HEAT TREATING CHARACTERISTICS
' OF FIVE BINARY ‘
BERY LLIU-M‘COPPER ALLOYS

Thesis for .the Degree of M. S.

MECHIGAN STATE COLLEGE

Vaughn Dale Hildebrandt
‘ ‘ 2945.

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acterietiee of Five

Heat Treating Char
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Binazy Beryllinnyc
presented by

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BEAT TREATIFG CHARACTERISTICS
CF FIVE IIHARY
BERYLLIUM—COIIER ALLOYS

by

VAUGHN DALE HILDEBHAEDT
m

A THESIS
Submitted to the School of Graduate Studies of Michigan
State College of Agriculture and Applied Science
in partial fulfillment of the requirements
for the degree of

EASTER OF SCIENCE

Department of Chemical and Metallurgical Engineering
1946

7/ZL/cu,

Title Page , . . . . . .
Table of Contents - - .
Acknowledgement . . . . .
Introduction . . . - . .
History . . . . . . . . .
Results . . . . . . . . .
Tabluated - - . . . .
Graphical . ¢ . . . .
Photomicrographs -
Discussion. . - . . . .
Conclusion. . . - . . . .
Appendix- . . . . . . . .

Bibliography

Selected-

Supplementary . . - .

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ACKNOWLEDGERENT
The author is deeply indebted to
Professor C. C. DeWitt and Mr. D. D. MoGrady
for their guidance, advice and assistance.
Appreciation is also expressed to the members
of the mechanical engineering staff for their

valuable advice.

INTRODUCTION

The problem of pr0perly heat treating beryllium-
QOpper alloys has been a nemesis to the engineer since the
early days of the war. The exceptional prOperties
developed by beryllium-copper alloys have been recognized
by many industries, but attainment of the desired physical
properties is not accomplished by haphazard, "hit or miss"
heat treating procedures.

The heat treatment of a particular alloy of COpper
and beryllium is dependent upon many factors. The most
important of these factors are: (l) the use to which the
material will be put, i.e., does it require maximum
hardness, maximum conductivity, maximum elongation or
minimum drift; (2) the metallurgical history of the alloy,
i.e., amount of "working” of cast alloy before and after
solution heat treatment; and, (3) the complete chemical
analysis of the alloy. At the present time, the
manufacturers of the alloys are supplying the heat
treating procedures with the alloy. However, it would
appear that these heat treating procedures have become
standardized and are unvariant.

In order that an intelligent analysis of the heat
treating processes be made, it was necessary to eliminate
as many of the variables as was possible. This

elimination procedure resulted in : (l) the selection of

five binary alloys of beryllium and COpper, (2) using
"unworked" cast test bars solution heat treated at
definite temperatures, and (3) aging to obtain maximum
hardness.

The data thus obtained enables one to draw many
general conclusions regarding the intricacies of proper

heat treatment.

hISTORY

The credit for the discovery of the remarkable
light metal, beryllium, must be given to the French
investigator Vauquelin.(22) In attempting to find
similarities between the precious stones, beryl and
emerald, Vauquelin found, in 1797, that an oxide of an
unknown constituent was common to both stones. The new
element was given the name glucinum because the salts
produced from the element were very sweet testing. The
name glucinum is still largely retained in French
scientific literature, but the element is more commonly
known as beryllium.

The problem of the isolation of elemental
beryllium was not solved until 1828,(5) when Wohler
succeeded in obtaining metallic beryllium from beryllium
chloride by heating it with flat, pressed balls of
calcium. From 182S until 1889 there was little research
devoted to beryllium and its compounds and alloys except
for minor discoveries of the unusual behavior of beryllium
salts. The first important advancement in the research
history of beryllium was the production of high purity
beryllium by electrolysis of the fused double flouride of
beryllium and sodium by LeBeau in 1889.(5) In addition to
the researches on the production of beryllium, LeBeau

studied several of the beryllium alloys. Among the alloys

flat
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studied was a series of beryllium-copper alloys ranging up
to 10% beryllium. The physical properties of the alloys
were recorded as regards color, malleability, tarnish
resistance, sonority and solubility in acids.(7) Research
develOpment again declined until about 1915. In 1916
Osterheld published his systematic investigation of the
beryllium-COpper alloys and their structures. The
equilibrium diagram proposed by Osterheld is shown in the
tOp figure of Figure I.(24)

In 1919 Stock and Goldschmidt began their
investigation of electrolytic production processes for
obtaining metallic beryllium. By 1921 Stock and
Goldschmidt had sucpeeded in producing molten beryllium
by electrolysis and the detailed description of their
laboratory eXperfments was published in 1925. Future work
was then undertaken by Siemens and Halske A.-G. The age-
hardening or precipitation hardening properties of
beryllium-copper alloys was discovered by Masing, about
1926, as a by-product of the study of the age-hardening
of aluminum-copper alloys. Easing then became interested
in redetermining the Osterheld equilibrium diagram
because the shape of the solid solubility lines did not
conform to the accepted diagram for age-hardenable alloys.
Masing confirmed his supposition about the inaccuracy of
the Osterheld diagram and the new equilibrium diagram
showed considerable alteration of the solid solubility

lines. Nasing's diagram is shown as the middle figure of

Figure I.

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Chronological de

I

velopment of the accepted

equilibrium diagram for beryllium-COpper alloys.

TOp diagram: PrOposed by Osterheld in 1916.

Center diagram:

Bottom diagram:

Proposed by Easing in 1929.

Accepted diagram. A combination
of the works of Easing (1929),
Borchers (1932), and Tanimura
and Wasserman (1935).

Figure I.
The.American counter-part of Siemens-Halske A.-G.
was the Beryllium Corporation of America which was

(2)

organized and began production in 1927. The early work
on beryllium was concerned primarily with the properties
of beryllium-COpper alloys as a possible substitute for
zinc and tin. The initial high cost of extracting pure
beryllium caused the investigations to be dropped.
However, the discovery of the exceptional spring
properties of beryllium-copper alloys caused a revival of
research interest. In 1932(15) J.K. Smith reported his
research results on a beryllium-copper alloy containing
2.5% beryllium. Smith's investigations established the
accepted mill procedure and confirmed the properties
obtainable upon age-hardening.

The accepted equilibrium diagram is a combination
of the works of Musing (published in 1932), Borchers
(published in 1952) and, Tanimura and Wasserman (published
in.l933). This diagram is shown as the bottom figure of

25)
Figure I.( A survey of more recent literature discloses
no marked changes in the accepted equilibrium diagram or

in the established procedures.

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TABULATED DATA

Table 1. Solution heat treating data for a cast 2.82% Be-
96.81% Cu alloy solution heat treated at lSlOOF.

Time at Temp. Hardness Readings (Rockwell "G”)
(Hours) Maximum Minimum Average
.25 51 47 50
.50 50 44 47
1.00 48 45 47
2.00 49 41 46
5.00 45 41 44
4.00 43 39 43
8.00 46 43 44
12.00 48 44 46
24.00 46 39 43
48.00 47 41 44

Table 2. Solution heat treating data for a cast 2.82% Re-
96.81% Cu alloy solution heat treated at 14700F.

Time at Temp. Hardness Readings (Rockwell "G")
(Hours) Maximum Minimum Average
.25 51 48 5O
.50 51 46 49
1.00 49 41 46
2.00 50 44 46
3.00 49 43 46
4.00 45 42 43
8.00 49 4O 44
12.00 44 41 43
24.00 47 40 43
48.00 43 36 40

Table 3. Solution heat treating data for a cast 2.82% Be-
96.81% Cu alloy solution heat treated at 14400F.

Time at Temp. Hardness Readings (Rockwell "G")
(Hours) Maximum Minimum Average
.25 51 48 p 50
.50 50 48 49
1.00 50 43 47
2.00 46 43 45
3.00 48 45 45
4.00 49 43 45
8.00 45 41 44
12.00 45 38 42
24.00 48 39 43

48.00 40 37 39

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Table 4. Solution heat treating data for a cast 2.61% Be-
97.16% Cu alloy solution heat treated at 15100F.

Time at Temp.
(Hours)

.25
.50
1.00
2.00
3.00
4.00
8.00
12.00
24.00
48.00

Hardness Reading (Rockwell "G")

maximum

57
54
54
53
52
53
51
52
52
52

Minimum
53
49
52
50
51
50
49
49
46
47

Average

55
52
53
52
52
51
50
5O
49
50

Table 5. Solution heat treating data for a cast 2.61% Be-

Time at Temp.
(Hours)

.25
.50
1.00
2.00
3.00
4.00
8.00
12.00
24.00
48.00

97.16% Cu alloy solution heat treated at 14700p.

