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Practice Midterm 02 Solutions 2000<br />

Question 1 (30 points)<br />

<strong>Use</strong> <strong>the</strong> <strong>grid</strong> <strong>below</strong> <strong>to</strong> <strong>draw</strong> <strong>the</strong> <strong>Al</strong>-<strong>Li</strong> <strong>phase</strong> <strong>diagram</strong> <strong>based</strong> <strong>upon</strong> <strong>the</strong> following<br />

experimental observations (all compositions in weight %). Label all <strong>phase</strong> fields.<br />

T(°C)<br />

800<br />

600<br />

400<br />

200<br />

Pure <strong>Al</strong> melts at 660°C; pure <strong>Li</strong> melts at 181°C. At 600°C, liquid of 10 %<strong>Li</strong> solidifies <strong>to</strong><br />

form α <strong>phase</strong> of 4 %<strong>Li</strong> and δ <strong>phase</strong> of 20 %<strong>Li</strong>. Pure δ <strong>phase</strong> containing 20 %<strong>Li</strong> melts<br />

congruently at 718°C. At 521°C, γ <strong>phase</strong> containing 34 %<strong>Li</strong> melts <strong>to</strong> form δ <strong>phase</strong> of 24<br />

%<strong>Li</strong> and liquid <strong>phase</strong> of 47 %<strong>Li</strong>. At 620°C, a 30 % <strong>Li</strong> alloy has equal parts of liquid<br />

<strong>phase</strong> and δ <strong>phase</strong>, while at 260°C, a 60 %<strong>Li</strong> alloy has equal parts of liquid <strong>phase</strong> and γ<br />

<strong>phase</strong>. At 179°C, liquid containing 98 %<strong>Li</strong> solidifies <strong>to</strong> form γ <strong>phase</strong> (34 %<strong>Li</strong>) and β<br />

<strong>phase</strong> (99 %<strong>Li</strong>). At 0°C, <strong>Al</strong> can dissolve up <strong>to</strong> 3 % <strong>Li</strong>, while <strong>Li</strong> can dissolve no more than<br />

0.5 % <strong>Al</strong>; however. <strong>Al</strong>so at 0°C, <strong>the</strong> solubility of <strong>Li</strong> in <strong>the</strong> δ <strong>phase</strong> ranges from 20 <strong>to</strong> 22<br />

%<strong>Li</strong>.<br />

α +L<br />

α<br />

α + δ<br />

L+δ<br />

δ<br />

δ +L<br />

γ<br />

<strong>Li</strong>quid<br />

δ + γ L+β<br />

β<br />

<strong>Al</strong> 20 40 60 80<br />

<strong>Li</strong><br />

wt% <strong>Li</strong><br />

γ +L<br />

γ + β<br />

page 1 of 8


Question 2 (20 points)<br />

T(°C)<br />

800<br />

0.02<br />

600<br />

α<br />

400<br />

(ferrite)<br />

200<br />

Practice Midterm 02 Solutions 2000<br />

Illustrate <strong>the</strong> microstructural evolution resulting from cooling a hypereutec<strong>to</strong>id AISI<br />

1095 steel through <strong>the</strong> eutec<strong>to</strong>id decomposition iso<strong>the</strong>rm. <strong>Use</strong> <strong>the</strong> templates at right,<br />

which show <strong>the</strong> prior austenite grains, and accurately <strong>draw</strong> <strong>the</strong> equilibrium<br />

microstructures at each of <strong>the</strong> temperatures identified on <strong>the</strong> right. Label each <strong>phase</strong>,<br />

and label all relevant microstructural constituents by <strong>the</strong>ir common metallurgical<br />

names.<br />

1600<br />

1538°<br />

1495°<br />

δ<br />

1400<br />

1394°<br />

1200<br />

γ<br />

(austenite)<br />

1000<br />

0.77<br />

γ +<br />

2.1<br />

1148°<br />

α +<br />

727°<br />

4.3<br />

Fe 1 2 3 4 5 6 7<br />

wt% C<br />

L<br />

γ +<br />

L+<br />

6.7<br />

Fe3<br />

(cementite)<br />

Austenite<br />

1150°C<br />

100% Austenite<br />

Proeutec<strong>to</strong>id cementite<br />

at grain boundaries<br />

750°C<br />

92% austenite; 8% cementite<br />

Proeutec<strong>to</strong>id cementite<br />

Pearlite<br />

450°C<br />

86% ferrite; 14%<br />

cementite<br />

Proeutec<strong>to</strong>id cementite<br />

Pearlite<br />

25°C<br />

86% ferrite; 14% cementite<br />

page 2 of 8


Question 3 (30 points)<br />

Sketch and label <strong>the</strong> iso<strong>the</strong>rmal cooling curves for <strong>the</strong> same AISI 1095 steel that<br />

produce <strong>the</strong> following microstructures: Note that <strong>the</strong>re are three TTT curves here.<br />

Label <strong>the</strong> first with a) and b), <strong>the</strong> second with c) and d), and <strong>the</strong> third with e) and f).<br />

a) 100% martensite<br />

b) 5% proeuctec<strong>to</strong>id cementite and 95% martensite<br />

T (°C)<br />

800<br />

700<br />

600<br />

500<br />

400<br />

300<br />

200<br />

100<br />

840°<br />

727°<br />

Ms<br />

M90<br />

1 sec<br />

γ + Fe3C<br />

α + Fe3C<br />

1 min 1 hour<br />

1 day<br />

0.1 1 10 102 103 104 105 0<br />

(a) (b)<br />

Time (sec)<br />

Practice Midterm 02 Solutions 2000<br />

page 3 of 8


c) 25% coarse pearlite, 75% martensite<br />

d) 100% fine pearlite<br />

T (°C)<br />

800<br />

700<br />

600<br />

500<br />

400<br />

300<br />

200<br />

100<br />

840°<br />

727°<br />

Ms<br />

M90<br />

1 sec<br />

γ + Fe3C<br />

α + Fe3C<br />

1 min 1 hour<br />

1 day<br />

0.1 1 10 102 103 104 105 0<br />

Time (sec)<br />

(c) (d)<br />

Practice Midterm 02 Solutions 2000<br />

page 4 of 8


e) 25% upper bainite and 75% tempered martensite<br />

f) 25% fine pearlite, 25% lower bainite, 50% martensite<br />

T (°C)<br />

800<br />

700<br />

600<br />

500<br />

400<br />

300<br />

200<br />

100<br />

840°<br />

727°<br />

Ms<br />

M90<br />

1 sec<br />

γ + Fe3C<br />

α + Fe3C<br />

1 min 1 hour<br />

1 day<br />

0.1 1 10 102 103 104 105 0<br />

Time (sec)<br />

(f)<br />

(e)<br />

Practice Midterm 02 Solutions 2000<br />

page 5 of 8


Question 4 (20 points)<br />

Mark <strong>the</strong> checkbox next <strong>to</strong> <strong>the</strong> best answer (only one) in each case.<br />

