U.S. patent application number 12/078378 was filed with the patent office on 2008-10-02 for austenitic free-cutting stainless steel.
This patent application is currently assigned to DAIDO TOKUSHUKO KABUSHIKI KAISHA. Invention is credited to Hisao Eto, Tetsuya Shimizu.
Application Number | 20080240970 12/078378 |
Document ID | / |
Family ID | 39494390 |
Filed Date | 2008-10-02 |
United States Patent
Application |
20080240970 |
Kind Code |
A1 |
Eto; Hisao ; et al. |
October 2, 2008 |
Austenitic free-cutting stainless steel
Abstract
The present invention relates to an austenitic free-cutting
stainless steel, containing: by weight percent, 0.500% or less of
C; 0.01 to 5.00% of Si; 0.01 to 10.00% of Mn; 5.00 to 25.00% of Ni;
7.50 to 30.00% of Cr; 0.300% or less of N; more than 0.0100% but
not more than 0.1000% of 0; 0.0020 to 0.1000% of B; 0.300% or less
of Al; and the remainder of Fe and inevitable impurities, the steel
satisfying the following formula (1):
0.68.ltoreq.[O]/[B].ltoreq.2.50 (1) in which [O] represents the
content of O and [B] represents the content of B.
Inventors: |
Eto; Hisao; (Nagoya-shi,
JP) ; Shimizu; Tetsuya; (Nagoya-shi, JP) |
Correspondence
Address: |
BACON & THOMAS, PLLC
625 SLATERS LANE, FOURTH FLOOR
ALEXANDRIA
VA
22314-1176
US
|
Assignee: |
DAIDO TOKUSHUKO KABUSHIKI
KAISHA
Nagoya-shi
JP
|
Family ID: |
39494390 |
Appl. No.: |
12/078378 |
Filed: |
March 31, 2008 |
Current U.S.
Class: |
420/84 ; 148/621;
420/112 |
Current CPC
Class: |
Y02E 50/12 20130101;
C21D 6/004 20130101; C22C 38/54 20130101; C22C 38/58 20130101; Y02E
50/10 20130101 |
Class at
Publication: |
420/84 ; 420/112;
148/621 |
International
Class: |
C22C 38/60 20060101
C22C038/60; C22C 38/08 20060101 C22C038/08; C21D 6/00 20060101
C21D006/00 |
Foreign Application Data
Date |
Code |
Application Number |
Mar 31, 2007 |
JP |
2007-095799 |
Jan 18, 2008 |
JP |
2008-008886 |
Claims
1. An austenitic free-cutting stainless steel, comprising: by
weight percent, 0.500% or less of C; 0.01 to 5.00% of Si; 0.01 to
10.00% of Mn; 5.00 to 25.00% of Ni; 7.50 to 30.00% of Cr; 0.300% or
less of N; more than 0.0100% but not more than 0.1000% of O; 0.0020
to 0.1000% of B; 0.300% or less of Al; and the remainder of Fe and
inevitable impurities, said steel satisfying the following formula
(1): 0.68.ltoreq.[O]/[B].ltoreq.2.50 (1) wherein [O] represents the
content of O and [B] represents the content of B.
2. The austenitic free-cutting stainless steel according to claim
1, which comprises an oxide-based inclusion containing B dispersed
therein.
3. The austenitic free-cutting stainless steel according to claim
2, wherein the oxide-based inclusion further contains Si.
4. The austenitic free-cutting stainless steel according to claim
1, further comprising: at least one kind selected from the group
consisting of a sulfide, a nitride, a carbosulfide and a
selenide.
5. The austenitic free-cutting stainless steel according to claim
2, further comprising: at least one kind selected from the group
consisting of a sulfide, a nitride, a carbosulfide and a
selenide.
6. The austenitic free-cutting stainless steel according to claim
3, further comprising: at least one kind selected from the group
consisting of a sulfide, a nitride, a carbosulfide and a
selenide.
7. The austenitic free-cutting stainless steel according to claim
1, which is obtained by a heat treatment conducted at a temperature
in the range of 1000 to 1300.degree. C. for a period of 5 min to 24
hr.
8. The austenitic free-cutting stainless steel according to claim
2, which is obtained by a heat treatment conducted at a temperature
in the range of 1000 to 1300.degree. C. for a period of 5 min to 24
hr.
9. The austenitic free-cutting stainless steel according to claim
3, which is obtained by a heat treatment conducted at a temperature
in the range of 1000 to 1300.degree. C. for a period of 5 min to 24
hr.
10. The austenitic free-cutting stainless steel according to claim
4, which is obtained by a heat treatment conducted at a temperature
in the range of 1000 to 1300.degree. C. for a period of 5 min to 24
hr.
11. The austenitic free-cutting stainless steel according to claim
5, which is obtained by a heat treatment conducted at a temperature
in the range of 1000 to 1300.degree. C. for a period of 5 min to 24
hr.
12. The austenitic free-cutting stainless steel according to claim
6, which is obtained by a heat treatment conducted at a temperature
in the range of 1000 to 1300.degree. C. for a period of 5 min to 24
hr.
13. The austenitic free-cutting stainless steel according to claim
any one of claims 1 to 12, further comprising: by weight percent,
at least one element selected from the group consisting of 0.01 to
0.50% of S, 0.01 to 0.50% of Se, 0.01 to 0.40% of Pb, 0.01 to 0.40%
of Bi, 0.01 to 0.40% of Te, 0.01 to 0.40% of Sn, 0.01 to 0.40% of
P, 0.01 to 8.00% of Mo, 0.01 to 4.00% of W, 0.01 to 5.00% of Cu,
0.01 to 2.00% of Ti, 0.01 to 2.00% of V, 0.01 to 2.00% of Nb, 0.01
to 2.00% of Zr, 0.0001 to 0.0100% of Mg, and 0.0001 to 0.0100% of
Ca.
14. A process for producing an austenitic free-cutting stainless
steel, which comprises: preparing a steel comprising: by weight
percent, 0.500% or less of C, 0.01 to 5.00% of Si, 0.01 to 10.00%
of Mn, 5.00 to 25.00% of Ni, 7.50 to 30.00% of Cr, 0.300% or less
of N, more than 0.0100% but not more than 0.1000% of O, 0.0020 to
0.1000% of B, 0.300% or less of Al, and the remainder of Fe and
inevitable impurities, said steel satisfying the following formula
(1): 0.68.ltoreq.[O]/[B].ltoreq.2.50 (1) wherein [O] represents the
content of O and [B] represents the content of B; melting and
casting the steel; and subjecting the steel to a heat treatment
conducted at a temperature in the range of 1000 to 1300.degree. C.
for a period of 5 min to 24 hr.
