U.S. patent application number 12/232198 was filed with the patent office on 2009-03-19 for low density titanium alloy, golf club head, and process for prouducing low density titanium alloy part.
This patent application is currently assigned to DAIDO TOKUSHUKO KABUSHIKI KAISHA. Invention is credited to Toshiharu Noda, Michiharu Ogawa.
Application Number | 20090074606 12/232198 |
Document ID | / |
Family ID | 40454673 |
Filed Date | 2009-03-19 |
United States Patent
Application |
20090074606 |
Kind Code |
A1 |
Ogawa; Michiharu ; et
al. |
March 19, 2009 |
Low density titanium alloy, golf club head, and process for
prouducing low density titanium alloy part
Abstract
The present invention relates to a low density titanium alloy,
containing: 7.1 to 10.0 mass % of Al; 0.1 to 3.0 mass % of Fe; 0.01
to 0.3 mass % of O; 0.5 mass % or less of N; 0.5 mass % or less of
C; and a remainder being Ti and inevitable impurities; a golf club
head using the alloy; and a production method for a low density
titanium alloy part using the alloy. The alloy of the invention may
further contain 0.01 to 2.0 mass % of V. The alloy of the invention
has higher specific strength as compared to the Ti-6Al-4V alloy, is
excellent in hot workability, and is reduced in cost.
Inventors: |
Ogawa; Michiharu;
(Nagoya-shi, JP) ; Noda; Toshiharu; (Nagoya-shi,
JP) |
Correspondence
Address: |
BACON & THOMAS, PLLC
625 SLATERS LANE, FOURTH FLOOR
ALEXANDRIA
VA
22314-1176
US
|
Assignee: |
DAIDO TOKUSHUKO KABUSHIKI
KAISHA
Nagoya
JP
|
Family ID: |
40454673 |
Appl. No.: |
12/232198 |
Filed: |
September 12, 2008 |
Current U.S.
Class: |
420/420 ;
420/418 |
Current CPC
Class: |
A63B 53/04 20130101;
C22C 14/00 20130101; A63B 60/00 20151001; A63B 2209/00
20130101 |
Class at
Publication: |
420/420 ;
420/418 |
International
Class: |
C22C 14/00 20060101
C22C014/00 |
Foreign Application Data
Date |
Code |
Application Number |
Sep 14, 2007 |
JP |
2007-239713 |
Claims
1. A low density titanium alloy, comprising: 7.1 to 10.0 mass % of
Al; 0.1 to 3.0 mass % of Fe; 0.01 to 0.3 mass % of O; 0.5 mass % or
less of N; 0.5 mass % or less of C; and a remainder being Ti and
inevitable impurities.
2. The low density titanium alloy according to claim 1, further
comprising: 0.01 to 2.0 mass % of V.
3. The low density titanium alloy according to claim 1, further
comprising; 2.0 mass % or less of at least one element selected
from the group consisting of Cr, Ni, and Mo.
4. The low density titanium alloy according to claim 2, further
comprising: 2.0 mass % or less of at least one element selected
from the group consisting of Cr, Ni, and Mo.
5. The low density titanium alloy according to claim 1, further
comprising: at least one of 0.01 to 0.3 mass % of B, and 0.01 to
0.3 mass % of Si.
6. The low density titanium alloy according to claim 2, further
comprising: at least one of 0.01 to 0.3 mass % of B, and 0.01 to
0.3 mass % of Si.
7. The low density titanium alloy according to claim 3, further
comprising: at least one of 0.01 to 0.3 mass % of B, and 0.01 to
0.3 mass % of Si.
8. The low density titanium alloy according to claim 4, further
comprising: at least one of 0.01 to 0.3 mass % of B, and 0.01 to
0.3 mass % of Si.
9. The low density titanium alloy according to claim 1, which has a
specific strength of 205 or more.
10. The low density titanium alloy according to claim 2, which has
a specific strength of 205 or more.
11. The low density titanium alloy according to claim 3, which has
a specific strength of 205 or more.
12. The low density titanium alloy according to claim 4, which has
a specific strength of 205 or more.
13. The low density titanium alloy according to claim 5, which has
a specific strength of 205 or more.
14. The low density titanium alloy according to claim 6, which has
a specific strength of 205 or more.
15. The low density titanium alloy according to claim 7, which has
a specific strength of 205 or more.
16. The low density titanium alloy according to claim 8, which has
a specific strength of 205 or more.
17. The low density titanium alloy according to claim 1, which has
a reduction of area at 1000.degree. C. of 40% or more and a flow
stress at 1000.degree. C. of 200 MPa or less.
