the science and engineering of materials -...
TRANSCRIPT
12/22/2008١Chapter 3 -
The Science and Engineering of Materials
W. CallisterR. Askeland
P. Phulé
S. M. RabieePhD in Biomedical Materials Engineering
&
Assistant Professor in Department Of Mechanical Engineering
Babol (Noshirvani) University Of Technology
٢Chapter 3 -
o What is Materials Science and Engineering?o Classification of Materialso Functional Classification of Materialso Classification of Materials Based on Structureo Environmental and Other Effectso Materials Design and Selection
Introduction to Materials Science and Engineering
٣Chapter 3 -
What is Materials Science and Engineering?
o Materials Science and Engineeringo Composition means the chemical make-up of a
material.o Structure means a description of the arrangements
of atoms or ions in a material.o Synthesis is the process by which materials are
made from naturally occurring or other chemicals.o Processing means different ways for shaping
materials into useful components or changing their properties.
٤Chapter 3 -
Classification of Materials
q Metals and Alloysq Ceramics, Glasses,and Glass-ceramicsq Polymers (plastics), Thermoplastics and Thermosetsq Composite Materials
٥Chapter 3 -
Types of Materials• Metals:
– Strong, ductile– high thermal & electrical conductivity– opaque, reflective.
• Polymers: Covalent bonding à sharing of e’s– Soft, ductile, low strength, low density– thermal & electrical insulators– Optically translucent or transparent.
• Ceramics: ionic bonding (refractory) –compounds of metallic & non-metallic elements (oxides, carbides, nitrides, sulfides)– Brittle, glassy, elastic– non-conducting (insulators)
٦Chapter 3 -
©2003 B
rooks/Cole Publishing / Thom
son Learning™
Figure : Representative strengths of various categories of materials
٧Chapter 3 -
Functional Classification of Materials
q Aerospaceq Biomedicalq Electronic Materialsq Energy Technology and Environmental Technologyq Magnetic Materialsq Photonic or Optical Materialsq Smart Materialsq Structural Materials
٨Chapter 3 -
©2003 B
rooks/Cole Publishing / Thom
son Learning™
Figure: Functional classification of materials. Notice that metals, plastics, and ceramics occur in different categories. A limited number of examples in each category is provided
٩Chapter 3 -
Example of Biomedical Material – Hip Implant
Adapted from Fig. 22.26, Callister 7e.
١٠Chapter 3 -
Hip Implant• Key problems to overcome
– fixation agent to hold acetabular cup
– cup lubrication material– femoral stem – fixing agent
(“glue”)– must avoid any debris in cup
Adapted from chapter-opening photograph, Chapter 22, Callister 7e.
Femoral Stem
Ball
AcetabularCup and Liner
١١Chapter 3 -
Classification of Materials-Based on Structure
q Crystalline material is a material comprised of one or many crystals. In each crystal, atoms or ions show a long-range periodic arrangement.q Single crystal is a crystalline material that is made of only one crystal (there are no grain boundaries).q Grains are the crystals in a polycrystalline material.q Polycrystalline material is a material comprised of many crystals (as opposed to a single-crystal material that has only one crystal).q Grain boundaries are regions between grains of a polycrystalline material.
١٢Chapter 3 -
Environmental and Other Effects
Effects of following factors must be accounted for in design to ensure that components do not fail unexpectedly:
q Temperature q Corrosionq Fatigueq Strain Rate
١٣Chapter 3 -
Materials Design and Selection
q Density is mass per unit volume of a material, usually expressed in units of g/cm3 or lb/in.3q Strength-to-weight ratio is the strength of a material divided by its density; materials with a high strength-to-weight ratio are strong but lightweight.
١٤Chapter 3 -
• Use the right material for the job.
• Understand the relation between properties,structure, and processing.
• Recognize new design opportunities offeredby materials selection.
Course Goals:SUMMARY
١٥Chapter 3 -
ISSUES TO ADDRESS...
• What promotes bonding?
• What types of bonds are there?
• What properties are inferred from bonding?
BONDING AND PROPERTIES
١٦Chapter 3 -
Atomic Structure • atom – electrons – 9.11 x 10-31 kg
protonsneutrons
• atomic number = # of protons in nucleus of atom= # of electrons of neutral species
• A [=] atomic mass unit = amuAtomic wt = wt of 6.023 x 1023 molecules or atoms
1 amu/atom = 1g/mol
C 12.011H 1.008 etc.
} 1.67 x 10-27 kg
١٧Chapter 3 -
Calculate the number of atoms in 100 g of silver.
Example SOLUTION
The number of silver atoms is =)868.107(
)10023.6)(100( 23
molg
molatomsg ×
=5.58 × 1023
Example :Calculate the Number of Atoms in Silver
١٨Chapter 3 -
Atomic Structure
• Valence electrons determine all of the following properties
1) Chemical2) Electrical 3) Thermal4) Optical
١٩Chapter 3 -
Electronic Structure• Electrons have wavelike and particulate
properties. – This means that electrons are in orbitals defined by a
probability.– Each orbital at discrete energy level determined by
quantum numbers.
Quantum # Designationn = principal (energy level-shell) K, L, M, N, O (1, 2, 3, etc.)l = subsidiary (orbitals) s, p, d, f (0, 1, 2, 3,…, n-1)ml = magnetic 1, 3, 5, 7 (-l to +l)
ms = spin ½, -½
٢٠Chapter 3 -
©2003 B
rooks/Cole Publishing / Thom
son Learning™
Figure:The atomic structure of sodium, atomic number 11, showing the electrons in the K, L, and M quantum shells
٢١Chapter 3 -
©2003 B
rooks/Cole Publishing / Thom
son Learning™
Figure : The complete set of quantum numbers for each of the 11 electrons in sodium
٢٢Chapter 3 -
• Most elements: Electron configuration not stable.SURVEY OF ELEMENTS
Electron configuration
(stable)
...
... 1s 22s22p 63s23p 6 (stable)... 1s 22s22p 63s23p 63d 10 4s24p 6 (stable)
Atomic #
18...36
Element1s 11Hydrogen1s 22Helium1s 22s13Lithium1s 22s24Beryllium1s 22s22p 15Boron1s 22s22p 26Carbon
...1s 22s22p 6 (stable)10Neon1s 22s22p 63s111Sodium1s 22s22p 63s212Magnesium1s 22s22p 63s23p 113Aluminum
...Argon...Krypton
٢٣Chapter 3 -
Electron Configurations• Valence electrons – those in unfilled shells• Filled shells more stable• Valence electrons are most available for
bonding and tend to control the chemical properties
– example: C (atomic number = 6)
1s2 2s2 2p2
valence electrons
٢٤Chapter 3 -
Ionic bond – metal + nonmetal
donates acceptselectrons electrons
Dissimilar electronegativities
ex: MgO Mg 1s2 2s2 2p6 3s2 O 1s2 2s2 2p4
[Ne] 3s2
Mg2+ 1s2 2s2 2p6 O2- 1s2 2s2 2p6
[Ne] [Ne]
٢٥Chapter 3 -
• Occurs between + and - ions.• Requires electron transfer.• Large difference in electronegativity required.• Example: NaCl
Ionic Bonding
Na (metal) unstable
Cl (nonmetal) unstable
electron
+ -CoulombicAttraction
Na (cation) stable
Cl (anion) stable
٢٦Chapter 3 -
Ionic Bonding• Energy – minimum energy most stable
– Energy balance of attractive and repulsive terms
Attractive energy EA
Net energy EN
Repulsive energy ER
Interatomic separation r
Adapted from Fig. 2.8(b), Callister 7e.
EN = EA + ER
٢٧Chapter 3 -
• Predominant bonding in Ceramics
Adapted from Fig. 2.7, Callister 7e. (Fig. 2.7 is adapted from Linus Pauling, The Nature of the Chemical Bond, 3rd edition, Copyright 1939 and 1940, 3rd edition. Copyright 1960 by Cornell University.
Examples: Ionic Bonding
Give up electrons Acquire electrons
NaClMgOCaF2CsCl
٢٨Chapter 3 -
C: has 4 valence e-,needs 4 more
H: has 1 valence e-,needs 1 more
Electronegativitiesare comparable.
Adapted from Fig. 2.10, Callister 7e.
Covalent Bonding• similar electronegativity ∴ share electrons• bonds determined by valence – s & p orbitals
dominate bonding• Example: CH4
shared electrons from carbon atom
shared electrons from hydrogen atoms
H
H
H
H
C
CH4
٢٩Chapter 3 -
Primary Bonding• Metallic Bond -- delocalized as electron cloud
• Ionic-Covalent Mixed Bonding
% ionic character =
where XA & XB are Pauling electronegativities
%)100(x
1− e− (X A−XB )2
4
ionic 70.2% (100%) x e1 characterionic % 4)3.15.3( 2
=
−=
−−
Ex: MgO XMg = 1.3XO = 3.5
٣٠Chapter 3 -
Arises from interaction between dipoles
• Permanent dipoles-molecule induced
• Fluctuating dipoles
-general case:
-ex: liquid HCl
Adapted from Fig. 2.13, Callister 7e.
Adapted from Fig. 2.14,Callister 7e.
SECONDARY BONDING
asymmetric electronclouds
+ - + -secondary bonding
HH HH
H2 H2
secondary bonding
ex: liquid H2
H Cl H Clsecondary bonding
secondary bonding+ - + -
٣١Chapter 3 -
TypeIonic
Covalent
Metallic
Bond EnergyLarge!
Variablelarge-Diamondsmall-Bismuth
Variablelarge-Tungstensmall-Mercury
CommentsNondirectional (ceramics)
Directional(semiconductors, ceramicspolymer chains)
Nondirectional (metals)
Summary: Bonding
٣٢Chapter 3 -
Ceramics(Ionic & covalent bonding):
Metals(Metallic bonding):
Polymers(Covalent & Secondary):
Large bond energylarge Tmlarge Esmall α
Variable bond energymoderate Tmmoderate Emoderate α
Directional PropertiesSecondary bonding dominates
small Tmsmall Elarge α
Summary: Primary Bonds
٣٣Chapter 3 -
ISSUES TO ADDRESS...
• How do atoms assemble into solid structures?(for now, focus on metals)
• How does the density of a material depend onits structure?
• When do material properties vary with thesample (i.e., part) orientation?
The Structure of Crystalline Solids
٣٤Chapter 3 -
• atoms pack in periodic, 3D arraysCrystalline materials...
-metals-many ceramics-some polymers
• atoms have no periodic packingNoncrystalline materials...
-complex structures-rapid cooling
crystalline SiO2
noncrystalline SiO2"Amorphous" = NoncrystallineAdapted from Fig. 3.22(b),Callister 7e.
Adapted from Fig. 3.22(a),Callister 7e.
Materials and Packing
Si Oxygen
• typical of:
• occurs for:
٣٥Chapter 3 -
Crystal Systems
7 crystal systems
14 crystal lattices
Unit cell: smallest repetitive volume which contains the complete lattice pattern of a crystal.
a, b, and c are the lattice constants
٣٦Chapter 3 -
Metallic Crystal Structures• How can we stack metal atoms to minimize
empty space?2-dimensions
vs.
