[0001]
The present invention relates to a method for producing a titanium casting
10 product for hot rolling made of commercially pure titauium, particularly to a titanium
casting product that cau keep excellent surface properties after hot rolling even when
a breakdown process such as slabing, forging, or the like is omitted aud a method for
producing the same.
15 Background Art
[0002]
In general, commercially pure titanium uses titanium sponge or titanium
scrap as a raw material. It is melted by non-consumable electrode arc remelting,
electron-beam remelting, plasma arc remelting, or the like into a titanium ingot
20 (titanium casting product). Non-consumable arc remelting uses titanium. sponge
pressed into a briquette as au electrode, aud causes arc discharge between the
electrode aud a mold to melt the electrode itself aud cast it into the mold, thereby
obtaining au ingot. Therefore, uniform discharge between the electrode aud the
mold is necessary, which limits the shape of the mold to a cylindrical shape;
25 accordingly, the shape of the ingot after casting is a cylindrical shape. On the other
haud, electron-beam remelting aud plasma arc remelting, which use electron beams
aud plasma arc, respectively, differ in melting method, but both the methods pour
molten titanium melted on a hearth into a mold, aud this allows free selection of the
shape of the mold; thus, it is possible to produce ingots with various shapes, such as
30 a rectaugular shape aud a billet shape, as well as a cylindrical shape.
[0003]
------------~-
PCT/JP2014/076076
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In the current titanium material production process, after this, a hot working
process, such as slabing or forging, which is called an ingot breakdown process, is
carried out and then hot rolling is performed; the breakdown process is necessary.
However, according to the shapes, it is considered that the breakdown process can be
5 omitted in producing a sheet material for a rectangular ingot (slab) and in producing
a bar or a wire rod for a cylindrical ingot and a billet, and a technology of performing
hot rolling without the breakdown process has been under study. If this technology
is established, it can be expected that cost will be improved by omission of a process
and an enhancement in yield.
10 [0004]
However, a titanium casting product produced by electron-beam remelting
or plasma arc remelting is as-cast and therefore comprises coarse grains with sizes as
large as several tens of millimeters. In regard to such a titanium casting product,
when hot rolling is performed without a breakdown process, because of the coarse
15 grains, the influence of deformation anisotropy in a grain and between crystal grains
causes surface unevenness, leading to surface defects. In order to remove surface
defects that occur in hot rolling, it is necessary to increase the amount of pickling of
the surface of a hot-rolled material in a pickling process, which is the following
process, and accordingly yield is worsened and may result in an increase in cost.
20 [0005]
Accordingly, for a titanium ingot produced by electron-beam remelting or
plasma arc remelting, while it is expected that cost will be improved by omission of a
breakdown process carried out by slabing, forging, or the like, there is a concern that
an increase in surface defects may cause an increase in cost. This has inhibited
25 practical utilization of a titanium casting product obtained without a breakdown
process.
[0006]
Patent Literature 1 discloses a method that provides an excellent casting
surface and can improve surface defects after hot rolling even when an ingot
30 breakdown process is omitted in the following case: in a cross-sectional
microstructure of a titanium slab produced in an electron beam remelting furnace and
PCT/JP2014/076076
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extracted directly from a mold, an angle 9 formed by the solidification direction from
the snrface layer toward the interior and the casting direction of the slab is in the
range of 45 to 90°, or in the crystal orientation distribution of the snrface layer, an
angle formed by the c-axis .of hcp and the normal to the slab surface layer is in the
5 range of 35 to 90°. That is, controlling the shape and crystal orientation of crystal
grains of the surface suppresses occurrence of defects due to coarse crystal grains.
[0007]
In Patent Literature 2, as a method for directly performing hot rolling
without an ingot breakdown process for a titanium material, the snrface layer at a
10 snrface corresponding to a snrface to be rolled is subjected to melting and
resolidification by high-frequency induction heating, arc heating, plasma heating,
electron-beam heating, laser heating, and the like; thus, a portion from the surface
layer to a depth of 1 mm or more undergoes grain refining. This slab surface layer
is quenched and solidified to have fine and irregular crystal orientation distribution,
15 which prevents occurrence of surface defects.