18. The low density titanium alloy according to claim 2, which has
a reduction of area at 1000.degree. C. of 40% or more and a flow
stress at 1000.degree. C. of 200 MPa or less.
19. The low density titanium alloy according to claim 3, which has
a reduction of area at 1000.degree. C. of 40% or more and a flow
stress at 1000.degree. C. of 200 MPa or less.
20. The low density titanium alloy according to claim 4, which has
a reduction of area at 1000.degree. C. of 40% or more and a flow
stress at 1000.degree. C. of 200 MPa or less.
21. The low density titanium alloy according to claim 5, which has
a reduction of area at 1000.degree. C. of 40% or more and a flow
stress at 1000.degree. C. of 200 MPa or less.
22. The low density titanium alloy according to claim 6, which has
a reduction of area at 1000.degree. C. of 40% or more and a flow
stress at 1000.degree. C. of 200 MPa or less.
23. The low density titanium alloy according to claim 7, which has
a reduction of area at 1000.degree. C. of 40% or more and a flow
stress at 1000.degree. C. of 200 MPa or less.
24. The low density titanium alloy according to claim 8, which has
a reduction of area at 1000.degree. C. of 40% or more and a flow
stress at 1000.degree. C. of 200 MPa or less.
25. The low density titanium alloy according to claim 9, which has
a reduction of area at 1000.degree. C. of 40% or more and a flow
stress at 1000.degree. C. of 200 MPa or less.
26. The low density titanium alloy according to claim 10, which has
a reduction of area at 1000.degree. C. of 40% or more and a flow
stress at 1000.degree. C. of 200 MPa or less.
27. The low density titanium alloy according to claim 11, which has
a reduction of area at 1000.degree. C. of 40% or more and a flow
stress at 1000.degree. C. of 200 MPa or less.
28. The low density titanium alloy according to claim 12, which has
a reduction of area at 1000.degree. C. of 40% or more and a flow
stress at 1000.degree. C. of 200 MPa or less.
29. The low density titanium alloy according to claim 13, which has
a reduction of area at 1000.degree. C. of 40% or more and a flow
stress at 1000.degree. C. of 200 MPa or less.
30. The low density titanium alloy according to claim 14, which has
a reduction of area at 1000.degree. C. of 40% or more and a flow
stress at 1000.degree. C. of 200 MPa or less.
31. The low density titanium alloy according to claim 15, which has
a reduction of area at 1000.degree. C. of 40% or more and a flow
stress at 1000.degree. C. of 200 MPa or less.
32. The low density titanium alloy according to claim 16, which has
a reduction of area at 1000.degree. C. of 40% or more and a flow
stress at 1000.degree. C. of 200 MPa or less.
Description
FIELD OF THE INVENTION
[0001] The present invention relates to a low density titanium
alloy, a golf club head, and a process for producing a low density
titanium alloy part, more specifically, to a low density titanium
alloy having high specific strength and excellent in hot
workability, a golf club head using the low density titanium alloy,
and a process for producing a low density titanium alloy part using
the low density titanium alloy.
BACKGROUND OF THE INVENTION
[0002] Practical titanium alloys are broadly classified into:
[0003] (1) an .alpha. type alloy formed of an .alpha.-phase (low
temperature phase) of a hexagonal closed packed lattice;
[0004] (2) a .beta. type alloy formed of a .beta.-phase (high
temperature phase) of a body-centered cubic crystal; and
[0005] (3) an .alpha.+.beta. type alloy having a mixed structure of
the .alpha.-phase and the .beta.-phase.
[0006] Among the above, the .alpha.+.beta. type alloy is a
well-balanced material as being excellent in strength, specific
strength, heat processability, workability, corrosion resistance,
and the like, and therefore it has heretofore been used mainly as
an aerospace material. Furthermore, the .alpha.+.beta. type alloy
has heretofore been used as an automobile material, a mechanical
structure part material, a general civilian goods material, and the
like. Particularly, a Ti-6Al-4V alloy among the .alpha.+.beta. type
alloys has widely been used as a general purpose high tensile
titanium alloy, and about 80% of whole the Ti alloy consumption is
occupied with the Ti-6Al-4V alloy consumption.
[0007] However, the Ti-6Al-4V alloy entails a high cost since it
contains V which is expensive. Further, although the Ti alloys are
generally high in specific strength, further reduction in cost and
further improvement in specific strength has been in demand for
certain applications such as application in golf club head.
[0008] In order to solve the above problems, various proposals have
heretofore been made.
