U.S. patent application number 09/987173 was filed with the patent office on 2002-06-13 for lead-free free-cutting copper alloys.
This patent application is currently assigned to Sambo Copper Alloy Co., Ltd.. Invention is credited to Oishi, Keiichiro.
Application Number | 20020069942 09/987173 |
Document ID | / |
Family ID | 26557241 |
Filed Date | 2002-06-13 |
United States Patent
Application |
20020069942 |
Kind Code |
A1 |
Oishi, Keiichiro |
June 13, 2002 |
LEAD-FREE FREE-CUTTING COPPER ALLOYS
Abstract
A lead-free free-cutting copper alloy having 69 to 79 percent,
by weight, of copper; greater than 3 percent, by weight, of
silicon; and a remaining percent, by weight, of zinc. The alloy
preferable has greater than 3.0 percent and less than or equal to
4.0 percent, by weight, of silicon; and at least one element
selected from among 0.02 to 0.4 percent, by weight, of bismuth,
0.02 to 0.4 percent, by weight, of tellurium, and 0.02 to 0.4
percent, by weight, of selenium. The alloy also preferable has at
least one element selected from among 0.3 to 3.5 percent, by
weight, of tin, 1.0 to 3.5 percent, by weight, of aluminum, and
0.02 to 0.25 percent, by weight, of phosphorus. In further
embodiments, the alloy has at least one element selected from among
0.02 to 0.15 percent, by weight, of antimony, and 0.02 to 0.15
percent, by weight, of arsenic.
Inventors: |
Oishi, Keiichiro;
(Sakai-shi, JP) |
Correspondence
Address: |
GRIFFIN & SZIPL, PC
SUITE PH-1
2300 NINTH STREET, SOUTH
ARLINGTON
VA
22204
US
|
Assignee: |
Sambo Copper Alloy Co.,
Ltd.
8-374, Sambo-cho
Sakai-shi
JP
590-0906
|
Family ID: |
26557241 |
Appl. No.: |
09/987173 |
Filed: |
November 13, 2001 |
Related U.S. Patent Documents
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Application
Number |
Filing Date |
Patent Number |
|
|
09987173 |
Nov 13, 2001 |
|
|
|
09555881 |
Jun 8, 2000 |
|
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Current U.S.
Class: |
148/432 ;
420/490 |
Current CPC
Class: |
C22F 1/08 20130101; C22C
9/04 20130101 |
Class at
Publication: |
148/432 ;
420/490 |
International
Class: |
C22C 009/04; C22C
009/00; C22C 009/10 |
Foreign Application Data
Date |
Code |
Application Number |
Oct 12, 1998 |
JP |
10-288590 |
Nov 16, 1998 |
JP |
PCT/JP98/05157 |
Claims
What is claimed is:
1. A lead-free free-cutting copper alloy, consisting essentially of
69 to 79 percent, by weight, of copper; from 3.0 up to and
including 4.0 percent, by weight, of silicon; and the remaining
percent, by weight, of zinc, wherein the percent by weight of
copper and silicon in the copper alloy satisfy the relationship
55.ltoreq.X-3Y.ltoreq.70, wherein X is the percent, by weight, of
copper, and Y is the percent, by weight, of silicon; and the copper
alloy has a metal construction comprising multiple phases
integrated to form a composite phase, wherein the composite phase
is an a phase matrix having a total phase area comprising not more
than 5% of a .beta. phase, and 5-70% of the total phase area is
provided by at least one phase selected from the group consisting
of a .gamma. phase, a .kappa. phase, and a .mu. phase.
2. A lead-free free-cutting copper alloy, consisting essentially of
69 to 79 percent, by weight, of copper; from 3.0 up to and
including 4.0 percent, by weight, of silicon; at least one element
selected from among 0.02 to 0.4 percent, by weight, of bismuth,
0.02 to 0.4 percent, by weight, of tellurium, and 0.02 to 0.4
percent, by weight, of selenium; and the remaining percent, by
weight, of zinc, wherein the percent by weight of copper and
silicon in the copper alloy satisfy the relationship
55.ltoreq.X-3Y.ltoreq.70, wherein X is the percent, by weight, of
copper, and Y is the percent, by weight, of silicon; and the copper
alloy has a metal construction comprising multiple phases
integrated to form a composite phase, wherein the composite phase
is an .alpha. phase matrix having a total phase area comprising not
more than 5% of a .beta. phase, and 5-70% of the total phase area
is provided by at least one phase selected from the group
consisting of a .gamma. phase, a .kappa. phase, and a .mu.
phase.
3. A lead-free free-cutting copper alloy, consisting essentially of
70 to 80 percent, by weight, of copper; 1.8 to 3.5 percent, by
weight, of silicon; at least one element selected from among 0.3 to
3.5 percent, by weight, of tin, and 0.02 to 0.25 percent, by
weight, of phosphorus; and the remaining percent, by weight, of
zinc, wherein the percent by weight of copper, silicon, tin and
phosphorus in the copper alloy satisfy the relationship
55.ltoreq.X-3Y+aZ+bW.ltoreq.70, wherein X is the percent, by
weight, of copper, Y is the percent, by weight, of silicon, Z is
the percent, by weight, of tin, W is the percent, by weight, of
phosphorus, a is -0.5, and b is -3; and the copper alloy has a
metal construction comprising multiple phases integrated to form a
composite phase, wherein the composite phase is an .alpha. phase
matrix having a total phase area comprising not more than 5% of a
.beta. phase, and 5-70% of the total phase area is provided by at
least one phase selected from the group consisting of a .gamma.
phase, a .kappa. phase, and a .mu. phase.
4. A lead-free free-cutting copper alloy, consisting essentially of
70 to 80 percent, by weight, of copper; 1.8 to 3.5 percent, by
weight, of silicon; at least one element selected from among 0.3 to
3.5 percent, by weight, of tin, and 0.02 to 0.25 percent, by
weight, of phosphorus; at least one element selected from among
0.02 to 0.4 percent, by weight, of bismuth, 0.02 to 0.4 percent, by
weight, of tellurium, and 0.02 to 0.4 percent, by weight, of
selenium; and the remaining percent, by weight, of zinc, wherein
the percent by weight of copper, silicon, tin and phosphorus in the
copper alloy satisfy the relationship
55.ltoreq.X-3Y+aZ+bW.ltoreq.70, wherein X is the percent, by
weight, of copper, Y is the percent, by weight, of silicon, Z is
the percent, by weight, of tin, W is the percent, by weight, of
phosphorus, a is -0.5, and b is -3; and the copper alloy has a
metal construction comprising multiple phases integrated to form a
composite phase, wherein the composite phase is an .alpha. phase
matrix having a total phase area comprising not more than 5% of a
.beta. phase, and 5-70% of the total phase area is provided by at
least one phase selected from the group consisting of a .gamma.
phase, a .kappa. phase, and a .mu. phase.
5. A lead-free free-cutting copper alloy, consisting essentially of
69 to 79 percent, by weight, of copper; 2.0 to 4.0 percent, by
weight, of silicon; at least one element selected from the group
consisting of 0.3 to 3.5 percent, by weight, of tin, and 0.02 to
0.25 percent, by weight, of phosphorus; at least one element
selected from the group consisting of 0.02 to 0.15 percent, by
weight, of antimony, and 0.02 to 0.15 percent, by weight, of
arsenic; and the remaining percent, by weight, of zinc, wherein the
percent by weight of copper, silicon, tin and phosphorus in the
copper alloy satisfy the relationship
55.ltoreq.X-3Y+aZ+bW.ltoreq.70, wherein X is the percent, by
weight, of copper, Y is the percent, by weight, of silicon, Z is
the percent, by weight, of tin, W is the percent, by weight, of
phosphorus, a is -0.5, and b is -3; and the copper alloy has a
metal construction comprising multiple phases integrated to form a
composite phase, wherein the composite phase is an .alpha. phase
matrix having a total phase area comprising not more than 5% of a
.beta. phase, and 5-70% of the total phase area is provided by at
least one phase selected from the group consisting of a .gamma.
phase, a .kappa. phase, and a .mu. phase.
6. A lead-free free-cutting copper alloy, consisting essentially of
69 to 79 percent, by weight, of copper; 2.0 to 4.0 percent, by
weight, of silicon; at least one element selected from the group
consisting of 0.3 to 3.5 percent, by weight, of tin, and 0.02 to
0.25 percent, by weight, of phosphorus; at least one element
selected from the group consisting of 0.02 to 0.15 percent, by
weight, of antimony, and 0.02 to 0.15 percent, by weight, of
arsenic; at least one element selected from among 0.02 to 0.4
percent, by weight, of bismuth, 0.02 to 0.4 percent, by weight, of
tellurium, and 0.02 to 0.4 percent, by weight, of selenium; and the
remaining percent, by weight, of zinc, wherein the percent by
weight of copper, silicon, tin and phosphorus in the copper alloy
satisfy the relationship 55.ltoreq.X-3Y+aZ+bW .ltoreq.70, wherein X
is the percent, by weight, of copper, Y is the percent, by weight,
of silicon, Z is the percent, by weight, of tin, W is the percent,
by weight, of phosphorus, a is -0.5, and b is -3; and the copper
alloy has a metal construction comprising multiple phases
integrated to form a composite phase, wherein the composite phase
is an .alpha. phase matrix having a total phase area comprising not
more than 5% of a .beta. phase, and 5-70% of the total phase area
is provided by at least one phase selected from the group
consisting of a .gamma. phase, a .kappa. phase, and a .mu.
phase.
7. A lead-free free-cutting copper alloy, consisting essentially of
62 to 78 percent, by weight, of copper; 2.5 to 4.5 percent, by
weight, of silicon; at least one element selected from among 0.3 to
3.0 percent, by weight, of tin, and 0.02 to 0.25 percent, by
weight, of phosphorus; and at least one element selected from among
0.7 to 3.5 percent, by weight, of manganese and 0.7 to 3.5 percent,
by weight, of nickel; and the remaining percent, by weight, of
zinc, wherein the percent by weight of copper, silicon, tin,
phosphorus, manganese and nickel in the copper alloy satisfy the
relationship 55.ltoreq.X-3Y+aZ+bW+cV+dU.ltoreq.70, wherein X is the
percent, by weight, of copper, Y is the percent, by weight, of
silicon, Z is the percent, by weight, of tin, W is the percent, by
weight, of phosphorus, V is the percent, by weight, of manganese, U
is the percent, by weight, of nickel, a is -0.5, b is -3, c is 2.5,
c is 2.5, d is 2.5, and the percent by weith of silicon, manganese
and nickel satisfy the relationship 0.7.ltoreq.Y/(V+U).ltoreq.6- ;
and the copper alloy has a metal construction comprising multiple
phases integrated to form a composite phase, wherein the composite
phase is an .alpha. phase matrix having a total phase area
comprising not more than 5% of a .beta. phase, and 5-70% of the
total phase area is provided by at least one phase selected from
the group consisting of a .gamma. phase, a .kappa. phase, and a
.mu. phase.
8. A lead-free free-cutting copper alloy, consisting essentially of
62 to 78 percent, by weight, of copper; 2.5 to 4.5 percent, by
weight, of silicon; at least one element selected from among 0.3 to
3.0 percent, by weight, of tin, and 0.02 to 0.25 percent, by
weight, of phosphorus; and at least one element selected from among
0.7 to 3.5 percent, by weight, of manganese and 0.7 to 3.5 percent,
by weight, of nickel; at least one element selected from among 0.02
to 0.4 percent, by weight, of bismuth, 0.02 to 0.4 percent, by
weight, of tellurium, and 0.02 to 0.4 percent, by weight, of
selenium; and the remaining percent, by weight, of zinc, wherein
the percent by weight of copper, silicon, tin, phosphorus,
manganese and nickel in the copper alloy satisfy the relationship
55.ltoreq.X-3Y+aZ+bW+cV+dU.ltoreq.70, wherein X is the percent, by
weight, of copper, Y is the percent, by weight, of silicon, Z is
the percent, by weight, of tin, W is the percent, by weight, of
phosphorus, a is -0.5, b is -3; and the copper alloy has a metal
construction comprising multiple phases integrated to form a
composite phase, wherein the composite phase is an .alpha. phase
matrix having a total phase area comprising not more than 5% of a
.beta. phase, and 5-70% of the total phase area is provided by at
least one phase selected from the group consisting of a .gamma.
phase, a .kappa. phase, and a .mu. phase. c is 2.5, d is 2.5, and
the percent by weith of silicon, manganese and nickel satisfy the
relationship 0.7.ltoreq.Y/(V+U).ltoreq.6; and the copper alloy has
a metal construction comprising multiple phases integrated to form
a composite phase, wherein the composite phase is an .alpha.phase
matrix having a total phase area comprising not more than 5% of a
.beta. phase, and 5-70% of the total phase area is provided by at
least one phase selected from the group consisting of a .gamma.
phase, a .kappa. phase, and a .mu. phase.
9. A lead-free free-cutting copper alloy, consisting essentially of
69 to 79 percent, by weight, of copper; 2.0 to 4.0 percent, by
weight, of silicon; 0.1 to 1.5 percent, by weight, of aluminum; and
0.02 to 0.25 percent, by weight, of phosphorus; and the remaining
percent, by weight, of zinc, wherein the percent by weight of
copper, silicon, aluminum and phosphorus in the copper alloy
satisfy the relationship 55.ltoreq.X-3Y+aZ+bW.ltoreq.70, wherein X
is the percent, by weight, of copper, Y is the percent, by weight,
of silicon, Z is the percent, by weight, of aluminum, W is the
percent, by weight, of phosphorus, a is -2, and b is -3; and the
copper alloy has a metal construction comprising multiple phases
integrated to form a composite phase, wherein the composite phase
is an .alpha. phase matrix having a total phase area comprising not
more than 5% of a .beta. phase, and 5-70% of the total phase area
is provided by at least one phase selected from the group
consisting of a .gamma. phase, a .kappa. phase, and a .mu.
phase.
10. A lead-free free-cutting copper alloy, consisting essentially
of 69 to 79 percent, by weight, of copper; 2.0 to 4.0 percent, by
weight, of silicon; 0.1 to 1.5 percent, by weight, of aluminum;
0.02 to 0.25 percent, by weight, of phosphorus; at least one
element selected from among 0.02 to 0.4 percent, by weight, of
chromium and 0.02 to 0.4 percent, by weight, of titanium; and the
remaining percent, by weight, of zinc, wherein the percent by
weight of copper, silicon, aluminum, phosphorus and chromium in the
copper alloy satisfy the relationship
55.ltoreq.X-3Y+aZ+bW+cV.ltoreq.70, wherein X is the percent, by
weight, of copper, Y is the percent, by weight, of silicon, Z is
the percent, by weight, of aluminum, W is the percent, by weight,
of phosphorus, V is the percent, by weight, of chromium, a is -2, b
is -3, c is 2; and the copper alloy has a metal construction
comprising multiple phases integrated to form a composite phase,
wherein the composite phase is an .alpha. phase matrix having a
total phase area comprising not more than 5% of a .beta. phase, and
5-70% of the total phase area is provided by at least one phase
selected from the group consisting of a .gamma. phase, a .kappa.
phase, and a .mu. phase.
11. A lead-free free-cutting copper alloy, consisting essentially
of 69 to 79 percent, by weight, of copper; 2.0 to 4.0 percent, by
weight, of silicon; 0.1 to 1.5 percent, by weight, of aluminum;
0.02 to 0.25 percent, by weight, of phosphorus; at least one
element selected from among 0.02 to 0.4 percent, by weight, of
bismuth, 0.02 to 0.4 percent, by weight, of tellurium and 0.02 to
0.4 percent, by weight, of selenium; and the remaining percent, by
weight, of zinc, wherein the percent by weight of copper, silicon,
tin and phosphorus in the copper alloy satisfy the relationship
55.ltoreq.X-3Y+aZ+bW.ltoreq.70, wherein X is the percent, by
weight, of copper, Y is the percent, by weight, of silicon, Z is
the percent, by weight, of aluminum, W is the percent, by weight,
of phosphorus, a is -2, and b is -3; and the copper alloy has a
metal construction comprising multiple phases integrated to form a
composite phase, wherein the composite phase is an .alpha. phase
matrix having a total phase area comprising not more than 5% of a
.beta. phase, and 5-70% of the total phase area is provided by at
least one phase selected from the group consisting of a .gamma.
phase, a .kappa. phase, and a .mu. phase.
12. A lead-free free-cutting copper alloy, consisting essentially
of 69 to 79 percent, by weight, of copper; 2.0 to 4.0 percent, by
weight, of silicon; 0.1 to 1.5 percent, by weight, of aluminum;
0.02 to 0.25 percent, by weight, of phosphorus; at least one
element selected from among 0.02 to 0.4 percent, by weight, of
chromium, and 0.02 to 0.4 percent by weight of titanium; at least
one element selected from among 0.02 to 0.4 percent, by weight, of
bismuth, 0.02 to 0.4 percent, by weight, of tellurium and 0.02 to
0.4 percent, by weight, of selenium; and the remaining percent, by
weight, of zinc, wherein the percent by weight of copper, silicon,
aluminum, phosphorus and chromium in the copper alloy satisfy the
relationship 55.ltoreq.X-3Y+aZ+bW+cV.ltoreq.70, wherein X is the
percent, by weight, of copper, Y is the percent, by weight, of
silicon, Z is the percent, by weight, of aluminum, W is the
percent, by weight, of phosphorus, V is the percent, by weight, of
chromium, a is -2, b is -3, c is 2; and the copper alloy has a
metal construction comprising multiple phases integrated to form a
composite phase, wherein the composite phase is an .alpha. phase
matrix having a total phase area comprising not more than 5% of a
.beta. phase, and 5-70% of the total phase area is provided by at
least one phase selected from the group consisting of a .gamma.
phase, a .kappa. phase, and a .mu.phase.
Description
[0001] This application is a continuation-in-part of U.S. patent
application Ser. No. 09/555,881, filed Jun. 8, 2000, the entire
disclosure of which is incorporated herein by reference, which
application claims priority from Japanese Application No.
10-288590, filed Oct. 12, 1998, the entire disclosure of which is
incorporated herein by reference.
BACKGROUND OF THE INVENTION
[0002] 1. Field of The Invention
[0003] The present invention relates to lead-free free-cutting
copper alloys.
[0004] 2. Prior Art
[0005] Among the copper alloys with a good machinability are bronze
alloys such as that having the JIS designation H5111 BC6 and brass
alloys such as those having the JIS designations H3250-C3604 and
C3771. These alloys are enhanced in machinability by the addition
of 1.0 to 6.0 percent, by weight, of lead, and provide an
industrially satisfactory machinability. Because of their excellent
machinability, those lead-contained copper alloys have been an
important basic material for a variety of articles such as city
water faucets, water supply/drainage metal fittings and valves.
[0006] However, the application of those lead-mixed alloys has been
greatly limited in recent years, because lead contained therein is
an environmental pollutant harmful to humans. That is, the
lead-contained alloys pose a threat to human health and
environmental hygiene because lead is contained in metallic vapor
that is generated in the steps of processing those alloys at high
temperatures, such as in melting and casting operations. There is
also a concern that lead contained in water system metal fittings,
valves, and other components made of those alloys will dissolve out
into drinking water.
[0007] For these reasons, the United States and other advanced
countries have been moving to tighten the standards for
lead-contained copper alloys, drastically limiting the permissible
level of lead in copper alloys in recent years. In Japan, too, the
use of lead-contained alloys has been increasingly restricted, and
there has been a growing call for development of free-cutting
copper alloys with a low lead content.
SUMMARY OF THE INVENTION
[0008] It is an object of the present invention to provide a
lead-free copper alloy which does not contain the
machinability-improving element lead, yet is quite excellent in
machinability and can be used as safe substitute for the
conventional free cutting (easy-to-cut) copper alloy that has a
high lead content, with concomitant environmental hygienic
problems. The lead-free copper alloy of the present invention also
permits recycling of chips without problems. Thus, the present
invention presents a timely answer to the mounting call for
restriction of lead-containing products.
[0009] It is an another object of the present invention to provide
a lead-free copper alloy that has high corrosion resistance as well
as excellent machinability, and is suitable as basic material for
cutting works, forgings, castings, and other applications, thus
having a very high practical value. The cutting works, forgings,
castings, and other applications include city water faucets, water
supply/drainage metal fittings, valves, stems, hot water supply
pipe fittings, shaft and heat exchanger parts.
[0010] It is yet another object of the present invention to provide
a lead-free copper alloy with high strength and wear resistance as
well as machinability. This lead-free copper alloy is suitable as
basic material for the manufacture of cutting works, forgings,
castings, and other uses requiring high strength and wear
resistance such as, for example, bearings, bolts, nuts, bushes,
gears, sewing machine parts, and hydraulic system parts. Hence,
this embodiment of the present invention has a very high practical
value.
