CA2649355A1 - Austenitic stainless steel and process for removing hydrogen therefrom - Google Patents
Austenitic stainless steel and process for removing hydrogen therefrom Download PDFInfo
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- CA2649355A1 CA2649355A1 CA002649355A CA2649355A CA2649355A1 CA 2649355 A1 CA2649355 A1 CA 2649355A1 CA 002649355 A CA002649355 A CA 002649355A CA 2649355 A CA2649355 A CA 2649355A CA 2649355 A1 CA2649355 A1 CA 2649355A1
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- Prior art keywords
- hydrogen
- stainless steel
- austenitic stainless
- diffusible
- mass
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- Abandoned
Links
- 239000001257 hydrogen Substances 0.000 title claims abstract description 192
- 229910052739 hydrogen Inorganic materials 0.000 title claims abstract description 192
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 title claims abstract description 158
- 229910000963 austenitic stainless steel Inorganic materials 0.000 title claims description 81
- 238000000034 method Methods 0.000 title claims description 36
- 230000008569 process Effects 0.000 title claims description 21
- 238000010438 heat treatment Methods 0.000 claims abstract description 56
- 150000002431 hydrogen Chemical class 0.000 claims abstract description 35
- 229910000734 martensite Inorganic materials 0.000 claims description 40
- 239000011651 chromium Substances 0.000 claims description 14
- 125000004122 cyclic group Chemical group 0.000 claims description 11
- 229910052804 chromium Inorganic materials 0.000 claims description 10
- 238000004519 manufacturing process Methods 0.000 claims description 10
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 9
- 239000002244 precipitate Substances 0.000 claims description 4
- 206010070834 Sensitisation Diseases 0.000 claims description 3
- 239000012141 concentrate Substances 0.000 claims description 3
- 230000008018 melting Effects 0.000 claims description 3
- 238000002844 melting Methods 0.000 claims description 3
- 230000008313 sensitization Effects 0.000 claims description 3
- 229910001220 stainless steel Inorganic materials 0.000 abstract description 31
- 239000010935 stainless steel Substances 0.000 abstract description 19
- 229910001566 austenite Inorganic materials 0.000 abstract description 5
- 238000009661 fatigue test Methods 0.000 description 48
- 238000012360 testing method Methods 0.000 description 39
- 239000000463 material Substances 0.000 description 35
- 238000005259 measurement Methods 0.000 description 29
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 19
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 17
- 230000000694 effects Effects 0.000 description 12
- 239000000446 fuel Substances 0.000 description 12
- 230000009466 transformation Effects 0.000 description 12
- 230000035882 stress Effects 0.000 description 11
- 239000000243 solution Substances 0.000 description 10
- 229910000831 Steel Inorganic materials 0.000 description 9
- 238000009792 diffusion process Methods 0.000 description 9
- 239000010959 steel Substances 0.000 description 9
- 229910052759 nickel Inorganic materials 0.000 description 8
- 230000032683 aging Effects 0.000 description 7
- 229910052742 iron Inorganic materials 0.000 description 7
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 6
- QAOWNCQODCNURD-UHFFFAOYSA-N Sulfuric acid Chemical compound OS(O)(=O)=O QAOWNCQODCNURD-UHFFFAOYSA-N 0.000 description 6
- 239000002801 charged material Substances 0.000 description 6
- 230000007797 corrosion Effects 0.000 description 6
- 238000005260 corrosion Methods 0.000 description 6
- 238000002474 experimental method Methods 0.000 description 6
- 239000000203 mixture Substances 0.000 description 5
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- 238000002441 X-ray diffraction Methods 0.000 description 4
- 238000003795 desorption Methods 0.000 description 4
- 239000011572 manganese Substances 0.000 description 4
- 238000005482 strain hardening Methods 0.000 description 4
- 239000000126 substance Substances 0.000 description 4
- 239000010936 titanium Substances 0.000 description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 3
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 3
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 3
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 3
- 230000001133 acceleration Effects 0.000 description 3
- 238000005275 alloying Methods 0.000 description 3
- 229910052786 argon Inorganic materials 0.000 description 3
- 229910052799 carbon Inorganic materials 0.000 description 3
- 239000013078 crystal Substances 0.000 description 3
- 230000003247 decreasing effect Effects 0.000 description 3
- 239000007789 gas Substances 0.000 description 3
- 229910052748 manganese Inorganic materials 0.000 description 3
- 239000002245 particle Substances 0.000 description 3
- 229910052710 silicon Inorganic materials 0.000 description 3
- 239000010703 silicon Substances 0.000 description 3
- 229910052719 titanium Inorganic materials 0.000 description 3
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 2
- 238000005097 cold rolling Methods 0.000 description 2
- 230000006835 compression Effects 0.000 description 2
- 238000007906 compression Methods 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 230000007613 environmental effect Effects 0.000 description 2
- 239000012535 impurity Substances 0.000 description 2
- 239000011261 inert gas Substances 0.000 description 2
- 238000013508 migration Methods 0.000 description 2
- 230000005012 migration Effects 0.000 description 2
- 229910052758 niobium Inorganic materials 0.000 description 2
- 239000010955 niobium Substances 0.000 description 2
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- BASFCYQUMIYNBI-UHFFFAOYSA-N platinum Chemical compound [Pt] BASFCYQUMIYNBI-UHFFFAOYSA-N 0.000 description 2
- 238000004881 precipitation hardening Methods 0.000 description 2
- 230000002829 reductive effect Effects 0.000 description 2
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- XBDQKXXYIPTUBI-UHFFFAOYSA-M Propionate Chemical compound CCC([O-])=O XBDQKXXYIPTUBI-UHFFFAOYSA-M 0.000 description 1
- SMEGJBVQLJJKKX-HOTMZDKISA-N [(2R,3S,4S,5R,6R)-5-acetyloxy-3,4,6-trihydroxyoxan-2-yl]methyl acetate Chemical compound CC(=O)OC[C@@H]1[C@H]([C@@H]([C@H]([C@@H](O1)O)OC(=O)C)O)O SMEGJBVQLJJKKX-HOTMZDKISA-N 0.000 description 1
- KXKVLQRXCPHEJC-UHFFFAOYSA-N acetic acid trimethyl ester Natural products COC(C)=O KXKVLQRXCPHEJC-UHFFFAOYSA-N 0.000 description 1
- 229940081735 acetylcellulose Drugs 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910052796 boron Inorganic materials 0.000 description 1
- 229920002301 cellulose acetate Polymers 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- -1 chromium carbides Chemical class 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000001419 dependent effect Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 229910001651 emery Inorganic materials 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 238000001704 evaporation Methods 0.000 description 1
- 230000008020 evaporation Effects 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- 230000036961 partial effect Effects 0.000 description 1
- 230000037361 pathway Effects 0.000 description 1
- 239000012466 permeate Substances 0.000 description 1
- 238000007747 plating Methods 0.000 description 1
- 229910052697 platinum Inorganic materials 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 230000002265 prevention Effects 0.000 description 1
- 230000002250 progressing effect Effects 0.000 description 1
- 238000004445 quantitative analysis Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 230000002441 reversible effect Effects 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 230000003068 static effect Effects 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 230000008646 thermal stress Effects 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D3/00—Diffusion processes for extraction of non-metals; Furnaces therefor
- C21D3/02—Extraction of non-metals
- C21D3/06—Extraction of hydrogen
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Fuel Cell (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
By focusing on non-diffusible hydrogen causing hydrogen embrittlement in austenite base stainless steel, it is intended to provide austenite base stainless steel free from the non-diffusible hydrogen by heating austenite base stainless steel at a heating temperature of 200 to 500oC for not longer than 460 hours while maintaining it in an evacuated atmosphere of 0.2 Pa or less to thereby eliminate hydrogen (H) contained in the austenite base stainless steel to 0.00007% by mass (0.7 ppm by mass) or less.
Description
DESCRIPTION
AUSTENITIC STAINLESS STEEL AND PROCESS FOR
REMOVING HYDROGEN THEREFROM
TECHNICAL FIELD
[0001]
The present invention concerns an austenitic stainless steel with reduced hydrogen embrittlement and a process for removing hydrogen therefrom. More specifically, the present invention concerns an austenitic stainless steel wherein the effect of hydrogen present therein on the growth of fatigue cracks occurring therein is reduced, and a process for removing hydrogen therefrom.
BACKGROUND
AUSTENITIC STAINLESS STEEL AND PROCESS FOR
REMOVING HYDROGEN THEREFROM
TECHNICAL FIELD
[0001]
The present invention concerns an austenitic stainless steel with reduced hydrogen embrittlement and a process for removing hydrogen therefrom. More specifically, the present invention concerns an austenitic stainless steel wherein the effect of hydrogen present therein on the growth of fatigue cracks occurring therein is reduced, and a process for removing hydrogen therefrom.
BACKGROUND
[0002]
From the standpoint of global environmental concerns, the use of hydrogen as a next generation energy source has received considerable attention, and R&D on this topic is quite active. Particularly, one important subject that has received emphasis is the development and practical application of stationary fuel cells, fuel cell-powered vehicles, etc., that utilize hydrogen as fuel. The use of stainless steel as a material for high pressure hydrogen tanks and parts thereof, piping, and the like in this fuel cell system has already been investigated (for example, see patent document 1).
From the standpoint of global environmental concerns, the use of hydrogen as a next generation energy source has received considerable attention, and R&D on this topic is quite active. Particularly, one important subject that has received emphasis is the development and practical application of stationary fuel cells, fuel cell-powered vehicles, etc., that utilize hydrogen as fuel. The use of stainless steel as a material for high pressure hydrogen tanks and parts thereof, piping, and the like in this fuel cell system has already been investigated (for example, see patent document 1).
[0003]
The components of typical austenitic stainless steel are shown in Table 1. The first column in this Table 1 lists the names of stainless steels and the heat-resistant steels as defined in the Japanese Industrial Standards (JIS). The last column of Table 1 shows the Vickers hardness of the stainless steel (hereinafter, HV). Other columns are the chemical compositions of the stainless steel, and the amounts of the components are expressed in units of mass%. However, the content of hydrogen (H) is expressed as mass ppm (parts per million by mass).
Ln N -I
Ln M
i Ln N
ll:~
.L-1 i i ~ N ,-i ~o N a (N Ln Q0 Ln oo N r-=I N N M r-I r1 (N ~4 ~4 N (V UJ Q) d) N N Q) 4) a) N N
'~ `o -rI -ri -ri - I
'~ -~--I -H =ri --I -~-I -ri =ri E
~ ~ ~, ~ N N N N N 41 rx rx a a a x a a) a 00 CC) I'D
0 O O O O pp N N N N N
~ l0 ri di H 0) ri O lQ (N tf) Ol lfl O N L(1 O N N O ri O O l0 ~-I 01) 00 CO 00 t~ lO LC L-~ J r i r-I r i r-I r I r-I rl rl H N N I N
Lrl I!1 LIl o ~ (N N r-I M
al l9 Vi 61 rl 0 H I N N M
r1 O ri O .
~ C`7 N 01 d1 O
Zi 00 61 OD 00 r-I r-i r I r i - I r-I L t N
M L~ L(]
N OD H
0 O O l0 `--I O '--I r-~ O
O O O O (N N 0 O O O
O O
~ O O O O O O O O O p O
V
~
~ O o0 N Lfl O O c-I L~ m M d Ol M N tn N M M N M N (N (N
rl O O O 0 Cp O O O O C) O O
S~ P O O 0 O O O O O O O O O
~ dl N Ol d ,~ l~ CO O L~ N L- CO
N
~ O O dl M M 01 O M
~ ~ rl rl O rl T-{
r-1 O ri O r--I r--I O
0\0 l0 Ln CCO L~ Ol M OC) M di dj (N
m M
U) ~ r Lfl N N Lfl C lf) M M
~ CI?. O O O O O O O O O 0 0 O
N LIl Ln Lt) Ltl N ~ r I
~ O
O O O O O O O O N ~
(D O p 1 ~ O O O O O ' . .