a) Martensite is a metastable <strong>phase</strong> produced in ferrous alloys by<br />

holding at a specific temperature for a specific time<br />

heating <strong>to</strong> a specific temperature over a specific time<br />

☒ cooling <strong>to</strong> a specific temperature over a specific time<br />

b) Martensite can be tempered by<br />

heating <strong>to</strong> a specific temperature over a specific time<br />

cooling <strong>to</strong> a specific temperature over a specific time<br />

☒ holding at a specific temperature for a specific time<br />

c) The microstructure of tempered martensite consists of<br />

pearlite and bainite<br />

only bainite<br />

☒ nei<strong>the</strong>r pearlite nor bainite<br />

d) Martensite is strong because<br />

it is not an equilibrium <strong>phase</strong><br />

☒ it presents many obstacles <strong>to</strong> dislocation motion<br />

it is a highly dis<strong>to</strong>rted arrangement of Fe and C a<strong>to</strong>ms<br />

e) Ferrous alloys can be precipitation-hardened by<br />

holding in <strong>the</strong> austenite+ferrite two-<strong>phase</strong> field<br />

☒ aging <strong>to</strong> produce alloy carbides<br />

quenching <strong>to</strong> produce martensite<br />

f) Nonferrous metallic alloys can be precipitation-hardened by<br />

☒ solutionizing, quenching and aging<br />

solutionizing slow-cooling and quenching<br />

quenching, aging and quenching<br />

g) Ni-base superalloys are known for <strong>the</strong>ir superior<br />

☒ strength at elevated temperatures<br />

<strong>to</strong>ughness at room temperature<br />

wear-resistant surface finish<br />

Practice Midterm 02 Solutions 2000<br />

page 6 of 8


h) <strong>Al</strong>-base alloys are protected from oxidation by<br />

☒ a passivating oxide film<br />

a high density of second <strong>phase</strong> particles<br />

an ASTM standard requiring painted surfaces<br />

i) During annealing, <strong>the</strong> driving force for <strong>the</strong> recovery stage is<br />

☒ reduction in strain energy<br />

reduction in surface energy<br />

reduction in chemical potential<br />

j) During annealing, <strong>the</strong> driving force for <strong>the</strong> recrystallization stage is<br />

☒ reduction in strain energy<br />

reduction in surface energy<br />

reduction in chemical potential<br />

k) During annealing, <strong>the</strong> driving force for <strong>the</strong> grain growth stage is<br />

reduction in strain energy<br />

☒ reduction in surface energy<br />

reduction in chemical potential<br />

l) Ceramics are often formed in<strong>to</strong> complex parts by sintering at<br />

one-forth of <strong>the</strong> melting temperature<br />

☒ one-third of <strong>the</strong> melting temperature<br />

two-thirds of <strong>the</strong> melting temperature<br />

m) Glass-ceramics are subjected <strong>to</strong> an aging treatment in order <strong>to</strong><br />

provide stress-relief<br />

remove surface cracks<br />

☒ precipitate a crystalline <strong>phase</strong><br />

n) The most significant attribute associated with a Griffith crack is<br />

its location at <strong>the</strong> surface<br />

its length<br />

☒ its tip radius<br />

Practice Midterm 02 Solutions 2000<br />

page 7 of 8


o) Addition polymerization is a reaction among small organic molecules involving<br />

isotropic growth<br />

☒ chain growth<br />

step growth<br />

p) Condensation polymerization involves<br />

a rapid “chain reaction”<br />

☒ individual chemical reactions between pairs of reactive monomers<br />

electron transport in <strong>the</strong> condensate<br />

q) The primary role of <strong>the</strong> initia<strong>to</strong>r in a polymerization reaction is <strong>to</strong><br />

begin <strong>the</strong> assembly of mers in<strong>to</strong> chains<br />

☒ convert double bonds in<strong>to</strong> single bonds<br />

nucleate <strong>the</strong> condensation reaction<br />

r) <strong>Li</strong>near polymers are <strong>the</strong> result of bonding between<br />

☒ bifunctional mers<br />

polyfunctional mers<br />

linear mers<br />

s) A block co-polymer can also be described as<br />

a solid solution<br />

☒ a two <strong>phase</strong> alloy<br />

a cubic crystal structure<br />

t) A polymer is described as “viscoelastic” when it shows<br />

☒ slow recovery of strain<br />

viscous fracture<br />

negative modulus of elasticity<br />

Practice Midterm 02 Solutions 2000<br />

page 8 of 8


UNIVERSITY OF CALIFORNIA<br />

College of Engineering<br />

Department of Materials Science and Engineering<br />

Professor R. Gronsky Fall Semester 2001<br />

ENGINEERING 45


E45•Midterm #2<br />

Question 1 The silver-mercury system forms <strong>the</strong> basis of an important biomaterial<br />

known as dental amalgam, which has been used for decades in res<strong>to</strong>rative<br />

dental fillings. The term “amalgam” is frequently used <strong>to</strong> depict many<br />

different alloys of mercury, originating from <strong>the</strong> “amalgamation” process <strong>to</strong><br />

refine ores of <strong>the</strong> precious metals, primarily silver and gold. The finely<br />

crushed ores in aqueous solution are mixed with mercury, allowing <strong>the</strong><br />

mercury <strong>to</strong> alloy with <strong>the</strong> precious metals, forming an amalgam. When <strong>the</strong><br />

amalgam is heated, <strong>the</strong> mercury is driven off as a vapor (collected and<br />

recycled of course), leaving behind pure precious metal “sponge.”<br />

1000<br />

961.93°<br />

800<br />

600<br />

T<br />

(°C)<br />

400<br />

Silver (Ag, Z = 47) is fcc and melts at 961.93°C, mercury (Hg, Z = 80)<br />

freezes at –38.862°C. The equilibrium β <strong>phase</strong> has AgHg s<strong>to</strong>ichiometry and<br />

an hcp Bravais lattice. The equilibrium γ <strong>phase</strong> has Ag2Hg3 s<strong>to</strong>ichiometry and<br />

a bcc Bravais Lattice.<br />

<strong>Use</strong> this information and <strong>the</strong> equilibrium <strong>phase</strong> <strong>diagram</strong> for <strong>the</strong> silver-mercury<br />

binary system due <strong>to</strong> M. Hanson (Constitution of Binary <strong>Al</strong>loys, 2 nd . Edition,<br />

