U.S. patent application number 14/113823 was filed with the patent office on 2014-02-13 for alpha + beta or beta titanium alloy and method for production thereof.
This patent application is currently assigned to TOHO TITANIUM CO., LTD.. The applicant listed for this patent is Osamu Kanou, Satoshi Sugawara, Hideo Takatori. Invention is credited to Osamu Kanou, Satoshi Sugawara, Hideo Takatori.
Application Number | 20140044584 14/113823 |
Document ID | / |
Family ID | 47072507 |
Filed Date | 2014-02-13 |
United States Patent
Application |
20140044584 |
Kind Code |
A1 |
Kanou; Osamu ; et
al. |
February 13, 2014 |
Alpha + beta or beta TITANIUM ALLOY AND METHOD FOR PRODUCTION
THEREOF
Abstract
A titanium alloy containing copper, which cannot be realized by
a conventional method, is provided, having a composition in which
copper is contained in titanium with no segregation, and having
improved strength and hardness. In addition a method is also
provided, in which the titanium alloy is produced at lower cost
than in a conventional method. The .alpha.+.beta. or .beta.
titanium alloy contains copper at 1 to 10 mass %, has a crystal
phase of .beta. and .alpha. phase or of .beta. phase, is formed of
crystal particles not more than 100 .mu.m, and has a copper
concentration per an arbitrary specified 1 mm.sup.3 portion of the
crystal phase at within .+-.40% compared to another arbitrary
specified portion. The .alpha.+.beta. or .beta. titanium alloy is
produced by mixing 1 to 10 mass % of copper powder and the
remainder of titanium alloy powder and then pressing and forming
while being heated. The method for production of the .alpha.+.beta.
or .beta. titanium alloy has a step of mixing 1 to 10 mass % of
copper powder and the remainder of titanium alloy powder and a step
of pressing and forming the mixture while being heated.
Inventors: |
Kanou; Osamu;
(Chigasaki-shi, JP) ; Sugawara; Satoshi;
(Chigasaki-shi, JP) ; Takatori; Hideo;
(Chigasaki-shi, JP) |
|
Applicant: |
Name |
City |
State |
Country |
Type |
Kanou; Osamu
Sugawara; Satoshi
Takatori; Hideo |
Chigasaki-shi
Chigasaki-shi
Chigasaki-shi |
|
JP
JP
JP |
|
|
Assignee: |
TOHO TITANIUM CO., LTD.
Chigasaki-shi, Kanagawa
JP
SANYO SPECIAL STEEL CO., LTD.
Himeji-shi, Hyogo
JP
|
Family ID: |
47072507 |
Appl. No.: |
14/113823 |
Filed: |
April 27, 2012 |
PCT Filed: |
April 27, 2012 |
PCT NO: |
PCT/JP2012/061782 |
371 Date: |
October 25, 2013 |
Current U.S.
Class: |
419/48 ;
75/245 |
Current CPC
Class: |
B22F 9/023 20130101;
B22F 3/20 20130101; C22C 14/00 20130101; B22F 3/14 20130101; C22C
1/0458 20130101 |
Class at
Publication: |
419/48 ;
75/245 |
International
Class: |
C22C 1/04 20060101
C22C001/04; C22C 14/00 20060101 C22C014/00 |
Foreign Application Data
Date |
Code |
Application Number |
Apr 27, 2011 |
JP |
2011-099116 |
Claims
1. (Amended) An .alpha.+.beta. or .beta. titanium alloy comprising:
copper contained in a range of 1 to 10 mass % as a result of adding
the copper powder, and at least aluminum and vanadium, wherein the
alloy crystal phase is .beta. or .alpha. and .beta. phase, the size
of a crystal phase consisting particles not greater than 100 .mu.m,
and the copper concentration per 1 mm.sup.3 of an arbitrary
specified portion in the crystal phase is within .+-.40% compared
to another arbitrary specified portion.
2. The .alpha.+.beta. or .beta. type titanium alloy according to
claim 1, wherein the titanium alloy is obtained by mixing copper
powder and titanium alloy powder and then pressing and forming the
mixed powder while being heated.
3. The .alpha.+.beta. or .beta. type titanium alloy according to
claim 2, wherein the titanium alloy powder is produced from raw
titanium alloy, and the titanium alloy contains at least one
selected from molybdenum, iron, chromium, and tin.
4. A method for production of .alpha.+.beta. or .beta. titanium
alloy containing copper, comprising the step of: 1 to 10 mass % of
copper powder and titanium alloy powder which contains at least
aluminum and vanadium are pressed and formed while being heated so
as to form a dense compact.
5. The method for production of the .alpha.+.beta. or .beta.
titanium alloy according to claim 4, wherein a temperature in the
pressing and forming while being heated (Tw(.degree. C.)) is in the
following range: (Td-100.degree. C.)<Tw<(Td+100.degree. C.)
Td(.degree. C.) being .beta. transformation temperature of titanium
alloy that is pressed and formed.
6. The method for production of the .alpha.+.beta. or .beta.
titanium alloy according to claim 4, wherein the titanium alloy
powder is produced from raw titanium alloy, and the titanium alloy
contains at least one selected from molybdenum, iron, chromium, and
tin.
Description
TECHNICAL FIELD
[0001] The present invention relates to titanium alloys, and in
particular, relates to a titanium alloy which has superior
mechanical properties, such as strength and hardness, compared to
Ti-6Al-4V alloys or the like, and has a composition that cannot be
produced by a conventional melting method, and relates to a method
for production of the titanium alloy in which the alloy is produced
at low cost.
BACKGROUND ART
[0002] Recently, the demand for titanium alloys has greatly
increased due to recent increase in the application fields, not
only in the aircraft industry, but also in the field of consumer
use. In particular, since high quality and various functions are
required in alloys for aircraft use, high quality is the most
important criteria, and in many cases, production cost reduction is
the secondary one.
[0003] However, the effort of production cost reduction for
titanium alloys would result in the increase of the amount used of
light titanium alloys from a viewpoint of energy conservation of
production processes of alloys and improvements in yields, that is,
it would result in energy load reduction of operation of machines,
and they would be considered to satisfying the needs of
society.
[0004] In particular, Ti-6Al-4V alloy (hereinafter simply referred
to as 64 alloy) has been conventionally used in the aircraft
industry since it has superior mechanical properties. However,
there is one problem in that the 64 alloy is difficult to be
assembled in complicated structure parts since it has inferior
workability.
[0005] In view of such circumstances, Ti-4.5Al-3V-2Fe-2Mo alloy (so
called "SP700") has been developed in order to improve workability
of the 64 alloy. Furthermore, Ti-10V-2Fe-3A1 (so called "10-2-3
alloy"), Ti-15V-3Cr-3Al-3Sn (so called "15-3-3-3-3 alloy") or the
similar alloy has been developed in which strength is further
improved while maintaining the 64 alloy elongation level. However,
vanadium, iron or the similar element is easily segregated in any
of the alloys SP700, 10-2-3, 15-3-3-3-3, therefore further
improvement has been required.
[0006] Non-patent document 1 below discloses that workability of
titanium material can be further improved by adding more than 1 wt
% of copper to pure titanium. However, it is difficult to add more
than 1% to titanium since copper would be segregated greatly in
titanium. Therefore, there is a limitation of further improvement
in above properties of the alloys, and the problem remains to be
solved.