O O O O O O O
u ~ d d ~h V l0 l0 l0 l0 l0 O O ~
d r i O O O O -i rl H r--1 r-~ H ~ ~ ~''~ M M M f+') M M M M M M M
U2 Cf~ CI~ Ul m C!] Cf~ ~ C/1 CI] C!~ U1 CD I'D ~D ~D ~D ~D
Cf~ Cf1 CI] L1] CI) C!~ U] CI~ U1 U? U1 C!) r1 O
O
II
N =
o II
r-t r-I
Lf) fYl r-I
O
f'') di r-I
O
O
O
r-i O
O
N
di O
Lfl O
O
O
a' O
~o U) [0005]
It is known that hydrogen diffuses through metallic materials and decreases both the static strength and fatigue strength thereof (non-patent documents 1 and 2). Various processes for removing this hydrogen and methods for predicting the effect of hydrogen have been proposed. In patent document 2, for example, after the plating process austenitic stainless steel is heat-treated by maintaining it at a temperature of 270 to 400 C for 10 minutes or more to remove the hydrogen and prevent hydrogen embrittlement. Patent document 3 discloses a method wherein the extent of the hydrogen embrittlement of austenitic stainless steel is predicted and judged based on the chemical composition thereof.
[0006]
Non-patent document 1 presents fatigue testing results for austenitic stainless steels in compliance with SUS304, SUS316, and SUS316L. This fatigue testing was conducted by comparing these austenitic stainless steels with their hydrogen-charged counterparts. The fatigue crack growth rate of hydrogen-charged SUS304 and SUS316 was faster than in the corresponding uncharged steels. However, no clear difference was seen with SUS316L.
[0007]
In addition, non-patent document 1 presents fatigue test results for JIS SUS304 and the SUS316L austenitic stainless steels after the ~est piece was prestrained and a microhole of about 100 m was formed therein. The fatigue crack growth rate was accelerated ten-fold in hydrogen-charged SUS304 compared with the uncharged steel counterpart. Likewise, the fatigue crack growth rate was accelerated two-fold in SUS316L.
[0008]
However, even semi-stable austenitic stainless steel can undergo stress-induced martensitic transformation due to cold-working and cyclic stress. Persons skilled in the art in this industry, including groups of researchers in academic societies, have commonly believed that hydrogen had almost no effect on the fatigue crack growth rate in the austenitic stainless steels such as JIS SUS316L. Non-patent document 1 presents results that reverse this common belief, and because these results were obtained by applying cyclic loading at a low frequency of 5Hz or less, this finding is very significant.
[0009]
in other words, it has been verified that the growth rate of fatigue cracks is accelerated by low-frequency cyclic loading in austenitic stainless steel such as SUS316L. On the other hand, non-patent document 2 points out the following:
"(3) The martensitic phase resulting from transformation in austenitic stainless steel becomes a pathway for hydrogen diffusion throughout the material, and the diffusion coefficient of hydrogen is increased thereby (see page 130)."
[0010]
[Patent document 1] Japanese Patent Application Laid-open No.
[Patent document 2] Japanese Patent Application Laid-open No.
[Patent document 3] Japanese Patent Application Laid-open No.
[Non-patent document 1] Toshihiko KANEZAKI, Chihiro NARAZAKI, Yoji MINE, Saburo MATSUOKA, and Yukitaka MURAKAMI: The effect of hydrogen on fatigue crack growth of pre-strained austenitic stainless steel. The Japan Society of Mechanical Engineers [No.
05-9] Proceedings of the 2005 Annual Meeting of JSME/MMD, Vol.
2005 (November 4 to 6, 2005, Fukuoka) P86 p. 595-596.
[Non-patent document 2] Toshihiko KANEZAKI, Chihiro NARAZAKI, Yoji MINE, Saburo MATSUOKA, and Yukitaka MURAKAMI: Effect of hydrogen on fatigue crack growth and martensitic transformation of stainless steels. Transactions of the Japan Society of Mechanical Engineers A. Vol. 72, No. 723, (November 2006), p. 123-130. (manuscript received: May 1, 2006) [0011]
At present, however, sufficient analysis has not been performed concerning how non-diffusible hydrogen, which is present in crystals, and diffusible hydrogen, which is charged from the outside, are related to the aforementioned fatigue crack growth rate in austenitic stainless steels. In addition, the relationships involving how diffusible hydrogen and non-diffusible hydrogen influence changes in the amount of martensitic transformation, the effect of acceleration in the hydrogen diffusion rate, and the fatigue crack growth rate in a material have not been sufficiently clarified.
[00121 Furthermore, when stainless steel is used for equipment and apparatuses related to hydrogen fuel utilization, it is exposed to a variety of environmental influences depending on the usage environment. For example, when stainless steel is used for the high pressure hydrogen container, piping, and the like in a fuel cell-powered vehicle, loading and release are repeated in a relatively slow cycle that involves the filling of the high pressure hydrogen container with hydrogen gas and the subsequent consumption thereof. In the past, however, fatigue tests have not taken this slow cycle into account. In other words, it was thought that a fatigue test using a load with a long cycle could be replaced by a fatigue test with a quick repetition rate.
[00131 Moreover, low frequency cyclic loading occurs due to temperature variations in the outside air temperature_and the like. An example of cyclic loading due to variations in the outside air temperature is thermal stress resulting from compression and expansion of the stainless steel itself and of the parts connected to stainless steel components as a result of temperature differences between day and night. As for the frequency of the cycle, the temperature gradient between day and night can range from only a few degrees to ten degrees centigrade or more, and one cycle is 24 hours long. This means that high pressure hydrogen tanks at fuel cell vehicle-related facilities, facilities for supplying fuel for fuel cells, and the like will have a cycle measured in single day units as noted above, and the hydrogen fill time will be long. In addition, a fuel cell-powered vehicle is dependent on the environment in which it operates, and it will have a temperature gradient cycle ranging from a few degrees to several tens of degrees centigrade, and a time cycle expressed in units ranging from subseconds to several hours.
DISCLOSURE OF THE INVENTION
[0014]
The present invention is based on the above technological background, and it attains the following objects.
An object of the present invention is to provide an austenitic stainless steel for reducing the effect of hydrogen on the growth rate of fatigue cracks that occur in austenitic stainless steel, and a process for removing the hydrogen therefrom.
[0015]
Another object of the present invention is to focus on both diffusible hydrogen and non-diffusible hydrogen that cause hydrogen embrittlement in austenitic stainless steel and provide an austenitic stainless steel having both removed therefrom, and to provide a process for removing the hydrogen therefrom.
[001,6]
Another object of the present invention is to focus on the diffusible hydrogen and the non-diffusible hydrogen that become a problem with cyclic loading having a long cycle time and provide an austenitic stainless steel having both removed therefrom, and to provide a process for removing the hydrogen therefrom.
[0017]
Another object of the present invention is to provide an austenitic stainless steel wherein the diffusible hydrogen and non-diffusible hydrogen present in austenitic stainless steel are removed therefrom during a manufacturing step thereof, and a process for removing the hydrogen therefrom.
[0018] Definition of terms The present invention uses the following technical terms in the meanings defined below. Hydrogen charge means causing hydrogen to permeate the material. Hydrogen charge method refers to a method whereby the material is exposed in a high pressure hydrogen chamber, a method wherein cathodic charging is performed, and a method wherein the material is immersed in a chemical solution and the like. Fatigue crack growth refers to the enlargement of defects and cracks that occur in the material during the manufacturing process or cracks from holes and the like that are artificially introduced into the material as a result of cyclic loading.
u B
[0019]
Fatigue crack growth rate means the rate at which the fatigue crack progresses. Austenitic stainless steel refers to Cr-Ni series steel wherein chromium and nickel are added to iron to produce a stainless steel in the austenitic phase with increased corrosion resistance in corrosive environments and the like. Table 1 shows a list of this kind of stainless steel.
The austenitic phase is a phase of iron at a temperature range of 911 to 1392 C in 100% pure iron (Fe), and it has a face centered cubic lattice structure (hereinafter, FCC lattice structure).
[0020]
The FCC lattice is shown in Figure 11(a). The austenitic phase can also exist at room temperature when alloying elements such as chromium and nickel are added to iron. The martensitic phase is a conformation obtained by quenching steel at a high-temperature, stable austenitic phase, and it has a body centered cubic lattice structure (hereinafter, BCC lattice structure). The BCC lattice is shown in Figure 11(b). Moreover, the martensitic phase is caused by adding stress such as cold-working and the like to austenitic phase stainless steel at ordinary ambient temperatures.
[0021]
This transformation from an austenitic phase with an FCC structure to a martensitic phase with a BCC structure by cold working is called stress-induced martensitic transformation. Diffusible hydrogen refers to hydrogen that is present in the material and exits the material over time at room temperature. This diffusible hydrogen causes the hydrogen embrittlement of the material. Hydrogen that cannot exit the material over time even at temperatures from room temperature to about 200 C, is called non-diffusible hydrogen.
[0022]
The present invention adopts the following means to achieve the aforementioned objects.
The inventors of the present invention ascertained the fact that non-diffusible hydrogen in an austenitic stainless steel is related to fatigue crack growth.
The present invention concerns an austenitic stainless steel having an austenitic phase in which the crystal structure is an FCC lattice structure and a process for removing the hydrogen therefrom. The present invention is one wherein the diffusible hydrogen and the non-diffusible hydrogen that cause hydrogen embrittlement of austenitic stainless steel are removed, with the hydrogen (H) contained in the austenitic stainless steel being removed to a level of 0.00007 mass% (0.7 mass ppm) or less.
[0023]
A heat treatment at a heating temperature of 200 C or higher is preferred for the removal of diffusible hydrogen and non-diffusible hydrogen from austenitic stainless steel.
Moreover, the upper limit of the heating temperature for the heat treatment at this time is preferably no more than 500 C.
It is preferred that the heat treatment to remove the diffusible hydrogen and non-diffusible hydrogen is performed under vacuum.
[0024]
Moreover, the temperature range for the heating temperature is 200 to 500 C, and this range is preferred for removing both the non-diffusible hydrogen and the diffusible hydrogen, which are present in austenitic stainless steel, diffuse via the stress-induced martensitic phase brought about by cyclic loading, concentrate in the cracks undergoing concentrated stress, and cause hydrogen embrittlement therein, to thereby remove the hydrogen (H) contained therein to the aforementioned amount.
[0025]
It is preferred that the heating temperature is a temperature lower than the sensitization temperature, which is the temperature at which chromium (Cr) carbide in austenitic stainless steel precipitates due to the heat. Moreover, it is preferred that the aforementioned vacuum atmosphere is an environment of 0.2 Pa or less. In addition, it is preferred that the heat treatment is performed by maintaining the heating temperature in the aforementioned vacuum atmosphere for 460 hours or less.
[0026]
The amount of hydrogen (H) contained in the austenitic stainless steel after removing the diffusible hydrogen and the non-diffusible hydrogen is preferably 0.00004 massa (0.4 mass ppm) or less. Furthermore, the amount of hydrogen (H) contained in the austenitic stainless steel after removing the diffusible hydrogen and the non-diffusible hydrogen is more preferably 0.00001 mass% (0.1 mass ppm) or less.