20
Patent Literature
[0008]
Patent Literature 1:
Patent Literature 2:
Technical Problem
Citation List
W0/2010/090353
JP 2007 -332420A
Sunnnary ofinvention
25 [0009]
The present invention provides a titanium casting product and a method for
producing the same, where the titanium casting product is obtained without either
any need of a cutting and conditioning process for an as-cast titanium casting product
surface layer or any breakdown process and the occurrence of the surface defects is
30 suppressed in a titanium material after subsequent hot rolling.
.I
PCT/JP2014/076076
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Solution to Problem
[0010]
The present inventors carried out extensive studies in order to achieve the
object. The resulting findings are as follows. When an as-cast titanium casting
5 product produced by electron-beam remelting or plasma arc remelting, as a method
for melting a titanium casting product made of pure titanium, is subjected to hot
rolling without a breakdown process, which has been conventionally necessary, a
material (powder, a chip, wire, or foil) containing a.~ stabilizer element is placed or
applied on the surface layer at a surface to be rolled of the as-cast titanium casting
10 product, and the surface layer of a titanium material is melted with the material as a
pre-process of the hot rolling. In this manner, a layer having a higher ~ stabilizer
element concentration than a base material, i.e., a ~ stabilizer element-rich layer, is
formed in the surface layer of the titanium material. This makes it possible to keep
excellent surface properties after hot rolling.
15 [0011]
20
That is, the present invention is as described below.
(1)
A titanium casting product made of commercially pure titanium,
compnsmg:
a layer containing one or more kinds of ~ stabilizer element in a range of I
mm or more in depth at a surface serving as a surface to be rolled,
wherein an average value of~ stabilizer element concentration in a range of
within 1 mm in depth is higher than ~ stabilizer element concentration in a base
material by, in mass%, equal to or more than 0.08 mass% and equal to or less than
25 1.50 mass%.
30
(2)
The titanium casting product according to (1 ),
wherein the~ stabilizer element (s) is/are one or more of Fe, Ni, and Cr.
(3)
The titanium casting product according to (1 ), containing one or more
kinds of a stabilizer elements or neutral elements together with the ~ stabilizer
element (s).
(4)
5/30
PCT/JP2014/076076
A method for producing a titanium casting product, comprising
melting a surface serving as a surface to be rolled of a titanium casting
5 product together with a material containing a ~ stabilizer element and then
solidifYing the surface to make an average value of~ stabilizer element concentration
in a range of within 1 mm in depth higher than ~ stabilizer element concentration in a
base material by, in mass%, equal to or more than 0.08 mass% and equal to or less
than 1.50 mass%, the titanium casting product being made of commercially pure
10 titanium.
(5)
The method for producing a titanium casting product according to ( 4),
wherein the material containing the ~ stabilizer element is in a form of any
of powder, a chip, wire, and foil.
15 (6)
20
The method for producing a titanium casting product according to ( 4 ),
wherein the surface serving as the surface to be rolled of the titanium
casting product is melted by electron-beam heating or plasma heating, the titanium
casting product being made of commercially pure titanium.
Advantageous Effects of Invention
[0012]
With a titanium casting product according to the present invention, even
when hot rolling is performed without a breakdown process such as slabing, forging,
25 or the like, which has been conventionally necessary, a titanium material having
surface properties equivalent to those of a conventional material can be produced.
A reduction in heating time due to omission of the breakdown process, a reduction in
cutting treatment achieved by smoothing of the surface layer of the titanium casting
product due to surface layer melting, a reduction in the amount of pickling due to an
30 enhancement in surface properties of the titanium material after hot rolling, and the
like lead to an enhancement in yield, producing an effect of reducing production
PCT/JP2014/076076
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cost; the present invention offers a great effect in industry.
Brief Description of Drawings
[0013]
5 [FIG. 1] FIG. 1 schematically shows a change in concentration of a molten and
resolidified layer.
10
Description of Embodiments
[0014]
Hereinafter, the present invention will be described in detail.
[0015]
In the present invention, commercially pure titanium includes commercially
pure titanium specified by classes 1 to 4 of the JIS standard, and classes 1 to 4 of the
ASTM standard and 3.7025 of the DIN standard corresponding thereto. That is,
15 commercially pure titanium of interest in the present invention can be said to be
titanium consisting of C: equal to or less than 0.1 mass%, H: equal to or less than
0.015 mass%, 0: equal to or less than 0.4 mass%, N: equal to or less than 0.07
mass%, Fe: equal to or less than 0.5mass%, and the balance: Ti. Note that Fe
contained in a large amount as compared with other ~ stabilizer elements in
20 commercially pure titanium is substantially contained in an amount of approximately
0.020 to 0.05 mass% in JIS classes 1 and 2, and approximately 0.08 mass% in JIS
class 3.