Hardness Reading (Rockwell "G")

maximum
56
54
55
53

Minimum
49
52
50
49
48
49
48
49
47
42

Average

Table 6. Solution heat treating data for a cast 2.61% Be-

Time at Temp.
(Hours)

.25

.50

1.00

2.00

3.00

‘ 4.00
8.00
12.00
24.00
48.00

97.16% Cu alloy solution heat treated at 14400F.

Hardness Reading (Rockwell "G")

Maximum

57
54
53
54
53
53
53
52

50

Minimum

6 54
51
50
51
50
49
50
4e

44

Average
55
52
52
52

Table 7. Solution heat treating data for a cast 2.26% Re-

Time at Temp.
(Hours)

.25
.50
1.00
2.00
3.00
4.00
8.00
12.00
24.00

Maximum

50
4a
46
49
44
46
46
4a
43

41
46
43
43
4o
40
39
44
30

97.58% Cu alloy solution heat treated at 15100F.

Hardness Readings (Rockwell "8")
Minimum

Average
46
47
44
45
43
43
43
46
40

Table 8. Solution heat treating data for a cast 2.26% Be-

Time at Temp.
(Hours)

.25
.50
1.00
2.00
3.00
4.00
8.00
12.00
24.00
48.00

Maximum

52
4o
46
42
42
42
42
4o
41

41
38
40
33
37
38
23
38
36

97.58% Cu alloy solution heat treated at 14700F.

Hardness Readings (Rockwell "8")
Minimum

Average
46
46
4O
42
39
39
39
36
39
39

Table 9. Solution heat treating data for a cast 2.26% Be-

Time at Temp.
(Hours)

.25
.50
1.00
2.00
3.00
4.00
8.00
12.00
24.00
48.00

Maximum

47
44
46
42
43
41
4o
46
43
46

42
41
32
30
32
35
30
33
37
38

97.58% Cu alloy solution heat treated at 144OOF.

Hardness Readings (Rockwell "8")
Minimum

Average
44
42
39
39
39
38
36
4O
40
43

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Table 10. Solution heat treating do ta for a cast 2. 01% Be-
97. 79% Cu alloy solution heat treated at 15100F.

Time at Temp. Hardness Readings (Rockwell "8")
(Hours) Maximum Minimum Average
.25 36 29 331
.50 34 31 33
1.00 32 27 31
2.00 36 30 33
3.00 33 16 26
4.00 31 27 29
8.00 34 27 30
12.00 34 31 32
24.00 33 25 29
48.00 33

Table 11. Solution heat treating data for a cast 2.01% Be-
97.79% Cu alloy solution heat treated at 14700F.

Time at Temp. Hardness Readings (Rockwell "8")
(Hours) Maximum Minimum Average
.25 37 30 33
.50 35 28 31
1.00 32 29 31
2.00 32 28 31
3.00 32 26 30
4.00 32 21 28
8.00 33 25 30
12.00 36 30 32
24.00 33 23 28
48.00 36 27 32

Table 12. Solution heat treating data for a cast 2. 01% Be-
97. 79% Cu alloy solution heat treated at 14400F.

Time at Temp. Hardness Readings (Rockwell "B")
(Hours) Maximum Minimum Average
.25 39 34 37
.50 38 29 32
1.00 38 28 33
2.00 33 32 33
3.00 37 27 32
4.00 34 30 31
8.00 36 28 31
12.00 34 29 31
24.00 38 31 35

48.00 ' 37 29 33

14

Table 13. Solution heat treating data for a cast 1.78% De-
97.9a% Cu alloy solution heat treated at lSlOOF.

Time at Temp. Hardness Readings (Rockwell "8")
(Hours) Maximum Minimum Avercge
.25 27 16 21
.50 23 12 17
1.00 18 7 12
2.00 17 5 10
3.00 7 1 4
4.00 14 7 10
8.00 17 5 12
12.00 15 5 10
24.00 12 1 7
48.00 24 4 15

Table 14. Solution heat treating data for a cast 1.78% Re-
97.98% Cu alloy solution heat treated at 14700F.

Time at Temp. Hardness Readings (Rockwell "8")
(HOUIS) Maximum Minimum Average
.25 30 2O 26
.50 21 1 12
1.00 12 5 e
2.00 12 7 10
3.00 12 2 8
4.00 12 1 8
8.00 13 4 9
12.00 11 6 8
24.00 18 1 11
48.00 15 12 14

Table 15. Solution heat treating data for a cast 1.78% Re-
97.98% Cu alloy solution heat treated at 14400F.—

Time at Temp. Hardness Readings (Rockwell "3")
(Hours) Maximum Minimum Average
.25 31 25 27
.50 23 18 22
1.00 23 14 20
2.00 . 23 20 21
3.00 16 10 12
4.00 18 10 12
8.00 19 12 16
12.00 22 14 17
24.00 21 18 20

Table 16. Aging data for a cast 2.82% Le-96.8l% Cu alloy

Time at Temp.
(hours)

.00
.50
1.00
2.00
4.00
8.00
12.00
16.00
24.00

solution heat treated at 151001. for 15 minutes
and aged at 68OOF.

hardness headings (Rockwell "0")

l"n’xaximum

4o
44
4o
40
37
30
26
25

1Minimum

33
4O
36
3O
29
27
22
22

Average
-13
36
42
39
34
33
3O
24
24

Table 17. Aging data for a cast 2.82% Be-96.81% Cu alloy

Time at Temp.
(hours)

.00
.50
1.00
2.00
4.00
8.00
12.00
16.00
24.00

solution heat treated at lSlOOF. for 15 minutes
and aged at 63OOF.

Hardness Readings (Rockwell "G")

Timximum

12
38
42
46
25
27
29
28

minimum

9
36
39
4O
2O
23
22
18

Average
-13
11
37
41
43
24
24
26
22

Table 18. Aging data for a cast 2.82% be-96.817‘5 Uu alloy

Time at Temp.
(hours)

.00
.50
1.00
2.00
4.00
8.00
12.00
16.00
24000

solution heat treated at lBlOOF. for 15 minutes
and aged at ssoofl.

Hardness Readings (Rockwell "0")

Max imum

33
41
45
46
41
4O
39
36

minimum

32
36
42
43
35
37
35
30

Average
-13
33
39
43
45
39
38
37
33

Table 19. Aging data for a cast 2.82% Be- 96.81% Cu alloy

Time at Temp.
(Hours)

.00
.50
1.00
2.00
4.00
8.00
12.00
16.00
24.00

solution heat trerted at 14700F. for 15 minutes
and aged at 6eooF.

hardness Readings (Rockwell "G")

haximum

43
43
43
39
35
31
31
23

minimum

40
40
37
28
26
25
22
19

hverage
-10
42
42
40
34
32
28
25
21.

Table 20. hging data for a crst 2.82% Be- 96.81% Cu alloy

Time at_Temp.
(hours)

.00
.50
1.00
2.00
4.00
8.00
12.00
16000
24.00

Table 21.

Time at Temp.
(hours)

.00
.50
1.00
2.00
4.00
8.00
12.00
16.00
24.00

solution heat treated at 147003. for 15 minutes
and aged at 6300F.

Hardness Readings (Rockwell "0")

haximum

20
37
44
46
25
23
27
24

hinimum

16
34
41
29
20
21
21
18

hverege
-10
18
35
43
4O
22
22
24
21

Asing dcta for a cast 2.82% be: 96.81% Cu alloy
solution heat treated at 14700F. for 15 minutes
and aged at 5800?-

hardness headings (Rockwell "0")

IVlaximum

35
43
43
45
43
42
41
35

ininimum

3O
36
38
38
35
37
34
31

Average
-10
34
4O
41
43
38
39
37
33

17

Table 22. Aging data for a cast 2.82% Be- 96.81% Cu alloy
solution heat treated at 14400F. for 15 minutes
and aged at 6800F.

Time at Temp. Hardness Readings (Rockwell "G")
(Hours) Maximum Minimum Average
.00 - 8
.50 41 39 40
1.00 44 38 41
2.00 42 38 40
4.00 36 31 33
8.00 35 26 30
12.00 33 25 28
16.00 29 25 27
24.00 27 19 22

Table 23. Aging data for a cast 2.82% Be- 96.81% Cu alloy
solution heat treated at 14400F. for 15 minutes
and aged at 63OOF.