[0027]
It is preferable that the heat treatment is performed for the predetermined time in the process of manufacturing the austenitic stainless steel, and the hydrogen is removed to adjust the hydrogen (H) to 0.00007 massa (0.7 mass ppm) or less. At that time, the heat treatment temperature is preferably 200 C or more, and less than the melting point temperature of the stainless steel. The heating time for this purpose preferably ranges from 30 seconds or more to several tens of hours or less. An inert gas flow atmosphere is preferred for this process. The manufacturing steps for austenitic stainless steel are the ones used when manufacturing stainless steel, and they include the steps of a solution heat treatment and an aging treatment.
[0028]
The hydrogen removal treatment in the manufacturing process can be performed in a vacuum or an atmosphere wherein the hydrogen partial pressure is low, e.g., an inert gas atmosphere. Moreover, the heat treatment preferably lasts from a few minutes to several tens of hours long.
In the case of a solution heat treatment, the most preferred temperature for the heat treatment is 920 C or higher.
In the case of an aging treatment, the most preferred temperature for the heat treatment is 700 C or higher.
In addition, it is preferred that the austenitic stainless steel is one of the aforementioned austenitic stainless steels or heat resistant austenitic steels shown in Table 1.
[0029]
The present invention provides the following advantageous effect. In the present invention austenitic stainless steel is heat-treated at a temperature of 200 C or higher to remove the non-diffusible hydrogen and the diffusible hydrogen, thereby making it possible to provide an austenitic stainless steel that is highly resistant to fatigue crack growth.
BRIEF DESCRIPTION OF THE DRAWINGS
[0073]
Figure 1 is a line drawing showing the fatigue test piece, Figure 1(a) is a drawing showing the shape of the fatigue test piece, and Figure 1(b) is a drawing showing the shape of the artificial microhole formed in the fatigue test piece;
Figure 2 shows a line drawing of the test area in the fatigue test piece and the fatigue crack starting at the small artificial hole and progressing therefrom;
Figure 3 is a schematic diagram of the procedure for applying the prestrain to the fatigue test piece;
Figure 4 is a photograph of the fatigue cracks emanating from the artificial microhole after fatigue testing;
Figure 5 shows results of x-ray examination of the austenitic phase and martensitic phase in the test area surface before fatigue testing and the fatigue cracked surface after fatigue testing wherein Figure 5(a) shows the measurement results for SUS304, Figure 5(b) shows the measurement results for SUS316, and Figure 5(c) shows the measurement results for SUS316L;
Figure 6 is a graph showing the relationship between the length of the cracks caused by fatigue testing and number of cycles wherein Figure 6(a) shows the results for SUS304, Figure 6(b) for SUS316, and Figure 6(c) for SUS316L;
Figure 7 shows photographs of fatigue cracks in SUS304, SUS316, and SUS316L observed by the replica method;
Figure 8 is a graph showing the results of fatigue testing of SUS316L;
Figure 9 is a graph showing the result of the fatigue testing of SUS316L;
Figure 10 is a conceptual drawing showing the circumstances wherein the diffusible hydrogen and the non-diffusible hydrogen diffuse through the transformed martensitic phase;
Figure 11 is a schematic drawing showing the lattices of the crystal structures of the austenitic phase and martensitic phase wherein Figure 11(a) shows the face centered cubic lattice structure (FCC) of the austenitic phase, and Figure 11(b) shows the body centered cubic lattice structure (BCC) of the martensitic phase;
Figure 12 is a graph showing the results of Additional Experimental Example 1; and Figure 13 is a graph showing the results of Additional Experimental Example 2.
BEST MODE FOR CARRYING OUT THE INVENTION
[00301 Below the mode of the present invention is explained through examples. First of all, the way hydrogen affects the growth rate of fatigue cracks in austenitic stainless steel will be explained. After a conventional heat treatment (solution heat treatment) is performed, austenitic stainless steels such as SUS304, SUS316, and SUS316L shown in Table 1 contain 1 to 4.7 mass ppm of non-diffusible hydrogen. In the past persons skilled in the art believed that this non-diffusible hydrogen had no effect on hydrogen embrittlement.
[00311 However, the fatigue tests described below have determined that non-diffusible hydrogen affects hydrogen embrittlement. Hydrogen embrittlement resulting from non-diffusible hydrogen has been verified at a low frequency fatigue testing speed of about 0.0015 Hz in (approximately 11 minutes as the repetition time of one cycle) in particular.
The inventors of the present invention performed the following tests and observed how non-diffusible hydrogen affected the growth rate of the fatigue cracks. One example of such testing is shown herein.
[0032]
Test piece The materials used were the SUS304, SUS316, and SUS316L(A) (hereinafter, simply called SUS316L) austenitic stainless steels shown in Table 1. A solution heat treatment was performed on the SUS304, SUS316, and SUS316L steels used.
The shape of the fatigue test piece is shown in Figure 1(a).
The surface of the test piece was finished by buffing after polishing with # 2000 emery paper.
[0033]
As shown in Figure i(b), an artificiai microhole 100 ~tm in diameter and 100 m deep was opened in the center of the fatigue test piece in the lengthwise direction with a drill having a radial tip angle of 120 to facilitate observation of fatigue crack growth. The artificial microhole was inserted in the center of the test area of the test piece. The test area was a cylindrical part at the center of the test piece, and the length of the cylinder was approximately 20 mm. The top and bottom surfaces of the cylinder were mutually parallel, and lay perpendicular to the lengthwise axis of the test piece..
Figure 2 illustrates an outline of the test piece and the shape of the inserted artificial microhole. In the case of a hydrogen-charged fatigue test piece, the piece buffed immediately after the end of hydrogen charging and the artificial microhole was drilled.
[0034]
X-ray diffraction The amount of the martensite in the test area of the fatigue test piece of austenitic stainless steel was measured by x-ray diffraction. The x-ray diffraction was performed using a miniature x-ray stress measurement apparatus PSPC-RSF/KM manufactured by Rigaku Corporation (Akishima, Tokyo).
Quantitative analysis was determined from the integrated intensity ratio of the diffraction peaks of the austenitic phase {220} plane and the martensitic phase {211} plane using CrK a-rays. In SUS304, SUS316, and SUS316L the content of martensite in the test area before fatigue testing was about 3%
o.
[0035]
The content of martensite in the hydrogen-charged test areas was also about 3%. The content of martensite was measured in two places before the artificial microhole was inserted. The first measurement region was a circular region 1 mm in diameter centered on the spot at which the artificial microhole was to be drilled. The second measurement region was a region 1 mm in diameter centered on a spot defined by rotating the lengthwise axis of the test piece 1800 from the spot where the artificial microhole was to be drilled. In other words, the second measurement region was located on the opposite side of the cylinder from the first measurement region.
[0036]
Hydrogen charging method Hydrogen charging was performed using the cathodic charging method. The hydrogen charging conditions were an aqueous sulfuric acid solution at pH = 3.5, platinum anode, and current density i = 27 A/m2. Hydrogen charging was performed for 672 hours (4 weeks) at a solution temperature of 50 C (323 K) and 336 hours (2 weeks) at a solution temperature of 80 C (353 K). The sulfuric acid solution was replaced once a week to minimize changes in the sulfuric acid concentration resulting from evaporation.
[0037]
Prestrained material To investigate the relationship between the acceleration in fatigue crack growth rate resulting from hydrogen and the amount of martensitic transformation, prestraining was performed on SUS304 and SUS316L, and martensite-transformed test pieces therefrom were used. Figure 3 shows a chart illustrating the prestraining procedure.
Because prestraining promotes martensitic transformation, it was performed in -70 C ethanol. After prestraining, the test piece was worked into the shape shown Figure 1(a). For the SUS304, prestraining was applied at a plastic strain (true strain) of sp = 0.28, and for SUS316L prestraining was applied at a plastic strain of EP = 0.35 [0038]
When the Vickers hardness was measured after the prestrain was applied (measurement load of 9.8 N), it was HV =
426 (10 point average) for SUS304, and HV = 351 (10 point average) for SUS316L. The variation was within 4%. After the test piece was polished, the amount of martensite in the test area after prestraining was measured by x-ray diffraction. The martensite content in SUS304 was 65o to 69% by specific volume, and in SUS316L was 26% to 28% by specific volume. The amount of martensite was measured at two locations before the artificial microhole was drilled. The measurement regions were 1 mm in diameter centered on the spot where the artificial microhole was to be drilled and a spot defined by rotating the lengthwise axis of the test piece 180 from the spot where the artificial microhole was to be drilled.
[0039]
Fatigue test method The fatigue test used a hydraulic servo-controlled tension and compression fatigue testing machine "Servopulser EHF-ED30KN" manufactured by Shimadzu Corporation (Chukyo-ku, Kyoto), with an repetition rate of 0.0015 to 5 Hz, and a stress ratio of R = -1. The repetition rate was adjusted so that the surface temperature of the test area did not exceed 60 C during the fatigue test. The fatigue cracks were observed using the replica method, and the length of the fatigue cracks measured.
[0040]
Observation of the fatigue cracks by the replica method revealed the following. After a 0.034 mm thick acetyl cellulose film (hereinafter, called the replica film) had been immersed in methyl acetate liquid for a short time, it was applied to observation site. Two or three minutes elapsed after the replica film was applied, and the replica film was then peel off after it had dried. Gold was deposited on the recovered replica film, and the fatigue cracks in the test area were observed with a metallurgical microscope.
[0041]
Therefore, even if the test piece was not observed directly, the location of a target fatigue crack could be observed. In the case of hydrogen-charged material, a sample 7 mm in diameter and 0.8 mm in thickness was cut out from the test area immediately after the end of fatigue testing, maintained in a vacuum chamber, and heated at a constant heating rate. The vacuum chamber internal pressure was 1x10-' Pa to 3x10-' Pa before the sample was heated. The temperature was raised up to 800 C at a heating rate of 0.5 C/sec.
[0042]
Heating the sample in the vacuum chamber caused hydrogen to escape therefrom, and the amount of escaped hydrogen was measured with a quadrupole mass analyzer type thermal desorption spectrometer (hereinafter, called TDS). The TDS used for measurement was a thermal desorption spectrometer model EMD-WA1000S/H manufactured by ESCO, Ltd. (Musashino, Tokyo). The precision of the TDS measurement was 0.01 mass ppm.
[0043]
Measured properties Figure 4 is a photograph of fatigue cracks that developed from the artificial microhole drilled in hydrogen-charged SUS304 after fatigue testing. From the photo it can be confirmed that the fatigue cracks spread from the artificial microhole. These fatigue cracks developed bilaterally from the artificial microhole, and it is clear that they grew in a roughly symmetrical manner.
[0044]
Figure 5 shows results of x-ray examination of the austenitic phase and martensitic phase in the test area surface before fatigue testing and the fatigue cracked surface after fatigue testing. The dotted line in Figure 5 shows the results of measuring the surface of the test area before fatigue testing. The solid line shows the results of measuring fatigue cracked surface after fatigue testing. Figure 5(a) shows the measurement results for SUS304, and from this measurement it is clear that after the fatigue testing the austenitic phase has decreased and the martensitic phrase has increased compared with before the fatigue testing.