McGraw –Hill, 1958) shown <strong>below</strong> <strong>to</strong> choose <strong>the</strong> best answers for 2 points<br />

each.<br />

(Ag)<br />

200<br />

127°<br />

β<br />

0<br />

γ<br />

-38.9°<br />

-38.862°<br />

(Hg)<br />

-200<br />

Ag 10 20 30 40 50 60 70 80 90 Hg<br />

Weight Percentage Hg<br />

2 of 10<br />

52.4<br />

L<br />

276°<br />

Hg Boiling Point 357°


E45•Midterm #2<br />

a. The number of components in this binary system is<br />

one (1)<br />

two (2)<br />

three (3)<br />

b. The <strong>phase</strong> called (Ag) is actually<br />

pure silver<br />

a silver-mercury solid solution<br />

a metastable <strong>phase</strong><br />

c. Based <strong>upon</strong> <strong>the</strong> Gibbs Phase Rule (P+F = C+2), <strong>the</strong> number of degrees of<br />

freedom available <strong>to</strong> pure Hg at 357°C in this system is<br />

zero (0)<br />

one (1)<br />

two (2)<br />

d. The number of degrees of freedom available <strong>to</strong> a 40 wt.% Ag alloy at 276°C is<br />

zero (0)<br />

one (1)<br />

two (2)<br />

e. The maximum solubility of mercury in silver is<br />

infinitesimally small<br />

undefined because mercury is a liquid at room temperature<br />

established by <strong>the</strong> highest temperature reaction iso<strong>the</strong>rm<br />

f. Both β <strong>phase</strong> and γ <strong>phase</strong> are in equilibrium with liquid Hg at a<br />

monotectic<br />

eutectic<br />

peritectic<br />

g. When β <strong>phase</strong> of 60 wt% Hg melts, it<br />

disappears completely<br />

passes through a β + L two-<strong>phase</strong> equilibrium<br />

generates mercury vapor<br />

h. A dental hygienist “mixes” amalgam immediately before <strong>the</strong> dentist applies it so<br />

that it will “harden” as a complete filling. The hardening process is due <strong>to</strong><br />

solid state diffusion<br />

solidification of liquid Hg<br />

dislocations created during mixing<br />

i. An amalgam of 20 wt % Hg in equilibrium will decompose when heated above<br />

276°C<br />

576 °C<br />

776°C<br />

j. Dental fillings made of silver amalgam are at risk of leaking mercury in<strong>to</strong> <strong>the</strong><br />

mouth if <strong>the</strong> equilibrium mercury concentration exceeds<br />

52.4%<br />

62.4%<br />

72.4%<br />

3 of 10


E45•Midterm #2<br />

Question 2 <strong>Use</strong> <strong>the</strong> same <strong>phase</strong> <strong>diagram</strong> <strong>to</strong> now sketch <strong>the</strong> microstructures expected<br />

during equilibrium solidification of <strong>the</strong> following alloys. The lever rule<br />

construction is important here. Draw a vertical line on <strong>the</strong> <strong>phase</strong> <strong>diagram</strong> for<br />

<strong>the</strong> specified composition and show all tie lines used <strong>to</strong> establish your<br />

equilibrium microstructures. Remember that <strong>the</strong> high temperature<br />

microstructure influences <strong>the</strong> lower temperature microstructure. Clearly label<br />

all <strong>phase</strong>s for full credit.<br />

T = 500°C<br />

85% (Ag)<br />

+ 15% L<br />

T = 25°C<br />

40% (Ag)<br />

+ 60% β<br />

T = 200°C<br />

50% L<br />

+ 50% β<br />

T = 25°C<br />

33% L<br />

+ 67% γ<br />

Each sketch is worth 5 points.<br />

a. Ag-55 wt% Hg<br />

L<br />

(Ag)<br />

b. Hg-20 wt% Ag<br />

β L<br />

γ L<br />

(Ag)<br />

1000<br />

961.93°<br />

800<br />

600<br />

T<br />

(°C)<br />

400<br />

200<br />

127°<br />

β<br />

0<br />

-38.862°<br />

-38.9°<br />

γ<br />

(Hg)<br />

-200<br />

Ag 10 20 30 40 50 60 70 80 90 Hg<br />

Weight Percentage Hg<br />

1000<br />

961.93°<br />

800<br />

600<br />

T<br />

(°C)<br />

400<br />

Note that in all cases here, <strong>the</strong>re are no microstructural remnants from higher<br />

temperature reactions <strong>to</strong> influence <strong>the</strong> products. <strong>Al</strong>l are peritectic reactions, which<br />

require longer times <strong>to</strong> reach equilibrium, but time is not a fac<strong>to</strong>r here since we are<br />

working from an equilibrium <strong>phase</strong> <strong>diagram</strong>.<br />

4 of 10<br />

(Ag)<br />

(Ag)<br />

52.4<br />

52.4<br />

L<br />

276°<br />

Hg Boiling Point 357°<br />

200<br />

127°<br />

β<br />

0<br />

-38.862°<br />

-38.9°<br />

γ<br />

(Hg)<br />

-200<br />

Ag 10 20 30 40 50 60 70 80 90 Hg<br />

Weight Percentage Hg<br />

L<br />

276°<br />

Hg Boiling Point 357°


E45•Midterm #2<br />

Question 3 The same TTT curve for a plain carbon steel of eutec<strong>to</strong>id composition is<br />

reproduced multiple times <strong>below</strong>. Draw directly on <strong>the</strong>se plots <strong>the</strong> cooling<br />

curves corresponding <strong>to</strong> <strong>the</strong> specified treatments. Remember that TTT curves<br />

are appropriate for iso<strong>the</strong>rmal transformations only. The actual start and<br />

termination of <strong>the</strong> decomposition of austenite during continuous cooling<br />