[0009] For instance, Patent Reference 1 discloses an .alpha.+.beta.
type Ti alloy containing, in terms of mass %, 5.5% to 7.0% of Al,
0.5% to 4.0% of Fe, 0.5% or less of O, and a remainder being Ti and
inevitable impurities.
[0010] The Patent Reference 1 discloses that:
[0011] (1) it is possible to impart mechanical property equal to or
better than the conventional Ti-6Al-4V alloy by using Fe in place
of V and mixing Fe at a predetermined ratio, and
[0012] (2) it is possible to produce the Ti alloy at an
industrially low cost since Fe is less expensive than V.
[0013] Patent Reference 2 discloses a high strength Ti alloy
containing, in terms of mass %, 5.00% to 7.00% of Al, 1.00 to 3.50%
of V, more than 0.40% but 1.00% or less of Fe, 0.20% to 0.50% of O,
0.05% or less of C, 0.05% or less of N, and a remainder being
substantially Ti, in which a V equivalent (=V %+4.2Fe %) is 3.00%
to 5.50%.
[0014] The Patent Reference 2 discloses that:
[0015] (1) it is possible to achieve strength that is higher than
or equal to the Ti-6Al-4V alloy by substituting a portion of V of
Ti-6Al-4V by Fe and maintaining the V equivalent within the
predetermined range; and
[0016] (2) it is possible to produce a high strength Ti alloy at a
low cost since it is possible to use, as a raw material, an
inexpensive sponge titanium containing Fe as impurity.
[0017] Further, Patent Reference 3 discloses a high strength Ti
alloy contaihing, in terms of mass %, 5.50% to 7.00% of Al, 0.50%
to 4.00% of Fe, 0.02% to 0.10% of N, 0.05% to 0.40% of O, and a
remainder being Ti and inevitable impurities.
[0018] The Patent Reference 3 discloses that:
[0019] (1) it is possible to achieve strength that is higher than
or equal to the Ti-6Al-4V alloy by substituting V of Ti-6Al-4V by
Fe and adding the appropriate amount of N; and
[0020] (2) it is possible to produce a high strength Ti alloy at a
low cost since it is possible to use, as a raw material, an
inexpensive sponge titanium containing Fe as impurity.
[0021] Patent Reference 1: Japanese Patent No. 3306878
[0022] Patent Reference 2: JP-A-2001-115221
[0023] Patent Reference 3: JP-A-2004-10963
SUMMARY OF THE INVENTION
[0024] In recent years, there has been an increasing demand for
achievement of a lower density of a golf club head among golf
equipment manufacturers. Therefore, Ti-6Al-1Fe alloy is being used
as a low density titanium alloy for golf club heads.
[0025] However, the effect of the Ti-6Al-1Fe alloy for the
achievement of low density is weaker than that of a Ti-6Al-4V alloy
that is the representative titanium alloy.
[0026] An increase in content of Al which is a light element is
effective for the achievement of low density. However, a simple
increase in Al content entails a reduction in hot workability.
[0027] An object of the invention is to provide a low density
titanium alloy having higher specific strength as compared to the
Ti-6Al-4V alloy, excellent in hot workability, and reduced in cost;
a golf club head using the low density titanium alloy; and a low
density titanium alloy part using the low density titanium
alloy.
[0028] In order to attain the above-described object, the present
invention relates to the following items 1 to 32.
[0029] 1. A low density titanium alloy, comprising:
[0030] 7.1 to 10.0 mass % of Al;
[0031] 0.1 to 3.0 mass % of Fe;
[0032] 0.01 to 0.3 mass % of O;
[0033] 0.5 mass % or less of N;
[0034] 0.5 mass % or less of C; and
[0035] a remainder being Ti and inevitable impurities.
[0036] 2. The low density titanium alloy according to item 1,
further comprising:
[0037] 0.01 to 2.0 mass % of V.
[0038] 3. The low density titanium alloy according to item 1,
further comprising:
[0039] 2.0 mass % or less of at least one element selected from the
group consisting of Cr, Ni, and Mo.
[0040] 4. The low density titanium alloy according to item 2,
further comprising:
[0041] 2.0 mass % or less of at least one element selected from the
group consisting of Cr, Ni, and Mo.
[0042] 5. The low density titanium alloy according to item 1,
further comprising:
[0043] at least one of
[0044] 0.01 to 0.3 mass % of B, and
[0045] 0.01 to 0.3 mass % of Si.
[0046] 6. The low density titanium alloy according to item 2,
further comprising:
[0047] at least one of
[0048] 0.01 to 0.3 mass % of B, and
[0049] 0.01 to 0.3 mass % of Si.