Time at Temp. Hardness Readings (Rockwell "0")
(Hours) Maximum Minimum Average
.00 - 8
.50 35 29 32
1.00 42 39 40
2.00 45 43 45
4.00 45 42 43
8.00 25 22 23
12.00 29 22 26
16.00 26 2O 23
24.00 26 24 23

Table 24. Aging data for a cast 2.82% Be- 96.81% Cu alloy
solution heat treated at 144OOF. for 15 minutes
and aged at 5800F.

Time at Temp. Hardness Readings (Rockwell "G")

(Hougg) Maximum Minimum Average

0 "' 8

.50 34 32 34

1.00 43 38 40

2.00 44 41 43

4.00 46 43 45

8.00 43 37 42

12.00 43 34 39

16.00 39 33 36

24.00 40 32 35

18

Table 25. Aging data for a cast 2.61% Ee- 97.16% Cu alloy
solution heat treated at lSlOOF. for 15 minutes
and aged at 6800F.

Time at Temp. Hardness Readings (Rockwell "0")
(Hours) maximum Minimum Average
.00 '33
.50 22 13 19
1.00 39 34 37
2.00 39 33 37
4.00 35 3O 32
8.00 36 31 33
12.00 31 22 27
16.00 28 23 26
24.00 27 21 24

Table 26. Aging data for a cast 2.61% Be- 97.16% Cu alloy
solution heat treated at 15100F. for 15 minutes
and aged at 63OOF.

Time at Temp. Hardness Readings (Rockwell "0")
(Hours) Maximum Minimum Average
.00 '53

050 - l - .5 - .5
1.00 35 33 34
2.00 43 3O 38
4.00 42 36 40
8.00 27 25 26

12.00 29 25 28
16.00 28 21 26
24.00 27 24 26

Table 27. Aging data for a cast 2.61% Be- 97.16% Cu alloy
solution heat treated at lSlOOF. for 15 minutes
and aged at 5809F.

Time at Temp. Hardness Readings (Rockwell "0")

(Hours) Maximum minimum Average

.00 '33

.5O 19 11 15

1.00 38 35 37

2.00 41 37 40

4.00 43 4O 41

8.00 41 34 38

12.00 37 31 35

16.00 36 26 32

24.00 33 3O 31

Table 28. Aging data for a cast 2.61% Be- 97.16% Cu alloy

Time at Temp.
(Hours)

.00
.50
1.00
2.00
4.00
8.00
12.00
16.00
24.00

solution heat treated at 14700F. for 15 minutes
and aged at 680°F.

Hardness Readings (Rockwell "0")

Maximum

38
43
4O
38
39
29
28
27

Ninimum

35
4O
34
31
29
26
25
22

Average
~13
37
41
39
35
35
27
27
25

Table 29. Aging data for a cast 2.61% Be- 97.16% Cu alloy

Time at Temp.
(Hours)

.00
.50
1.00
2.00
4.00
8.00
12.00
16.00
24.00

solution heat treated at 14700F. for 15 minutes
and aged at 63OOF.

Hardness Readings (Rockwell "G")

Maximum

29
37
44
46
26
27
25
24

Minimum

26
33
38
35
22
21

20
20

Average
-13
28
35
42
4O
24
23
21
22

Table 30. Aging data for a cast 2.61% Be- 97.16% Cu alloy

Time at Temp.
(Hours)

.00
.50
1.00
2.00
4.00
8.00
12.00
16.00
24.00

solution heat treated at 14700F. for 15 minutes
and aged at 580°F.

Hardness Readings (Rockwell "G")

maximum

30
39
42
44
42
41
39
38

Minimum

27
35
38
39
35
35
32
30

Average
-13
29
37
41
41
39
38
36
34

Table 31. Aging data for a cast 2.61% Be- 97.16% Cu alloy
solution heat treated at 14400F. for 15 minutes
and aged at 68OOF.

Time at Temp. Hardness Readings (Rockwell "0")
(Hours) Maximum Hinimum Average
.00 -16
.50 40 38 39
1.00 43 41 42
2.00 43 36 39
4.00 38 33 35
8.00 35 31 33
12.00 28 22 26
16.00 28 2O 24
24.00 24 20 22

Table 52. Aging data for a cast 2.61% Be- 97.16% Cu alloy
solution heat treated at 14400F. for 15 minutes
and aged at 63OOF.

Time at Temp. Hardness Readings (Rockwell "G")
(Hours) Maximum Minimum Average
.00 -16
.50 17 9 ' 13
1.00 39 36 38
2.00 43 42 43
4.00 44 39 42
8.00 26 23 25
12.00 27 21 24
16.00 28 2O 25
24.00 26 19 24

Table 33. Aging data for a cast 2.61% Be- 97.16% Cu alloy
' solution heat treated at 14400F. for 15 minutes
and aged at 5800F.

Time at Temp. Hardness Readings (Rockwell "0")

(Hours) Haximum Minimum ~ Average

.00 -16

.50 35 - 32 34

1.00 42 36 39

2.00 44 39 42

4.00 46 42 44

8.00 43 37 40

12.00 41 34 38

16.00 39 33 35

24.00 34 28 3O

Table 34. Aging data for a cast 2.26% Be- 97.58% Cu alloy
solution heat treated at 15100F. for 15 minutes
and aged at 68002.

Time at Temp. Hardness Readings (Rockwell "0")
(Hours) Maximum Minimum Average
.00 “38
050 14 - 2 7
1.00 45 40 42
2.00 38 32 36
4.00 36 26 32
8.00 29 21 26
12.00 51 24 27
16.00 27 20 26
24.00 23 19 21

Table 35. Aging data for a cast 2.26% Be- 97.58% Cu alloy
solution heat treated at 15100F. for 15 minutes
and aged at 630°F.

Time at Temp. Hardness Readings (Rockwell "0")
(Hours) Maximum Minimum Average
.00 '38
.50 15 8 11
1.00 37 29 33
2.00 40 37 39
4.00 43 36 39
8.00 26 20 24
12.00 30 21 25
16.00 29 20 26
24.00 28 24 26

Table 36. Aging data for a cast 2.26% Be- 97.58% Cu alloy
solution heat treated at lSlOOF. for 15 minutes
and aged at 5800F.

Time at Temp. Hardness Readings (Rockwell "0")

(Hours) Maximum Minimum Average

.00 . -38

050 " 6 3 l

1.00 33 3O 31

2.00 41 38 40

4.00 43 41 41

8.00 41 34 37

12.00 40 34 36

16.00 40 34 37

24.00 37 31 33

TD
(\3

Table 37. Aging data for a cast 2.26% Be- 97.58% Cu alloy
solution heat treated at 147OOF. for 15 minutes
and aged at 6800F.

Time at Temp. Hardness Readings (Rockwell "0")
(Hours) Maximum Minimum Average
.00 -22
.5O 41 36 39
1.00 44 4O 43
2.00 40 37 39
4.00 37 3O 34
8.00 36 31 34
12.00 30 24 28
16.00 31 23 27
24.00 26 16 22

Table 38. Aging data for a cast 2.26% Be- 97.58% Cu alloy
solution heat treated at 14700F. for 15 minutes
and aged at 6300F.

Time at Temp. Hardness Readings (Rockwell "G")
(Hours) Maximum Minimum Average
.00 ~22
.50 41 32 38
1.00 43 40 41
2.00 44 39 42
4.00 45 38 42
8.00 24 2O 22
12.00 27 20 22
16.00 24 21 23
24.00 23 2O 21

Table 39. Aging data for a cast 2.26% Be— 97.58% Cu alloy
solution heat treated at 1470 F. for 15 minutes
and aged at 5800F.

Time at Temp. Hardness Readings (Rockwell "0")

(Hours) Maximum Minimum Average

.00 “22

.50 32 29 32

1.00 39 35 37

2.00 44 37 41

4.00 47 41 44

8.00 40 36 38

12.00 37 34 36

16.00 39 31 34

24.00 39 27 30

23

Table 40. Aging data for a cast 2.26% Be- 97.58% Cu alloy
solution heat treated at 14400F. for 15 minutes
and aged at 6800F.

Time at Temp. Hardness Readings (Rockwell "G")
(Hours) Maximum Minimum Average
.00 ~19
.50 40 36 38
1.00 38 5o 35
2.00 42 38 39
4.00 36 31 33
8.00 36 24 32
12.00 31 23 27
16.00 28 25 25
24.00 23 16 20

Table 41. Aging data for a cast 2.26% Be- 97.58% Cu alloy
solution heat treated at 14400F. for 15 minutes
and aged at 63OOF.