[0016]
Titanium casting products of interest in the present invention include
25 rectangular ingots (slab ingots), cylindrical ingots, and billet ingots. The surface
layer of a titanium casting product with such a shape is melted together with a
material containing a ~ stabilizer element, so that surface defects are suppressed for a
titanium material after hot rolling.
[0017]
30 In the present invention, only a surface layer part of an as-cast titanium
casting product is heated to be melted l mm or more in depth. The surface layer
PCT/JP2014/076076
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part of the titanium casting product melted in this manner is quenched and
resolidified after melting, and a cross-sectional microstructure of a molten and
resolidified layer cooled to room temperature (a solidified layer that is obtained by
melting only a surface layer part of an as-cast titanium casting product by heating
5 and then performing quenching and resolidification in this manner is called a
"molten and resolidified layer") is a fine acicular microstructure. Moreover, in
melting the surface layer, the surface layer of a base material is melted concurrently
with a p stabilizer element; thus, the p stabilizer element concentration in the molten
and resolidified layer becomes higher than that in the base material, and consequently,
10 an enhancement in hardenability due to the addition of the p stabilizer element makes
the molten and resolidified layer have an even finer microstructure. The
"enhancement in hardenability" here refers to low temperature transformation
achieved by shifting the nose of transformation in continuous cooling to the longtime
side by containing the p stabilizer element in the surface layer of the titanium
15 casting product. The purpose of the low temperature transformation is to increase
nucleation sites to make crystal grains finer.
[0018]
As will be described later, in the present invention, the formed molten and
resolidified layer includes a deep portion and a shallow portion. In the present
20 invention, the specified depth of the molten and resolidified layer is 1 mm or more;
this depth refers to the depth of the shallowest portion as viewed in a cross-section in
a direction perpendicular to a scanning direction of a molten bead.
[0019]
Normally, commercially pure titanium is subjected to hot rolling in a single-
25 phase region, which is below p transformation point temperature. Therefore, a
titanium casting product is heated to a-phase high temperature region, which is the
temperature of heating for hot rolling. In general, commercially pure titanium
contains, as an alloy element, a p stabilizer element, such as Fe, in a trace amount,
and thus a+p temperature region slightly exists. In normal commercially pure
30 titanium, however, the a+P temperature region is a very narrow temperature region
of only several tens of degrees. In contrast, in a titanium casting product obtained
PCT/JP2014/076076
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by adiling a ~ stabilizer element to the surface layer of the above-described titanium
casting product and melting the ~ stabilizer element concurrently with the surface
layer of the titanium material and performing resolidification, the ~ stabilizer element
concentration in the surface layer is higher than that in the base material. The
5 stability of ~ phase is therefore high in the molten and resolidified layer, which
widens the temperature region of the a+~ region; thus, the interior of the molten and
resolidified layer can be brought into the state of the a+~ region in heating for hot
rolling. Since the ~ phase forms in a grain boundary of a phase, grain growth of the
a phase is suppressed, so that fine crystal grains after the melting and resolidification
10 can be maintained until hot rolling after heating for hot rolling. Accordingly,
unevenness of the surface of the titanium material due to coarse crystal grains can be
suppressed, and thus a titanium hot-rolled material without surface defects can be
produced.
15
[0020]
In addition, when melting is performed as described above, the ~ stabilizer
element is not dispersed uniformly at the molten surface of the titanium casting
product, and consequently a region with a high concentration of the element forms
partially, in which portion the temperature region of the a+~ region can be further
widened, so that grain growth of the a phase in heating for hot rolling can be further
20 suppressed.