Now stack these 2-D layers to make 3-D structures
٣٧Chapter 3 -
• Tend to be densely packed.• Reasons for dense packing:
- Typically, only one element is present, so all atomicradii are the same.
- Metallic bonding is not directional.- Nearest neighbor distances tend to be small in
order to lower bond energy.- Electron cloud shields cores from each other
• Have the simplest crystal structures.
We will examine three such structures...
Metallic Crystal Structures
٣٨Chapter 3 -
• Rare due to low packing denisty (only Po has this structure)• Close-packed directions are cube edges.
• Coordination # = 6(# nearest neighbors)
(Courtesy P.M. Anderson)
Simple Cubic Structure (SC)
٣٩Chapter 3 -
• APF for a simple cubic structure = 0.52
APF = a3
43
π (0.5a) 31atoms
unit cellatom
volume
unit cellvolume
Atomic Packing Factor (APF)
APF = Volume of atoms in unit cell*
Volume of unit cell
*assume hard spheres
Adapted from Fig. 3.23,Callister 7e.
close-packed directions
a
R=0.5a
contains 8 x 1/8 = 1 atom/unit cell
٤٠Chapter 3 -
• Coordination # = 8
Adapted from Fig. 3.2,Callister 7e.
(Courtesy P.M. Anderson)
• Atoms touch each other along cube diagonals.--Note: All atoms are identical; the center atom is shaded
differently only for ease of viewing.
Body Centered Cubic Structure (BCC)
ex: Cr, W, Fe (α), Tantalum, Molybdenum
2 atoms/unit cell: 1 center + 8 corners x 1/8
٤١Chapter 3 -
Atomic Packing Factor: BCC
a
APF =
43
π ( 3a/4)32atoms
unit cell atomvolume
a3unit cellvolume
length = 4R =Close-packed directions:
3 a
• APF for a body-centered cubic structure = 0.68
aR
Adapted from Fig. 3.2(a), Callister 7e.
a2
a3
٤٢Chapter 3 -
• Coordination # = 12
Adapted from Fig. 3.1, Callister 7e.
(Courtesy P.M. Anderson)
• Atoms touch each other along face diagonals.--Note: All atoms are identical; the face-centered atoms are shaded
differently only for ease of viewing.
Face Centered Cubic Structure (FCC)
ex: Al, Cu, Au, Pb, Ni, Pt, Ag
4 atoms/unit cell: 6 face x 1/2 + 8 corners x 1/8
٤٣Chapter 3 -
• APF for a face-centered cubic structure = 0.74Atomic Packing Factor: FCC
maximum achievable APF
APF =
43
π ( 2a/4)34atoms
unit cell atomvolume
a3unit cellvolume
Close-packed directions: length = 4R = 2 a
Unit cell contains:6 x1/2 + 8 x1/8
= 4 atoms/unit cella
2 a
Adapted fromFig. 3.1(a),Callister 7e.
٤٤Chapter 3 -
A sites
B B
B
BB
B B
C sites
C C
CAB
B sites
• ABCABC... Stacking Sequence• 2D Projection
• FCC Unit Cell
FCC Stacking Sequence
B B
B
BB
B B
B sitesC C
CAC C
CA
AB
C
٤٥Chapter 3 -
• Coordination # = 12
• ABAB... Stacking Sequence
• APF = 0.74
• 3D Projection • 2D Projection
Adapted from Fig. 3.3(a),Callister 7e.
Hexagonal Close-Packed Structure (HCP)
6 atoms/unit cell
ex: Cd, Mg, Ti, Zn
• c/a = 1.633
c
a
A sites
B sites
A sites Bottom layer
Middle layer
Top layer
٤٦Chapter 3 -
Theoretical Density, ρ
where n = number of atoms/unit cellA = atomic weight VC = Volume of unit cell = a3 for cubicNA = Avogadro’s number
= 6.023 x 1023 atoms/mol
Density = ρ =
VCNA
n Aρ =
CellUnitofVolumeTotalCellUnitinAtomsofMass
٤٧Chapter 3 -
• Ex: Cr (BCC) A = 52.00 g/molR = 0.125 nmn = 2
ρtheoretical
a = 4R/ 3 = 0.2887 nm
ρactual
aR
ρ = a3
52.002atoms
unit cell molg
unit cellvolume atoms
mol
6.023 x1023
Theoretical Density, ρ
= 7.18 g/cm3
= 7.19 g/cm3
٤٨Chapter 3 -
Densities of Material Classesρmetals > ρceramics > ρpolymers
Why?
Data from Table B1, Callister 7e.
ρ(g
/cm
)3
Graphite/ Ceramics/ Semicond
Metals/ Alloys
Composites/ fibersPolymers
1
2
20
30Based on data in Table B1, Callister
*GFRE, CFRE, & AFRE are Glass,Carbon, & Aramid Fiber-ReinforcedEpoxy composites (values based on60% volume fraction of aligned fibers
in an epoxy matrix).10
345
0.30.40.5
Magnesium
Aluminum
Steels
Titanium
Cu,NiTin, Zinc
Silver, Mo
TantalumGold, WPlatinum
GraphiteSiliconGlass -sodaConcrete
Si nitrideDiamondAl oxide
Zirconia
HDPE, PSPP, LDPEPC
PTFE
PETPVCSilicone
Wood
AFRE*CFRE*GFRE*Glass fibers
Carbon fibersAramid fibers
Metals have...• close-packing
(metallic bonding)• often large atomic masses
Ceramics have...• less dense packing• often lighter elements
Polymers have...• low packing density
(often amorphous)• lighter elements (C,H,O)
Composites have...• intermediate values
In general
٤٩Chapter 3 -
Figure: Coordinates of selected points in the unit cell. The number refers to the distance from the origin in terms of lattice parameters.
٥٠Chapter 3 -
Crystallographic Directions
1. Vector repositioned (if necessary) to pass through origin.
2. Read off projections in terms of unit cell dimensions a, b, and c
3. Adjust to smallest integer values4. Enclose in square brackets, no commas
[uvw]
ex: 1, 0, ½ => 2, 0, 1 => [ 201 ]
-1, 1, 1
families of directions <uvw>
z
x
Algorithm
where overbar represents a negative index
[ 111 ]=>
y
٥١Chapter 3 -
Determine the Miller indices of directions A, B, and Cin Figure
Example: Determining Miller Indices of Directions
(c) 2003 Brooks/Cole Publishing / Thomson Learning™
Figure . Crystallographic directions and coordinates
٥٢Chapter 3 -
(c) 2003 Brooks/Cole Publishing / Thomson Learning™
Figure . Equivalency of crystallographic directions of a form in cubic systems.
٥٣Chapter 3 -
٥٤Chapter 3 -
ex: linear density of Al in [110] direction
a = 0.405 nm
Linear Density• Linear Density of Atoms ≡ LD =
a
[110]
Unit length of direction vectorNumber of atoms
# atoms
length
13.5 nma2
2LD −==
٥٥Chapter 3 -
HCP Crystallographic Directions
1. Vector repositioned (if necessary) to pass through origin.
2. Read off projections in terms of unitcell dimensions a1, a2, a3, or c
3. Adjust to smallest integer values4. Enclose in square brackets, no commas
[uvtw]
[ 1120 ]ex: ½, ½, -1, 0 =>
Adapted from Fig. 3.8(a), Callister 7e.
dashed red lines indicate projections onto a1 and a2 axes a1
a2
a3
-a32
a2
2a1
-a3
a1
a2
zAlgorithm
٥٦Chapter 3 -
HCP Crystallographic Directions• Hexagonal Crystals
– 4 parameter Miller-Bravais lattice coordinates are related to the direction indices (i.e., u'v'w') as follows.
=
=
=
'wwt
v
u
)vu( +-
)'u'v2(31 -
)'v'u2(31 -=
]uvtw[]'w'v'u[ →
Fig. 3.8(a), Callister 7e.
-a3
a1
a2
z
٥٧Chapter 3 -
Crystallographic Planes• Miller Indices: Reciprocals of the (three) axial
intercepts for a plane, cleared of fractions & common multiples. All parallel planes have same Miller indices.
• Algorithm1. Read off intercepts of plane with axes in
terms of a, b, c2. Take reciprocals of intercepts3. Reduce to smallest integer values4. Enclose in parentheses, no
commas i.e., (hkl)
٥٨Chapter 3 -
Determine the Miller indices of planes A, B, and C in Figure
Example: Determining Miller Indices of Planes
(c) 2003 Brooks/Cole Publishing / Thomson Learning™
Figure . Crystallographic planes and intercepts
٥٩Chapter 3 -
SOLUTIONPlane A1. x = 1, y = 1, z = 12.1/x = 1, 1/y = 1,1 /z = 13. No fractions to clear4. (111)Plane B
1. The plane never intercepts the z axis, so x = 1, y = 2, and z = 2.1/x = 1, 1/y =1/2, 1/z = 03. Clear fractions:1/x = 2, 1/y = 1, 1/z = 04. (210)Plane C
1. We must move the origin, since the plane passes through 0, 0, 0. Let’s move the origin one lattice parameter in the y-direction. Then, x = , y = -1, and z =2.1/x = 0, 1/y = 1, 1/z = 03. No fractions to clear.
)010( .4
∞
∞∞
٦٠Chapter 3 -
Crystallographic Planesz
x
ya b
c
4. Miller Indices (110)
example a b cz
x
ya b
c
4. Miller Indices (100)
1. Intercepts 1 1 ∞2. Reciprocals 1/1 1/1 1/∞
1 1 03. Reduction 1 1 0
1. Intercepts 1/2 ∞ ∞2. Reciprocals 1/½ 1/∞ 1/∞
2 0 03. Reduction 2 0 0
example a b c
٦١Chapter 3 -
Crystallographic Planesz
x
ya b
c•
••
4. Miller Indices (634)
example1. Intercepts 1/2 1 3/4
a b c
2. Reciprocals 1/½ 1/1 1/¾2 1 4/3
3. Reduction 6 3 4
(001)(010),
Family of Planes {hkl}
(100), (010),(001),Ex: {100} = (100),
٦٢Chapter 3 -
Crystallographic Planes (HCP)• In hexagonal unit cells the same idea is used
example a1 a2 a3 c
4. Miller-Bravais Indices (1011)
1. Intercepts 1 ∞ -1 12. Reciprocals 1 1/∞
1 0 -1-1
11
3. Reduction 1 0 -1 1
a2
a3
a1
z
Adapted from Callister 7e.
٦٣Chapter 3 -
Example:Drawing Direction and Plane
Draw (a) the direction and (b) the plane in a cubic unit cell.
