Note : Les descriptions sont présentées dans la langue officielle dans laquelle elles ont été soumises.
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TITLE OF THE INVENTION
FREE-CUTTING COPPER ALLOYS
BACKGROUND OF THE INVENTION
1. Field of The Invention
The present invention relates to free-cutting copper alloys.
2. Prior Art
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 H32S0-C3604 and C3771. Those alloys are enhanced
in machinability with the addition of 1.0 to 6.0 percent, by weight, of lead
so as to
give industrially satisfactory results as easy-to-work copper alloys. Because
of
their excellent machinability, those lead-containing copper alloys have been
an
important basic material for a variety of articles such as city water faucets
and
water supply/drainage metal fittings and valves.
In those conventional free-cutting copper alloys, lead does not form a solid
solution in the matrix but disperses in granular form, thereby improving the
machinability of those alloys. To produce the desired results, lead has to be
added in as much as .2.0 or more percent by weight. If the addition of lead is
less
than 1.0 percent by weight, chippings will be spiral in form, as (D) in Fig.
1.
Spiral chippings cause various troubles such as, for example, tangling with
the
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tool. If, on the other hand, the content of lead is 1.0 or more percent by
weight
and not larger than 2.0 percent by weight, the cut surface will be rough,
though
that will produce some results such as reduction of cutting resistance. It is
usual,
therefore, that lead is added to an extent of not less than 2.0 percent by
weight.
Some expanded copper alloys in which a high degree of cutting property is
required are mixed with some 3.0 or more percent by weight of lead. Further,
some bronze castings have a lead content of as much as some 5.0 percent, by
weight. The alloy having the JIS designation H 5111 BC6, for example, contains
some 5.0 percent by weight of lead.
However, the application of those lead-mixed alloys has been greatly
limited in recent years, because lead contained therein is harmful to humans
as
an environment pollutant. That is, the lead-containing alloys pose a threat to
human health and environmental hygiene because lead finds its way into
metallic
vapor that generates in the steps of processing those alloys at high
temperatures
such as melting and casting. There is also a danger that lead contained in the
water system metal fittings, valves, and so on made of those alloys will
dissolve
out into drinking water.
For these reasons, the United States and other advanced nations have
been moving in recent years to tighten the standards for lead-containing
copper
alloys to drastically limit the permissible level of lead in copper alloys. In
Japan,
too, the use of lead-containing alloys has been increasingly restricted, and
there
has been a growing call for the development of free-cutting copper alloys with
a
low lead content.
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SUMMARY OF THE INVENTION
It is an object of the present invention to provide a free-cutting copper
alloy
that contains an extremely small amount (0.02 ~ 0.4 percent, by weight) of the
machinability-improving element lead, yet which is quite excellent in
machinability,
that can be used as safe substitute for the conventional easy-to-cut copper
alloys
that have a large lead content, and that presents no environmental hygienic
problems while permitting the recycling of chippings, thus providing a timely
answer
to the mounting call for the restriction of lead-containing products.
It is an another object of the present invention to provide a free-cutting
copper alloy that has high corrosion resistance coupled with excellent
machinability
and is suitable as basic material for cutting works, forgings, castings and
others,
thus having a very high practical value. The cutting works, forgings,
castings, and
so on, including city water faucets, water supply/drainage metal fittings,
valves,
stems, hot water supply pipe fittings, shaft and heat exchanger parts.
It is yet another object of the present invention to provide a free-cutting
copper alloy, with a high strength and wear resistance coupled with an easy-to-
cut
property, that 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, and which therefore is of great practical value.
It is a further object of the present invention to provide a free-cutting
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copper alloy with a excellent high-temperature oxidation resistance combined
with an
easy-to-cut property, which is suitable as basic material for the manufacture
of cutting
works, forgings, castings, and other uses where a high thermal oxidation
resistance is
essential, e.g. nozzles for kerosene oil and gas heaters, burner heads, and
gas nozzles for
hot-water dispensers, and which therefore has great practical value.
Accordingly, in one aspect the present invention resides in a free-cutting
copper
alloy for use as a free-cutting basic material for cutting works, forgings and
castings;
said alloy comprising 69 to 79 percent, by weight, of copper; 2.0 to 4.0
percent, by
weight, of silicon; 0.02 to 0.4 percent, by weight, of lead; and the remaining
percent, by
weight, of zinc; and wherein the metal structure of the free-cutting copper
alloy includes
a precipitated 'y phase.
In a further aspect, the present invention resides in a free-cutting copper
alloy
which comprises 69 to 79 percent, by weight, of copper; 2.0 to 4.0 percent, by
weight,
of silicon; 0.02 to 0.4 percent, by weight, of lead; 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; and wherein the metal structure of the free-cutting copper alloy
includes a
precipitated y phase.
In yet another aspect, the present invention resides in a free-cutting copper
alloy
for use as a free-cutting basic material for cutting works, forgings and
castings, said alloy
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comprising 70 to 80 percent, by weight, of copper; 1.8 to 3.5 percent, by
weight, of
silicon; 0.02 to 0.4 percent, by weight, of lead; at lest 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; and the remaining percent, by
weight, of zinc;
and wherein the metal structure of the free-cutting copper alloy has a
precipitated 'y
phase.
The objects of the present inventions are achieved by provision of the
following
copper alloys:
1. A free-cutting copper alloy with an excellent easy-to-cut feature which is
composed of 69 to 79 percent, by weight, of copper, 2.0 to 4.0 percent, by
weight, of
silicon, 0.02 to 0.4 percent, by weight, of lead and the remaining percent, by
weight, of
zinc. For purpose of simplicity, this copper alloy will be hereinafter called
the "first
invention alloy."
Lead forms no solid solution in the matrix but disperses in a granular form to
improve the machinability. Silicon raises the easy-to-cut property by
producing a gamma
phase (in some cases, a kappa phase) in the structure of metal. That way, both
are the
same in that they are effective in improving the machinability, though they
are quite
different in contribution to the properties of the alloy. On the basis of that
recognition,
silicon is added to the first invention alloy so as to bring about a high
level of
machinability meeting industrial requirements while making it possible to
greatly reduce
the lead content. That is, the first invention alloy is improved in
machinability through
formation of a gamma phase with the addition of silicon.
The addition of less than 2.0 percent, by weight, of silicon can not form a
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gamma phase sufficient enough to secure an industrially satisfactory
machinability.
With the increase 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 go
up in proportion. The problem is, however, that silicon is high in melting
point and
low in specific gravity and also liable to oxidize. If unmixed silicon is fed
into the
furnace in the melting step, silicon will float on the molten metal and is
oxidized into
oxides of silicon (silicon oxide), hampering the production of a silicon-
containing
copper alloy. In producing the 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 or plateau of machinability
improvement, that is, 4.0 percent by weight. An experiment showed that when
silicon is added in the amount of 2.0 to 4.0 percent by weight, it is
desirable to hold
the content of copper at 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 2.0 to 4.0 percent, by weight, of silicon respectively. The
addition of
silicon 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 de-zinc-ing
corrosion
resistance will be improved to some extent.
The addition of lead is set at 0.02 to 0.4 percent by weight for this reason.
In
the first invention alloy, a sufficient level of machinability is obtained by
adding
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silicon that has the aforesaid effect even if the addition of lead is reduced.
Yet,
lead has to be added in an amount not smaller than 0.02 percent by weight if
the
alloy is to be superior to the conventional free-cutting copper alloy in
machinability, while the addition of lead in an amount exceeding 0.4 percent
by
weight would have adverse effects, resulting in a rough surface condition,
poor
hot workability such as poor forging behavior, and low cold ductility.
Meanwhile,
it is expected that such a small content of not higher than 0.4 percent by
weight
will be able to clear the lead-related regulations however strictly they are
to be
stipulated in the advanced nations including Japan in the future. For that
reason,
the addition range of lead is set at 0.02 to 0.4 percent by weight in the
first and
also second to eleventh invention alloys which will be described later.
2. Another embodiment of the present invention is a free-cutting
copper alloy also with an excellent easy-to-cut feature which is composed of
69 to
79 percent, by weight, of copper; 2.0 to 4.0 percent, by weight, of silicon;
0.02 to
0.4 percent, by weight, of lead; one additional 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. This second copper alloy will be hereinafter called the
"second
invention alloy."
That is, the second invention alloy is composed of the first invention alloy
and, in addition, 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.