Time at Temp. Hardness Readings (Rockwell "0")
(Hours) maximum Minimum Average
.00 “19
.50 21 13 18
1.00 37 32 34
2.00 43 37 40
4.00 45 37 41
8.00 25 2O 23
12.00 24 20 23
16.00 27 20 24
24.00 23 19 22

Table 42. Aging data for a cast 2.26% Be- 97.58% Cu alloy
solution heat treated at 14400F. for 15 minutes
and aged at 5800F.

Time at Temp. Hardness Readings (Rockwell "0")

(Hours) Maximum Minimum Average

.00 ~19

.50 32 27 30

1.00 39 35 37

2.00 42 37 41

4.00 43 41 42

8.00 39 36 38

12.00 36 28 34

16.00 33 30 32

24.00 32 28 30

Table 43. Aging data for a cast 2.01% Ee- 97.79% Cu alloy
solution heat treated at 15100F. for 15 minutes
and aged at 6800F.

Time at Temp. Hardness Readings (Rockwell "G")
(Hours) Maximum Hinimum Average
.00 '15
.50 2O 17 18
1.00 70 54 62
2.00 95 85 89
4.00 93 91 93
8.00 91 80 88
12.00 90 82 85
16.00 88 8O 84
24.00 85 79 83

Table 44. Aging data for a cast 2.01% Be- 97.79% Cu alloy
solution heat treated at 15100F. for 15 minutes
and aged at 63OOF.

Time at Temp. Hardness Readings (Rockwell "G")

(Hours) Maximum Minimum Average

.00 -15

050 8 " 2 2

1.00 58 46 51

2.00 88 75 80

8.00 91 82 88

12.00 90 83 87

16.00 91 83 87

24.00 90 85 88

Table 45. Aging data for a cast 2.01% Be- 97.79% Cu alloy
solution heat treated at 15100F. for 15 minutes
and aged at 580°F.

Time at Temp. Hardness Readings (Rockwell "G")

(Hours) Maximum Minimum Average

.00 -15

.50 25 11 19

1.00 70 62 65

2.00 90 72 83

4.00 98 92 96

8.00 98 93 96

12.00 99 94 96

16.00 99 93 96

24.00 ' 97 90 95

Table 46. Aging data for a cast 2.01% Be- 97.79% Cu alloy
solution heat treated at 14709F. for 15 minutes
and aged at 6800F.

Time at Temp. Hardness Readings (Rockwell "G")
(Hours) Maximum Minimum Average
.00 -16
.50 2O 13 17
1.00 88 6O 77
2.00 96 83 88
4.00 91 83 88
8.00 96 85 91
12.00 90 78 86
16.00 87 86 87
24.00 83 74 80

Table 47. Aging data for a cast 2.01% Be- 97.79% Cu alloy
solution heat treated at 14700F. for 15 minutes
and aged at 6500F.

Time at Temp. Hardness Readings (Rockwell "G")
(Hours) Maximum Minimum Average
.00 -16
.50 2O 7 12
1.00 54 46 51
2.00 95 9O 93
4.00 97 92 95
8.00 94 91 93
12.00 92 89 89
16.00 94 88 91
24.00 93 86 90

Table 48. Aging data for a cast 2.01% Be- 97.79% Cu alloy
solution heat treated at 147OOF. for 15 minutes
and aged at 5800F.

Time at Temp. Hardness Readings (Rockwell "G")

(Hours) Maximum Minimum Average

.00 '16

.50 2 ll 8

1.00 58 5O 55

2.00 85 55 68

4.00 97 88 92

8.00 98 88 94

12.00 98 91 95

16.00 98 '95 96

24.00 97 9O 94

Table 49. Aging data for a cast 2.01% Be- 97.79% Cu alloy
solution heat treated at 144OOF. for 15 minutes
and aged at 68OOF.

Time at Temp. Hardness Readings (Rockwell "G")
(Hours) maximum Minimum Average
.00 “'17
.50 23 12 18
1.00 78 62 58
2.00 93 76 84
4.00 95 85 92
8.00 96 91 94
12.00 91 89 90
16.00 89 84 87
24.00 88 83 86

Table 50. Aging data for a cast 2.01% Be- 97.79% Cu alloy
solution heat treated at 14400F. for 15 minutes
and aged at 63OOF.

Time at Temp. Hardness Readings (Rockwell "G")
(Hours) Maximum Minimum Average
.00 ’17
.50 15 1 7
1.00 82 66 74
2.00 95 92 94
4.00 98 97 98
8.00 92 87 89
12.00 90 85 88
16.00 92 86 89
24.00 89 80 85

Table 51. Aging data for a cast 2.01% Be- 97.79% Cu alloy
solution heat treated at 14400F. for 15 minutes
and aged at 580°F.

Time at Temp. Hardness Readings (Rockwell "G")

(Hours) Maximum Rinimum ‘amx'Average

.OO 1.- ~17

.5O 16 2 7

1.00 62 55 57

2.00 90 86 87

4.00 100 95 98

8.00 99 96 98

12.00 99 94 97

16.00 100 97 98

24.00 99 92 96

28

Table 55. Aging data for a cast 1.78% Be- 97.98% Cu alloy
solution heat treated at 147OOF. for 15 minutes
and aged at 6800F.

Time at Temp. Hardness Readings (Rockwell "B")

(Hours) Maximum Minimum iverage

.OO 23

.50 26 13 19

1.00 61 33 42

2.00 75 49 63

4.00 85 68 78

8.00 97 68 88

12.00 94 87 91

24.00 94 85 91

Table 56. Aging data for a cast 1.78% Be- 97.98% Cu alloy
solution heat treated at 14700F. for 15 minutes
and aged at 63OOF.

Time at Temp. Hardness Readings (Rockwell "B")
(Hours) Maximum Minimum Average
.00 23
.50 28 19 24
1.00 42 31 39
2.00 27 21 26
4.00 51 33 44
8.00 91 83 87
12.00 90 82 86
16.00 92 8O 87
24.00 92 83 88

Table 57. Aging data for a cast 1.78% Be- 97.98% Cu alloy
solution heat treated at 14700F. for 15 minutes
and aged at 5800F.

Time at Temp. Hardness Readings (Rockwell "8")

(Hours) Maximum Minimum ' Average

.00 23

.50 42 10 23

1.00 55 4O 45

2.00 73 46 60

4.00 59 47 55

8.00 90 73 85

12.00 90 79 87

16.00 93 84 88

24.00 96 92 94

flgble 58. Aging data for a cast 1.78% Be-797.98% Cu alloy
solution heat treated at 144OOF. for 15 minutes
and aged at 68OOF.

Time at Temp. Hardness Readings (Rockwell "R")
(Hours) Maximum Minimum Average
.00 24
.50 34 19 25
1.00 57 37 48
2.00 71 58 66
4.00 86 76 81
8.00 94 , 73 86
12.00 97 86 92
16.00 89 79 85
24.00 90 81 86

Table 59. Aging data for a cast 1. 78% Be- 97. 98% Cu alloy
solution heat treated at 144OOF. for 15 minutes
and aged at 6300 b.

Time at Temp. Hardness Readings (Rockwell "B”)
(Hours) Maximum Minimum Average
.00 24
.50 34 3O 33
1.00 47 50 37
2.00 60 39 49
4.00 74 61 68
8.00 98 91 95
12.00 98 93 95
16.00 98 92 94
24.00 95 86 91

Table 60. Aging data for a cast 1.78% Be- 97.9 8% Cu alloy
solution he8t tre8ted at 14400 F. for 15 minutes
and aged at 58OOF.

Time at Temp. Hardness Readings (Rockwell "8")

(Hours) Maximum Minimum Average

.00 24

.50 32 23 28

1.00 49 31 43

2.00 52 33 40

4.00 79 45 61

8.00 77 66 73

12.00 90 76 82

16.00 91 79 86

24.00 96 88 91

Table 61.

Rockwell

Rockwell

Table 62.

30

Hardness conversion data, Rockwell “L”- Rockwell
“(1:11

”B” 12 31 46 54 68 78 80

I!