occurs at slightly lower temperatures and longer times than shown here.<br />

Each curve is worth 5 points.<br />

a. Austempering, a commercial<br />

treatment used <strong>to</strong> avoid quench<br />

cracking. Show and label <strong>the</strong><br />

curves corresponding <strong>to</strong> both<br />

<strong>the</strong> surface and <strong>the</strong> interior of a<br />

thick cross section steel beam.<br />

b. Martempering, a commercial<br />

treatment used <strong>to</strong> avoid quench<br />

cracking. Show and label <strong>the</strong><br />

curves corresponding <strong>to</strong> both<br />

<strong>the</strong> surface and <strong>the</strong> interior of a<br />

thick cross section steel beam.<br />

Both (a) and (b) are <strong>the</strong> classic, traditional methods used widely throughout <strong>the</strong><br />

engineering community <strong>to</strong> prevent quench-cracking in large cross-section steel<br />

components.<br />

5 of 10<br />

°C<br />

800<br />

700<br />

600<br />

500<br />

727°<br />

γ<br />

γ<br />

α + Fe 3 C<br />

400<br />

upper bainite<br />

Surface Interior<br />

300<br />

215°<br />

200<br />

Transform<br />

lower<br />

bainite<br />

100<br />

martensite<br />

sec min<br />

Quench<br />

hour day<br />

°C<br />

800<br />

700<br />

600<br />

500<br />

0.1 1 10 10 2 10 3 10 4 10 5<br />

727°<br />

γ<br />

γ<br />

time (sec)<br />

α + Fe 3 C<br />

coarse pearlite<br />

fine pearlite<br />

400<br />

upper Temper bainite<br />

Surface Interior<br />

300<br />

215°<br />

200<br />

martensite<br />

100 sec<br />

Quench<br />

min hour<br />

lower<br />

bainite<br />

day<br />

0.1 1 10 10 2 10 3 10 4 10 5<br />

time (sec)<br />

coarse pearlite<br />

fine pearlite


E45•Midterm #2<br />

c. An “interrupted quench”<br />

technique that would generate a<br />

final microstructure of 50%<br />

lower bainite and 50% fine<br />

pearlite. In this case <strong>the</strong><br />

workpiece is a small diameter<br />

rod <strong>to</strong> be used as an axle in a<br />

mo<strong>to</strong>r-genera<strong>to</strong>r set.<br />

The only way this treatment can be an “interrupted quench” is <strong>to</strong> begin with <strong>the</strong> high<br />

temperature transformation (fine pearlite), holding iso<strong>the</strong>rmally until <strong>the</strong> reaction<br />

progresses half way between <strong>the</strong> start and finish lines. Note that this amounts <strong>to</strong><br />

only a few seconds. The untransformed austenite is <strong>the</strong>n lowered in temperature<br />

and held iso<strong>the</strong>rmally until it fully transforms <strong>to</strong> lower bainite as shown.<br />

d. An approximation. Show<br />

without compensation for<br />

continuous cooling <strong>the</strong> T-t<br />

trajec<strong>to</strong>ry for a sample that was<br />

left in <strong>the</strong> furnace during a<br />

power outage. The initial<br />

temperature was 800°C at<br />

midnight when <strong>the</strong> power failed.<br />

The cooling rate for <strong>the</strong> wellinsulated<br />

furnace was previously<br />

calibrated at 100°C / minute.<br />

The sample was recovered 8<br />

hours later at <strong>the</strong> start of <strong>the</strong><br />

daylight shift.<br />

In question (d), note that a linear rate of 100°C / min is dramatically curved on <strong>the</strong><br />

log scale used here. <strong>Al</strong>though this is only an “approximation” because <strong>the</strong> cooling<br />

treatment is not iso<strong>the</strong>rmal, it is reasonable <strong>to</strong> expect that <strong>the</strong> final microstructure<br />

would be fully pearlitic, and ra<strong>the</strong>r coarse.<br />

6 of 10<br />

°C<br />

800<br />

700<br />

600<br />

500<br />

400<br />

300<br />

200<br />

100<br />

°C<br />

800<br />

700<br />

600<br />

500<br />

400<br />

300<br />

200<br />

100<br />

727°<br />

γ<br />

215°<br />

γ<br />

α + Fe 3 C<br />

martensite<br />

sec min hour day<br />

0.1 1 10 10 2 10 3 10 4 10 5<br />

727°<br />

γ<br />

215°<br />

50%<br />

γ<br />

time (sec)<br />

coarse pearlite<br />

fine pearlite<br />

upper bainite<br />

lower<br />

remaining 50%<br />

bainite<br />

100°C/min<br />

coarse pearlite<br />

α + Fe3C fine pearlite<br />

martensite<br />

sec min hour day<br />

0.1 1 10 10 2 10 3 10 4 10 5<br />

time (sec)<br />

upper bainite<br />

lower<br />

bainite


E45•Midterm #2<br />

Question 4 Pure zirconia undergoes an allotropic transformation at 1000°C from a high<br />

temperature tetragonal structure <strong>to</strong> a low temperature monoclinic structure.<br />

A massive volume expansion <strong>upon</strong> cooling through <strong>the</strong> tetragonal-<strong>to</strong>monoclinic<br />

transformation literally results in <strong>the</strong> self destruction of <strong>the</strong> crystal.<br />

Thermal cycling through <strong>the</strong> transformation temperature pulverizes <strong>the</strong><br />

material in<strong>to</strong> a fine powder.<br />

However, alloying zirconia with 25 mol % calcia yields a cubic <strong>phase</strong> that<br />

persists up <strong>to</strong> its melting point with no structural instabilities. This<br />

“stabilized” zirconia is a very popular structural ceramic for that reason.<br />

T<br />

(°C)<br />

2500<br />

2000<br />

Tetragonal<br />

ZrO2 SS<br />

1500<br />

1000<br />

Monoclinic<br />

ZrO2 SS<br />

500<br />

ZrO 2<br />

10<br />

Cubic<br />

ZrO 2 SS<br />

20 30 40 50<br />

Mole Percentage CaO<br />

a. Using this information, explain how “partially-stabilized” zirconia, which<br />

contains some cubic, some tetragonal, and some monoclinic <strong>phase</strong>s, is<br />

prepared. Be specific, using <strong>the</strong> equilibrium <strong>phase</strong> <strong>diagram</strong> above and your<br />

understanding of <strong>phase</strong> transformation kinetics for 10 points.<br />