[0011] It is a further object of the present invention to provide a
lead-free copper alloy with excellent high-temperature oxidation
resistance as well as machinability, which alloy is suitable as
basic material for the manufacture of cutting works, forgings,
castings, and other uses where high thermal oxidation resistance is
essential, e.g., nozzles for kerosene oil and gas heaters, burner
heads, and gas nozzles for hot-water dispensers. Hence, this
embodiment of the present invention too has a very high practical
value.
[0012] The objects of the present inventions are achieved by
provision of the following copper alloys:
[0013] A lead-free free-cutting copper alloy with an excellent
machinability, which is composed of 69 to 79 percent, by weight, of
copper, more than 3.0 to 4.0 percent or less, by weight, of
silicon, and the remaining percent, by weight, of zinc, wherein the
percent by weight of copper and silicon in the copper alloy satisfy
the relationship; 55.ltoreq.X-3Y .ltoreq.70, wherein X is the
percent, by weight, of copper, and Y is the percent, by weight, of
silicon; and the copper alloy has a metal construction comprising
multiple phases integrated to form a composite phase, wherein the
composite phase is an .alpha. phase matrix having a total phase
area comprising not more than 5% of a .beta. phase, and 5-70% of
the total phase area is provided by at least one phase selected
from the group consisting of a .gamma. phase, a .kappa. phase, and
a .mu. phase. For purpose of simplicity, this copper alloy will be
hereinafter called the "first invention alloy".
[0014] Lead does not form a solid solution in the matrix but
instead disperses in a granular form to improve the machinability
of an alloy. Silicon enhances the easy-to-cut property of an alloy
by producing a gamma phase (in some cases, a kappa phase) in the
structure of metal. That way, both act to improve alloy
machinability, though they are quite different in their respective
contributions to the properties of the alloy. On the basis of that
recognition, silicon is added to the first invention alloy in place
of lead so as to bring about a high level of machinability meeting
industrial requirements. That is, the first invention alloy is
improved in machinability through formation of a gamma phase with
the addition of silicon.
[0015] The addition of less than 2.0 percent, by weight, of silicon
cannot form a gamma phase sufficient to provide industrially
satisfactory machinability. With increases above 2.0 weight-percent
in the addition of silicon, the machinability improves. But with
the addition of more than 4.0 percent, by weight, of silicon, the
machinability will not improve proportionally. A problem is,
however, that silicon has a high melting point and a low specific
gravity and is also liable to oxidize. If silicon alone is fed in a
simple substance into a furnace in an alloy melting step, silicon
will float on the molten metal and be oxidized into oxides of
silicon (or silicon oxide), hampering production of a
silicon-containing copper alloy. In making an ingot of
silicon-containing copper alloy, therefore, silicon is usually
added in the form of a Cu--Si alloy, which boosts the production
cost. In the light of the cost of making the alloy, too, it is not
desirable to add silicon in a quantity exceeding the saturation
point where machinability improvement levels off, i.e., 4.0 percent
by weight. Experimentation has shown that when silicon is added in
an amount of more than 3.0 percent and up to and including 4.0
percent, by weight, it is desirable to hold the content of copper
to 69 to 79 percent, by weight, in consideration of its relation to
the content of zinc in order to maintain the intrinsic properties
of the Cu--Zn alloy. For this reason, the first invention alloy is
composed of 69 to 79 percent, by weight, of copper and more than
3.0 percent and up to and including 4.0 percent, by weight, of
silicon. It is stressed that the range of silicon content included
, by weight, in the composition of the first invention alloy
excludes 3 percent, by weight, of silicon. The addition of silicon,
as specified above, improves not only the machinability but also
the flow of the molten metal in casting, strength, wear resistance,
resistance to stress corrosion cracking, high-temperature oxidation
resistance. Also, the ductility and dezincification resistance will
be improved to some extent.
[0016] A lead-free free-cutting copper alloy, also with an
excellent machinability, which is composed of 69 to 79 percent, by
weight, of copper; 2.0 to 4.0 percent, by weight, of silicon; at
least one element selected from among 0.02 to 0.4 percent, by
weight, of bismuth, 0.02 to 0.4 percent, by weight, of tellurium,
and 0.02 to 0.4 percent, by weight, of selenium; and the remaining
percent, by weight, of zinc, wherein the percent by weight of
copper and silicon in the copper alloy satisfy the relationship;
55.ltoreq.X-3Y.ltoreq.70, wherein X is the percent, by weight, of
copper, and Y is the percent, by weight, of silicon; and the copper
alloy has a metal construction comprising multiple phases
integrated to form a composite phase, wherein the composite phase
is an .alpha. phase matrix having a total phase area comprising not
more than 5% of a .beta. phase, and 5-70% of the total phase area
is provided by at least one phase selected from the group
consisting of a .gamma. phase, a .kappa. phase, and a .mu. phase.
This second copper alloy will be hereinafter called the "second
invention alloy."
[0017] That is, the second invention alloy is composed of the first
invention alloy and at least one element selected from among 0.02
to 0.4 percent, by weight, of bismuth, 0.02 to 0.4 percent, by
weight, of tellurium, and 0.02 to 0.4 percent, by weight, of
selenium.
[0018] Bismuth, tellurium, and selenium, like lead, do not form a
solid solution in the matrix but disperse in granular form to
enhance machinability through a mechanism different from that of
silicon. Hence, the addition of those elements along with silicon
could further improve the machinability beyond the level obtained
by the addition of silicon alone. From this finding, the second
invention alloy is provided in which at least one element selected
from among bismuth, tellurium, and selenium is mixed to further
improve the machinability obtained by the first invention alloy.
The addition of bismuth, tellurium, or selenium in addition to
silicon produces a high machinability such that complicated forms
can be freely cut at a high speed. But no improvement in
machinability can be realized from the addition of bismuth,
tellurium, or selenium in an amount less than 0.02 percent, by
weight. However, those elements are expensive as compared with
copper. Even if the addition exceeds 0.4 percent by weight, the
proportional improvement in machinability is so small that the
addition beyond that does not pay economically. What is more, if
the addition is more than 0.4 percent by weight, the alloy will
deteriorate in hot workability such as forgeability and cold
workability such as ductility. While there might be a concern that
heavy metals like bismuth would cause problems similar to those of
lead, addition of a very small amount of less than 0.4 percent by
weight is negligible and would present no particular problems.
Based upon these considerations, the second invention alloy is
prepared with the addition of bismuth, tellurium, or selenium kept
to 0.02 to 0.4 percent by weight. The addition of those elements,
which positively affect the machinability of the copper alloy
though a mechanism different from that of silicon, as mentioned
above, would not affect the proper contents of copper and silicon.
On this ground, the contents of copper and silicon in the second
invention alloy are set at the same level as those in the first
invention alloy.
[0019] A lead-free free-cutting copper alloy that also has
excellent machinability which is composed of 70 to 80 percent, by
weight, of copper; 1.8 to 3.5 percent, by weight, of silicon; at
least one element selected from among 0.3 to 3.5 percent, by
weight, of tin, and 0.02 to 0.25 percent, by weight, of phosphorus;
and the remaining percent, by weight, of zinc, wherein the percent
by weight of copper, silicon, tin and phosphorus in the copper
alloy satisfy the relationship; 55.ltoreq.X-3Y+aZ +bW.ltoreq.70,
wherein X is the percent, by weight, of copper, Y is the percent,
by weight, of silicon, Z is the percent, by weight, of tin, W is
the percent, by weight, of phosphorus, a is -0.5, and b is -3; and
the copper alloy has a metal construction comprising multiple
phases integrated to form a composite phase, wherein the composite
phase is an .alpha. phase matrix having a total phase area
comprising not more than 5% of a .beta. phase, and 5-70% of the
total phase area is provided by at least one phase selected from
the group consisting of a .gamma. phase, a .kappa. phase, and a
.mu. phase. This third copper alloy will be hereinafter called the
"third invention alloy."
[0020] Tin works the same way as silicon. That is, if tin is added
to the Cu--Zn alloy, a gamma phase will be formed and the
machinability of the Cu--Zn alloy will be improved. For example,
the addition of tin in an amount of 1.8 to 4.0 percent by weight
would bring about a high machinability in the Cu--Zn alloy
containing 58 to 70 percent, by weight, of copper; even if silicon
is not added. Therefore, the addition of tin to the Cu--Si--Zn
alloy can facilitate the formation of a gamma phase and further
improve the machinability of the Cu--Si--Zn alloy. The gamma phase
is formed with the addition of tin in an amount of 1.0 or more
percent by weight, and gamma phase formation reaches the saturation
point at 3.5 percent, by weight, of tin. If tin exceeds 3.5 percent
by weight, the ductility will drop instead. With the addition of
tin in amounts less than 1.0 percent by weight, on the other hand,
no gamma phase will be formed. If the addition is 0.3 percent or
more by weight, then tin will be effective in uniformly dispersing
the gamma phase formed by silicon. Machinability is improved
through that effect of dispersing the gamma phase. In other words,
the addition of tin in amounts of not less than 0.3 percent by
weight improves the machinability of the alloy.
[0021] As for phosphorus, it has no property of forming the gamma
phase as in the case of tin. However, phosphorus works to uniformly
disperse and distribute the gamma phase formed as a result of the
addition of silicon alone or with tin. In that way, improvement in
machinability through gamma phase formation is further enhanced. In
addition to dispersing the gamma phase, phosphorus helps to refine
the crystal grains in the alpha phase in the matrix, improving hot
workability and also strength and resistance to stress corrosion
cracking. Furthermore, phosphorus substantially increases the flow
of molten metal in casting. To produce such results, phosphorus
will have to be added in an amount not smaller than 0.02 percent by
weight. But if the addition exceeds 0.25 percent by weight, no
proportional effect is obtained. Instead, there will be a decrease
in hot forging properties and in extrudability.
[0022] In consideration of those observations, the third invention
alloy is improved in machinability by adding to the Cu--Si--Zn
alloy at least one element selected from among 0.3 to 3.5 percent,
by weight, of tin, and 0.02 to 0.25 percent, by weight, of
phosphorus.
[0023] Meanwhile, tin and phosphorus serve to improve the
machinability by forming a gamma phase or dispersing that phase,
and work closely with silicon in promoting the improvement in
machinability through the gamma phase. In the third invention alloy
mixed with silicon along with tin or phosphorus, therefore, silicon
does not work alone. Machinability is improved not only by the
silicon, but by tin or phosphorus, and thus the required addition
of silicon is smaller than that in the second invention alloy in
which the machinability is enhanced by adding bismuth, tellurium,
or selenium. That is, those elements bismuth, tellurium, and
selenium contribute to improving the machinability, not by acting
on the gamma phase but by dispersing in the form of grains in the
matrix. Even if the addition of silicon is less than 2.0 percent by
weight, silicon along with tin or phosphorus will be able to
enhance the machinability to an industrially satisfactory level as
long as the percentage of silicon is 1.8 or more percent by weight.
But even if the addition of silicon is not larger than 4.0 percent
by weight, the effect of silicon in improving machinability is
saturated and is not promoted any further in the cases where tin or
phosphorus is added, when the silicon content exceeds 3.5 percent
by weight. For this reason, the addition of silicon is set at 1.8
to 3.5 percent by weight in the third invention alloy. Also, in
consideration of the added amount of silicon and also the addition
of tin or phosphorus, the content range of copper in this third
invention alloy is slightly raised from the level in the second
invention alloy and is set at 70 to 80 percent by weight as
preferred content of copper.
[0024] A lead-free free-cutting copper alloy also with an excellent
easy-to-cut (i.e., machinability) feature which is composed of 70
to 80 percent, by weight, of copper; 1.8 to 3.5 percent, by weight,
of silicon; at least one element selected from among 0.3 to 3.5
percent, by weight, of tin and 0.02 to 0.25 percent, by weight, of
phosphorus; at least one element selected from among 0.02 to 0.4
percent, by weight, of bismuth, 0.02 to 0.4 percent, by weight, of
tellurium, and 0.02 to 0.4 percent, by weight, of selenium; and the
remaining percent, by weight, of zinc, wherein the percent by
weight of copper, silicon, tin and phosphorus in the copper alloy
satisfy the relationship; 55.ltoreq.X-3Y+aZ+bW.ltoreq.70- , wherein
X is the percent, by weight, of copper, Y is the percent, by
weight, of silicon, Z is the percent, by weight, of tin, W is the
percent, by weight, of phosphorus, a is -0.5, and b is -3; and the
copper alloy has a metal construction comprising multiple phases
integrated to form a composite phase, wherein the composite phase
is an .alpha. phase matrix having a total phase area comprising not
more than 5% of a .beta. phase, and 5-70% of the total phase area
is provided by at least one phase selected from the group
consisting of a .gamma. phase, a .kappa. phase, and a .mu. phase.
This fourth copper alloy will be hereinafter called the "fourth
invention alloy."
[0025] The fourth invention alloy thus contains at least one
element selected from among 0.02 to 0.4 percent, by weight, of
bismuth, 0.02 to 0.4 percent, by weight, of tellurium, and 0.02 to
0.4 percent, by weight, of selenium, in addition to the components
in the third invention alloy. The grounds for adding those
additional elements and setting the amounts to be added are the
same as given for the second invention alloy.
[0026] A lead-free free-cutting copper alloy having excellent
machinability and exhibiting a high degree of corrosion resistance,
which is composed of 69 to 79 percent, by weight, of copper; 2.0 to
4.0 percent, by weight, of silicon; at least one element selected
from among 0.3 to 3.5 percent, by weight, of tin and 0.02 to 0.25
percent, by weight, of phosphorus, at least one element selected
from among 0.02 to 0.15 percent, by weight, of antimony, and 0.02
to 0.15 percent, by weight, of arsenic, and the remaining percent,
by weight, of zinc, wherein the percent by weight of copper,
silicon, tin and phosphorus in the copper alloy satisfy the
relationship; 55.ltoreq.X-3Y+aZ+bW.ltoreq.70- , wherein X is the
percent, by weight, of copper, Y is the percent, by weight, of
silicon, Z is the percent, by weight, of tin, W is the percent, by
weight, of phosphorus, a is -0.5, and b is -3; and the copper alloy
has a metal construction comprising multiple phases integrated to
form a composite phase, wherein the composite phase is an .alpha.
phase matrix having a total phase area comprising not more than 5%
of a .beta. phase, and 5-70% of the total phase area is provided by
at least one phase selected from the group consisting of a .gamma.
phase, a .kappa. phase, and a .mu. phase. This fifth copper alloy
will be hereinafter called the "fifth invention alloy."
[0027] The fifth invention alloy thus contains at least one element
selected from among 0.3 to 3.5 percent, by weight, of tin and 0.02
to 0.25 percent, by weight, of phosphorus, at least one element
selected from among 0.02 to 0.15 percent, by weight, of antimony,
and 0.02 to 0.15 percent, by weight, of arsenic, in addition to the
first invention alloy.
[0028] Tin is effective in improving not only the machinability but
also the corrosion resistance properties (dezincification
resistance and erosion corrosion resistance) and forgeability of
the alloy. In other words, tin improves the corrosion resistance in
the alpha phase matrix and, by dispersing the gamma phase, the
corrosion resistance, forgeability, and stress corrosion cracking
resistance. The fifth invention alloy is thus improved in corrosion
resistance by such property of tin and in machinability mainly by
adding silicon. Therefore, the contents of silicon and copper in
this alloy are set at the same as those in the first invention
alloy. To raise the corrosion resistance and forgeability, on the
other hand, tin would have to be added in an amount of at least 0.3
percent by weight. But even if the addition of tin exceeds 3.5
percent by weight, the corrosion resistance and forgeability will
not improve in proportion to the added amount of tin. The addition
of amounts of tin in excess of 3.5 percent by weight is, therefore,
uneconomical.
[0029] As described above, phosphorus disperses the gamma phase
uniformly and at the same time refines the crystal grains in the
alpha phase in the matrix, thereby improving the machinability and
also the corrosion resistance properties (dezincification
resistance and erosion corrosion resistance), forgeability, stress
corrosion cracking resistance, and mechanical strength. The fifth
invention alloy is thus improved in corrosion resistance and other
properties by such properties of phosphorus and in machinability
mainly by adding silicon. The addition of phosphorus in a very
small quantity; that is, 0.02 or more percent by weight can produce
beneficial results. But the addition in an amount of more than 0.25
percent by weight would not produce proportional benefits, and
instead would reduce hot forgeability and extrudability.
[0030] Just as with phosphorus, antimony and arsenic in a very
small quantities--0.02 or more percent by weight--are effective in
improving the dezincification resistance and other properties. But
their addition in amounts exceeding 0.15 percent by weight would
not produce results in proportion to the quantity mixed. Instead,
it would lower the hot forgeability and extrudability, as would
phosphorus applied in excessive amounts.
[0031] Those observations indicate that the fifth invention alloy
is improved in machinability and also corrosion resistance and
other properties by adding at least one element selected from among
tin and phosphorus, and by adding at least one element selected
from among antimony and arsenic, in quantities within the aforesaid
limits, in addition to the same quantities of copper and silicon as
in the first invention copper alloy. In the fifth invention alloy,
the additions of copper and silicon are set at 69 to 79 percent by
weight and 2.0 to 4.0 percent by weight respectively--the same
level as in the first invention alloy in which any other
machinability improver than silicon is not added--because tin and
phosphorus work mainly as corrosion resistance improvers like
antimony and arsenic.
[0032] A lead-free free-cutting copper alloy, also with excellent
machinability and with high corrosion resistance, which is composed
of 69 to 79 percent, by weight, of copper; 2.0 to 4.0 percent, by
weight, of silicon; at least one element selected from among 0.3 to
3.5 percent, by weight, of tin and 0.02 to 0.25 percent, by weight,
of phosphorus, at least one element selected from among 0.02 to
0.15 percent, by weight, of antimony, and 0.02 to 0.15 percent, by
weight, of arsenic; at least one element selected from among 0.02
to 0.4 percent, by weight, of bismuth, 0.02 to 0.4 percent, by
weight, of tellurium, and 0.02 to 0.4 percent, by weight, of
selenium; and the remaining percent, by weight, of zinc, wherein
the percent by weight of copper, silicon, tin and phosphorus in the
copper alloy satisfy the relationship;
55.ltoreq.X-3Y+aZ+bW.ltoreq.70- , wherein X is the percent, by
weight, of copper, Y is the percent, by weight, of silicon, Z is
the percent, by weight, of tin, W is the percent, by weight, of
phosphorus, a is -0.5, and b is --3; and the copper alloy has a
metal construction comprising multiple phases integrated to form a
composite phase, wherein the composite phase is an .alpha. phase
matrix having a total phase area comprising not more than 5% of a
.beta. phase, and 5-70% of the total phase area is provided by at
least one phase selected from the group consisting of a .gamma.
phase, a .kappa. phase, and a .mu. phase. This sixth copper alloy
will be hereinafter called the "sixth invention alloy."
[0033] The sixth invention alloy thus contains at least one element
selected from among 0.02 to 0.4 percent, by weight, of bismuth,
0.02 to 0.4 percent, by weight, of tellurium, and 0.02 to 0.4
percent, by weight, of selenium, in addition to the components in
the fifth invention alloy. The machinability of the alloy is
improved by adding silicon and at least one element selected from
among bismuth, tellurium, and selenium as in the second invention
alloy and the corrosion resistance and other properties are raised
by using at least one element selected from among tin, phosphorus,
antimony, and arsenic as in the fifth invention alloy. Therefore,
the additions of copper, silicon, bismuth, tellurium, and selenium
are set at the same levels as those in the second invention alloy,
while the contents of tin, phosphorus, antimony, and arsenic are
adjusted to the levels of the same elements in the fifth invention
alloy.
[0034] A lead-free free-cutting copper alloy, also with excellent
machinability and with excellent high strength features and high
corrosion resistance, which is composed of 62 to 78 percent, by
weight, of copper; 2.5 to 4.5 percent, by weight, of silicon; at
least one element selected from among 0.3 to 3.0 percent, by
weight, of tin and 0.02 to 0.25 percent, by weight, of phosphorus;
and at least one element selected from among 0.7 to 3.5 percent, by
weight, of manganese and 0.7 to 3.5 percent, by weight, of nickel;
and the remaining percent, by weight, of zinc, wherein the percent
by weight of copper, silicon, tin, phosphorus, manganese and nickel
in the copper alloy satisfy the relationship; 55.ltoreq.X-3Y+aZ+bW
+cV+dU.ltoreq.70, wherein X is the percent, by weight, of copper, Y
is the percent, by weight, of silicon, Z is the percent, by weight,
of tin, W is the percent, by weight, of phosphorus, V is the
percent, by weight, of manganese, U is the percent, by weight, of
nickel, a is -0.5, b is -3, c is 2.5, d is 2.5, and the percent by
weith of silicon, manganese and nickel satisfy the relationship;
0.7.ltoreq.Y/(V+U).ltoreq.6; and the copper alloy has a metal
construction comprising multiple phases integrated to form a
composite phase, wherein the composite phase is an .alpha. phase
matrix having a total phase area comprising not more than 5% of a
.beta. phase, and 5-70% of the total phase area is provided by at
least one phase selected from the group consisting of a .gamma.
phase, a .kappa. phase, and a .mu. phase. The seventh copper alloy
will be hereinafter called the "seventh invention alloy."