Description
FIELD OF THE INVENTION
[0001] The invention relates to an austenitic free-cutting
stainless steel.
BACKGROUND OF THE INVENTION
[0002] Since an austenitic stainless steel contains relatively
large amount of alloy elements such as Cr or Ni, the raw material
itself is expensive in comparison with that of an ordinary steel.
Accordingly, in order to reduce the production cost of the entire
member, it is important to improve the workability. So far, in the
applications where the free-cutting property is required, a
free-cutting stainless steel (such as SUS303) containing a
machinability-improving element such as Pb or S has been used.
[0003] However, Pb, which is a typical free-cutting element, is not
preferred to be add in steel materials from the viewpoint of the
recent environmental concerns. Furthermore, S, which is a
free-cutting element, forms a sulfide such as MnS in the steel and
improves the machinability. However, since a large amount of
sulfide deteriorates the corrosion resistance that is the greatest
characteristic of the stainless steel, the addition amount thereof
is limited. Still furthermore, an addition of various kinds of
free-cutting elements deteriorates the hot workability in some
cases.
[0004] In this connection, in order to overcome the above-mentioned
problems, various proposals have been made.
[0005] For instance, JP-A-62-278252 discloses an austenitic
stainless steel that contains, by weight percent, C: 0.01 to 0.15%,
Si: 0.35 to 0.73%, Mn: 0.15 to 9.53%, P: 0.011 to 0.025%, S: 0.002
to 0.024%, Cr: 10.32 to 30.00%, Ni: 4.98 to 30.00%, Bi: 0.02 to
0.20%, Sn: 0.02 to 0.21%, B: 0.0040 to 0.0200%, O: 0.0047 to
0.0100%, N: 0.02 to 0.07%, and the remainder of Fe and inevitable
impurities.
[0006] This literature describes that the deterioration of the hot
workability due to the addition of Bi and Sn in combination which
are added for improving the machinability can be inhibited by the
addition of B, and that O is a harmful element to the hot
workability.
[0007] Furthermore, JP-A-62-30860 discloses a Bi-containing
austenitic free-cutting stainless steel that contains, by weight
percent, C: 0.01 to 0.16%, Si: 0.28 to 0.75%, Mn: 0.75 to 9.05%,
Cr: 15.25 to 26.40%, Ni: 2.00 to 30.00%, Bi: 0.02 to 0.30%, B:
0.021 to 0.080%, S: 0.004 to 0.050%, P: 0.015 to 0.050%, N: 0.022
to 0.051%, O: 0.0016 to 0.0065%, and the remainder being Fe and
inevitable impurities.
[0008] In this literature, it is disclosed that an addition of Bi
may improve the machinability and the deterioration of the hot
workability due to the addition of Bi can be inhibited by the
addition of B.
[0009] The free-cutting effect of an free-cutting element, Pb,
means a liquid metal induced embrittlement. When a cutting portion
is heated to a high temperature during the cutting of steel, Pb
that is a low melting metal (melting temperature: 330.degree. C.)
melts. The molten Pb makes a work brittle to thereby improve the
machinability.
[0010] As a non-Pb free-cutting steel, various Pb-free steels have
been developed. However, all of such reports describe that a
machinability equivalent to that of a Pb-containing free cutting
steel may be realized "under some cutting conditions". A
free-cutting element that may substitute a free-cutting effect
(liquid metal induced embrittlement) equivalent to that of a
free-cutting element Pb, except for Bi that is scarce in source,
has not been reported yet.
SUMMARY OF THE INVENTION
[0011] A problem that the invention intends to solve is to provide
an austenitic free-cutting stainless steel which, without
deteriorating the corrosion resistance, has a machinability
equivalent to that of a Pb-containing free cutting steel.
[0012] In order to overcome the problems, the present invention
provides the following (1) to (14).
[0013] (1) An austenitic free-cutting stainless steel,
comprising:
[0014] by weight percent,
[0015] 0.500% or less of C;
[0016] 0.01 to 5.00% of Si;
[0017] 0.01 to 10.00% of Mn;
[0018] 5.00 to 25.00% of Ni;
[0019] 7.50 to 30.00% of Cr;
[0020] 0.300% or less of N;
[0021] more than 0.0100% but not more than 0.1000% of O;
[0022] 0.0020 to 0.1000% of B;
[0023] 0.300% or less of Al; and
[0024] the remainder of Fe and inevitable impurities,
[0025] said steel satisfying the following formula (1):
0.68.ltoreq.[O]/[B].ltoreq.2.50 (1)
[0026] wherein [O] represents the content of O and [B] represents
the content of B.
[0027] (2) The austenitic free-cutting stainless steel according to
(1), which comprises an oxide-based inclusion containing B
dispersed therein.
[0028] (3) The austenitic free-cutting stainless steel according to
(2), wherein the oxide-based inclusion further contains Si.
[0029] (4) The austenitic free-cutting stainless steel according to
(1), further comprising:
[0030] at least one kind selected from the group consisting of a
sulfide, a nitride, a carbosulfide and a selenide.
[0031] (5) The austenitic free-cutting stainless steel according to
(2), further comprising:
[0032] at least one kind selected from the group consisting of a
sulfide, a nitride, a carbosulfide and a selenide.
[0033] (6) The austenitic free-cutting stainless steel according to
(3), further comprising:
[0034] at least one kind selected from the group consisting of a
sulfide, a nitride, a carbosulfide and a selenide.
[0035] (7) The austenitic free-cutting stainless steel according to
(1), which is obtained by a heat treatment conducted at a
temperature in the range of 1000 to 1300.degree. C. for a period of
5 min to 24 hr.
[0036] (8) The austenitic free-cutting stainless steel according to
(2), which is obtained by a heat treatment conducted at a
temperature in the range of 1000 to 1300.degree. C. for a period of
5 min to 24 hr.
[0037] (9) The austenitic free-cutting stainless steel according to
(3), which is obtained by a heat treatment conducted at a
temperature in the range of 1000 to 1300.degree. C. for a period of
5 min to 24 hr.
[0038] (10) The austenitic free-cutting stainless steel according
to (4), which is obtained by a heat treatment conducted at a
temperature in the range of 1000 to 1300.degree. C. for a period of
5 min to 24 hr.
[0039] (11) The austenitic free-cutting stainless steel according
to (5), which is obtained by a heat treatment conducted at a
temperature in the range of 1000 to 1300.degree. C. for a period of
5 min to 24 hr.
[0040] (12) The austenitic free-cutting stainless steel according
to (6), which is obtained by a heat treatment conducted at a
temperature in the range of 1000 to 1300.degree. C. for a period of
5 min to 24 hr.
