/8
50 1/2
60 3/4
summary of relationships of CE, section size and properties of unalloyed grey iron24/26
Heat Treatment of Grey Irons
Since grey irons may be heated to austenite zone, heat treatments
similar to steels can be applied
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Principal purposes to heat treat grey irons:
1. improve machinability – sub-critical annealing to 650-675°C for 2-4 hrs, followed by
slow cooling; spherodisation of pearlite with some graphitisation
2. improve wear resistance – hardening at 900-925°C, followed by oil or water
quenching and then tempering to suit the need
3. improve strength – rarely used; hardening followed by tempering at 425-535°C
produces optimum tensile strength; may cause warpage or cracking
4. dimensional stability and stress relief – often desirable; annealing or normalising
can be used; a specific stress-relief anneal consists in heating to 480-595°C for 1 hr or
more, followed by slow cooling
Next ClassMME 345, Lecture 37
Cast Iron Foundry Practices4. Grey irons foundry practice