[0035] Manganese and nickel combine with silicon to form
intermetallic compounds, which may be represented by the formulas
Mn.sub.xSi.sub.y or Ni.sub.xSi.sub.y, which intermetallic compounds
are evenly precipitated in the matrix, thereby raising the wear
resistance and strength of the alloy containing them. Thus the
addition of manganese and/or nickel improves high strength features
and wear resistance. Improved effects are exhibited when manganese
and nickel are added in amounts not less than 0.7 percent by
weight, respectively. But the saturation state is reached at 3.5
percent by weight, and even if the addition is increased beyond
that, no proportional results will be obtained. The addition of
silicon is set at 2.5 to 4.5 percent by weight to match the
addition of manganese or nickel, taking into consideration the
consumption to form intermetallic compounds with those
elements.
[0036] It is also noted that tin and phosphorus help to reinforce
the alpha phase in the matrix, thereby improving strength, wear
resistance, and also machinability. Tin and phosphorus disperse the
alpha and gamma phases, by which the strength, wear resistance, and
machinability are improved. Tin in an amount of 0.3 or more percent
by weight is effective in improving the strength and machinability.
However, if the addition exceeds 3.0 percent by weight, ductility
will decrease. For this reason, the addition of tin is set at 0.3
to 3.0 percent by weight, to raise the high strength features and
wear resistance in the seventh invention alloy and also to enhance
the machinability thereof. The addition of phosphorus disperses the
gamma phase and at the same time refines the crystal grains in the
alpha phase in the matrix, thereby improving hot workability as
well as the strength and wear resistance. Furthermore, phosphorus
is very effective in improving the flow of molten metal in casting.
Such results will be produced when phosphorus is added in the range
of 0.02 to 0.25 percent by weight. The content of copper is set at
62 to 78 percent by weight, in view of the addition of silicon and
the bonding of silicon with manganese and nickel.
[0037] A lead-free free-cutting copper alloy, also with excellent
machinability and with excellent high strength features as well as
high wear resistance, comprises 62 to 78 percent, by weight, of
copper; 2.5 to 4.5 percent, by weight, of silicon; at least one
element selected from among 0.3 to 3.0 percent, by weight, of tin
and 0.02 to 0.25 percent, by weight, of phosphorus; and at least
one element selected from among 0.7 to 3.5 percent, by weight, of
manganese and 0.7 to 3.5 percent, by weight, of nickel; at least
one element selected from among 0.02 to 0.4 percent, by weight, of
bismuth, 0.02 to 0.4 percent, by weight, of tellurium, and 0.02 to
0.4 percent, by weight, of selenium; and the remaining percent, by
weight, of zinc, wherein the percent by weight of copper, silicon,
tin, phosphorus, manganese and nickel in the copper alloy satisfy
the relationship; 55.ltoreq.X-3Y+aZ+bW+cV+dU.ltoreq.70, wherein X
is the percent, by weight, of copper, Y is the percent, by weight,
of silicon, Z is the percent, by weight, of tin, W is the percent,
by weight, of phosphorus, V is the percent, by weight, of
manganese, U is the percent, by weight, of nickel, a is -0.5, b is
-3, c is 2.5, d is 2.5, and the percent by weith of silicon,
manganese and nickel satisfy the relationship;
0.7.ltoreq.Y/(V+U).ltoreq.6; and the copper alloy has a metal
construction comprising multiple phases integrated to form a
composite phase, wherein the composite phase is an .alpha. phase
matrix having a total phase area comprising not more than 5% of a
.beta. phase, and 5-70% of the total phase area is provided by at
least one phase selected from the group consisting of a .gamma.
phase, a .kappa. phase, and a .mu. phase. The eighth copper alloy
will be hereinafter called the "eighth invention alloy."
[0038] The eighth copper alloy contains at least one element
selected from among 0.02 to 0.4 percent, by weight, of bismuth,
0.02 to 0.4 percent, by weight, of tellurium, and 0.02 to 0.4
percent, by weight, of selenium in addition to the components in
the seventh invention alloy. While high-strength features and wear
resistance as high as in the seventh invention alloy are secured,
the eighth invention alloy is further improved in machinability by
the addition of at least one element selected among bismuth and
other elements which are effective in raising the machinability
through a mechanism different from that exhibited by silicon. The
reasons for adding machinability improvers such as bismuth and
others and deciding on the quantities thereof to be added are the
same as those given for the second, fourth, and sixth invention
alloys. The grounds for adding the other elements, that is, copper,
zinc, tin, manganese, and nickel, and setting the contents thereof,
are the same as given for the seventh invention alloy.
[0039] A lead-free free-cutting copper alloy also with excellent
machinability coupled with a good high-temperature oxidation
resistance which is composed of 69 to 79 percent, by weight, of
copper; 2.0 to 4.0 percent, by weight, of silicon; 0.1 to 1.5
percent, by weight, of aluminum; 0.02 to 0.25 percent, by weight,
of phosphorus; and the remaining percent, by weight, of zinc,
wherein the percent by weight of copper, silicon, aluminum and
phosphorus in the copper alloy satisfy the relationship;
55.ltoreq.X-3Y+aZ+bW.ltoreq.70, wherein X is the percent, by
weight, of copper, Y is the percent, by weight, of silicon, Z is
the percent, by weight, of aluminum, W is the percent, by weight,
of phosphorus, a is -2, and b is -3; and the copper alloy has a
metal construction comprising multiple phases integrated to form a
composite phase, wherein the composite phase is an .alpha. phase
matrix having a total phase area comprising not more than 5% of a
.beta. phase, and 5-70% of the total phase area is provided by at
least one phase selected from the group consisting of a .gamma.
phase, a .kappa. phase, and a .mu. phase. The ninth copper alloy
will be hereinafter called the "ninth invention alloy."
[0040] Aluminum is an element which improves the strength,
machinability, wear resistance, and also high-temperature oxidation
resistance. Silicon, too, has a property of enhancing the
machinability, strength, wear resistance, resistance to stress
corrosion cracking, and also high-temperature oxidation resistance
of an alloy, as mentioned above. Aluminum works to raise the
high-temperature oxidation resistance when the aluminum is added in
amounts of not less than 0.1 percent by weight, together with
silicon. But when increasing the addition of aluminum beyond 1.5
percent by weight, no proportional results can be expected with
respect to high-temperature oxidation resistance. For this reason,
the addition of aluminum is set at 0.1 to 1.5 percent by
weight.
[0041] Aluminum is also effective in promoting the formation of the
gamma phase. The addition of aluminum together with tin or in place
of tin could further improve the machinability of the Cu--Si--Zn
alloy. Aluminum is also effective in improving the strength, wear
resistance, and high-temperature oxidation resistance as well as
the machinability and also in minimizing the specific gravity. If
the machinability is to be improved at all, aluminum will have to
be added in amounts of at least 1.0 percent by weight.
[0042] Phosphorus is added to enhance the flow of molten metal in
casting. Phosphorus also works to improve the aforesaid
machinability, dezincification resistance, and high-temperature
oxidation resistance, in addition to the flow of molten metal.
Those effects are exhibited when phosphorus is added in an amount
not smaller than 0.02 percent by weight. But even if phosphorus is
used in an amount of more than 0.25 percent by weight, it will not
result in a proportional increase in effect. For this reason, the
addition of phosphorus is set at 0.02 to 0.25 percent by
weight.
[0043] While silicon is added to improve the machinability of an
alloy as mentioned above, it is also capable of increasing the flow
of molten metal as is phosphorus. The effect of silicon in
improving the flowability of molten metal is exhibited when it is
added in an amount not smaller than 2.0 percent by weight. The
range of the addition of silicon for improving the flowability of
molten metal overlaps that for improvement of the machinability
thereof. Taking both of these factors into consideration, the
addition of silicon is set in the range 2.0 to 4.0 percent by
weight.
[0044] A lead-free free-cutting copper alloy also with excellent
machinability and good high-temperature oxidation resistance which
is composed of 69 to 79 percent, by weight, of copper; 2.0 to 4.0
percent, by weight, of silicon; 0.1 to 1.5 percent, by weight, of
aluminum; 0.02 to 0.25 percent, by weight, of phosphorus; at least
one element selected from among 0.02 to 0.4 percent, by weight, of
chromium and 0.02 to 0.4 percent, by weight, of titanium; and the
remaining percent, by weight, of zinc, wherein the percent by
weight of copper, silicon, aluminum, phosphorus and chromium in the
copper alloy satisfy the relationship;
55.ltoreq.X-3Y+aZ+bW+cV.ltoreq.70, wherein X is the percent, by
weight, of copper, Y is the percent, by weight, of silicon, Z is
the percent, by weight, of aluminum, W is the percent, by weight,
of phosphorus, V is the percent, by weight, of chromium, a is -2, b
is -3, c is 2; and the copper alloy has a metal construction
comprising multiple phases integrated to form a composite phase,
wherein the composite phase is an a phase matrix having a total
phase area comprising not more than 5% of a .beta. phase, and 5-70%
of the total phase area is provided by at least one phase selected
from the group consisting of a .gamma. phase, a .kappa. phase, and
a .mu. phase. The tenth copper alloy will be hereinafter called the
"tenth invention alloy."
[0045] Chromium and/or titanium are added in order to improve
high-temperature oxidation resistance. Good results can be expected
especially when they are added together with aluminum to produce a
synergistic effect. Those effects are exhibited when the addition
is 0.02 percent or more by weight, whether they are used alone or
in combination. The saturation point is 0.4 percent by weight. In
consideration of these observations, the tenth invention alloy
contains at least one element selected from among 0.02 to 0.4
percent by weight of chromium and 0.02 to 0.4 percent by weight of
titanium in addition to the components of the ninth invention
alloy, and thus is an improvement over the ninth invention alloy
with regard to the high- temperature oxidation resistance of the
alloy produced.
[0046] A lead-free free-cutting copper alloy also with excellent
machinability and a good high-temperature oxidation resistance
which is composed of 69 to 79 percent, by weight, of copper; 2.0 to
4.0 percent, by weight, of silicon; 0.1 to 1.5 percent, by weight,
of aluminum; 0.02 to 0.25 percent, by weight, of phosphorus; at
least one element selected from among 0.02 to 0.4 percent, by
weight, of bismuth, 0.02 to 0.4 percent, by weight, of tellurium,
and 0.02 to 0.4 percent, by weight, of selenium; and the remaining
percent, by weight, of zinc, wherein the percent by weight of
copper, silicon, tin and phosphorus in the copper alloy satisfy the
relationship; 55.ltoreq.X-3Y+aZ+bW.ltoreq.70, wherein X is the
percent, by weight, of copper, Y is the percent, by weight, of
silicon, Z is the percent, by weight, of aluminum, W is the
percent, by weight, of phosphorus, a is -2, and b is -3; and the
copper alloy has a metal construction comprising multiple phases
integrated to form a composite phase, wherein the composite phase
is an .alpha. phase matrix having a total phase area comprising not
more than 5% of .beta. phase, and 5-70% of the total phase area is
provided by at least one phase selected from the group consisting
of a .gamma. phase, a .kappa. phase, and a .mu. phase. The eleventh
copper alloy will be hereinafter called the "eleventh invention
alloy."
[0047] The eleventh invention alloy contains at least one element
selected from among 0.02 to 0.4 percent, by weight, of bismuth,
0.02 to 0.4 percent, by weight, of tellurium, and 0.02 to 0.4
percent, by weight, of selenium, in addition to the components of
the ninth invention alloy. While having as high a high-temperature
oxidation resistance as the ninth invention alloy, the eleventh
invention alloy is further improved in machinability by the
addition of at least one element selected from among bismuth and
other elements which are effective in raising machinability through
a mechanism other than that exhibited by silicon.
[0048] A lead-free free-cutting copper alloy also with excellent
machinability and a good high-temperature oxidation resistance
which is composed of 69 to 79 percent, by weight, of copper; 2.0 to
4.0 percent, by weight, of silicon; 0.1 to 1.5 percent, by weight,
of aluminum; 0.02 to 0.25 percent, by weight, of phosphorus; at
least one element selected from among 0.02 to 0.4 percent, by
weight, of chromium, and 0.02 to 0.4 percent by weight of titanium;
at least one element selected from among 0.02 to 0.4 percent, by
weight, of bismuth, 0.02 to 0.4 percent, by weight, of tellurium,
and 0.02 to 0.4 percent, by weight, of selenium; and the remaining
percent, by weight, of zinc, wherein the percent by weight of
copper, silicon, aluminum, phosphorus and chromium in the copper
alloy satisfy the relationship; 55.ltoreq.X-3Y+aZ+bW+cV.ltoreq.70,
wherein X is the percent, by weight, of copper, Y is the percent,
by weight, of silicon, Z is the percent, by weight, of aluminum, W
is the percent, by weight, of phosphorus, V is the percent, by
weight, of chromium, a is -2, b is -3, c is 2; and the copper alloy
has a metal construction comprising multiple phases integrated to
form a composite phase, wherein the composite phase is an .alpha.
phase matrix having a total phase area comprising not more than 5%
of a .beta. phase, and 5-70% of the total phase area is provided by
at least one phase selected from the group consisting of a .gamma.
phase, a .kappa. phase, and a .mu. phase. The twelfth copper alloy
will be hereinafter called the "twelfth invention alloy."
[0049] The twelfth invention alloy contains, in addition to the
components of the tenth invention alloy, at least one element
selected from among 0.02 to 0.4 percent, by weight, of bismuth,
0.02 to 0.4 percent, by weight, of tellurium, and 0.02 to 0.4
percent, by weight, of selenium. While as high a high-temperature
oxidation resistance as in the tenth invention alloy is obtained,
the twelfth invention alloy is further improved in machinability by
adding at least one element selected from among bismuth and other
elements which are effective in raising the machinability through a
mechanism other than that exhibited by silicon.
[0050] A lead-free free-cutting copper alloy, also with further
improved machinability, is obtained by subjecting any one of the
preceding invention alloys to a heat treatment for 30 minutes to 5
hours at a temperature of from 400.degree. C. to 600.degree. C.
This thirteenth copper alloy will be hereinafter called the
"thirteenth invention alloy."
[0051] The first to twelfth invention alloys contain machinability
improving elements such as silicon and have an excellent
machinability because of the addition of such elements. Of those
invention alloys, the alloys with a high copper content which have
large amounts of other phases--mainly alloys having a kappa phase
percentage greater than the total percentage of their alpha, beta,
gamma, and delta phases together--can further improve in
machinability in a heat treatment. As a result of the specified
heat treatment, the kappa phase turns into a gamma phase. The gamma
phase finely disperses and precipitates to further enhance the
machinability of the alloy. The present alloys with high copper
content are high in ductility of the matrix and low in absolute
quantity of gamma phase, and therefore are excellent in cold
workability. But in cases where cold working, such as caulking and
cutting, are required, the aforesaid heat treatment is very
useful.
[0052] In other words, among the first to twelfth invention alloys,
those which are high in copper content--with gamma phase in small
quantities and kappa phase in large quantities--(hereinafter
referred to as the "high copper content alloy") undergo a change in
phase from the kappa phase to the gamma phase during the heat
treatment. As a result, the gamma phase is finely dispersed and
precipitated, and the machinability of the alloy is improved. In
practice, during the manufacturing process of castings, expanded
metals, and hot forgings, the materials are often force-air-cooled
or water cooled depending on the forging conditions, productivity
after hot working (hot extrusion, hot forging, etc.), working
environment, and other factors. In such cases, among the first to
twelfth invention alloys, those with a low content of copper
(hereinafter called the "low copper content alloy") are rather low
in the content of the gamma phase and contain beta phase. During
the heat treatment, the beta phase changes into the gamma phase,
and the gamma phase is finely dispersed and precipitated, whereby
the machinability is improved.
[0053] Experiments show that heat treatment is especially
effective: with high copper content alloys, where the mixing ratio
of copper and silicon to other added elements (except for zinc) A
is given as 67.ltoreq.Cu-3Si+aA; and with low copper content
alloys, where the mixing ratio of copper and silicon to other added
elements (except for zinc) A is given as 64.gtoreq.Cu -3Si+aA. It
is noted that "a" is a coefficient. The coefficient is different
depending on the added element A. For example, with tin, a is -0.5;
aluminum, -2; phosphorus, -3; antimony, 0; arsenic, 0; manganese,
+2.5; and nickel, +2.5.
[0054] In accordance with the present invention, heat treatment at
a temperature of less than 400.degree. C. is not economical and
practical, because the aforesaid phase change will proceed slowly
and much time will be needed to obtain satisfactory results. At
temperatures over 600.degree. C., on the other hand, the kappa
phase will grow or the beta phase will appear, bringing about no
improvement in machinability. From a practical viewpoint,
therefore, it is contemplated that the heat treatment be performed
for 30 minutes to 5 hours at 400.degree. C. to 600.degree. C.
BRIEF DESCRIPTION OF THE DRAWING
[0055] FIG. 1 shows perspective views of cuttings formed in cutting
a round bar of copper alloy by lathe.
DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS
EXAMPLE 1
[0056] As the first series of examples of the present invention,
cylindrical ingots with compositions given in Tables 1 to 29, each
100 mm in outside diameter and 150 mm in length, were hot extruded
into a round bar 15 mm in outside diameter at 750.degree. C. to
produce the following test pieces:
[0057] first invention alloys Nos. 1001 to 1005, second invention
alloys Nos. 2001 to 2008, third invention alloys Nos. 3001 to 3012,
fourth invention alloys Nos. 4001 to 4035, fifth invention alloys
Nos. 5001 to 5020, sixth invention alloys Nos. 6001 to 6105,
seventh invention alloys Nos. 7001 to 7030, eighth invention alloys
Nos. 8001 to 8147, ninth invention alloys Nos. 9001 to 9005, tenth
invention alloys Nos. 10001 to 10008, eleventh invention alloys
Nos. 11001 to 11007, and twelfth invention alloys Nos. 12001 to
12021.
[0058] Also, cylindrical ingots with the compositions given in
Table 30, each 100 mm in outside diameter and 150 mm in length,
were hot extruded into a round bar 15 mm in outside diameter at
750.degree. C. to produce the following test pieces: thirteenth
invention alloys Nos. 13001 to 13006. That is, No. 13001 is an
alloy test piece obtained by heat-treating an extruded test piece
with the same composition as first invention alloy No. 1005 for 30
minutes at 580.degree. C. No. 13002 is an alloy test piece obtained
by heat-treating an extruded test piece with the same composition
as No. 13001 for two hours at 450.degree. C. No. 13003 is an alloy
test piece obtained by heat-treating an extruded test piece with
the same composition as first invention alloy No. 1007 under the
same conditions as for No. 13001--for 30 minutes at 580.degree. C.
No. 13004 is an alloy test piece obtained by heat-treating an
extruded test piece with the same composition as No. 13007 under
the same conditions as for 13002--for two hours at 450.degree. C.
No. 13005 is an alloy test piece obtained by heat-treating an
extruded test piece with the same composition as first invention
alloy No. 1008 under the same conditions as for No. 13001--for 30
minutes at 580.degree. C. No. 13006 is an alloy test piece obtained
by heat-treating an extruded test piece with the same composition
as No. 1008 and heat-treated under the same conditions as for
13002--for two hours at 450.degree. C.
[0059] As comparative examples from the prior art, cylindrical
ingots with the compositions as shown in Table 31, each 100 mm in
outside diameter and 150 mm in length, were hot extruded into a
round bar 15 mm in outside diameter at 750.degree. C. to obtain the
following round extruded test pieces: Nos. 14001 to 14006
(hereinafter referred to as the "conventional alloys"). No. 14001
corresponds to the alloy JIS C 3604, No.14002 to the alloy CDA C
36000, No. 14003 to the alloy JIS C 3771, and No. 14004 to the
alloy CDA C 69800. No. 14005 corresponds to the alloy JIS C 6191.
This aluminum bronze is the most excellent of those expanded copper
alloys having a JIS designation with regard to strength and wear
resistance.
[0060] To study the machinability of the first to thirteenth
invention alloys in comparison with the conventional alloys,
cutting tests were carried out. In the cutting tests, evaluations
were made on the basis of cutting force, condition of chips, and
cut surface condition.