[0045]
Figure 5(b) shows the measurement results for SUS316, and from this measurement it is clear that after fatigue testing the austenitic phase has decreased a little and the martensitic phrase has increased compared with before fatigue testing. Figure 5(c) shows the measurement results for SUS316L, and from this measurement it is clear that after fatigue testing the martensitic phrase has increased compared with before fatigue testing. Almost no change in the austenitic phase was seen for SUS316L.
[0046]
Figure 6 is a graph showing the relationship between the length of the cracks caused by fatigue testing and number of cycles. Figure 6(a) shows the results for SUS304, Figure 6(b) for SUS316, and Figure 6(c) for SUS316L. For each material (SUS304, SUS316, and SUS316L) the measurement results are shown for hydrogen-charged pieces and uncharged pieces.
The repetition rate was 1.2 Hz for SUS304 and SUS316, and 5 Hz for SUS316L.
[0047]
From this graph it is clear that the crack growth rate is accelerated in hydrogen-charged SUS304 and SUS316 compared with the uncharged material. For example, in hydrogen-charged material the number of cycles N until crack length 2a reaches 400 m is lower than in uncharged material. In these cases, the fatigue crack growth rate is approximately twice as fast in the hydrogen-charged pieces. On the other hand, for SUS316L
the fatigue crack growth rate is slightly higher in the hydrogen-charged material than in the uncharged material, but no clear difference is seen.
[0048]
Figure 7 shows photographs of fatigue cracks in SUS304, SUS316, and SUS316L observed by the replica method. As can be seen in the photograph in Figure 4, the fatigue cracks essentially grow symmetrically, and therefore the photographs in Figure 7 show only one side of the microhole. From the photographs it can be observed that the fatigue cracks in hydrogen-charged material tend to grow more linearly than in uncharged material. Whereas in the hydrogen-charged material the slip bands occur over a broad region, it is clear that in the uncharged material the slip bands are localized near the fatigue cracks.
[0049) Figure 8 is a graph showing the results of fatigue testing of SUS316L. This figure shows the fatigue test results of materials with a hydrogen content of 0.4 mass ppm and 2.6 mass ppm when uncharged, and after the material with a hydrogen content of 2.6 mass ppm was charged with hydrogen to raise the content to 3.9 mass ppm. The repetition rate until the fatigue crack reached a length of 200 m was 1.5 Hz. When the length of the fatigue crack became 200 m, the repetition rate was changed from 1.5 Hz to 0.0015 Hz. The fatigue cracks grew in material with a hydrogen content of 2.6 mass ppm and 3.9 mass ppm.
[0050]
However, fatigue cracks grew only slightly in the material with a hydrogen content of 0.4 mass ppm. Figure 9 is a graph showing the result of the fatigue testing of SUS316L.
This figure shows the fatigue test results of materials with a hydrogen content of 0.4 mass ppm and 2.6 mass ppm when uncharged, and results after the material with a hydrogen content of 2.6 mass ppm was charged with hydrogen to raise the content to 3.9 mass ppm and 5.1 mass ppm. The repetition rates were 1.5 Hz and 0.0015 Hz.
[0051]
From this graph it is clear that the fatigue cracks have grown in the material with a hydrogen content of 2.6 mass ppm and in the same material charged with hydrogen to a content of 3.9 mass ppm and 5.1 mass ppm. It is clear that when the repetition rate was a low 0.0015 Hz, the fatigue crack growth rate is faster than at a repetition rate of 1.5 Hz. However, it is also clear that in material with a hydrogen content of 0.4 mass ppm the fatigue crack growth rate is slower at repetition rates of both 0.0015 Hz and 1.5 Hz. This illustrates the fact that fatigue cracks do not grow much when the hydrogen content in the material is 0.4 mass ppm or less.
L0052]
Figure 10 is a conceptual drawing showing the situation wherein the diffusible hydrogen and the non-diffusible hydrogen diffuse through the transformed martensitic phase. In the figure the tip of the fatigue crack undergoes martensitic transformation, and the diffusible hydrogen and non-diffusible hydrogen diffuse via the martensitic phase. In other words, the hydrogen moves using the martensitic phase with its fast diffusion rate as a passageway, and it accumulates at the tip of the fatigue crack.
This is a phenomenon related to hydrogen diffusion and migration time. The rate of diffusion of the hydrogen in the austenitic phase (FCC) is four decimal places slower than the rate of diffusion in the martensitic phase (BCC). The fatigue crack periphery undergoes martensitic transformation, and the surrounding hydrogen diffuses through this martensitic phase and gathers at the tip of the fatigue crack.
[0053]
Involvement of non-diffusible hydrogen Therefore, through the above test it was shown that not only diffusible hydrogen, but also non-diffusible hydrogen, which has been disregarded in prior art, is involved in fatigue crack growth. This is a novel finding concerning hydrogen embrittlement, and the martensitic transformation of the fatigue crack tip (transformation from FCC to BCC) affects this.
[0054]
Relationship between fatigue test rate and fatigue crack growth rate In addition, from Figure 9 showing the above test results, it is clear that the fatigue crack growth rate accelerates in austenitic stainless steel such as SUS316L if the fatigue test rate is slow. In a similar manner, as shown in Figure 6, the fatigue crack growth rate is faster in hydrogen-charged material such as the test pieces charged with diffusible hydrogen than in uncharged material. As shown in Figures 8 and 9, fatigue cracks grow very little in material with a hydrogen content of 0.4 mass ppm or less. Thus, the effect of slowing the fatigue test rate is a phenomenon related to hydrogen diffusion and migration time (the diffusion rate is four decimal places slower in FCC than in BCC).
[0055]
Below the alloying components in the austenitic stainless steel of the present invention, the content thereof, and the manufacturing steps, etc., stipulated in the manufacturing process of the present invention are explained.
Austenitic stainless steel Austenitic stainless steel is also called Cr-Ni stainless steel, and it involves the addition of chromium and nickel to iron. The principal components of austenitic stainless steel are iron, chromium, and nickel with various additives shown in Table 2 below.
[0056]
Table 2 below shows preferred examples of the austenitic stainless steel of the present invention, but the mode of the present invention is by no means limited thereto.
[0057]
[Table 2]
Component Composition 1 Composition 2 (mass ratio) (mass ratio) C <-0.030 <0.08 Si. <1.00 <_1.50 Mn <_2.00 <2.00 Ni 12.00 to 15.00 8.00 to 27.00 Cr 16.00 to 18.00 13. 50 to 26. 00 Mo 2.00 to <-3.00 <_3.00 Al - 50.35 N - <-0.50 Ti - <_2.35 V - <-0.50 B - <-0.010 H <-0.00007 (0.7ppm) <_0.00007 (0.7ppm) Other Remainder Fe and Remainder Fe and inevitable impurities inevitable impurities [0058]
Chemical composition of austenitic stainless steel Chromium is added to iron to improve corrosion resistance. Nickel is added to iron in combination with chromium to increase corrosion resistance. Nickel and manganese are elements for insuring nonmagnetic properties after cold rolling. The nickel content must be 10.0 mass% or more to insure the nonmagnetic properties after cold rolling.
In addition, it is necessary to adjust the content of nickel according to the content of silicon and manganese so that a stress-induced martensitic phase of ?l vol% does not occur.
Manganese also has the effect of improving the solid solubility of nitrogen.
[0059]
Carbon is an element for a strong austenite formation.
In addition, carbon is an effective element for enhancing the strength of stainless steel. When an excess of carbon is added, coarse chromium carbides precipitate during the recrystallization process, and that causes a decrease in intergranular corrosion resistance and fatigue properties.
Silicon is added for deacidification and strengthening of the solid solution. Because generation of the martensitic phase during cold-working is promoted when the content of silicon increases, adding only a small amount thereof is preferred.
Nitrogen brings about solution hardening.
[0060]
Molybdenum is added for improved corrosion resistance.
In addition, it has the effect of bringing about the fine dispersion of carbonitrides in the aging treatment. Titanium is an effective element for precipitation hardening and is added to increase the strength brought about by the aging treatment. Boron is an effective alloying component for the prevention of edge cracks in the hot rolled steel area caused by the difference in the deformation resistance between the S-ferrite phase in the hot working temperature region and the austenitic phase. Aluminum is an element added for deacidification during steelmaking and is effective in precipitation hardening in a similar manner to titanium.
[0061]
The mode for carrying out the present invention can also be used by adding elements such as niobium, copper, etc., as needed in addition to the elements described in Table 2 above. Niobium can serve as a substitute for titanium.
Austenitic phase Austenitic stainless steel wherein the austenitic phase is essentially 100% of the total volume is preferred.
Austenitic stainless steel having no martensitic phase contained therein is preferable.
[0062]
Other properties The average crystalline particle diameter is preferably about 50 m or less. In modern materials the average crystalline particle diameter is about 50 m, but a smaller the average crystalline particle diameter is preferred.
[0063]
Hydrogen removal treatment by heating The hydrogen removal treatment involving the heating of austenitic stainless steel will now be described. The inventors of the present invention ascertained that non-diffusible hydrogen takes part in fatigue crack growth, and based upon that discovery, the heat treatment described below is performed to remove the non-diffusible hydrogen and the diffusible hydrogen present in austenitic stainless steel.
[0064]
Removal of the diffusible hydrogen and the non-diffusible hydrogen involves performing a heat treatment on the austenitic stainless steel at a heating temperature of 200 C or more. The heat treatment is performed in a vacuum.
The vacuum environment is 0.2 Pa or less. Moreover, for the heat treatment the austenitic stainless steel is maintained under vacuum at the heating temperature for 460 hours or less.
The temperature of the heat treatment is lower than the sensitization temperature, which is the temperature at which the carbides of chromium (Cr) in the austenitic stainless steel precipitate due to heating.
[0065]
For the austenitic stainless steels shown in Table 1 and Table 2, for example, the upper limit of the heating temperature is 500 C. As a result, both the non-diffusible hydrogen, and the diffusible hydrogen (which are present in austenitic stainless steel, diffuse via the stress-induced martensitic phase brought about by cyclic loading, concentrate in the cracks undergoing concentrated stress, and cause hydrogen embrittlement) can be removed.
[0066]
By such a heat treatment it is possible to remove from austenitic stainless steel the diffusible hydrogen and the non-diffusible hydrogen that cause hydrogen embrittlement therein, and thereby adjust the hydrogen (H) contained in austenitic stainless steel to 0.00007 mass% (0.7 mass ppm) or less. The preferred content of hydrogen (H) in austenitic stainless steel after this heat treatment is ~0.00004 mass%
(<-0.4 mass ppm), and <-0.00001 masso (<-0.1 mass ppm) is even more preferred.
[0067]
Thus, it is possible to provide an excellent austenitic stainless steel wherein the content of hydrogen therein is less than in the prior art austenitic stainless steels, and acceleration of fatigue crack growth does not occur even with cyclic loading involving a long cycle time.
[0068]
Additional Experimental Example 1 The experiment was performed on a heat-treated test piece of SUS316. The test piece was a rod 7 mm in diameter.
For the TDS measurement a disk 7 mm in diameter and 0.8 mm in thickness was cut from the rod. For the experiment the test piece was heat-treated at 800 C for 20 minutes. The atmospheres during the experiment were an air atmosphere, a vacuum atmosphere (approximately 0.006 Pa), and an argon gas atmosphere. The heat treatment was performed while supplying argon gas thereto. The heating rate for the TDS measurement was 0.5 C/second up to 700 C. The escaped hydrogen was measured for heating up to 700 C.