[0007] On the other hand, a "raw powder mixing method" is known
(see below patent document 1 and non-patent document 2) in which
the 64 alloy is produced using metallic powder. The raw powder
mixing method is known in that each element powders required for
alloy are prepared independently, and these powders are uniformly
mixed to form complex powders, and the complex powders are used for
raw materials of titanium alloys.
[0008] However, although the raw powder mixing method is promising
on a laboratory scale experiment, there are big hurdles to overcome
the cost reducing solution in the actual production scales, and the
raw powder mixing method is merely in practical use, and moreover,
there is no report of production of titanium alloy containing
copper in high concentration.
[0009] The cost of titanium powder should depend on the high price
of pure titanium raw material, and further improvement is required
for reducing the cost of titanium powder.
[0010] Titanium alloys having mechanical properties superior to
those of the 64 alloy are desired, and a method of producing the
low cost alloys are desired as explained.
[0011] Patent document 1: Japanese Unexamined Patent Application
Publication No. Hei05 (1993)-009630
[0012] Non-patent document 1: Material, Vol. 48 (2009), (11), pp.
547-554, by Fujii, Takahashi, Mori, Kawakami, Kunieda and
Otsuka
[0013] Non patent document 2: Toyota Central Institute R&D
Review Vol. 29 (1994), (3), pp. 49-60, by Saito and Furuta
SUMMARY OF THE INVENTION
[0014] As is explained, an object of the present invention is to
provide titanium alloy containing copper with no segregation, which
cannot be realized by a conventional method, and having improved
strength and hardness. In addition, another object is to provide a
method for producing the copper containing titanium alloy at lower
cost than a conventional one.
[0015] The inventors have researched in view of the above
circumstances, and they have found that titanium alloy having
superior strength, elongation and hardness compared to a
conventional method can be produced by using a metallurgical powder
method to produce titanium alloy, rather than a melting method, by
producing titanium alloy powder while employing a
hydrogenation-dehydrogenation method on raw titanium alloy, and
furthermore, by mixing the titanium alloy powder and copper powder
and then pressing and forming this mixed powder while being heated,
and thus the present invention has been completed. Here, in the
present invention, "pressing and forming while being heated" means
that mixed powder in which copper powder is added to titanium
powder is pressed and formed under warm or hot conditions.
[0016] As a result, they found that a titanium alloy containing
copper in high concentration, which has been difficult to produce
by conventional methods, can be produced, and that titanium alloy
having a uniform structure and few segregations of copper can be
produced in the reasonable cost range, and the present invention
was completed.
[0017] Furthermore, a titanium alloy produced by the method above
mentioned not only has higher strength due to low segregation of
alloy components, but also has superior hardness compared with a
titanium alloy produced by the conventional method.
[0018] That is, an .alpha.+.beta. or .beta. titanium alloy of the
present invention contains copper in a range of 1 to 10 mass %,
crystal phase of the alloy is .beta. phase or is .alpha. and .beta.
phase, the crystal particle size in .beta. phase or is .alpha. and
.beta. phase is not more than 100 .mu.m, and copper concentration
per 1 mm.sup.3 of arbitrary specified portion in the crystal phase
is within .+-.40% compared to another arbitrary specified
portion.
[0019] Furthermore, it is desirable that the .alpha.+.beta. or the
.beta. titanium alloy according to the present invention is
obtained by mixing copper powder and titanium alloy powder prepared
independently, and then pressing and forming the mixed powder while
being heated.
[0020] Furthermore, in the.alpha.+.beta. or the .beta. titanium
alloy according to the present invention, it is desirable that the
titanium alloy powder is produced by titanium alloy as a raw
material, and the titanium alloy contains at least one kind
selected from aluminum, vanadium, molybdenum, iron, chromium, and
tin.
[0021] A method for production of the .alpha.+.beta. or the .beta.
titanium alloy of the present invention is a production method of
the .alpha.+.beta. or the .beta. titanium alloy containing copper,
and includes a step in which 1 to 10 mass % of copper powder and
titanium alloy powder are pressed and formed while being heated so
as to form dense compact.
[0022] In the method for production of the .alpha.+.beta. or .beta.
titanium alloy according to the present invention, it is desirable
that temperature in the pressing and forming while being heated
(Tw(.degree. C.)) is employed in the range of (Td-100.degree.
C.)<Tw<(Td+100.degree. C.), and in this case, Td(.degree. C.)
means .beta. transformation temperature of titanium alloy which is
pressed and formed.
[0023] Furthermore, in the method for production of the
.alpha.+.beta. or the .beta. titanium alloy according to the
present invention, it is desirable that the titanium alloy powder
is produced from titanium alloy as a raw material, and the titanium
alloy contains at least one kind selected from aluminum, vanadium,
molybdenum, iron, chromium, and tin.
[0024] By the method for production of the .alpha.+.beta. or .beta.
titanium alloy according to the present invention mentioned above,
titanium alloy containing copper at high concentration, having
structure with no segregation of copper, and having strength and
hardness, which cannot be produced by a conventional method, can be
produced in the reasonable cost range.
[0025] As a result, the titanium alloy according to the present
invention can be appropriately employed to fields of high-strength
mechanical parts, medical materials, and aircraft materials.
BRIEF DESCRIPTION OF DRAWINGS
[0026] FIG. 1 is a flowchart diagram showing the method for
production of the .alpha.+.beta. or .beta. titanium alloy according
to the present invention.
[0027] FIG. 2 is a microscope photograph showing a structure of a
sintered body of an Example, FIG. 2A is the sintered body of
Example 2-1, and FIG. 2B is the sintered body of Example 2-2.
[0028] FIG. 3 is an EPMA image showing distribution of elements of
Ti, V, Al, and Cu in an Example.
BEST MODE FOR CARRYING OUT THE INVENTION
[0029] The best mode for carrying out the present invention is
explained with reference to the drawings.
[0030] The .alpha.+.beta. or .beta. titanium alloy according to the
present invention contains copper in a range of 1 to 10 mass %,
crystal phase of the alloy is .beta. phase or is .alpha. phase and
.beta. phase, the crystal phase consists of crystal particles not
more than 100 .mu.m, and copper concentration per 1 mm.sup.3 of an
arbitrary specified portion in the crystal phase is within .+-.40%
compared to another arbitrary specified portion.
[0031] In a conventional powder metallurgical method, due to
addition of copper powder to alloy powder, which is produced using
titanium alloy as a raw material, there may be a case in which
differences of concentration are generated among multiple portions
that are mutually different in an alloy. However, in the titanium
alloy according to the present invention, since copper
concentration per 1 mm.sup.3 of an arbitrary specified portion in
the crystal phase is reduced to within .+-.40% compared to another
arbitrary specified portion, the overall alloy structure is
maintained sufficiently uniform.
[0032] Furthermore, the .alpha.+.beta.-type or .beta.-type titanium
alloy according to the present invention is produced by a method in
which titanium alloy powder containing copper powder in a range
from 1 to 10 mass % is pressed and formed while being heated.
[0033] Here, in the present invention, "titanium alloy powder
containing copper powder in a range of 1 to 10 mass %" means
complex powder in which copper powder separately prepared is added
and mixed to titanium alloy powder not containing copper
powder.