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Bismuth, tellurium, and selenium, as with lead, do not form a solid solution
with the matrix but disperse in granular form to enhance machinability. That
makes up for the reduction of the lead content. The addition of any one of
those
elements along with silicon and lead could further improve the machinability
beyond the level obtained from the addition of silicon and lead. From this
finding,
the second invention alloy was developed, in which one element selected from
among bismuth, tellurium, and selenium is mixed. The addition of bismuth,
tellurium, or selenium as well as silicon and lead can make the copper alloy
so
machinable that complicated forms can be freely cut out at a high speed. But
no
improvement in machinability can be realized from the addition of bismuth,
tellurium, or selenium in an amount of 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 addition beyond that level does not pay off
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 a problem similar to that of lead, a very small addition of less
than
0.4 percent by weight is negligible and would present no particular problems.
From those 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.
In this regard, it is desired to keep the combined content of lead and
bismuth,
tellurium, or selenium to not higher than 0.4 percent by weight. That is
because
if the combined content exceeds 0.4 percent by weight, if slightly, then there
will
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begin a deterioration in hot workability and cold ductility and also there is
fear
that the form of chippings will change from (B) to (A) in Fig. 1. But the
addition
of bismuth, tellurium or selenium, which improves the machinability of the
copper
alloy though a mechanism different from that of silicon as mentioned above,
S would not affect the proper contents of copper and silicon. For this reason,
the
contents of copper and silicon in the second invention alloy are set at the
same
level as those in the first invention alloy.
3. Another embodiment of the present invention is a free-cutting
copper alloy, also with an excellent easy-to-cut feature, which is composed of
70
to 80 percent, by weight, of copper; 1.8 to 3.5 percent, by weight, of
silicon; 0.02
to 0.4 percent, by weight, of lead; 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; and the remaining percent, by
weight, of zinc. This third copper alloy will be hereinafter called the "third
invention alloy."
Tin works the same way as silicon. That is, if tin is added, a gamma phase
will be formed and the machinability of the Cu-Zn alloy will be improved. For
example, the addition of tin in the 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 present. Therefore, the addition
of tin
to the Cu-Si-Zn alloy could 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 the amount of 1.0 or more percent by weight and the
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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
aH insHy~~c;e~rt
of tin in an amount less than 1.0 percent by weight, on the other hand~Re--
gamma phase will be formed. If the addition is 0.3 or more percent by weight,
then tin will be effective in uniformly dispersing the gamma phase formed by
silicon. Through that effect of dispersing the gamma phase, too, the
machinability is improved. In other words, the addition of tin in an amount
not
smaller than 0.3 percent by weight improves the machinability.
Aluminum is, too, effective in facilitating the formation of the gamma
phase. The addition of aluminum together with 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 keeping down the specific
gravity. If the machinability is to be improved at all, aluminum will have to
be
added in an amount of at least 1.0 percent by weight. But the addition of more
than 3.5 percent by weight could not produce the proportional results.
Instead,
that could lower the ductility as is the case with tin.
As to phosphorus, it has no property of forming the gamma phase as tin
and aluminum. But phosphorus works to uniformly disperse and distribute the
gamma phase formed as a result of the addition of silicon alone or with tin or
aluminum or both of them. That way, the machinability improvement through the
formation of gamma phase is further enhanced. In addition to dispersing the
gamma phase, phosphorus helps refine the crystal grains in the alpha phase in
the matrix, improving hot workability and also strength and resistance to
stress
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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 will be obtained.
Instead,
there would be a decrease in hot forging property and extrudability.
In consideration of those observations, the third invention alloy is improved
in machinability by adding to the Cu-Si-Pb-Zn alloy (first invention alloy) at
least
one additional 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.
Tin, aluminum, and phosphorus act to improve 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 to which silicon is added along with tin, aluminum, or
phosphorus,
thus the addition of silicon is smaller than that in the second invention
alloy to
which is added bismuth, tellurium, or selenium, which replaces silicon of the
first
invention in improving machinability. That is, those elements bismuth,
tellurium,
and selenium contribute to improving the machinability, not acting on the
gamma
phase but 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, aluminum,
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,
adding tin,
aluminum, or phosphorus together with silicon will saturate the effect of
silicon in
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improving the machinability, 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 addition of
silicon and also
the addition of tin, aluminum, or phosphorus, the content range of copper in
this
third invention alloy is slightly raised from the level in the second
invention alloy and
copper is properly set at 70 to 80 percent by weight.
4. A free-cutting copper alloy also with an excellent easy-to-cut feature
which is composed of 70 to 80 percent, by weight, of copper; 1.8 to 3.5
percent, by
weight, of silicon; 0.02 to 0.4 percent, by weight, of lead; 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; 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. This fourth copper alloy will
be
hereinafter called the "fourth invention alloy."
The fourth invention alloy has any one 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 mixing those additional elements and setting
those
amounts to be added are the same as given for the second invention alloy.
5. A free-cutting copper alloy with an excellent easy-to-cut feature
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and with a 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; 0.02 to 0.4
percent,
by weight, of lead; at least one element selected from among 0.3 to 3.5
percent,
by weight, of tin, 0.02 to 0.25 percent, by weight, of phosphorus, 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. This fifth copper alloy will be
hereinafter called the "fifth invention alloy."
The fifth invention alloy has, in addition to the first invention alloy, at
least
one element selected from among 0.3 to 3.5 percent, by weight, of tin, 0.02 to
0.25 percent, by weight, of phosphorus, 0.02 to 0.15 percent, by weight, of
antimony, and 0.02 to 0.15 percent, by weight, of arsenic.
Tin is effective in improving not only the machinability but also corrosion
resistance properties (de-zinc-ification corrosion resistance) and
forgeability. 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 the inclusion 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 the 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 increased amount of tin. Thus tin in excess of 3.5 percent would be
uneconomical.
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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
(de-zinc-iflcation corrosion resistance), forgeability, stress corrosion
cracking
resistance, and mechanical strength. The fifth invention alloy is thus
improved in
corrosion resistance and other properties through the action 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, could produce beneficial
results.
But the addition in more than 0.25 percent by weight would not be so effective
as
hoped from the quantity added. Rather, that would reduce the hot forgeability
and extrudability.
As with phosphorus, antimony and arsenic in a very small quantity - 0.02
or more percent by weight - are effective in improving the de-zinc-ification
corrosion resistance and other properties. But their addition exceeding 0.15
percent by weight would not produce results in proportion to the excess
quantity
added. Rather, it would affect the hot forgeability and extrudability as does
phosphorus applied in excessive amounts.
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, phosphorus, antimony, and arsenic (which
improve corrosion resistance) 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
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as in the first invention alloy in which any other machinability improver than
silicon
and a small amount of lead is not added - because tin and phosphorus work
mainly
as corrosion resistance improvers like antimony and arsenic.
6. A free-cutting copper alloy also with an excellent easy-to-cut feature
and with a 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; 0.02 to 0.4
percent, by
weight, of lead; at least one element selected from among 0.3 to 3.5 percent,
by
weight, of tin, 0.02 to 0.25 percent, by weight, of phosphorus, 0.02 to 0.15
percent,
by weight, of antimony, and 0.2 to 0.15 percent, by weight, of arsenic; one
element
selected from among 0.02 to 0.4, 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. This sixth copper alloy will be
hereinafter
called the "sixth invention alloy."
The sixth invention alloy has any 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 is improved by adding in addition to
silicon and
lead, any 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 adding at least one selected from among tin, phosphorus, antimony
and
arsenic as in the fifth invention alloy. Therefore, the additions of copper,
silicon,
lead, bismuth, tellurium and selenium are set at the same levels as those in
the
second invention alloy, while the additions of tin, phosphorus, antimony, and
arsenic are
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adjusted to those in the fifth invention alloy.
7. A free-cutting copper alloy also with an excellent easy-to-cut
feature and with an excellent high strength feature 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; 0.02 to 0.4 percent, by weight, of lead; at least one
element
selected from among 0.3 to 3.0 percent, by weight, of tin, 0.2 to 2.5 percent,
by
weight, of aluminum, 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. The seventh copper alloy will be hereinafter
called
the "seventh invention alloy."
Manganese and nickel combine with silicon to form intermetallic
compounds represented by MnxSiY or NiXSiy, which are evenly precipitated in
the
matrix, thereby raising the wear resistance and strength. Therefore, the
addition
of manganese and nickel or either of the two would improve the high strength
feature and wear resistance. Such effects will be exhibited if manganese and
nickel are added in an amount not smaller 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.
It is also noted that tin, aluminum, and phosphorus help to reinforce the
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Alpha phase in the matrix, thereby improving the machinability. Tin and
phosphorus disperse the alpha and gamma phases, by which the strength, wear
resistance, and also machinability are improved. Tin in an amount of 0.3 or
more
percent by weight is effective in improving the strength and machinability.