G“ -35 -20 0 20 38 50 55

Hardness conversion data, Rockwell “G”- Rockwell

"Cu.
Rockwell "G" 69 80 96
Rockwell ”C" 1 14 33
Table 63. Physical pronerties of five binary beryllium-
COpper alloys in the "as cast" condition.
Heat Humber l 2 3 4 5
% Beryllium 2.82 2.61 2.26 2.01 1.78
Tensile Strength 80,000 78,200 55,400 39,750 30.150
(psi)
% Elongation in 24.55 21.5 15.4 17.5 6.8
2 Inches.
Rockwell Hardness
Maximum 50 G 44 G 71 B 61 B 46 B
Minimum 44 G 36 G 62 B 38 B 25 B
Average 47 G 40 G 68 B 54 B 34 B
Condition of Good Good Good Good Good

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(«Du Itenxooa) a'GUPJ‘H

I“: ’IV,

 

Figure 1. Microstructure of a 2.82% Be-96.82% Cu
alloy in the "as cast" condition.
Magnification: 100x . Etchant: Fe015

 

Figure 2. Microstructure of a 2.82% Be-96.82% Cu
alloy in the "as cast" condition.
Magnification: 500x Etchant: FeCl3

Figure 3.

figure 4.

 

 

 

 

 

 

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a u ; 5..);‘7 ...A‘r’, »‘ ’ .i.

Microstructure of a 2.61% Be-97.16% Cu~
alloy in the "as cast" condition.
magnification: lOOX Etchant: FeCl3

 

fiicrostructure of a 2.26% Be-97.58% Cu
alloy in the "as cast" condition. '

Magnification: 100K Etchant: FeCl3

97

 

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.Figure 5. Microstructure of a 2.01% Be-97.79% Cu,
alloy in the "as cast" condition.
Magnification: 100x Etchant: FeClB

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-

 

 

;Figure 6. ‘Microstructure of a 1.78% Be-97.98% Cu
alloy in the "as cast" condition.

magnification: lOOX Etchant: FeCl3

z. ._-'
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Figure 7. Microstructure of a cast 2.82% Be-96.82%
Cu 31108 after solution heat treatment
at 1470 F. for 15 minutes.
flagnification: lOOX Etchant: FeClB

 

.Figure 8. Microstructure of a cast 2.61% Be-97.82%
Cu allog after solution heat treatment
at 1470 F. for 15 minutes.
Magnification: lOOX Etchant: FeClS

99

 

Figure 9. Microstructure of a cast 2.26% Be-97.58%
Cu allog after solution heat treatment
at 1470 F. for 15 minutes.
Magnification: lOOX Etchant: FeCl3

 

 

,Figure 10. Microstructure of a cast 2.01% Be-97.7§%

Cu allo after solution heat treatment
at 1470 F. for 15 minutes.
Magnification: lOOX Etchant: Fe013

100

5:

 

Figure 11. Microstructure of a cast 1.78% Be-97.98%.
Cu allog after solution heat treatment
at 1470 F. for 15 minutes.
Magnification: lOOX Etchant: Fe013

     

p.515 " ’ -. ’

. . .. .' . a , --. . .' .1 ...) , ‘

.95 1e ~ 53
. ‘ u.» ' z \ ’2'.‘ ‘ u _

 

 

Figure 12. Microstructure of a cast 2.82% Be-96.82%
Cu allog after solution heat treatment
at 1510 F. for 15 minutes and aging at
680°F. for 1 hours.

Magnification: 100x Etchant: Fe013

lOl

 

~Figure 15. Nicrostructure of a cast 2.61% Be-97.16%
Cu allog after solution heat treatment
at 1510 F. for 15 minutes and aging at
680°F. for 1 hours.
Magnification: lCOX Etchant: FeCl3

 

 

 

.Figure 14. Nicrostructure of a cast 2.26% Be-97.58%
Cu allox after solution heat treatment
at 1510 F. for 15 minutes and aging at
6800F. for 1 hours.

Magnification: lOOX Etchant: FeCl3

Figure 15.

 

102

 

 

Microstructure of a cast 2.01% Be-97.79%
Cu alloy after solution heat treatment
at 15100F. for 15 minutes and aging at
6800F. for 4 hours.

Magnification: 100K Etchant: FeCl3

 

Microstructure of a cast 1.78% Be-97.98%
Cu allog after solution heat treatment
at 1510 F. for 15 minutes and aging at
680°F. for 16 hours.

Magnification: lOOX Etchant: Fe013

103

DISCUSSION

As indicated in the introduction to this
investigation, the remarkable physical prOperties of
beryllium-copper alloys are dependent upon the close
control of heat treating processes. The object of this
investigation is concerned with the correlation of
beryllium content, heat treating temperatures, time at
temperature and hardness; noting characteristic.
microstructures, tensile strength and elongation at
various stages of processing.

Since commercial heat treating processes seem to
have become standardized over a narrow temperature range,
it was deemed advisable to investigate the heat treating r
characteristics of five binary alloys of beryllium and
copper over the temperature range recommended in
commercial practice.

Inspection of the equilibrium diagram (Figure I.)
shows that the solution heat treating temperature, over
the range of 1.7% Be to 2.9% Be, ranges from 12000F. to
15450F. Commercial practices recommend that the solution
heat treating temperatures be in the range of 14000F.
(5’18’19) to 15000F.(3’6) However, the common commercial
beryllium-cepper alloys contain 2.0% Be to 2.5% Be. The
most probable explanation for the 50° difference in the

upper limit of the theoretical and recommended

104
:temperatures is fear of "burning out" the alloy. ”Burning‘
out” is defined as the segregation of the beta phase at the
grain boundries due to solution heat treating at too high a
temperature. The beta phase has a melting point of 1545OF.
and commercial processes do not have the close temperature
contrgl necessary to remain within the narrow temperature
range, 15200F. to 15450F. It is also logical to assume
that solution heat tr ating at the higher temperatures
would require less time at temperature than at a lower
temperature. At temperatures slightly above the minimum
solution temperature, there is considerably less driving
force than at a higher temperature and the atomic mobility
is very low. As the temperature increases, atomic
mobility increases and the rate of diffusion is high,
hence, the equilibrium condition is reached more rapidly.
There is still another factor to be considered and that is
the effect of cold and hot working. Both hot and cold
working of the alloys would tend to increase the rate of
diffusion because of the high stress condition existing in
the structure; possibly lowering the solution heat
treating an appreciable amount.

In view of the factors enumerated in the previous
discussion, the cast alloys were subjected to solution
heat treatment at temperatures of 14400F., 14700F. and
15100F. for periods up to 48 hours. In order that the
super-saturated condition be retained, a necessary

Condition for age hardening, the alloys were quenched in

105

cold water. Commercial processes nearly all call for a
water quench because the temperature gradients are much
higher than those obtained by Oil quenching.

After the problem of solution heat treating has
been solved, there remains the problem of aging the alloy.
Inspection of the equilibrium diagram discloses that the
possible hardening temperature range is from room-
temperature to lO65OF. Commercial hardening practices call
for hardening over a narrow temperature range from 525OF.
to 7OOOF.(5’5’6’7’ll:l5’17218219221) Ihis narrow
temperature range for hardening is characteristic of many
of the age hardenable alloys, e.g., magnesium-aluminum
alloys (Dowmetal) and aluminum-COpper alloys (Dural). In
accordance with the accepted theory of hardening, there
is an Optimum particle size which causes the maximum
amount of keying action on the potential slip planes with
a resulting maximum increase in hardness and tensile
strength. In order to secure the desired precipitation,
the temperature must be such that there is sufficient
atomic mobility to produce the Optimum particle size. As
the temperature increases, the atomic mobility increases
and the rate of diffusion is high, causing a coalescence
of precipitated particles to a size greater than the
Optimum. The desired physical properties decrease as the
particle size increases. The selection of the commercial
aging tempe aturea is not easily justified on the basis

of the previous discussion because it is believed that

106

time at temperature is as important as the temperature.
Commercial processes are generally constituted so that
time at temperatures are as short as possible without
sacrificing uniformity of product.

The problem confronting the commercial heat
treaters of beryllium—COpper alloys is one of selecting
a solution heat treatixg temperature and an aging
temperature that can be utilized on a production basis
and still maintain uniformity of products. This problem
resolves itself into two separate problems, (1.) accuracy
of temperature control, and (2.) accuracy in controlling
time at temperature.

The aging characteristics of the alloys used were
studied at temperatures of SBOOF., 6500F. and 6800F.
after solution heat treatment at 144OOF., 147OOF. and
lSlOoF.

The relationship of commercial and laboratory
practices has been discussed in sufficient detail to
warrant a discussion of laboratory results.

The selected alloys were cast without a great deal
of difficulty in accordance with the technique described
in Part 2 of the Appendix. The analysis of the first heat
did not conform to the calculated composition, however,
the master alloy was not analyzed until after the heats
were cast because of the analysis supplied with the alloy.
The beryllium content of the master alloy, as determined

in the laboratory, was .50 percent higher than indicated

107

by the data supplied with the alloy. Caculating the
heats showed that the analysis obtained (see analysis
data, Part 1, Appendix) were correct and the amount of
beryllium loss was negligible.