[0034] In the present invention, as the titanium alloy powder, it
is desirable to use titanium alloy powder containing aluminum or
vanadium. As a desirable example of such an alloy powder, Ti-6Al-4V
alloy powder, Ti-3Al-2.5V alloy powder or the like may be
mentioned.
[0035] In addition to aluminum or vanadium, alloy powder containing
molybdenum, iron, chromium, or tin may be mentioned. Typical alloy
powders of these may be mentioned as follows. [0036] Ti-10V-2Fe-3Al
alloy powder, [0037] Ti-15V-3Al-3Al-3Cr-3Sn alloy powder, [0038]
Ti-4.5Al-3V-2Fe-2Mo alloy powder, [0039] Ti-5Al-5V-5Mo-3Cr alloy
powder, and [0040] Ti-5Al-4V-0.6Mo-0.4Fe alloy powder.
[0041] It is desirable that the above-mentioned titanium alloy
powder is produced by a hydrogenation-dehydrogenation method
(hereinafter simply referred to as an HDH method) using cut chips
or cut powder or scraps of ingots as a raw material.
[0042] FIG. 1 shows a preferable embodiment of a process for
production of titanium alloy according to the present invention. As
a raw material for titanium alloy supplied to the present
invention, alloy scraps or titanium alloy ingots which originally
had desirable components, such as titanium alloy cut powder,
titanium alloy forged pieces, edge materials of titanium alloy rods
or the like can be mentioned.
[0043] By using the alloy scrap material as a raw material,
production costs of the titanium alloy powder can be effectively
reduced. It is desirable that these titanium alloy scraps or
titanium alloy ingots (hereinafter simply referred to as "titanium
alloy raw material") be adjusted beforehand within a predetermined
length or size.
[0044] For example, it is desirable to cut beforehand to a length
not more than 100 mm in a case of alloy cut powder. By cutting to
such a length, a hydrogenation process, which is the next process,
can be efficiently promoted. Furthermore, in a case of forged
chips, which are block shaped alloy scraps, it is not particularly
necessary for it to be processed beforehand, as long as it has size
that can be placed in a hydrogenation furnace. It is desirable to
be cut into powder in a case in which the raw material is titanium
alloy ingots.
[0045] As mentioned above, the titanium alloy raw material, which
is modified is provided to the hydrogenation treatment process
under a hydrogen atmosphere. It is desirable that the hydrogenation
treatment be performed in a temperature range of 500 to 650.degree.
C. Since the hydrogenation treatment reaction of the alloy raw
material is an exothermic reaction, any operation to increase
temperature is not necessary along with promoting of the
hydrogenation reaction, and the hydrogenation reaction can be
promoted spontaneously.
[0046] It is desirable that the titanium alloy raw material, which
has been treated by hydrogenation treatment (hereinafter simply
referred to as "hydrogenated titanium alloy"), be cooled to room
temperature, and then be ground and sieved under an inert gas
atmosphere such as argon gas, so as be of predetermined particle
size.
[0047] Then, it is desirable that the hydrogenated titanium alloy
powder that has been ground and sieved in powder shape be heated up
to a high temperature range under a reduced pressure
atmosphere.
[0048] It is desirable that the dehydrogenation treatment be
performed in a temperature range of 500 to 800.degree. C. while
evacuating the atmosphere to form a vacuum. Since the
dehydrogenation reaction is an endothermic reaction, which is the
opposite to the above-mentioned hydrogenation treatment reaction,
heating operation is necessary until hydrogen is no longer
generated from the hydrogenated titanium alloy powder.
[0049] The titanium alloy powder according to the present invention
can be obtained by the abovementioned operation. It is desirable
that the titanium alloy powder of the present invention be adjusted
in its particle size so as to be in a range from 1 to 300 .mu.m,
and more desirably from 5 to 150 .mu.m. There may be a tendency for
it to be difficult to increase the densities of alloys in final
products if the particle diameter is rougher than this range, but
on the other hand, undesirably, bulk density may be decreased, it
may become easily oxidized, content of oxygen may be increased, and
it may easily burn if finer than this range.
[0050] There may be a case in which the titanium alloy powder
obtained by finishing the dehydrogenation treatment is sintered. In
this case, it is desirable to perform breaking and grinding if
necessary.
[0051] In the present invention, copper powder of 1 to 10 mass % is
added to the titanium alloy powder produced by the above
method.
[0052] By adding copper powder from 1 to 10 mass % to the titanium
alloy powder produced, strength and hardness of the titanium alloy
material, which is obtained by pressing and forming using the above
alloy powder as a raw material, can be maintained in high
level.
[0053] It is desirable that the particle size of copper powder to
be added to the titanium alloy powder be adjusted to be in a range
from 1 to 300 .mu.m. Copper powder in a range of 1 to 50 .mu.m is
more desirably used.
[0054] Since the finer the copper powder, the more advantageous it
is in the production of titanium alloy powder having uniform
composition, it is desirable that the average particle size of the
copper powder (d50) be adjusted in a range of 10 to 40 .mu.m, in
the range of particle size of 1 to 50 .mu.m mentioned above.
[0055] In the present invention, it is desirable that the
copper-added titanium alloy powder obtained by the above method be
mixed uniformly, and then be pressed and formed while being
heated.
[0056] As a pressing and forming method performed in the present
invention, a conventional technique such as HIP, hot pressing,
CIP-HIP, Hot-extrusion or the like can be employed, and in
particular, the Hot-extrusion is superior from a viewpoint of
productivity since sintering and shape forming are simultaneously
promoted in a short time.
[0057] In the present invention, it is desirable that the titanium
alloy powder in which copper powder is mixed be filled in metallic
capsule and then be pressed and formed while being heated.
[0058] Titanium alloy material which is obtained by extrusion of
titanium alloy powder in which copper powder is mixed and which is
filled in the metallic capsule is a titanium alloy containing
copper of high composition which could not be produced by a
conventional method, exhibiting small segregation of copper, and
exhibiting the superior mechanical properties of being strong and
hard.
[0059] It is desirable that temperature (Tw) of pressing and
forming mentioned above be in a range of (Td-100.degree.
C.)<Tw<(Td+100.degree. C.). Here, Td means .beta. transition
temperature of titanium alloy, which is an objective of pressing
and forming. By heating the titanium alloy powder beforehand to be
in the above range, the above-mentioned pressing and forming can be
smoothly promoted.
[0060] In a case in which the temperature of pressing and forming
is lower than (Td-100.degree. C.), deformation resistance of
titanium alloy becomes great, and it may be difficult to maximally
densify the titanium alloy powder after pressing and forming. In
particular, in a case in which pressing and forming are performed
by extrusion, there may be a case in which raw material undesirably
clogs up in a die.
[0061] On the other hand, in the present invention, in a case in
which the temperature of pressing and forming is higher than
(Td+100.degree. C.), there may be a tendency for crystal particles
of titanium alloy material to be more coarse than 100 .mu.m, and
mechanical properties of a titanium alloy material may be
undesirably adversely affected.
[0062] Furthermore, in the present invention, in a case in which
the temperature of pressing and forming is between (Td-100.degree.
C.) and Td, that is, pressing and forming is performed in the
.alpha.+.beta. region, and since crystal structure of titanium
alloy material after pressing and forming is uniform and fine, it
is not only strong and hard, but also exhibits superior mechanical
properties which has a good balance of tensile strength and
elongation.