[0061] The tests were conducted in this way: The extruded test
pieces obtained as described above were cut on the circumferential
surface by a lathe mounted with a point noise straight tool at a
rake angle of -8 degrees and at a cutting rate of 50 meters/minute,
a cutting depth of 1.5 mm, a feed of 0.11 mm/rev. Signals from a
three-component dynamometer mounted on the tool were converted into
electric voltage signals and recorded on a recorder. From the
signals were then calculated the cutting resistance. It is noted
that while, to be perfectly exact, an amount of cutting resistance
should be judged by three component forces--cutting force, feed
force, and thrust force, the judgment was made on the basis of the
cutting force (N) of the three component forces in the present
example. The results are shown in Table 32 to Table 58.
[0062] Furthermore, the chips from the cutting work were examined
and classified into four forms (A) to (D) as shown in FIG. 1. The
results are enumerated in Table 32 to Table 58. In this regard, the
chips in the form of a spiral with three or more windings as (D) in
FIG. 1 are difficult to process, that is, recover or recycle, and
could cause trouble in cutting work as, for example, getting
tangled with the tool and damaging the cut metal surface. Chips in
the form of an arc with a half winding to a spiral with about two
windings as shown in (C), FIG. 1 do not cause such serious trouble
as the chips in the form of a spiral with three or more windings
yet are not easy to remove and could get tangled with the tool or
damage the cut metal surface. In contrast, chips in the form of a
fine needle as (A) in FIG. 1 or in the form of an arc as (B) will
not present such problems as mentioned above and are not bulky as
the chips in (C) and (D) and easy to process. But fine chips as (A)
still could creep into the sliding surfaces of a machine tool such
as a lathe and cause mechanical trouble, or could be dangerous
because they could stick into the worker's finger, eye, or other
body parts. Taking these factors into account, it is appropriate to
consider that the chips in (B) are the best, and the second best is
the chips in (A). Those in (C) and (D) are not good. In Table 32 to
Table 58, the chips judged to be as shown in (B), (A), (C), and (D)
are indicated by the symbols "{circle over (o)}", "o", ".DELTA.",
and "x", respectively.
[0063] In addition, the surface condition of the cut metal surface
was checked after cutting work. The results are shown in Table 32
to Table58. In this regard, the commonly used basis for indication
of the surface roughness is the maximum roughness (Rmax). While
requirements are different depending on the application field of
brass articles, the alloys with Rmax<10 microns are generally
considered excellent in machinability. The alloys with 10
microns.ltoreq.Rmax.ltoreq.15 microns are judged as industrially
acceptable, while those with Rmax.gtoreq.15 microns are taken as
poor in machinability. In Table 32 to Table 57, the alloys with
Rmax.ltoreq.10 microns are marked "o", those with 10
microns.ltoreq.Rmax.ltoreq.15 microns are indicated in ".DELTA."
and those with Rmax.gtoreq.15 microns are represented by a symbol
"x".
[0064] As is evident from the results of the cutting tests shown in
Table 32 to Table 58, the following invention alloys are all equal
to the conventional lead-contained alloys Nos. 14001 to 14003 of
the prior art in machinability: first invention alloys Nos. 1001 to
1008, second invention alloys Nos. 2001 to 2008, third invention
alloys Nos. 3001 to 3012, fourth invention alloys Nos. 4001 to
4035, fifth invention alloys Nos. 5001 to 5020, sixth invention
alloys Nos. 6001 to 6105, seventh invention alloys Nos. 7001 to
7030, eighth invention alloys Nos. 8001 to 8147, ninth invention
alloys Nos. 9001 to 9005, tenth invention alloys Nos. 10001 to
10008, eleventh invention alloys Nos. 11001 to 11007, and twelfth
invention alloys Nos. 12001 to 12021. Especially with regard to
formation of the chips, those invention alloys are favorably
compared not only with the conventional alloys Nos. 14004 to 14005
with a lead content of not higher than 0.1 percent by weight but
also with Nos. 14001 to 14003 which contain large quantities of
lead.
[0065] Also to be noted is that, as is clear from Tables Nos. 32 to
57, thirteenth invention alloys Nos. 13001 to 13006 are improved
over first invention alloys No. 1005 and No. 1007--with the same
composition as the thirteenth invention alloys--in machinability.
It is thus confirmed that a proper heat treatment can further
enhance machinability in accordance with the present invention.
[0066] In another series of tests, the first to thirteenth
invention alloys were examined in comparison with the conventional
alloys in hot workability and mechanical properties. For this
purpose, hot compression and tensile tests were conducted the
following way.
[0067] First, two test pieces--first and second test pieces--in the
same shape, 15 mm in outside diameter and 25 mm in length, were cut
out of each extruded test piece obtained as described above. In the
hot compression tests, the first test piece was held for 30 minutes
at 700.degree. C., and then compressed 70 percent in the direction
of axis to reduce the length from 25 mm to 7.5 mm. The surface
condition after the compression (700.degree. C. deformability) was
visually evaluated. The results are given in Table 32 through Table
58. The evaluation of deformability was made by visually checking
for cracks on the side of the test piece. In Table 32-Table 58, the
test pieces with no cracks found are marked "o", those with small
cracks are indicated by ".DELTA.", and those with large cracks are
represented by a symbol "x". The second test pieces were subjected
to tensile testing by conventional testing procedures to determine
their tensile strength, in N/mm.sup.2, and their elongation, in
%.
[0068] As the test results of the hot compression and tensile tests
in Table 32 through Table 58 indicate, it was confirmed that the
first to thirteenth invention alloys are equal to or superior to
the conventional alloys Nos. 14001 to 14004 and No. 14006 in hot
workability and mechanical properties and are suitable for
industrial use. The seventh and eighth invention alloys in
particular have the same level of mechanical properties as the
conventional alloy No. 14005, the aluminum bronze alloy which is
highest in strength of the expanded copper alloys having JIS
designations. Thus, the seventh and eighth invention alloys are
characterized by prominent high strength features.
[0069] Furthermore, the first to six and ninth to thirteenth
invention alloys were subjected to dezincing corrosion and stress
corrosion cracking tests in accordance with the test methods
detailed in ISO 6509 and JIS H 3250, respectively, in order to
examine their corrosion resistance and resistance to stress
corrosion cracking in comparison with the conventional alloys.
[0070] In the dezincification corrosion test conducted according to
the ISO 6509 method, a sample taken from each extruded test piece
was imbedded in a phenolic resin material in such a way that part
of the side surface of the sample is exposed, the exposed surface
being perpendicular to the extrusion direction of the extruded test
piece. The surface of the sample was polished with emery paper No.
1200, and then ultrasonic-washed in pure water and dried. The
sample thus prepared was dipped in a 12.7 g/l aqueous solution of
cupric chloride dehydrate (CuCl.sub.2.multidot.2 H.sub.2O) 1.0% and
left standing for 24 hours at 75.degree. C. The sample was taken
out of the aqueous solution and the maximum depth of
dezincification corrosion was determined. The measurements of the
maximum dezincification corrosion depth are given in Table 32 to
Table 43 and Table 53 to Table 58.
[0071] As is clear from the results of dezincification corrosion
tests shown in Table 32 to Table 43 and Table 53 to Table 58, the
first to fourth invention alloys and the ninth to thirteenth
invention alloys are excellent in corrosion resistance and compare
favorably to the conventional alloys of the prior art Nos. 14001 to
14003 containing great amounts of lead. Also it was confirmed that
especially the fifth and sixth invention alloys, which seek
improvement in both machinability and corrosion resistance, are
very high in corrosion resistance.
[0072] In stress corrosion cracking tests conducted in accordance
with the test method described in JIS H 3250, a 150-mm-long sample
was cut out from each extruded test piece. The sample was bent with
its center placed on an arc-shaped tester with a radius of 40 mm in
such a way that one end and the other end form an angle of 45
degrees. The test sample thus subjected to a tensile residual
stress was degreased and dried, and then placed in an ammonia
environment in the desiccator with a 12.5% aqueous ammonia (ammonia
diluted in the equivalent of pure water). The test sample was held
some 80 mm above the surface of aqueous ammonia in the desiccator.
After the test sample was left standing in the ammonia environment
for periods of two hours, 8 hours, and 24 hours, the test sample
was taken out from the desiccator, washed in sulfuric acid solution
10%, and examined for cracks under a magnifier of 10
magnifications. The results are given in Table 32 to Table 43 and
Table 53 to Table 58. In those tables, the alloys which have
developed clear cracks when held in the ammonia environment for two
hours are marked "xx" The test samples which had no cracks after
two hours but were found to be clearly cracked at 8 hours are
indicated by "x." The test samples which had no cracks at 8 hours,
but were found to have clear cracks at 24 hours were indicated by
".DELTA.". The test samples which were found to have no cracks at
all at 24 hours are identified by the symbol "o."
[0073] As is indicated by the results of the stress corrosion
cracking tests reported in Table 32 to Table 43 and Table 53 to
Table 58, it was confirmed that not only the fifth and sixth
invention alloys which seek improvement in both machinability and
corrosion resistance but also the first to fourth invention alloys
and the ninth and thirteenth alloys in which nothing particular was
done to improve corrosion resistance were both equal to
conventional alloy No. 14005, an aluminum bronze alloy containing
no zinc, in stress corrosion cracking resistance.
[0074] In addition, oxidation tests were carried out to study the
high-temperature oxidation resistance of the ninth to twelfth
invention alloys in comparison with the conventional alloys. A test
piece in the shape of a round bar with the surface cut to a outside
diameter of 14 mm and the length cut to 30 mm was prepared from
each of the following extruded test pieces: No. 9001 to No. 9005,
No. 10001 to No. 10008, No.11001 to No. 11007, No. 12001 to No.
12021, and No. 14001 to No. 14005. Each test piece was then weighed
to measure the weight before oxidation. After that, the test piece
was placed in a porcelain crucible and held in an electric furnace
maintained at 500.degree. C. After the passage of 100 hours, the
test piece was taken out of the electric furnace and was weighed to
measure the weight after oxidation. The increase in weight by
oxidation was calculated from the measurements before and after
oxidation. It is understood that the increase due to oxidation is
an amount, in mg, of increase in weight by oxidation per 10
cm.sup.2 of the surface area of the test piece and is calculated by
the equation: increase in weight by oxidation, mg/10
cm.sup.2=(weight, mg, after oxidation-weight, mg, before oxidation)
x (10 cm.sup.2/surface area, in cm.sup.2, of test piece). The
weight of each test piece increased after oxidation. This increase
was brought about by high-temperature oxidation. When subjected to
a high temperature, oxygen combines with copper, zinc, and silicon
to form Cu.sub.2O, ZnO, SiO.sub.2, respectively. Thus, an increase
of oxygen contributes to the weight gain. It can be said,
therefore, that the smaller in weight increase by oxidation of the
alloy, the more excellent in high-temperature oxidation resistance.
The results obtained are shown in Table 53 to Table 56 and Table
58.
[0075] As is evident from the test results shown in Table 53 to
Table 56 and Table 58, the ninth to twelfth invention alloys are
equal to conventional alloy No. 14005, an aluminum bronze alloy
ranking high in resistance to high-temperature oxidation among the
expanded copper alloys having JIS designations. Thus, it was
confirmed that the ninth to twelfth invention alloys are very
excellent in machinability and that they are resistant to high-
temperature oxidation as well.
EXAMPLE 2
[0076] As the second series of examples of the present invention,
cylindrical ingots with compositions given in Tables 13 to 25, each
100 mm in outside diameter and 200 mm in length, were hot extruded
into a round bar 35 mm in outside diameter at 700.degree. C. to
produce the following test pieces: seventh invention alloys Nos.
7001a to 7030a and eighth invention alloys Nos. 8001a to 8147a. In
parallel, cylindrical ingots with compositions given in Table 31,
each 100 mm in outside diameter and 200 mm in length, were hot
extruded into a round bar 35 mm in outside diameter at 700.degree.
C. to produce the following alloy test pieces: Nos. 14001a to
14005a, as second comparative examples from the prior art
(hereinafter referred to as the "conventional alloys"). It is noted
that the alloys Nos. 7001a to 7030a, Nos. 8001a to 8147a, and Nos.
14001a to 14005a are identical in composition with the aforesaid
copper alloys Nos. 7001 to 7030, Nos. 8001 to 8147, and Nos. 14001
to No. 14005, respectively.
[0077] These seventh invention alloys Nos. 7001a to 7030a and
eighth invention alloys Nos. 8001a to 8147a were put to wear
resistance tests in comparison with the conventional alloys Nos.
14001a to 14005a. The tests were carried out in the following
manner. Each extruded test piece thus obtained was cut on the
circumferential surface, holed, and cut down into a ring-shaped
test piece 32 mm in outside diameter and 10 mm in thickness (that
is, length in the axial direction). The test piece was then fitted
around a free-rotating shaft, and a roll 48 mm in outside diameter
placed in parallel with the axis of the shaft was urged against the
test piece under a load of 50 kg. The roll was made of stainless
steel having the JIS designation SUS 304. Then, the SUS 304 roll
and the test piece put in rotational sliding contact with the roll
were rotated at the same rate of revolutions/minute--209 r.p.m.--
with multipurpose gear oil dropping to the circumferential surface
of the test piece. When the number of revolutions reached 100,000,
the SUS 304 roll and the test piece were stopped, and the weight
difference between the start and the end of rotation, that is, the
loss of weight by wear, in mg, was determined. It can be said that
the alloys which show less loss of weight by wear are higher in
wear resistance. The results are given in Tables 59 to 68.
[0078] As is clear from the wear resistance test results shown in
Tables 59 to 68, these tests showed that seventh invention alloys
Nos. 7001a to 7030a and eighth invention alloys Nos. 8001a to 8147a
were excellent in wear resistance as compared with not only
conventional alloys Nos. 14001a to 14004a but also No. 14005a,
which is an aluminum bronze alloy characterized by the highest wear
resistance of the expanded copper alloys having JIS designations.
From comprehensive considerations of the test results including the
tensile test results, it may be concluded that the seventh and
eighth invention alloys are excellent in machinability and that
they also possess higher strength features and wear resistance than
does the aluminum bronze which is the highest in wear resistance of
all the expanded copper alloys listed in the JIS designations.
[0079] Alloy Composition Constraint Formula
[0080] Another feature of the copper alloys of the present
invention is that each copper alloy composition is constrained by
the general formula relationship
55.ltoreq.X-3Y+a.sub.0Z.sub.0.ltoreq.70 (1)
[0081] where X is the percent, by weight, of copper; Y is the
percent, by weight, of silicon; and a.sub.0Z.sub.0 represents the
contribution to the relationship of elements other than copper,
silicon and zinc. In other words, the relationship described by the
alloy composition constraint formula (1) is required to make copper
alloy compositions with the advantages described above. If formula
(1) is not satisfied, then by experiment it has been found that the
resulting copper alloy does not provide the degree of machinability
and other properties shown in Tables 32-57.
[0082] We describe the contribution to the relationship of
constraint formula (1) by elements other than copper, silicon and
zinc in formula (2) as follows:
a.sub.0Z.sub.0=a.sub.1Z.sub.1+a.sub.2Z.sub.2+a.sub.3Z.sub.3+. . .
(2)
[0083] where a.sub.1, a.sub.2, a.sub.3, etc., are experimentally
determined coefficients, and Z.sub.1, Z.sub.2, Z.sub.3 , etc., are
percents, by weight, of elements in the composition other than
copper, silicon and zinc.
[0084] Specifically, it has been determined that in order to
practice the copper alloys of the present invention, the "a"
coefficients are as follows: for bisthmuth, tellurium, selenium,
antimony, arsenic and titanium, the a coefficient is zero; for tin,
the a coefficient is -0.5; for aluminum, the a coefficient is -2;
for phosphorus, the a coefficient is -3; for chromium, the a
coefficient is +2; and for manganese and nickel, the a coefficient
is +2.5. It will be appreciated by one skilled in the art, that
formula (1) does not directly constrain the amounts of bismuth,
tellurium, selenium, antimony, arsenic and titanium in the copper
alloys of the present invention because the a coefficient is zero
for these elements; however, these elements are indirectly
constrained by the fact that the percent, by weight, of copper,
silicon, and those elements in the copper alloy and having non-zero
a coefficients must satisfy constraint formula (1).
[0085] To be even more specific, for the first and second invention
alloys, constraint formula (1) can be written as:
55.ltoreq.X-3Y.ltoreq.c70, (3)
[0086] where X is the percent, by weight, of copper; and Y is the
percent, by weight, of silicon in the alloy.
[0087] For the third, fourth, fifth and sixth invention alloys,
constraint formula (1) can be written as:
55.ltoreq.X-3Y+aZ+bW.ltoreq.70, (4)
[0088] where X is the percent, by weight, of copper; Y is the
percent, by weight, of silicon; Z is the percent, by weight of tin;
W is the percent, by weight, of phosphorus in the alloy; a is -0.5;
and b is -3.
[0089] For the nineth and eleventh invention alloys, constraint
formula (1) can be written as:
55.ltoreq.X-3Y+aZ+bW.ltoreq.70, (5)
[0090] where X is the percent, by weight, of copper; Y is the
percent, by weight, of silicon; Z is the percent, by weight of
aluminum; W is the percent, by weight, of phosphorus in the alloy;
a is -2; and b is -3.
[0091] For the tenth and twelfth invention alloys, constraint
formula (1) can be written as:
55.ltoreq.X-3Y+aZ+bW+cV.ltoreq.70, (6)
[0092] where X is the percent, by weight, of copper; Y is the
percent, by weight, of silicon; Z is the percent, by weight of
aluminum; W is the percent, by weight, of phosphorus; V is the
percent, by weight, of chromium in the alloy; a is -2; b is -3; and
c is +2.
[0093] For the seventh and eighth invention alloys constraint
formula (1) can be written as:
55.ltoreq.X-3Y+aZ+bW+cV+dU.ltoreq.70, (7)
[0094] where X is the percent, by weight, of copper; Y is the
percent, by weight, of silicon; Z is the percent, by weight of tin;
W is the percent, by weight, of phosphorus; V is the percent, by
weight, of manganese; U is the percent, by weight, of nickel; a is
-0.5; b is -3; c is +2.5; and d is +2.5. It has also been
determined for the seventh and eighth invention alloys that a
secondary alloy composition constraint is necessary to practice the
invention. This secondary alloy composition constraint formula is a
ratio involving silicon, manganese and nickel describing the
constraining composition as follows:
0.7.ltoreq.Y/(V+U).ltoreq.6, (8)
[0095] where Y, V and U are the percents, by weight, of silicon,
manganese, and nickel respectively.
[0096] To summarize, all of the first through the twelfth invention
alloys of the present invention must satisfy the alloy composition
constraint of Formula 1, and all of the illustrative examples in
Tables 1-29 comply with this composition constraint. Only the
seventh and eighth invention alloys are further constrained by the
secondary alloy composition constraint of Formula 8. Other copper
alloys that contain the same elements as the copper alloys of the
present invention, but which do not have a composition satisfying
the requirements of Formula 1, and when appropriate Formula 8 as
well, will not have the characteristics of the copper alloys
disclosed in Tables 1-29.
[0097] In addition, it is emphasized that the desired metallurgic
characteristics of the copper metal alloys of the present invention
are present when constraint formula 1 has an upper limit of 70 and
a lower limit of 55; however, the preferred range includes the
upper limit of 70 and a lower limit of 60. In other words, the the
preferred relationship is 60.ltoreq.X-3Y+a.sub.0Z.sub.0.ltoreq.70,
although the relationship 55.ltoreq.X-3Y+a.sub.0Z.sub.0.ltoreq.70
still produces lead free copper alloys having suitable metallurgic
characteristics such as excellent strength and wear resistance.
This is because copper alloys satisfying formula 1 in the range 55
.ltoreq.X-3Y+a.sub.0Z.sub.0<60 have acceptable machinability,
but due to an increase in the .beta. phase of the metal matrix as
is discussed in detail below, the copper alloys in this range have
less corrosion resistance and less impact strength than copper
alloys in the range 60.ltoreq.X-3Y+a.sub.0Z.sub.0.ltoreq.70.
Consequently, to produce copper alloys in accordance with the
present invention, the composition of the alloy must satisfy the
relationship 60.ltoreq.X-3Y+a.sub.0Z.sub.0.ltoreq.70 if superior
ductility and impact resistance are also desired.