1]2[1 10]2[
(c) 2003 Brooks/Cole Publishing / Thomson Learning™
Figure Construction of a (a) direction and (b) plane within a unit cell
٦٤Chapter 3 -
SOLUTION
a. Because we know that we will need to move in the negative y-direction, let’s locate the origin at 0, +1, 0. The ‘‘tail’’ of the direction will be located at this new origin. A second point on the direction can be determined by moving +1 in the x-direction, 2 in the y-direction, and +1 in the z direction [Figure 3.24(a)].
b. To draw in the plane, first take reciprocals of the indices to obtain the intercepts, that is:
x = 1/-2 = -1/2 y = 1/1 = 1 z = 1/0 =
Since the x-intercept is in a negative direction, and we wish to draw the plane within the unit cell, let’s move the origin +1 in the x-direction to 1, 0, 0. Then we can locate the x-intercept at 1/2 and the y-intercept at +1. The plane will be parallel to the z-axis [Figure 3.24(b)].
10]2[
∞
٦٥Chapter 3 -
Determine the Miller-Bravais indices for planes A and B and directions C and D in Figure
Example: Determining the Miller-Bravais Indices for
Planes and Directions
(c) 2003 Brooks/Cole Publishing / Thomson Learning™
Figure 3.25 Miller-Bravais indices are obtained for crystallographic planes in HCP unit cells by using a four-axis coordinate system. The planes labeled A and B and the direction labeled C and D are those discussed in Example 3.11.
٦٦Chapter 3 -
Example SOLUTION
Plane A1. a1 = a2 = a3 = , c = 12. 1/a1 = 1/a2 = 1/a3 = 0, 1/c = 13. No fractions to clear4. (0001)
Plane B1. a1 = 1, a2 = 1, a3 = -1/2, c = 12. 1/a1 = 1, 1/a2 = 1, 1/a3 = -2, 1/c = 13. No fractions to clear4.
Direction C1. Two points are 0, 0, 1 and 1, 0, 0.2. 0, 0, 1, -1, 0, 0 = 1, 0, 13. No fractions to clear or integers to reduce.4.
∞
)1211(
113]2[or ]011[
٦٧Chapter 3 -
SOLUTION (Continued)
Direction D1. Two points are 0, 1, 0 and 1, 0, 0.2. 0, 1, 0, -1, 0, 0 = -1, 1, 03. No fractions to clear or integers to reduce.4. 100]1[or ]101[
٦٨Chapter 3 -
٦٩Chapter 3 -
Planar Density of (100) IronSolution: At T < 912°C iron has the BCC structure.
(100)
Radius of iron R = 0.1241 nm
R3
34a =
Adapted from Fig. 3.2(c), Callister 7e.
2D repeat unit
= Planar Density =a2
1atoms
2D repeat unit
= nm2
atoms12.1m2
atoms= 1.2 x 10191
2
R3
34area2D repeat unit
٧٠Chapter 3 -
o Interstitial sites - Locations between the ‘‘normal’’ atoms or ions in a crystal into which another - usually different - atom or ion is placed. Typically, the size of this interstitial location is smaller than the atom or ion that is to be introduced.
o Cubic site - An interstitial position that has a coordination number of eight. An atom or ion in the cubic site touches eight other atoms or ions.
o Octahedral site - An interstitial position that has a coordination number of six. An atom or ion in the octahedral site touches six other atoms or ions.
o Tetrahedral site - An interstitial position that has a coordination number of four. An atom or ion in the tetrahedral site touches four other atoms or ions.
Interstitial Sites
٧١Chapter 3 -
(c) 2003 Brooks/Cole Publishing / Thomson Learning™
Figure . The location of the interstitial sites in cubic unit cells. Only representative sites are shown.
٧٢Chapter 3 -
Example Calculating Octahedral Sites
Calculate the number of octahedral sites that uniquelybelong to one FCC unit cell.
SOLUTION
The octahedral sites include the 12 edges of the unit cell, with the coordinates
211,,0
211,,1
210,,1
21,0,0
,121,0 ,1
21,1 ,0
21,1 ,0
21,0
1,1,21 0,1,
21 1,0,
21 0,0,
21
plus the center position, 1/2, 1/2, 1/2.
٧٣Chapter 3 -
Which sites will cations occupy?Site Selection
1. Size of sites– does the cation fit in the site
2. Stoichiometry– if all of one type of site is full the
remainder have to go into other types of sites.
3. Bond Hybridization
٧٤Chapter 3 -
٧٥Chapter 3 -
• Coordination # increases with
Coordination # and Ionic Radii
Adapted from Table 12.2, Callister 7e.
2
rcationranion
Coord#
< 0.155
0.155 - 0.225
0.225 - 0.414
0.414 - 0.732
0.732 - 1.0
3
4
6
8
linear
triangular
TD
OH
cubic
Adapted from Fig. 12.2, Callister 7e.
Adapted from Fig. 12.3, Callister 7e.
Adapted from Fig. 12.4, Callister 7e.
ZnS(zincblende)
NaCl(sodium chloride)
CsCl(cesium chloride)
rcationranion
Issue: How many anions can youarrange around a cation?
٧٦Chapter 3 -
Cation Site Size• Determine minimum rcation/ranion for OH site
(C.N. = 6)
a = 2ranion
2ranion + 2rcation = 2 2ranion
ranion + rcation = 2ranion rcation = ( 2 −1)ranion
2ranion + 2rcation = 2a
4140anion
cation .rr
=
٧٧Chapter 3 -
Rock Salt StructureSame concepts can be applied to ionic solids
in general. Example: NaCl (rock salt) structure
rNa = 0.102 nm
rNa/rCl = 0.564
∴ cations prefer OH sites
Adapted from Fig. 12.2, Callister 7e.
rCl = 0.181 nm
٧٨Chapter 3 -
MgO and FeOMgO and FeO also have the NaCl
structureO2- rO = 0.140 nm
Mg2+ rMg = 0.072 nm
rMg/rO = 0.514
∴ cations prefer OH sites
So each oxygen has 6 neighboring Mg2+
Adapted from Fig. 12.2, Callister 7e.
٧٩Chapter 3 -
• On the basis of ionic radii, what crystal structurewould you predict for FeO?
• Answer:
550014000770
anion
cation
...
rr
=
=
based on this ratio,--coord # = 6--structure = NaCl
Data from Table 12.3, Callister 7e.
Example: Predicting Structure of FeO
Ionic radius (nm)0.0530.0770.0690.100
0.1400.1810.133
Cation
Anion
Al3+
Fe2+
Fe3+
Ca2+
O2-
Cl-
F-
٨٠Chapter 3 -
AX Crystal StructuresAX–Type Crystal Structures include NaCl, CsCl, and
zinc blende
939.0181.0170.0
Cl
Cs ==−
+
rr
Adapted from Fig. 12.3, Callister 7e.
Cesium Chloride structure:
∴ cubic sites preferred
So each Cs+ has 8 neighboring Cl-
٨١Chapter 3 -
AX Crystal Structures
So each Zn2+ has 4 neighboring O2-
Zinc Blende structure
Adapted from Fig. 12.4, Callister 7e.
?? 529.0140.0074.0
2
2
O
ZnHO
rr
⇒==−
+
• Size arguments predict Zn2+
in OH sites, • In observed structure Zn2+
in TD sites
• Why is Zn2+ in TD sites?– bonding hybridization of
zinc favors TD sites
Ex: ZnO, ZnS, SiC
٨٢Chapter 3 -
(c) 2003 Brooks/Cole Publishing / Thomson Learning™
Figure 3.33 (a) The zinc blende unit cell, (b) plan view.
٨٣Chapter 3 -
AX2 Crystal Structures
Fluoritestructure
• Calcium Fluorite (CaF2)• cations in cubic sites
• UO2, ThO2, ZrO2, CeO2
• antifluorite structure –cations and anions reversed
Adapted from Fig. 12.5, Callister 7e.
٨٤Chapter 3 -
ABX3 Crystal Structures
• Perovskite
Ex: complex oxide BaTiO3
Adapted from Fig. 12.6, Callister 7e.
٨٥Chapter 3 -
o Covalently bonded materials frequently have complex structures in order to satisfy the directional restraints imposed by the bonding.
o Diamond cubic (DC) - A special type of face-centered cubic crystal structure found in carbon, silicon, and other covalently bonded materials.
Covalent Structures
٨٦Chapter 3 -
(c) 2003 Brooks/C
ole Publishing / Thomson Learning
Figure . (a) Tetrahedron and (b) the diamond cubic (DC) unit cell. This open structure is produced because of the requirements of covalent bonding.
٨٧Chapter 3 -
(c) 2003 Brooks/C
ole Publishing / Thomson
Learning
Figure . The silicon-oxygen tetrahedron and the resultant β-cristobalite form of silica.
٨٨Chapter 3 -
X-Ray Diffraction
• Diffraction gratings must have spacings comparable to the wavelength of diffracted radiation.
• Can’t resolve spacings < λ• Spacing is the distance between parallel planes of
atoms.
٨٩Chapter 3 -
X-Rays to Determine Crystal Structure
X-ray intensity (from detector)
θ
θc
d =nλ
2 sin θc
Measurement of critical angle, θc, allows computation of planar spacing, d.
• Incoming X-rays diffract from crystal planes.
Adapted from Fig. 3.19, Callister 7e.
reflections must be in phase for a detectable signal
spacing between planes
d
incoming
X-rays
outgo
ing X
-rays
detector
θλ
θextra distance travelledby wave “2”
“1”
“2”
“1”
“2”
٩٠Chapter 3 -
X-Ray Diffraction Pattern
Adapted from Fig. 3.20, Callister 5e.
(110)
(200)
(211)
z
x
ya b
c
Diffraction angle 2θ
Diffraction pattern for polycrystalline α-iron (BCC)
Inte
nsity
(rel
ativ
e)
z
x
ya b
cz
x
ya b
c
٩١Chapter 3 -
• Atoms may assemble into crystalline or amorphous structures.
• We can predict the density of a material, provided we know the atomic weight, atomic radius, and crystal geometry (e.g., FCC, BCC, HCP).
SUMMARY
• Common metallic crystal structures are FCC, BCC, and HCP. Coordination number and atomic packing factorare the same for both FCC and HCP crystal structures.
• Crystallographic points, directions and planes are specified in terms of indexing schemes. Crystallographic directions and planes are related to atomic linear densities and planar densities.
٩٢Chapter 3 -
• Some materials can have more than one crystal structure. This is referred to as polymorphism (or allotropy).
SUMMARY
• Materials can be single crystals or polycrystalline. Material properties generally vary with single crystal orientation (i.e., they are anisotropic), but are generally non-directional (i.e., they are isotropic) in polycrystals with randomly oriented grains.
• X-ray diffraction is used for crystal structure and interplanar spacing determinations.
٩٣Chapter 3 -
ISSUES TO ADDRESS...
• What types of defects arise in solids?
• Can the number and type of defects be variedand controlled?
• How do defects affect material properties?
• Are defects undesirable?
IMPERFECTIONS IN SOLIDS
• What are the solidification mechanisms?
٩٤Chapter 3 -
Imperfections in Solids
There is no such thing as a perfect crystal. • What are these imperfections? • Why are they important?
Many of the important properties of materials are due to the presence of imperfections.