[0063] The titanium alloy according to the present invention is
characterized in that the content of copper composition is 1 to 10
mass %, and copper concentration per 1 mm.sup.3 of an arbitrary
specified portion in the alloy is within .+-.40% compared to copper
concentration in another arbitrary specified portion.
[0064] The abovementioned aspect means that copper is distributed
almost uniformly in the titanium alloy according to the present
invention.
[0065] Among titanium alloys having such a structure, in
particular, as exemplified by the Ti-6Al-4V alloy, tensile strength
is from 1400 to 1550 MPa, and elongation is from 2 to 7%, which are
high values. The alloy exhibits superior elongation values in
addition to superior tensile strength compared to a conventional
alloy.
[0066] The titanium alloy having superior mechanical properties
mentioned above is desirably produced by a so-called "pre-alloy
method", in particular among powder methods, in which alloy powder
obtained by powdering of alloys obtained by a melting method is
used as raw material, and it is then made dense.
[0067] Here, the "pre-alloy method" means that powders which are
produced using alloys which are produced by a melting method is
used as a raw material for sintering, the method is opposed to
mixed powder raw material in which metallic powders each consisting
of a single element are separately prepared and these metallic
powders are mixed.
[0068] Among the powder methods mentioned above, in particular by
using the pre-alloy powder as raw material, it becomes possible to
produce titanium alloy having uniform alloy composition.
[0069] Regarding desirable densifying condition in order to realize
abovementioned properties, the extrusion is explained as an
example, as follows.
[0070] First, titanium alloy powder and copper powder are prepared
so as to yield the desired composition, they are uniformly mixed,
and the mixed powder is inserted into a metallic capsule. Then,
after keeping the inside of the capsule under a vacuum of not more
than 10.sup.-1 Torr, it is desirably pressed and formed by HIP,
CIP-sintering or extrusion. It is also desirable that the powder be
filled in dies and be hot-pressed in a vacuum not more than
10.sup.-2 Torr.
[0071] Temperature (Tw) of pressing and forming while being heated
is desirably in the range of (Td-100.degree.
C.)<Tw<(Td+100.degree. C.).
[0072] As explained, the pressing and forming while being heated
according to the present invention can be achieved by using a
conventional method such as HIP, hot-press, CIP-HIP, or
Hot-extrusion.
[0073] In the present invention, among the methods for pressing and
forming while being heated, in particular in the pressing and
forming by Hot-extrusion, it is desirable that the ratio of the
cross-sectional area of the titanium alloy material that is to be
extruded versus the cross-sectional area of the capsule that is to
be inserted in the extrusion apparatus (hereinafter simply referred
to as the "extrusion ratio") be in a range of 1/10 to 1/30.
[0074] By setting the extrusion ratio in the above range, extent of
flow in the capsule having titanium alloy powder inside is
controlled, forge degree of the titanium alloy material that is to
be extruded can be adjusted, and more preferable mechanical
properties can be given.
[0075] Also the pressed and formed body by the HIP, hot pressing,
or CIP-HIP can improve mechanical properties imparted to the
titanium alloy material produced by forging processing by rolling,
forging or the like while being heated with the abovementioned
cross-sectional area ratio.
[0076] It should be noted that the capsule that covers the titanium
alloy material produced by HIP, CIP-HIP, Hot-extrusion or the like
is desirably removed by cutting or acid washing. The titanium alloy
material from which the capsule is removed in this way can be again
heated to a high temperature in a vacuum.
[0077] Since the titanium alloy material which has been processed
by the treatment mentioned above has extremely superior strength,
has fine crystal particles, and is strengthen by Cu which is
distributed uniformly, it can be preferably used as a structural
material such as in a high-strength mechanical part.
[0078] That is, not only is the strength of the titanium alloy
material containing copper according to the present invention 10 to
30% higher than in a conventional titanium alloy material not
containing copper, but also raw material cost can be reduced in the
case in which titanium alloy scrap is used as the raw material, and
as a result, cost of titanium alloy material that is the final
product can be reduced 50 to 70% compared to in a conventional
case.
[0079] In addition, the titanium alloy material according to the
present invention exhibits high hardness value, that is, 10 to 30%
higher than a material in which copper is not added.
[0080] The titanium alloy according to the present invention has
the above-mentioned superior mechanical properties, and as a
result, the material can be employed appropriately for medical
materials in addition to industrial precision mechanical parts, and
furthermore, the material can also be employed appropriately in
aircraft parts to which not only strength but also abrasion
resistance is required.
[0081] It should be noted that the titanium alloy containing copper
can be produced by a melting method; however, there may be
noticeable segregation, and it may be difficult to produce a
practical alloy.
[0082] It is desirable that the titanium alloy material produced in
the present invention contain at least aluminum and vanadium, and
it can further contain molybdenum, iron, chromium, and/or tin in an
appropriate amount. Typical alloys of these are mentioned as
follows. It should be noted that the alloy that can be produced in
the present invention is not limited to these, and the present
invention can be employed in many kinds of other titanium alloys
not shown here.
[0083] Ti-(9-10)V-(1.8-2)Fe-(2.7-3)Al-(1-10)Cu,
[0084] Ti-(13.5-15)V-(2.7-3)Cr-(2.7-3)Al-(2.7-3)Sn-(1-10)Cu,
[0085] Ti-(4.1-4.5)Al-(2.7-3)V-(1.8-2)Fe-(1.8-2)Mo-(1-10)Cu,
[0086] Ti-(4.5-5)Al-(4.5-5)V-(4.5-5)Mo-(2.7-3)Cr-(1-10)Cu,
[0087] Ti-(4.5-5)Al-(3.6-4)V-(0.5-0.6)Mo-(0.3-0.4)Fe-(1-10)Cu.
[0088] As explained so far, the present invention can provide the
copper containing titanium alloy not having segregation of copper,
having superior strength and hardness, and having a composition
which is impossible to be produced by a conventional method.
Furthermore, in the present invention, the titanium alloy can be
produced more efficiently and at lower cost than in a conventional
method.
EXAMPLES
[0089] Data according to Examples and Comparative Examples were
collected under the following conditions.
1. Raw material
1) 64 Alloy Powder
[0090] Production method: HDH method was applied to 64 alloy scrap
and then broken and ground
[0091] Average particle diameter (d50): 52 .mu.m
2) Copper Powder
[0092] Production method: Electrolyzed copper powder, trade name
51-N, produced by JX Nippon Mining and Metals Corporation
[0093] Average particle diameter (d50): 35 .mu.m
3) Mixed Ratio of Copper Powder Versus Titanium Alloy Powder
[0094] 1 to 10 mass %
4) Mixing
[0095] The 64 alloy powder and copper powder were uniformly mixed
by a commercially available mixing apparatus.
2. Pretest
[0096] In order to determine conditions of pressing and forming
while being heated, samples were made by adding each of 0%, 3%, 5%,
7%, and 10% of copper powder to 64 alloy powder, and then
deformation resistance of the samples at the .beta. transformation
temperature (Td) and temperature near the .beta. transformation
temperature (Td) were observed. Measuring electric resistance by
the four terminals method with increasing temperature of the test
piece in an argon gas atmosphere, and a temperature at which
temperature dependency of the electric resistance variation was
varied was determined as the .beta. transformation temperature
(Td). As the apparatus, an electric resistance measuring apparatus
(trade name: ARC-TER-1 type) was used. The results were as
follows.