[0021]
When the surface layer of the titanium casting product is remelted I mm or
more in depth as described above and then solidified, a portion from the surface layer
to a depth of 1 mm or more has a fine acicular microstructure obtained by
25 solidification after remelting, whereas the center side in the sheet thickness direction
of the titanium material with respect to the molten and resolidified layer and a
portion thermally influenced thereby keeps the microstructure as-cast. At least the
surface layer corresponding to a surface to be rolled of the titanium casting product is
remelted together with a material containing a ~ stabilizer element and then solidified,
30 so that the average value of concentrations of the ~ stabilizer element in a portion
from the surface layer to a depth of 1 mm in the molten and resolidified layer is
PCT/JP2014/076076
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higher than the ~ stabilizer element concentration in the base material by, in mass%,
equal to or more than 0.08 mass% and equal to or less than 1.50 mass%. As the ~
stabilizer element, a plurality of ~ stabilizer elements may be added in combination,
in which case the ~ stabilizer element concentration refers to the sum of the
5 concentrations of the contained ~ stabilizer elements. If a difference in ~ stabilizer
· element coqcentration between the base material and the molten and resolidified
layer is less than 0.08 mass%, the addition of the ~ stabilizer element does not
sufficiently provide the effects of enhancing hardenability and suppressing crystal
grain growth, and surface defects easily occur in the titanium material after hot
10 rolling. In order to further exert the effect of suppressing surface defects, the ~
stabilizer element concentration difference preferably exceeds 0.2 mass%, and it is
most preferable that the ~ stabilizer element difference exceed 0.5 mass%.
Moreover, when the difference in ~ stabilizer element concentration between the base
material and the molten and resolidified layer is within the aforementioned range, the
15 ~ stabilizer element-enriched layer at the surface layer is removed by pickling carried
out by shot blasting and pickling, which are processes after hot rolling, and the ~
stabilizer element enriched in the molten and resolidified layer is detoxified. That
is, the processes of shot blasting and pickling removes the ~ stabilizer elementenriched
layer, making it possible to obtain components and mechanical properties
20 equivalent to those of a cold-rolled sheet produced by a normal method. However,
if the difference in ~ stabilizer element concentration between the base material and
the molten and resolidified layer is more than 1.50 mass%, the volume fraction of the
~ phase in the surface layer of the titanium casting product increases in hot rolling, so
that a slab surface layer portion is oxidized intensely as compared with the base
25 material. Furthermore, the increase in the ~ stabilizer element concentration in the
surface layer of the titanium casting product may lead to an increase in the hardness
of the molten and resolidified layer as compared with the base material, causing
surface crack or the like in hot rolling. These causes make it necessary to increase
the amount of pickling of the surface in a pickling process, which significantly
30 reduces yield. In addition, it becomes difficult to detoxify the ~ stabilizer elementenriched
layer in a post-process. Hence, the average value of concentrations of the
PCT/JP2014/076076
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~ stabilizer element in a portion from the surface layer to a depth of 1 mrn is made to
differ from the ~ stabilizer element concentration in the base material by 1.50 mass%
or less. In addition, although the specified melting depth is 1 mrn or more, too deep
melting depth may cause the ~ stabilizer element -enriched layer to remain after the
5 processes of shot blasting and pickling; hence, it is desirable that the melting depth
be approximately 5 mrn or less.
[0022]
Moreover, normally, a titanium casting . product in casting undergoes
solidification from a surface layer part of the titanium casting product in contact with
10 the mold; therefore, components slightly differ between the surface layer and the
interior of the titanium casting product depending on distribution of a solute for each
element. Since a ~ stabilizer element, such as Fe, exhibits normal segregation, in
solidification or in transformation, the Fe concentration in the surface layer part of
the titanium casting product decreases and the Fe concentration tends to become
15 higher toward the interior of the titanium casting product. Therefore, it is very
effective to make the ~ stabilizer element concentration in the molten and resolidified
layer equivalent to or higher than that in the base material by melting the ~ stabilizer
element and the base material concurrently.
[0023]
20 In addition, in casting of the titanium material, components are adjusted to
be uniform in the entire slab by controlling input of raw materials. However,
fluctuation of components or the like may occur partially. Therefore, even in
commercially pure titanium, JIS class 3 or JIS class 4, which originally has a high
content of Fe, which is a ~ stabilizer element, a region exists in which crystal grains
25 are not sufficiently fine in the molten and resolidified layer, according to component
fluctuation of Fe, and surface defects often occur partially after hot rolling. Hence,
it is very effective to add a~ stabilizer element in melting and resolidification to raise
the amount of the ~ stabilizer element added; thus, partial surface defects can also be
suppressed.