[0098] Metal Construction
[0099] Another important feature of the copper alloys of the
present invention is the metal construction, being the matrix of
the metal, formed by the integration of multiple phase states of
the component metals, which produces a composite phase for the
copper alloy. Specifically, as one skilled in the art will
appreciate, a given metal alloy may have different characteristics
depending upon the environment in which it was produced. For
example, applying heat to temper steel is well known. The fact that
a given metal alloy may behave differently depending upon the
conditions in which it was forged is due to the integration and
conversion of components of the metal to different phase states. As
is illustrated in Tables 1-30, the copper alloys of the present
invention all include an .alpha. phase of about 30 percent or more
of the total phase area to practice the invention. This is because
the .alpha. phase is a soft phase and is the only phase that gives
metal alloys a degree of cold workability. In other words, if the
copper alloy has less than about 30% a phase comprising the total
phase area of the metal, then the copper alloy is not cold workable
and can not be further processed by cutting in any practical
manner. Therefore, all of the copper alloys of the present
invention have a metal construction that is a composite phase that
is an .alpha. phase matrix to which other phases are provided. The
presence of a sufficient percentage, relative to the total phase
area of the metal construction, of the .alpha. phase improves the
machinability of the copper alloy even without the presence of lead
in the composition of the alloy.
[0100] As mentioned above, the presence of silicon in the copper
alloys of the present invention is to improve the machinability of
the copper alloy, and this occurs partly because silicon induces a
.gamma. phase. Silicon concentrations in any one of the .gamma.,
.kappa., and .mu. phases of a copper alloy are 1.5 to 3.5 times as
high as that in the .alpha. phase. Silicon concentrations in the
various phases, from high to low, are as follows:
.mu..gtoreq..gamma..gtoreq..kappa..gtoreq..beta..gto- req..alpha..
The .gamma., .kappa., and .mu. phases also share the characteristic
that they are harder and more brittle than the .alpha. phase, and
impart an appropriate hardness to the alloy so that the alloy is
machinable and so that the cuttings formed by machining are less
likely to damage the cutting tools as describe regarding FIG. 1.
Therefore, to practice the invention, each copper alloy must have
at least one of the .gamma. phase, the .kappa. phase, and the .mu.
phase, or any combination of these phases, in the .alpha. phase in
order to provide a suitable degree of hardness to the copper
alloy.
[0101] Another goal of the copper alloys of the present invention
is to limit the amount of .beta. phase in the a matrix of the metal
construction. It is desired to limit the .beta. phase to 5% or less
of the total phase area because the .beta. phase does not
contribute to either the machinability or the cold workability of
the copper alloy. Preferably, the .beta. phase is zero in the metal
construction of the present invention, but it is acceptable to have
the .beta. phase contribute up to 5% of the total phase area.
[0102] Therefore, the copper alloys of the present invention, as
illustrated in Tables 1-30, are constrained to a metal construction
as follows: (1) an .alpha. phase matrix of about 30% or more; (2) a
.beta. phase of 5% or less; and consequently (3) any combination of
the .gamma. phase, the .kappa. phase, and the .mu. phase totaling
between 5-70% of the total phase area.
[0103] In other words, the forging conditions described above and
in the tables in combination with the elemental composition of the
copper alloys of the present invention are constrained so that any
one of: (a) .alpha.+.gamma.+.kappa.+.mu. phases
(5%.ltoreq..gamma.+.kappa.+.mu..ltore- q.70%), (b)
.alpha.+.gamma.+.kappa. phases (5%.ltoreq..gamma.+.kappa.+.mu.-
.ltoreq.70%), (c) .alpha.+.gamma.+.mu. phases
(5%.ltoreq..gamma.+.mu..ltor- eq.70%), (d) .alpha.+.kappa.+.mu.
phases (5%.ltoreq..kappa.+.mu..ltoreq.70- %), (e) .alpha.+.gamma.
phases (5%.ltoreq..gamma..ltoreq.70%), (f) .alpha.+.kappa. phases
(5%.ltoreq..kappa..ltoreq.70%), and (g) .alpha.+.mu. phases
(5%.ltoreq..mu..ltoreq.70%), are acceptable composite phases
forming the metal construction subject to the caveat that the metal
construction includes no more than 5% of the .beta. phase.
[0104] Lastly, it is pointed out that although metal constructions
are possible where the .gamma., .kappa., and .mu. phases may make
up more than 70% of the total phase area, the result is a copper
alloy that has no problem with machinability, but has an .alpha.
phase matrix of less than 30% which results in such a poor degree
of cold workability as to render the alloy of no practical value.
On the other hand, if the copper has less than 5% of the total
phase area comprised of the .gamma., .kappa., and .mu. phases then
the machinability of the copper alloy is rendered unsatisfactory.
The .beta. phase is minimized to less than 5% of the total phase
area because the .beta. phase does not contribute to either the
machinability or cold workability of the copper alloy. In addition,
because the .alpha. phase is the soft phase for the metal
construction, and therefore has ductility, the machinability of the
copper alloy is excellent even in the absence of lead. The result
is that the metal construction of the present invention utilizes
the .alpha. phase as the matrix in which the .gamma., .kappa., and
.mu. phases disperse.
[0105] Lastly, in light of the above discussion and Tables 32-57
and 59-67, which showcase the various advantages of the lead free
copper alloys of the present invention when compared to the
metallurgic characteristics of the prior art conventional alloys
illustrated in Tables 58 and 68, several aspects of the present
invention are highlighted. Specifically, with respect to the first
and second invention alloys the silicon percentage, by weight, is
set at greater than 3 weight percent (wt %) to maintain the
excellent corrosion resistance; however, in the copper metal alloys
of the present invention that include tin and phosphorous, such as
for the third and fourth invention alloys, the weight percent of
silicon is less critical because the tin and phosphorous provide
the corrosion resistance.
[0106] It is additionally pointed out that the third and fourth
invention alloys do not contain aluminum because these alloys are
produced to have excellent corrosion resistance (also known as
"dezincification resistance") as well as excellent strength and
machinability. In fact, the strength and machinability of the third
and fourth invention alloys is comparable to the strength and
machinability of the first and second invention alloys. These
metallurgical characteristics are achieved by the presence of tin
and phosphorous in the composition of the third and fourth
invention alloys, but the addition of aluminum would defeat the
benefits provided by the tin and phosphorous.
[0107] Likewise, the seventh and eighth invention alloys do not
contain aluminum. The goal of the compositions of the seventh and
eighth invention alloys is to improve the strength and wear
resistance of the copper alloy relative to the strength and wear
resistances of the third and fourth invention alloys. However, in
order to retain the excellent dezincification resistance as is seen
in the third and fourth invention alloys it is necessary to include
at least one of tin or phosphorous in the compositions of the
seventh and eighth invention alloys and to exclude the presence of
aluminum.
[0108] While the present invention has been described with
reference to certain preferred embodiments, one of ordinary skill
in the art will recognize that additions, deletions, substitutions,
modifications and improvements can be made while remaining within
the spirit and scope of the present invention as defined by the
appended claims.
1 TABLE 1 alloy composition (wt %) metal construction No. Cu Si Zn
phases .gamma. + .kappa. + .mu. (%) 1001 72.8 3.1 remainder .alpha.
+ .beta. + .gamma. 30 1002 76.5 3.4 remainder .alpha. + .kappa. +
.mu. 50 1003 74.8 3.1 remainder .alpha. + .gamma. + .kappa. 30 1004
77.6 3.7 remainder .alpha. + .kappa. + .mu. 65 1005 78.5 3.2
remainder .alpha. + .kappa. + .mu. 40
[0109]
2 TABLE 2 metal construction .gamma. + alloy composition (wt %)
.kappa. + No. Cu Si Bi Te Se Zn phases .mu. (%) 2001 75.2 3.2 0.19
remainder .alpha. + .gamma. + .kappa. 40 2002 72.6 3.1 0.25
remainder .alpha. + .beta. + .gamma. 30 2003 77.6 3.8 0.05 0.09
remainder .alpha. + .kappa. + .mu. 65 2004 75.8 3.5 0.11 0.05
remainder .alpha. + .kappa. + .mu. 55 2005 76.4 3.4 0.03 0.05 0.11
remainder .alpha. + .kappa. + .mu. 50 2006 78.2 3.4 0.14 0.03
remainder .alpha. + .kappa. 50 2008 78.2 3.7 0.33 remainder .alpha.
+ .kappa. + .mu. 65
[0110]
3 TABLE 3 metal construction .gamma. + alloy composition (wt %)
.kappa. + No. Cu Si Sn P Zn phases .mu. (%) 3001 71.8 2.4 3.1
remainder .alpha. + .beta. + .gamma. 35 3004 74.9 3.2 0.09
remainder .alpha. + .gamma. + .kappa. 40 3005 71.6 2.4 2.3 0.03
remainder .alpha. + .beta. + .gamma. 30 3008 77.5 3.5 0.4 remainder
.alpha. + .gamma. + .kappa. + .mu. 60 3009 75.4 3 1.7 remainder
.alpha. + .beta. + .gamma. + .kappa. 40 3010 76.5 3.3 0.21
remainder .alpha. + .gamma. + .kappa. 50 3011 73.8 2.7 0.04
remainder .alpha. + .gamma. + .kappa. 20 3012 75 2.9 1.6 0.1
remainder .alpha. + .gamma. + .kappa. 40
[0111]
4 TABLE 4 alloy composition (wt %) metal construction No. Cu Si Sn
Bi Te Se Zn phases .gamma. + .kappa. + .mu. (%) 4001 70.8 1.9 3.4
0.36 remainder .alpha. + .beta. + .gamma. 30 4002 76.3 3.4 1.3 0.03
remainder .alpha. + .gamma. + .kappa. 60 4003 73.2 2.5 1.9 0.15
remainder .alpha. + .beta. + .gamma. 30 4004 72.3 2.4 0.6 0.29 0.23
remainder .alpha. + .gamma. 25 4005 74.2 2.7 2 0.03 0.26 remainder
.alpha. + .gamma. + .kappa. 35 4006 75.4 2.9 0.4 0.31 0.03
remainder .alpha. + .gamma. + .kappa. 30 4007 71.5 2.1 2.6 0.11
0.05 0.23 remainder .alpha. + .beta. + .gamma. 30
[0112]
5 TABLE 5 alloy composition (wt %) metal construction No. Cu Si Sn
Bi Te Se P Zn phases .gamma. + .kappa. + .mu. (%) 4022 70.9 2.1
0.11 0.11 remainder .alpha. + .beta. + .gamma. 10 4023 74.8 3.1
0.07 0.06 remainder .alpha. + .gamma. + .kappa. 30 4024 76.3 3.2
0.05 0.02 remainder .alpha. + .gamma. + .kappa. 35 4025 78.1 3.1
0.26 0.02 0.15 remainder .alpha. + .kappa. 35 4026 71.1 2.2 0.13
0.02 0.05 remainder .alpha. + .beta. + .gamma. 10 4027 74.1 2.7
0.03 0.06 0.03 0.03 remainder .alpha. + .gamma. + .kappa. 20 4028
70.6 1.9 3.2 0.31 0.04 remainder .alpha. + .beta. + .gamma. 30 4029
73.6 2.4 2.3 0.03 0.04 remainder .alpha. + .beta. + .gamma. 35 4030
73.4 2.6 1.7 0.31 0.22 remainder .alpha. + .beta. + .gamma. +
.kappa. 35 4031 74.8 2.9 0.5 0.03 0.02 0.05 remainder .alpha. +
.gamma. + .kappa. 30 4032 73 2.6 0.7 0.09 0.02 0.08 remainder
.alpha. + .gamma. 25 4033 74.5 2.8 0.03 0.12 0.05 remainder .alpha.
+ .gamma. + .kappa. 25 4034 77.2 3.3 1.3 0.03 0.12 0.04 remainder
.alpha. + .gamma. + .kappa. 50 4035 74.9 3.1 0.4 0.02 0.05 0.05
0.08 remainder .alpha. + .gamma. + .kappa. 35
[0113]
6 TABLE 6 alloy composition (wt %) metal construction No. Cu Si Sn
P Sb As Zn phases .gamma. + .kappa. + .mu. (%) 5001 69.9 2.1 3.3
remainder .alpha. + .beta. + .gamma. 30 5002 74.1 2.7 0.21
remainder .alpha. + .gamma. + .kappa. 20 5003 75.8 2.4 0.14
remainder .alpha. + .kappa. + .mu. 15 5004 77.3 3.4 0.05 remainder
.alpha. + .kappa. + .mu. 45 5005 73.4 2.4 2.1 0.04 remainder
.alpha. + .gamma. 35 5006 75.3 2.7 0.4 0.04 remainder .alpha. +
.kappa. 25 5007 70.9 2.2 2.4 0.07 remainder .alpha. + .beta. +
.gamma. 30 5008 71.2 2.6 1.1 0.03 0.03 remainder .alpha. + .beta. +
.gamma. 30 5009 77.3 2.9 0.7 0.19 0.03 remainder .alpha. + .kappa.
+ .mu. 35 5010 78.2 3.1 0.4 0.09 0.15 remainder .alpha. + .kappa.
40 5011 72.5 2.1 2.8 0.02 0.1 0.03 remainder .alpha. + .beta. +
.gamma. 35 5012 79 3.3 0.24 0.02 remainder .alpha. + .kappa. + .mu.
45 5013 75.6 2.9 0.07 0.14 remainder .alpha. + .kappa. 25 5014 74.8
3 0.11 0.02 remainder .alpha. + .gamma. + .kappa. 30 5015 74.3 2.8
0.06 0.02 0.03 remainder .alpha. + .gamma. + .kappa. 20 5016 72.9
2.5 0.03 remainder .alpha. + .gamma. 20 5017 77 3.4 0.14 remainder
.alpha. + .kappa. + .mu. 50 5018 76.8 3.2 0.7 0.12 remainder
.alpha. + .gamma. + .kappa. 45 5019 74.5 2.8 1.8 remainder .alpha.
+ .gamma. + .kappa. 40 5020 74.9 3 0.2 0.05 remainder .alpha. +
.gamma. + .kappa. 30
[0114]
7 TABLE 7 alloy composition (wt %) metal construction No. Cu Si Sn
Bi Te P Sb As Zn phases .gamma. + .kappa. + .mu. (%) 6001 69.6 2.1
3.2 0.15 remainder .alpha. + .beta. + .gamma. 30 6002 77.3 3.7 0.5
0.02 0.23 remainder .alpha. + .kappa. + .mu. 65 6003 75.2 2.4 1.1
0.33 0.12 remainder .alpha. + .gamma. 25 6004 70.9 2.3 3.1 0.11
0.03 remainder .alpha. + .beta. + .gamma. 30 6005 78.1 2.7 0.6 0.14
0.02 0.07 remainder .alpha. + .kappa. + .mu. 30 6006 74.5 2.6 1.5
0.21 0.1 0.04 remainder .alpha. + .gamma. + .kappa. 35 6007 74.7
3.2 2.1 0.05 0.02 0.12 remainder .alpha. + .beta. + .gamma. 45 6008
73.8 2.5 0.7 0.31 0.03 0.02 0.1 remainder .alpha. + .gamma. 25 6009
74.5 2.9 0.05 0.19 remainder .alpha. + .gamma. + .kappa. 25 6010
78.1 3.1 0.11 0.15 remainder .alpha. + .kappa. + .mu. 45 6011 74.6
3.3 0.02 0.22 remainder .alpha. + .gamma. 45 6012 69.9 2.3 0.35
0.08 0.02 remainder .alpha. + .beta. + .gamma. 15 6013 73.2 2.6
0.21 0.03 0.07 remainder .alpha. + .gamma. + .kappa. 20 6014 76.3
2.9 0.07 0.09 0.02 remainder .alpha. + .gamma. + .kappa. 30 6015
74.4 2.8 0.19 0.13 0.03 0.02 remainder .alpha. + .gamma. + .kappa.
25 6016 70.5 2.3 2.9 0.1 0.02 remainder .alpha. + .beta. + .gamma.
30 6017 74.7 2.4 0.9 0.31 0.04 0.05 remainder .alpha. + .gamma. +
.kappa. 25 6018 78.1 3.8 0.6 0.02 0.33 0.07 remainder .alpha. +
.kappa. + .mu. 65 6019 69.4 2 3.4 0.11 0.03 0.03 remainder .alpha.
+ .beta. + .gamma. 20 6020 77.8 2.8 0.5 0.06 0.11 0.21 0.02
remainder .alpha. + .kappa. + .mu. 30
[0115]
8 TABLE 8 alloy composition (wt %) metal construction No. Cu Si Sn
Bi Te Se P Sb As Zn phases .gamma. + .kappa. + .mu. (%) 6021 74.2
2.6 0.6 0.2 0.03 0.02 0.14 remainder .alpha. + .gamma. + .kappa. 25
6022 75.8 3.3 1.8 0.03 0.06 0.11 0.02 remainder .alpha. + .beta. +
.gamma. + .kappa. 50 6023 74.3 2.6 1.5 0.09 0.12 0.03 0.02 0.06
remainder .alpha. + .beta. + .gamma. 35 6024 77.3 3.1 0.02 0.25
0.08 remainder .alpha. + .kappa. 35 6025 70.5 2.4 0.12 0.04 0.06
0.03 remainder .alpha. + .beta. + .gamma. 15 6026 74.3 2.9 0.24
0.02 0.13 0.11 remainder .alpha. + .gamma. + .kappa. 25 6027 69.8
2.3 0.34 0.03 0.21 0.02 0.02 remainder .alpha. + .beta. + .gamma.
10 6028 74.5 2.9 0.03 0.11 0.13 remainder .alpha. + .gamma. +
.kappa. 25 6029 78.4 3.2 0.02 0.08 0.04 0.05 remainder .alpha. +
.kappa. + .mu. 45 6030 73.8 3 0.08 0.31 0.23 remainder .alpha. +
.beta. + .gamma. 25 6031 72.8 2.5 1.6 0.11 0.36 remainder .alpha. +
.beta. + .gamma. 30 6032 78.1 3.7 0.5 0.03 0.02 0.05 remainder
.alpha. + .kappa. + .mu. 60 6033 77.2 2.8 0.6 0.09 0.04 0.07
remainder .alpha. + .kappa. 30 6034 76.9 3.8 0.4 0.03 0.06 0.07
remainder .alpha. + .gamma. + .kappa. 65 6035 74.1 2.3 3.3 0.06
0.03 0.02 0.05 remainder .alpha. + .beta. + .gamma. 40 6036 69.8 2
2.5 0.31 0.12 0.03 0.06 remainder .alpha. + .beta. + .gamma. 20
6037 74.9 3 1.1 0.07 0.21 0.12 0.02 remainder .alpha. + .gamma. 40
6038 72.6 2.8 0.6 0.02 0.05 0.21 0.07 0.03 remainder .alpha. +
.beta. + .gamma. 25 6039 69.7 2.3 0.23 0.06 0.1 remainder .alpha. +
.beta. + .gamma. 15 6040 75.4 3 0.02 0.09 0.11 0.03 remainder
.alpha. + .gamma. + .kappa. 30
[0116]
9 TABLE alloy composition (wt %) metal construction No. Cu Si Sn Bi
Te Se P Sb As Zn phases .gamma. + .kappa. + .mu. (%) 6041 73.2 2.5
0.11 0.36 0.05 0.02 remainder .alpha. + .gamma. 20 6042 78.2 3.7
0.03 0.04 0.03 0.04 0.1 remainder .alpha. + .kappa. + .mu. 65 6043
77.8 2.8 0.09 0.02 0.04 remainder .alpha. + .kappa. 30 6044 73.4
2.6 0.16 0.06 0.03 0.02 remainder .alpha. + .gamma. + .kappa. 20
6045 71.2 2.4 0.35 0.14 0.08 remainder .alpha. + .beta. + .gamma.