TABLE-US-00001 TABLE 1 No. Copper content (%) Td (.degree. C.) 1 0
985 2 3 935 3 5 910 4 7 870 5 10 830
[0097] The .beta. transformation temperature (Td) of 64 alloy (0%
copper) is known to be 995.degree. C. from a conventional document,
and the test result was almost the same as the value.
[0098] Next, deformation resistance at the .beta. transformation
temperature measured above (Td), at a temperature 30.degree. C.
lower than the .beta. transformation temperature (Td), and at a
temperature 50.degree. C. higher than the .beta. transformation
temperature (Td) were measured. The measurement was performed by a
compression test using a hot processing duplicating apparatus
(trade name: Thermec Master Z, produced by Fuji Electronic
Industrial Co., Ltd.). The results are shown in Table 2.
TABLE-US-00002 TABLE 2 Copper content Td -30.degree. C. Td Td
+50.degree. C. No. (%) (MPa) (MPa) (MPa) 1 0 140 95 80 2 3 180 140
120 3 5 215 185 150 4 7 300 245 180 5 10 380 310 255
3. Extrusion
[0099] Extrusion temperature was determined in consideration of
extrusion force of extruding apparatus and deformation resistance
of material. Each of complex powders in which copper powder was
mixed to 64 alloy powder at 0%, 3%, 5%, 7% and 10% was filled in a
mild steel capsule, the inside of which was evacuated to
1.times.10.sup.-2 Torr, and was then sealed. Each of the powder
sealed capsules was formed by Hot-extrusion as an example of
pressing and forming while being heated. The temperature of heating
in this process depending on copper content is shown in Table 3.
Heating was performed for 2 hours. The heating temperature in each
alloy containing copper and temperature difference of the
temperature from the .beta. transformation temperature (Td) are
shown in Table 3.
TABLE-US-00003 TABLE 3 Copper content Heating temperature
Difference from Td No (%) (.degree. C.) (.degree. C.) 1 0 930 -55 2
3 910 -20 3 5 950 +40 4 7 930 +60 5 10 930 +100
4. Processing of Pressed and Formed Material
[0100] The capsule which was remaining on the surface of titanium
alloy material produce by pressing and forming while being heated
was dissolved and removed by acid washing.
5. Measurement of Mechanical Properties
1) Measurement of Tensile Strength
[0101] Tensile testing apparatus (Trade name: 5985 type, produced
by Instron Corporation) was used.
2) Observation of Crystal Structure
[0102] Measuring apparatus EPMA (trade name: JXA-8100, produced by
JEOL Ltd.) was used.
3) Distribution of Copper in the Crystal Structure
[0103] Measuring apparatus EPMA (trade name: JXA-8100, produced by
JEOL Ltd.) was used.
Example 1 and Comparative Example 1
(Difference in Effect of Addition or No Addition of Copper
Powder)
[0104] Mechanical properties in a case in which copper powder was
added to 64 alloy powder and a case in which copper powder was not
added were investigated. As shown in Table 4, it was confirmed that
yield strength, tensile strength and hardness were superior in the
case of addition of copper powder. Among copper added alloys,
elongation was slightly less in the material of 5% or more copper
content in particular, and it was considered that the pressing and
forming temperature were influenced by being in the .beta.
temperature range.
TABLE-US-00004 TABLE 4 Copper Yield Tensile content strength
strength Elongation Hardness No. (%) (MPa) (MPa) (%) (Hv) Example
1-1 3 1,290 1,400 7.2% 380 Example 1-2 5 1,300 1,450 3.8% 420
Example 1-3 7 1,380 1,500 3.1% 460 Example 1-4 10 1,430 1,550 2.2%
500 C. Example 1 0 1,100 1,200 8.1% 350
Example 2 and Comparative Example 2
(Difference of Temperature of Pressing and Forming)
[0105] Influence of pressing and forming temperature which is
exerted on crystal structure of sintered body obtained by pressing
and forming the 64 alloy in which 5% of copper was added (.beta.
transformation temperature: 950.degree. C.) was investigated.
[0106] Mixed phase structure of the .beta. phase and the .alpha.
phase was observed in Examples 2-1 and 2-2 in which pressing and
forming temperature was within the range of the present invention,
as shown in FIG. 2. On the other hand, in Comparative Example 2-1
in which pressing and forming temperature was out of the range of
the present invention, the .beta. phase in crystal structure was
coarsened. In addition, in Comparative Example 2-2, pressed and
formed material could not be obtained since material became clogged
in dies.
TABLE-US-00005 TABLE 5 Temperature of Difference Particle size of
pressing and forming from Td crystal of formed No. (.degree. C.)
(.degree. C.) body Result of evaluation Example 2-1 950 +40 55
.mu.m Tabular structure existing inside of .beta. particle, and
.alpha. phase existing along crystal particle interface Example 2-2
880 -30 10 .mu.m Fine .alpha. phase and .beta. phase structure C.
Example 2-1 1030 +120 225 .mu.m .beta. phase coarsened C. Example
2-2 790 -120 -- Material clogged in dies
Example 3
(Copper Concentration Distribution of Titanium Material
Produced)
[0107] Concentration of composition in crystal structure of
titanium material produced by pressing and forming in Example 2 was
investigated by EPMA. Regarding Ti, Al, V, and Cu, each X-ray image
was measured. These images are shown in FIG. 3, and the results
were as follows. The number shown here means count number of EPMA,
and sensitivity is different in each element. Therefore, due to
conversion of the count number to concentration, defining an
average count number as a nominal concentration of each element,
the correction coefficient of concentration was calculated as shown
in Table 6. Based on this correction coefficient, existence ratio
for each concentration was calculated as shown in Tables 7 and 8.
The minimal concentration and the maximal concentration in each
element were as follows.
[0108] Ti (Average concentration 85.5%): Minimal concentration
74.8% and maximal concentration 96.3%
[0109] Al (Average concentration 5.7%): Minimal concentration 3.8%
and maximal concentration 8.6%
[0110] V (Average concentration 3.8%): Minimal concentration 3.0%
and maximal concentration 4.8%
[0111] Cu (Average concentration 5.0%): Minimal concentration 2.0%
and maximal concentration 8.2%
[0112] There is a region of composition almost 100% different from
the nominal value of the material if observing Cu concentration
from the microscopic viewpoint; however, the average value of Cu
concentration in the arbitrary specified portion of 1 mm.sup.3 is
always in a range from 4.5 to 5.5% no matter how the 1 mm.sup.3
part is selected, and is within .+-.10% versus the nominal value 5%
of the material. That is, there is no segregation seen from the
macroscopic viewpoint. Also, regarding Al and V, the average value
of the concentration in the arbitrary specified portion 1 mm.sup.3
part was within .+-.8% versus the nominal value of the material in
the case of Al and was within .+-.15% versus the nominal value of
the material in the case of V.