٩٥Chapter 3 -
• Vacancy atoms• Interstitial atoms• Substitutional atoms
Point defects
Types of Imperfections
• Dislocations Line defects
• Grain Boundaries Area defects
٩٦Chapter 3 -
• Vacancies:-vacant atomic sites in a structure.
• Self-Interstitials:-"extra" atoms positioned between atomic sites.
Point Defects
Vacancydistortion of planes
self-interstitial
distortion of planes
٩٧Chapter 3 -
Boltzmann's constant(1.38 x 10 -23 J/atom-K) (8.62 x 10-5 eV/atom-K)
NvN
= exp−QvkT
No. of defects
No. of potential defect sites.
Activation energy
Temperature
Each lattice site is a potential vacancy site
• Equilibrium concentration varies with temperature!
Equilibrium Concentration:Point Defects
٩٨Chapter 3 -
• Find the equil. # of vacancies in 1 m3 of Cu at 1000°C.• Given:
ACu = 63.5 g/molρ = 8.4 g/cm3
Qv = 0.9 eV/atom NA = 6.02 x 1023 atoms/mol
Estimating Vacancy Concentration
For 1 m3 , N =NAACu
ρ x x 1 m3= 8.0 x 1028 sites8.62 x 10-5 eV/atom-K
0.9 eV/atom
1273K
NvN
= exp−QvkT
= 2.7 x 10-4
• Answer:Nv = (2.7 x 10-4)(8.0 x 1028) sites = 2.2 x 1025 vacancies
٩٩Chapter 3 -
• Low energy electronmicroscope view ofa (110) surface of NiAl.
• Increasing T causessurface island ofatoms to grow.
• Why? The equil. vacancyconc. increases via atommotion from the crystalto the surface, where
they join the island.Reprinted with permission from Nature (K.F. McCarty, J.A. Nobel, and N.C. Bartelt, "Vacancies inSolids and the Stability of Surface Morphology",Nature, Vol. 412, pp. 622-625 (2001). Image is5.75 µm by 5.75 µm.) Copyright (2001) Macmillan Publishers, Ltd.
Observing Equilibrium Vacancy Conc.
Island grows/shrinks to maintain equil. vancancy conc. in the bulk.
١٠٠Chapter 3 -
Two outcomes if impurity (B) added to host (A):• Solid solution of B in A (i.e., random dist. of point defects)
• Solid solution of B in A plus particles of a newphase (usually for a larger amount of B)
OR
Substitutional solid soln.(e.g., Cu in Ni)
Interstitial solid soln.(e.g., C in Fe)
Second phase particle--different composition--often different structure.
Point Defects in Alloys
١٠١Chapter 3 -
Imperfections in Solids• Specification of composition
– weight percent 100x 21
11 mm
mC+
=
m1 = mass of component 1
100x 21
1'1
mm
m
nnnC+
=
nm1 = number of moles of component 1
– atom percent
١٠٢Chapter 3 -
• are line defects,• slip between crystal planes result when dislocations move,• produce permanent (plastic) deformation.
Dislocations:
Schematic of Zinc (HCP):• before deformation • after tensile elongation
slip steps
Line Defects
Adapted from Fig. 7.8, Callister 7e.
١٠٣Chapter 3 -
Imperfections in Solids
Linear Defects (Dislocations)– Are one-dimensional defects around which atoms are
misaligned• Edge dislocation:
– extra half-plane of atoms inserted in a crystal structure– b ⊥ to dislocation line
• Screw dislocation:– spiral planar ramp resulting from shear deformation– b || to dislocation line
Burger’s vector, b: measure of lattice distortion
١٠٤Chapter 3 -
Imperfections in Solids
Fig. 4.3, Callister 7e.
Edge Dislocation
١٠٥Chapter 3 -
• Dislocation motion requires the successive bumpingof a half plane of atoms (from left to right here).
• Bonds across the slipping planes are broken andremade in succession.
Atomic view of edgedislocation motion fromleft to right as a crystalis sheared.
(Courtesy P.M. Anderson)
Motion of Edge Dislocation
١٠٦Chapter 3 -
Imperfections in Solids
Screw Dislocation
Adapted from Fig. 4.4, Callister 7e.
Burgers vector b
Dislocationline
b
(a)(b)
Screw Dislocation
١٠٧Chapter 3 -
Edge, Screw, and Mixed Dislocations
Adapted from Fig. 4.5, Callister 7e.
Edge
Screw
Mixed
١٠٨Chapter 3 -
Imperfections in Solids
Dislocations are visible in electron micrographs
Adapted from Fig. 4.6, Callister 7e.
١٠٩Chapter 3 -
Grain boundaries...• are imperfections,• are more susceptible
to etching,• may be revealed as
dark lines,• change in crystal
orientation across boundary. Adapted from Fig. 4.14(a)
and (b), Callister 7e.(Fig. 4.14(b) is courtesyof L.C. Smith and C. Brady, the National Bureau of Standards, Washington, DC [now the National Institute of Standards and Technology, Gaithersburg, MD].)
Optical Microscopy
Fe-Cr alloy(b)
grain boundarysurface groove
polished surface
(a)
١١٠Chapter 3 -
• Point, Line, and Area defects exist in solids.
• The number and type of defects can be variedand controlled (e.g., T controls vacancy conc.)
• Defects affect material properties (e.g., grainboundaries control crystal slip).
• Defects may be desirable or undesirable(e.g., dislocations may be good or bad, dependingon whether plastic deformation is desirable or not.)
Summary
١١١Chapter 3 -١١١
ISSUES TO ADDRESS...• Stress and strain: What are they and why are
they used instead of load and deformation?• Elastic behavior: When loads are small, how much
deformation occurs? What materials deform least?• Plastic behavior: At what point does permanent
deformation occur? What materials are most resistant to permanent deformation?
• Toughness and ductility: What are they and howdo we measure them?
Mechanical Properties
١١٢Chapter 3 -١١٢
Terminology for Mechanical Propertiesq Stress - Force or load per unit area of cross-section over
which the force or load is acting.q Strain - Elongation change in dimension per unit length.q Young’s modulus - The slope of the linear part of the stress-strain curve in the elastic region, same as modulus of elasticity.q Shear modulus (G) - The slope of the linear part of the shear stress-shear strain curve.q Viscosity ( ) - Measure of resistance to flow, defined as the ratio of shear stress to shear strain rate (units Poise or Pa-s).q Thixotropic behavior - Materials that show shear thinning and also an apparent viscosity that at a constant rate of shear decreases with time.
η
١١٣Chapter 3 -١١٣
(photo courtesy P.M. Anderson)Canyon Bridge, Los Alamos, NM
oσ = F
A
• Simple compression:
Note: compressivestructure member(σ < 0 here).(photo courtesy P.M. Anderson)
OTHER COMMON STRESS STATES (1)
Ao
Balanced Rock, Arches National Park
١١٤Chapter 3 -١١٤
∴ Stress has units:N/m2 or lbf/in2
Engineering Stress• Shear stress, τ:
Area, A
Ft
Ft
Fs
F
F
Fs
τ = FsAo
• Tensile stress, σ:
original area before loading
Area, A
Ft
Ft
σ = FtAo
2f
2mNor
inlb=
١١٥Chapter 3 -١١٥
• Tensile strain: • Lateral strain:
• Shear strain:
Strain is alwaysdimensionless.
Engineering Strain
θ
90º
90º - θy
∆x θγ = ∆x/y = tan
ε = δLo
−δεL = L
wo
Adapted from Fig. 6.1 (a) and (c), Callister 7e.
δ/2
δL/2
Lowo
١١٦Chapter 3 -١١٦
١١٧Chapter 3 -١١٧
Figure (a) Tensile, compressive, shear and bending stresses. (b) Illustration showing how Young’s modulus is defined for elastic material. (c) For nonlinear materials, we use the slope of a tangent as a variable quantity that replaces the Young’s modulus constant
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١١٨Chapter 3 -١١٨
Linear Elastic Properties• Modulus of Elasticity, E:
(also known as Young's modulus)
• Hooke's Law:σ = E ε σ
Linear-elastic
E
ε
F
Fsimple tension test
١١٩Chapter 3 -١١٩
• Elastic Shearmodulus, G:
τG
γτ = G γ
Other Elastic Properties
simpletorsiontest
M
M
• Special relations for isotropic materials:
2(1 + ν)EG =
3(1 − 2ν)EK =
١٢٠Chapter 3 -١٢٠
Poisson's ratio, ν• Poisson's ratio, ν:
Units:E: [GPa] or [psi]ν: dimensionless
–ν > 0.50 density increases
–ν < 0.50 density decreases (voids form)
εL
ε
-ν
εν = − L
ε
metals: ν ~ 0.33ceramics: ν ~ 0.25polymers: ν ~ 0.40
١٢١Chapter 3 -١٢١
Stress-Strain Testing• Typical tensile test
machine
Adapted from Fig. 6.3, Callister 7e. (Fig. 6.3 is taken from H.W. Hayden, W.G. Moffatt, and J. Wulff, The Structure and Properties of Materials, Vol. III, Mechanical Behavior, p. 2, John Wiley and Sons, New York, 1965.)
specimenextensometer
• Typical tensile specimen
Adapted from Fig. 6.2,Callister 7e.
gauge length
١٢٢Chapter 3 -١٢٢
Tensile Strength, TS
• Metals: occurs when noticeable necking starts.• Polymers: occurs when polymer backbone chains are
aligned and about to break.
Adapted from Fig. 6.11, Callister 7e.
σy
strain
Typical response of a metal
F = fracture or ultimate strength
Neck – acts as stress concentrator
engi
neer
ing
TSst
ress
engineering strain
١٢٣Chapter 3 -١٢٣
(c)2003 Brooks/Cole, a division of Thomson Learning, Inc. Thomson Learning™ is a trademark used herein under license.
Figure 6.12 Localized deformation of a ductile material during a tensile test produces a necked region. The micrograph shows necked region in a fractured sample
١٢٤Chapter 3 -١٢٤
١٢٥Chapter 3 -١٢٥
(c)2003 Brooks/Cole, a division of Thomson Learning, Inc. Thomson Learning™ is a trademark used herein under license.
Figure :The stress-strain curve for an aluminum alloy
١٢٦Chapter 3 -١٢٦
Example :Tensile Testing of Aluminum Alloy
Convert the change in length data in Table 6-1 to engineering stress and strain and plot a stress-strain curve.
١٢٧Chapter 3 -١٢٧
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Figure: Tensile stress-strain curves for different materials. Note that these are qualitative
١٢٨Chapter 3 -١٢٨
(c)2003 Brooks/Cole, a division of Thomson Learning, Inc. Thomson Learning™ is a trademark used herein under license.