30 [0024]
In a cross-section in a direction perpendicular to a scanning direction of a
li
PCT/JP2014/076076
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molten bead, the molten and resolidified layer tends to be deepest at the center of the
molten bead in remelting of the surface layer of the titanium casting product, and,
when molten beads are overlapped, is shallowest at a portion midway between
adjacent molten beads, the deepest portion and the shallowest portion being repeated
5 periodically. Here, if a difference between the deepest portion and the shallowest
portion is large, this difference causes a difference in deformation resistance in hot
rolling, which may cause defects. Hence, it is desirable that the above difference be
less than 2 mm. Note that in the present invention, the specified depth of the
molten and resolidified layer is 1 mm or more; this depth refers to the depth of the
10 shallowest portion as viewed in a cross-section in a direction perpendicular to a
scanning direction of a molten bead.
[0025]
Description will be given on a method for measuring the depth of the molten
and resolidified layer and ununiformity of the molten and resolidified layer. A
15 portion cut out from the surface layer portion of the titanium casting product in a
cross-section in a direction perpendicular to a scanning direction of a molten bead is
used as an embedding and polishing sample for scanning electron microscopy
(SEM)/ an electron probe microanalyser (EPMA); thus, the molten and resolidified
layer can be distinguished easily. In the present invention, since the depth of the
20 molten and resolidified layer is defined as the depth of the shallowest portion, a
melting depth can be simply obtained by elemental mapping analysis. FIG. 1 shows
an example of measured values of changes in concentration of the base material and
the molten and resolidified layer. This is obtained by linear analysis of ~ stabilizer
element concentration in the thickness direction from a base material portion near the
25 surface layer at a surface to be rolled of the titanium casting product toward the
surface to be rolled. In the base material, the ~ stabilizer element concentration is
low and substantially uniform, whereas in the molten and resolidified layer, the ~
stabilizer element concentration is high and also exhibits concentration fluctuation,
which indicates ununiformity.
30 [0026]
Examples of the ~ stabilizer element include V, Mo, Fe, Cr, Mn, Ta, Nb, Ni,
--~~~--------~----~--~---~---·~·--------
PCT/JP2014/076076
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Co, Cu, and W. In titanium, however, an element such as W or Ta having a high
melting point causes high density inclusion (HDI), and serves as a starting point of
fatigue when it remains in the titanium material without being melted or without
being diffused sufficiently; therefore, such an element needs to be used with care.
5 Moreover, Mo, Nb, and the like have lower melting points than W and Ta, but still
have melting points of 2000°C or higher; therefore, when using Mo or Nb, it is
desirable to alloy it with an element such as Ti in advance to make the melting point
lower and add the resulting alloy. ~ stabilizer elements can be classified into a
complete solid solution type, such as V, Mo, Ta, and Nb, and an eutectoid type, such
10 as Fe, Cr, Mn, Co, Ni, and Cu. ~stabilizer elements of the eutectoid type have low
solid solubility but have high ~ stabilizing ability; therefore, addition of a ~ stabilizer
element of the eutectoid type is effective even in a small amount. In regard to Fe,
Cr, Mn, Co, Ni, and Cu, which are of the eutectoid type, surface defects after hot
rolling can be suppressed when ~ stabilizer element concentration in the molten and
15 resolidified layer is higher than that in the base material by approximately 0.08 to
0.60 mass%; hence, this range is preferable. In regard to V, Mo, Ta, and Nb, which
are of the complete solid solution type, which have low ~ stabilizing ability as
compared with the eutectoid type, an effect is more easily exerted by adding a ~
stabilizer element in a large amount such that ~ stabilizer element concentration in
20 the molten and resolidified layer is higher than that in the base material by
approximately 0.60 to 1.50 mass%. Even when a ~ stabilizer element of the
eutectoid type is used, since quenching is performed in solidification after remelting,
cooling rate is high and no precipitate forms, and also in heating for hot rolling, no
precipitate forms because the state is the a+~ region. Furthermore, the material
25 containing the ~ stabilizer element may contain an a stabilizer element typified by Al,
or a neutral element, such as Sn or Zr. Either one or both of an a stabilizer element
and a neutral element may be contained. The total amount of an a stabilizer
element and a neutral element in the molten and resolidified layer is preferably 2.0
mass% or less with respect to the base material. Fe, Ni, and Cr, which are relatively
30 inexpensive ~ stabilizer elements, are preferably used as the material to be melted
together with the surface layer of the as-cast titanium casting product. It is also
5
PCT/JP20 14/076076
13/30
effective to use Fe powder or the like or stainless steel powder or the like, or utilize
crushed scrap of ordinary steel or stainless steel. Similarly, crushed scrap of
titanium alloy may be used.