TABLE-US-00006 TABLE 6 Ti Al V Cu Count of average value 2544 158
282 129 Composition of average value 85.5 5.7 3.8 5 Correction
coefficient 29.8 27.7 74.2 25.8
TABLE-US-00007 TABLE 7 Ti Al V Cu Concentration Intensity
Concentration Intensity Concentration Intensity Concentration
Intensity More than 96.3 0 More than 8.6 0 More than 4.8 0 More
than 8.2 0 92.7-96.3 0.3 7.6-8.6 0.1 4.6-4.8 0.1 7.6-8.2 0.2
89.2-92.7 10.1 6.7-7.6 4.2 4.4-4.6 0.7 7.1-7.6 0.8 85.6-89.2 39.6
5.7-6.7 41.9 4.3-4.4 2.8 6.5-7.1 2.8 82.0-85.6 36.9 4.8-5.7 49.6
4.1-4.3 10.7 6.0-6.5 8.1 78.4-82.0 12.7 3.8-4.8 4.1 3.9-4.1 20.8
5.4-6.0 18.7 74.8-78.4 0.4 Less than 3.8 0 3.7-3.9 29.5 4.8-5.4
27.2 Less than 74.8 0 3.5-3.7 22.7 4.3-4.8 22.8 3.3-3.5 9.6 3.7-4.3
13.4 3.2-3.3 2.6 3.1-3.7 4.4 3.0-3.2 0.4 2.6-3.1 1.2 Less than 3.0
0 2.0-2.6 0.3 Less than 2.0 0
Comparative Example 3
(Production Method of Alloy by the Raw Powder Mixing Method)
[0113] The 64 alloy containing copper powder was produced in a
condition similar to Example 1, except that mixed powder in which
aluminum powder (60 wt %) and vanadium powder (40%) are weighed in
certain amounts and uniformly mixed was used instead of the 64
alloy powder.
[0114] There is no significant difference in mechanical properties
between the 64 alloy produced and the results of Table 1 of Example
1. However, the production cost was almost double to three times
compared to the material produced in Example 1. This is mainly
because of difference in cost of the 64 alloy powder.
Comparative Example 4
(Alloy by Melting Method)
[0115] The 64 alloy block instead of alloy powder used in Example
1, and electrolyzed copper were prepared. The electrolyzed copper
was mixed at 3, 5, and 10 wt %, and copper containing 64 alloy
ingots of diameter (1)100 each having the above corresponding
copper content were obtained by using an electron beam melting
furnace.
[0116] Test pieces were cut out of the copper containing 64 alloy
ingots, mechanical properties thereof were investigated, and the
results are shown in Table 8. Tensile strength of the ingots
produced in the Comparative Example was 20% to 25% lower than the
value in Example 1.
[0117] Distribution of copper in the ingot was investigated by
using a CX ray micro analyzer in order to determine the cause.
There was a region observed in which the Cu concentration was less
than 1/10 versus the average concentration, such as being 0.3 to
0.5%, and a region was observed in which the Cu concentration was
more than ten times versus the average concentration, such as being
20% to 40%, over a wide range greater than 1 mm.sup.3.
[0118] In light of the above test results, it was confirmed that
the titanium alloy according to the present invention has
mechanical properties superior to those of a titanium alloy
produced by a conventional melting method. Furthermore, by using
alloy powder produced by the pre-alloy method used in the present
invention, it was confirmed that production cost can be reduced 30
to 40% even though the mechanical properties were of the same level
as in the conventional raw powder mixing method.
TABLE-US-00008 TABLE 8 Copper Yield Tensile content strength
strength Elongation Hardness No. (%) (MPa) (MPa) (%) (Hv) C.
Example 4-1 3 1020 1080 5% 370 C. Example 4-2 5 1080 1140 4% 400 C.
Example 4-3 10 1150 1200 3% 480
Example 4
(Cu Added 5% to Ti-10V-2Fe-3Al Alloy Powder)
[0119] Cut chips and cut powder of Ti-10V-2Fe-3Al alloy ingot was
hydrogenated to produce hydrogenated product thereof, and it was
crushed, ground, and sifted to obtain alloy powder of D50=50 .mu.m.
Electrolyzed copper powder used in Example 1 was added at 5% to
this powder, so as to obtain mixed powder consisting of
Ti-10V-2Fe-3Al alloy powder and electrolyzed copper powder. This
mixed powder was charged in a mild steel capsule and was processed
by Hot-extrusion. The extrusion was performed after heating for 2
hours at 800.degree. C. Observation of structure, tensile test,
hardness measurement, and EPMA observation of the extruded material
were performed. The crystal particle diameter, yield strength,
tensile strength, elongation, and hardness are shown in Table
9.
[0120] By X ray mapping of EPMA in a manner similar to that in
Example 3, correction coefficients were calculated according to
EPMA count and average concentration of each of Ti, V, Fe, Al, and
Cu, and concentration distribution of each composition was
measured. The results are shown in Table 10.
Comparative Example 5
(Ti-10V-2Fe-3Al Alloy Power, Copper Powder Not Added)
[0121] Ti-10V-2Fe-3Al alloy powder produced in Example 4 was
inserted into the mild steel capsule without mixing copper powder,
and it was processed by Hot-extrusion. The extrusion conditions
were the same as in Example 4. Observation of structure, tensile
test, and hardness measurement of the extruded material were
performed. The results are shown in Table 9.
Example 5
(Cu Powder Added 5% to Ti-15V-3Al-3Cr-3Sn Alloy Powder)
[0122] Cut chips and cut powder of a Ti-15V-3Al-3Cr-3Sn alloy ingot
was hydrogenated to produce a hydrogenated product thereof, and it
was crushed, ground, and sifted to obtain an alloy powder of D50=50
.mu.m. Electrolyzed copper powder used in Example 1 was added at 5%
to this powder, so as to obtain mixed powder consisting of
Ti-15V-3Al-3Cr-3Sn alloy powder and electrolyzed copper powder.
This mixed powder was inserted in a mild steel capsule and was
processed by Hot-extrusion. The extrusion was performed after
heating for 2 hours at 750.degree. C. Observation of structure,
tensile test, hardness measurement, and EPMA observation of the
extruded material were performed. The crystal particle diameter,
yield strength, tensile strength, elongation, and hardness are
shown in Table 9.
[0123] By X-ray mapping of EPMA in a manner similar to that in
Example 3, correction coefficients were calculated according to
EPMA count and average concentration of each of Ti, V, Al, Cr, Sn,
and Cu, and concentration distribution of each composition was
measured. The results are shown in Table 11.
Comparative Example 6
(Ti-15V-3Al-3Cr-3Sn Alloy Powder, Copper Powder Not Added)
[0124] The Ti-15V-3Al-3Cr-3Sn alloy powder produced in Example 5
was inserted into the mild steel capsule without mixing copper
powder, and it was processed by Hot-extrusion. The extrusion
conditions were the same as in Example 5. Observation of structure,
tensile test, and hardness measurement of the extruded material
were performed. The results are shown in Table 9.
Example 6
(Cu Powder Added 5% to Ti-4.5Al-3V-2Fe-2Mo Alloy Powder)
[0125] Cut chips and cut powder of a Ti-4.5Al-3V-2Fe-2Mo alloy
ingot was hydrogenated to produce hydrogenated product thereof, and
it was crushed, ground, and sifted to obtain alloy powder of D50=50
.mu.m. Electrolyzed copper powder used in Example 1 was added at 5%
to this powder, so as to obtain a mixed powder consisting of
Ti-4.5Al-3V-2Fe-2Mo alloy powder and electrolyzed copper powder.