[0050] 7. The low density titanium alloy according to item 3,
further comprising:
[0051] at least one of
[0052] 0.01 to 0.3 mass % of B, and
[0053] 0.01 to 0.3 mass % of Si.
[0054] 8. The low density titanium alloy according to item 4,
further comprising:
[0055] at least one of
[0056] 0.01 to 0.3 mass % of B, and
[0057] 0.01 to 0.3 mass % of Si.
[0058] 9. The low density titanium alloy according to item 1, which
has a specific strength of 205 or more.
[0059] 10. The low density titanium alloy according to item 2,
which has a specific strength of 205 or more.
[0060] 11. The low density titanium alloy according to item 3,
which has a specific strength of 205 or more.
[0061] 12. The low density titanium alloy according to item 4,
which has a specific strength of 205 or more.
[0062] 13. The low density titanium alloy according to item 5,
which has a specific strength of 205 or more,
[0063] 14. The low density titanium alloy according to item 6,
which has a specific strength of 205 or more.
[0064] 15. The low density titanium alloy according to item 7,
which has a specific strength of 205 or more.
[0065] 16. The low density titanium alloy according to item 8,
which has a specific strength of 205 or more.
[0066] 17. The low density titanium alloy according to item 1,
which has a reduction of area at 1000.degree. C. of 40% or more and
a flow stress at 1000.degree. C. of 200 MPa or less.
[0067] 18. The low density titanium alloy according to item 2,
which has a reduction of area at 1000.degree. C. of 40% or more and
a flow stress at 1000.degree. C. of 200 MPa or less.
[0068] 19. The low density titanium alloy according to item 3,
which has a reduction of area at 1000.degree. C. of 40% or more and
a flow stress at 1000.degree. C. of 200 MPa or less.
[0069] 20. The low density titanium alloy according to item 4,
which has a reduction of area at 1000.degree. C. of 40% or more and
a flow stress at 1000.degree. C. of 200 MPa or less.
[0070] 21. The low density titanium alloy according to item 5,
which has a reduction of area at 1000.degree. C. of 40% or more and
a flow stress at 1000.degree. C. of 200 MPa or less.
[0071] 22. The low density titanium alloy according to item 6,
which has a reduction of area at 1000.degree. C. of 40% or more and
a flow stress at 1000.degree. C. of 200 MPa or less.
[0072] 23. The low density titanium alloy according to item 7,
which has a reduction of area at 1000.degree. C. of 40% or more and
a flow stress at 1000.degree. C. of 200 MPa or less.
[0073] 24. The low density titanium alloy according to item 8,
which has a reduction of area at 1000.degree. C. of 40% or more and
a flow stress at 1000.degree. C. of 200 MPa or less.
[0074] 25. The low density titanium alloy according to item 9,
which has a reduction of area at 1000.degree. C. of 40% or more and
a flow stress at 1000.degree. C. of 200 MPa or less.
[0075] 26. The low density titanium alloy according to item 10,
which has a reduction of area at 1000.degree. C. of 40% or more and
a flow stress at 1000.degree. C. of 200 MPa or less.
[0076] 27. The low density titanium alloy according to item 11,
which has a reduction of area at 1000.degree. C. of 40% or more and
a flow stress at 1000.degree. C. of 200 MPa or less.
[0077] 28. The low density titanium alloy according to item 12,
which has a reduction of area at 1000.degree. C. of 40% or more and
a flow stress at 1000.degree. C. of 200 MPa or less.
[0078] 29. The low density titanium alloy according to item 13,
which has a reduction of area at 1000.degree. C. of 40% or more and
a flow stress at 1000.degree. C. of 200 MPa or less.
[0079] 30. The low density titanium alloy according to item 14,
which has a reduction of area at 1000.degree. C. of 40% or more and
a flow stress at 1000.degree. C. of 200 MPa or less.
[0080] 31. The low density titanium alloy according to item 15,
which has a reduction of area at 1000.degree. C. of 40% or more and
a flow stress at 1000.degree. C. of 200 MPa or less.
[0081] 32. The low density titanium alloy according to item 16,
which has a reduction of area at 1000.degree. C. of 40% or more and
a flow stress at 1000.degree. C. of 200 MPa or less.
[0082] Furthermore, the present invention also relates to a golf
club head containing the above-mentioned low density titanium
alloy.
[0083] In addition, the present invention also relates to a process
for producing a low density titanium alloy part, the process
including: blending raw materials so as to obtain the
above-mentioned low density titanium alloy, followed by melting and
casting the raw materials to thereby obtain an ingot; and heating
the ingot to a temperature which is .beta. transus temperature or
higher and is 1200.degree. C. or lower, followed by forging or
rolling the ingot to thereby complete a rough processing step.