Figure: (a) Determining the 0.2% offset yield strength in gray cast ion, and (b) upper and lower yield point behavior in a low-carbon steel
١٢٩Chapter 3 -١٢٩
• Stress at which noticeable plastic deformation hasoccurred.
when εp = 0.002
Yield Strength, σy
σy = yield strength
Note: for 2 inch sample
ε = 0.002 = ∆z/z
∴ ∆z = 0.004 in
Adapted from Fig. 6.10 (a),Callister 7e.
tensile stress, σ
engineering strain, ε
σy
εp = 0.002
١٣٠Chapter 3 -١٣٠
Figure 6.13 Typical yield strength values for different engineered materials. (Source: Reprinted fromEngineering Materials I, Second Edition, M.F. Ashby and D.R.H. Jones, 1996, Fig. 8-12, p. 85. Copyright ©Butterworth-Heinemann. Reprinted with permission from Elsevier Science.)
١٣١Chapter 3 -١٣١
١٣٢Chapter 3 -١٣٢
Figure : Range of elastic moduli for different engineered materials. (Source: Reprinted from Engineering Materials I, Second Edition, M.F. Ashby and D.R.H. Jones, 1996, Fig. 3-5, p. 35, Copyright © 1996 Butterworth-Heinemann. Reprinted with permission from Elsevier Science.)
١٣٣Chapter 3 -١٣٣
True Stress & StrainNote: S.A. changes when sample
stretched
• True stress
• True Strain
iT AF=σ
( )oiT llln=ε( )( )ε+=ε
ε+σ=σ1ln1
T
T
Adapted from Fig. 6.16, Callister 7e.
١٣٤Chapter 3 -١٣٤
Example : Young’s Modulus of Aluminum Alloy
From the data in Example 6.1, calculate the modulus of elasticity of the aluminum alloy. Use the modulus to determine the length after deformation of a bar of initial length of 50 in. Assume that a level of stress of 30,000 psi is applied.
Example SOLUTION
١٣٥Chapter 3 -١٣٥
Example: True Stress and True Strain Calculation
Compare engineering stress and strain with true stress and strain for the aluminum alloy in Example 6.1 at (a) the maximum load and (b) fracture. The diameter at maximum load is 0.497 in. and at fracture is 0.398 in.
Example 6.5 SOLUTION
١٣٦Chapter 3 -١٣٦
Example : SOLUTION (Continued)
١٣٧Chapter 3 -١٣٧
Hardening
• Curve fit to the stress-strain response:
σT = K εT( )n“true” stress (F/A) “true” strain: ln(L/Lo)
hardening exponent:n = 0.15 (some steels) to n = 0.5 (some coppers)
• An increase in σy due to plastic deformation.σ
ε
large hardening
small hardeningσy0
σy1
١٣٨Chapter 3 -١٣٨
Resilience, Ur
• Ability of a material to store energy – Energy stored best in elastic region
If we assume a linear stress-strain curve this simplifies to
Adapted from Fig. 6.15, Callister 7e.
yyr 21U εσ≅
∫ε
εσ= y dU r 0
١٣٩Chapter 3 -١٣٩
• Energy to break a unit volume of material• Approximate by the area under the stress-strain
curve.
Toughness
Brittle fracture: elastic energyDuctile fracture: elastic + plastic energy
very small toughness (unreinforced polymers)
Engineering tensile strain, ε
Engineeringtensile stress, σ
small toughness (ceramics)
large toughness (metals)
Adapted from Fig. 6.13, Callister 7e.
١٤٠Chapter 3 -١٤٠
Impact Testing
final height initial height
• Impact loading:-- severe testing case-- makes material more brittle-- decreases toughness
Adapted from Fig. 8.12(b), Callister 7e. (Fig. 8.12(b) is adapted from H.W. Hayden, W.G. Moffatt, and J. Wulff, The Structure and Properties of Materials, Vol. III, Mechanical Behavior, John Wiley and Sons, Inc. (1965) p. 13.)
(Charpy)
١٤١Chapter 3 -١٤١
• Plastic tensile strain at failure:
Adapted from Fig. 6.13, Callister 7e.
Ductility
• Another ductility measure: 100xA
AARA%o
fo -=
x 100L
LLEL%o
of −=
Engineering tensile strain, ε
Engineeringtensile stress, σ
smaller %EL
larger %ELLf
Ao AfLo
١٤٢Chapter 3 -١٤٢
(c)2003 Brooks/Cole, a division of Thomson Learning, Inc. Thomson Learning™ is a trademark used herein under license.
Figure : The stress-strain behavior of brittle materials compared with that of more ductile materials
١٤٣Chapter 3 -١٤٣
(c)2003 Brooks/Cole, a division of Thomson Learning, Inc. Thomson Learning™ is a trademark used herein under license.
Figure : The effect of temperance (a) on the stress-strain curve and (b) on the tensile properties of an aluminum alloy
١٤٤Chapter 3 -١٤٤
Example : Ductility of an Aluminum Alloy
The aluminum alloy in Example 6.1 has a final length after failure of 2.195 in. and a final diameter of 0.398 in. at the fractured surface. Calculate the ductility of this alloy.
Example SOLUTION
١٤٥Chapter 3 -١٤٥
Hardness• Resistance to permanently indenting the surface.• Large hardness means:
--resistance to plastic deformation or cracking incompression.
--better wear properties.
e.g., 10 mm sphere
apply known force measure size of indent after removing load
dDSmaller indents mean larger hardness.
increasing hardness
most plastics
brasses Al alloys
easy to machine steels file hard
cutting tools
nitridedsteels diamond
١٤٦Chapter 3 -١٤٦
Hardness: Measurement
• Rockwell– No major sample damage– Each scale runs to 130 but only useful in range
20-100. – Minor load 10 kg– Major load 60 (A), 100 (B) & 150 (C) kg
• A = diamond, B = 1/16 in. ball, C = diamond
• HB = Brinell Hardness– TS (psia) = 500 x HB– TS (MPa) = 3.45 x HB
١٤٧Chapter 3 -١٤٧
Hardness: MeasurementTable
١٤٨Chapter 3 -١٤٨
ISSUES TO ADDRESS...• How do flaws in a material initiate failure?• How is fracture resistance quantified; how do different
material classes compare?• How do we estimate the stress to fracture?• How do loading rate, loading history, and temperature
affect the failure stress?
Ship-cyclic loadingfrom waves.
Computer chip-cyclicthermal loading.
Hip implant-cyclicloading from walking.
Adapted from Fig. 22.30(b), Callister 7e.(Fig. 22.30(b) is courtesy of National Semiconductor Corporation.)
Adapted from Fig. 22.26(b), Callister 7e.
Mechanical Failure
Adapted from chapter-opening photograph, Chapter 8, Callister 7e. (by Neil Boenzi, The New York Times.)
١٤٩Chapter 3 -١٤٩
Fracture mechanisms
• Ductile fracture– Occurs with plastic deformation
• Brittle fracture– Little or no plastic deformation– Catastrophic
١٥٠Chapter 3 -١٥٠
Ductile vs Brittle FailureVery
DuctileModerately
Ductile BrittleFracturebehavior:
Large Moderate%AR or %EL Small• Ductilefracture is usuallydesirable!
Adapted from Fig. 8.1, Callister 7e.
• Classification:
Ductile:warning before
fracture
Brittle:No
warning
١٥١Chapter 3 -١٥١
• Ductile failure:--one piece--large deformation
Figures from V.J. Colangelo and F.A. Heiser, Analysis of Metallurgical Failures(2nd ed.), Fig. 4.1(a) and (b), p. 66 John Wiley and Sons, Inc., 1987. Used with permission.
Example: Failure of a Pipe
• Brittle failure:--many pieces--small deformation
١٥٢Chapter 3 -١٥٢
• Evolution to failure:
• Resultingfracturesurfaces(steel)
50 mm
particlesserve as voidnucleationsites.
50 mm
From V.J. Colangelo and F.A. Heiser, Analysis of Metallurgical Failures (2nd ed.), Fig. 11.28, p. 294, John Wiley and Sons, Inc., 1987. (Orig. source: P. Thornton, J. Mater. Sci., Vol. 6, 1971, pp. 347-56.)
100 mmFracture surface of tire cord wire loaded in tension. Courtesy of F. Roehrig, CC Technologies, Dublin, OH. Used with permission.
Moderately Ductile Failurenecking
σ
void nucleation
void growth and linkage
shearing at surface fracture
١٥٣Chapter 3 -١٥٣
Ductile vs. Brittle Failure
Adapted from Fig. 8.3, Callister 7e.
cup-and-cone fracture brittle fracture
١٥٤Chapter 3 -١٥٤
Fracture Mechanics
o Fracture mechanics - The study of a material’s ability to withstand stress in the presence of a flaw.
o Fracture toughness - The resistance of a material to failure in the presence of a flaw.
١٥٥Chapter 3 -١٥٥
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Figure : The fracture toughness Kc of a 3000,000psi yield strength steel decreases with increasing thickness, eventually leveling off at the plane strain fracture toughness Klc
١٥٦Chapter 3 -١٥٦
Design of a Nondestructive Test
A large steel plate used in a nuclear reactor has a plane strain fracture toughness of 80,000 psi and is exposed to a stress of 45,000 psi during service. Design a testing or inspection procedure capable of detecting a crack at the edge of the plate before the crack is likely to grow at a catastrophic rate.
SOLUTION
.in
١٥٧Chapter 3 -١٥٧
Design of a Ceramic Support
Design a supporting 3-in.-wide plate made of sialon, which has a fracture toughness of 9,000 psi , that will withstand a tensile load of 40,000 lb. The part is to be nondestructively tested to assure that no flaws are present that might cause failure.
.in
١٥٨Chapter 3 -١٥٨
Flaws are Stress Concentrators!Results from crack
propagation• Griffith Crack
where ρt = radius of curvatureσo = applied stressσm = stress at crack tip
ot
/
tom Ka
σ=
ρ
σ=σ21
2
ρt
Adapted from Fig. 8.8(a), Callister 7e.
١٥٩Chapter 3 -١٥٩
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n un
der l
icen
se.
Figure:Schematic diagram of the Griffith flaw in a ceramic
١٦٠Chapter 3 -١٦٠
Concentration of Stress at Crack Tip
١٦١Chapter 3 -١٦١
Crack PropagationCracks propagate due to sharpness of crack
tip • A plastic material deforms at the tip,
“blunting” the crack.deformed region
brittle
Energy balance on the crack• Elastic strain energy-
• energy stored in material as it is elastically deformed• this energy is released when the crack propagates• creation of new surfaces requires energy
plastic
١٦٢Chapter 3 -١٦٢
When Does a Crack Propagate?Crack propagates if above critical
stress
• where– E = modulus of elasticity– γs = specific surface energy– a = one half length of internal crack– Kc = σc/σ0
For ductile => replace γs by γs + γpwhere γp is plastic deformation energy
212 /s
c aE
πγ
=σi.e., σm > σc
or Kt > Kc
١٦٣Chapter 3 -١٦٣
Fatigue• Fatigue = failure under cyclic stress.
• Stress varies with time.-- key parameters are S, σm, and
frequency
σmax
σmin
σ
time
σmS
• Key points: Fatigue...--can cause part failure, even though σmax < σc.--causes ~ 90% of mechanical engineering failures.