[0041] (13) The austenitic free-cutting stainless steel according
to any one of (1) to (12), further comprising:
[0042] by weight percent,
[0043] at least one kind selected from the group consisting of
[0044] 0.01 to 0.50% of S,
[0045] 0.01 to 0.50% of Se,
[0046] 0.01 to 0.40% of Pb,
[0047] 0.01 to 0.40% of Bi,
[0048] 0.01 to 0.40% of Te,
[0049] 0.01 to 0.40% of Sn,
[0050] 0.01 to 0.40% of P,
[0051] 0.01 to 8.00% of Mo,
[0052] 0.01 to 4.00% of W,
[0053] 0.01 to 5.00% of Cu,
[0054] 0.01 to 2.00% of Ti,
[0055] 0.01 to 2.00% of V,
[0056] 0.01 to 2.00% of Nb,
[0057] 0.01 to 2.00% of Zr,
[0058] 0.0001 to 0.0100% of Mg, and
[0059] 0.0001 to 0.0100% of Ca.
[0060] (14) A process for producing an austenitic free-cutting
stainless steel, which comprises:
[0061] preparing a steel comprising:
[0062] by weight percent,
[0063] 0.500% or less of C,
[0064] 0.01 to 5.00% of Si,
[0065] 0.01 to 10.00% of Mn,
[0066] 5.00 to 25.00% of Ni,
[0067] 7.50 to 30.00% of Cr,
[0068] 0.300% or less of N,
[0069] more than 0.0100% but not more than 0.1000% of O,
[0070] 0.0020 to 0.1000% of B,
[0071] 0.300% or less of Al, and
[0072] the remainder of Fe and inevitable impurities,
[0073] said steel satisfying the following formula (1):
0.68.ltoreq.[O]/[B].ltoreq.2.50 (1)
[0074] wherein [O] represents the content of O and [B] represents
the content of B;
[0075] melting and casting the steel; and
[0076] subjecting the steel to a heat treatment conducted at a
temperature in the range of 1000 to 1300.degree. C. for a period of
5 min to 24 hr.
[0077] When a specific amount or more of O that has been
conventionally said detrimental to the hot workability is added to
an austenitic stainless steel containing a specific amount of B and
a heat treatment at a predetermined temperature is applied to the
steel, high machinability can be obtained even in the case that
conventionally known free-cutting elements such as S, Pb, Se and Te
are not contained in the steel. This is considered because, when a
relatively large amount of O is contained, an oxide of B, which is
a low melt oxide (melting temperature: 480.degree. C.), or a
composite oxide containing B is dispersed in the steel to thereby
develop a liquid metal induced embrittlement during the
cutting.
BRIEF DESCRIPTION OF THE DRAWINGS
[0078] FIG. 1 shows an EPMA analysis result of an inclusion
contained in the material obtained in example 1.
BEST MODE FOR CARRYING OUT THE INVENTION
[0079] In what follows, one embodiment of the invention will be
described in detail.
[0080] The austenitic free-cutting stainless steel according to the
invention includes elements shown below and the remainder of Fe and
inevitable impurities. The types of the addition elements, the
component ratios thereof, the reason for limitation thereof, and
the like are as follows. Herein, in the present specification, all
the percentages defined by weight are the same as those defined by
mass, respectively.
[0081] (1) C: 0.500% by Weight or Less
[0082] An element C is an austenite-generating element and
contributes to stabilize an austenite phase. Furthermore, since C
is an interstitial element, it contributes to the improvement in
mechanical strength. On the other hand, when a content of C is
excessive, Cr carbide is formed to decrease the dissolved Cr in a
mother phase, whereby the corrosion resistance is deteriorated.
Accordingly, the content of C is preferably 0.500% by weight or
less. The content of C is more preferably 0.100% by weight or
less.
[0083] (2) Si: 0.01 to 5.00% by Weight
[0084] An element Si is added as a deoxidizer. In order to attain a
sufficient deoxidizing effect, the content of Si is preferably
0.01% by weight or more.
[0085] On the other hand, since Si is a ferrite-generating element,
an excessive addition thereof destabilizes an austenite phase.
Furthermore, Si promotes precipitation of a .sigma.-phase to
thereby deteriorate the corrosion resistance. Accordingly, the
content of Si is preferably 5.00% by weight or less. The content of
Si is more preferably 3.00% by weight or less.
[0086] (3) Mn: 0.01 to 10.00% by Weight
[0087] An element Mn is an austenite-generating element and
contributes to stabilize an austenite phase. In order to attain
such an effect, the content of Mn is preferably 0.01% by weight or
more.
[0088] On the other hand, when Mn is excessively contained, the
pitting corrosion resistance of the steel is deteriorated.
Accordingly, the content of Mn is preferably 10.00% by weight or
less.
[0089] (4) Ni: 5.00 to 25.00% by Weight
[0090] An element Ni is an austenite-generating element and
contributes to stabilize an austenite phase. In order to attain
such an effect, the content of Ni is preferably 5.00% by weight or
more.
[0091] On the other hand, when Ni is added excessively, the
precipitation of an .sigma.-phase is promoted to thereby
deteriorate the corrosion resistance. Accordingly, an addition
amount of Ni is preferably 25.00% by weight or less.
[0092] (5) Cr: 7.50 to 30.00% by Weight
[0093] An element Cr is an important element that greatly
contributes to the improvement in the corrosion resistance and the
mechanical strength. In order to attain such an effect, the content
of Cr is preferably 7.50% by weight or more. The content of Cr is
more preferably 15.00% by weight or more.
[0094] On the other hand, an excessive addition of Cr increases a
residual amount of an undissolved Cr carbonitride during the
solution treatment, to thereby considerably deteriorate the
corrosion resistance. Accordingly, the amount of Cr is preferably
30.0% by weight or less. The content of Cr is more preferably
25.00% by weight or less.
[0095] (6) N: 0.300% by Weight or Less
[0096] An element N is an interstitial element and is significantly
effective for improving the mechanical strength, stabilizing an
austenite phase, and improving the corrosion resistance. On the
other hand, when N is added excessively, a large amount of an
undissolved Cr nitride and a large amount of a nitride remain in
the steel during the solution treatment, to thereby considerably
deteriorate the corrosion resistance. Accordingly, the content of N
is preferably 0.300% by weight or less. The content of N is more
preferably 0.100% by weight or less and still more preferably
0.050% by weight or less.