[0084] In the .alpha.+.beta. type low density titanium alloy, it is
possible to reduce density of the alloy by increasing an Al
content.
[0085] On the other hand, the increase in Al content generally
entails deterioration of hot workability. However, it is possible
to improve the hot workability while ensuring the low density by
optimizing a Fe content and an O content and optionally further
adding a very small amount of V, as well as increasing the Al
content.
[0086] Further, since Fe is contained in the alloy as a principal
addition element, it is possible to reduce a cost by using the
inexpensive raw materials and reducing the amount of expensive
V.
[0087] The low density titanium alloy according to the invention is
usable for various structure parts, parts for anti-corrosion, and
the like that are used for golf club heads, chemical industrial
apparatuses, electric appliances, aerospace appliances, airplanes,
boats and ships, wheeled vehicles, medical equipments, condensers,
heat exchangers, desalination apparatuses, and the like.
BEST MODE FOR CARRYING OUT THE INVENTION
[0088] Hereinafter, one embodiment of the invention will be
described in detail.
[0089] Herein, in the present specification, all the percentages
defined by mass are the same as those defined by weight.
1. Low Density Titanium Alloy
[0090] A low density titanium alloy according to the invention
contains following elements with a remainder being Ti and
inevitable impurities. Types of addition elements, component ratios
thereof, and reasons for limitation are as follows.
(1) 7.1.ltoreq.Al.ltoreq.10.0 Mass %
[0091] Al is the element that achieves solution hardening of an
.alpha.-phase of the alloy. Further, since Al is lighter than Ti,
Al acts for reducing density of the alloy (i.e. for achieving high
specific strength). In order to attain such effects, an Al content
may preferably be 7.1 mass % or more.
[0092] On the other hand, when the Al content is excessive, an
intermetallic compound Ti.sub.3Al is precipitated to cause
embrittlement of the alloy. Therefore, the Al content may
preferable by 10.0 mass % or less.
(2) 0.1.ltoreq.Fe.ltoreq.3.0 Mass %
[0093] Fe has an effect of stabilizing a .beta.-phase. In order to
attain such effect, a Fe content may preferably be 0.1 mass % or
more.
[0094] On the other hand, although strength is increased along with
an increase in Fe content, rigidity is increased when the Fe
content is excessive. Therefore, the Fe content may preferably be
3.0 mass % or less.
(3) 0.01.ltoreq.O.ltoreq.0.3 Mass %
[0095] O has an effect of strengthening the .alpha.-phase as being
dissolved into the .alpha.-phase. In order to attain such effect,
an O content may preferably be 0.01 mass % or more.
[0096] On the other hand, when the O content is excessive, rigidity
is increased to deteriorate ductibility. Therefore, the O content
may preferably be 0.3 mass % or less.
(4) N.ltoreq.0.5 Mass %
[0097] Similar to O, N has an effect of strengthening the
.alpha.-phase as being dissolved into the .alpha.-phase. On the
other hand, when a N content is excessive, an inclusion such as TiN
is formed, and the low density inclusion becomes the cause of
fatigue breaking to reduce fatigue strength. Therefore, the N
content may preferably be 0.5 mass % or less.
(5) C.ltoreq.0.5 Mass %
[0098] Similar to O and N, C has an effect of strengthening the
.alpha.-phase as being dissolved into the .alpha.-phase. On the
other hand, when a C content is excessive, carbonate is formed to
deteriorate hot workability. Therefore, the C content may
preferably be 0.5 mass % or less.
[0099] The low density titanium alloy according to the invention
may further contain one or more of elements described below.
(6) 0.01.ltoreq.V.ltoreq.2.0 Mass %
[0100] Similar to Fe, V has an effect of stabilizing a
.beta.-phase. In order to attain such effect, a V content may
preferably be 0.01 mass % or more.
[0101] On the other hand, when the V content is excessive, a
specific gravity is increased. Therefore, the V content may
preferably be 2.0 mass % or less.
[0102] In this regard, a pure metal or a Ti-6Al-4V alloy scrap may
be used as a V source in the production of the alloy.
(7) At Least One of Cr, Ni and Mo.ltoreq.2.0 Mass %
[0103] Each of Cr, Ni and Mo has an effect of stabilizing the
.beta.-phase. On the other hand, when a content of these elements
is excessive, a specific gravity is increased. Therefore, a sole or
total amount of at least one element selected from the group
consisting of Cr, Ni and Mo may preferably be 2.0 mass % or
less.