[0027]
The material used for adding the ~ stabilizer element to the surface layer of
the casting product may have any of the shapes of powder, a chip, wire, and foil, and
it is desirable that the material be in a small piece. It is effective to use any of the
following materials: powder with a particle size in a.range of 1 fill1 to 0.5 mm, a chip
with a size in a range of 2 mm square to 5 mm square, wire with a diameter in a
10 range of 0.5 mm to 5 mm, and foil with a thickness in a range of 1 fill1 to 0.1 mm.
Such a material is disposed uniformly on the surface of the casting product when
placed or applied on the surface of the casting product; thus, a region with the same
concentration as the concentration in the base material can be reduced at the surface
layer of the titanium casting product, which provides a titanium casting product with
15 more excellent surface properties.
[0028]
Methods for melting the surface layer together with the ~ stabilizer element
include electron-beam heating, arc heating, laser heating, and induction heating.
Titanium is active metal, and when the surface layer is melted in atmospheric air, a
20 molten portion is oxidized significantly. Hence, the following methods are suitable:
electron-beam heating, arc heating (in particular, a heating method using inert gas,
such as plasma arc heating or tungsten inert gas (TIG) welding), laser heating, and
the like, which can perform treatment in a vacuum atmosphere or an inert gas
atmosphere. The aforementioned treatment can be performed by any of these
25 methods. Of these, electron-beam heating or plasma arc heating, which can apply
high energy at once, is suitable for industry and preferred to be used.
[Examples]
[0029]
30 Hereinafter, the present invention will be described m more detail m
Examples.
Difference in {3 stabilizer element concentration (mass%)
No. Glade
between base material and molten and resolidified layer
(surface layer 1 mm) Melting method
Form of additive Fo Cc N; Fe+Cr+Ni
1 Pure titanium JIS class 1 none Q.OO - Q,QQ none
2 Pure titanium JIS class 1 none Q,QQ 0.00 none
3 Pure titanium JJS class 1 none Q,QQ Q,QQ electron beam
4 Pure titanium JIS class 1 Fe powder 0 07 Q.Ql electron beam
5 Pure titanium JIS class 1 Fe powder 0.22 0.22 electron beam
6 Pure titanium JJS class 1 Fe powder 0.08 0.08 electron beam
7 Pure titanium JJS class 1 Fe powder 0.87 0.87 electron beam
a Pure titanium JIS class 2 Fe powder 1.50 1.50 electron beam
9 Pure titanium JIS class 2 Fe powder 0.49 0.49 electron beam
10 Pure titanium JIS class 1 Fe powder 1.65 JM electron beam
11 Pure titanium JIS class 1 Fe chip 0.13 0.13 electron beam
12 Pure titanium JIS class 2 Fe chip 1.30 1.30 electron beam
13 Pure titanium JIS class 1 Fe wire 0.11 - - 0.11 electron beam
14 Pure titanium JJS class 1 Fe wire 1.39 - - 1.39 electron beam
15 Pure titanium JIS class 1 Fe foil 0.20 - 0.20 electron beam
16 Pure titanium JIS class 1 Fe foil 1.36 - 1.36 electron beam
17 Pure titanium JIS class 1 Fe powder 0.14 0.14 plasma arc
16 Pure titanium JIS class 2 Fe powder 1.35 1.35 plasma arc
19 Pure titanium JIS class 1 SUS304 powder 0.05 0,01 0,01 0.07 electron beam
20 Pure titanium JIS class 1 SUS304 powder 0.06 0.02 0,01 0.09 electron beam