But if the
addition exceeds 3.0 percent by weight, the 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
feature and wear resistance in the seventh invention alloy, and also to
enhance the
machinability. Aluminum also contributes to improving the wear resistance and
exhibits its effect of reinforcing the matrix when added in an amount of 0.2
or more
percent by weight. But if the addition exceeds 2.5 percent by weight, there
will be a
decrease in ductility. Therefore, the addition of aluminum is set at 0.2 to
2.5 in
consideration of improvement of machinability. Also, 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 the hot workability and also the
strength and wear resistance. Furthermore, it is very effective in improving
the flow
of molten metal in casting. Such results will be produced when phosphorus is
added in an amount of 0.02 to 0.25 percent by weight. The content of copper is
set
at 62 to 78 percent by weight in the light of the addition of silicon and the
property
of manganese and nickel of combining with silicon.
8. A free-cutting copper alloy also with an excellent easy-to-cut feature
and with an excellent high-temperature oxidation resistance which comprises 69
to
79 percent, by weight, of copper, 2.0 to 4.0 percent, by weight,
16
CA 02303512 2000-03-14
of silicon, 0.02 to 0.4 percent, by weight, of lead, 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. The eighth copper alloy will be
hereinafter
called the "eighth invention alloy."
Aluminum is an element which improves strength, machinability, wear
resistance, and also high-temperature oxidation resistance. Silicon, too, has
a
property of enhancing machinability, strength, wear resistance, resistance to
stress corrosion cracking, and also high-temperature oxidation resistance.
Aluminum works to raise the high-temperature oxidation resistance when it is
used together with silicon in amounts not smaller than 0.1 percent by weight.
But
even if the addition of aluminum increases beyond 1.5 percent by weight, no
proportional results can be expected. For this reason, the addition of
aluminum is
set at 0.1 to 1.5 percent by weight.
Phosphorus is added to enhance the flow of molten metal in casting.
Phosphorus also works to improve the aforesaid machinability, de-zinc-
ification
corrosion resistance, and also high-temperature oxidation resistance, in
addition
to the flow of molten metal. Those effects are exhibited when phosphorus is
added in amounts not smaller than 0.02 percent by weight. But even if
phosphorus is used in amounts greater than 0.25 percent by weight, it will not
result in a proportional increase in effect, rather weakening the alloy. Based
upon
this consideration, phosphorus is added to within a range of 0.02 to 0.25
percent
by weight.
While silicon is added to improve machinability as mentioned above, it is
also capable of improving the flow of molten metal like phosphorus. The effect
of
17
CA 02303512 2000-03-14
silicon in improving the flow of molten metal is exhibited when it is added in
an
amount not small than 2.0 percent by weight. The range of the addition for
flow
improvement overlaps that for improvement of the machinability. These taken
into consideration, the addition of silicon is set to 2.0 to 4.0 percent by
weight.
S
9. A free-cutting copper alloy also with excellent easy-to-cut feature
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;
0.02 to 0.4 percent, by weight, of lead; 0.1 to 1.5 percent, by weight, of
aluminum; 0.02 to 0.25 percent, by weight, of phosphorus; 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. The ninth copper alloy will be
hereinafter
called the "ninth invention alloy."
The ninth invention alloy contains 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 eighth invention alloy. While a high-temperature oxidation resistance as
good
as in the eighth invention alloy is secured, the machinability is further
improved
by adding one element selected from among bismuth and other elements which
are as effective as lead in raising the machinability,
10. A free-cutting copper alloy also with excellent easy-to-cut feature
and a good high-temperature oxidation resistance which is composed of 69 to 79
18
CA 02303512 2000-03-14
percent, by weight, of copper; 2.0 to 4.0 percent, by weight, of silicon; 0.02
to
0.4 percent, by weight, of lead; 0.1 to 1.5 percent, by weight, of aluminum;
0.02
to 0.25 percent, by weight, of phosphorus; at least one 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. The tenth copper
alloy
will be hereinafter called the "tenth invention alloy."
Chromium and titanium are intended for improving the high-temperature
oxidation resistance of the alloy. 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 no less than 0.02 percent by
weight,
whether they are added alone or in combination. The saturation point is 0.4
percent by weight. For consideration of such observations, the tenth invention
alloy has 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 eighth invention alloy and thus further improved over the
eighth invention alloy with regard to high-temperature oxidation resistance.
11. A free-cutting copper alloy also with excellent easy-to-cut feature
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; 0.02
to
0.4 percent, by weight, of lead; 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; one element selected from among 0.02 to 0.4 percent, by
19
CA 02303512 2000-03-14
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.
The eleventh copper alloy will be hereinafter called the "eleventh invention
alloy."
The eleventh invention alloy contains any 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 tenth invention alloy. While as high a high-temperature
oxidation resistance as in the tenth invention alloy is secured, the eleventh
invention alloy is further improved in machinability by adding one element
selected from among bismuth and these other elements, which are as effective
as
lead in improving machinability.
12. A free-cutting copper alloy with further improved easy-to-cut
properties, obtained by subjecting any one of the preceding respective
invention
alloys to a heat treatment for 30 minutes to 5 hours at 400 to 600°C.
The twelfth
copper alloy will be hereinafter called the "twelfth invention alloy."
The first to eleventh invention alloys contain machinability improving
elements such as silicon and have an excellent machinability because of the
addition of such elements. The effect of those machinability improving
elements
could be further enhanced by heat treatment. For example, the first to
eleventh
invention alloys which are high in copper content with gamma phase in small
quantities and kappa phase in large quantities undergo a change in phase from
the kappa phase to the gamma phase in a heat treatment. As a result, the
gamma phase is finely dispersed and precipitated, and the machinability is
CA 02303512 2003-03-18
improved. In the manufacturing process of castings, expanded metals and hot
forgings in
practice, 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, with the first to eleventh
invention alloys, the
alloys with a low content of copper in particular are rather low in the
content of the gamma phase
and contain beta phase. In a heat treatment, the beta phase changes into gamma
phase, and the
gamma phase is finely dispersed and precipitated, whereby the machinability is
improved.
But a heat treatment temperature at less than 400°C is not economical
and practical in
any case, because the aforesaid phase change will proceed slowly and much time
will be needed.
At temperatures over 600°C, on the other hand, the kappa phase will
grow or the beta phase will
appear, bringing about no improvement in machinability. From the practical
viewpoint,
therefore, it is desired to perform the heat treatment for 30 minutes to 5
hours at 400 to 600°C.
Accordingly, in one aspect, the present invention resides in a free-cutting
copper alloy
which comprises 69 to 79 percent, by weight, of copper; 2.0 to 4.0 percent, by
weight, of silicon;
0.02 to 0.4 percent, by weight, of lead; and the remaining percent, by weight,
of zinc; and
wherein the metal structure of the free cutting copper alloy has at least one
phase selected from
the y phase and the x phase.
In a further aspect, the present invention resides in a free-cutting copper
alloy which
comprises 69 to 79 percent, by weight, of copper; 2.0 to 4.0 percent, by
weight, of silicon; 0.02
to 0.4 percent, by weight, of lead; 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; and
wherein the metal
structure of the free cutting copper alloy has at least one phase selected
from the y phase and the
x phase.
21
CA 02303512 2003-03-18
In a further aspect, the present invention resides in A free-cutting copper
alloy which
comprises 70 to 80 percent, by weight, of copper; 1.8 to 3.5 percent, by
weight, of silicon; 0.02
to 0.4 percent, by weight, of lead; at lest 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; and the remaining percent, by weight, of zinc; and wherein the
metal structure of
the free cutting copper alloy has at least one phase selected from the y phase
and the x phase.
BRIEF DESCRIPTION OF THE DRAWING
Fig. 1 shows perspective views of cuttings formed in cutting a round bar of
copper alloy by lathe.
DETAILED DESCRIPTION OF PREFERRED EMBODIMENTS
21a
CA 02303512 2000-03-14
Example 1
As the first series of examples of the present invention, cylindrical ingots
with compositions given in Tables 1 to 15, 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°C to produce the following test pieces: first invention alloys
Nos. 1001 to
1007, second invention alloys Nos. 2001 to 2006, third invention alloys Nos.
3001
to 3010, fourth invention alloys Nos. 4001 to 4021, fifth invention alloys
Nos.
5001 to 5020, sixth invention alloys Nos. 6001 to 6045, seventh invention
alloys
Nos. 7001 to 7029, eighth invention alloys Nos. 8001 to 8008, ninth invention
alloys Nos. 9001 to 9006, tenth invention alloys Nos. 10001 to 10008, and
eleventh invention alloys Nos. 11001 to 11011. Also, cylindrical ingots with
the
compositions given in Table 16, 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°C
to produce the following test pieces: twelfth invention alloys Nos. 12001 to
12004. That is, No. 12001 is an alloy test piece obtained by heat-treating an
extruded test piece with the same composition as first invention alloy No.