[0097] (7) O: More than 0.0100% by Weight but Not More than 0.1000%
by Weight
[0098] An element O is generally said to deteriorate the cleanness
of steel to thereby considerably deteriorate the corrosion
resistance and the hot workability. However, when B is added to an
austenitic stainless steel and a specific amount or more of O is
further added thereto, the free cutting property equivalent to that
of Pb-containing free cutting steel can be obtained without the
necessity of adding a conventionally known free-cutting element. In
order to attain such an effect, the content of O is preferably more
than 0.0100% by weight. More preferably, the content of O is more
than 0.0200% by weight.
[0099] On the other hand, when O is added excessively, the
corrosion resistance and the hot workability are deteriorated.
Accordingly, the content of O is preferably 0.1000% by weight or
less. The content of O is more preferably 0.0500% by weight or
less.
[0100] (8) B: 0.0020 to 0.1000% by Weight
[0101] An element B is generally said effective for improving the
mechanical strength and the hot workability. However, when B is not
dissolved in the matrix but dispersed in the steel as an
oxide-based inclusion containing B, the machinability is improved.
In order to attain such an effect, the content of B is preferably
0.0020% by weight or more. The content of B is more preferably
0.0080% by weight or more and still more preferably 0.0120% by
weight or more.
[0102] On the other hand, when B is excessively added, the hot
workability is deteriorated as well as the corrosion resistance is
also deteriorated. Accordingly, the content of B is preferably
0.1000% by weight or less. The content of B is more preferably
0.0800% by weight or less.
[0103] (9) Al: 0.300% by Weight or Less
[0104] An element Al is an oxide-forming element. When Al is added
excessively, Al.sub.2O.sub.3 is preferentially generated to make it
difficult to form an oxide containing B that improves the
machinability in the invention. Accordingly, the content of Al is
preferably 0.300% by weight or less.
[0105] (10) [O]/[B] Ratio
[0106] In the invention, in order to improve the free cutting
property, an oxide-based inclusion containing B is dispersed in the
steel. The invention is different from conventional free-cutting
stainless steels in this respect.
[0107] In order to attain practically sufficient free cutting
effect, a ratio of a content of O ([O]) to a content of B ([B])
preferably satisfies the following formula (1).
0.68.ltoreq.[O]/[B].ltoreq.2.50 (1)
[0108] When the ratio of [O]/[B] is too small, since the amount of
O is relatively small, a sufficient amount of oxide-based inclusion
may not be dispersed in the steel. Accordingly, the ratio of
[O]/[B] is preferably 0.68 or more.
[0109] On the other hand, when the ratio of [O]/[B] is too large,
the amount of O becomes excessive to thereby cause deterioration of
the corrosion resistance and the hot workability. Accordingly, the
ratio of [O]/[B] is preferably 2.50 or less.
[0110] The austenitic free-cutting stainless steel according to the
invention is obtained, as will be described below, by melting and
casting a steel having a predetermined composition, followed by
subjecting the steel to a heat treatment conducted under
predetermined conditions. When the steel is heat-treated under
predetermined conditions, B which is contained in the steel can be
entirely or partially dispersed in the steel as an oxide-based
inclusion containing B. In order to attain high machinability, an
oxide-based inclusion preferably further contains Si. The
machinability is improved by the coexistence of B and Si. This is
considered because B is dissolved in the oxide having a silicate
structure formed by SiO.sub.2 to thereby form a borosilicate oxide,
and the borosilicate oxide is dispersed in the steel.
[0111] In general, the more the oxide-based inclusion containing B
is contained, the more the machinability is improved. In order to
attain high machinability, an area ratio of the oxide-based
inclusion containing B is preferably 0.01% or more.
[0112] On the other hand, when an amount of the oxide-based
inclusion is excessive, the hot workability and the corrosion
resistance are deteriorated. Accordingly, an area ratio of the
oxide-based inclusion containing B is preferably 0.10% or less.
[0113] Furthermore, in the steel, an inclusion other than the
oxide-based inclusion containing B is present as well. Such an
oxide other than the oxide-based inclusion containing B does not
contribute to an improvement in the machinability. Accordingly, a
ratio of the oxide-based inclusion containing B in the entire
oxides is preferably 50% or more.
[0114] In the austenitic free-cutting stainless steel according to
the invention, the machinability is improved by dispersing the
oxide-based inclusion containing B in the steel. The austenitic
free-cutting stainless steel may contain only the oxide-based
inclusion containing B, or may contain, in addition to the
oxide-based inclusion containing B, a conventional free-cutting
element (that is, at least any one of a sulfide, a nitride, a
carbosulfide and a selenide, which are effective for improving the
machinability) as well.
[0115] That is, the austenitic free-cutting stainless steel
according to the invention may further contain, in addition to the
foregoing elements, at least one element selected from the group
consisting of S and Se (first additional element).
[0116] (11) S: 0.01 to 0.50% by Weight
[0117] An element S forms MnS with Mn in the steel to thereby
improve the machinability effectively. In order to attain such as
effect, the content of S is preferably 0.01% by weight or more.
[0118] On the other hand, when S is added excessively, the hot
workability is deteriorated and, due to the formation of MnS, the
corrosion resistance is also deteriorated. Furthermore, when the
amount of S is unnecessarily reduced, the production cost becomes
increased. Accordingly, the content of S is preferably 0.50% by
weight or less.
[0119] (12) Se: 0.01 to 0.50% by Weight
[0120] An element Se also contributes to improve the machinability.
In order to attain such an effect, the content of Se is preferably
0.01% by weight or more.
[0121] On the other hand, when Se is added excessively, the
corrosion resistance, the toughness and ductility, and the hot
workability are deteriorated. Accordingly, the content of Se is
preferably 0.50% by weight or less.
[0122] Furthermore, the austenitic free-cutting stainless steel
according to the invention may contain, in addition to the first
additional elements or in place thereof, at least one element
selected from the group consisting of Pb, Bi, Te, Sn and P (second
additional element).
[0123] (13) Pb: 0.01 to 0.40% by Weight
[0124] (14) Bi: 0.01 to 0.40% by Weight
[0125] (15) Te: 0.01 to 0.40% by Weight
[0126] (16) Sn: 0.01 to 0.40% by Weight
[0127] (17) P: 0.01 to 0.40% by Weight
[0128] All of Pb, Bi, Te, Sn and P have an effect for improving the
machinability. In order to attain such an effect, the content of
each element is preferably 0.01% by weight or more.
[0129] On the other hand, when these elements each are added
excessively, the toughness is deteriorated. Accordingly, an
addition amount of each element is preferably 0.40% by weight or
less.
[0130] Furthermore, an austenitic free-cutting stainless steel
according to the invention may contain, in addition to the first
additional elements and/or second additional elements, or in place
thereof, at least one element selected from the group consisting of
Mo, W and Cu (third additional element).