Adapted from Fig. 8.18, Callister 7e. (Fig. 8.18 is from Materials Science in Engineering, 4/E by Carl. A. Keyser, Pearson Education, Inc., Upper Saddle River, NJ.)tension on bottom
compression on top
countermotor
flex coupling
specimen
bearing bearing
١٦٤Chapter 3 -١٦٤
• Fatigue limit, Sfat:--no fatigue if S < Sfat
Adapted from Fig. 8.19(a), Callister 7e.
Fatigue Design Parameters
Sfat
case for steel (typ.)
N = Cycles to failure103 105 107 109
unsafe
safe
S = stress amplitude
• Sometimes, thefatigue limit is zero!
Adapted from Fig. 8.19(b), Callister 7e.
case for Al (typ.)
N = Cycles to failure103 105 107 109
unsafe
safe
S = stress amplitude
١٦٥Chapter 3 -١٦٥
CreepSample deformation at a constant stress (σ) vs.
time
Adapted fromFig. 8.28, Callister 7e.
Primary Creep: slope (creep rate) decreases with time.
Secondary Creep: steady-statei.e., constant slope.
Tertiary Creep: slope (creep rate) increases with time, i.e. acceleration of rate.
σσ,ε
0 t
١٦٦Chapter 3 -١٦٦
• Occurs at elevated temperature, T > 0.4 Tm
Adapted from Figs. 8.29, Callister 7e.
Creep
elastic
primarysecondary
tertiary
١٦٧Chapter 3 -١٦٧
Strategies for Strengthening: 1: Reduce Grain Size
• Grain boundaries arebarriers to slip.
• Barrier "strength"increases withIncreasing angle of misorientation.
• Smaller grain size:more barriers to slip.
• Hall-Petch Equation: 21 /yoyield dk −+σ=σ
Adapted from Fig. 7.14, Callister 7e.(Fig. 7.14 is from A Textbook of Materials Technology, by Van Vlack, Pearson Education, Inc., Upper Saddle River, NJ.)
١٦٨Chapter 3 -١٦٨
• Impurity atoms distort the lattice & generate stress.• Stress can produce a barrier to dislocation motion.
Strategies for Strengthening: 2: Solid Solutions
• Smaller substitutionalimpurity
Impurity generates local stress at Aand B that opposes dislocation motion to the right.
A
B
• Larger substitutionalimpurity
Impurity generates local stress at Cand D that opposes dislocation motion to the right.
C
D
١٦٩Chapter 3 -١٦٩
Stress Concentration at Dislocations
Adapted from Fig. 7.4, Callister 7e.
١٧٠Chapter 3 -١٧٠
Strengthening by Alloying• small impurities tend to concentrate at
dislocations• reduce mobility of dislocation ∴ increase
strength
Adapted from Fig. 7.17, Callister 7e.
١٧١Chapter 3 -١٧١
Strengthening by alloying
• large impurities concentrate at dislocations on low density side
Adapted from Fig. 7.18, Callister 7e.
١٧٢Chapter 3 -١٧٢
Ex: Solid SolutionStrengthening in Copper
• Tensile strength & yield strength increase with wt% Ni.
• Empirical relation:
• Alloying increases σy and TS.
21 /y C~σ
Adapted from Fig. 7.16 (a) and (b), Callister 7e.
Tens
ile s
treng
th (M
Pa)
wt.% Ni, (Concentration C)
200
300
400
0 10 20 30 40 50 Yiel
d st
reng
th (M
Pa)
wt.%Ni, (Concentration C)
60
120
180
0 10 20 30 40 50
١٧٣Chapter 3 -١٧٣
Strategies for Strengthening: 3: Cold Work (%CW)
• Room temperature deformation.• Common forming operations change the cross
sectional area:
Adapted from Fig. 11.8, Callister 7e.
-Forging
Ao Ad
force
dieblank
force-Drawing
tensile force
AoAddie
die
-Extrusion
ram billet
container
containerforce die holder
die
Ao
Adextrusion
100 x %o
doA
AACW −=
-Rolling
roll
AoAd
roll
١٧٤Chapter 3 -١٧٤
• Ti alloy after cold working:
• Dislocations entanglewith one anotherduring cold work.
• Dislocation motionbecomes more difficult.
Adapted from Fig. 4.6, Callister 7e.(Fig. 4.6 is courtesy of M.R. Plichta, Michigan Technological University.)
Dislocations During Cold Work
0.9 µm
١٧٥Chapter 3 -١٧٥
• What is the tensile strength &ductility after cold working?
Adapted from Fig. 7.19, Callister 7e. (Fig. 7.19 is adapted from Metals Handbook: Properties and Selection: Iron and Steels, Vol. 1, 9th ed., B. Bardes (Ed.), American Society for Metals, 1978, p. 226; and Metals Handbook: Properties and Selection: Nonferrous Alloys and Pure Metals, Vol. 2, 9th ed., H. Baker (Managing Ed.), American Society for Metals, 1979, p. 276 and 327.)
%6.35100 x % 2
22=
π
π−π=
o
dor
rrCW
Cold Work Analysis
% Cold Work
100
300
500
700
Cu
200 40 60
yield strength (MPa)
σy = 300MPa
300MPa
% Cold Work
tensile strength (MPa)
200Cu
0
400
600
800
20 40 60
ductility (%EL)
% Cold Work
20
40
60
20 40 6000
Cu
Do =15.2mm
Cold Work
Dd =12.2mm
Copper
340MPa
TS = 340MPa
7%
%EL = 7%
١٧٦Chapter 3 -١٧٦
ISSUES TO ADDRESS...
• How does diffusion occur?
• Why is it an important part of processing?
• How can the rate of diffusion be predicted forsome simple cases?
• How does diffusion depend on structureand temperature?
Diffusion in Solids
١٧٧Chapter 3 -١٧٧
Diffusion
Diffusion - Mass transport by atomic motion
Mechanisms• Gases & Liquids – random (Brownian)
motion• Solids – vacancy diffusion or interstitial
diffusion
١٧٨Chapter 3 -١٧٨
• Interdiffusion: In an alloy, atoms tend to migratefrom regions of high conc. to regions of low conc.
Initially
Adapted from Figs. 5.1 and 5.2, Callister7e.
Diffusion
After some time
١٧٩Chapter 3 -١٧٩
• Self-diffusion: In an elemental solid, atomsalso migrate.
Label some atoms After some time
Diffusion
A
B
C
DA
B
C
D
١٨٠Chapter 3 -١٨٠
Diffusion MechanismsVacancy Diffusion:• atoms exchange with vacancies• applies to substitutional impurities atoms • rate depends on:
--number of vacancies--activation energy to exchange.
increasing elapsed time
١٨١Chapter 3 -١٨١
• Simulation of interdiffusionacross an interface:
• Rate of substitutionaldiffusion depends on:--vacancy concentration--frequency of jumping.
(Courtesy P.M. Anderson)
Diffusion Simulation
١٨٢Chapter 3 -١٨٢
Diffusion Mechanisms• Interstitial diffusion – smaller
atoms can diffuse between atoms.
More rapid than vacancy diffusionAdapted from Fig. 5.3 (b), Callister 7e.
١٨٣Chapter 3 -١٨٣
Adapted from chapter-opening photograph, Chapter 5, Callister 7e. (Courtesy ofSurface Division, Midland-Ross.)
• Case Hardening:--Diffuse carbon atoms
into the host iron atomsat the surface.
--Example of interstitialdiffusion is a casehardened gear.
• Result: The presence of C atoms makes iron (steel) harder.
Processing Using Diffusion
١٨٤Chapter 3 -١٨٤
• Doping silicon with phosphorus for n-type semiconductors:• Process:
3. Result: Dopedsemiconductorregions.
silicon
Processing Using Diffusion
magnified image of a computer chip
0.5mm
light regions: Si atoms
light regions: Al atoms
2. Heat it.
1. Deposit P richlayers on surface.
silicon
Adapted from chapter-opening photograph, Chapter 18, Callister 7e.
١٨٥Chapter 3 -١٨٥
Diffusion• How do we quantify the amount or rate of
diffusion?
• Measured empirically– Make thin film (membrane) of known surface area– Impose concentration gradient– Measure how fast atoms or molecules diffuse through
the membrane
( )( ) smkgor
scmmol
timearea surfacediffusing mass) (or molesFlux 22=≡≡J
dtdM
Al
AtMJ ==
M =mass
diffusedtime
J ∝ slope
١٨٦Chapter 3 -١٨٦
Steady-State Diffusion
dxdCDJ −=
Fick’s first law of diffusionC1
C2
x
C1
C2
x1 x2
D ≡ diffusion coefficient
Rate of diffusion independent of timeFlux proportional to concentration gradient =
dxdC
12
12 linear ifxxCC
xC
dxdC
−−
=∆∆
≅
١٨٧Chapter 3 -١٨٧
Example: Chemical Protective Clothing (CPC)
• Methylene chloride is a common ingredient of paint removers. Besides being an irritant, it also may be absorbed through skin. When using this paint remover, protective gloves should be worn.
• If butyl rubber gloves (0.04 cm thick) are used, what is the diffusive flux of methylene chloride through the glove?
• Data:– diffusion coefficient in butyl rubber:
D = 110 x10-8 cm2/s– surface concentrations:
C2 = 0.02 g/cm3C1 = 0.44 g/cm3
١٨٨Chapter 3 -١٨٨
scmg 10 x 16.1
cm) 04.0()g/cm 44.0g/cm 02.0(/s)cm 10 x 110( 2
5-33
28- =−
−=J
Example (cont).
12
12- xxCCD
dxdCDJ
−−
−≅=
Dtb 6
2l=
gloveC1
C2
skinpaintremover
x1 x2
• Solution – assuming linear conc. gradient
D = 110x10-8 cm2/s
C2 = 0.02 g/cm3
C1 = 0.44 g/cm3
x2 – x1 = 0.04 cm
Data:
١٨٩Chapter 3 -١٨٩
Diffusion and Temperature
• Diffusion coefficient increases with increasing T.
D = Do exp
−
Qd
RT
= pre-exponential [m2/s]= diffusion coefficient [m2/s]
= activation energy [J/mol or eV/atom] = gas constant [8.314 J/mol-K]= absolute temperature [K]
DDo
Qd
RT
١٩٠Chapter 3 -١٩٠
Diffusion and Temperature
Adapted from Fig. 5.7, Callister 7e. (Date for Fig. 5.7 taken from E.A. Brandes and G.B. Brook (Ed.) Smithells Metals Reference Book, 7th ed., Butterworth-Heinemann, Oxford, 1992.)
D has exponential dependence on T
Dinterstitial >> DsubstitutionalC in α-FeC in γ-Fe
Al in AlFe in α-FeFe in γ-Fe
1000K/T
D (m2/s) C in α-Fe
C in γ-Fe
Al in Al
Fe in α-Fe
Fe in γ-Fe
0.5 1.0 1.510-20
10-14
10-8T(°C)15
00
1000
600
300
١٩١Chapter 3 -١٩١
Example: At 300ºC the diffusion coefficient and activation energy for Cu in Si are
D(300ºC) = 7.8 x 10-11 m2/sQd = 41.5 kJ/mol
What is the diffusion coefficient at 350ºC?