[0069]
The measurement was performed with a thermal desorption spectrometer model EMD-WA1000S/H manufactured by ESCO, Ltd. (Musashino, Tokyo). Figure 12 shows the measurement results. In the graph the horizontal axis shows the measurement temperature, and the vertical axis shows the hydrogen intensity. The hydrogen concentration of the test piece that had not been heat-treated was 1.5 mass ppm. When the heat treatment was performed in air, the hydrogen concentration of the test piece became 0.7 mass ppm. When the heat treatment was performed in a vacuum, the hydrogen concentration of the test piece became 0.4 mass ppm. When the heat treatment was performed under with the argon gas flow, the hydrogen concentration decreased to 0.4 mass ppm.
[0070]
Additional Experimental Example 2 The experiment was performed on a heat-treated test piece of SUH660. The test piece was a rod 7 mm in diameter.
For the TDS measurement a disk 7 mm in diameter and 0.8 mm in thickness was cut from the rod. For the experiment the test piece was heat-treated at 720 C for 16 hours. The atmosphere during the experiment was a vacuum atmosphere (approximately 0.006 Pa). The hydrogen concentration was 1.3 ppm before the aging treatment and 0.6 ppm after the aging treatment.
[0071]
In this manner, an aging treatment and the like was performed during the manufacturing process of stainless steel, and the hydrogen contained therein could be removed. The heating rate for the TDS measurement was 0.33 C/second up to 600 C. The escaped hydrogen was measured for heating up to 600 C. The measurement was performed with a thermal desorption spectrometer model EMD-WA1000S/H manufactured by ESCO, Ltd.
(Musashino, Tokyo). Figure 13 shows the measurement results.
The horizontal axis in the graph shows the measurement temperature, and vertical axis shows the hydrogen escape strength.
INDUSTRIAL APPLICABILITY
[0072]
The present invention is good for use in fields where corrosion resistance and high pressure hydrogen are necessary.
More specifically, the present invention is good for use in metal gaskets, various types of valves used in automobiles, springs, steel belts, cutting blade material, fuel cells, and material for valves, springs, etc., surrounding fuel cell systems.
The components of typical austenitic stainless steel are shown in Table 1. The first column in this Table 1 lists the names of stainless steels and the heat-resistant steels as defined in the Japanese Industrial Standards (JIS). The last column of Table 1 shows the Vickers hardness of the stainless steel (hereinafter, HV). Other columns are the chemical compositions of the stainless steel, and the amounts of the components are expressed in units of mass%. However, the content of hydrogen (H) is expressed as mass ppm (parts per million by mass).
Ln N -I
Ln M
i Ln N
ll:~
.L-1 i i ~ N ,-i ~o N a (N Ln Q0 Ln oo N r-=I N N M r-I r1 (N ~4 ~4 N (V UJ Q) d) N N Q) 4) a) N N
'~ `o -rI -ri -ri - I
'~ -~--I -H =ri --I -~-I -ri =ri E
~ ~ ~, ~ N N N N N 41 rx rx a a a x a a) a 00 CC) I'D
0 O O O O pp N N N N N
~ l0 ri di H 0) ri O lQ (N tf) Ol lfl O N L(1 O N N O ri O O l0 ~-I 01) 00 CO 00 t~ lO LC L-~ J r i r-I r i r-I r I r-I rl rl H N N I N
Lrl I!1 LIl o ~ (N N r-I M
al l9 Vi 61 rl 0 H I N N M
r1 O ri O .
~ C`7 N 01 d1 O
Zi 00 61 OD 00 r-I r-i r I r i - I r-I L t N
M L~ L(]
N OD H
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O O O O (N N 0 O O O
O O
~ O O O O O O O O O p O
V
~
~ O o0 N Lfl O O c-I L~ m M d Ol M N tn N M M N M N (N (N
rl O O O 0 Cp O O O O C) O O
S~ P O O 0 O O O O O O O O O
~ dl N Ol d ,~ l~ CO O L~ N L- CO
N
~ O O dl M M 01 O M
~ ~ rl rl O rl T-{
r-1 O ri O r--I r--I O
0\0 l0 Ln CCO L~ Ol M OC) M di dj (N
m M
U) ~ r Lfl N N Lfl C lf) M M
~ CI?. O O O O O O O O O 0 0 O
N LIl Ln Lt) Ltl N ~ r I
~ O
O O O O O O O O N ~
(D O p 1 ~ O O O O O ' . .
O O O O O O O
u ~ d d ~h V l0 l0 l0 l0 l0 O O ~
d r i O O O O -i rl H r--1 r-~ H ~ ~ ~''~ M M M f+') M M M M M M M
U2 Cf~ CI~ Ul m C!] Cf~ ~ C/1 CI] C!~ U1 CD I'D ~D ~D ~D ~D
Cf~ Cf1 CI] L1] CI) C!~ U] CI~ U1 U? U1 C!) r1 O
O
II
N =
o II
r-t r-I
Lf) fYl r-I
O
f'') di r-I
O
O
O
r-i O
O
N
di O
Lfl O
O
O
a' O
~o U) [0005]
It is known that hydrogen diffuses through metallic materials and decreases both the static strength and fatigue strength thereof (non-patent documents 1 and 2). Various processes for removing this hydrogen and methods for predicting the effect of hydrogen have been proposed. In patent document 2, for example, after the plating process austenitic stainless steel is heat-treated by maintaining it at a temperature of 270 to 400 C for 10 minutes or more to remove the hydrogen and prevent hydrogen embrittlement. Patent document 3 discloses a method wherein the extent of the hydrogen embrittlement of austenitic stainless steel is predicted and judged based on the chemical composition thereof.
[0006]
Non-patent document 1 presents fatigue testing results for austenitic stainless steels in compliance with SUS304, SUS316, and SUS316L. This fatigue testing was conducted by comparing these austenitic stainless steels with their hydrogen-charged counterparts. The fatigue crack growth rate of hydrogen-charged SUS304 and SUS316 was faster than in the corresponding uncharged steels. However, no clear difference was seen with SUS316L.
[0007]
In addition, non-patent document 1 presents fatigue test results for JIS SUS304 and the SUS316L austenitic stainless steels after the ~est piece was prestrained and a microhole of about 100 m was formed therein. The fatigue crack growth rate was accelerated ten-fold in hydrogen-charged SUS304 compared with the uncharged steel counterpart. Likewise, the fatigue crack growth rate was accelerated two-fold in SUS316L.
[0008]
However, even semi-stable austenitic stainless steel can undergo stress-induced martensitic transformation due to cold-working and cyclic stress. Persons skilled in the art in this industry, including groups of researchers in academic societies, have commonly believed that hydrogen had almost no effect on the fatigue crack growth rate in the austenitic stainless steels such as JIS SUS316L. Non-patent document 1 presents results that reverse this common belief, and because these results were obtained by applying cyclic loading at a low frequency of 5Hz or less, this finding is very significant.
[0009]
in other words, it has been verified that the growth rate of fatigue cracks is accelerated by low-frequency cyclic loading in austenitic stainless steel such as SUS316L. On the other hand, non-patent document 2 points out the following:
"(3) The martensitic phase resulting from transformation in austenitic stainless steel becomes a pathway for hydrogen diffusion throughout the material, and the diffusion coefficient of hydrogen is increased thereby (see page 130)."
[0010]
[Patent document 1] Japanese Patent Application Laid-open No.
[Patent document 2] Japanese Patent Application Laid-open No.
[Patent document 3] Japanese Patent Application Laid-open No.
[Non-patent document 1] Toshihiko KANEZAKI, Chihiro NARAZAKI, Yoji MINE, Saburo MATSUOKA, and Yukitaka MURAKAMI: The effect of hydrogen on fatigue crack growth of pre-strained austenitic stainless steel. The Japan Society of Mechanical Engineers [No.
05-9] Proceedings of the 2005 Annual Meeting of JSME/MMD, Vol.
2005 (November 4 to 6, 2005, Fukuoka) P86 p. 595-596.
[Non-patent document 2] Toshihiko KANEZAKI, Chihiro NARAZAKI, Yoji MINE, Saburo MATSUOKA, and Yukitaka MURAKAMI: Effect of hydrogen on fatigue crack growth and martensitic transformation of stainless steels. Transactions of the Japan Society of Mechanical Engineers A. Vol. 72, No. 723, (November 2006), p. 123-130. (manuscript received: May 1, 2006) [0011]
At present, however, sufficient analysis has not been performed concerning how non-diffusible hydrogen, which is present in crystals, and diffusible hydrogen, which is charged from the outside, are related to the aforementioned fatigue crack growth rate in austenitic stainless steels. In addition, the relationships involving how diffusible hydrogen and non-diffusible hydrogen influence changes in the amount of martensitic transformation, the effect of acceleration in the hydrogen diffusion rate, and the fatigue crack growth rate in a material have not been sufficiently clarified.
[00121 Furthermore, when stainless steel is used for equipment and apparatuses related to hydrogen fuel utilization, it is exposed to a variety of environmental influences depending on the usage environment. For example, when stainless steel is used for the high pressure hydrogen container, piping, and the like in a fuel cell-powered vehicle, loading and release are repeated in a relatively slow cycle that involves the filling of the high pressure hydrogen container with hydrogen gas and the subsequent consumption thereof. In the past, however, fatigue tests have not taken this slow cycle into account. In other words, it was thought that a fatigue test using a load with a long cycle could be replaced by a fatigue test with a quick repetition rate.
[00131 Moreover, low frequency cyclic loading occurs due to temperature variations in the outside air temperature_and the like. An example of cyclic loading due to variations in the outside air temperature is thermal stress resulting from compression and expansion of the stainless steel itself and of the parts connected to stainless steel components as a result of temperature differences between day and night. As for the frequency of the cycle, the temperature gradient between day and night can range from only a few degrees to ten degrees centigrade or more, and one cycle is 24 hours long. This means that high pressure hydrogen tanks at fuel cell vehicle-related facilities, facilities for supplying fuel for fuel cells, and the like will have a cycle measured in single day units as noted above, and the hydrogen fill time will be long. In addition, a fuel cell-powered vehicle is dependent on the environment in which it operates, and it will have a temperature gradient cycle ranging from a few degrees to several tens of degrees centigrade, and a time cycle expressed in units ranging from subseconds to several hours.
DISCLOSURE OF THE INVENTION
[0014]
The present invention is based on the above technological background, and it attains the following objects.
An object of the present invention is to provide an austenitic stainless steel for reducing the effect of hydrogen on the growth rate of fatigue cracks that occur in austenitic stainless steel, and a process for removing the hydrogen therefrom.
[0015]
Another object of the present invention is to focus on both diffusible hydrogen and non-diffusible hydrogen that cause hydrogen embrittlement in austenitic stainless steel and provide an austenitic stainless steel having both removed therefrom, and to provide a process for removing the hydrogen therefrom.
[001,6]
Another object of the present invention is to focus on the diffusible hydrogen and the non-diffusible hydrogen that become a problem with cyclic loading having a long cycle time and provide an austenitic stainless steel having both removed therefrom, and to provide a process for removing the hydrogen therefrom.
[0017]
Another object of the present invention is to provide an austenitic stainless steel wherein the diffusible hydrogen and non-diffusible hydrogen present in austenitic stainless steel are removed therefrom during a manufacturing step thereof, and a process for removing the hydrogen therefrom.