1006 for
30 minutes at 580°C. No. 12002 is an alloy test piece obtained by heat-
treating
an extruded test piece with the same composition as No. 1006 for two hours at
450°C. No. 12003 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. 12001 - for 30 minutes at 580°C. No. 12004
is an
alloy test piece obtained by heat-treating an extruded test piece with the
same
composition as No. 1007 under the same conditions as for No. 12002 - for two
hours at 450°C.
22
CA 02303512 2000-03-14
As comparative examples, cylindrical ingots with the compositions as shown
in Table 17, 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°C to obtain
the
following round extruded test pieces: Nos. 13001 to 13006 (hereinafter
referred to
as the "conventional alloys"). No. 13001 corresponds to the alloy "JIS C
3604," No.
13002 to the alloy "CDA C 36000," No. 13003 to the alloy "JIS C 3771", and No.
13004 to the alloy "CDA C 69800." No. 13005 corresponds to the alloy "JIS C
6191." This aluminum bronze is the most excellent of the expanded copper
alloys
under the JIS designations with regard to strength and wear resistance. No.
13006
corresponds to the naval brass alloy "JIS C 4622" and is the most excellent of
the
expanded copper alloys under the JIS designations with regard to corrosion
resistance.
To study the machinability of the first to twelfth invention alloys in
comparison with the conventional alloys, cutting tests were carried out. In
the tests,
evaluations were made on the basis of cutting force, condition of chippings,
and cut
surface condition. The tests were conducted in this manner: The extruded test
pieces thus obtained were cut on the circumferential surface by a lathe
provided
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, and 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. The signals were then
converted into the cutting resistance. It is noted that while, to be perfectly
exact,
the amount of the cutting
23
CA 02303512 2000-03-14
resistance should be judged by three component forces - cutting force, feed
force,
and thrust force, the judgement 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 18 to Table 33.
S 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
18 to Table 33. In this regard, the chippings 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. Chippings in the form of a spiral arc
from one with a half winding to one with two windings as shown in (C) in Fig.
1
do not cause such serous trouble as chippings 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, chippings in the form of a fine
needle
as (A) in Fig. 1 or in the form of arc shaped pieces as (B) in Fig. 1 will not
present
such problems as mentioned above, are not as bulky as the chippings in (C) and
(D), and are easy to process. But fine chippings as (A) still could creep in
on the
slide table 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. Those factors taken into account, when judging
machinability,
the alloy with the chippings in (B) is the best, and the second best is that
with the
chippings in (A). Those with the chippings in (C) and (D) are not good. In
Table
18 to Table 33, the alloys with the chippings shown in (B), (A), (C), and (D)
are
24
CA 02303512 2000-03-14
indicated by the symbols "o", "o", "D", and "x" respectively.
In addition, the surface condition of the cut metal surface was checked
after cutting work. The results are shown in Table 18 to Table 33. 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 <_ Rmax < 15
microns are judged as industrially acceptable while those with Rmax >_ 15
microns
are taken as poor in machinability. In Table 18 to Table 33, the alloys with
Rmax
< 10 microns are marked "o", those with 10 microns _< Rmax < 15 microns are
indicated by "D", and those with Rmax >_ 15 microns are indicated by "x".
As is evident from the results of the cutting tests shown in Table 18 to
Table 33, the following invention alloys are all equal to the conventional
lead-
containing alloys Nos. 13001 to 13003 in machinability: first invention alloys
Nos.
1001 to 1007, second invention alloys Nos. 2001 to 2006, third invention
alloys
Nos. 3001 to 3010, fourth invention alloys Nos. 4001 to 4021, fifth invention
alloys Nos. 5001 to 5020, sixth invention alloys Nos. 6001 to 6045, seventh
invention alloys Nos. 7001 to 7029, eighth invention alloys Nos. 8001 to 8008,
ninth invention alloys Nos. 9001 to 9006, tenth invention alloys Nos. 10001 to
10008, eleventh invention alloys Nos. 11001 to 11011, and twelfth invention
alloys Nos. 12001 to 12004. Especially with regard to the form of chippings,
those invention alloys compare favorably not only with conventional alloys
Nos.
13004 to 13006 having a lead content of not higher than 0.1 percent by weight
CA 02303512 2000-03-14
but also Nos. 13001 to 13003 which contain large quantities of lead. Also to
be
noted is that the twelfth invention alloys Nos. 12001 to 12004, which are
obtained
by heat-treating the first invention alloys Nos. 1006 and 1007, are improved
over
the first invention alloys in machinability. It is understood that a proper
heat
treatment could further enhance machinability of the first to eleventh
invention
alloys, depending upon the alloy compositions and other conditions.
In another series of tests, the first to twelfth invention alloys were
examined in comparison with conventional alloys in hot workability and
mechanical properties. For the purpose, hot compression and tensile tests were
conducted in the following manner.
First, two test pieces, the first and second test pieces, in the same shape,
mm in outside diameter and 25 mm in length, were cut out of each extruded
test piece obtained as described above. In hot compression tests, the first
test
15 piece was held for 30 minutes at 700°C, and then compressed at the
compression
rate of 70 percent in the axial direction to reduce the length from 25 mm to
7.5
mm. The surface condition after the compression (700°C deformability)
was
visually evaluated. The results are given in Table 18 to Table 33. The
evaluation
of deformability was made by visually checking for cracks on the side of the
test
piece. In Table 18 to Table 33, the test pieces with no cracks found are
marked
"o", those with small cracks are indicated by "D", and those with large cracks
are
represented by the symbol "x".
The tensile strength, N/mm2, and elongation, %, of the second test pieces
was determined by the commonly practiced test method.
26
CA 02303512 2000-03-14
As the test results of the hot compression and tensile tests in Table 18 to
Table 33 indicate, it was confirmed that the first to twelfth invention alloys
are
equal to or superior to the conventional alloys Nos. 13001 to 13004 and No.
13006 in hot workability and mechanical properties and are suitable for
industrial
use. The seventh invention alloys in particular have the same level of
mechanical
properties as the conventional alloy No. 13005, i.e. the aluminum bronze which
is
the most excellent in strength of the expanded copper alloys under the JIS
designations, and thus clearly have a prominent high strength feature.
Furthermore, the first to six and eighth to twelfth invention alloys were put
to de-zinc-ification corrosion and stress corrosion cracking tests in
accordance
with the test methods specified under "ISO 6509" and "JIS H 3250",
respectively,
to examine the corrosion resistance and resistance to stress corrosion
cracking in
comparison with conventional alloys.
In the de-zinc-ing corrosion test by the "ISO 6509" method, the test piece
taken from each extruded test piece was imbedded laid in a phenolic resin
material in such a way that the exposed test piece surface is perpendicular to
the
extrusion direction of the extruded test piece. The surface of the test piece
was
polished with emery paper No. 1200, and then ultrasonic-washed in pure water
and dried. The test piece thus prepared was dipped in a 12.7 g/1 aqueous
solution of cupric chloride dehydrate (CuCl2 ~ 2 H20) 1.0% and left standing
for 24
hours at 75°C. The test piece was taken out of the aqueous solution and
the
maximum depth of de-zinc-ing corrosion was determined. The measurements of
the maximum de-zinc-ification corrosion depth are given in Table 18 to Table
25
27
r
CA 02303512 2000-03-14
and Table 28 to Table 33.
As is clear from the results of de-zinc-ification corrosion tests shown in
Table 18 to Table 25 and Table 28 to Table 33, the first to fourth invention
alloys
and the eighth to twelfth invention alloys are excellent in corrosion
resistance
in comparison with the conventional alloys Nos. 13001 to 13003 which contain
large amounts of lead. And it was confirmed that especially the fifth and
sixth
invention alloys which whose improvement in both machinability and corrosion
resistance has been intended are very high in corrosion resistance in
comparison
with the conventional alloy No. 13006, a naval brass which is the most
resistant to
corrosion of all the expanded alloys under the JIS designations.