(8) 0.01.ltoreq.B.ltoreq.0.3 Mass %
(9) 0.01.ltoreq.Si.ltoreq.0.3 Mass %
[0104] Each of B and Si has an effect of fining grains. In order to
attain such effect, each of a B content and a Si content may
preferably be 0.01 mass % or more.
[0105] On the other hand, when the contents of these elements are
increased, crude boride and silicide are deposited to deteriorate
fatigue strength. Therefore, each of the B content and the Si
content may preferably be 0.3 mass % or less. In this regard, B and
Si may be added solely or both of them may be added
simultaneously.
2. Actions of Low Density Titanium Alloy
[0106] In the .alpha.+.beta. type low density titanium alloy, it is
possible to reduce density of the alloy by increasing the Al
content.
[0107] On the other hand, the increase in Al content generally
entails deterioration of hot workability. However, it is possible
to improve the hot workability while ensuring the low density by
optimizing a Fe content and an O content and optionally further
adding a very small amount of V, as well as increasing the Al
content.
[0108] Therefore, by optimizing contents of the addition elements,
it is possible to obtain:
[0109] (1) a low density titanium alloy having a specific strength
of 205 or more;
[0110] (2) a low density titanium alloy having a reduction of area
at 1000.degree. C. of 40% or more, and/or
[0111] (3) a low density titanium alloy having a flow stress at
1000.degree. C. of 200 MPa or less.
[0112] Since the low density titanium alloy according to the
invention contains Fe as the principal addition element, it is
possible to use, as a raw material, an inexpensive sponge titanium
containing Fe as impurity. Further, by adding Fe, it is possible to
reduce the amount of expensive V to be used. Therefore, it is
possible to reduce a cost of the low density titanium alloy.
[0113] Furthermore, since the low density titanium alloy according
to the invention has high specific strength and is excellent in hot
workability, it is possible to obtain, for example, a golf club
head, that is inexpensive, light-weight, and high in repulsion by
using the low density titanium alloy.
3. Process for Producing Low Density Titanium Alloy Part
[0114] A process for producing a low density titanium alloy part
according to the invention includes a melting/casting step, a rough
processing step, a finish processing step, and an annealing
step.
3.1. Melting/Casting Step
[0115] The melting/casting step is a step of blending raw materials
so as to obtain the low density titanium alloy of the invention,
followed by melting and casting the raw materials.
[0116] Since the low density titanium alloy according to the
invention contains Fe as the essential element, it is possible to
use, as a Ti source, not only a high purity sponge titanium but
also a low purity sponge titanium containing 0.1 to 2.0 mass % of
Fe or a Ti-6Al-4V alloy scrap. Therefore, it is possible to reduce
a cost for the titanium alloy part.
[0117] The melting/casting of the blended materials is not
particularly limited, and it is possible to employ a conventional
method.
3.2. Rough Processing Step
[0118] The rough processing step is a step of heating an ingot,
which is obtained by blending the raw materials so as to obtain the
low density titanium alloy according to the invention followed by
melting and casting the raw materials, to a temperature which is
.beta. transus temperature (.beta. transforming point) or higher
and is 1200.degree. C. or lower, followed by forging or rolling the
ingot.
[0119] When the processing temperature is too low, the
.alpha.-phase remains to cause cracking and creasing. Therefore,
the processing temperature in the rough processing may preferably
be the .beta. transus temperature or higher at which only the
.beta.-phase remains.
[0120] On the other hand, when the processing temperature is too
high, crystal grains tend to be coarsened. Therefore, the
processing temperature in the rough processing may preferably be
1200.degree. C. or less.
3.3. Finish Processing Step
[0121] The finish processing step is a step of performing a
finish-forging or finish-rolling of the low density titanium alloy
forged or rolled in the rough processing step after heating the
alloy to a temperature which is 600.degree. C. or higher and is
less than the .beta. transus temperature. The finish processing
step is performed according to the necessity.
[0122] When the finish processing step is performed at a relatively
low temperature, grains are fined to achieve high strength.
However, when the processing temperature is too low, flow stress is
increased to make the processing difficult. Therefore, the
processing temperature in the finish processing step may preferably
be 600.degree. C. or more.
[0123] On the other hand, when the processing temperature is too
high, grains tend to be coarsened due to recrystallization.
Therefore, the processing temperature in the finish processing step
may preferably be less than .beta. transus temperature.
3.4. Annealing Step
[0124] The annealing step is a step of annealing the low density
titanium alloy forged or rolled in the finish processing step. The
annealing step is performed according to the necessity.
[0125] The annealing is performed for the purpose of eliminating a
strain after the finish processing step. Annealing conditions are
not particularly limited, and optimum conditions may be selected
depending on the alloy composition.