[0131] (18) Mo: 0.01 to 8.00% by Weight
[0132] An element Mo considerably improves the corrosion
resistance. Furthermore, Mo improves the mechanical strength as a
solid solution hardening element. In order to attain such an
effect, the content of Mo is preferably 0.01% by weight or
more.
[0133] On the other hand, when Mo is added excessively, since a
brittle phase is generated to deteriorate the toughness and
ductility, which also becomes harmful during the forging.
Accordingly, the content of Mo is preferably 8.00% by weight or
less.
[0134] (19) W: 0.01 to 4.00% by Weight
[0135] Similar to Mo, an element W contributes to the improvement
in the corrosion resistance as well as the improvement in the
mechanical strength as a solid solution hardening element. In order
to attain such an effect, the content of W is preferably at 0.01%
by weight or more.
[0136] On the other hand, similar to Mo, when W is added
excessively, since a brittle phase is generated to deteriorate the
toughness and ductility, which also becomes harmful during the
forging. Accordingly, the content of W is preferably 4.00% by
weight or less.
[0137] (20) Cu: 0.01 to 5.00% by Weight
[0138] An element Cu is an austenite-generating element and
contributes to stabilize an austenite phase. Furthermore, Cu
contributes to improve the gap corrosion resistance. In order to
attain such an effect, the content of Cu is preferably 0.01% by
weight or more.
[0139] On the other hand, when Cu is added excessively, the hot
workability is deteriorated. Accordingly, the content of Cu is
preferably 5.00% by weight or less.
[0140] Furthermore, an austenitic free-cutting stainless steel
according to the invention may contain, in addition to at least one
of the first through third additional elements, or in place
thereof, at least one element selected from the group consisting of
Ti, V, Nb and Zr (fourth addition element).
[0141] (21) Ti: 0.01 to 2.00% by Weight
[0142] An element Ti binds with C or N to thereby contribute to the
improvement in the mechanical strength and the miniaturization of
crystal grains. In order to attain such an effect, the content of
Ti is preferably 0.01% by weight or more.
[0143] On the other hand, when Ti is added excessively, large
amounts of oxide and nitride remain in the steel to thereby
deteriorate the corrosion resistance. Accordingly, the content of
Ti is preferably 2.00% by weight or less.
[0144] (22) V: 0.01 to 2.00% by Weight
[0145] Similar to Ti, an element V binds with C or N to thereby
contribute to the improvement in the mechanical strength and
miniaturization of crystal grains. In order to attain such an
effect, the content of V is preferably 0.01% by weight or more.
[0146] On the other hand, when V is added excessively, a large
amount of nitride remains in the steel to thereby deteriorate the
corrosion resistance. Accordingly, the content of V is preferably
2.00% by weight or less.
[0147] (23) Nb: 0.01 to 2.00% by Weight
[0148] Similar to Ti and V, an element Nb binds with C or N to
thereby contribute to the improvement in the mechanical strength
and miniaturization of crystal grains. In order to attain such an
effect, the content of Nb is preferably 0.01% by weight or
more.
[0149] On the other hand, when Nb is added excessively, a large
amount of nitride remains in the steel to thereby deteriorate the
corrosion resistance. Accordingly, the content of Nb is preferably
2.00% by weight or less.
[0150] (24) Zr: 0.01 to 2.00% by Weight
[0151] An element Zr contributes to the improvement in the
mechanical strength. In order to attain such an effect, the content
of Zr is preferably 0.01% by weight or more.
[0152] On the other hand, when Zr is added excessively, the
toughness and ductility are deteriorated. Accordingly, the content
of Zr is preferably 2.00% by weight or less.
[0153] Furthermore, an austenitic free-cutting stainless steel
according to the invention may contain, in addition to at least one
of the first through fourth additional elements, or in place
thereof, at least one element selected from the group consisting of
Mg and Ca (fifth additional element).
[0154] (25) Mg: 0.0001 to 0.0100% by Weight
[0155] (26) Ca: 0.0001 to 0.0100% by Weight
[0156] Elements Mg and Ca are effective for improving the hot
workability.
[0157] Furthermore, Ca is also effective for improving the
machinability. This is considered because Ca has an action of
enabling an oxide having a silicate structure which contributes to
the improvement in the machinability to be present more stably in
the steel. In order to attain such an effect, the content of each
of Mg and Ca is preferably 0.0001% by weight or more.
[0158] On the other hand, when these elements are added
excessively, contrary to the above, the hot workability is
deteriorated. Accordingly, the content of each thereof is
preferably 0.0100% by weight or less.
[0159] In this regard, with regard to each element contained in the
steel of the invention, according to an embodiment, the minimal
amount thereof present in the steel is the smallest non-zero amount
used in the Examples of the developed steels as summarized in
Tables 1 and 2. According to a further embodiment, the maximum
amount thereof present in the steel is the maximum amount used in
the Examples of the developed steels as summarized in Tables 1 and
2.
[0160] In the next place, a producing method of the austenitic
free-cutting stainless steel according to the invention will be
described.
[0161] The austenitic free-cutting stainless steel according to the
invention is obtained by melting and casting the steel having the
above-mentioned composition, followed by subjecting the steel to a
heat-treatment under predetermined conditions. When the steel is
subjected to a heat-treatment under predetermined conditions, B
contained in the steel is entirely or partially dispersed in the
steel as an oxide-based inclusion containing B. In order to attain
high machinability, an oxide-based inclusion may preferably further
contain Si.
[0162] In general, when the heat treatment temperature is too low,
an oxide-based inclusion containing B cannot be generated in the
steel. In order to generate an oxide-based inclusion containing B,
the heat treatment temperature is preferably at 1000.degree. C. or
more. The heat treatment temperature is more preferably at
1150.degree. C. or more.
[0163] Furthermore, in general, the higher the heat treatment
temperature becomes, the easier the oxide-based inclusion
containing B tends to be formed. However, when the heat treatment
temperature is too high, local melting occurs to unfavorably result
in a material having an inhomogeneous composition. Accordingly, the
heat treatment temperature is preferably at 1300.degree. C. or
less. The heat treatment temperature is more preferably at
1250.degree. C. or less.
[0164] Still furthermore, the heat treatment period affects on an
amount of the oxide-based inclusion containing B. In general, the
longer the heat treatment period is, the larger the amount of the
oxide-based inclusion containing B becomes. In order to generate a
practically sufficient amount of the oxide-based inclusion
containing B, the heat treatment period is preferably in the range
of 5 min to 24 hr. The heat treatment time is more preferably in
the range of 5 min to 4 hr.
[0165] In the next place, actions of the austenitic free-cutting
stainless steel according to the invention will be described.