In the stress corrosion cracking tests in accordance with the test method
described in ")IS H 3250," a 150-mm-long test piece was cut out from each
extruded material. The test piece was bent with the center placed on an arc-
shaped tester with a radius of 40 mm in such a way that one end forms an angle
of 45 degrees with respect to the other end. The test piece 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). To be exact, the test piece was held some 80
mm above the surface of aqueous ammonia in the desiccator: After the test
piece
was left standing in the ammonia environment for 2 hours, 8 hours, and 24
hours,
the test piece was taken out from the desiccator, washed in sulfuric acid
solution
10% and examined for cracks under 10X magnifications. The results are given in
Table 18 to Table 25 and Table 28 to Table 33. In those tables, the alloys
which
developed clear cracks when held in the ammonia environment for two hours are
28
CA 02303512 2000-03-14
marked "xx." The test pieces which had no cracks at 2 hours but were found
clearly
cracked in 8 hours are indicated by "x." The test pieces which had no cracks
at 8
hours, but were found to clearly have cracks in 24 hours are identified by the
symbol "o". The test pieces which were found to have no cracks at all in 24
hours
are indicated by the symbol "o."
As is indicated by the results of the stress corrosion cracking test given in
Table 18 to Table 25 and Table 28 to Table 33, it was confirmed that not only
the
fifth and sixth invention alloys whose improvement in both machinability and
corrosion resistance has been intended but also the first to fourth invention
alloys
and the eighth to twelfth alloys in which nothing particular was done to
improve
corrosion resistance were both equal to the conventional alloy No. 13005, an
aluminum bronze containing no zinc, in stress corrosion cracking resistance.
Those invention alloys were superior in stress corrosion cracking resistance
to the
conventional naval brass alloy No. 13006, the best in corrosion resistance of
all the
expanded copper alloys under the JIS designations.
In addition, oxidation tests were carried out to study the high-temperature
oxidation resistance of the eighth to eleventh invention alloys in comparison
with
conventional alloys.
Test pieces 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 were prepared from each of the
following extruded materials: No. 8001 to No. 8008, No. 9001 to No. 9006, No.
10001 to No. 10008, No. 11001 to No. 11011, and No. 13001 to No. 13006. Each
test piece was then weighed to measure the weight before oxidation. After
29
CA 02303512 2000-03-14
that, the test piece was placed in a porcelain crucible and held in an
electric
furnace maintained at 500°C. At the passage of 100 hours, the test
piece was
taken out of the electric furnace and was weighed to measure the weight after
oxidation. From the measurements before and after oxidation was calculated the
increase in weight by oxidation. It is understood that the increase by
oxidation is
the amount, mg, of increase in weight by oxidation per 10 cm2 of the surface
area
of the test piece, and is calculated by the equation: increase in weight by
oxidation, mg/10 cm2 = (weight, mg, after oxidation - weight, mg, before
oxidation) x (10 cmZ / surface area, cm2, of test piece). The weight of each
test
piece increased after oxidation. The increase was brought about by high-
temperature oxidation. Subjected to a high temperature, oxygen combines with
copper, zinc, and silicon to form Cu20, ZnO, Si02, respectively. That is,
oxygen
adds to the weight. It can be said, therefore, that the alloys with a smaller
weight increase due to oxidation are better in high-temperature oxidation
resistance. The results obtained are shown in Table 28 to Table 31 and Table
33.
As is evident from the test results shown in Table 23 to Table 31 and Table
33, the eighth to eleventh invention alloys are equal, in regard to weight
increase
by oxidation, to the conventional alloy No. 13005, an aluminum bronze ranking
high in resistance to high-temperature oxidation among the expanded copper
alloys under the )IS designations, and are far smaller than any other
conventional
copper alloy. Thus, it was confirmed that the eighth to eleventh invention
alloys
are very excellent in machinability as well as resistance to high-temperature
oxidation.
CA 02303512 2000-03-14
Example 2
As the second series of examples of the present invention, circular
cylindrical ingots with compositions given in Tables 9 to 11, 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°C to produce seventh invention alloys
Nos. 7001a
to 7029a. In parallel, circular cylindrical ingots with compositions given in
Table
17, 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°C to produce the
following
alloy test pieces: Nos. 13001a to 13006a as second comparative examples
(hereinafter referred to as the "conventional alloys). It is noted that the
alloys
Nos. 7001a to 7029a and Nos. 13001a to 13006a are identical in composition
with
the aforesaid copper alloys Nos. 7001 to 7029 and Nos. 13001 to No. 13006,
respectively.
Seventh invention alloys Nos. 7001a to 7029a were subjected to wear
resistance tests in comparison with conventional alloys Nos. 13001a to 13006a.
The tests were carried out in this 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,
the
length in the axial direction). The test piece was then fitted and clamped on
a
rotatable shaft, and a roll 48 mm in diameter placed in parallel with the axis
of
the shaft was thrust 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 against the roll were rotated at the same number
of
revolutions/minute - 209 r:p.m., with multipurpose gear oil being dropping on
the
31
CA 02303512 2000-03-14
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 before rotation and after the end of rotation, that
is,
the loss of weight by wear, mg, was determined. It can be said that the alloys
which are smaller in the loss of weight by wear are higher in wear resistance.
The results are given in Tables 34 to 36.
As is clear from the wear resistance test results shown in Tables 34 to 36,
the tests showed that those seventh invention alloys Nos. 7001a to 7029a were
excellent in wear resistance as compared with not only the conventional alloys
Nos. 13001a to 13004a and 13006a but also No. 13005a, which is an aluminum
bronze most excellent in wear resistance among expanded copper designated in
JIS. From comprehensive considerations of the test results including the
tensile
test results, it may safely be said that the seventh invention alloys are
excellent in
machinability and also possess a high strength feature and wear resistance
equal
to or superior to the aluminum bronze which is the highest in wear resistance
of
all the expanded copper alloys under the JIS designations.
32
CA 02303512 2000-03-14
C Table 17
alloy
composition
Cwt9K)
N Cu S Pb Zn
o. i
100174.8 2.9 0.03 remainder
100274.1 2.7 0.21 remainder
100378.1 3.6 0.10 remainder
100470.6 2.1 0.36 remainder
100574.9 3.1 0.11 remainder
100669.3 2.3 0.05 remainder
100778.5 2.9 0.05 remainder
C Table 2 7
alloy
composition
(wt~)
No. Cu Si Pb Bi Te Se Zn
200173.8 2.7 0.05 0.03 remainder
200269.9 2.0 0.33 0.27 remainder
200374.5 2.8 0.03 0.31 remainder
200478.0 3.6 0.12 0.05 remainder
200576.2 3.2 0.05 0.33 remainder
200672.9 2.6 0.24 0.06 remainder
C Table 3
alloy
composition
(wt~)
No. ~u Si Pb Sn Al P Zn
300170.8 1.9 0.23 3.2 remainder
300274.5 3.0 0.05 0.4 remainder
300378.8 2.5 0.15 3.4 remainder
300474.9 2.7 0.09 1.2 remainder
300574.6 2.3 0.26 1.2 1.9 remainder
300674.8 2.8 0.18 0.03 remainder
300776.5 3.3 0.04 0.21 remainder
300873.5 2.5 0.05 1.6 0.05 remainder
300974.9 2.0 0.35 2.7 0.13 remainder
301075.2 2.9 0.23 0.8 1.4 0.04 remainder
33
CA 02303512 2000-03-14
[ Table 4 J
__
alloy
composition
(wt,~)
~
No.Cu Si Pb Sn A1 P Bi Te Se Zn
400173.8 2.8 0.040.5 0.10 remainder
400274.5 2.6 0.11 1.5 0.04 remainder
400373.7 2.1 0.211.2 2.2 0.03 remainder
900476.8 3.2 0.05 0.030.31 remainder
400574:1 2.6 0.071.4 0.090.09 remainder
400675.5 1.9 0.32 3.2 0.150.16 remainder
900774.8 2.8 0.100.7 1.2 0.050.05 remainder
400870.5 1.9 0.223.4 0.03 remainder
400979.1 2.7 0.15 3.4 0.05 remainder
401074.5 2.8 0.10 0.05 0.05 remainder
401177.3 3.3 0.070.4 0.21 0.31 remainder
401276.8 2.8 0.05 2.0 0.03 0.13 remainder
401374.5 2.6 0.181.4 2.1 0.21 remainder
401474.0 2.5 0.202.1 1.1 0.10 0.07 remainder
401572.5 2.4 0.111.0 0.05 remainder
401676.1 2.5 0.07 2.3 0.10 remainder
901776.4 2.7 0.050.6 3.1 0.22 remainder
401874.0 2.5 0.23 0.22 0.03 remainder
.