EXAMPLES
Examples 1 to 40 and Comparative Examples 1 to 5
1. Preparation of Samples
[0126] Raw materials were weighed so as to achieve predetermined
compositions, and titanium alloy ingots each having a mass of 6 kg
and a diameter of 100 mm were produced through melting using a
plasma skull furnace. Shown in Table 1 are chemical compositions of
the thus-obtained ingots.
[0127] From each of the ingots, a test piece for high-temperature
high-speed tensile test was cut out.
[0128] Additionally, each of the ingots was heated to 1000.degree.
C., and a round bar having a diameter of 20 mm was obtained by hot
forging. Further, a heat treatment at 750.degree. C. for 2 h under
an air cooling (AC) was performed. From the round bar after the
heat treatment, a No. 3 tensile test piece (diameter: 6.35 mm,
evaluation distance: 25 mm) defined in ASTM E8 was prepared.
TABLE-US-00001 TABLE 1 Composition (mass %) Al Fe V O N C Others
Ex. 1 7.2 0.1 -- 0.07 0.01 0.01 Ex. 2 9.9 0.2 -- 0.09 0.02 0.01 Ex.
3 8.1 0.8 -- 0.14 0.01 0.01 Ex. 4 7.9 2.8 -- 0.16 0.02 0.02 Ex. 5
7.1 0.5 -- 0.27 0.01 0.01 Ex. 6 7.1 0.1 0.01 0.08 0.01 0.02 Ex. 7
7.5 0.2 0.02 0.05 0.02 0.01 Ex. 8 8.2 0.2 0.02 0.07 0.01 0.01 Ex. 9
8.5 0.2 0.02 0.09 0.02 0.01 Ex. 10 8.7 0.2 0.01 0.10 0.01 0.02 Ex.
11 9.0 0.1 0.01 0.08 0.02 0.01 Ex. 12 9.2 0.2 0.02 0.07 0.01 0.02
Ex. 13 9.5 0.2 0.02 0.06 0.01 0.01 Ex. 14 9.7 0.2 0.01 0.10 0.01
0.01 Ex. 15 9.9 0.2 0.01 0.10 0.02 0.01 Ex. 16 10.0 0.2 0.01 0.09
0.01 0.02 Ex. 17 8.2 0.8 0.02 0.15 0.01 0.01 Ex. 18 8.3 1.2 0.01
0.16 0.01 0.01 Ex. 19 8.0 1.5 0.02 0.14 0.01 0.02 Ex. 20 9.0 2.0
0.01 0.13 0.01 0.01 Ex. 21 8.8 2.2 0.01 0.15 0.02 0.01 Ex. 22 8.0
2.8 0.02 0.16 0.02 0.02 Ex. 23 7.8 3.0 0.01 0.17 0.01 0.02 Ex. 24
8.2 0.8 1.00 0.14 0.02 0.01 Ex. 25 8.0 1.0 1.20 0.15 0.01 0.02 Ex.
26 8.2 1.2 1.50 0.16 0.01 0.01 Ex. 27 8.5 0.9 1.80 0.15 0.01 0.01
Ex. 28 8.2 1.1 2.00 0.14 0.01 0.02 Ex. 29 7.1 0.5 0.02 0.21 0.01
0.01 Ex. 30 7.2 0.5 0.01 0.28 0.01 0.02 Ex. 31 7.1 0.5 0.02 0.13
0.30 0.01 Ex. 32 7.5 0.4 0.03 0.15 0.50 0.01 Ex. 33 7.2 0.4 0.02
0.13 0.01 0.10 Ex. 34 7.1 0.5 0.02 0.11 0.01 0.40 Ex. 35 7.5 0.4
0.03 0.02 0.01 0.01 Cr: 0.4, Ni: 0.1, Mo: 0.2 Ex. 36 7.4 0.3 0.02
0.02 0.01 0.02 Cr: 0.2, Ni: 0.1, Mo: 0.5 Ex. 37 7.1 0.5 0.02 0.01
0.01 0.01 B: 0.08 Ex. 38 7.5 0.4 0.03 0.02 0.01 0.02 B: 0.15 Ex. 39
7.2 0.3 0.03 0.02 0.01 0.03 Si: 0.02 Ex. 40 7.6 0.5 0.02 0.03 0.02
0.01 Si: 0.10 Comp. Ex. 1 10.5 1.0 0.03 0.15 0.01 0.02 Comp. Ex. 2
11.9 1.2 0.02 0.11 0.01 0.01 Comp. Ex. 3 13.0 1.3 0.03 0.15 0.01
0.01 Comp. Ex. 4 8.5 5.0 0.01 0.25 0.01 0.02 Comp. Ex. 5 6.0 4.00
0.12 0.03 0.01
2. Test Method
[0129] 2.1. High-Temperature High-Speed Tensile Test
[0130] A high-temperature high-speed tensile test was performed at
1000.degree. C. to measure flow stress and reduction of area at
1000.degree. C.