−=
−=
101
202
1lnln and 1lnlnTR
QDDTR
QDD dd
−−==−∴
121
212
11lnlnln TTR
QDDDD d
transform data
D
Temp = T
ln D
1/T
١٩٢Chapter 3 -١٩٢
Example (cont.)
−
−= −
K 5731
K 6231
K-J/mol 314.8J/mol 500,41exp /s)m 10 x 8.7( 211
2D
−−=
1212
11exp TTR
QDD d
T1 = 273 + 300 = 573KT2 = 273 + 350 = 623K
D2 = 15.7 x 10-11 m2/s
١٩٣Chapter 3 -١٩٣
Non-steady State Diffusion
• The concentration of diffucing species is a function of both time and position C = C(x,t)
• In this case Fick’s Second Law is used
2
2
xCD
tC
∂∂
=∂∂Fick’s Second Law
١٩٤Chapter 3 -١٩٤
Non-steady State Diffusion
Adapted from Fig. 5.5, Callister 7e.
B.C. at t = 0, C = Co for 0 ≤ x ≤ ∞
at t > 0, C = CS for x = 0 (const. surf. conc.)
C = Co for x = ∞
• Copper diffuses into a bar of aluminum.
pre-existing conc., Co of copper atoms
Surface conc., C of Cu atoms bars
Cs
١٩٥Chapter 3 -١٩٥
Diffusion FASTER for...
• open crystal structures
• materials w/secondarybonding
• smaller diffusing atoms
• lower density materials
Diffusion SLOWER for...
• close-packed structures
• materials w/covalentbonding
• larger diffusing atoms
• higher density materials
Summary
١٩٦Chapter 3 -
ISSUES TO ADDRESS...• When we combine two elements...
what equilibrium state do we get?• In particular, if we specify...
--a composition (e.g., wt% Cu - wt% Ni), and--a temperature (T)
then...How many phases do we get?What is the composition of each phase?How much of each phase do we get?
Chapter : Phase Diagrams
Phase BPhase A
Nickel atomCopper atom
١٩٧Chapter 3 -
Phase Equilibria: Solubility LimitIntroduction
– Solutions – solid solutions, single phase– Mixtures – more than one phase
• Solubility Limit:Max concentration forwhich only a single phase solution occurs.
Question: What is thesolubility limit at 20°C?
Answer: 65 wt% sugar.If Co < 65 wt% sugar: syrupIf Co > 65 wt% sugar: syrup + sugar. 65
Sucrose/Water Phase Diagram
Pure
Su
gar
Tem
pera
ture
(°C
)
0 20 40 60 80 100Co =Composition (wt% sugar)
L(liquid solution
i.e., syrup)
Solubility Limit L
(liquid) + S
(solid sugar)20
40
60
80
100
Pure
W
ater
Adapted from Fig. 9.1, Callister 7e.
١٩٨Chapter 3 -
• Components:The elements or compounds which are present in the mixture
(e.g., Al and Cu)• Phases:
The physically and chemically distinct material regionsthat result (e.g., α and β).
Aluminum-CopperAlloy
Components and Phases
α (darker phase)
β (lighter phase)
Adapted from chapter-opening photograph, Chapter 9, Callister 3e.
١٩٩Chapter 3 -
Effect of T & Composition (Co)• Changing T can change # of phases:
Adapted from Fig. 9.1, Callister 7e.
D (100°C,90)2 phases
B (100°C,70)1 phase
path A to B.• Changing Co can change # of phases: path B to D.
A (20°C,70)2 phases
70 80 1006040200
Tem
pera
ture
(°C
)
Co =Composition (wt% sugar)
L(liquid solution
i.e., syrup)
20
100
40
60
80
0
L(liquid)
+ S
(solid sugar)
water-sugarsystem
٢٠٠Chapter 3 -
Phase Equilibria
0.1278
1.8FCCCu0.124
61.9FCCNi
r (nm)electroneg
CrystalStructur
e
• Both have the same crystal structure (FCC) and have similar electronegativities and atomic radii (W. Hume –Rothery rules) suggesting high mutual solubility.
Simple solution system (e.g., Ni-Cu solution)
• Ni and Cu are totally miscible in all proportions.
٢٠١Chapter 3 -
Phase Diagrams• Indicate phases as function of T, Co, and P. • For this course:
-binary systems: just 2 components.-independent variables: T and Co (P = 1 atm is almost always used).
• PhaseDiagramfor Cu-Nisystem
Adapted from Fig. 9.3(a), Callister 7e.(Fig. 9.3(a) is adapted from Phase Diagrams of Binary Nickel Alloys, P. Nash (Ed.), ASM International, Materials Park, OH (1991).
• 2 phases:L (liquid)α (FCC solid solution)
• 3 phase fields: LL + αα
wt% Ni20 40 60 80 10001000
1100
1200
1300
1400
1500
1600T(°C)
L (liquid)
α(FCC solid solution)
L + αliquidus
solidus
٢٠٢Chapter 3 -
wt% Ni20 40 60 80 10001000
1100
1200
1300
1400
1500
1600T(°C)
L (liquid)
α(FCC solid solution)
L + αliquidus
solidusCu-Niphase
diagram
Phase Diagrams:# and types of phases
• Rule 1: If we know T and Co, then we know:--the # and types of phases present.
• Examples:A(1100°C, 60):
1 phase: α
B(1250°C, 35): 2 phases: L + α
Adapted from Fig. 9.3(a), Callister 7e.(Fig. 9.3(a) is adapted from Phase Diagrams of Binary Nickel Alloys, P. Nash (Ed.), ASM International, Materials Park, OH, 1991).
B(1
250°
C,3
5)A(1100°C,60)
٢٠٣Chapter 3 -
wt% Ni20
1200
1300
T(°C)
L (liquid)
α(solid)L + α
liquidus
solidus
30 40 50
L + α
Cu-Ni system
Phase Diagrams:composition of phases
• Rule 2: If we know T and Co, then we know:--the composition of each phase.
• Examples:TA A
35Co
32CL
At TA = 1320°C: Only Liquid (L) CL = Co ( = 35 wt% Ni)
At TB = 1250°C: Both α and LCL = C liquidus ( = 32 wt% Ni here) Cα = Csolidus ( = 43 wt% Ni here)
At TD = 1190°C: Only Solid ( α) Cα = Co ( = 35 wt% Ni)
Co = 35 wt% Ni
Adapted from Fig. 9.3(b), Callister 7e.(Fig. 9.3(b) is adapted from Phase Diagramsof Binary Nickel Alloys, P. Nash (Ed.), ASM
International, Materials Park, OH, 1991.)
BTB
DTD
tie line
4Cα3
٢٠٤Chapter 3 -
• Rule 3: If we know T and Co, then we know:--the amount of each phase (given in wt%).
• Examples:
At TA: Only Liquid (L) WL = 100 wt%, Wα = 0
At TD: Only Solid ( α) WL = 0, Wα = 100 wt%
Co = 35 wt% Ni
Adapted from Fig. 9.3(b), Callister 7e.(Fig. 9.3(b) is adapted from Phase Diagrams of Binary Nickel Alloys, P. Nash (Ed.), ASM International, Materials Park, OH, 1991.)
Phase Diagrams:weight fractions of phases
wt% Ni20
1200
1300
T(°C)
L (liquid)
α(solid)L + α
liquidus
solidus
30 40 50
L + α
Cu-Ni system
TA A
35Co
32CL
BTB
DTD
tie line
4Cα3
R S
At TB: Both α and L
% 7332433543 wt=
−−
=
= 27 wt%
WL = SR +S
Wα = RR +S
٢٠٥Chapter 3 -
• Tie line – connects the phases in equilibrium with each other - essentially an isotherm
The Lever Rule
How much of each phase?Think of it as a lever (teeter-totter)
ML Mα
R S
RMSM L ⋅=⋅α
L
L
LL
LL CC
CCSR
RWCCCC
SRS
MMMW
−−
=+
=−−
=+
=+
=α
αα
α
α
00
wt% Ni20
1200
1300
T(°C)
L (liquid)
α(solid)L + α
liquidus
solidus
30 40 50
L + αB
TB
tie line
CoCL Cα
SR
Adapted from Fig. 9.3(b), Callister 7e.
٢٠٦Chapter 3 -
wt% Ni20
1200
1300
30 40 501100
L (liquid)
α(solid)
L + α
L + α
T(°C)
A
35Co
L: 35wt%NiCu-Ni
system
• Phase diagram:Cu-Ni system.
• System is:--binary
i.e., 2 components:Cu and Ni.
--isomorphousi.e., completesolubility of onecomponent inanother; α phasefield extends from0 to 100 wt% Ni.
Adapted from Fig. 9.4, Callister 7e.
• ConsiderCo = 35 wt%Ni.
Ex: Cooling in a Cu-Ni Binary
46354332
α: 43 wt% Ni
L: 32 wt% Ni
L: 24 wt% Ni
α: 36 wt% Ni
Bα: 46 wt% NiL: 35 wt% Ni
C
D
E
24 36
٢٠٧Chapter 3 -
• Cα changes as we solidify.• Cu-Ni case:
• Fast rate of cooling:Cored structure
• Slow rate of cooling:Equilibrium structure
First α to solidify has Cα = 46 wt% Ni.Last α to solidify has Cα = 35 wt% Ni.
Cored vs Equilibrium Phases
First α to solidify: 46 wt% Ni
Uniform Cα:
35 wt% Ni
Last α to solidify: < 35 wt% Ni
٢٠٨Chapter 3 -
: Min. melting TE
2 componentshas a special compositionwith a min. melting T.
Adapted from Fig. 9.7, Callister 7e.
Binary-Eutectic Systems
• Eutectic transitionL(CE) α(CαE) + β(CβE)
• 3 single phase regions (L, α, β)
• Limited solubility: α: mostly Cu β: mostly Ag
• TE : No liquid below TE
• CE
composition
Ex.: Cu-Ag systemCu-Agsystem
L (liquid)
α L + α L+ββ
α + β
Co , wt% Ag20 40 60 80 1000
200
1200T(°C)
400
600
800
1000
CE
TE 8.0 71.9 91.2779°C
٢٠٩Chapter 3 -
L+αL+β
α + β
200
T(°C)
18.3
C, wt% Sn20 60 80 1000
300
100
L (liquid)
α 183°C61.9 97.8
β
• For a 40 wt% Sn-60 wt% Pb alloy at 150°C, find...--the phases present: Pb-Sn
system
EX: Pb-Sn Eutectic System (1)
α + β--compositions of phases:
CO = 40 wt% Sn
--the relative amountof each phase:
150
40Co
11Cα
99Cβ
SR
Cα = 11 wt% SnCβ = 99 wt% Sn
Wα=Cβ - COCβ - Cα
= 99 - 4099 - 11 = 59
88 = 67 wt%
SR+S =
Wβ =CO - Cα
Cβ - Cα=R
R+S
= 2988
= 33 wt%= 40 - 1199 - 11
Adapted from Fig. 9.8, Callister 7e.