401971.2 2.2 0.112.8 0.05 0.30 remainder
402075.3 2.7 0.22 1.4 0.03 0.05 remainder
402179.1 2.5 0.052.4 1.2 0.07 0.07 remainder
( Table 5
alloy
composition
(wt9o)
N' Cu Si Pb Sn P Sb As Zn
500174.3 2.9 0.050.4 remainder
' 69. 2. 0. 3. remainder
50028 1 31 1
500379.8 2.8 0.03 0.08 remainder
500478.2 3.4 0.16 0.21 remainder
500574.9 3.1 0.09 0.07 remainder
500672.2 2.4 0.25 0.13 remainder
500773.5 2.5 0.182.2 0.04 remainder
500877.0 3.3 0.060.7 0.15 remainder
500976.9 3.6 0.121.2 remainder
501071.4 2.3 0.262.6 0.03 remainder
501177.3 3.4 0.170.5 0.14 remainder
501274.8 2.8 0.071.4 0.03 remainder
501374.5 2.7 0.05 0.03 0.12 remainder
501476.1 3.1 0.14 0.18 0.03 remainder
501573. 2. 0. _ 0. 0. remainder
~ 9 5 08 07 05
501674.5 2.8 0.07 0.080.04 remainder
501777.3 3.1 0.121.5 0.13 0.05 remainder
501872.8 2.4 0.180.7 0.030.09 remainder
501974.2 2.7 0.070.5 0.11 0.10 remainder
502074. 2.8 0. 0. 0. 0. 0.03 remainder
6 05 9 07 05
34
CA 02303512 2000-03-14
[ Table 6 7
alloy
composition
(wt:K)
No. _ Si Pb Bi Te Se Sn P Sb As Zn
Cu
600170.7 2.3 0.17 0.05 2.8 remainder
600274.6 2.5 0.08 0.03 0.7 0.06 remainder
600378.0 3.7 0.05 0.34 0.4 0.05 remainder
600469.5 2.1 0.32 0.02 3.3 0.03 remainder
600576.8 2.8 0.03 0.07 0.8 0.21 0.02 remainder
600674.2 2.7 0.18 0.10 0.5 0.03 0.13 remainder
600776.1 3.2 0.12 0.05 1.7 0.12 0.02 remainder
600875.3 2.8 0.20 0.16 1.3 0.10 0.03 0.05 remainder
600977.0 3.1 0.14 0.06 0.21 remainder
601072.5 2.5 0.07 0.09 0.05 0.03 remainder
601174.7 2.9 0.10 0.32 0.14 0.10 remainder
601271.4 2.3 0.25 0.14 0.07 0.03 0.02 remainder
601374.7 3.0 0.13 0.05 0.12 remainder
601477.2 3.2 0.27 0.23 0.07 0.04 remainder
601574.0 2.8 0.07 0.03 0.03 remainder
601669.8 2.1 0.22 0.17 3.2 remainder
601773.8 2.9 0.15 0.03 1.6 0.07 remainder
601875.8 2.8 0.08 0.06 0.4 0.03 remainder
601971.2 2.3 0.15 0.07 2.5 0.07 remainder
602072 2 0 0 ~ 0. 0. 0. ~ remainder
0 6 12 04 ~ 9 03 05
~ ~ ~
CA 02303512 2000-03-14
C Table 7
alloy
composition
(wtX)
No. ~u Si Pb Bi Te Se Sn P Sb As Zn
602176.8 2.9 0.20 0.30 0.8 0.17 0.03 remainder
602278.3 3.2 0.15 0.36 0.4 0.06 0.14 remainder
602373.4 2.3 0.12 0.06 2.7 0.02 0.11 0.03 remainder
602474.6 2.8 0.05 0.08 0.19 remainder
602578.5 3.7 0.22 0.25 0.23 0.03 remainder
602674.9 2.9 0.16 0.05 0.05 0.10 remainder
602773.8 2.5 0.07 0.03 0.06 0.02 0.04 remainder
602874.8 2.6 0.12 0.02 0.12 remainder
602974.2 2.8 0.37 0.10 0.11 0.02 remainder
603076.3 3.2 0.08 0.05 0.07 remainder
603170.8 2.4 0.11 0.05 2.6 remainder
603274.6 3.0 0.25 0.32 0.6 0.06 remainder
603375.0 2.8 0.03 0.12 0.3 0.13 remainder
603473.5 2.8 0.12 0.07 1.0 0.11 remainder
603578.0 3.3 0.07 0.03 0.5 0.16 0.02 remainder
603672.4 2.5 0.13 0.05 3.1 0.03 0.05 remainder
603778.0 2.8 0.18 0.20 1.7 0.08 0.02 remainder
603876.5 3.1 0.10 0.11 1.7 0.03 0.03 0.04 remainder
603971.9 2.4 0.12 0.17 0.04 remainder
604077.0 3.5 0.03 0.35 0.23 0.03 remainder
36
CA 02303512 2000-03-14
C Table 8 ]
alloy
Composition
(wt~)
.
No. ~u Si Pb Bi Te Se Sn P Sb As Zn
604174.7 2.9 0.07 0.12 0.06 0.03 remainder
604272.8 2.5 0.20 0.06 0.03 remainder
604378.0 3.7 0.33 0.15 0.02 0.10 remainder
604474.0 2.8 0.12 0.05 0.08 remainder
60457fi. 3.1 0. 0. 0. 0. 0.03 remainder
1 05 07 03 09 I
I I
C Table 9 ]
alloy
composition
(wt%)
No. ~a ~Si Pb Sn A1 P Mn Ni Zn
7001 67 8 0 6 3 remainder
0 3 04 1 2
7001a, . . . .
7002 69 4 15 0 2 remainder
3 2 0 4 2
7002a. . . . .
8 6 0 8 0 remainder
63 2 33 2 9
7003a. . . . .
5 3 07 5 0 remainder
66 4 0 1 2
7004a. . . . .
7005 67 3 0 0 8 0 remainder
2 6 10 9 1 9
7005a. . . . . .
7006 63 7 27 7 1 2 remainder
0 2 0 2 2 1
7006a. . . . . .
7007 6g 3 05 1 3 0 remainder
7 4 0 4 1 9
7007a. . . . . .
7008 70 1 03 0 6 4 remainder
6 4 0 5 1 3
7008a. . . . . .
7009 67 6 0 6 1 3 remainder
8 3 12 2 2 3
7009a. . . . . .
7010 6g 5 0 0 0 1 remainder
4 3 O6 4 3 8
7010a_ . . . . .
37
CA 02303512 2000-03-14
C Table 1 0 J
alloy
composition
(wt%)
No. ~u Si Pb Sn AI P M_n Ni Zn
7011 73 4 17 2 7 8 5 remainder
9 4 0 1 1 0 1
7011a. . . . . . .
7012 65 2 20 5 1 0 3 remainder
5 9 0 1 0 12 2
7012a. . . . . . .
7013 66 3 0 8 1 0 6 remainder
1 3 08 1 1 03 2
7013a. . . . . . .
7014 70 3 15 0 1 0 8 1 remainder
3 9 0 1 4 21 1 2
7014a. . . . . . . .
7015 66 7 0 6 14 7 remainder
8 3 20 2 0 2
7015a. . . . . .
7016 69 4 07 0 0 3 remainder
0 0 0 5 20 2
7016a. . . . . .
7017 64 2 0 8 0 5 0 remainder
5 9 19 1 05 1 8
7017a. . . . . . .
7018 72 3 0 5 1 remainder
4 5 08 1 1
7018a. . . . .
7019 6g 3 0 0 3 remainder
2 9 03 4 1
7019a, . . . .
7020 76 3 0 3 9 re
6 4 14 2 1 ainder
7020a, . . . . m
C Table 1 1 J
alloy
composition
(wt~)
No. ~u Si Pb Sn A1 P Mn Ni Zn
7021 75 4 0 7 2 remainder
0 2 19 1 1
7021a. . . . .
7022 7 7 0:05 1 1 0 der
3 3 4 1 8 i
7022a2. . . . . rema
n
7023 5 3 0 0 0 3 de
8 35 3 2 2 i
64. . . . . . rema
7023a n
r
7024 8 3 0 7 0 0 d
9 05 2 04 1 i
75. . . . . . rema
7024a n
er
7025 70 5 0 2 23 0 ainder
3 06 1 0 3 e
7025a.1 . . . . . r
m
7026 67 2 0 8 0 2 0 remainder
2 8 22 1 14 2 9
7026a. . . . . . .
7027 70 3 0 0 3 remainder
2 8 11 03 2
7027a. . . . .