15 6046 70.3 2.5 1.9 0.09 0.05 0.03 remainder .alpha. + .beta. +
.gamma. 30 6047 74.5 3.6 2.2 0.02 0.2 0.04 0.04 remainder .alpha. +
.beta. + .gamma. 50 6048 73.8 2.9 1.2 0.03 0.1 0.05 0.12 remainder
.alpha. + .beta. + .gamma. 40 6049 69.8 2.1 3.1 0.32 0.03 0.05 0.13
remainder .alpha. + .beta. + .gamma. 25 6050 74.2 2.2 0.6 0.19 0.11
0.02 0.02 0.03 remainder .alpha. + .gamma. + .kappa. 20 6051 74.8
3.2 0.5 0.03 0.07 0.03 0.05 0.02 remainder .alpha. + .gamma. 40
6052 78 2.8 0.6 0.06 0.04 0.11 0.11 0.03 remainder .alpha. +
.kappa. 30 6053 76.3 2.4 0.8 0.05 0.03 0.22 0.03 0.04 0.03
remainder .alpha. + .kappa. + .mu. 25 6054 74.2 2.6 0.21 0.02 0.04
0.05 remainder .alpha. + .gamma. + .kappa. 20 6055 78.2 2.9 0.16
0.08 0.03 0.21 0.03 remainder .alpha. + .kappa. 25 6056 72.3 2.5
0.08 0.36 0.02 0.1 0.04 remainder .alpha. + .gamma. + .kappa. 20
6057 69.8 2.4 0.36 0.04 0.04 0.06 0.07 0.22 remainder .alpha. +
.beta. + .gamma. 15 6058 74.6 3.1 0.05 0.09 0.04 0.14 remainder
.alpha. + .gamma. + .kappa. 30 6059 73.8 2.5 0.08 0.05 0.03 0.02
0.04 remainder .alpha. + .gamma. + .kappa. 20 6060 74.9 2.7 0.03
0.16 0.02 0.03 remainder .alpha. + .gamma. + .kappa. 20
[0117]
10 TABLE 10 alloy composition (wt %) metal construction No. Cu Si
Sn Te Se P Sb As Zn phases .gamma. + .kappa. + .mu. (%) 6061 69.7
2.6 3.1 0.26 remainder .alpha. + .beta. + .gamma. 25 6062 74.2 3.2
0.6 0.03 0.04 remainder .alpha. + .gamma. 40 6063 74.9 2.6 0.7 0.14
0.14 remainder .alpha. + .gamma. + .kappa. 25 6064 73.8 3 0.4 0.07
0.13 remainder .alpha. + .gamma. 35 6065 78.1 3.3 0.8 0.02 0.12
0.02 remainder .alpha. + .gamma. + .kappa. 55 6066 72.8 2.4 1.2
0.32 0.03 0.05 remainder .alpha. + .beta. + .gamma. 25 6067 73.6
2.7 2.1 0.03 0.07 0.02 remainder .alpha. + .beta. + .gamma. 35 6068
72.3 2.6 0.5 0.16 0.02 0.04 0.03 remainder .alpha. + .beta. +
.gamma. 25 6069 70.6 2.3 0.33 0.09 remainder .alpha. + .beta. +
.gamma. 15 6070 76.5 3.2 0.14 0.21 0.03 remainder .alpha. + .gamma.
+ .kappa. 40 6071 74.5 3.1 0.05 0.03 0.03 remainder .alpha. +
.gamma. + .kappa. 35 6072 72.8 2.7 0.08 0.13 remainder .alpha. +
.gamma. + .kappa. 25 6073 78 3.8 0.04 0.02 0.12 remainder .alpha. +
.kappa. + .mu. 65 6074 73.8 2.9 0.2 0.1 remainder .alpha. + .gamma.
+ .kappa. 30 6075 74.5 2.9 0.07 0.04 0.1 0.02 remainder .alpha. +
.gamma. + .kappa. 25 6076 73.6 3.2 2.1 0.04 0.07 remainder .alpha.
+ .beta. + .gamma. 40 6077 74.1 2.5 0.8 0.21 0.18 0.05 remainder
.alpha. + .gamma. + .kappa. 25 6078 77.8 2.9 0.6 0.11 0.05 0.07
remainder .alpha. + .kappa. 35 6079 71.5 2.1 1.1 0.06 0.03 0.06
remainder .alpha. + .beta. + .gamma. 20 6080 72.6 2.3 0.5 0.15 0.23
0.11 0.02 remainder .alpha. + .beta. + .gamma. 25
[0118]
11 TABLE 1 alloy composition (wt %) metal construction No. Cu Si Sn
Te Se P Sb As Zn phases .gamma. + .kappa. + .mu. (%) 6081 74.2 3
0.5 0.03 0.03 0.2 0.02 remainder .alpha. + .gamma. 35 6082 70.6 2.2
2.6 0.32 0.05 0.13 0.03 remainder .alpha. + .beta. + .gamma. 30
6083 73.7 2.6 0.8 0.14 0.16 0.06 0.02 0.03 remainder .alpha. +
.gamma. + .kappa. 30 6084 74.5 3.1 0.04 0.04 0.05 remainder .alpha.
+ .gamma. + .kappa. 30 6085 72.8 2.7 0.09 0.21 0.04 0.02 remainder
.alpha. + .gamma. + .kappa. 20 6086 76.2 3.3 0.03 0.04 0.11 0.04
remainder .alpha. + .gamma. + .kappa. + .mu. 45 6087 73.8 2.7 0.11
0.03 0.02 0.04 0.03 remainder .alpha. + .gamma. + .kappa. 20 6088
74.9 2.9 0.05 0.31 0.05 remainder .alpha. + .gamma. + .kappa. 25
6089 75.8 2.8 0.08 0.04 0.03 0.14 remainder .alpha. + .kappa. 25
6090 73.6 2.4 0.27 0.1 0.06 remainder .alpha. + .gamma. + .kappa.
15 6091 72.4 2.2 3.2 0.33 remainder .alpha. + .beta. + .gamma. 35
6092 75 3.2 0.6 0.05 0.1 remainder .alpha. + .gamma. 45 6093 76.8
3.1 0.5 0.04 0.11 remainder .alpha. + .gamma. + .kappa. 55 6094
74.5 2.9 0.7 0.08 0.15 remainder .alpha. + .gamma. + .kappa. 35
6095 73.2 2.7 1.2 0.12 0.06 0.03 remainder .alpha. + .gamma. 30
6096 69.6 2.4 2.3 0.14 0.04 0.02 remainder .alpha. + .beta. +
.gamma. 30 6097 74.2 2.8 0.8 0.07 0.02 0.03 remainder .alpha. +
.gamma. 35 6098 74.4 2.9 0.8 0.06 0.03 0.03 0.03 remainder .alpha.
+ .gamma. 40 6099 74.8 3.1 0.09 0.04 remainder .alpha. + .gamma. +
.kappa. 30 6100 73.9 2.8 0.05 0.1 0.04 remainder .alpha. + .gamma.
+ .kappa. 25
[0119]
12 TABLE 12 alloy composition (wt %) metal construction No. Cu Si
Se P Sb As Zn phases .gamma. + .kappa. + .mu. (%) 6101 76.1 3 0.04
0.05 0.02 remainder .alpha. + .gamma. + .kappa. 30 6102 74.5 2.8
0.03 0.04 0.02 0.03 remainder .alpha. + .gamma. + .kappa. 25 6103
74.3 2.6 0.31 0.04 remainder .alpha. + .kappa. 20 6104 75 3.3 0.06
0.02 0.05 remainder .alpha. + .gamma. + .kappa. 45 6105 73.9 2.9
0.1 0.11 remainder .alpha. + .gamma. + .kappa. 25
[0120]
13 TABLE 13 metal construction alloy composition (wt %) .gamma. +
.kappa. + .mu. No. Cu Si Sn Mn Ni Zn phases (%) 7001 62.9 2.7 2.6
2.2 remainder .alpha. + .beta. + .gamma. 10 7001a 7002 64.8 3.4 1.8
3.1 remainder .alpha. + .beta. + .gamma. 20 7002a 7003 68.2 4.1 0.6
1.9 1.5 remainder .alpha. + .beta. + .gamma. 30 7003a
[0121]
14 TABLE 14 alloy composition (wt %) metal construction No. Cu Si
Sn P Mn Ni Zn phases .gamma. + .kappa. + .mu. (%) 7016 68.1 4 0.4
0.04 2.8 remainder .alpha. + .beta. + .gamma. 25 7016a 7017 63.8
2.6 2.7 0.19 0.9 remainder .alpha. + .beta. + .gamma. 20 7017a 7018
66.7 3.4 1.3 0.07 1.2 0.8 remainder .alpha. + .beta. + .gamma. 25
7018a 7019 67.2 3.6 0.21 1.9 remainder .alpha. + .beta. + .gamma.
15 7019a 7020 69.1 3.8 0.06 2.2 remainder .alpha. + .beta. +
.gamma. + .kappa. 25 7020a
[0122]
15 TABLE 15 alloy composition (wt %) metal construction No. Cu Si
Sn P Mn Ni Zn phase .gamma. + .kappa. + .mu. (%) 7021 72.1 4.3 0.07
2 0.8 remainder .alpha. + .gamma. + .kappa. 45 7021a 7030 68.4 4.2
2.6 3.3 remainder .alpha. + .beta. + .gamma. 35 7030a
[0123]
16 TABLE 16 alloy composition (wt %) metal construction No. Cu Si
Sn Bi Te Se Mn Zn phases .gamma. + .kappa. + .mu. (%) 8001 62.6 2.6
2.6 0.31 1.9 remainder .alpha. + .beta. + .gamma. 10 8001a 8002
65.3 3.4 1.8 0.11 0.02 2.5 remainder .alpha. + .beta. + .gamma. 20
8002a 8003 66.4 4.2 0.5 0.05 0.03 3.4 remainder .alpha. + .beta. +
.gamma. 35 8003a 8004 72.1 4.4 0.4 0.06 0.05 0.02 2.8 remainder
.alpha. + .beta. + .gamma. + .kappa. 45 8004a 8005 67.4 3.3 2.3
0.31 0.9 remainder .alpha. + .beta. + .gamma. 25 8005a 8006 63.8
2.8 2.9 0.06 0.07 2.1 remainder .alpha. + .beta. + .gamma. 15 8006a
8007 71.5 3.9 1.5 0.2 1.4 remainder .alpha. + .beta. + .gamma. 40
8007a
[0124]
17 TABLE 17 alloy composition (wt %) metal construction No. Cu Si
Sn Bi Te Se P Mn Zn phases .gamma. + .kappa. + .mu. (%) 8015 62.8
2.6 2.9 0.12 0.03 1.2 remainder .alpha. + .beta. + .gamma. 10 8015a
8016 64.4 2.9 2.7 0.23 0.09 0.13 1.8 remainder .alpha. + .beta. +
.gamma. 15 8016a 8017 68.3 3.6 0.4 0.05 0.05 0.04 2.2 remainder
.alpha. + .beta. + .gamma. 30 8017a 8018 73.2 4.3 0.5 0.06 0.02
0.11 0.02 3.1 remainder .alpha. + .kappa. 60 8018a 8019 72.4 4.1
0.7 0.14 0.21 2.1 remainder .alpha. + .gamma. + .kappa. 50 8019a
8020 69.5 3.7 0.7 0.06 0.04 0.05 1.9 remainder .alpha. + .beta. +
.gamma. + .kappa. 35 8020a
[0125]
18 TABLE 18 alloy composition (wt %) metal construction No. Cu Si
Sn Se P Mn Zn phases .gamma. + .kappa. + .mu. (%) 8021 64.2 3.4 2.5
0.31 0.03 1.9 remainder .alpha. + .beta. + .gamma. 15 8021a
[0126]
19 TABLE 19 alloy composition (wt %) metal construction No. Cu Si
Sn Bi Te Se P Mn Ni Zn phases .gamma. + .kappa. + .mu. (%) 8043 77
4.5 0.03 0.12 1.7 remainder .alpha. + .kappa. + .mu. 55 8043a 8044
70.6 3.9 0.1 0.06 0.04 2.6 remainder .alpha. + .gamma. + .kappa. 30
8044a 8045 74.2 4.3 0.11 0.21 0.16 2.8 remainder .alpha. + .kappa.
45 8045a 8046 69.9 3.8 0.06 0.11 0.03 0.08 1.2 remainder .alpha. +
.beta. + .gamma. 20 8046a 8047 66.8 3.4 0.09 0.06 2.2 remainder
.alpha. + .beta. + .gamma. 15 8047a 8048 71.3 4.2 0.04 0.05 0.05
1.4 remainder .alpha. + .beta. + .gamma. 35 8048a 8049 72.4 4.1
0.12 0.09 2.7 remainder .alpha. + .gamma. + .kappa. 40 8049a 8050
62.9 2.8 2.8 0.12 1.5 remainder .alpha. + .beta. + .gamma. 15
8050a
[0127]
20 TABLE 20 alloy composition (wt %) metal construction No. Cu Si
Sn Bi Te Se Ni Zn phases .gamma. + .kappa. + .mu. (%) 8051 64.8 3.1
2.4 0.08 0.03 2 remainder .alpha. + .beta. + .gamma. 15 8051a 8052
68.9 3.9 0.3 0.03 0.06 1.8 remainder .alpha. + .beta. + .gamma. 30
8052a 8053 67.3 3.7 0.7 0.05 0.04 0.04 2.1 remainder .alpha. +
.beta. + .gamma. 25 8053a 8054 66.5 3.8 0.9 0.31 2.2 remainder
.alpha. + .beta. + .gamma. 25 8054a 8055 73.8 4.3 2.1 0.03 0.05 3.3
remainder .alpha. + .gamma. 55 8055a 8056 74.2 4.4 1.3 0.03 2.7
remainder .alpha. + .gamma. 60 8056a
[0128]
21 TABLE 21 alloy composition (wt %) metal construction No. Cu Si
Sn Bi Te Se P Ni Zn phases .gamma. + .kappa. + .mu. (%) 8064 68.2
3.6 2.6 0.04 0.05 1.5 remainder .alpha. + .beta. + .gamma. 25 8064a
8065 63.9 2.9 2.3 0.32 0.02 0.08 0.8 remainder .alpha. + .beta. +
.gamma. 15 8065a 8066 70.5 3.9 1.1 0.05 0.05 0.05 2.2 remainder
.alpha. + .beta. + .gamma. 35 8066a 8067 67.7 3.7 1.2 0.09 0.03
0.02 0.04 2 remainder .alpha. + .beta. + .gamma. 30 8067a 8068 66.6
3.5 1.4 0.06 0.04 2.6 remainder .alpha. + .beta. + .gamma. 25 8068a
8069 72.3 4.1 0.6 0.05 0.04 0.1 3 remainder .alpha. + .gamma. +
.kappa. 45 8069a 8070 70.6 4 0.4 0.16 0.05 3.2 remainder .alpha. +
.gamma. 40 8070a
[0129]
22 TABLE 22 alloy composition (wt %) metal construction No. Cu Si
Sn Bi Te Se P Mn Ni Zn phases .gamma. + .kappa. + .mu. (%) 8092
67.2 3.4 0.05 0.04 2 remainder .alpha. + .beta. + .gamma. 20 8092a
8093 65.8 3.2 0.15 0.03 0.06 1.2 remainder .alpha. + .beta. +
.gamma. 10 8093a 8094 67.7 3.7 0.06 0.1 0.08 2.1 remainder .alpha.
+ .beta. + .gamma. 20 8094a 8095 64.7 2.9 0.31 0.04 0.05 0.09 1.5
remainder .alpha. + .beta. + .gamma. 10 8095a 8096 66.5 3.6 0.18
0.21 2.3 remainder .alpha. + .beta. + .gamma. 15 8096a 8097 67.3
3.8 0.08 0.05 0.12 2.2 remainder .alpha. + .beta. + .gamma. 20
8097a 8098 65.9 3.6 0.21 0.2 2.5 remainder .alpha. + .beta. +
.gamma. 10 8098a 8099 64.9 3.6 0.4 0.18 0.8 2.6 remainder .alpha. +
.beta. + .gamma. 15 8099a 8100 67.3 3.8 1.8 0.03 0.06 1.9 1
remainder .alpha. + .beta. + .gamma. 30 8100a
[0130]
23 TABLE 23 alloy composition (wt %) metal construction No. Cu Si
Sn Bi Te Se Mn Ni Zn phases .gamma. + .kappa. + .mu. (%) 8101 62.9
2.9 2.4 0.2 0.16 1.3 0.9 remainder .alpha. + .beta. + .gamma. 15
8101a 8102 66.3 3.4 0.5 0.04 0.04 0.05 1.5 0.8 remainder .alpha. +
.beta. + .gamma. 20 8102a 8103 65.8 8 2.6 0.03 1.4 1.2 remainder
.alpha. + .beta. + .gamma. 30 8103a 8104 64.7 3.6 2.7 0.25 0.03 1.3
1.6 remainder .alpha. + .beta. + .gamma. 20 8104a 8105 70.4 3.9 1.8
0.07 1 2 remainder .alpha. + .beta. + .gamma. + .kappa. 35
8105a
[0131]
24 TABLE 24 alloy composition (wt %) metal construction No. Cu Si
Sn Bi Te Se P Mn Ni Zn phases .gamma. + .kappa. + .mu. (%) 8113 72
3.9 1.1 0.25 0.2 2.4 0.9 remainder .alpha. + .gamma. 35 8113a 8114
66.5 3.6 1.2 0.06 0.04 0.05 1.3 1.1 remainder .alpha. + .beta. +
.gamma. 25 8114a 8115 67 3.5 1.3 0.12 0.04 0.08 0.9 1.2 remainder
.alpha. + .beta. + .gamma. 25 8115a 8116 64 2.8 2.6 0.3 0.08 0.03
0.05 0.8 1 remainder .alpha. + .beta. + .gamma. 15 8116a 8117 67.3
3.7 2.3 0.03 0.03 1.2 1.3 remainder .alpha. + .beta. + .gamma. 30
8117a 8118 66.4 3.8 2.4 0.05 0.15 0.03 1 1.6 remainder .alpha. +
.beta. + .gamma. 30 8118a 8119 70.2 3.9 0.5 0.3 0.07 1.7 0.9
remainder .alpha. + .gamma. + .kappa. 35 8119a
[0132]
25 TABLE 25 alloy composition (wt %) metal construction No. Cu Si
Bi Te Se P Mn Ni Zn phases .gamma. + .kappa. + .mu. (%) 8141 66.5
3.6 0.05 0.05 1.5 1.2 remainder .alpha. + .beta. + .gamma. 20 8141a
8142 63.9 2.9 0.3 0.03 0.04 1.2 0.9 remainder .alpha. + .beta. +
.gamma. 10 8142a 8143 68.4 3.8 0.03 0.05 0.12 0.9 2.5 remainder
.alpha. + .gamma. 20 8143a 8144 65.8 3.4 0.1 0.05 0.02 0.03 1 1.4
remainder .alpha. + .beta. + .gamma. 15 8144a 8145 70.5 3.9 0.12
0.05 2.6 0.8 remainder .alpha. + .gamma. + .kappa. 25 8145a 8146 72
4.2 0.04 0.05 0.18 1 2.4 remainder .alpha. + .kappa. + .mu. 35
8146a 8147 68 3.7 0.2 0.06 1.5 1 remainder .alpha. + .beta. +
.gamma. 20 8147a
[0133]
26 TABLE 26 metal construction alloy composition (wt %) .gamma. +
.kappa. + .mu. No. Cu Si Al P Zn phases (%) 9001 72.6 2.3 0.8 0.03
remainder .alpha. + .beta. + .gamma. 15 9002 74.8 2.8 1.3 0.09
remainder .alpha. + .gamma. 30 9003 77.2 3.6 0.2 0.21 remainder
.alpha. + .gamma. + .kappa. 55 9004 75.7 3 1.1 0.07 remainder
.alpha. + .gamma. + .kappa. 35 9005 78 3.8 0.7 0.12 remainder
.alpha. + .kappa. + .mu. 65
[0134]
27 TABLE 27 alloy composition (wt %) metal construction No. Cu Si
Al P Cr Ti Zn phases .gamma. + .kappa. + .mu. (%) 10001 74.3 2.9
0.6 0.05 0.03 remainder .alpha. + .gamma. + .kappa. 25 10002 74.8 3
0.2 0.12 0.32 remainder .alpha. + .gamma. + .kappa. 30 10003 74.9
2.8 0.9 0.08 0.33 remainder .alpha. + .gamma. + .kappa. 30 10004
77.8 3.6 1.2 0.22 0.08 remainder .alpha. + .gamma. + .kappa. 55
10005 71.9 2.3 1.4 0.07 0.02 0.24 remainder .alpha. + .beta. +
.gamma. 20 10006 76 2.8 1.2 0.03 0.15 remainder .alpha. + .gamma. +
.kappa. 30 10007 75.5 3 0.3 0.06 0.2 remainder .alpha. + .gamma. +
.kappa. 35 10008 71.5 2.2 0.7 0.12 0.14 0.05 remainder .alpha. +
.gamma. 20
[0135]
28 TABLE 28 alloy compositon (wt %) metal construction No. Cu Si Al
P Bi Te Se Zn phase .gamma. + .kappa. + .mu. (%) 11001 74.8 2.8 1.4
0.1 0.03 remainder .alpha. + .gamma. 35 11002 76.1 3 0.6 0.06 0.21
remainder .alpha. + .gamma. + .kappa. 40 11003 78.3 3.5 1.3 0.19
0.18 remainder .alpha. + .gamma. + .kappa. 60 11004 71.7 2.4 0.8
0.04 0.21 0.03 remainder .alpha. + .beta. + .gamma. 25 11005 73.9
2.8 0.3 0.09 0.33 0.03 remainder .alpha. + .gamma. 25 11006 74.8
2.8 0.7 0.11 0.16 0.02 remainder .alpha. + .gamma. + .kappa. 30
11007 78.3 3.8 1.1 0.05 0.22 0.05 0.04 remainder .alpha. + .gamma.