The <strong>phase</strong> <strong>diagram</strong> indicates that it is not possible <strong>to</strong> find all three <strong>phase</strong>s (cubic,<br />

tetragonal and monoclinic) in equilibrium. So this is a problem involving kinetics. At<br />

CaO concentrations less than 15 mol%, monoclinic and cubic <strong>phase</strong>s are in equilibrium<br />

at room temperature. To include a tetragonal <strong>phase</strong> at room temperature, all that is<br />

required is <strong>to</strong> heat above <strong>the</strong> eutec<strong>to</strong>id temperature (900°C) where tetragonal<br />

<strong>phase</strong> is in equilibrium, <strong>the</strong>n “quench” <strong>to</strong> retain it kinetically at lower temperature.<br />

7 of 10<br />

L<br />

ZrCaO 3


E45•Midterm #2<br />

b. For ano<strong>the</strong>r 10 points, explain in detail how <strong>the</strong> partially-stabilized zirconia<br />

structure leads <strong>to</strong> “transformation <strong>to</strong>ughening” of an o<strong>the</strong>rwise brittle ceramic<br />

material. Comment specifically on <strong>the</strong> volume expansion associated with <strong>the</strong><br />

tetragonal <strong>to</strong> monoclinic transformation, and its role in causing an increase in<br />

fracture <strong>to</strong>ughness. Recall that fracture <strong>to</strong>ughness refers <strong>to</strong> <strong>the</strong> performance<br />

of a material with pre-existing flaws, and focus your attention on <strong>the</strong> crack<br />

shown in <strong>the</strong> following sketch.<br />

Recalling from above that only <strong>the</strong> cubic<br />

and monoclinic <strong>phase</strong>s are in equilibrium<br />

at room temperature, <strong>the</strong> metastable<br />

tetragonal <strong>phase</strong> becomes <strong>the</strong> key<br />

constituent in this problem.<br />

As <strong>the</strong> crack advances through <strong>the</strong><br />

forest of tetragonal precipitates, it<br />

relaxes <strong>the</strong> constraints of <strong>the</strong> cubic<br />

monoclinic<br />

matrix confining <strong>the</strong> tetragonal<br />

particles. This relaxation induces <strong>the</strong><br />

cubic matrix<br />

transformation of <strong>the</strong> metastable<br />

tetragonal <strong>phase</strong> <strong>to</strong> <strong>the</strong> equilibrium<br />

monoclinic <strong>phase</strong> in <strong>the</strong> vicinity of <strong>the</strong><br />

crack tip. The resulting volume<br />

expansion (as described in <strong>the</strong> problem<br />

statement) exerts a closing force on<br />

<strong>the</strong> crack tip, retarding its progress<br />

through <strong>the</strong> ceramic. It is for this reason that <strong>the</strong> mechanism described here is<br />

known as “transformation <strong>to</strong>ughening.” The transformation from <strong>the</strong> tetragonal <strong>to</strong><br />

monoclinic <strong>phase</strong>s gives partially stabilized zirconia (PSZ) <strong>the</strong> highest fracture<br />

<strong>to</strong>ugnhness of all structural ceramics.<br />

8 of 10<br />

tetragonal


E45•Midterm #2<br />

Question 5 Polymers or “many mers” may result from chain growth, also known as<br />

addition polymerization, which generates linear or branched polymers, or<br />

from step growth, also known as condensation polymerization, which<br />

generates network polymers. The mechanical properties of polymers are, like<br />

all materials, linked <strong>to</strong> <strong>the</strong>ir structure.<br />

(a) The styrene mer is shown schematically <strong>below</strong>. Show how polystyrene results<br />

from a polymerization reaction by sketching <strong>the</strong> final product containing at<br />

least five mers. Is polystyrene a (check all that apply)<br />

linear,<br />

branched, or<br />

network polymer?<br />

Showing <strong>the</strong> correct polymeric structure and checking <strong>the</strong> correct box(es)<br />

above earns 10 points.<br />

The signature feature of <strong>the</strong> styrene mer that marks it as a candidate for<br />

polymerization is its double carbon bond. Conversion of this bond in<strong>to</strong> two single<br />

bonds functionalizes <strong>the</strong> mer. Its resulting bifunctional character makes it a<br />

candidate for chain growth in<strong>to</strong> a linear polymer, just like polyethylene. A segment<br />

of <strong>the</strong> polymer backbone chain is shown <strong>below</strong>.<br />

H H<br />

C C<br />

H<br />

H C CH 2<br />

This particular configuration is <strong>the</strong> isotactic one, with all of <strong>the</strong> large side groups on<br />

<strong>the</strong> same side. The syndiotactic configuration shown <strong>below</strong>, and <strong>the</strong> atactic<br />

configuration (random) are also acceptable.<br />

H H<br />

C C<br />

H<br />

H H<br />

C C<br />

H<br />

H<br />

H<br />

C C<br />

H<br />

9 of 10<br />

H H<br />

C C<br />

H<br />

H H<br />

C C<br />

H<br />

H H<br />

C C<br />

H<br />

H<br />

H<br />

C C<br />

H<br />

H H<br />

C C<br />

H<br />

H H<br />

C C<br />

H


E45•Midterm #2<br />

(b) Polymers, like metals and ceramics, can be described by a lattice and motif,<br />

but <strong>the</strong>y are never fully crystalline. In fact, numerous polymers are<br />

completely amorphous. Those that possess some crystallinity have <strong>the</strong>ir<br />

polymeric chains arranged in a regular, parallel alignment, and <strong>the</strong>se<br />

crystallites or “fringed micelles” are embedded in an amorphous matrix.<br />

A partially crystallized <strong>the</strong>rmoplastic polymer shows “viscoelastic” mechanical<br />

behavior. Using <strong>the</strong> coordinate axes <strong>below</strong>, plot <strong>the</strong> elastic modulus as a<br />

function of temperature for a viscoelastic polymer. Note particularly <strong>the</strong><br />

changes seen at <strong>the</strong> glass transition temperature and <strong>the</strong> melting<br />

temperature. On your plot, label <strong>the</strong> four distinct regions of behavior<br />

associated with viscoelasticity, that is, rubbery, viscous, lea<strong>the</strong>ry, and rigid<br />