7028 0 0 1 inder
03 20 1
7028a75.9 4.4 . . . rema
7029 0 0 0 0 2 i
18 12 1 1 d
66.0 3. . . . . rema
7029a er
n
38
CA 02303512 2000-03-14
[ Table 1 2
alloy
composition
(wt96)
No. Cu Si Pb A1 P Zn
8001 74.5 2.9 0.16 0.2 0.05 remainder
8002 76.0 2.7 0.03 1.2 0.21 remainder
8003 76.3 3.0 0.35 0.6 0.12 remainder
8004 69.9 2.1 0.27 0.3 0.03 remainder
8005 71.5 2.3 0.12 0.8 0.10 remainder
8006 78.1 3.6 0.05 0.2 0.13 remainder
8007 77.7 3.4 0.18 1.4 0.06 remainder
i 77.5 3.5 0.03 0.9 0.15 remainder
8008
[ Table 1 3 ]
alloy
composition
(wt9G)
No. Cu Si .~Pb A1 P Bi Te Se Zn
9001 74.8 2.8 0.05 0.6 0.07 0.03 remainder
9002 76.6 2.9 0.12 0.9 0.03 0.32 remainder
9003 72.3 2.2 0.32 0.5 0.12 0.25 remainder
9004 77.2 3.0 0.07 1.4 0.21 0.05 remainder
9005 78.1 3.6 0.16 0.3 0.15 ~ 0.29 remainder
9006 74.5 2.6 0.05 0.6 0.08 0.07 remainder
[ Table 1 4 ]
alloy
composition
(wt~)
No. Cu Si Pb Al P Cr Ti Zn
1000176.0 2.8 0.12 0.7 0.13 0.21 remainder
1000275.0 3.0 0.03 0.2 0.05 0.03 remainder
1000378.3 3.4 0.06 1.3 0.20 0.34 remainder
1000469.6 2.1 0.25 0.8 0.03 0.17 remainder
1000577.5 3.6 0.12 0.7 0.15 0.23 remainder
1000671.8 2.2 0.32 1.2 0.08 0.32 remainder
1000774.7 2.7 0.1 0.6 0.10 0.03 remainder
1000875.4 2.9 0.03 0.3 0.06 0.12 0.08 remainder
39
CA 02303512 2000-03-14
C Table 1 5
alloy
composition
(wt~)
No. Cu _ Pb A1 Bi Te Se P Cr Ti Zn
Si
1100176.52.9 0.08 0.9 0.03 0.120.03 remainder
1100270.42.2 0.32 0.5 0.21 0.030.18 remainder
1100378.23.5 0.16 1.3 0.35 0.20 0.34 remainder
1100473.92.7 0.03 0.3 0.11 0.06 0.22 remainder
1100575.83.0 0.06 0.6 0.08 0.110.10 0.07 remainder
1100671.62.1 0.24 1.0 0.21 0.040.32 remainder
1100773.82.4 0.10 1.1 0.04 0.07 0.03 remainder
1100875.53.0 0.13 0.2 0.36 0.120.06 0.14 remainder
1100977.73.2 0.03 1.4 0.17 0.230.23 remainder
1101075.02.7 0.15 0.7 0.03 0.03 0.12 remainder
1101172.92.4 0.20 0.8 0.31 0.060.09 0.05 remainder
C Table 1 6
alloy heat
composition treatment
Cwt%)
N C S P Z n temperaturetime
o. a i b
1200169.32.3 0.05 remainder580C 30mia
1200269.32.3 0.05 remainder450C 2hr.
1200378.52.9. 0.05 remainder580C 30mia
1200478.52.9 0.05 remainder450C 2hr.
C Table 17 ]
alloy
composition
(wt9K)
' Cu Si Pb Sn A1 Mn Ni Fe Zn
1300158 3 0 0.2 remainder
8 1 2
13001a. . .
1300261 3 0 0.2 remainder
4 0 2
13002a. . .
1300359 2 0
1 0 2 0.2 remainder
13003a. . .
130046g 2 0
2 1 1 remainder
13004a. . .
13005
d 8 1.1 1.2 3.9
i 9
13005aer .
n
rema
130066 0 0
8 1 1 remainder
13006a1. . .
CA 02303512 2000-03-14
[ Table 18 ]
machinability ~rrosionhot mechanical stress
resistancework- properties resistance
ability
N form conditi-cutti-maximum 7 0 tensile elongat-corrosion
o. of on ng depth 0C strength ion cracking
chipp-of forceof deformabi-CN /m C%) resistance
ings cut CN) corrosionlity m 2 )
surface Cu m)
100100 O 117 160 O 533 35 O
1002OO O 114 170 O 520 32 O
1003OO O 119 140 D 575 36 O
1004OO O 118 220 D 490 30 D
1005OO O 114 170 O 546 34 O
1006D O 126 230 O 504 32 D
100700 D 127 170 D 515 44 O
C Table 1 9 ]
machinability ~rrosionhot mechanical stress
resistancework- properties resistance
ability
N form conditi-cutti-maximum 7 0 tensile elongat-corrosion
o. of on ng depth 0C strength ion cracking
chipp-of forceof deformabi-CN /mm C%) resistance
ings cut CN) corrosionlity 2 )
surface Cu m)
2001OO O 1 1 8 0 O 5 1 0 3 O
1 3
6
2002OO O 115 230 D 475 28 D
2003OO O 1 1 6 0 D 5 4 0 3 O
1 2
5
2004OO O 1 1 5 0 D 5 7 6 3 O
1 5
7
2005OO O 1 1 4 0 D 5 4 3 3 O
1 7
6
2006OO O 114 180 D I 502 I 32 O
I
41
CA 02303512 2000-03-14
C Table 2 0 7
machinability ~rrosionhot mechanical stress
resistancework- properties resistance
ability
N form conditi-cutti-maximum 7 0 tensile elongat-corrosion
o. of on n8 depth 0C strength ion cracking
chipp-of forceof deformabi-(N/mm2 (%) resistance
ings cut (N) corrosionlity )
surface Cu m)
3001OO O 120 30 O 542 23 O
3002OO O 1 7 0 O 5 5 0 3 0 O
1
7
3003OO O 1 1 1 0 D 5 6 5 3 4 O
1
9
300400 O 1 1 4 0 O 5 3 2 3 5 O
. 1
8
3005OO O 119 50 D 547 27 O
3006OO O 115 30 O 538 34 O
3007OO O 1 < 5 D 5 6 2 3 6 O
1
7
3008OO O 1 < 5 O 5 2 9 2 6 O
1
9
3009a0 O 1 < 5 D 5 1 8 3 0 O
1
8
301000 O 1 < 5 O 5 5 5 2 8 O
1
6
C Table 2 17
machinability ~rrosionhot mechanical stress
resistancework- properties resistance
ability
N form conditi-cutti-maximum 7 0 tensile elongat-corrosion
o. of on ng depth 0C strength ion cracking
chipp-of forceof deformabi-(N/mm2 (%) resistance
ings cut (N) corrosionlity )
surface (u m)
4001OO O 119 70 O 535 30 O
4002OO O 1 1 2 0 O 5 4 7 3 3 O
1
6
4003OO O 118 60 D 539 26 O
4004O O 1 3 0 D 5 5 0 3 1 O
1
3
4005OO O 1 < 5 O 5 3 4 2 7 O
1
7
4006OO O 1 < 5 D 5 4 2 3 0 O
1
8
4007O O 1 < 5 O 5 6 3 3 2 O
1
6
4008OO O 120 40 D 507 25 O
400900 O 1 1 1 0 D 5 7 2 3 6 O
1
7
4010OO O 115 10 O 524 33 O
4011OO O 1 < 5 O 5 8 0 3 1 O
1
6
4012OO O 114 20 O 575 34 O
4013O O 1 5 0 D 5 8 8 2 8 O
1
5
401400 O 117 <5 O 543 26 O
401500 O 117 60 O 501 27 O
4016OO O 116 130 D 539 32 O
4017OO O 118 50 O 574 34 O
4018Oo O 115 <5 O 506 30 O
4019OO O 118 <5 O 523 28 O
4020OO O 1 2 0 D 5 4 8 3 2 O
1
5
4021OO O 1 < 5 O 5 5 3 2 7 O
1
8
42
CA 02303512 2000-03-14
C Table 2 2 7
machinability ~rrosionhot mechanical stress
resistancework- properties resistance
ability
N formconditi-cutti-maximum 7 0 tensile elongat-corrosion
o. of on n8 depth 0C strength ion cracking
chipp-of forceof deformabi-(N/mmz C%) resistance
ingscut CN) corrosionlity )
surface Cu m)
5001a0 O 116 70 O 525 34 O
500200 O 120 40 D 501 25 O
500300 O 1 < 5 O 5 1 0 3 3 O
1
7
5004a0 O 1 < 5 D 5 4 7 4 2 O
1
7
500500 O 1 < 5 O 5 3 3 3 4 O
1
5
500600 O 1 < 5 O 4 7 0 3 0 D
1
6
500700 O 1 < 5 O 5 1 2 2 8 O
1
8
500800 O 1 < 5 O 5 5 8 3 6 O
1
9
500900 O 120 50 D 595 31 O
5010OO O 121 <5 O 516 27 O
5011OO O 118 <5 D 569 34 O
5012O O 117 <5 O 523 30 O
5013OO O 116 <5 O 504 33 O
5014O O 114 <5 O 536 35 O
5015OO O 117 <5 O 488 31 O
5016OO O 116 <5 O 510 37 O
5017OO O 118 <5 D 557 32 O
501800 O 117 <5 O 480 30 O
501900 O 117 <5 O 511 31 O
5020OO O 1 < 5 O 5 2 8 3 0 O
1
5
43
CA 02303512 2000-03-14
( Table 2 3
machinability con'osionhot mechanical stress
resistancework- properties resistance
ability
N formconditi-cutti-maximum 7 0 tensile elongat-corrosion
o. of on ng depth 0C strength ion cracking
chipp-of forceof deformabi-CN/mm2 C%) resistance
ingscut CN) corrosionlity )
surface Cum)
6001OO O 1 4 0 O 5 1 5 2 5 O
1
9
6002OO O 1 < 5 O 4 9 6 3 5 O
1
7
6003OO O 1 < 5 D 5 7 0 3 4 O
1
9
6004C~ O 1 < 5 D 5 0 3 2 6 O
1
8
6005O O 1 < 5 O 5 3 6 3 7 O
1
5
6006O O 1 < 5 O 5 1 2 3 3 O
1
3
6007O O 1 < 5 D 5 5 9 2 9 O
1
7
6008O O 1 < 5 D 5 2 7 3 1 O
1
5
600900 O 1 < 5 D 5 4 6 4 0 O
1
5
6010O O 116 <5 O 507 30 O
6011O O 113 <5 D 520 30 O
6012O O 115 <5 D 488 29 D
6013O O 114 <5 O 531 32 O
6014O O 114 <5 D 564 31 O
6015C O 115 20 O 525 34 O
6016C O 121 30 O 514 25 O
6017O O 119 <5 O 510 27 O
6018C O 116 <5 O 528 32 O
6019O O 119 <5 O 526 28 O
6020O O 1 < 5 O 5 0 9 3 0 O
1
6
44
CA 02303512 2000-03-14
[ Table 2 4 7
corrosionhot work-mechanical stress
machinability resistanceability properties resistance
N form conditi-cutti-maximum 7 0 0C tensile elongat-corrosion
o.