This mixed powder was filled into a mild steel capsule and was
processed by Hot-extrusion. The extrusion was performed after
heating for 2 hours at 880.degree. C. Observation of structure,
tensile test, hardness measurement, and EPMA observation of the
extruded material were performed. The crystal particle diameter,
yield strength, tensile strength, elongation, and hardness are
shown in Table 9.
[0126] By X-ray mapping of EPMA in a manner similar to that of
Example 3, correction coefficients were calculated according to
EPMA count and average concentration of each of Ti, Al, V, Fe, Mo,
and Cu, and concentration distribution of each composition was
measured. The results are shown in Table 12.
Comparative Example 7
(Ti-4.5Al-3V-2Fe-2Mo Alloy Powder, Copper Powder Not Added)
[0127] The Ti-4.5Al-3V-2Fe-2Mo alloy powder produced in Example 6
was filled into the mild steel capsule without mixing copper
powder, and it was processed by Hot-extrusion. The extrusion
conditions were the same as in Example 6. Observation of structure,
tensile testing, and hardness measurement of the extruded material
were performed. The results are shown in Table 9.
Example 7
(Cu Powder Added 5% to Ti-5Al-5V-5Mo-3Cr Alloy Powder)
[0128] Cut chips and cut powder of a Ti-5Al-5V-5Mo-3Cr alloy ingot
were hydrogenated to produce a hydrogenated product thereof, and it
was crushed, ground, and sifted to obtain alloy powder of D50=50
.mu.m. Electrolyzed copper powder used in Example 1 was added at 5%
to this powder, so as to obtain a mixed powder consisting of
Ti-5Al-5V-5Mo-3Cr alloy powder and electrolyzed copper powder. This
mixed powder was filled into a mild steel capsule and processed by
Hot-extrusion. The extrusion was performed after heating for 2
hours at 840.degree. C. Observation of structure, tensile testing,
hardness measurement, and EPMA observation of the extruded material
were performed. The crystal particle diameter, yield strength,
tensile strength, elongation, and hardness are shown in Table
9.
[0129] By X-ray mapping of EPMA in a manner similar to that in
Example 3, correction coefficients were calculated according to
EPMA count and the average concentration of each of Ti, Al, V, Fe,
Mo, and Cu, and concentration distribution of each composition was
measured. The results are shown in Table 13.
Comparative Example 8
(Ti-5Al-5V-5Mo-3Cr Alloy Powder, Copper Powder Not Added)
[0130] Ti-5Al-5V-5Mo-3Cr alloy powder produced in Example 7 was
filled into the mild steel capsule without mixing copper powder,
and it was processed by Hot-extrusion. The extrusion conditions
were the same as in Example 7. Observation of structure, tensile
testing, and hardness measurement of the extruded material were
performed. The results are shown in Table 9.
Example 8
(Cu Powder Added 5% to Ti-5Al-4V-0.6Mo-0.4Cr Alloy Powder)
[0131] Cut chips and cut powder of a Ti-5Al-4V-0.6Mo-0.4Cr alloy
ingot were hydrogenated to produce a hydrogenated product thereof,
and this was crushed, ground, and sifted to obtain an alloy powder
of D50=50 .mu.m. Electrolyzed copper powder used in Example 1 was
added at 5% to this powder, so as to obtain mixed powder consisting
of Ti-5Al-4V-0.6Mo-0.4Cr alloy powder and electrolyzed copper
powder. This mixed powder was inserted in a mild steel capsule and
was processed by Hot-extrusion. The extrusion was performed after
heating for 2 hours at 900.degree. C. Observation of structure,
tensile testing, hardness measurement, and EPMA observation of the
extruded material were performed. The crystal particle diameter,
yield strength, tensile strength, elongation, and hardness are
shown in Table 9.
[0132] By X-ray mapping of EPMA in a manner similar to that in
Example 3, correction coefficients were calculated according to
EPMA count and average concentration of each of Ti, Al, V, Mo, Cr,
and Cu, and concentration distribution of each composition was
measured. The results are shown in Table 14.
Comparative Example 9
[0133] (Ti-5Al-4V-0.6Mo-0.4Cr Alloy Powder, Copper powder Not
Added)
[0134] Ti-5Al-4V-0.6Mo-0.4Cr alloy powder produced in Example 8 was
filled into the mild steel capsule without mixing copper powder,
and it was processed by Hot-extrusion. The extrusion conditions
were the same as in Example 8. Observation of structure, tensile
testing, and hardness measurement of the extruded material were
performed. The results are shown in Table 9.
TABLE-US-00009 TABLE 9 Crystal Copper Yield Tensile particle
content strength strength Elongation Hardness diameter No. Alloy
(%) (MPa) (MPa) (%) (Hv) (.mu.m) Example 4 Ti--10V--2Fe--3Al 5 1330
1470 9 420 20 Example 5 Ti--15V--3Al--3Cr--3Sn 5 1180 1310 10 400
20 Example 6 Ti--4.5Al--3V--2Fe--2Mo 5 1070 1200 11 360 15 Example
7 Ti--5Al--5V--5Mo--3Cr 5 1250 1350 9 450 15 Example 8
Ti--5Al--4V--0.6Mo--0.4Cr 5 980 1080 13 370 20 C. Example 5
Ti--10V--2Fe--3Al -- 1200 1300 9 350 20 C. Example 6
Ti--15V--3Al--3Cr--3Sn -- 1020 1100 12 330 20 C. Example 7
Ti--4.5Al--3V--2Fe--2Mo -- 900 980 13 300 15 C. Example 8