+ .kappa. + .mu. 65
[0136]
29 TABLE 29 alloy composition (wt %) metal construction No. Cu Si
Al Bi Te Se P Cr Ti Zn phases .gamma. + .kappa. + .mu. (%) 12001
73.8 2.6 0.5 0.21 0.05 0.11 remainder .alpha. + .gamma. 25 12002
76.5 3.2 0.9 0.03 0.11 0.03 remainder .alpha. + .gamma. + .kappa.
40 12003 78.1 3.4 1.3 0.09 0.2 0.05 remainder .alpha. + .kappa. +
.mu. 55 12004 70.8 2.1 0.6 0.22 0.06 0.08 0.32 remainder .alpha. +
.beta. + .gamma. 20 12005 77.8 3.8 0.2 0.02 0.03 0.03 0.26
remainder .alpha. + .kappa. + .mu. 65 12006 74.6 2.9 0.7 0.15 0.02
0.1 0.06 remainder .alpha. + .gamma. + .kappa. 30 12007 73.9 2.8
0.3 0.04 0.05 0.16 0.03 0.18 remainder .alpha. + .gamma. 25 12008
75.7 2.9 1.2 0.03 0.12 0.05 remainder .alpha. + .gamma. + .kappa.
35 12009 72.9 2.6 0.5 0.33 0.04 0.12 remainder .alpha. + .beta. +
.gamma. 20 12010 76.5 3.2 0.3 0.32 0.03 0.35 remainder .alpha.+
.kappa. + .mu. 40 12011 71.9 2.5 0.8 0.19 0.03 0.03 0.03 remainder
.alpha. + .beta. + .gamma. 25 12012 74.7 2.9 0.6 0.07 0.05 0.21
0.06 remainder .alpha. + .gamma. + .kappa. 30 12013 74.8 2.8 1.3
0.04 0.21 0.06 0.26 remainder .alpha. + .gamma. + .kappa. 35 12014
78.2 3.8 1.1 0.22 0.05 0.03 0.04 0.24 remainder .alpha. + .gamma.
60 12015 74.6 2.7 1 0.15 0.03 0.02 0.1 remainder .alpha. + .gamma.
+ .kappa. + .mu. 30 12016 75.5 2.9 0.7 0.22 0.05 0.34 0.02
remainder .alpha. + .gamma. 35 12017 76.2 3.4 0.3 0.05 0.12 0.08
0.31 remainder .alpha. + .gamma. + .kappa. 50 12018 77 3.3 1.1 0.03
0.14 0.03 0.05 0.03 remainder .alpha. + .kappa. 50 12019 73.7 2.8
0.3 0.32 0.03 0.1 0.03 0.19 remainder .alpha. + .gamma. + .kappa.
25 12020 74.8 2.8 1.2 0.02 0.14 0.05 0.14 0.05 remainder .alpha. +
.gamma. 35 12021 74 2.9 0.4 0.07 0.05 0.05 0.08 0.11 0.26 remainder
.alpha. + .gamma. + .kappa. 25
[0137]
30 TABLE 30 alloy heat treatment metal construction composition (wt
%) tem- .gamma. + .kappa. + No. Cu Si Zn perature time phases .mu.
(%) 13001 78.5 3.2 remainder 580.degree. C. 30 .alpha. + .gamma. +
.kappa. 45 min. 13002 78.5 3.2 remainder 450.degree. C. 2 hr.
.alpha. + .gamma. + 45 .kappa. + .mu. 13003 77 2.9 remainder
580.degree. C. 30 .alpha. + .gamma. + .kappa. 35 min. 13004 77 2.9
remainder 450.degree. C. 2 hr. .alpha. + .gamma. + 35 .kappa. +
.mu. 13005 69.9 2.3 remainder 580.degree. C. 30 .alpha. + .gamma. +
.kappa. 20 min. 13006 69.9 2.3 remainder 450.degree. C. 2 hr.
.alpha. + .gamma. + 20 .kappa. + .mu.
[0138]
31 TABLE 3 metal con- alloy composition (wt %) struction No. Cu Si
Sn Al Mn Pb Fe Ni Zn phases 14001 53.8 0.2 3.1 0.2 re- .alpha. +
.beta. 14001a mainder 14002 61.4 0.2 3 0.2 re- .alpha. + .beta.
14002a mainder 14003 59.1 0.2 2 0.2 re- .alpha. + .beta. 14003a
mainder 14004 69.2 1.2 0.1 re- .alpha. + .beta. 14004a mainder
14005 re- 9.8 1.1 3.9 1.2 .alpha. + .beta. 14005a mainder
[0139]
32 TABLE 32 corrosion stress machinability resistance hot
mechanical properties resistance condition maximum depth
workability tensile corrosion form of of cut cutting of corrosion
700.degree. C. strength elongation cracking No. chippings surface
force (N) (.mu.m) deformability (N/mm.sup.2) (%) resistance 1001
.circleincircle. .smallcircle. 118 190 .smallcircle. 575 32
.smallcircle. 1002 .circleincircle. .smallcircle. 123 180
.smallcircle. 575 35 .smallcircle. 1003 .circleincircle.
.smallcircle. 119 190 .smallcircle. 543 34 .smallcircle. 1004
.circleincircle. .smallcircle. 126 170 .DELTA. 590 37 .smallcircle.
1005 .DELTA. .smallcircle. 134 150 .DELTA. 532 42 .smallcircle.
[0140]
33 TABLE 33 corrosion hot stress machinability resistance
workability mechanical properties resistance condition maximum
depth 700.degree. C. tensile corrosion form of of cut cutting of
corrosion deform- strength elongation cracking No. chippings
surface force (N) (.mu.m) ability (N/mm.sup.2) (%) resistance 2001
75.2 3.2 0.19 remainder .alpha. + .gamma. + .kappa. 40 2002 72.6
3.1 0.25 remainder .alpha. + .beta. + .gamma. 30 2003 77.6 3.8 0.05
0.09 remainder .alpha. + .kappa. + .mu. 65 2004 75.8 3.5 0.11 0.05
remainder .alpha. + .kappa. + .mu. 55 2005 76.4 3.4 0.03 0.05 0.11
remainder .alpha. + .kappa. + .mu. 50 2006 .circleincircle.
.largecircle. 119 170 .DELTA. 552 36 .largecircle. 2008
.circleincircle. .largecircle. 115 140 .DELTA. 570 34
.largecircle.
[0141]
34 TABLE 34 corrosion hot stress machinability resistance
workability mechanical properties resistance condition maximum
depth 700.degree. C. tensile corrosion form of of cut cutting of
corrosion deform- strength elongation cracking No. chippings
surface force (N) (.mu.m) ability (N/mm.sup.2) (%) resistance 3001
.circleincircle. .DELTA. 128 40 .largecircle. 553 26 .largecircle.
3004 .circleincircle. .largecircle. 119 <5 .largecircle. 533 36
.largecircle. 3005 .circleincircle. .largecircle. 125 50
.largecircle. 525 28 .largecircle. 3008 .circleincircle.
.largecircle. 122 80 .largecircle. 570 36 .largecircle. 3009
.circleincircle. .largecircle. 123 50 .largecircle. 541 29
.largecircle. 3010 .circleincircle. .largecircle. 118 <5
.largecircle. 560 35 .largecircle. 3011 .circleincircle.
.largecircle. 119 20 .largecircle. 502 34 .largecircle. 3012
.circleincircle. .largecircle. 120 <5 .largecircle. 534 31
.largecircle.
[0142]
35 TABLE 35 corrosion hot stress machinability resistance
workability mechanical properties resistance condition maximum
depth 700.degree. C. tensile corrosion form of of cut cutting of
corrosion deform- strength elongation cracking No. chippings
surface force (N) (.mu.m) ability (N/mm.sup.2) (%) resistance 4001
.circleincircle. .largecircle. 119 40 .DELTA. 512 24 .largecircle.
4002 .circleincircle. .largecircle. 122 50 .largecircle. 543 30
.largecircle. 4003 .circleincircle. .largecircle. 123 50
.largecircle. 533 30 .largecircle. 4004 .circleincircle.
.largecircle. 117 80 .DELTA. 520 31 .largecircle. 4005
.circleincircle. .largecircle. 119 50 .largecircle. 535 32
.largecircle. 4006 .circleincircle. .largecircle. 116 60
.largecircle. 532 31 .largecircle. 4007 .circleincircle.
.largecircle. 122 50 .largecircle. 528 26 .largecircle.
[0143]
36 TABLE 36 corrosion hot stress machinability resistance
workability mechanical properties resistance condition maximum
depth 700.degree. C. tensile corrosion form of of cut cutting of
corrosion deform- strength elongation cracking No. chippings
surface force (N) (.mu.m) ability (N/mm.sup.2) (%) resistance 4022
.circleincircle. .largecircle. 123 <5 .largecircle. 487 32
.DELTA. 4023 .circleincircle. .largecircle. 117 <5 .largecircle.
524 34 .largecircle. 4024 .circleincircle. .largecircle. 117 40
.largecircle. 541 37 .largecircle. 4025 .circleincircle.
.largecircle. 115 <5 .DELTA. 526 43 .largecircle. 4026
.circleincircle. .largecircle. 122 30 .largecircle. 498 30 .DELTA.
4027 .circleincircle. .largecircle. 118 30 .largecircle. 516 35
.largecircle. 4028 .circleincircle. .largecircle. 120 <5
.largecircle. 529 27 .largecircle. 4029 .circleincircle.
.largecircle. 121 <5 .largecircle. 544 28 .largecircle. 4030
.circleincircle. .largecircle. 118 <5 .largecircle. 536 30
.largecircle. 4031 .circleincircle. .largecircle. 116 <5
.largecircle. 524 31 .largecircle. 4032 .circleincircle.
.largecircle. 114 <5 .largecircle. 515 32 .largecircle. 4033
.circleincircle. .largecircle. 118 <5 .largecircle. 519 37
.largecircle. 4034 .circleincircle. .largecircle. 118 <5
.largecircle. 582 31 .largecircle. 4035 .circleincircle.
.largecircle. 117 <5 .largecircle. 538 32 .largecircle.
[0144]
37 TABLE 37 corrosion hot stress machinability resistance
workability mechanical properties resistance condition maximum
depth 700.degree. C. tensile corrosion form of of cut cutting of
corrosion deform- strength elongation cracking No. chippings
surface force (N) (.mu.m) ability (N/mm.sup.2) % resistance 5001
.circleincircle. .DELTA. 127 30 .largecircle. 501 25 .largecircle.
5002 .circleincircle. .largecircle. 119 <5 .largecircle. 524 37
.largecircle. 5003 .circleincircle. .DELTA. 135 10 .largecircle.
488 41 .largecircle. 5004 .circleincircle. .largecircle. 126 20
.DELTA. 552 38 .largecircle. 5005 .circleincircle. .largecircle.
123 <5 .largecircle. 518 29 .largecircle. 5006 .circleincircle.
.largecircle. 122 <5 .largecircle. 520 34 .largecircle. 5007
.circleincircle. .DELTA. 125 <5 .largecircle. 507 23
.largecircle. 5008 .circleincircle. .largecircle. 122 <5
.largecircle. 515 30 .largecircle. 5009 .circleincircle.
.largecircle. 124 <5 .largecircle. 544 35 .largecircle. 5010
.circleincircle. .largecircle. 123 <5 .DELTA. 536 36
.largecircle. 5011 .circleincircle. .DELTA. 126 <5 .largecircle.
511 27 .largecircle. 5012 .circleincircle. .largecircle. 124 <5
.largecircle. 596 36 .largecircle. 5013 .circleincircle.
.largecircle. 119 <5 .largecircle. 519 39 .largecircle. 5014
.circleincircle. .largecircle. 122 <5 .largecircle. 523 37
.largecircle. 5015 .circleincircle. .largecircle. 123 <5
.largecircle. 510 40 .largecircle. 5016 .circleincircle.
.largecircle. 120 20 .largecircle. 490 35 .DELTA. 5017
.circleincircle. .largecircle. 121 <5 .largecircle. 573 40
.largecircle. 5018 .circleincircle. .largecircle. 120 <5
.largecircle. 549 39 .largecircle. 5019 .circleincircle.
.largecircle. 122 50 .largecircle. 537 30 .largecircle. 5020
.circleincircle. .largecircle. 118 <5 .largecircle. 521 37
.largecircle.
[0145]
38 TABLE 38 corrosion hot stress machinability resistance
workability mechanical properties resistance condition maximum
depth 700.degree. C. tensile corrosion form of of cut cutting of
corrosion deform- strength elongation cracking No. chippings
surface force (N) (.mu.m) ability (N/mm.sup.2) (%) resistance 6001
.circleincircle. .largecircle. 121 30 .largecircle. 512 24
.largecircle. 6002 .circleincircle. .largecircle. 122 <5
.largecircle. 574 31 .largecircle. 6003 .circleincircle.
.largecircle. 117 <5 .DELTA. 501 32 .largecircle. 6004
.circleincircle. .largecircle. 120 <5 .largecircle. 514 26
.largecircle. 6005 .circleincircle. .largecircle. 121 <5 .DELTA.
525 42 .largecircle. 6006 .largecircle. .largecircle. 115 <5
.largecircle. 514 32 .largecircle. 6007 .circleincircle.
.largecircle. 120 <5 .largecircle. 548 27 .largecircle. 6008
.circleincircle. .largecircle. 119 <5 .largecircle. 503 30
.largecircle. 6009 .circleincircle. .largecircle. 117 <5
.largecircle. 522 38 .largecircle. 6010 .circleincircle.
.largecircle. 122 <5 .DELTA. 527 41 .largecircle. 6011
.circleincircle. .largecircle. 119 <5 .largecircle. 536 32
.largecircle. 6012 .circleincircle. .largecircle. 123 20
.largecircle. 478 27 .DELTA. 6013 .circleincircle. .largecircle.
118 <5 .largecircle. 506 30 .largecircle. 6014 .circleincircle.
.largecircle. 118 <5 .largecircle. 525 39 .largecircle. 6015
.largecircle. .largecircle. 114 <5 .largecircle. 503 35
.largecircle. 6016 .circleincircle. .largecircle. 122 40
.largecircle. 526 27 .largecircle. 6017 .circleincircle.
.largecircle. 119 <5 .DELTA. 507 30 .largecircle. 6018
.circleincircle. .largecircle. 121 <5 .largecircle. 589 31
.largecircle. 6019 .circleincircle. .largecircle. 120 <5
.largecircle. 508 25 .largecircle. 6020 .circleincircle.
.largecircle. 121 <5 .DELTA. 504 43 .largecircle.
[0146]
39 TABLE 39 corrosion hot stress machinability resistance
workability mechanical properties resistance condition maximum
depth 700.degree. C. tensile corrosion form of of cut cutting of
corrosion deform- strength elongation cracking No. chippings
surface force (N) (.mu.m) ability (N/mm.sup.2) (%) resistance 6021
.circleincircle. .largecircle. 116 <5 .largecircle. 501 33
.largecircle. 6022 .circleincircle. .largecircle. 120 <5
.largecircle. 547 29 .largecircle. 6023 .largecircle. .largecircle.
119 <5 .largecircle. 523 30 .largecircle. 6024 .circleincircle.
.largecircle. 120 <5 .DELTA. 525 40 .largecircle. 6025
.circleincircle. .largecircle. 120 <5 .largecircle. 496 30
.largecircle. 6026 .largecircle. .largecircle. 114 <5
.largecircle. 518 34 .largecircle. 6027 .circleincircle.
.largecircle. 119 <5 .largecircle. 487 28 .DELTA. 6028
.circleincircle. .largecircle. 118 <5 .largecircle. 524 35
.largecircle. 6029 .circleincircle. .largecircle. 122 <5 .DELTA.
540 41 .largecircle. 6030 .circleincircle. .largecircle. 118 <5
.largecircle. 511 29 .largecircle. 6031 .circleincircle.
.largecircle. 119 40 .largecircle. 519 28 .largecircle. 6032
.circleincircle. .largecircle. 120 <5 .largecircle. 572 32
.largecircle. 6033 .circleincircle. .largecircle. 123 <5 .DELTA.
515 36 .largecircle. 6034 .circleincircle. .largecircle. 122 <5
.largecircle. 580 35 .largecircle. 6035 .circleincircle.
.largecircle. 123 <5 .largecircle. 517 27 .largecircle. 6036
.circleincircle. .largecircle. 121 <5 .largecircle. 503 26
.largecircle. 6037 .largecircle. .largecircle. 117 <5
.largecircle. 536 30 .largecircle. 6038 .circleincircle.
.largecircle. 116 <5 .largecircle. 506 30 .largecircle. 6039
.circleincircle. .largecircle. 120 <5 .largecircle. 485 28
.DELTA. 6040 .largecircle. .largecircle. 116 <5 .largecircle.
528 36 .largecircle.
[0147]
40 TABLE 40 corrosion hot stress machinability resistance
workability mechanical properties resistance condition maximum
depth 700.degree. C. tensile corrosion form of of cut cutting of
corrosion deform- strength elongation cracking No. chippings
surface force (N) (.mu.m) ability (N/mm.sup.2) (%) resistance 6041
.circleincircle. .largecircle. 117 <5 .largecircle. 496 30
.largecircle. 6042 .circleincircle. .largecircle. 120 <5 .DELTA.
574 34 .largecircle. 6043 .circleincircle. .largecircle. 123 10
.DELTA. 506 43 .largecircle. 6044 .circleincircle. .largecircle.
115 10 .largecircle. 500 30 .largecircle. 6045 .circleincircle.
.largecircle. 119 20 .DELTA. 485 27 .DELTA. 6046 .circleincircle.
.largecircle. 121 40 .largecircle. 512 24 .largecircle. 6047
.circleincircle. .largecircle. 123 <5 .largecircle. 557 25
.largecircle. 6048 .circleincircle. .largecircle. 120 <5
.largecircle. 526 30 .largecircle. 6049 .circleincircle.
.largecircle. 120 <5 .largecircle. 502 24 .largecircle. 6050
.circleincircle. .largecircle. 124 <5 .largecircle. 480 31
.largecircle. 6051 .largecircle. .largecircle. 117 <5
.largecircle. 534 32 .largecircle. 6052 .circleincircle.
.largecircle. 123 <5 .DELTA. 523 38 .largecircle. 6053
.circleincircle. .largecircle. 123 <5 .largecircle. 506 39
.largecircle. 6054 .circleincircle. .largecircle. 115 <5
.largecircle. 485 31 .largecircle. 6055 .circleincircle.
.largecircle. 122 <5 .DELTA. 512 44 .largecircle. 6056
.circleincircle. .largecircle. 120 <5 .largecircle. 480 33
.DELTA. 6057 .circleincircle. .largecircle. 121 <5 .largecircle.
479 25 .DELTA. 6058 .largecircle. .largecircle. 116 <5
.largecircle. 525 34 .largecircle. 6059 .circleincircle.
.largecircle. 119 20 .largecircle. 482 35 .largecircle. 6060
.largecircle. .largecircle. 118 30 .largecircle. 513 38
.largecircle.
[0148]
41 TABLE 41 corrosion hot stress machinability resistance
workability mechanical properties resistance condition maximum
depth 700.degree. C. tensile corrosion form of of cut cutting of
corrosion deform- strength elongation cracking No. chippings
surface force (N) (.mu.m) ability (N/mm.sup.2) (%) resistance 6061
.circleincircle. .largecircle. 123 30 .largecircle. 530 22
.largecircle. 6062 .circleincircle. .largecircle. 119 10
.largecircle. 538 33 .largecircle. 6063 .circleincircle.
.largecircle. 118 <5 .largecircle. 504 37 .largecircle. 6064
.circleincircle. .largecircle. 121 <5 .largecircle. 526 30
.largecircle. 6065 .circleincircle. .largecircle. 123 <5
.largecircle. 565 35 .largecircle. 6066 .circleincircle.
.largecircle. 120 <5 .largecircle. 501 25 .largecircle. 6067
.circleincircle. .largecircle. 119 <5 .largecircle. 526 26
.largecircle. 6068 .circleincircle. .largecircle. 122 <5
.largecircle. 502 30 .largecircle. 6069 .circleincircle.
.largecircle. 124 <5 .largecircle. 484 28 .DELTA. 6070
.largecircle. .largecircle. 115 <5 .largecircle. 548 37
.largecircle. 6071 .circleincircle. .largecircle. 118 <5
.largecircle. 530 34 .largecircle. 6072 .circleincircle.
.largecircle. 119 <5 .largecircle. 515 30 .largecircle. 6073
.circleincircle. .largecircle. 121 <5 .DELTA. 579 35
.largecircle. 6074 .circleincircle. .largecircle. 117 <5
.largecircle. 517 32 .largecircle. 6075 .circleincircle.
.largecircle. 117 <5 .largecircle. 513 38 .largecircle. 6076
.circleincircle. .largecircle. 122 40 .largecircle. 535 28
.largecircle. 6077 .largecircle. .largecircle. 119 <5
.largecircle. 490 30 .largecircle. 6078 .circleincircle.