of on n8 depth deformabi-strength ion cracking
of of
chipp-cut forcecorrosionlity CN/mm' C%) resistance
)
ings surfaceCN) Cum)
6021OO O 113 <5 O 534 30 O
6022OO O 1 < 5 O 5 6 2 3 4 O
1
7
6023OO O 120 <5 O 527 27 O
6024OO O 1 < 5 O 5 1 5 3 3 O
1
6
6025OO O 1 < 5 D 5 7 5 3 5 O
1
7
6026OO O 1 < 5 O 5 2 4 3 2 O
1
4
602700 O 1 < 5 O 5 0 3 3 4 O
1
9
6028OO O 1 < 5 O 5 1 0 3 3 O
1
7
6029O O 1 < 5 O 5 2 2 3 0 O
1
4
6030OO O 118 40 O 546 37 O
6031OO O 119 <5 O 529 27 O
6032OO O 1 < 5 D 5 4 5 3 0 O
1
5
603300 O 1 < 5 O 5 2 1 3 4 O
1
6
603400 O 1 < 5 O 5 1 3 3 1 O
1
6
6035OO O 1 < 5 D 5 6 8 3 5 O
1
8
6036OO O 118 <5 O 536 26 O
6037O O 1 < 5 O 5 3 0 2 9 O
1
6
6038OO O 1 < 5 D 5 5 5 3 0 O
1
7
603900 O 1 2 0 O 4 9 7 3 1 O
1
7
604000 O I < 5 D 5 7 4 3 5 O
1
1
8
[ Table 2 5 7
~rrosionhot work-mechanical stress
machinability resistanceability properties resistance
_
.
N form conditi-cutti-maximum 7 0 0C tensile elongat-corrosion
o.
of on n8 depth deformabi-strength ion cracking
of of
chipp-cut forcecorrosionlity CN/mmZ C%) resistance
)
ings surfaceCN) Cu m)
6041OO O 115 <5 O 520 34 O
6042OO O 1 2 0 D 5 0 1 3 1 O
1
7
6043OO O 1 < 5 D 5 8 5 3 2 O
1
8
6044OO O 1 < 5 O 5 1 6 3 2 O
1
6
6045OO O 116 <5 O 538 35 O -
I
45
CA 02303512 2000-03-14
C Table 2 6 7
machinability hot mechanical
work- properties
ability
N form conditi-cutti-7 0 tensile elongat-
o. of on ng 0C strength ion
chipp-of forcedeformabi-(N/mm' (%)
ings cut CN) lity )
surface
7001OO O 1 O 7 5 5 1 7
3
2
7002OO O 1 O 7 7 6 1 9
2
7
7003OO D 135 O 620 15
7004OO O 1 O 7 1 4 1 8
3
0
7005OO O 1 O 7 0 8 1 9
2
8
7006OO O 1 O 6 8 5 1 6
3
0
7007~ O 1 O 7 1 7 1 8
3
2
7008OO O 1 O 8 1 1 1 8
3
0
700900 O 1 O 7 9 0 1 5
3
0
701000 O 131 O 708 18
701100 O 1 O 8 1 0 1 7
2
8
7012OO O 1 O 6 9 4 1 7
2
8
7013OO O 1 O 7 4 2 1 6
3
2
7014OO O 1 O 8 0 9 1 7
2
8
7015OO O 1 O 7 2 5 1 5
2
9
7016OO O 1 O 7 6 5 1 8
2
8
7017OO O 130 O 684 16
7018OO O 1 O 7 1 0 2 1
2
8
7019OO O 1 O 7 4 6 2 0
2
8
7020OO O 1 O 8 0 2 1 9
2
6
C Table 2 7 7
machinability hot mechanical
work- properties
ability
',N formconditi-cutti-7 0 tensile elongat-
o. of on ng 0C strength ion
chipp-of forcedeformabi-(N/mm2 C%)
ingscut (N) lity )
surface
7021OO O 1 O 7 9 2 1 9
2
6
7022OO O 128 O 762 20
7023OO O 1 O 7 2 5 1 7
2
9
70240 O 1 O 7 4 4 2 1
2
8
7025OO O 130 O 750 20
7026D O 1 O 6 7 1 2 3
3
2
7027OO O 1 O 7 4 0 2 3
2
8
7028OO O 1 O 7 6 3 2 2
~ 3
3
7029D O 1 ~ O 6 4 7 ~ 2
2 ~ 4
9
46
.....
CA 02303512 2000-03-14
a~
H
B E
C ~ U lC~N Q'~7M C N M
..~ ...r
O_
\ O O O O O O O O
b0
C'~0~ .O
.fl E
.C C1 .O
O
O
'.-sS O O O d O O O O
tn
H
t~
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CA 02303512 2000-03-14
C Table 3 2
machinability iTOSion hot mechanical stress
work-
resistanceability_ properties resistance
~
N formconditi-cutti-maximum 7 0 tensile elongat-corrosion
o. 0C
of on ng depth deformabi-strength ion cracking
of of
chipp-cut forcecorrosionlity (N /m m (%) resistance
' )
ingssurface(N) (u m)
12001OO O 122 210 O 486 36 O
12002OO O 119 200 O 490 35 O
12003OO O 120 160 D 501 40 O
1200400 O 1 1 6 0 D 5 0 5 4 1 O
1
9
51
CA 02303512 2000-03-14
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C Table 3 4 7 C Table 3 5 7
wear resistance wear resistance
N weight loss N weight loss
o. by wear o. by wear
(mg/100000rot.) (mg/100000rot.)
7001a0. 7 7021a1. 5
7002a1. 4 7022a1. 4
7003a2. 0 7023a0. 9
7004a1. 4 7024a2. 0
7005a1. 2 7025a1. 2
7006a1. 8 7026a1. 2
7007a2. 3 7027a1. 1
7008a0. 7 7028a2. 1
7009a0. 6 7029a1. 5
7010a1. 3
7011a0. 8
7012a1. 7
7013a1. 1
7014a0. 8
7015a1: 1
7016a1. 0
7017a1. 6
7018a1. 9
7019a1. 1
7020a1. 4
C Table 3 6
wear resistance
N weight loss
o. by wear
(mg/100000rot.
)
13001a5 0 0
13002a6 2 0
13003a5 2 0
13009a4 5 0
13005a2 5
13006a6 0 0
53