[0018] Definition of terms The present invention uses the following technical terms in the meanings defined below. Hydrogen charge means causing hydrogen to permeate the material. Hydrogen charge method refers to a method whereby the material is exposed in a high pressure hydrogen chamber, a method wherein cathodic charging is performed, and a method wherein the material is immersed in a chemical solution and the like. Fatigue crack growth refers to the enlargement of defects and cracks that occur in the material during the manufacturing process or cracks from holes and the like that are artificially introduced into the material as a result of cyclic loading.
u B
[0019]
Fatigue crack growth rate means the rate at which the fatigue crack progresses. Austenitic stainless steel refers to Cr-Ni series steel wherein chromium and nickel are added to iron to produce a stainless steel in the austenitic phase with increased corrosion resistance in corrosive environments and the like. Table 1 shows a list of this kind of stainless steel.
The austenitic phase is a phase of iron at a temperature range of 911 to 1392 C in 100% pure iron (Fe), and it has a face centered cubic lattice structure (hereinafter, FCC lattice structure).
[0020]
The FCC lattice is shown in Figure 11(a). The austenitic phase can also exist at room temperature when alloying elements such as chromium and nickel are added to iron. The martensitic phase is a conformation obtained by quenching steel at a high-temperature, stable austenitic phase, and it has a body centered cubic lattice structure (hereinafter, BCC lattice structure). The BCC lattice is shown in Figure 11(b). Moreover, the martensitic phase is caused by adding stress such as cold-working and the like to austenitic phase stainless steel at ordinary ambient temperatures.
[0021]
This transformation from an austenitic phase with an FCC structure to a martensitic phase with a BCC structure by cold working is called stress-induced martensitic transformation. Diffusible hydrogen refers to hydrogen that is present in the material and exits the material over time at room temperature. This diffusible hydrogen causes the hydrogen embrittlement of the material. Hydrogen that cannot exit the material over time even at temperatures from room temperature to about 200 C, is called non-diffusible hydrogen.
[0022]
The present invention adopts the following means to achieve the aforementioned objects.
The inventors of the present invention ascertained the fact that non-diffusible hydrogen in an austenitic stainless steel is related to fatigue crack growth.
The present invention concerns an austenitic stainless steel having an austenitic phase in which the crystal structure is an FCC lattice structure and a process for removing the hydrogen therefrom. The present invention is one wherein the diffusible hydrogen and the non-diffusible hydrogen that cause hydrogen embrittlement of austenitic stainless steel are removed, with the hydrogen (H) contained in the austenitic stainless steel being removed to a level of 0.00007 mass% (0.7 mass ppm) or less.
[0023]
A heat treatment at a heating temperature of 200 C or higher is preferred for the removal of diffusible hydrogen and non-diffusible hydrogen from austenitic stainless steel.
Moreover, the upper limit of the heating temperature for the heat treatment at this time is preferably no more than 500 C.
It is preferred that the heat treatment to remove the diffusible hydrogen and non-diffusible hydrogen is performed under vacuum.
[0024]
Moreover, the temperature range for the heating temperature is 200 to 500 C, and this range is preferred for removing both the non-diffusible hydrogen and the diffusible hydrogen, which are present in austenitic stainless steel, diffuse via the stress-induced martensitic phase brought about by cyclic loading, concentrate in the cracks undergoing concentrated stress, and cause hydrogen embrittlement therein, to thereby remove the hydrogen (H) contained therein to the aforementioned amount.
[0025]
It is preferred that the heating temperature is a temperature lower than the sensitization temperature, which is the temperature at which chromium (Cr) carbide in austenitic stainless steel precipitates due to the heat. Moreover, it is preferred that the aforementioned vacuum atmosphere is an environment of 0.2 Pa or less. In addition, it is preferred that the heat treatment is performed by maintaining the heating temperature in the aforementioned vacuum atmosphere for 460 hours or less.
[0026]
The amount of hydrogen (H) contained in the austenitic stainless steel after removing the diffusible hydrogen and the non-diffusible hydrogen is preferably 0.00004 massa (0.4 mass ppm) or less. Furthermore, the amount of hydrogen (H) contained in the austenitic stainless steel after removing the diffusible hydrogen and the non-diffusible hydrogen is more preferably 0.00001 mass% (0.1 mass ppm) or less.
[0027]
It is preferable that the heat treatment is performed for the predetermined time in the process of manufacturing the austenitic stainless steel, and the hydrogen is removed to adjust the hydrogen (H) to 0.00007 massa (0.7 mass ppm) or less. At that time, the heat treatment temperature is preferably 200 C or more, and less than the melting point temperature of the stainless steel. The heating time for this purpose preferably ranges from 30 seconds or more to several tens of hours or less. An inert gas flow atmosphere is preferred for this process. The manufacturing steps for austenitic stainless steel are the ones used when manufacturing stainless steel, and they include the steps of a solution heat treatment and an aging treatment.
[0028]
The hydrogen removal treatment in the manufacturing process can be performed in a vacuum or an atmosphere wherein the hydrogen partial pressure is low, e.g., an inert gas atmosphere. Moreover, the heat treatment preferably lasts from a few minutes to several tens of hours long.
In the case of a solution heat treatment, the most preferred temperature for the heat treatment is 920 C or higher.
In the case of an aging treatment, the most preferred temperature for the heat treatment is 700 C or higher.
In addition, it is preferred that the austenitic stainless steel is one of the aforementioned austenitic stainless steels or heat resistant austenitic steels shown in Table 1.
[0029]
The present invention provides the following advantageous effect. In the present invention austenitic stainless steel is heat-treated at a temperature of 200 C or higher to remove the non-diffusible hydrogen and the diffusible hydrogen, thereby making it possible to provide an austenitic stainless steel that is highly resistant to fatigue crack growth.
BRIEF DESCRIPTION OF THE DRAWINGS
[0073]
Figure 1 is a line drawing showing the fatigue test piece, Figure 1(a) is a drawing showing the shape of the fatigue test piece, and Figure 1(b) is a drawing showing the shape of the artificial microhole formed in the fatigue test piece;
Figure 2 shows a line drawing of the test area in the fatigue test piece and the fatigue crack starting at the small artificial hole and progressing therefrom;
Figure 3 is a schematic diagram of the procedure for applying the prestrain to the fatigue test piece;
Figure 4 is a photograph of the fatigue cracks emanating from the artificial microhole after fatigue testing;
Figure 5 shows results of x-ray examination of the austenitic phase and martensitic phase in the test area surface before fatigue testing and the fatigue cracked surface after fatigue testing wherein Figure 5(a) shows the measurement results for SUS304, Figure 5(b) shows the measurement results for SUS316, and Figure 5(c) shows the measurement results for SUS316L;
Figure 6 is a graph showing the relationship between the length of the cracks caused by fatigue testing and number of cycles wherein Figure 6(a) shows the results for SUS304, Figure 6(b) for SUS316, and Figure 6(c) for SUS316L;
Figure 7 shows photographs of fatigue cracks in SUS304, SUS316, and SUS316L observed by the replica method;
Figure 8 is a graph showing the results of fatigue testing of SUS316L;
Figure 9 is a graph showing the result of the fatigue testing of SUS316L;
Figure 10 is a conceptual drawing showing the circumstances wherein the diffusible hydrogen and the non-diffusible hydrogen diffuse through the transformed martensitic phase;
Figure 11 is a schematic drawing showing the lattices of the crystal structures of the austenitic phase and martensitic phase wherein Figure 11(a) shows the face centered cubic lattice structure (FCC) of the austenitic phase, and Figure 11(b) shows the body centered cubic lattice structure (BCC) of the martensitic phase;
Figure 12 is a graph showing the results of Additional Experimental Example 1; and Figure 13 is a graph showing the results of Additional Experimental Example 2.
BEST MODE FOR CARRYING OUT THE INVENTION
[00301 Below the mode of the present invention is explained through examples. First of all, the way hydrogen affects the growth rate of fatigue cracks in austenitic stainless steel will be explained. After a conventional heat treatment (solution heat treatment) is performed, austenitic stainless steels such as SUS304, SUS316, and SUS316L shown in Table 1 contain 1 to 4.7 mass ppm of non-diffusible hydrogen. In the past persons skilled in the art believed that this non-diffusible hydrogen had no effect on hydrogen embrittlement.
[00311 However, the fatigue tests described below have determined that non-diffusible hydrogen affects hydrogen embrittlement. Hydrogen embrittlement resulting from non-diffusible hydrogen has been verified at a low frequency fatigue testing speed of about 0.0015 Hz in (approximately 11 minutes as the repetition time of one cycle) in particular.
The inventors of the present invention performed the following tests and observed how non-diffusible hydrogen affected the growth rate of the fatigue cracks. One example of such testing is shown herein.
[0032]
Test piece The materials used were the SUS304, SUS316, and SUS316L(A) (hereinafter, simply called SUS316L) austenitic stainless steels shown in Table 1. A solution heat treatment was performed on the SUS304, SUS316, and SUS316L steels used.
The shape of the fatigue test piece is shown in Figure 1(a).
The surface of the test piece was finished by buffing after polishing with # 2000 emery paper.
[0033]
As shown in Figure i(b), an artificiai microhole 100 ~tm in diameter and 100 m deep was opened in the center of the fatigue test piece in the lengthwise direction with a drill having a radial tip angle of 120 to facilitate observation of fatigue crack growth. The artificial microhole was inserted in the center of the test area of the test piece. The test area was a cylindrical part at the center of the test piece, and the length of the cylinder was approximately 20 mm. The top and bottom surfaces of the cylinder were mutually parallel, and lay perpendicular to the lengthwise axis of the test piece..
Figure 2 illustrates an outline of the test piece and the shape of the inserted artificial microhole. In the case of a hydrogen-charged fatigue test piece, the piece buffed immediately after the end of hydrogen charging and the artificial microhole was drilled.
[0034]
X-ray diffraction The amount of the martensite in the test area of the fatigue test piece of austenitic stainless steel was measured by x-ray diffraction. The x-ray diffraction was performed using a miniature x-ray stress measurement apparatus PSPC-RSF/KM manufactured by Rigaku Corporation (Akishima, Tokyo).
Quantitative analysis was determined from the integrated intensity ratio of the diffraction peaks of the austenitic phase {220} plane and the martensitic phase {211} plane using CrK a-rays. In SUS304, SUS316, and SUS316L the content of martensite in the test area before fatigue testing was about 3%
o.
[0035]
The content of martensite in the hydrogen-charged test areas was also about 3%. The content of martensite was measured in two places before the artificial microhole was inserted. The first measurement region was a circular region 1 mm in diameter centered on the spot at which the artificial microhole was to be drilled. The second measurement region was a region 1 mm in diameter centered on a spot defined by rotating the lengthwise axis of the test piece 1800 from the spot where the artificial microhole was to be drilled. In other words, the second measurement region was located on the opposite side of the cylinder from the first measurement region.
[0036]
Hydrogen charging method Hydrogen charging was performed using the cathodic charging method. The hydrogen charging conditions were an aqueous sulfuric acid solution at pH = 3.5, platinum anode, and current density i = 27 A/m2. Hydrogen charging was performed for 672 hours (4 weeks) at a solution temperature of 50 C (323 K) and 336 hours (2 weeks) at a solution temperature of 80 C (353 K). The sulfuric acid solution was replaced once a week to minimize changes in the sulfuric acid concentration resulting from evaporation.
[0037]
Prestrained material To investigate the relationship between the acceleration in fatigue crack growth rate resulting from hydrogen and the amount of martensitic transformation, prestraining was performed on SUS304 and SUS316L, and martensite-transformed test pieces therefrom were used. Figure 3 shows a chart illustrating the prestraining procedure.