[0166] When a specific amount or more of O that has been
conventionally said detrimental to the hot workability is added to
an austenitic stainless steel containing a specific amount of B and
a heat treatment at a predetermined temperature is applied to the
steel, high machinability can be obtained even in the case that
conventionally known free-cutting elements such as S, Pb, Se and Te
are not contained in the steel. This is considered because, when a
relatively large amount of O is contained, an oxide of B, which is
a low melt oxide (melting temperature: 480.degree. C.), or a
composite oxide containing B is dispersed in the steel to thereby
develop a liquid metal induced embrittlement during the
cutting.
[0167] Furthermore, when Si is further contained in an oxide-based
inclusion in addition to B, high machinability can be obtained.
This is considered because, when Si is contained in the oxide-based
inclusion, a liquid phase mainly made of a borosilicate oxide is
readily formed during the cutting.
[0168] Still furthermore, the austenitic free-cutting stainless
steel according to the invention is relatively less in the tool
wear. This is considered because a deposition of an oxide
containing B (so-called, belag) tends to be readily generated on a
surface of a tool.
EXAMPLES
[0169] Examples 1 to 42 and Comparative Examples 1 to 13
[0170] By the use of a high frequency induction furnace, each of
alloys having a chemical composition shown in Tables 1 and 2 was
melted and cast to obtain 50 kg of an ingot. In the next place, the
ingot was uniformly heated, followed by hot forging into a round
bar having a diameter of 24 mm. The round bar thus obtained was
then subjected to a heat treatment. The heat treatment was
conducted by holding the bar at 1150.degree. C. for 1 hr followed
by cooling with water.
TABLE-US-00001 TABLE 1 Composition (% by weight) C Si Mn Ni Cr N Al
O B Others [O]/[B] Example 1 0.011 0.29 0.85 9.5 17.5 0.021 0.001
0.0215 0.014 1.54 Example 2 0.010 0.82 1.21 9.4 17.7 0.014 0.002
0.0250 0.016 1.56 Example 3 0.035 0.52 0.11 7.8 17.3 0.022 0.001
0.0188 0.021 0.90 Example 4 0.005 1.42 1.16 9.8 18.4 0.011 0.001
0.0231 0.029 0.80 Example 5 0.018 0.66 1.52 8.9 18.7 0.006 0.004
0.0102 0.007 1.46 Example 6 0.068 1.17 0.47 9.5 19.3 0.043 0.005
0.0224 0.022 1.02 Example 7 0.033 1.40 0.27 8.7 19.2 0.018 0.003
0.0273 0.016 1.71 Example 8 0.054 1.06 0.87 10.1 17.7 0.021 0.002
0.0125 0.007 1.79 Example 9 0.016 0.74 0.44 7.9 17.6 0.016 0.001
0.0216 0.009 S: 0.06 2.40 Example 10 0.022 0.53 1.19 9.4 18.5 0.021
0.001 0.0253 0.019 S: 0.31 1.33 Example 11 0.066 0.26 0.29 10.3
18.7 0.023 0.009 0.0206 0.011 S: 0.48 1.87 Example 12 0.005 0.13
1.19 9.7 17.9 0.011 0.011 0.0213 0.021 Se: 0.07 1.01 Example 13
0.025 0.29 0.58 9.3 16.9 0.009 0.001 0.0196 0.016 Se: 0.43 1.23
Example 14 0.002 0.08 1.87 10.3 15.3 0.008 0.002 0.0163 0.018 Pb:
0.04 0.91 Example 15 0.044 0.09 1.45 12.6 19.3 0.011 0.002 0.0253
0.029 Pb: 0.31 0.87 Example 16 0.019 0.12 0.03 16.2 18.3 0.009
0.001 0.0195 0.028 Bi: 0.11 0.70 Example 17 0.014 0.44 0.54 11.8
17.4 0.005 0.002 0.0228 0.011 Bi: 0.34 2.07 Example 18 0.031 0.99
0.29 9.2 16.9 0.016 0.001 0.0218 0.015 Te: 0.09 1.45 Example 19
0.022 1.42 0.65 8.4 13.2 0.021 0.043 0.0257 0.019 Te: 0.33 1.35
Example 20 0.006 4.32 0.85 7.2 16.1 0.015 0.055 0.0241 0.011 Sn:
0.02 2.19 Example 21 0.036 0.89 0.39 19.4 11.2 0.018 0.001 0.0281
0.031 Sn: 0.39 0.91 Example 22 0.006 3.83 2.65 23.2 9.2 0.011 0.002
0.0246 0.024 P: 0.02 1.03 Example 23 0.009 0.68 1.20 9.6 17.3 0.011
0.001 0.0210 0.011 P: 0.12 1.91 Example 24 0.026 2.46 0.73 20.3 8.9
0.014 0.001 0.0228 0.022 P: 0.36 1.04 Example 25 0.421 1.85 0.98
18.4 7.9 0.019 0.001 0.0266 0.014 Mo: 0.21 1.90 Example 26 0.015
1.56 1.62 13.9 26.0 0.002 0.021 0.0246 0.011 Mo: 4.38 2.24 Example
27 0.094 1.29 2.48 9.7 25.7 0.006 0.265 0.0192 0.012 W: 0.09 1.60
Example 28 0.088 0.20 3.10 7.3 29.3 0.004 0.003 0.0198 0.009 W:
2.39 2.20 Example 29 0.021 0.29 1.11 23.4 26.3 0.009 0.002 0.0178
0.008 Cu: 0.06 2.23 Example 30 0.016 0.91 1.84 17.5 21.3 0.022
0.004 0.0159 0.014 Cu: 2.68 1.14
TABLE-US-00002 TABLE 2 Composition (% by weight) C Si Mn Ni Cr N Al
O B Others [O]/[B] Example 31 0.021 3.11 0.44 9.8 22.4 0.081 0.003
0.0111 0.008 Ti: 1.83 1.39 Example 32 0.008 2.84 0.74 6.3 17.9
0.068 0.001 0.0220 0.009 V: 1.49 2.44 Example 33 0.009 0.22 2.63
17.3 13.7 0.211 0.001 0.0291 0.023 Nb: 1.73 1.27 Example 34 0.013
0.42 1.18 14.9 18.9 0.191 0.001 0.0225 0.018 Zr: 1.79 1.25 Example
35 0.049 0.33 6.90 22.5 15.9 0.248 0.002 0.0416 0.049 Mg: 0.0013
0.85 Example 36 0.016 0.24 1.62 21.5 16.3 0.137 0.001 0.0338 0.032
Mg: 0.0065 1.06 Example 37 0.052 0.31 8.44 11.6 19.3 0.133 0.001
0.0612 0.029 Ca: 0.0009 2.11 Example 38 0.009 0.29 0.85 9.5 17.5
0.021 0.001 0.0102 0.007 Ca: 0.0003 1.46 Example 39 0.013 0.55 0.53
9.4 17.7 0.014 0.002 0.0188 0.021 Ca: 0.0005 0.90 Example 40 0.028
0.52 0.11 7.8 17.3 0.022 0.001 0.0215 0.014 Ca: 0.0008 1.54 Example
41 0.006 1.42 1.16 9.8 20.3 0.011 0.001 0.0250 0.016 Ca: 0.0017
1.56 Example 42 0.016 0.66 1.52 8.9 18.7 0.006 0.004 0.0231 0.029
Ca: 0.0046 0.80 Comparative 0.522 0.10 2.95 13.4 17.9 0.011 0.003
0.0492 0.021 2.34 Example 1 Comparative 0.012 7.80 1.62 21.5 16.3
0.012 0.002 0.0338 0.032 1.06 Example 2 Comparative 0.002 3.20
12.40 21.3 18.4 0.043 0.009 0.0440 0.022 2.00 Example 3 Comparative