(or elastic). A correctly labeled plot is worth 10 points.<br />

Modulus<br />

of<br />

Elasticity<br />

(log scale)<br />

T g<br />

Temperature<br />

In its traditional definition, <strong>the</strong> glass transition temperature marks <strong>the</strong> transition<br />

from rigid “crystal-like” <strong>to</strong> viscous “glass-like” mechanical behavior. Crystals deform<br />

by dislocation motion, glasses deform by <strong>the</strong> viscous flow.<br />

At <strong>the</strong> melting point, viscous flow is most obvious because <strong>the</strong> material cannot<br />

sustain its own weight against gravity. The elastic modulus drops <strong>to</strong> zero.<br />

10 of 10<br />

Rigid (or "Elastic")<br />

T m<br />

Lea<strong>the</strong>ry<br />

Rubbery<br />

Viscous


UNIVERSITY OF CALIFORNIA<br />

College of Engineering<br />

Department of Materials Science & Engineering<br />

Professor R. Gronsky Fall Semester, 2005<br />

Engineering 45 Midterm 02<br />

SOLUTIONS<br />

INSTRUCTIONS<br />

LATTICE seating .................. Please be seated with occupied seats <strong>to</strong> your front and back, vacant seats <strong>to</strong> your left and right.<br />

CLOSED BOOK format ...... <strong>Al</strong>l you need are writing instruments and a straightedge. Please s<strong>to</strong>re all books, reference materials,<br />

calcula<strong>to</strong>rs, PDAs, cell phones (OFF), and iPods.<br />

NO DISRUPTION rule ......... Questions cause <strong>to</strong>o much of a disturbance <strong>to</strong> o<strong>the</strong>rs in <strong>the</strong> room. Instead of asking questions,<br />

write any concerns or alternative interpretations in your answers.<br />

PROFESSIONAL pro<strong>to</strong>col ... Engineers do not cheat on <strong>the</strong> job and <strong>the</strong>y certainly don’t cheat on exams.<br />

Do not open until “START” is announced.


E 45 Midterm 02 SOLUTIONS:<br />

1. Defects in Solids (10 points)<br />

Mark ☒ <strong>the</strong> ballot box corresponding <strong>to</strong> <strong>the</strong> best answer.<br />

Two (+2) points for correct answers, -1 if wrong, 0 if blank.<br />

(a) Point defects in solids include<br />

☒ vacancies<br />

☐ dislocations<br />

☐ both<br />

(b) The defect known as a “Frenkel pair” is shown in this<br />

sketch <strong>to</strong> have<br />

☐ body-centered symmetry<br />

☒ an extended strain field<br />

☐ both<br />

(c) Vacancies in solids<br />

☐ participate in diffusion<br />

☐ increase <strong>the</strong> entropy of a material<br />

☒ both<br />

(d) Dislocations in solids<br />

☒ participate in plastic deformation<br />

☐ decrease <strong>the</strong> entropy of a material<br />

☐ both<br />

(e) Fick’s First Law for diffusion flux<br />

Jx = −D ∂c<br />

∂x<br />

expresses <strong>the</strong> fact that<br />

☐ diffusion requires a negative diffusivity<br />

☒ mass flows down a concentration gradient<br />

☐ both<br />

page 2 of 6<br />

2. Defects in Solids (10 points)<br />

For this problem you must <strong>draw</strong> and label all requested<br />

features directly on <strong>the</strong> figures provided.<br />

(a) (2 points) Fill in <strong>the</strong> a<strong>to</strong>ms comprising <strong>the</strong> extra-half<br />

plane and label with <strong>the</strong> conventional symbol (⊥) <strong>the</strong> edge<br />

of <strong>the</strong> extra half-plane that establishes <strong>the</strong> line direction<br />

vec<strong>to</strong>r of <strong>the</strong> edge dislocation shown <strong>below</strong>.<br />

(b) (3 points) On <strong>the</strong> same figure <strong>below</strong>, trace and label a<br />

Burgers circuit in finish-start-right-hand (FSRH) convention,<br />

and identify <strong>the</strong> resulting Burgers vec<strong>to</strong>r (b).<br />

b 1<br />

F<br />

3<br />

S<br />

2<br />

1<br />

3<br />

(c) (2 points) Fill in <strong>the</strong> a<strong>to</strong>ms comprising <strong>the</strong> extra-half<br />

plane and label with <strong>the</strong> conventional symbol (⊥) <strong>the</strong> edge<br />

of <strong>the</strong> extra half-plane that establishes <strong>the</strong> line direction<br />

vec<strong>to</strong>r of <strong>the</strong> edge dislocation shown <strong>below</strong>.<br />

(d) (3 points) On <strong>the</strong> same figure, <strong>draw</strong> in and label <strong>the</strong><br />

location of <strong>the</strong> slip plane on which this edge dislocation<br />

glides.<br />

2<br />

2<br />

Slip<br />

Plane<br />

3<br />

1<br />

1<br />

3<br />

2


E 45 Midterm 02 SOLUTIONS:<br />

3. Phases and Phase Equilibria (10 points)<br />

Refer <strong>to</strong> <strong>the</strong> Cu-Zn binary <strong>phase</strong> <strong>diagram</strong> <strong>below</strong> (from ASM<br />

Metals Handbook, 8 th edition, Vol. 8, (1973), p. 301) <strong>to</strong><br />

answer <strong>the</strong> following questions. Recall that “brass” is <strong>the</strong><br />

common name applied <strong>to</strong> this alloy.<br />

T (°C)<br />

1100<br />

1000<br />

900<br />

800<br />

700<br />

600<br />

500<br />

400<br />

300<br />

200<br />

100<br />

0<br />

Cu<br />

at % Zn<br />

10 20 30 40 50 60 70 80 90<br />

"<br />

903°<br />

(a)<br />

456°<br />

(b)<br />

!<br />

!’<br />

(c)<br />

468°<br />

10 20 30 40 50 60 70 80 90<br />

wt % Zn<br />

#<br />

L<br />

835°<br />

(d)<br />

700°<br />

598°<br />

$<br />

558°<br />

424°<br />

% &<br />

(a) (2 points) What is <strong>the</strong> maximum concentration of Zn<br />

that can be dissolved in α brass?<br />

Ans: 39 wt. % Zn<br />

(b) (2 points) Apply <strong>the</strong> <strong>phase</strong> rule (F = C-P+1) <strong>to</strong> calculate<br />