21 Pure titanium JIS class 1 SUS304 powder 0.14 0.04 0.02 020 electron beam
22 Pure titanium JIS class 2 SU$304 powder 0.98 0.24 0.11 1.33 electron beam
23 Pure titanium JIS class 1 SUS430 powder 0.06 O.D1 Q.Ql electron beam
24 Pure titanium JIS class 1 SUS430 powder 0.08 O.D1 0.09 electron beam
25 Pure titanium JIS class 1 SUS430 powder 0.65 0.12 0.77 electron beam
26 Pure titanium JIS class 2 SUS430 powder 1.16 0.22 1.38 electron beam
27 Pure titanium JIS class 1 Or chip 0.00 0.12 0.12 electron beam
28 Pure titanium JIS class 1 Or chip 0.00 0.25 0.25 electron beam
29 Pure titanium JJS class 2 Or chip 0.00 1.70 - 170 electron beam
30 Pure titanium JJS class 1 Ni chip 0.00 0.05 QQq electron beam
31 Pure titanium JIS class 1 Ni chip 0.00 0.16 0.16 electron beam
32 Pure titanium JIS class 2 Ni chip 0.00 1.20 1.20 electron beam
33 Pure titanium JIS class 1 none Q,QQ 000 none
34 Pure titanium JIS class 1 Fe powder 0.06 Q.ru; electron beam
35 Pure titanium JJS class 2 Fe powder 1.30 1.30 electron beam
36 Pure titanium JJS class 1 Or chip 0.00 0.35 0.35 electron beam
37 Pure titanium JIS class 1 Ni chip 0.00 1.47 1.47 electron beam
Depth of
molten layer Slabbing Surface defects
(mm)
0 y., minor
0 No coarse
2 No partial!y coarse defects
2 No partially coarse defects
05 No partially coarse defects
3 No partially somewhat coarse defects
1 No minor
5 No minor
7 No minor
4 No partially coarse defects
3 No partially somewhat coarse defects
3 No minor
3 No partially somewhat coarse defects
3 No minor
3 No minor
3 No minor
4 No minor
4 No minor
2 No partially coarse defeats
2 No partially somewhat coarse defects
2 No minor
2 No minor
2 No partially coarse defects
2 No partially somewhat coarse defects
2 No minor
2 No minor
3 No partially somewhat coarse defects
3 No minor
3 No partially coarse defeats
3 No partially coarse defeats
3 No partially somewhat coarse defects
3 No minor
0 y., minor
3 No partially coarse defects
3 No minor
3 No minor
3 No minor
Evaluation
Good
Poor
Poor
Poor
Poor
Fair
Good
Good
Fair
Poor
Fair
Good
Fair
Good
Good
Good
Good
Good
Poor
Fair
Good
Good
Poor
Fair
Good
Good
Fair
Good
Poor
Poor
Fair
Good
Good
Poor
Good
Good
Good
Remarks
Reference Example
Comparative Example
Comparative Example
Comparative Example
Comparative Example
Example
Example
Example
Example
Comparative Example
Example
Example
Example
Example
Example
Example
Example
Example
Comparative Example
Example
Example
Example
Comparative Example
Example
Example
Example
Example
Example
Comparative Example
Comparative Example
Example
Example
Reference Example
Comparative Example
Example
Example
Example
~ ~ o;l 0
0
-0" w 0 " ~ -~
-it 0
"d
~
"0 "
>-'
.~..,
0>
.0. .,
0>
Difference in 8 ·stabilizer element concentration (mass~i)
No. Glade between base material and molten and resolidified layer (surface layer 1 mm) Surface defects Evaluation Remarks
Form of additive Fe I Mo I V I Ta j Mn J Nb Co Gu c. Sum
38 Pure titanium JIS class 1 Ti-Mo chip 0.00 I 0.06 I - I - I - I - I 0.06 partially coarse defects J Poor J Comparative Example
.32. ...~. '" ,_ ~-"~ l-"~ "'1 ~-~--~~.:.-~!:!.~..::!!~-=!_a~ o13 - ---=-L::_ _ I - -____ z .____!i-M~~l.e ___ ~~~-- o32 - - ___ _L __ ::_l.-=.J . -=-"· -=~