0.035 4.20 0.04 4.3 8.9 0.280 0.022 0.0600 0.052 1.15 Example 4
Comparative 0.002 0.08 1.87 28.5 15.3 0.150 0.019 0.0441 0.039 1.13
Example 5 Comparative 0.018 0.59 0.92 8.9 6.8 0.005 0.051 0.0224
0.033 0.68 Example 6 Comparative 0.009 0.22 2.63 17.3 32.4 0.184
0.002 0.0291 0.021 1.39 Example 7 Comparative 0.013 2.33 1.92 9.2
21.5 0.410 0.004 0.0118 0.016 0.74 Example 8 Comparative 0.012 0.95
1.32 9.6 18.4 0.022 0.008 0.0039 0.004 0.98 Example 9 Comparative
0.009 0.22 2.63 17.3 13.6 0.211 0.002 0.1031 0.023 4.48 Example 10
Comparative 0.005 0.10 2.95 16.8 17.4 0.009 0.004 0.0492 0.002
32.80 Example 11 Comparative 0.011 0.29 0.85 9.5 17.5 0.021 0.210
0.0215 0.101 0.21 Example 12 Comparative 0.011 0.32 0.84 9.5 17.3
0.016 0.380 0.0221 0.023 0.96 Example 13
[0171] 2. Evaluation (1)
[0172] The following evaluations were carried out on the obtained
round bars.
[0173] (1) Composition of Inclusion:
[0174] After the heat treatment, randomly-selected oxides (30
pieces) were subjected to a composition analysis by the use of
EPMA. As the result of the composition analysis, those where B was
confirmed in 15 or more pieces of the oxides are expressed by "A"
and those where B was confirmed in 15 or less pieces of the oxides
are expressed by "B".
[0175] (2) Oxide Area Ratio:
[0176] Typical microphotographs were measured by a microscope of
200 times power and all the oxide-based inclusions were extracted
by colors. By means of an image processing, an area ratio of the
oxide-based inclusions was measured.
[0177] (3) Corrosion Resistance
[0178] A heat-treated round bar was maintained in a saline spray
atmosphere for 96 hr. Subsequently, the rust generation rate was
measured. Those where the rust was not found after the saline spray
are expressed by "A", those where the rust area rate was less than
3% are expressed by "B", and those where the rust area rate was 3%
or more are expressed by "C]", respectively.
[0179] (4) Drill Perforation Property:
[0180] A heat treated round bar was perforated with a SKH 51 drill
(diameter: 5 mm). A grinding speed was set at 15 mm/min and a depth
of a hole was set at 15 mm. The drill perforation property was
evaluated by the number of holes perforated until the drill was
destroyed.
[0181] (5) Grinding Resistance Value:
[0182] The grinding resistance value at the drill perforation test
was measured.
[0183] (6) Chip Fractureness:
[0184] A curl of a chip arbitrarily sampled at the time of the
drill perforation property test was measured. Those where the
number of curl was three or less are expressed by "A", those where
the number of curl was three to ten were expressed by "B", and
those where the number of curl exceeded ten are expressed by "C",
respectively.
[0185] 3. Result (1)
[0186] Results of the composition analysis on the materials
obtained in example 1 by means of EPMA are shown in FIG. 1. From
the results shown in FIG. 1, it is found that, from a position
where an oxygen peak is confirmed, peaks of B and Si are also
confirmed. This shows that the inclusion is an oxide containing B
and Si.
[0187] In Tables 3 and 4, evaluation test results are shown.
TABLE-US-00003 TABLE 3 Drill Perforation Grinding Composition Oxide
Area Corrosion Property Resistance Chip of Inclusion Ratio (%)
Resistance (pieces) Value (MPa) Fractureness Example 1 A 0.02 A 45
219 A Example 2 A 0.03 A 49 224 A Example 3 A 0.02 A 47 224 A
Example 4 A 0.02 A 49 227 A Example 5 A 0.02 A 38 231 A Example 6 A
0.02 A 49 205 A Example 7 A 0.03 A 51 221 A Example 8 A 0.02 A 39
220 A Example 9 A 0.02 A 51 204 A Example 10 A 0.03 A 55 214 A
Example 11 A 0.02 A 58 211 A Example 12 A 0.02 A 51 221 A Example
13 A 0.02 A 39 219 A Example 14 A 0.02 A 39 216 A Example 15 A 0.03
A 55 217 A Example 16 A 0.02 A 39 219 A Example 17 A 0.03 A 56 221
A Example 18 A 0.02 A 46 206 A Example 19 A 0.03 A 52 201 A Example
20 A 0.03 A 51 209 A Example 21 A 0.03 A 46 205 A Example 22 A 0.03
A 45 217 A Example 23 A 0.02 A 49 214 A Example 24 A 0.02 A 51 211
A Example 25 A 0.03 A 47 219 A Example 26 A 0.02 A 49 221 A Example
27 A 0.02 A 39 220 A Example 28 A 0.02 A 39 216 A Example 29 A 0.02
A 38 205 A Example 30 A 0.02 A 39 221 A
TABLE-US-00004 TABLE 4 Drill Perforation Grinding Composition Oxide
Area Corrosion Property Resistance Chip of Inclusion Ratio (%)
Resistance (pieces) Value (MPa) Fractureness Example 31 A 0.02 A 39
218 A Example 32 A 0.02 A 49 208 A Example 33 A 0.03 A 45 205 A
Example 34 A 0.03 A 49 216 A Example 35 A 0.05 A 48 221 A Example
36 A 0.04 A 45 218 A Example 37 A 0.03 A 42 219 A Example 38 A 0.02
A 49 220 A Example 39 A 0.02 A 52 217 A Example 40 A 0.02 A 53 215
A Example 41 A 0.03 A 55 210 A Example 42 A 0.02 A 57 206 A
Comparative A 0.05 C 44 220 B Example 1 Comparative A 0.03 C 43 211
B Example 2 Comparative A 0.04 C 44 216 A Example 3 Comparative A
0.06 C 42 221 A Example 4 Comparative A 0.02 C 41 218 B Example 5
Comparative A 0.02 C 40 210 B Example 6 Comparative B 0.01 C 11 319
C Example 7 Comparative B 0.01 A 16 289 C Example 8 Comparative A
0.01 A 17 281 B Example 9 Comparative B 0.04 B 12 299 B Example 10
Comparative B 0.01 C 24 304 C Example 11 Comparative A 0.01 C 49
216 B Example 12 Comparative B 0.02 A 12 302 C Example 13
[0188] The stainless steel of Comparative Example 1 is poor in the
corrosion resistance. This is because an amount of C was excessive,
whereby Cr carbide was generated.