After completing the casting, the test bars were
cut from the pouring basin, properly labeled, machined to
size (see Figure 17a) and punch marked for elongation

measurements. One bar was selected from each heat for

YJZ’flJJay—é'fl .295 1.00-Mia.
f _ LI: 1 I

_e—cm' ~—-—aaFL—+ L¢—+-

55"

 

 

 

 

 

 

 

 

 

Figure 17a. Dimensions of Figure 17b. Sampling The Test
_. Test Bars. .i Bars.

determining the physical properties in the "as cast"
condition. The specimens were mounted in a Dillon Tensile
Tester in the manner shown in Figures 18a and 18b.
Tension was applied until the Specimen broke and the
breaking load, the elongation and the appearance of the
fracture were noted and recorded. The hardness of the
bottom end of the test bar was determined and the same
end cut into 5 equal portions as shown in Figure 17b. The

"as cast"

physical properties of the alloys in the
condition are shown in Table 63.
It is interesting to note that hardness, tensile

strength and elongation are proportional to the amount of

108

beryllium that is present in the alloy. The values
obtained are in accordance with those obtained by other
investigators, although the test specimen was not of
adequate size. It is recommended that future work be
carried on using test specimens not less than one inch in
diameter.

The microstruoture of each of the broken specimens
was examined after a macros00pic examination disclosed
the presence of a dendritic structure upon fracture.
Typical microstruotures are shown in Figures 1, 3, 4, 5
and 6, representing, reSpectively, each of the heats cast.
It should be noted that there is a definite dendritic I
pattern in evidence in the first four heats cast, while
the last heat cast exhibits a modified dendritic structure.
The equilibrium diagram shows that there should be two
phases, alpha and gamma solid solution, present in the
microstruoture if a condition of true equilibrium exists.
However, equilibrium does not exist because of the high
cooling rate obtained upon casting. Under the existing
condition of non-equilibrium, the microstruoture should
be constituted of alpha and beta solid solutions with
traces of gamma solid solution. All three of the
components, alpha, beta and gamma solid solutions, can be
recognized in the microstruotures of each of the heats
cast. The alpha solid solution is the light etching
constituent which constitutes the bulk of the structure.

The alpha solid solution is the first solid solution

109

formed and solidifies in a dendritic pattern. The beta
solid solution is the last of the melt to solidify and it
is found in the dendritic interstices and outlining the
grains of alpha solid solution. The beta solid solution
is the dark etching constituent in the microstruoture.
The gamma solid solution is a transformation product of
the beta solid solution. It is found in the middle of the
beta solid solution areas that have remained at
temperature long enough for some transformation to occur.
The gamma solid solution appears as light etching areas.

A representative sample (Section A., Figure 17b.)
was taken from each heat and solution heat treated at
lSlOOF. Hardness readings were taken after solution heat
treating for .25, .50, 1.0, 2.0, 3.0, 4.0, 8.0, 12.0,
24.0 and 48.0 hours.

The second portion of each broken test bar was
heat treated at 147OOF. according to the scheme described
above. The same procedure was repeated using the third
portion of the test bar at a temperature of 144OOF.

The cumulative data obtained is expressed in
tabular form, Tables 1 through 15, and in graphical form,
Graphs 1 through 15.

There are several characteristics of the graphical
data that merit considerable comment. It should be noted
that the six hardness readings were taken to determine
the average hardness. The maximum and minimum hardness

readings were recorded to show the degree of uniformity

110

or non-uniformity obtained by the heat treating processes.
Average values may be misleading unless there are
indications as to the amount of variation encountered.

A significant feature of the time hardness solution
heat treating curves is the slight increase in hardness
exhibited by the alloys of 2.82% Be- 96.81% Cu and 2.62%
Be- 97.16% Cu upon initial solution heat treatment. This is
in contrast to characteristics of the other three alloys
which exhibit a rapid drop in hardness in the early stages
of solution heat treatment. The most probable eXplanation
for the increase in hardness is that of accelerated age
hardening. The composition of the alloys is beyond the
alpha solid solubility limit and, There is an appreciable
quantity of the gamma phase to be found in the
microstruoture. Upon rapid cooling of the cast alloy, there
would be an appreciable degree of supersaturated solid
solution. 0n short time at high temperatures, the gamma
solid solution would precipitate causing a slight increase
in hardness and correSponding physical properties.

The heat treating characteristics, exemplified by
time-hardness relationships, may be best summarized by
examining a consolidation of the series of curves for the
various alloys at a Specific temperature. A generalized set
of curves is shown in Figure 19a. As the beryllium content
increases, the hardness of the solution heat treated alloy
increases. However, beyond a critical time limit there is

little change in the inherent hardness of each alloy.

111

‘.h.T. at 144OOF.

S.H.T. at 147OOE-
wf<ff__ S.H.T. at
151003.

\

' 0 ~ - 0 “ Cu
2.‘m re- 97.2% Cu
2

\\\‘-__ .3% Be- 97.6% Cu
t::::::2,0% Be- 97.8% Cu

1-8% Be- QBAOm Cu

 
      

 

 

 

 

Time ‘ ' Time
Figure 19a. Time-hardness Figure 19b. Time-hrrdness
curves for a series of curves for a cast 2.01%
cast Ee-Cu alloys Ee- 97.79% Cu alloy S.H.
S.h.T. at 15100r. T. at 14%OOF., 147OOF.
and 1510 F. ‘

The critical time limit will be a function of the solution
heat treating temperature as evidenced by an inspection of
a generalized, consolidated, time-hardness curve for a
particular alloy at various solution heat treating
temperatures. This curve is shown in Figure 19b. It should
be noted that the critical time limit increases as the
solution heat treating temperature decreases. Beyond the
critical time limit there is very little change in the
hardness value no matter what the solution heat treating
temperature may be. In other words, short time-high
temperature solution heat treatment may be duplicated by
prolonged solution heat treatment at lower temperatures.
Since the greatest changes seem to appear in all
the alloys after 15 minutes of solution heat treatment at
each of the selected temperatures, it was considered that a

15 minute solution heat treatment would add to the interest

 

 

 

 

 

 

Figure 18a. Dillon Tensile Figure 18b. Detailed view of the
Tester with Specimen mounted specimen.
mounted.

113

of the investigation. It is realized that Optimum aging
prOperties cannot be expected with insufficient heat
treatment.

Three test bars from each of the heats cast were
solution heat treated at 14400F., 14700F. and 15100F. for
a period of 15 minutes and quenched in cold water. One
bar from each heat solution heat treated at the
apprOpriate temperatures (15 bars in all) were selected
to determine the physical prOperties of the alloys at
this stage of processing. The Specimens were broken in
the Dillon Tensile Tester and the following facts noted
and recorded: breaking load, elongation and fracture
appearance. The hardness of the bottom end of the test
bar was determined and the same end cut into 5 equal
portions. The physical prOperties of the alloys in the
solution heat treated condition are summarized in Table
64.

The most striking feature of the alloys in the
solution heat treated state is the erratic character of
the physical properties. Although the everzge hardness
for each alloy solution host treated at the selected
temperatures is uniform, the variation in the hardness of
each specimen is considerable. This would Seem to

f‘l

indicate that the microstruoture or the alloys w uld show

Ii‘

soft and hard constituents. rensilc strength and
elongation are very erratic, which ma be due, in part,

to the size of the test Specimen. Light porsity in a

114

small diameter test bar will accentuate a decrease in
tensile strength because the effective area will be
greatly decreased. Khen bars of larger diameter are used,
the decrease in the effective area is not so great.
Elongation is also dependent upon the soundness of the
test bars.

ChQTacteristic microstruotures are exhibited in
Figures 7 through ll. Examination of the photomicrographs
shows that the microstruoture of each of the alloys is a
transformation product of the cast structures. The beta
phase has disappeared leaving the microstruoture c mposed
of two solid solutions. The darker etching constituent is
the supersaturated alpha solid solution, which is very
soft a1d ductile. The light etching constituent, standing
in relief, is the gamma solid solution. The gamma phase is
very hard and brittle. Decreasing beryllium content gives
a decreasing amount of gamma phase in the microstruoture.
This is justifiable on the basis of the following
eXplanation. When high beryllium alloys are cast, there w
will be considerable beta phase present in massive form.
As the beryllium content decreases the amount of the beta
phase will become smaller and smaller. In alloys of low
beryllium content, the beta phase would have disappeared
almost completely leaving only alpha solid solution.
Solution heat treating would decompose the beta phase
leaving the gamma phase in the form of massive particles.