Because prestraining promotes martensitic transformation, it was performed in -70 C ethanol. After prestraining, the test piece was worked into the shape shown Figure 1(a). For the SUS304, prestraining was applied at a plastic strain (true strain) of sp = 0.28, and for SUS316L prestraining was applied at a plastic strain of EP = 0.35 [0038]
When the Vickers hardness was measured after the prestrain was applied (measurement load of 9.8 N), it was HV =
426 (10 point average) for SUS304, and HV = 351 (10 point average) for SUS316L. The variation was within 4%. After the test piece was polished, the amount of martensite in the test area after prestraining was measured by x-ray diffraction. The martensite content in SUS304 was 65o to 69% by specific volume, and in SUS316L was 26% to 28% by specific volume. The amount of martensite was measured at two locations before the artificial microhole was drilled. The measurement regions were 1 mm in diameter centered on the spot where the artificial microhole was to be drilled and a spot defined by rotating the lengthwise axis of the test piece 180 from the spot where the artificial microhole was to be drilled.
[0039]
Fatigue test method The fatigue test used a hydraulic servo-controlled tension and compression fatigue testing machine "Servopulser EHF-ED30KN" manufactured by Shimadzu Corporation (Chukyo-ku, Kyoto), with an repetition rate of 0.0015 to 5 Hz, and a stress ratio of R = -1. The repetition rate was adjusted so that the surface temperature of the test area did not exceed 60 C during the fatigue test. The fatigue cracks were observed using the replica method, and the length of the fatigue cracks measured.
[0040]
Observation of the fatigue cracks by the replica method revealed the following. After a 0.034 mm thick acetyl cellulose film (hereinafter, called the replica film) had been immersed in methyl acetate liquid for a short time, it was applied to observation site. Two or three minutes elapsed after the replica film was applied, and the replica film was then peel off after it had dried. Gold was deposited on the recovered replica film, and the fatigue cracks in the test area were observed with a metallurgical microscope.
[0041]
Therefore, even if the test piece was not observed directly, the location of a target fatigue crack could be observed. In the case of hydrogen-charged material, a sample 7 mm in diameter and 0.8 mm in thickness was cut out from the test area immediately after the end of fatigue testing, maintained in a vacuum chamber, and heated at a constant heating rate. The vacuum chamber internal pressure was 1x10-' Pa to 3x10-' Pa before the sample was heated. The temperature was raised up to 800 C at a heating rate of 0.5 C/sec.
[0042]
Heating the sample in the vacuum chamber caused hydrogen to escape therefrom, and the amount of escaped hydrogen was measured with a quadrupole mass analyzer type thermal desorption spectrometer (hereinafter, called TDS). The TDS used for measurement was a thermal desorption spectrometer model EMD-WA1000S/H manufactured by ESCO, Ltd. (Musashino, Tokyo). The precision of the TDS measurement was 0.01 mass ppm.
[0043]
Measured properties Figure 4 is a photograph of fatigue cracks that developed from the artificial microhole drilled in hydrogen-charged SUS304 after fatigue testing. From the photo it can be confirmed that the fatigue cracks spread from the artificial microhole. These fatigue cracks developed bilaterally from the artificial microhole, and it is clear that they grew in a roughly symmetrical manner.
[0044]
Figure 5 shows results of x-ray examination of the austenitic phase and martensitic phase in the test area surface before fatigue testing and the fatigue cracked surface after fatigue testing. The dotted line in Figure 5 shows the results of measuring the surface of the test area before fatigue testing. The solid line shows the results of measuring fatigue cracked surface after fatigue testing. Figure 5(a) shows the measurement results for SUS304, and from this measurement it is clear that after the fatigue testing the austenitic phase has decreased and the martensitic phrase has increased compared with before the fatigue testing.
[0045]
Figure 5(b) shows the measurement results for SUS316, and from this measurement it is clear that after fatigue testing the austenitic phase has decreased a little and the martensitic phrase has increased compared with before fatigue testing. Figure 5(c) shows the measurement results for SUS316L, and from this measurement it is clear that after fatigue testing the martensitic phrase has increased compared with before fatigue testing. Almost no change in the austenitic phase was seen for SUS316L.
[0046]
Figure 6 is a graph showing the relationship between the length of the cracks caused by fatigue testing and number of cycles. Figure 6(a) shows the results for SUS304, Figure 6(b) for SUS316, and Figure 6(c) for SUS316L. For each material (SUS304, SUS316, and SUS316L) the measurement results are shown for hydrogen-charged pieces and uncharged pieces.
The repetition rate was 1.2 Hz for SUS304 and SUS316, and 5 Hz for SUS316L.
[0047]
From this graph it is clear that the crack growth rate is accelerated in hydrogen-charged SUS304 and SUS316 compared with the uncharged material. For example, in hydrogen-charged material the number of cycles N until crack length 2a reaches 400 m is lower than in uncharged material. In these cases, the fatigue crack growth rate is approximately twice as fast in the hydrogen-charged pieces. On the other hand, for SUS316L
the fatigue crack growth rate is slightly higher in the hydrogen-charged material than in the uncharged material, but no clear difference is seen.
[0048]
Figure 7 shows photographs of fatigue cracks in SUS304, SUS316, and SUS316L observed by the replica method. As can be seen in the photograph in Figure 4, the fatigue cracks essentially grow symmetrically, and therefore the photographs in Figure 7 show only one side of the microhole. From the photographs it can be observed that the fatigue cracks in hydrogen-charged material tend to grow more linearly than in uncharged material. Whereas in the hydrogen-charged material the slip bands occur over a broad region, it is clear that in the uncharged material the slip bands are localized near the fatigue cracks.
[0049) Figure 8 is a graph showing the results of fatigue testing of SUS316L. This figure shows the fatigue test results of materials with a hydrogen content of 0.4 mass ppm and 2.6 mass ppm when uncharged, and after the material with a hydrogen content of 2.6 mass ppm was charged with hydrogen to raise the content to 3.9 mass ppm. The repetition rate until the fatigue crack reached a length of 200 m was 1.5 Hz. When the length of the fatigue crack became 200 m, the repetition rate was changed from 1.5 Hz to 0.0015 Hz. The fatigue cracks grew in material with a hydrogen content of 2.6 mass ppm and 3.9 mass ppm.
[0050]
However, fatigue cracks grew only slightly in the material with a hydrogen content of 0.4 mass ppm. Figure 9 is a graph showing the result of the fatigue testing of SUS316L.
This figure shows the fatigue test results of materials with a hydrogen content of 0.4 mass ppm and 2.6 mass ppm when uncharged, and results after the material with a hydrogen content of 2.6 mass ppm was charged with hydrogen to raise the content to 3.9 mass ppm and 5.1 mass ppm. The repetition rates were 1.5 Hz and 0.0015 Hz.
[0051]
From this graph it is clear that the fatigue cracks have grown in the material with a hydrogen content of 2.6 mass ppm and in the same material charged with hydrogen to a content of 3.9 mass ppm and 5.1 mass ppm. It is clear that when the repetition rate was a low 0.0015 Hz, the fatigue crack growth rate is faster than at a repetition rate of 1.5 Hz. However, it is also clear that in material with a hydrogen content of 0.4 mass ppm the fatigue crack growth rate is slower at repetition rates of both 0.0015 Hz and 1.5 Hz. This illustrates the fact that fatigue cracks do not grow much when the hydrogen content in the material is 0.4 mass ppm or less.
L0052]
Figure 10 is a conceptual drawing showing the situation wherein the diffusible hydrogen and the non-diffusible hydrogen diffuse through the transformed martensitic phase. In the figure the tip of the fatigue crack undergoes martensitic transformation, and the diffusible hydrogen and non-diffusible hydrogen diffuse via the martensitic phase. In other words, the hydrogen moves using the martensitic phase with its fast diffusion rate as a passageway, and it accumulates at the tip of the fatigue crack.
This is a phenomenon related to hydrogen diffusion and migration time. The rate of diffusion of the hydrogen in the austenitic phase (FCC) is four decimal places slower than the rate of diffusion in the martensitic phase (BCC). The fatigue crack periphery undergoes martensitic transformation, and the surrounding hydrogen diffuses through this martensitic phase and gathers at the tip of the fatigue crack.
[0053]
Involvement of non-diffusible hydrogen Therefore, through the above test it was shown that not only diffusible hydrogen, but also non-diffusible hydrogen, which has been disregarded in prior art, is involved in fatigue crack growth. This is a novel finding concerning hydrogen embrittlement, and the martensitic transformation of the fatigue crack tip (transformation from FCC to BCC) affects this.
[0054]
Relationship between fatigue test rate and fatigue crack growth rate In addition, from Figure 9 showing the above test results, it is clear that the fatigue crack growth rate accelerates in austenitic stainless steel such as SUS316L if the fatigue test rate is slow. In a similar manner, as shown in Figure 6, the fatigue crack growth rate is faster in hydrogen-charged material such as the test pieces charged with diffusible hydrogen than in uncharged material. As shown in Figures 8 and 9, fatigue cracks grow very little in material with a hydrogen content of 0.4 mass ppm or less. Thus, the effect of slowing the fatigue test rate is a phenomenon related to hydrogen diffusion and migration time (the diffusion rate is four decimal places slower in FCC than in BCC).
[0055]
Below the alloying components in the austenitic stainless steel of the present invention, the content thereof, and the manufacturing steps, etc., stipulated in the manufacturing process of the present invention are explained.
Austenitic stainless steel Austenitic stainless steel is also called Cr-Ni stainless steel, and it involves the addition of chromium and nickel to iron. The principal components of austenitic stainless steel are iron, chromium, and nickel with various additives shown in Table 2 below.
[0056]
Table 2 below shows preferred examples of the austenitic stainless steel of the present invention, but the mode of the present invention is by no means limited thereto.
[0057]
[Table 2]
Component Composition 1 Composition 2 (mass ratio) (mass ratio) C <-0.030 <0.08 Si. <1.00 <_1.50 Mn <_2.00 <2.00 Ni 12.00 to 15.00 8.00 to 27.00 Cr 16.00 to 18.00 13. 50 to 26. 00 Mo 2.00 to <-3.00 <_3.00 Al - 50.35 N - <-0.50 Ti - <_2.35 V - <-0.50 B - <-0.010 H <-0.00007 (0.7ppm) <_0.00007 (0.7ppm) Other Remainder Fe and Remainder Fe and inevitable impurities inevitable impurities [0058]
Chemical composition of austenitic stainless steel Chromium is added to iron to improve corrosion resistance. Nickel is added to iron in combination with chromium to increase corrosion resistance. Nickel and manganese are elements for insuring nonmagnetic properties after cold rolling. The nickel content must be 10.0 mass% or more to insure the nonmagnetic properties after cold rolling.
In addition, it is necessary to adjust the content of nickel according to the content of silicon and manganese so that a stress-induced martensitic phase of ?l vol% does not occur.
Manganese also has the effect of improving the solid solubility of nitrogen.
[0059]
Carbon is an element for a strong austenite formation.
In addition, carbon is an effective element for enhancing the strength of stainless steel. When an excess of carbon is added, coarse chromium carbides precipitate during the recrystallization process, and that causes a decrease in intergranular corrosion resistance and fatigue properties.
Silicon is added for deacidification and strengthening of the solid solution. Because generation of the martensitic phase during cold-working is promoted when the content of silicon increases, adding only a small amount thereof is preferred.
Nitrogen brings about solution hardening.
[0060]
Molybdenum is added for improved corrosion resistance.