[0131] 2.2. Tensile Test
[0132] A tensile test was performed using an insutoron type tensile
test at a crosshead speed of 5.times.10.sup.-5 m/s machine to
measure tensile strength.
[0133] 2.3. Specific Strength
[0134] A specific gravity of each of the tensile test pieces was
measured by employing a water-impregnation method. Specific
strength was calculated from the detected specific gravity and
tensile strength.
[0135] 2.4. Manufacturability
[0136] Manufacturability was evaluated in terms of reduction of
area at 1000.degree. C. Those having reduction of area at
1000.degree. C. of 40% or more is evaluated as "good", and those
having reduction of area at 1000.degree. C. of less than 40% is
evaluated as "poor".
3. Results
[0137] Shown in Table 2 are test results. Comparative Examples 1 to
3 are remarkably poor in manufacturability due to the high content
of Al. Particularly, it was impossible to measure the flow stress
and reduction of area of Comparative Examples 2 and 3 having the Al
content exceeding 11 mass %. Comparative Example 4 having the Fe
content exceeding 3.0 mass % has poor manufacturability though it
has high tensile strength and specific strength. Comparative
Example 5 (Ti-4Al-6V alloy) has good manufacturability, but it has
low tensile strength and specific strength.
[0138] In contrast, each of Examples 1 to 40 has high tensile
strength and specific strength due to the appropriate content of
Al. Furthermore, each of Examples 1 to 40 also has good hot
workability due to the adjustment of the Fe content and the O
content and the optional addition of the small amount of V, as well
as the relatively increased Al content.
TABLE-US-00002 TABLE 2 High-Temperature High-Speed Tensile Test
(1000.degree. C.) Flow Reduction Tensile stress of Strength
Specific (MPa) area (%) (MPa) Strength Manufacturability Ex. 1 127
91 1040 238 good Ex. 2 148 73 1215 281 good Ex. 3 141 80 1155 264
good Ex. 4 152 69 1245 280 good Ex. 5 150 71 1230 281 good Ex. 6
127 91 1040 238 good Ex. 7 130 89 1065 244 good Ex. 8 133 87 1090
250 good Ex. 9 135 85 1100 253 good Ex. 10 137 83 1125 259 good Ex.
11 140 81 1150 265 good Ex. 12 142 79 1165 269 good Ex. 13 144 77
1180 272 good Ex. 14 146 75 1200 277 good Ex. 15 148 73 1215 281
good Ex. 16 150 70 1230 285 good Ex. 17 141 80 1155 264 good Ex. 18
143 78 1175 268 good Ex. 19 145 75 1190 270 good Ex. 20 147 73 1205
274 good Ex. 21 150 71 1230 279 good Ex. 22 152 69 1245 280 good
Ex. 23 155 66 1270 285 good Ex. 24 142 79 1170 267 good Ex. 25 144
77 1175 267 good Ex. 26 145 75 1180 268 good Ex. 27 147 73 1190 271
good Ex. 28 148 74 1200 272 good Ex. 29 145 75 1190 272 good Ex. 30
150 71 1230 281 good Ex. 31 152 69 1245 284 good Ex. 32 155 66 1270
290 good Ex. 33 135 85 1110 254 good Ex. 34 138 82 1130 258 good
Ex. 35 139 82 1140 259 good Ex. 36 137 83 1125 255 good Ex. 37 139
83 1140 260 good Ex. 38 141 80 1155 264 good Ex. 39 138 82 1130 258
good Ex. 40 140 80 1150 263 good Comp. 295 15 1350 311 poor Ex. 1
Comp. impossible impossible -- -- poor Ex. 2 to measure to measure
Comp. impossible impossible -- -- poor Ex. 3 to measure to measure
Comp. 205 38 1300 289 poor Ex. 4 Comp. 110 98 900 202 good Ex.
5
[0139] While the present invention has been described in detail and
with reference to specific embodiments thereof, it will be apparent
to one skilled in the art that various changes and modifications
can be made therein without departing from the spirit and scope
thereof.
[0140] The present application is based on Japanese Patent
Application No. 2007-239713 filed on Sep. 14, 2007 and Japanese
Patent Application No. 2008-231619 filed on Sep. 10, 2008, the
contents thereof being incorporated herein by reference.
* * * * *