64

Larger particles of gamma phase are more difficult to

115

dissolve because the alpha solid solution in the '
immediate vicinity of the gamma particles become
supersaturated very quickly and the rate of diffusion is
materially decreased.

One section from each test bar was taken, as
previously described, and aged at 58003. Hardness readings
were taken on each specimen after aging for periods of .50,
1.0, 2.0, 4.0, 8.0, 12.0 and 24.0 hours. The second
portion of each test bar was aged at 6300F. according to
the scheme described above. The same procedure was
repeated using the third portion of the test bar at a
temperature of 6800F.

The cumulative data is expressed in tabular form,
Tables 16 through 60, and in graphical form, Graphs l6
through-60.

The graphical data has several characteristics
that are worthy of considerable comment. It should be
noted that six hardness readings were taken to determine
the average hardness. Kaximum and minimum hardness
readings were recorded to show the degree of uniformity
obtained upon aging.

It was found that maximum hardness obtainable
upon age hardening is a function of the beryllium content,
up to a certain concentration, 2.26% Be. Alloys richer in
beryllium showed little or no increase in hardness. This
is explainable upon investigation of the equilibrium

diagrc . The solubility of beryllium in the alpha solid

ll6

solution increases to a maximum at 2.4% Be at
approximately lSBOOF. At the solution heat treating
temperature, the maximum amount of beryllium expected in
the alpha solid solution is approximately 2.3 percent.
This concentration of beryllium will produce the maximum
amount of precipitation of gamma solid solution along
the potential slip planes with maximum hardness
resulting. iowever, a large excess of the gamma phase
will cause a higher reading by virtue of the inherent
hardness of the gamma solid solution. This extremely
hard condition was observed in the master alloy
(containing 4.28% Be).

Solution heat treating at different temperatures
appears to have no noticable effect on the time-hardness
curve. However, the temperature at which aging proceeds
has a very pronounced effect on the shape of the time-
hardness curves. Examination of the shapes of the curves
discloses that the rate of aging increases with
increasing aging temperatures. After full hardening, the
rate of overaging also increases as the aging temperature
is increased. It should be noted that full hardening is
dependent upon time at temperature and not on aging
temperature. This is true of all the alloys studied.

There is still another characteristic of the
series of curves that is of prime importance and should
be commented upon. Although maximum hardness is not a

.37-,
strict function of beryllium content, rate of aging and

117

beryllium content are very closely related. Alloys of
beryllium, richer in beryllium than 2.4 percent, produce
a highly supersaturated solution upon proper solution
heat treatment. Upon aging, the gamma phase precipitates
very readily and optimum particle size is obtained very
quickly and, hence, produce full hardness over short time
intervals. Alloys containing less than 2.4 percent
beryllium are not highly supersaturated, even though
properly solution heat treated. Aging low beryllium (2.4%
Be or less) causes precipitation of the gamma phase once
again. However, since the solid solution is not highly
supersaturated, much diffusion may be necessary before
the particles may coalesce to the Optimum size. This

rate of diffusion is greater at higher temperatures
giving rise to the possibility of using considerably
higher temperatures when aging the low beryllium alloys.
As discussed above, maximum hardness is a function of
time at temperaturesand not temperature.

Lack of sufficient time forced the investigation
to a close and it was decided to determine the physical
properties of the aged alloys after aging as indicated
on the following page.

Each specimen was broken in an Olsen Tensile
Tester and the following facts noted and recorded:
breaking load, elongation and fracture appearance.
Hardness readings were taken on the bottom end of the

_ba . The physical properties of the alloys in the aged

118
hondition are summarized in Table 65.

Table 1. Aging procedure.

% Be S.L.T. Time at Aging Temp. Time at
Temp. Temp. Temp.

2.82 15100F. 15 min. 6800B. 1 hour

2.62 15100r. 15 min. 6800F. 1 howr

2.26 15100F. 15 min. 68003. 1 hour

2.01 1510??. 15 min. 6800F. 4 hours
1.78 151003. 15 min. 6800F. 16 hours
2.82 147OOF. 15 min. 6500F. 2 hours
2.62 14700F. 15 min. 6500B. 2 hours
2.26 14700F. 15 min. 6500B. 2 hours
2.01 14700F. 15 min. 6500B. 4 hours
1.78 14700F. 15 min. 6500F. 16 hours
2.82 14400F. 15 min. 5800B. 4 hours
2.62 14400F. 15 min. 5800F. 4 hours
2.26 14400F. 15 min. 5800?. 4 hours
2.01 14400F. 15 min. 5800B. - 8 hours
1.78 14400F. 15 min. 5800?. 24 hours.

The most significant feature of the physical
prOperties is, of course, the great increase in hardness.
It should be noted that the tensile strength and
elongation have behaved in the manner that wes expected,
i.e., tensile strength increased and elongation decreased
greatly. The prOperties of the aged alloys are in
accordance with results of other investigations.

The microstructure of a typical aged specimen
from each heat was investigated and photographed.
Photomicrographs of typical structures are shown in
Figures 12 through 16. The photomicrographs give
evidence that hardening has taken place because of the
dark-etching gamma phase precipitated at the grain
boundaries. The lighter etching constituent is that part
of the gamma phase remaining after solution heat
treatment. The matrix is the hardened alpha solid

solution phase.

119

COSCLUSION

It is realized that the results of this
investigation are not complete enough to warrant their
incorporation into commercial practices, however, several
general conclusions can be drawn as regards the effect of
heat treatment upon cast alloys.

The results indicate that the physical prOperties
of the cast alloys are preportional to the ammount of
beryllium in the alloy. hardness, tensile strength and
elongation increase as the beryllium content increases
from 1.78 percent to 2.82 percent. The physical
prOperties obtained are in good agreement with those
obtained by other investigators.

It was found that the solution heat treating
temperature does not materially affect the physical
properties of the alloys in the aged condition, if the

solution heat treatment has been proper, i.e., time at

"

f
I

temperature has been long enough to insure homogenity. As
the solution heat treating temperatures are increased,
shorter times at temperature may be employed with the

same resultant preperties. Preper solution heat treatment
results in a decrease in hardness and tensile strength and
an increase in elongation as compared to the corresponding
prOperties of the cast alloy. When high beryllium alloys

are used, accelerated aging may ‘ake place in the early

120

stages 0f solution_heat treatment._Because of insufficient
heat treatment, the physical properties obtained were

only in fair agreement with those obtained by other
investigators.

The greatest effect of heat treatment was obtained
upon aging. The shape of the aging curve is dependent
upon the beryllium content of the alloy and the
temperature. As the beryllium content increases, the
alloys harden more rapidly until the beryllium content
reaches 2.3 percent. Alloys richer than 2.5% Be all age
harden in approximately the same time interval.
Increasing the aging temperature decreases the aging time,
however, the maximum hardness is dependent on the
beryllium content. Above 2.5% Be, the hardness increases
by virtue of the inherent hardness of the gamma phase.
The tensile strength of aged alloys is increased greatly
as compared to the cast and solution heat treated alloys.
The elongation is extremely low as was expected. The
physical properties obtained are in fair agreement with
those obtained by other investigators.

Even though the investigation is incomplete, it is
believed that commercial practices could utilize higher
solution heat treating temperatures, lSlOOF. to lSBSOF.,
if accurate temperature control were maintained. It is
also believed that higher aging temperatures, 7OOOF. to
7500F., could be used with low beryllium alloys. For

.aincreasing beryllium content the aging temperature

121

should be lower prOportionately.

122

APPENDIX
Part 1. Analysis Procedure.(25)
Determination of Copper.

In a 400 ml. beaker, dissolve 5 g. of well mixed
turnings in 50 ml. of mixed acid solution. Dilute to 250
ml. and determine COpper by electrolytic method (Fischer
Electro-Analyzer) using platinum gauze cathodes. Pass .3
amperes through the solution for a period of 24 hours.
From the weight of COpper deposited, calculate the
percentage of copper
Determination of Silicon, Iron and Aluminum, and
Beryllium.

Evaporate solution from COpper determination to
100 ml. concentrated sulfuric acid and evaporate to
fumes of sulfur trioxide. Take up with 100 ml. of water
containing 10 ml. hydrochloric acid, bring to a boil and
filter through ashless paper. Wash thoroughly with hot
water and save filtrate for determination of iron,
aluminum and beryllium. Ignite residue in a weighed
platinum crucible and weigh, moisten the residue with a
few drops of sulfuric acid, add 10 ml. hydroflourio acid
and evaporate to dryness. Ignite at a dull red heat for
5 minutes, cool and weigh. The loss in weight is silicon
dioxide. If any residue remains it must be redissolved

in hydrochloric acid and added to the original filtrate.