٢١٠Chapter 3 -
L+β
α + β
200
T(°C)
C, wt% Sn20 60 80 1000
300
100
L (liquid)
α βL+α
183°C
• For a 40 wt% Sn-60 wt% Pb alloy at 200°C, find...--the phases present: Pb-Sn
system
Adapted from Fig. 9.8, Callister 7e.
EX: Pb-Sn Eutectic System (2)
α + L--compositions of phases:
CO = 40 wt% Sn
--the relative amountof each phase:
Wα =CL - CO
CL - Cα=
46 - 4046 - 17
=629 = 21 wt%
WL =CO - Cα
CL - Cα=
2329 = 79 wt%
40Co
46CL
17Cα
220SR
Cα = 17 wt% SnCL = 46 wt% Sn
٢١١Chapter 3 -
• Co < 2 wt% Sn• Result:
--at extreme ends--polycrystal of α grains
i.e., only one solid phase.
Adapted from Fig. 9.11, Callister 7e.
Microstructures in Eutectic Systems: I
0
L+ α200
T(°C)
Co, wt% Sn10
2
20Co
300
100
L
α
30
α+β
400
(room T solubility limit)
TE(Pb-SnSystem)
αL
L: Co wt% Sn
α: Co wt% Sn
٢١٢Chapter 3 -
• 2 wt% Sn < Co < 18.3 wt% Sn• Result:§ Initially liquid + α§ then α alone§ finally two phasesØ α polycrystalØ fine β-phase inclusions
Adapted from Fig. 9.12, Callister 7e.
Microstructures in Eutectic Systems: II
Pb-Snsystem
L + α
200
T(°C)
Co , wt% Sn10
18.3
200Co
300
100
L
α
30
α+ β
400
(sol. limit at TE)
TE
2(sol. limit at Troom)
Lα
L: Co wt% Sn
αβ
α: Co wt% Sn
٢١٣Chapter 3 -
• Co = CE• Result: Eutectic microstructure (lamellar structure)
--alternating layers (lamellae) of α and β crystals.
Adapted from Fig. 9.13, Callister 7e.
Microstructures in Eutectic Systems: III
Adapted from Fig. 9.14, Callister 7e.160µm
Micrograph of Pb-Sneutectic microstructure
Pb-Snsystem
L + β
α + β
200
T(°C)
C, wt% Sn20 60 80 1000
300
100
L
α βL+α
183°C
40
TE
18.3
α: 18.3 wt%Sn
97.8
β: 97.8 wt% Sn
CE61.9
L: Co wt% Sn
٢١٤Chapter 3 -
Lamellar Eutectic Structure
Adapted from Figs. 9.14 & 9.15, Callister 7e.
٢١٥Chapter 3 -
• 18.3 wt% Sn < Co < 61.9 wt% Sn• Result: α crystals and a eutectic microstructure
Microstructures in Eutectic Systems: IV
18.3 61.9
SR
97.8
SR
primary αeutectic α
eutectic β
WL = (1- Wα) = 50 wt%
Cα = 18.3 wt% SnCL = 61.9 wt% Sn
SR + S
Wα= = 50 wt%
• Just above TE :
• Just below TE :Cα = 18.3 wt% SnCβ = 97.8 wt% Sn
SR + S
Wα= = 73 wt%
Wβ = 27 wt%Adapted from Fig. 9.16, Callister 7e.
Pb-Snsystem
L+β200
T(°C)
Co, wt% Sn
20 60 80 1000
300
100
L
α βL+α
40
α+β
TE
L: Co wt% Sn LαLα
٢١٦Chapter 3 -
L+αL+β
α + β
200
Co, wt% Sn20 60 80 1000
300
100
L
α βTE
40
(Pb-SnSystem)
Hypoeutectic & Hypereutectic
Adapted from Fig. 9.8, Callister 7e. (Fig. 9.8 adapted from Binary Phase Diagrams, 2nd ed., Vol. 3, T.B. Massalski (Editor-in-Chief), ASM International, Materials Park, OH, 1990.)
160 µmeutectic micro-constituent
Adapted from Fig. 9.14, Callister 7e.
hypereutectic: (illustration only)
β
ββ
ββ
β
Adapted from Fig. 9.17, Callister 7e. (Illustration only)
(Figs. 9.14 and 9.17 from Metals Handbook, 9th ed.,Vol. 9, Metallography and Microstructures, American Society for Metals, Materials Park, OH, 1985.)
175 µm
α
α
α
αα
α
hypoeutectic: Co = 50 wt% Sn
Adapted from Fig. 9.17, Callister 7e.
T(°C)
61.9eutectic
eutectic: Co =61.9wt% Sn
٢١٧Chapter 3 -
Intermetallic Compounds
Mg2Pb
Note: intermetallic compound forms a line - not an area -because stoichiometry (i.e. composition) is exact.
Adapted from Fig. 9.20, Callister 7e.
٢١٨Chapter 3 -
Eutectoid & Peritectic• Eutectic - liquid in equilibrium with two
solidsL α + β
coolheat
intermetallic compound - cementite
coolheat
• Eutectoid - solid phase in equation with two solid phasesS2 S1+S3
γ α + Fe3C (727ºC)
cool
heat
• Peritectic - liquid + solid 1 à solid 2 (Fig 9.21)S1 + L S2
δ + L γ (1493ºC)
٢١٩Chapter 3 -
Eutectoid & Peritectic
Cu-Zn Phase diagram
Adapted from Fig. 9.21, Callister 7e.
Eutectoid transition δ γ + ε
Peritectic transition γ + L δ
٢٢٠Chapter 3 -
Iron-Carbon (Fe-C) Phase Diagram• 2 important
points
-Eutectoid (B):γ ⇒ α +Fe3C
-Eutectic (A):L ⇒ γ +Fe3C
Adapted from Fig. 9.24,Callister 7e.
Fe3C
(cem
entit
e)
1600
1400
1200
1000
800
600
4000 1 2 3 4 5 6 6.7
L
γ (austenite)
γ+L
γ+Fe3C
α+Fe3C
α+γ
L+Fe3C
δ
(Fe) Co, wt% C
1148°C
T(°C)
α 727°C = Teutectoid
ASR
4.30Result: Pearlite = alternating layers of α and Fe3C phases
120 µm
(Adapted from Fig. 9.27, Callister 7e.)
γ γγγ
R S
0.76
Ceu
tect
oid
B
Fe3C (cementite-hard)α (ferrite-soft)
٢٢١Chapter 3 -
Hypoeutectoid Steel
Adapted from Figs. 9.24 and 9.29,Callister 7e. (Fig. 9.24 adapted from Binary Alloy Phase Diagrams, 2nd ed., Vol. 1, T.B. Massalski (Ed.-in-Chief), ASM International, Materials Park, OH, 1990.)
Fe3C
(cem
entit
e)
1600
1400
1200
1000
800
600
4000 1 2 3 4 5 6 6.7
L
γ (austenite)
γ+L
γ + Fe3C
α+ Fe3C
L+Fe3C
δ
(Fe) Co, wt% C
1148°C
T(°C)
α727°C
(Fe-C System)
C0
0.76
Adapted from Fig. 9.30,Callister 7e.proeutectoid ferritepearlite
100 µm Hypoeutectoidsteel
R S
α
wα =S/(R+S)wFe3C =(1-wα)
wpearlite = wγpearlite
r s
wα =s/(r+s)wγ =(1- wα)
γγ γ
γα
αα
γγγ γ
γ γγγ
٢٢٢Chapter 3 -
Hypereutectoid Steel
Fe3C
(cem
entit
e)
1600
1400
1200
1000
800
600
4000 1 2 3 4 5 6 6.7
L
γ (austenite)
γ+L
γ +Fe3C
α +Fe3C
L+Fe3C
δ
(Fe) Co, wt%C
1148°C
T(°C)
α
Adapted from Figs. 9.24 and 9.32,Callister 7e. (Fig. 9.24 adapted from Binary Alloy Phase Diagrams, 2nd ed., Vol. 1, T.B. Massalski (Ed.-in-Chief), ASM International, Materials Park, OH, 1990.)
(Fe-C System)
0.76 Co
Adapted from Fig. 9.33,Callister 7e.
proeutectoid Fe3C
60 µmHypereutectoid steel
pearlite
R S
wα =S/(R+S)wFe3C =(1-wα)
wpearlite = wγpearlite
sr
wFe3C =r /(r+s)wγ =(1-w Fe3C)
Fe3C
γγγ γ
γγγ γ
γγγ γ
٢٢٣Chapter 3 -
Example: Phase Equilibria
For a 99.6 wt% Fe-0.40 wt% C at a temperature just below the eutectoid, determine the following
a) composition of Fe3C and ferrite (α)b) the amount of carbide (cementite) in
grams that forms per 100 g of steelc) the amount of pearlite and
proeutectoid ferrite (α)
٢٢٤Chapter 3 -
Chapter 9 – Phase EquilibriaSolution:
g 3.94g 5.7 CFe
g7.5100 022.07.6022.04.0
100xCFe
CFe
3
CFe3
3
3
=α
=
=−−
=
−−
=α+ α
α
x
CCCCo
b) the amount of carbide (cementite) in grams that forms per 100 g of steel
a) composition of Fe3C and ferrite (α)
CO = 0.40 wt% CCα = 0.022 wt% CCFe C = 6.70 wt% C
3
Fe3C
(cem
entit
e)
1600
1400
1200
1000
800
600
4000 1 2 3 4 5 6 6.7
L
γ (austenite)
γ+L
γ + Fe3C
α + Fe3C
L+Fe3C
δ
Co , wt% C
1148°C
T(°C)
727°C
CO
R S
CFe C3Cα
٢٢٥Chapter 3 -
Chapter 9 – Phase Equilibriac. the amount of pearlite and proeutectoid ferrite (α)
note: amount of pearlite = amount of γ just above TE
Co = 0.40 wt% CCα = 0.022 wt% CCpearlite = Cγ = 0.76 wt% C
γγ + α
=Co −CαCγ −Cα
x 100 = 51.2 g
pearlite = 51.2 gproeutectoid α = 48.8 g
Fe3C
(cem
entit
e)
1600
1400
1200
1000
800
600
4000 1 2 3 4 5 6 6.7
L
γ (austenite)
γ+L
γ + Fe3C
α + Fe3C
L+Fe3C
δ
Co , wt% C
1148°C
T(°C)
727°C
CO
R S
CγCα
٢٢٦Chapter 3 -
• Phase diagrams are useful tools to determine:--the number and types of phases,--the wt% of each phase,--and the composition of each phase for a given T and composition of the system.
• Alloying to produce a solid solution usually--increases the tensile strength (TS)--decreases the ductility.
• Binary eutectics and binary eutectoids allow fora range of microstructures.
Summary