.-.. ~-~ .... . ~re_titanium~~~-~~-~--.. ~--M~ehip _ 000 -~-S~ ---=- __ =..__L_:=I- . -. - _F'"' ~"ni'!"_:l!~_:!•_=:_ __ l _Il-Mo chip _ 09~. _'l'!. =- - L .. J -~~~..:::::t~. 43 Pu" titonlom JIS clo« 1 V chip 000 - 007 - I - I - 1 - ~
0.13 I partially somewhat coarse defects~air"_ i Example '--~__:~~-·-o~(.fp~rti.· a~y. ".me~t-z;~.d.e f~ct~: F~.. ir . .C.omparati':._.e ~~~~~--~
-=. 0.6~- ------~-~-o-'--·~·~- GO?~-- .?~r:;Jn~rati~.:..!:_~amp.!!_ t==: .LQl;-~- _partially co~~~c~~- --~o~ _Compar~.!!.'~e Examp..!!_
' Q.Ql 1 partially coarse defects Poor Comparative Example
44 Pure titanium JIS class V chip 0.00 024 I - i - I 0.24 !partially somewhat coarse defects I Fak I Example
45 I Pure titanium JIS class 2 I V chip I G.OO J - I 0.67 J - I - I - I - J - J - J 0.67 J minor J Good J Example
46 Pure titanium JIS class 1 Mn chip ~5-]·----~ - Q,QQ I partially coarse defects Comparative Example
47 Pure titanium JIS class 1 Mn chip I 0.22 _1_ I 0.22 minor Example
48 I Pure titanium J!S clnss 2 ! Mn chip I 0.00 I - I - I - j 1.31__ .l___- I - ! - J :::-:::-.. J 1.34 minor ! Good Example
;~ -~;~~i;;~:~~:~~= =i;~~~:::::: =~}~~== --= _== ~t =~ J=Hif_ =-= ~:~- =- -~¥.- ----·=-~;;~ :~=~===~-~:: _.~: =~~~::~~-==-~
--~--- --~~---~~-~i~--:!!.~~ss ~- __ ...£~=-~~~~~p___ ~!i_.r=-- --=--- _. =-.... [1 •... .::...~-r-=-- ... ...=._ .. .=... -~ ~-Par!!.?.!!Y.. c~rse ~~cts ~-· ---~~ __ _0Jrfll!~~~~~--~~am~~~q,
~2_ _ --~-:.:..!'_!:~nium JIS _c la~.::..! .. -----~~!:iE.. __ ~E~ ---=---··· ~=-- ~=-~ _::_ ___ L.=..-t_?_;_f!!.__ '--=----r-:-__ -~- -~·-·-earti~~-~5:!.efects ····- ____ Poor-··· Co~arative -~~-':!!.E.I_:.._
53 Pure titanium JIS clnss 1 Go chip 0.00 - - - - -T - 0.23 - - 0.23 minor Good Example
54
55
56
57
58
59
60
~--~ 62
63
64
65
66
67
68
Pure titanium J[S ~-·'-~~-~- "L '"'· ·'·'- 0.00 I I Q.11 0.11 1 minor Good Example I vv '-"'"'"'
Pure titanium JlS class 1
Pure titanilltl""! JIS class 1
Pure titanium JlS class 2
Pure titanium JIS class 1
Pure titanium JIS ciass 1
·---~--------····--····
Pure titanium JIS class 2
---~----·--·-·--····-
Pure titanitnn JIS cl=s 1
~0---··-··----·
Pure titanium JIS class 1
-······-···--·····--···-··-~ ... ·-~·-
Pure titanium JIS cl1!.Ss 2
Pure titanium JIS class 3
Pure titanium JIS cl1!.Ss 3
Pure titanium JIS class 3
Pure titanium JIS class 4
Pure titanium J!S class 4
Ou chip o.oo I - I - I - I - I - I - I O.D7
Cu chip o.ool-1-1- -l-1-10.16
Cu chip o.oo I - I - I - ! - [ - ! - I 12s
6-4V chip o.oo 1 - 1 o.os I - I - I - I
6-4" _ ... ,_
... _ _?.~-~rl!.!:__.
15-3-3-3 c~ip_
15-3-~-3 chip
15--3-3--3 chip
. _..,~ ~-"'"~-1 ___ :::__1_o.1z.t-=-L- 1--=-L _ _ •, . .-~:-~~-·--~---=--·- --6~-~ --·-·--=-·--l+- -=-:---+r·--=----1 +· --=--~I
~,b~----=- ~~:- =..1 1,·-:::-t- :::_l =- . . '
Fe chip 0.051-1-1-l- -1
Fe chip 0.861-1-1-l-1-
Fe chip 1~ I - I - I - I - I - I
Fe chip 0.061-1-1-i-1-l
Fe chip 0.96 I - I - I - I - ! - _l
0."07 partially coarse defects Po« Comparative Example
0.16 minor Good Comparative Example
128 I minor I Good I Comparative Example
.Q.,Q§. I partially coarse defects ! Poor I Comparative Example
+--~·- 0.12 J~:Ual!~me~at coarse ~efects~ '"' r ~
I - 0.64 I minor . . Good Comparative Exarnpl_e _
, __ o.ot o.o~L~=pa~~~~~~~-d-;-fuc:t~~~ -~Po