123

Evaporate original filtrate plus "silica
washings" to 100 ml., add 3 drOps of methyl red indicator,
neutralize with ammonium hydroxide and, then, add
hydrochloric acid dropwise until the solution is acid and
clear. Heat to 6000. and add an excess of 8-hydroxy-
quinoline. Add 2.0-N. ammonium acetate solution until all
the aluminum and iron are precipitated, then add 25 ml.
excess. Filter and wash with cold water. Ignite precipitate
' in a weighed platinum crucible for 1 hour at 100000.
Difference in weight is the combined weight of A1205 and
Fe203 from which the combined percentage of iron and
aluminum may be calculated. The iron may be determined by
making a potassium bisulfate fusion, dissolving the fusion
in sulfuric acid, passing the solution through a Jones'
reductor and then titrating the iron with a standard
potassium permanganate solution. The iron is also
calculated in terms of Fe205 so that the A1203 and, hence,
the percentage of aluminum may be calculated.

Heat the filtrate from the iron-aluminum
determination plus the "cold water washings" to 6000. and
add ammonium hydroxide until alkaline to phenOpthalein.
Cool to room temperature and filter precipitate on
ashless paper. Wash precipitate with 1% ammonium

chloride solution. Evaporate filtrate and washings to

one-forth their original volume and precipitate any
remaining beryllium. Filter and add the second
precipitate to the first precipitate. Ignite in a
weighed platinum crucible at lOOOOC. after the paper
has been burned off. Cool, weigh rapidly and record
increase in weight as BeO. Calculate percentage
beryllium. Duplicate samples are run throughout the
entire analysis.

Preparation of Reagents
Mixed Acid Solution.

To 625 ml. of distilled water add 250 ml. of
concentrated sulfuric acid and 175 ml. of nitric acid.
8-Hydroxyquinoline Solution.

Triturate 2.5 g. of solid reagent with 5 ml. of
glacial acetic acid. When completely dissolved pour
into 100 ml. of distilled water and heat to 60°C.
Ammonium Chloride Washing Solution.

Dissolve 10 g. ammonium chloride in distilled
water, make just alkaline with ammonium hydroxide and
dilute to 100 ml.

Ammonium Acetate 2.0-N. Solution.
Dissolve 15.4 g. ammonium acetate in distilled

water and dilute to 100 ml.

125

Tabulated Analysis Data

Heat Number 1 2 3 4 5

% Beryllium 2.82 2.61 2.26 2.01 1.78
% Copper 96.81 97.16 97.58 97.79 97.98
% Silicon .104 .101 .105 .085 .063

% Iron and

Aluminum .150 .153 .135 .125 .168

 

Total 99.984 100.004 99.980 100.000 99.991

Part 2. Casting Procedure

Mold Preparation

All heats were cast in core-sand molds made up in
the following manner. To 100 parts of lake sand add 5
parts of cereal binder and mix well, add 5 parts of water
and mix well, and finally, add 2.5 parts of oil binder
and mix well. The resulting core~sand mixture is rammed
tightly in a mold—box (shown in Figure 21.) and the mold-
box removed. The green molds are then baked for 24 hours
at approximately 5000F. When cool, the cured molds are
given a light wash with mold-coating in order to secure a
cleaner casting. The coated molds are dried at SOOOF. for
16 hours.
Melting and Casting Technique‘a)

Calculate the correct proportions of master alloy
and electrolytic copper necessary to make up a heat of the
required size. Melt the copper in a crucible (shown in

Figure 23.) using a layer of coarse graphite as a

protective covering. When the molten c0pper reaches a
temperature of 2000°F., the pigs of master alloy are
dropped in, one by one. Raise the temperature of the‘
melt to 2lOOOF. and remove the crucible from the furnace.
Stir the melt with the thermocouple to insure homogenity
and remove the protective layer of graphite with a ”slag
skimmer". Allow the melt to cool to 2000-19500F. and
pour the melt into the molds with a minimum amount of
delay.
The loss of beryllium, by oxidation, in the Q

melting practice used, was negligible.

Calculation of Heats Melted

Heat Number 1 2 3 4 5
% Beryllium 2.50 2.25 2.00 1.75 1.50
(Calculated)

Weight of Master‘ 5966a. 5270g. 5250g. 4949g. 4148g.
Alloy Used

Master Alloy.

Estimated Losst 17g. 15g. 15g. l4g. 12g.
of Beryllium”

Weight of COpper 29243. 3530a. 49705. 5508g. 6052g.
Used

% Beryllium 2.82 2.61 2.26 2.01 1.78
(Actual)

* Calculated on the basis of 4% beryllium in the master
alloy.

# Calculated on the basis of a theoretical loss of 7%
of the contained beryllium.

 

127

 

 

 

 

Figure 21. Two views of the mold box.

28

 

Figure 22. View of coated and
uncoated molds.

 

 

 

. o h! ‘2‘. f1! 0 TI" "1’ .
A '1' I! 33*” . '

Figure 23. Materials and equipment.

129

SELECTED BIBLIOGRAPHY

ARTICLES
(1) Cone, E.F., "Beryllium Copper Alloys", Iron.Age,

(2)

(3)

(4)

(5)

(6)

(10)

(ll)

(12)

(l5)

(14)

132, 14, 18, (1955).

Sloman, K.A., "Beryllium And Its Alloys", Fetal

Industry (Bond), 44, 160, 183, 210, (I934).

_____ "Beryllium Copper", Fetal Industry (NY), 32,
48, (1954).

 

Corson, N.W. and Zeiser, J.D., "Beryllium And
Beryllium Alloys', Iron Age, 137, 28. (1936).

Delmonte, J., "Beryllium And Its Alloys", Petals and
AllO‘S, 7, 175, (1936).

 

Haydock, J., "Copper That Can Be Hardened", American
Machinist, 80, 841, (1956).

 

Silliman, H.F., "Beryllium Copper Alloys",
Industrial and Engineering Chemistry, 28,
I424, (1936)}

 

Honda, K., "Incubation 0f Alloys", Fetal Progress,

31, 536, (1937).

 

Sawyer, C.B. and Kjellgren, B.R., "Beryllium And
Beryllium Copper", Metal Industry (Lond),
52, 553, (1938).

 

Sawyer, C.B. and Kjellgren, B.R., "Newer Developments
In Beryllium", Industrial and Engineering

Chemistry, 30, SOI, (I938).

Halls, E.E., "Beryllium-Copper Alloys", Metals and
Alloys, 12, 337, (1940).

 

 

Spwyer’ C.B,, "Beryllium And Rational Defense",
Metals and alloys, 12, 426, (1940).

 

Jones, F.W. and Leach, P., "Precipitation In COpper
Beryllium Alloys", Engineering, 151, 398,
(1941).

 

‘F‘

Stott, L.L., "Physical Properties And Applications
Of Beryllium Alloys", Aero Digest, 39, 189,
(1941).

 

130

(15) Carson, R. I., "Iaking Beryllium Copper Behav
Iete 1s and Alloys, 18,1314, (1943).

 

(16) Foster, E. M., "Beryllium Copper" , The Electrician,
131,56, (1945).

 

(l7) Hunt, L. B., "Processing Beryllium-COpper" , Netals
and hlloys, 17, 594', (1943).

(18) Martin, I., "Quality Inspection 0f Beryllium
Copper" , IMet ls and Alloys, 17, 1203, (1943).

 

(19) Martin, I., "Heat Treating Beryllium-Copper" , Iron
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(20) Iilliams, H.G., "Available Beryllium In Copper",
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(21) Yarham, E. B., "Beryllium Copper", Iron Age, 155,
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BOOKS

(22) Iellor, J. I., A Comprehensive Treatise 0n Inorganic
And Theoretical CI; emistry, Iew York,
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204-48.
(23) ----- Fetals Handbook, Cleveland, Ohio, American
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1411-2

(24) Rimbach, R, and Iichel, A. J., Beryllium, Its
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(25) Scott, I .I., Standard Iethods 0f Chemical Ana.1ysis,
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.,.—s-

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o
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155

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l'
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a. r.

----- "Brush Announce Cheaper Beryllium For Beryllium-
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O

 

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156

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O

 

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----- "Light Metals", Business Week, 55, August 28, (1945).
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