Ti--5Al--5V--5Mo--3Cr -- 1060 1150 9 330 15 C. Example 9
Ti--5Al--4V--0.6Mo--0.4Fe -- 820 900 15 300 20
TABLE-US-00010 TABLE 10 Ti V Fe Al Cu Concentration Intensity
Concentration Intensity Concentration Intensity Concentration
Intensity Concentration Intensity More than 89.6 0 More than 13.5 0
More than 3 0 More than 3.8 0 More than 8.2 0 85.5-89.6 1.3
12.9-13.5 0.2 2.4-3.sup. 15 3.4-3.8 8 7.6-8.2 0.2 82.5-85.5 28.5
12.2-12.9 1.6 1.8-2.4 31 2.9-3.4 25 7.1-7.6 0.9 78.8-82.5 38.9
11.5-12.2 5.5 1.2-1.8 38 2.4-2.9 34 6.5-7.1 2.9 74.3-78.8 22.6
10.8-11.5 18.7 0.8-1.2 16 1.8-2.4 20 6.0-6.5 8.3 71.1-74.3 7.8
10.0-10.8 27.6 Less than 0.8 0 1.4-1.8 8 5.4-6.0 18.7 66.4-71.1 0.9
9.2-10.0 27.8 0.9-1.4 5 4.8-5.4 26.8 Less than 66.4 0 8.4-9.2 14.2
Less than 0.9 0 4.3-4.8 23.5 7.6-8.4 3.6 3.7-4.3 13.1 7.0-7.6 0.6
3.1-3.7 4.4 6.4-7.0 0.2 2.6-3.1 1.1 Less than 6.4 0 2.0-2.6 0.1
Less than 2.0 0
TABLE-US-00011 TABLE 11 Ti V Al Cr Sn Cu Concen- Concen- Concen-
Concen- Concen- Concen- tration Intensity tration Intensity tration
Intensity tration Intensity tration Intensity tration Intensity
More than 0 More than 0 More than 0 More than 0 More than 0 More
than 0 81.6 17.9 3.8 3.8 3.8 8.2 78.5-81.6 1.1 17.1-17.9 0.2
3.4-3.8 8 3.4-3.8 7 3.4-3.8 5 7.6-8.2 0.2 74.1-78.5 28.7 16.5-17.1
1.6 3.1-3.4 28 3.1-3.4 25 3.1-3.4 28 7.1-7.6 0.9 70.3-74.1 38.7
15.9-16.5 5.5 2.7-3.1 33 2.7-3.1 34 2.7-3.1 36 6.5-7.1 2.9
67.1-70.3 22.3 15.2-15.9 18.7 2.2-2.7 18 2.2-2.7 21 2.2-2.7 22
6.0-6.5 8.3 63.9-67.1 8.3 14.5-15.2 27.6 1.8-2.2 9 1.8-2.2 9
1.8-2.2 7 5.4-6.0 19.2 59.9-63.9 0.9 13.9-14.5 27.8 1.5-1.8 4
1.5-1.8 4 1.5-1.8 2 4.8-5.4 26.8 Less than 0 13.2-13.9 14.2 Less
than 0 Less than 0 Less than 0 4.3-4.8 23.5 59.9 1.5 1.5 1.5
12.4-13.2 3.6 3.7-4.3 13.3 11.7-12.4 0.6 3.1-3.7 4.5 11.1-11.7 0.2
2.6-3.1 0.3 Less than 0 2.0-2.6 0.1 11.1 Less than 0 2.0
TABLE-US-00012 TABLE 12 Ti Al V Fe Mo Cu Concen- Concen- Concen-
Concen- Concen- Concen- tration Intensity tration Intensity tration
Intensity tration Intensity tration Intensity tration Intensity
More than 0 More than 0 More than 0 More than 0 More than 0 More
than 0 88.5 3.8 3.6 2.5 2.5 8.2 84.3-88.5 1.1 3.5-3.8 7 3.5-3.6 7
2.2-2.5 10 2.3-2.5 3 7.6-8.2 0.2 80.2-84.3 28.7 3.1-3.5 27 3.3-3.5
28 1.9-2.2 32 2.1-2.3 28 7.1-7.6 0.9 76.4-80.2 38.7 2.7-3.1 33
3.2-3.3 34 1.6-1.9 38 1.9-2.1 36 6.5-7.1 3.1 72.5-76.4 22.3 2.4-2.7
19 3.1-3.2 19 1.3-1.6 20 1.7-1.9 23 6.0-6.5 8.5 69.0-72.5 8.3
2.1-2.4 10 3.0-3.1 9 Less than 0 1.5-1.7 8 5.4-6.0 19.2 1.3
65.5-69.0 0.9 1.8-2.1 4 2.8-3.0 3 1.3-1.5 2 4.8-5.4 26.4 Less than
0 Less than 0 2.7-2.8 0 Less than 0 4.3-4.8 23.3 65.5 1.8 1.3
2.5-2.7 3.7-4.3 13.4 2.4-2.5 3.1-3.7 4.5 2.2-2.4 2.6-3.1 0.4 Less
than 2.0-2.6 0.1 2.2 Less than 0 2.0
TABLE-US-00013 TABLE 13 Ti Al V Mo Cr Cu Concen- Concen- Concen-
Concen- Concen- Concen- tration Intensity tration Intensity tration
Intensity tration Intensity tration Intensity tration Intensity
More than 0 More than 0 More than 0 More than 0 More than 0 More
than 0 95.5 6.1 5.9 5.7 3.8 8.2 91.3-95.5 0.8 5.6-6.1 7 5.7-5.9 0.3
5.3-5.7 3 3.4-3.8 6 7.6-8.2 0.2 87.5-91.3 22.4 5.1-5.6 27 5.5-5.7
1.6 4.9-5.3 28 3.1-3.4 25 7.1-7.6 1.1 83.9-87.5 40.4 4.6-5.1 33
5.3-5.5 5.5 4.4-4.9 34 2.7-3.1 33 6.5-7.1 2.9 80.1-83.9 26.2
4.1-4.6 18 5.1-5.3 18.7 4.1-4.4 23 2.2-2.7 22 6.0-6.5 8.3 76.6-80.1
9.1 3.6-4.1 10 4.9-5.1 27.6 3.7-4.1 9 1.8-2.2 11 5.4-6.0 18.7
73.1-76.6 1.1 3.1-3.6 5 4.7-4.9 27.3 3.3-3.7 3 1.5-1.8 3 4.8-5.4
26.4 Less than 0 Less than 0 4.5-4.7 14.4 Less than 0 Less than 0
4.3-4.8 23.5 73.1 3.1 3.3 1.5 4.2-4.5 3.6 3.7-4.3 13.5 4.0-4.2 0.7
3.1-3.7 4.9 3.7-4.0 0.3 2.6-3.1 0.4 Less than 0 2.0-2.6 0.1 3.7
Less than 0 2.0
TABLE-US-00014 TABLE 14 Ti Al V Mo Fe Cu Concen- Concen- Concen-
Concen- Concen- Concen- tration Intensity tration Intensity tration
Intensity tration Intensity tration Intensity tration Intensity
More than 0 More than 0 More than 0 More than 0 More than 0 More
than 0 97.1 6.1 5.0 1.3 1.0 8.2 93.7-97.1 1.1 5.6-6.1 8 4.8-5.0 0.4
1.1-1.3 3 0.8-1.0 13 7.6-8.2 0.2 90.2-93.7 22.2 5.1-5.6 26 4.6-4.8
1.6 1.0-1.1 26 0.6-0.8 31 7.1-7.6 1.4 86.5-90.2 40.1 4.6-5.1 32
4.4-4.6 5.4 0.8-1.0 36 0.4-0.6 39 6.5-7.1 3.7 82.7-86.5 26.5
4.1-4.6 18 4.2-4.4 18.3 0.7-0.8 24 0.2-0.4 17 6.0-6.5 8.3 79.1-82.7
9.2 3.6-4.1 11 4.0-4.2 27.9 0.5-0.7 9 Less than 0 5.4-6.0 17.9 0.2
75.3-79.1 0.9 3.1-3.6 5 3.8-4.0 27.2 0.4-0.5 2 4.8-5.4 26.6 Less
than 0 Less than 0 3.6-3.8 14.4 Less than 0 4.3-4.8 22.8 75.3 3.1
0.4 3.4-3.6 3.6 3.7-4.3 13.5 3.2-3.4 0.8 3.1-3.7 4.9 3.0-3.2 0.4
2.6-3.1 0.6 Less than 0 2.0-2.6 0.1 3.0 Less than 0 2.0
[0135] The present invention relates to titanium alloy produced by
a powder method and to a method for production thereof. In the
present invention, strong and hard titanium alloy containing copper
in high concentration, which has been difficult to produce by a
conventional method, and having no segregation of copper, can be
produced at lower cost than in a conventional method.
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