<strong>the</strong> number of degrees of freedom available <strong>to</strong> a 40<br />

wt% Zn alloy at room temperature.<br />

Ans: F = 2 - 2 + 1 = 1<br />

(c) (2 points) What <strong>phase</strong>(s) is (are) in equilibrium when<br />

β brass (50:50 composition) is held at 500°C.<br />

Ans: β + γ<br />

(d) (2 points) Write <strong>the</strong> reaction that occurs on cooling<br />

through <strong>the</strong> 700°C peritectic iso<strong>the</strong>rm.<br />

Ans: γ + L ➔ δ<br />

(e) (2 points) Both <strong>the</strong> ε and η <strong>phase</strong>s of brass have hexagonal<br />

crystal structures. What composition would yield<br />

equal weight fractions of <strong>the</strong> <strong>the</strong>se two <strong>phase</strong>s in equilibrium<br />

at 100°C?<br />

Ans: 92.5 wt % Zn<br />

(e)<br />

Zn<br />

page 3 of 6<br />

4. Phases and Phase Equilibria (10 points)<br />

These questions refer <strong>to</strong> <strong>the</strong> same Cu-Zn binary <strong>phase</strong> <strong>diagram</strong><br />

from Problem 3.<br />

(a) (5 points) Sketch <strong>the</strong> microstructure resulting when a<br />

70 wt% Zn alloy with initially large γ grains at 550°C, as<br />

shown <strong>below</strong>, is cooled slowly <strong>to</strong> room temperature. Label<br />

all <strong>phase</strong>s.<br />

Slow cooling will result in grain<br />

boundary precipitation of <strong>the</strong> ε <strong>phase</strong><br />

(volume fraction ≈ 25%) within <strong>the</strong> γ<br />

grains (volume fraction ≈ 75%)..<br />

(b) (5 points) The eutec<strong>to</strong>id composition at 558°C is 74.1<br />

wt % Zn. Sketch <strong>the</strong> microstructure resulting when an alloy<br />

of this composition, showing a δ <strong>phase</strong> morphology at<br />

560°C as shown <strong>below</strong>, is cooled slowly <strong>to</strong> room temperature.<br />

Label all <strong>phase</strong>s.<br />

!<br />

"<br />

! "<br />

At <strong>the</strong> eutec<strong>to</strong>id iso<strong>the</strong>rm, all of <strong>the</strong> δ<br />

<strong>phase</strong> will decompose <strong>to</strong> <strong>the</strong> ε + γ in a<br />

lamellar constituent, in volume fractions<br />

of 40% ε and 60% γ.


E 45 Midterm 02 SOLUTIONS:<br />

7. Metallic <strong>Al</strong>loys (10 points)<br />

Temper Definition<br />

H1 Strain-hardened<br />

H2 Strain-hardened, partially annealed<br />

T3 Solution-treated, cold-worked, naturally<br />

aged<br />

T6 Solution-treated, artificially aged<br />

T9 Solution-treated, artificially-aged, cold<br />

worked<br />

The above table is a partial list of <strong>the</strong> “temper designations”<br />

for aluminum alloys specified by <strong>the</strong> <strong>Al</strong>uminum Association<br />

and published in <strong>the</strong> ASM Metals Handbook, 9 th<br />

edition, Volume 2 (1979). Recognizing that <strong>the</strong> specified<br />

treatments appearing in <strong>the</strong> “definition” column occur in<br />

sequence, and in <strong>the</strong> order given, rank <strong>the</strong> various temper<br />

treatments in order of highest strength <strong>to</strong> lowest strength.<br />

1. T9<br />

2. T3<br />

3. T6<br />

4. H1<br />

5. H2<br />

Reasoning: In general, <strong>the</strong> combination of work-hardening<br />

and precipitation hardening gives <strong>the</strong> highest overall<br />

strength. The T3 temper designation is <strong>the</strong> one given <strong>to</strong><br />

aircraft rivets, as described in lecture. Strain hardening<br />

alone can be considerable, but if an alloy was designed <strong>to</strong><br />

be precipitation-hardened (by choice of suitable alloying<br />

additions in appropriate amounts), it is expected that an<br />

aging treatment can also be designed <strong>to</strong> maximize strength<br />

without <strong>the</strong> damage of cold work. Those alloys for which<br />

<strong>the</strong> only available streng<strong>the</strong>ning option is strain hardening<br />

would be treated <strong>to</strong> earn an H designation, with a judicious<br />

amount of cold-work <strong>to</strong> avoid non-uniform stress distributions<br />

that might lead <strong>to</strong> cracking and/or brittle fracture.<br />

Annealing of course softens a material, putting it at <strong>the</strong><br />

bot<strong>to</strong>m of <strong>the</strong> list.<br />

page 5 of 6<br />

8. Metallic <strong>Al</strong>loys (10 points)<br />

Streng<strong>the</strong>ned by Weakened by<br />

Porosity (casting)<br />

Cold working Annealing<br />

<strong>Al</strong>loying Welding<br />

Phase Transformations Phase Transformations<br />

The above table lists some of <strong>the</strong> general effects of “processing”<br />

of metals and alloys on <strong>the</strong>ir mechanical strength.<br />

For example, an alloy used in <strong>the</strong> “as-cast” condition is<br />

generally weaker due <strong>to</strong> <strong>the</strong> porosity that occurs because of<br />

air entrapment during solidification from <strong>the</strong> liquid <strong>phase</strong>.<br />

Similarly, welding is listed as a cause of “weakening,” due<br />

<strong>to</strong> <strong>the</strong> fact that <strong>the</strong> local application of heat needed <strong>to</strong> weld<br />

alloys causes significant a<strong>to</strong>mic transport, including some<br />

in <strong>the</strong> liquid <strong>phase</strong>.<br />

Explain why “<strong>phase</strong> transformations” is listed in both columns.<br />

Answer: The <strong>phase</strong> transformations in <strong>the</strong> “streng<strong>the</strong>n”<br />

column are those that cause precipitation hardening. Such<br />

transformations result from carefully controlled <strong>the</strong>rmal<br />

treatments, beginning with homogenization in a single<br />

<strong>phase</strong> field, followed by rapid quenching <strong>to</strong> generate a supersaturated<br />

solid solution, finishing with an aging treatment<br />

<strong>to</strong> produce a fine dispersion of second <strong>phase</strong> particles<br />

that impede dislocation motion.<br />

The <strong>phase</strong> transformations in <strong>the</strong> “weaken” column<br />

are those that are not carefully controlled, such as<br />

slow cooling from <strong>the</strong> homogenization temperature, which<br />

usually results in a detrimental distribution of second <strong>phase</strong><br />

particles occurring exclusively at grain boundaries. The<br />

grain interiors are <strong>the</strong>refore made much less resistant <strong>to</strong><br />

dislocation motion because <strong>the</strong>y have no precipitate particles<br />

<strong>to</strong> serve as obstacles, and many fewer solute a<strong>to</strong>ms that<br />

also serve as impediments <strong>to</strong> dislocation motion (stronger<br />

metallic bonding). When such a material is deformed, dislocations<br />

move freely through <strong>the</strong> grains, sometimes with<br />

even lower strength than <strong>the</strong> solution solution would have<br />

shown.