[0189] The stainless steel of Comparative Example 2 is poor in the
corrosion resistance. This is because an amount of Si was
excessive, whereby a .sigma. phase remained a lot.
[0190] The stainless steel of Comparative Example 3 is poor in the
corrosion resistance. This is because an amount of Mn was
excessive, whereby the pitting corrosion resistance was
deteriorated.
[0191] The stainless steel of Comparative Example 4 is poor in the
corrosion resistance. This is because an amount of Ni was too
small, whereby a corrosion resistance effect of Ni itself could not
be exerted.
[0192] The stainless steel of Comparative Example 5 is poor in the
corrosion resistance. This is because an amount of Ni was
excessive, whereby a .sigma.-phase remained a lot.
[0193] The stainless steel of Comparative Example 6 is poor in the
corrosion resistance. This is because an amount of Cr was too
small, whereby the corrosion resistance was not improved.
[0194] The stainless steel of Comparative Example 7 is poor in the
corrosion resistance and the machinability. This is because an
amount of Cr was excessive, whereby undissolved Cr nitride remained
a lot and Cr and B formed a compound.
[0195] The stainless steel of Comparative Example 8 is poor in the
machinability. This is because since an amount of N was excessive,
whereby undissolved Cr nitride remained a lot and Cr and N formed a
compound.
[0196] The stainless steel of Comparative Example 9 is poor in the
machinability. This is because an amount of oxygen was less,
whereby an amount of a B-based oxide that is effective for an
improvement in the machinability was small.
[0197] The stainless steel of Comparative Example 10 is rather poor
in the corrosion resistance and poor in the machinability. This is
because an amount of oxygen was excessive, whereby an amount of B
in the oxide became relatively small.
[0198] The stainless steel of Comparative Example 11 is poor in the
corrosion resistance and the machinability. This is because the
ratio of [O]/[B] was too large.
[0199] The stainless steel of c Comparative Example 12 is poor in
the corrosion resistance. This is because an amount of B was
excessive.
[0200] Furthermore, the stainless steel of Comparative Example 13
is poor in the machinability because an amount of Al was
excessive.
[0201] On the other hand, since the stainless steels of Examples 1
to 37 are optimized in the composition and subjected to a heat
treatment in an appropriate temperature region, both the corrosion
resistance and the machinability were excellent. In particular,
when the amount of oxygen exceeded 0.02%, irrespective of
compositions of other components, high machinability was
obtained.
[0202] Furthermore, the stainless steels of Examples 38 to 42 are
further improved in the machinability in comparison with those of
the other stainless steels. This is considered because the addition
of Ca enables the oxide having a silicate structure which
contributes to the improvement in the machinability to be present
more stably in the steel.
[0203] 4. Evaluation (2)
[0204] The composition of Example 1 was subjected to a heat
treatment at 840 to 1330.degree. C. for 1 hr. The heat-treated
sample was evaluated, in accordance with the procedures same as
those mentioned above, in terms of the inclusion composition, oxide
area ratio, corrosion resistance, drill perforation property,
grinding resistance value and chip fractureness.
[0205] 5. Result (2)
[0206] Results thereof are shown in Table 5. When the heat
treatment temperature is lower than 1000.degree. C., the
machinability and the corrosion resistance are poor. This is
considered because an oxide-based inclusion containing B is not
sufficiently generated and Cr and B form a compound. Furthermore,
when the heat treatment temperature exceeds 1300.degree. C., the
corrosion resistance becomes poor. This is considered because the
local melting is caused, whereby a composition becomes partially
uneven.
[0207] On the other hand, when the heat treatment was applied at a
temperature in the range of 1000 to 1300.degree. C., it is found
that the machinability can be improved without deteriorating the
corrosion resistance.
TABLE-US-00005 TABLE 5 Drill Composition Oxide Perforation Grinding
Heat Treatment of Area Corrosion Property Resistance Chip
Temperature (.degree. C.) Inclusion Ratio (%) Resistance (pieces)
Value (MPa) Fractureness 840 B 0.02 C 15 289 C 950 B 0.02 B 18 292
B 1020 A 0.02 A 45 219 A 1060 A 0.02 A 47 219 A 1140 A 0.02 A 49
217 A 1230 A 0.02 A 50 214 A 1280 A 0.02 A 51 216 A 1330 A 0.02 C
48 220 A
[0208] The austenitic free-cutting stainless steel according to the
invention can be used in marine-related instruments, beach
environmental members, structural members of marine structures,
members for desalination plants, members for saline heat
converters, submarine cables, structural members of submarine
structures, mooring ropes, aquafarming nets, bridge wires at beach
sites, saline pumps, shafts, tightening members such as bolts, nuts
and screws, and the like.
[0209] Furthermore, the austenitic free-cutting stainless steel
according to the invention can be used in bolts, nuts, cylinder
liners, shafts, hubs, connectors, bearings, laces, rails, gears,
pins, screws, rolls, turbine blades, metal molds, dices, drills,
valves, valve seats, cutting tools, nozzles, gaskets, rings,
springs, industrial furnace members, chemical plant members, drug
production members, food production members, food production device
members, petroleum rig members, petroleum refining plant members,
waste incinerator members, steam turbine members, gas turbine
members, nuclear furnace members, aircraft members, biomass plant
members and the like.
[0210] 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.
[0211] The present application is based on Japanese Patent
Application No. 2007-095799 filed on Mar. 31, 2007 and Japanese
Patent Application No. 2008-008886 filed on Jan. 18, 2008, the
contents thereof being incorporated herein by reference.
* * * * *