.largecircle. 122 <5 .DELTA. 513 40 .largecircle. 6079
.circleincircle. .largecircle. 118 <5 .largecircle. 524 30
.largecircle. 6080 .circleincircle. .largecircle. 123 <5
.largecircle. 482 35 .largecircle.
[0149]
42 TABLE 42 corrosion hot stress machinability resistance
workability mechanical properties resistance condition maximum
depth 700.degree. C. tensile corrosion form of of cut cutting of
corrosion deform- strength elongation cracking No. chippings
surface force (N) (.mu.m) ability (N/mm.sup.2) (%) resistance 6081
.circleincircle. .largecircle. 118 <5 .largecircle. 536 34
.largecircle. 6082 .circleincircle. .largecircle. 123 <5
.largecircle. 510 25 .largecircle. 6083 .circleincircle.
.largecircle. 119 <5 .largecircle. 504 32 .largecircle. 6084
.circleincircle. .largecircle. 117 <5 .largecircle. 533 34
.largecircle. 6085 .circleincircle. .largecircle. 118 10
.largecircle. 501 30 .largecircle. 6086 .circleincircle.
.largecircle. 117 <5 .largecircle. 545 37 .largecircle. 6087
.circleincircle. .largecircle. 119 <5 .largecircle. 503 34
.largecircle. 6088 .largecircle. .largecircle. 115 <5
.largecircle. 526 36 .largecircle. 6089 .circleincircle.
.largecircle. 119 <5 .largecircle. 514 39 .largecircle. 6090
.circleincircle. .largecircle. 121 20 .DELTA. 480 35 .largecircle.
6091 .circleincircle. .largecircle. 122 30 .largecircle. 516 24
.largecircle. 6092 .circleincircle. .largecircle. 118 <5
.largecircle. 532 30 .largecircle. 6093 .circleincircle.
.largecircle. 119 <5 .largecircle. 539 34 .largecircle. 6094
.largecircle. .largecircle. 117 <5 .largecircle. 528 32
.largecircle. 6095 .circleincircle. .largecircle. 119 <5
.largecircle. 507 30 .largecircle. 6096 .circleincircle.
.largecircle. 122 <5 .largecircle. 508 22 .largecircle. 6097
.circleincircle. .largecircle. 117 <5 .largecircle. 510 31
.largecircle. 6098 .circleincircle. .largecircle. 117 <5
.largecircle. 527 32 .largecircle. 6099 .circleincircle.
.largecircle. 116 <5 .largecircle. 529 34 .largecircle. 6100
.circleincircle. .largecircle. 119 <5 .largecircle. 515 32
.largecircle.
[0150]
43 TABLE 43 corrosion hot stress machinability resistance
workability mechanical properties resistance condition maximum
depth 700.degree. C. tensile corrosion form of of cut cutting of
corrosion deform- strength elongation cracking No. chippings
surface force (N) (.mu.m) ability (N/mm.sup.2) (%) resistance 6101
.largecircle. .largecircle. 115 <5 .largecircle. 530 38
.largecircle. 6102 .circleincircle. .largecircle. 118 <5
.largecircle. 512 36 .largecircle. 6103 .circleincircle.
.largecircle. 119 <5 .largecircle. 501 35 .largecircle. 6104
.circleincircle. .largecircle. 117 <5 .largecircle. 535 32
.largecircle. 6105 .circleincircle. .largecircle. 117 <5
.largecircle. 517 37 .largecircle.
[0151]
44 TABLE 44 hot work- machinability ability mechanical properties
condition cutting 700.degree. C. tensile form of of cut force
deform- strength elongation No. chippings surface (N) ability
(N/mm.sup.2) (%) 7001 .circleincircle. .DELTA. 138 .largecircle.
670 18 7002 .circleincircle. .DELTA. 136 .largecircle. 712 20 7003
.circleincircle. .largecircle. 132 .largecircle. 783 23 7016
.circleincircle. .largecircle. 129 .largecircle. 759 20 7017
.DELTA. .largecircle. 139 .largecircle. 638 18 7018
.circleincircle. .largecircle. 135 .largecircle. 717 20 7019
.circleincircle. .largecircle. 136 .largecircle. 694 24 7020
.DELTA. .largecircle. 138 .largecircle. 712 25
[0152]
45 TABLE 45 hot work- machinability ability mechanical properties
condition cutting 700.degree. C. tensile form of of cut force
deform- strength elongation No. chippings surface (N) ability
(N/mm.sup.2) (%) 7021 .circleincircle. .largecircle. 130
.largecircle. 754 24 7030 .circleincircle. .largecircle. 135
.largecircle. 820 18
[0153]
46 TABLE 46 hot work- machinability ability mechanical properties
condition cutting 700.degree. C. tensile form of of cut force
deform- strength elongation No. chippings surface (N) ability
(N/mm.sup.2) (%) 8001 .circleincircle. .largecircle. 132
.largecircle. 655 15 8002 .circleincircle. .largecircle. 129
.largecircle. 708 17 8003 .circleincircle. .largecircle. 127
.largecircle. 768 20 8004 .circleincircle. .largecircle. 128
.largecircle. 785 18 8005 .circleincircle. .largecircle. 131
.largecircle. 714 16 8006 .circleincircle. .largecircle. 134
.largecircle. 680 16 8007 .circleincircle. .largecircle. 132
.largecircle. 764 17 8015 .circleincircle. .largecircle. 133
.largecircle. 679 15 8016 .circleincircle. .largecircle. 130
.largecircle. 706 16 8017 .circleincircle. .largecircle. 129
.largecircle. 707 18 8018 .circleincircle. .largecircle. 131
.largecircle. 780 16 8019 .circleincircle. .largecircle. 128
.largecircle. 768 16 8020 .circleincircle. .largecircle. 132
.largecircle. 723 19
[0154]
47 TABLE 47 hot work- machinability ability mechanical properties
condition cutting 700.degree. C. tensile form of of cut force
deform- strength elongation No. chippings surface (N) ability
(N/mm.sup.2) (%) 8021 .circleincircle. .largecircle. 134
.largecircle. 765 16
[0155]
48 TABLE 48 hot work- machinability ability mechanical properties
condition cutting 700.degree. C. tensile form of of cut force
deform- strength elongation No. chippings surface (N) ability
(N/mm.sup.2) (%) 8043 .circleincircle. .largecircle. 131
.largecircle. 780 18 8044 .circleincircle. .largecircle. 126
.largecircle. 726 21 8045 .circleincircle. .largecircle. 128
.largecircle. 766 22 8046 .circleincircle. .largecircle. 127
.largecircle. 712 23 8047 .circleincircle. .largecircle. 128
.largecircle. 674 21 8048 .circleincircle. .largecircle. 129
.largecircle. 753 24 8049 .circleincircle. .largecircle. 127
.largecircle. 768 22 8050 .circleincircle. .largecircle. 132
.largecircle. 691 17 8051 .circleincircle. .largecircle. 131
.largecircle. 717 17 8053 .circleincircle. .largecircle. 128
.largecircle. 730 22 8054 .circleincircle. .largecircle. 127
.largecircle. 735 20 8055 .circleincircle. .largecircle. 134
.largecircle. 818 15 8056 .circleincircle. .largecircle. 132
.largecircle. 812 16
[0156]
49 TABLE 49 hot work- machinability ability mechanical properties
condition cutting 700.degree. C. tensile form of of cut force
deform- strength elongation No. chippings surface (N) ability
(N/mm.sup.2) (%) 8064 .circleincircle. .largecircle. 131
.largecircle. 746 17 8065 .circleincircle. .largecircle. 133
.largecircle. 652 19 8066 .circleincircle. .largecircle. 130
.largecircle. 758 19 8067 .circleincircle. .largecircle. 129
.largecircle. 734 19 8068 .circleincircle. .largecircle. 131
.largecircle. 710 17 8069 .circleincircle. .largecircle. 131
.largecircle. 767 20 8070 .circleincircle. .largecircle. 131
.largecircle. 753 18
[0157]
50 TABLE 50 hot work- machinability ability mechanical properties
condition cutting 700.degree. C. tensile form of of cut force
deform- strength elongation No. chippings surface (N) ability
(N/mm.sup.2) (%) 8092 .circleincircle. .largecircle. 130
.largecircle. 680 22 8093 .circleincircle. .largecircle. 131
.largecircle. 655 23 8094 .circleincircle. .largecircle. 128
.largecircle. 714 21 8095 .circleincircle. .largecircle. 132
.largecircle. 638 24 8096 .circleincircle. .largecircle. 128
.largecircle. 689 22 8097 .circleincircle. .largecircle. 129
.largecircle. 711 21 8098 .circleincircle. .largecircle. 130
.largecircle. 693 20 8099 .circleincircle. .largecircle. 127
.largecircle. 702 21 8100 .circleincircle. .largecircle. 129
.largecircle. 724 18
[0158]
51 TABLE 51 hot work- machinability ability mechanical properties
condition cutting 700.degree. C. tensile form of of cut force
deform- strength elongation No. chippings surface (N) ability
(N/mm.sup.2) (%) 8101 .circleincircle. .largecircle. 131
.largecircle. 685 18 8102 .circleincircle. .largecircle. 132
.largecircle. 690 21 8103 .circleincircle. .largecircle. 133
.largecircle. 744 17 8104 .circleincircle. .largecircle. 130
.largecircle. 726 17 8105 .circleincircle. .largecircle. 133
.largecircle. 751 19 8113 .circleincircle. .largecircle. 129
.largecircle. 745 22 8114 .circleincircle. .largecircle. 132
.largecircle. 722 20 8115 .circleincircle. .largecircle. 130
.largecircle. 706 17 8116 .circleincircle. .largecircle. 133
.largecircle. 684 19 8117 .circleincircle. .largecircle. 132
.largecircle. 740 18 8118 .circleincircle. .largecircle. 133
.largecircle. 765 16 8119 .circleincircle. .largecircle. 128
.largecircle. 733 22
[0159]
52 TABLE 52 hot work- machinability ability mechanical properties
condition cutting 700.degree. C. tensile form of of cut force
deform- strength elongation No. chippings surface (N) ability
(N/mm.sup.2) (%) 8141 .circleincircle. .largecircle. 131
.largecircle. 687 22 8142 .circleincircle. .largecircle. 130
.largecircle. 635 20 8143 .circleincircle. .largecircle. 129
.largecircle. 710 23 8144 .circleincircle. .largecircle. 130
.largecircle. 662 24 8145 .circleincircle. .largecircle. 128
.largecircle. 728 23 8146 .circleincircle. .largecircle. 129
.largecircle. 753 21 8147 .circleincircle. .largecircle. 130
.largecircle. 709 24
[0160]
53 TABLE 53 corrosion hot stress high-temperature machinability
resistance workability mechanical properties resistance oxidation
condition maximum depth 700.degree. C. tensile corrosion increase
in weight form of of cut cutting of corrosion deform- strength
elongation cracking by oxidation No. chippings surface force (N)
(.mu.m) ability (N/mm.sup.2) (%) resistance (mg/10 cm.sup.2) 9001
.circleincircle. .DELTA. 132 20 .largecircle. 500 37 .largecircle.
0.3 9002 .circleincircle. .largecircle. 122 <5 .largecircle. 564
35 .largecircle. 0.2 9003 .circleincircle. .largecircle. 123 <5
.largecircle. 585 39 .largecircle. 0.5 9004 .circleincircle.
.largecircle. 118 <5 .largecircle. 558 34 .largecircle. 0.2 9005
.DELTA. .largecircle. 132 <5 .DELTA. 593 37 .largecircle.
0.3
[0161]
54 TABLE 54 corrosion hot stress high-temperature machinability
resistance workability mechanical properties resistance oxidation
condition maximum depth 700.degree. C. tensile corrosion increase
in weight form of of cut cutting of corrosion deform- strength
elongation cracking by oxidation No. chippings surface force (N)
(.mu.m) ability (N/mm.sup.2) (%) resistance (mg/10 cm.sup.2) 10001
.circleincircle. .largecircle. 124 <5 .largecircle. 534 35
.largecircle. 0.3 10002 .circleincircle. .largecircle. 120 <5
.largecircle. 540 33 .largecircle. 0.2 10003 .circleincircle.
.largecircle. 122 <5 .largecircle. 539 38 .largecircle. 0.2
10004 .circleincircle. .largecircle. 124 <5 .largecircle. 575 40
.largecircle. 0.1 10005 .circleincircle. .DELTA. 128 <5
.largecircle. 512 33 .largecircle. 0.1 10006 .circleincircle.
.largecircle. 120 20 .largecircle. 560 35 .largecircle. 0.1 10007
.circleincircle. .largecircle. 119 <5 .largecircle. 536 36
.largecircle. 0.3 10008 .DELTA. .largecircle. 132 <5
.largecircle. 501 31 .DELTA. 0.1
[0162]
55 TABLE 55 corrosion hot stress high-temperature machinability
resistance workability mechanical properties resistance oxidation
condition maximum depth 700.degree. C. tensile corrosion increase
in weight form of of cut cutting of corrosion deform- strength
elongation cracking by oxidation No. chippings surface force (N)
(.mu.m) ability (N/mm.sup.2) (%) resistance (mg/10 cm.sup.2) 11001
.circleincircle. .largecircle. 117 <5 .largecircle. 540 36
.largecircle. 0.2 11002 .circleincircle. .largecircle. 117 <5
.largecircle. 537 34 .largecircle. 0.3 11003 .circleincircle.
.largecircle. 121 <5 .DELTA. 573 38 .largecircle. 0.2 11004
.circleincircle. .largecircle. 119 30 .largecircle. 512 30
.largecircle. 0.3 11005 .largecircle. .largecircle. 114 <5
.DELTA. 518 30 .largecircle. 0.4 11006 .circleincircle.
.largecircle. 118 <5 .largecircle. 535 32 .largecircle. 0.3
11007 .circleincircle. .largecircle. 119 <5 .DELTA. 586 37
.largecircle. 0.2
[0163]
56 TABLE 56 corrosion hot stress high-temperature machinability
resistance workability mechanical properties resistance oxidation
condition maximum depth 700.degree. C. tensile corrosion increase
in weight form of of cut cutting of corrosion deform- strength
elongation cracking by oxidation No. chippings surface force (N)
(.mu.m) ability (N/mm.sup.2) (%) resistance (mg/10 cm.sup.2) 12001
.circleincircle. .largecircle. 121 <5 .largecircle. 512 32
.largecircle. 0.2 12002 .circleincircle. .largecircle. 119 <5
.largecircle. 544 36 .largecircle. 0.2 12003 .circleincircle.
.largecircle. 123 <5 .largecircle. 570 38 .largecircle. 0.1
12004 .circleincircle. .largecircle. 124 <5 .DELTA. 495 31
.DELTA. 0.2 12005 .circleincircle. .largecircle. 123 30 .DELTA. 583
32 .largecircle. 0.3 12006 .circleincircle. .largecircle. 118 <5
.largecircle. 537 33 .largecircle. 0.2 12007 .circleincircle.
.largecircle. 118 20 .largecircle. 516 30 .largecircle. 0.2 12008
.circleincircle. .largecircle. 117 <5 .largecircle. 543 38
.largecircle. 0.1 12009 .circleincircle. .largecircle. 122 20
.largecircle. 501 32 .largecircle. 0.2 12010 .circleincircle.
.largecircle. 119 30 .largecircle. 546 35 .largecircle. 0.2 12011
.circleincircle. .largecircle. 121 20 .largecircle. 516 31
.largecircle. 0.1 12012 .circleincircle. .largecircle. 117 <5
.largecircle. 539 33 .largecircle. 0.2 12012 .circleincircle.
.largecircle. 121 <5 .largecircle. 544 33 .largecircle. <0.1
12014 .circleincircle. .largecircle. 121 <5 .DELTA. 590 37
.largecircle. <0.1 12015 .circleincircle. .largecircle. 120 20
.largecircle. 528 32 .largecircle. 0.1 12016 .circleincircle.
.largecircle. 117 <5 .largecircle. 535 33 .largecircle. 0.1
12017 .circleincircle. .largecircle. 121 <5 .largecircle. 577 35
.largecircle. 0.2 12018 .circleincircle. .largecircle. 120 <5
.DELTA. 586 37 .largecircle. 0.1 12019 .circleincircle.
.largecircle. 115 <5 .largecircle. 520 31 .largecircle. 0.2
12020 .circleincircle. .largecircle. 118 <5 .largecircle. 549 34
.largecircle. 0.1 12021 .circleincircle. .largecircle. 116 <5
.largecircle. 533 34 .largecircle. 0.1
[0164]
57 TABLE 57 corrosion stress machinability resistance hot
mechanical properties resistance condition maximum depth
workability tensile corrosion form of of cut cutting of corrosion
700.degree. C. deform strength elongation cracking No. chippings
surface force (N) (.mu.m) ability (N/mm.sup.2) (%) resistance 13001
.circleincircle. .largecircle. 128 140 .DELTA. 521 39 .largecircle.
13002 .circleincircle. .largecircle. 126 130 .DELTA. 524 41
.largecircle. 13003 .circleincircle. .largecircle. 127 150 .DELTA.
500 38 .largecircle. 13004 .circleincircle. .largecircle. 127 160
.DELTA. 508 38 .largecircle. 13005 .circleincircle. .largecircle.
128 180 .largecircle. 483 35 .largecircle. 13006 .circleincircle.
.largecircle. 129 170 .largecircle. 488 37 .largecircle.
[0165]
58 TABLE 58 corrosion stress high-temperature machinability
resistance hot mechanical properties resistance oxidation condition
maximum depth workability tensile corrosion increase in weight form
of of cut cutting of corrosion 700.degree. C. deform strength
elongation cracking by oxidation No. chippings surface force (N)
(.mu.m) ability (N/mm.sup.2) (%) resistance (mg/10 cm.sup.2) 14001
.largecircle. .largecircle. 103 1100 .DELTA. 408 37 X X 1.8 14002
.largecircle. .largecircle. 101 1000 X 387 39 X X 1.7 14003
.largecircle. .DELTA. 112 1050 .largecircle. 414 38 X X 1.7 14004 X
.largecircle. 223 900 .largecircle. 438 38 X 1.2 14005 X
.largecircle. 178 350 .DELTA. 735 28 .largecircle. 0.2
[0166]
59 TABLE 59 wear resistance weight loss by wear No. (mg/100000
rot.) 7001a 1.3 7002a 0.8 7003a 0.9 7016a 1.3 7017a 1.6 7018a 1.4
7019a 1.9 7020a 1.5
[0167]
60 TABLE 60 wear resistance weight loss by wear No. (mg/100000
rot.) 7021a 1.3 7030a 1.4
[0168]
61 TABLE 61 wear resistance weight loss by wear No. (mg/100000
rot.) 8001a 1.4 8002a 1.1 8003a 0.9 8004a 1.2 8005a 1.8 8006a 1.3
8007a 1.5 8015a 1.5 8016a 0.9 8017a 1.4 8018a 0.9 8019a 1 8020a
1.5
[0169]
62 TABLE 63 wear resistance weight loss by wear No. (mg/100000
rot.) 8043a 1.6 8044a 1.2 8045a 1 8046a 2 8047a 1.6 8048a 1.7 8049a
1.3 8050a 1.5 8051a 1 8052a 1.5 8053a 1.3 8054a 1.2 8055a 0.7 8056a
0.9
[0170]
63 TABLE 62 wear resistance weight loss by wear No. (mg/100000
rot.) 8021a 1
[0171]
64 TABLE 64 wear resistance weight loss by wear No. (mg/100000
rot.) 8064a 1.7 8065a 2 8066a 1.4 8067a 1.5 8068a 1.2 8069a 0.9
8070a 1
[0172]
65 TABLE 66 wear resistance weight loss by wear No. (mg/100000
rot.) 8101a 1.4 8102a 1.3 8103a 0.8 8104a 0.8 8105a 0.7 8113a 0.9
8114a 1.2 8115a 1.1 8116a 1.4 8117a 1.1 8118a 0.9 8119a 1.1
[0173]
66 TABLE 65 wear resistance weight loss by wear No. (mg/100000
rot.) 8092a 1.6 8093a 2.1 8094a 1.5 8095a 1.9 8096a 1.5 8097a 1.5
8098a 1.4 8099a 1.1 8100a 0.9
[0174]
67 TABLE 67 wear resistance weight loss by wear No. (mg/100000
rot.) 8141a 1.4 8142a 1.8 8143a 1.6 8144a 1.9 8145a 1.1 8146a 1.2
8147a 1.4
[0175]
68 TABLE 68 wear resistance weight loss by wear No. (mg/100000
rot.) 14001a 500 14002a 620 14003a 520 14004a 450 14005a 25
* * * * *