E 45 Midterm 02 SOLUTIONS:<br />

9. Ceramics and Glasses (10 points)<br />

An important family of “magnetic” ceramics is <strong>based</strong> <strong>upon</strong><br />

<strong>the</strong> spinel (Mg<strong>Al</strong>2O4) structure. Spinel is formed from an<br />

fcc Bravais lattice and a basis of fourteen (14) ions per lattice<br />

point: 2 Mg 2+ , 4 <strong>Al</strong> 3+ and 8 O 2- . The magnesium ions<br />

are tetrahedrally coordinated by four oxygen ions, while<br />

<strong>the</strong> aluminum ions are octahedrally coordinated by six<br />

oxygen ions. Note that both <strong>the</strong> motif and <strong>the</strong> chemical<br />

formula preserve charge neutrality.<br />

However, <strong>the</strong> magnetic (known as “ferrimagnetic”) version<br />

of this structure is called an “inverse spinel,” in which <strong>the</strong><br />

octahedral sites are occupied by <strong>the</strong> divalent ions and onehalf<br />

of <strong>the</strong> trivalent ions, while <strong>the</strong> remaining trivalent ions<br />

are in <strong>the</strong> tetrahedral sites.<br />

One example of <strong>the</strong> ferrimagnetic ceramics is magnetite,<br />

<strong>the</strong> naturally occurring “lodes<strong>to</strong>ne” that was used <strong>to</strong> make<br />

<strong>the</strong> original compass. It is also found in meteorites. This<br />

could be <strong>the</strong> reason why, in Fox's hit series The X-Files,<br />

FBI investiga<strong>to</strong>rs observed that magnetite could disrupt<br />

alien life forms, often causing <strong>the</strong>ir death or destruction (?).<br />

Magnetite is an inverse spinel, yet its chemical formula is<br />

Fe3O4. Explain.<br />

Answer: The apparent anomaly here is charge balance. If<br />

you count up <strong>the</strong> number of negative charges on <strong>the</strong> eight<br />

(8) O 2- ions (= -16) and compare that number with <strong>the</strong><br />

number of positive charges on six (6) Fe 2+ ions (= +12),<br />

you arrive at a conundrum. However, taking a clue from<br />

<strong>the</strong> opening paragraph above, a spinel consists of both divalent<br />

and trivalent cations in <strong>the</strong> correct ratio (2 of <strong>the</strong><br />

divalent species and 4 of <strong>the</strong> trivalent species (= +16) <strong>to</strong><br />

achieve charge neutrality. So, if <strong>the</strong> chemical formula of<br />

magnetite is correct, its charge distribution must be reconciled.<br />

And <strong>the</strong> way <strong>to</strong> do that is <strong>to</strong> give Fe a multivalent<br />

character. Assume that it can be ei<strong>the</strong>r divalent or trivalent.<br />

The answer <strong>the</strong>n is that <strong>the</strong>re are must be two (2) Fe 2+ ions<br />

and four (4) Fe 3+ ions in this inverse spinel. You can think<br />

of <strong>the</strong> chemical formula in <strong>the</strong> same format as that for <strong>the</strong><br />

original spinel, Mg<strong>Al</strong>2O4, which would be expressed as<br />

FeFe2O4, but <strong>the</strong> more efficient form is Fe3O4.<br />

page 6 of 6<br />

10. Ceramics and Glasses (10 points)<br />

The following plot shows <strong>the</strong> <strong>the</strong>rmal expansion behavior<br />

typical of a glass. Note that strain is plotted on <strong>the</strong> vertical<br />

axis, with temperature increasing <strong>to</strong> <strong>the</strong> right on <strong>the</strong> horizontal<br />

axis. At <strong>the</strong> softening temperature (Ts), <strong>the</strong> glass is<br />

unable <strong>to</strong> support its own weight and flows freely, invalidating<br />

<strong>the</strong> <strong>the</strong>rmal expansion data.<br />

!L / L 0<br />

During <strong>the</strong> processing of safety glass for windows, a treatment<br />

is used <strong>to</strong> place <strong>the</strong> surface of <strong>the</strong> glass in residual<br />

compression, so that it will not be as susceptible <strong>to</strong> fine<br />

surface cracks. In one of <strong>the</strong>se treatments, <strong>the</strong> glass is first<br />

equilibrated above its glass transition temperature (Tg).<br />

Next it is subjected <strong>to</strong> cold air blast on both sides, a “surface<br />

quench,” <strong>to</strong> form a rigid but thin “skin” on both surfaces.<br />

The skin is cool enough <strong>to</strong> remain <strong>below</strong> <strong>the</strong> glass<br />

transition temperature while <strong>the</strong> interior of <strong>the</strong> glass is still<br />

above Tg. The glass is <strong>the</strong>n allowed <strong>to</strong> cool slowly and<br />

uniformly <strong>to</strong> room temperature.<br />

Explain how this treatment causes residual surface compression.<br />

Answer: The schematic at<br />

right shows how <strong>the</strong> stress<br />

distribution varies with each<br />

<strong>the</strong>rmal treatment. The residual<br />

surface compression<br />

comes during <strong>the</strong> final stages<br />

of cooling, when <strong>the</strong> larger<br />

interior mass of glass contracts,<br />

pulling <strong>the</strong> surface skin<br />

in<strong>to</strong> compression.<br />

T g<br />

T 0<br />

T g<br />

T 0<br />

T g<br />

T 0<br />

T g<br />

T f<br />

Temp<br />

T s<br />

T<br />

Compression<br />

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