In addition, it has the effect of bringing about the fine dispersion of carbonitrides in the aging treatment. Titanium is an effective element for precipitation hardening and is added to increase the strength brought about by the aging treatment. Boron is an effective alloying component for the prevention of edge cracks in the hot rolled steel area caused by the difference in the deformation resistance between the S-ferrite phase in the hot working temperature region and the austenitic phase. Aluminum is an element added for deacidification during steelmaking and is effective in precipitation hardening in a similar manner to titanium.
[0061]
The mode for carrying out the present invention can also be used by adding elements such as niobium, copper, etc., as needed in addition to the elements described in Table 2 above. Niobium can serve as a substitute for titanium.
Austenitic phase Austenitic stainless steel wherein the austenitic phase is essentially 100% of the total volume is preferred.
Austenitic stainless steel having no martensitic phase contained therein is preferable.
[0062]
Other properties The average crystalline particle diameter is preferably about 50 m or less. In modern materials the average crystalline particle diameter is about 50 m, but a smaller the average crystalline particle diameter is preferred.
[0063]
Hydrogen removal treatment by heating The hydrogen removal treatment involving the heating of austenitic stainless steel will now be described. The inventors of the present invention ascertained that non-diffusible hydrogen takes part in fatigue crack growth, and based upon that discovery, the heat treatment described below is performed to remove the non-diffusible hydrogen and the diffusible hydrogen present in austenitic stainless steel.
[0064]
Removal of the diffusible hydrogen and the non-diffusible hydrogen involves performing a heat treatment on the austenitic stainless steel at a heating temperature of 200 C or more. The heat treatment is performed in a vacuum.
The vacuum environment is 0.2 Pa or less. Moreover, for the heat treatment the austenitic stainless steel is maintained under vacuum at the heating temperature for 460 hours or less.
The temperature of the heat treatment is lower than the sensitization temperature, which is the temperature at which the carbides of chromium (Cr) in the austenitic stainless steel precipitate due to heating.
[0065]
For the austenitic stainless steels shown in Table 1 and Table 2, for example, the upper limit of the heating temperature is 500 C. As a result, both the non-diffusible hydrogen, and the diffusible hydrogen (which are present in austenitic stainless steel, diffuse via the stress-induced martensitic phase brought about by cyclic loading, concentrate in the cracks undergoing concentrated stress, and cause hydrogen embrittlement) can be removed.
[0066]
By such a heat treatment it is possible to remove from austenitic stainless steel the diffusible hydrogen and the non-diffusible hydrogen that cause hydrogen embrittlement therein, and thereby adjust the hydrogen (H) contained in austenitic stainless steel to 0.00007 mass% (0.7 mass ppm) or less. The preferred content of hydrogen (H) in austenitic stainless steel after this heat treatment is ~0.00004 mass%
(<-0.4 mass ppm), and <-0.00001 masso (<-0.1 mass ppm) is even more preferred.
[0067]
Thus, it is possible to provide an excellent austenitic stainless steel wherein the content of hydrogen therein is less than in the prior art austenitic stainless steels, and acceleration of fatigue crack growth does not occur even with cyclic loading involving a long cycle time.
[0068]
Additional Experimental Example 1 The experiment was performed on a heat-treated test piece of SUS316. The test piece was a rod 7 mm in diameter.
For the TDS measurement a disk 7 mm in diameter and 0.8 mm in thickness was cut from the rod. For the experiment the test piece was heat-treated at 800 C for 20 minutes. The atmospheres during the experiment were an air atmosphere, a vacuum atmosphere (approximately 0.006 Pa), and an argon gas atmosphere. The heat treatment was performed while supplying argon gas thereto. The heating rate for the TDS measurement was 0.5 C/second up to 700 C. The escaped hydrogen was measured for heating up to 700 C.
[0069]
The measurement was performed with a thermal desorption spectrometer model EMD-WA1000S/H manufactured by ESCO, Ltd. (Musashino, Tokyo). Figure 12 shows the measurement results. In the graph the horizontal axis shows the measurement temperature, and the vertical axis shows the hydrogen intensity. The hydrogen concentration of the test piece that had not been heat-treated was 1.5 mass ppm. When the heat treatment was performed in air, the hydrogen concentration of the test piece became 0.7 mass ppm. When the heat treatment was performed in a vacuum, the hydrogen concentration of the test piece became 0.4 mass ppm. When the heat treatment was performed under with the argon gas flow, the hydrogen concentration decreased to 0.4 mass ppm.
[0070]
Additional Experimental Example 2 The experiment was performed on a heat-treated test piece of SUH660. The test piece was a rod 7 mm in diameter.
For the TDS measurement a disk 7 mm in diameter and 0.8 mm in thickness was cut from the rod. For the experiment the test piece was heat-treated at 720 C for 16 hours. The atmosphere during the experiment was a vacuum atmosphere (approximately 0.006 Pa). The hydrogen concentration was 1.3 ppm before the aging treatment and 0.6 ppm after the aging treatment.
[0071]
In this manner, an aging treatment and the like was performed during the manufacturing process of stainless steel, and the hydrogen contained therein could be removed. The heating rate for the TDS measurement was 0.33 C/second up to 600 C. The escaped hydrogen was measured for heating up to 600 C. The measurement was performed with a thermal desorption spectrometer model EMD-WA1000S/H manufactured by ESCO, Ltd.
(Musashino, Tokyo). Figure 13 shows the measurement results.
The horizontal axis in the graph shows the measurement temperature, and vertical axis shows the hydrogen escape strength.
INDUSTRIAL APPLICABILITY
[0072]
The present invention is good for use in fields where corrosion resistance and high pressure hydrogen are necessary.
More specifically, the present invention is good for use in metal gaskets, various types of valves used in automobiles, springs, steel belts, cutting blade material, fuel cells, and material for valves, springs, etc., surrounding fuel cell systems.
Claims (12)
1. An austenitic stainless steel having an austenitic phase in which a crystalline structure is a face centered cubic lattice structure, wherein diffusible hydrogen and non-diffusible hydrogen, which are cause of hydrogen embrittlement in the austenitic stainless steel, are removed therefrom such that the hydrogen (H) contained in the austenitic stainless steel is removed to a level of 0.00007 mass% (0.7 mass ppm) or less.
2. The austenitic stainless steel according to claim 1, wherein the diffusible hydrogen and non-diffusible hydrogen are removed therefrom such that the hydrogen (H) is removed to a level of 0.00004 mass% (0.4 mass ppm) or less.
3. The austenitic stainless steel according to claim 2, wherein the diffusible hydrogen and non-diffusible hydrogen are removed therefrom such that the hydrogen (H) is removed to a level of 0.00001 mass% (0.1 mass ppm) or less.
4. The austenitic stainless steel according to any one of claims 1 to 3, wherein the austenitic stainless steel is heat-treated at a heating temperature of 200°C or higher to remove the diffusible and non-diffusible hydrogen therefrom.
5. The austenitic stainless steel according to claim 4, wherein the heating temperature is a temperature from 200°C to 500°C.
6. A process for removing hydrogen from an austenitic stainless steel, in which the austenitic stainless steel having an austenitic phase in which a crystalline structure is a face centered cubic lattice structure is heat-treated in a heat treatment to remove the hydrogen present in the austenitic stainless steel, wherein the austenitic stainless steel is heated to a heating temperature of 200°C or higher to remove the diffusible hydrogen and non-diffusible hydrogen in the austenitic stainless steel to a level of 0.00007 mass% (0.7 mass ppm) or less.
7. The process for removing hydrogen from austenitic stainless steel according to claim 6, wherein the heating temperature is a temperature from 200°C to 500°C, and both the diffusible hydrogen and non-diffusible hydrogen, which are present in the austenitic stainless steel, diffuse via the stress-induced martensitic phase brought about by cyclic loading, concentrate in the cracks undergoing concentrated stress, and cause hydrogen embrittlement therein, are removed therefrom such that the hydrogen (H) contained therein is removed to a level of 0.00007 mass% (0.7 mass ppm) or less.
8. The process for removing hydrogen from austenitic stainless steel according to claim 6, wherein the austenitic stainless steel is maintained at a temperature from 200°C to 500°C, which is a temperature lower than the sensitization temperature at which chromium (Cr) carbide in the austenitic stainless steel precipitates due to the heat, for 460 hours or less, and both the diffusible hydrogen and non-diffusible hydrogen, which cause hydrogen embrittlement in the austenitic stainless steel, are removed therefrom such that the hydrogen (H) contained in the austenitic stainless steel is removed to a level of 0.00004 mass% (0.4 mass ppm) or less.
9. The process for removing hydrogen from an austenitic stainless steel according to claim 7 or 8, wherein the hydrogen (H) contained in the austenitic stainless steel is removed to a level of 0.00001 mass% (0.1 mass ppm) or less.
10. The process for removing hydrogen from an austenitic stainless steel according to claim 6, wherein the austenitic stainless steel is maintained at the heating temperature and in a temperature range below a melting point thereof for 30 seconds or more during the manufacturing process thereof to remove the diffusible hydrogen and non-diffusible hydrogen contained therein to a level of 0.00007 mass% (0.7 mass ppm) or less.
11. The process for removing hydrogen from austenitic stainless steel according to claim 10, wherein the heating temperature in the heat treatment to remove the hydrogen present therein is 700°C or more and also in a temperature range below the melting point of the austenitic stainless steel.
12. The process for removing hydrogen from austenitic stainless steel according to claim 11, wherein the heating temperature in the heat treatment to remove the hydrogen present therein is 920°C or higher, and the diffusible hydrogen and non-diffusible hydrogen therein are removed to a level of 0.00004 mass% (0.4 mass ppm) or less.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2007-022467 | 2007-01-31 | ||
| JP2007022467 | 2007-01-31 | ||
| PCT/JP2007/069589 WO2008093453A1 (en) | 2007-01-31 | 2007-10-05 | Austenite based stainless steel and method of dehydrogenating the same |
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| Publication Number | Publication Date |
|---|---|
| CA2649355A1 true CA2649355A1 (en) | 2008-08-07 |
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| Application Number | Title | Priority Date | Filing Date |
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| CA002649355A Abandoned CA2649355A1 (en) | 2007-01-31 | 2007-10-05 | Austenitic stainless steel and process for removing hydrogen therefrom |
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| Country | Link |
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| US (2) | US20090263269A1 (en) |
| EP (1) | EP2108710A4 (en) |
| JP (1) | JP2008208451A (en) |
| KR (1) | KR20090109466A (en) |
| CN (1) | CN101443469B (en) |
| CA (1) | CA2649355A1 (en) |
| WO (1) | WO2008093453A1 (en) |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| WO2008112620A1 (en) * | 2007-03-09 | 2008-09-18 | Federal-Mogul Corporation | Metal gasket |
| KR101212866B1 (en) * | 2008-02-29 | 2012-12-14 | 도꾸리쯔교세이호진상교기쥬쯔소고겡뀨죠 | Austenitic stainless steel and process for hydrogen removal thereof |
| JP4702900B2 (en) * | 2008-04-18 | 2011-06-15 | 株式会社日立メタルプレシジョン | Fe-base alloy clip and manufacturing method thereof |
| JP5177747B2 (en) * | 2008-08-06 | 2013-04-10 | 独立行政法人産業技術総合研究所 | Austenitic stainless steel and its hydrogenation method |
| KR101475679B1 (en) * | 2012-12-14 | 2014-12-23 | 한국에너지기술연구원 | Hydrogen membrane module for carbon dioxide capture |
| MX2015013607A (en) * | 2013-03-28 | 2016-01-12 | Nippon Steel & Sumikin Sst | Heat-resistant austenitic stainless steel sheet. |
| FI126798B (en) * | 2013-07-05 | 2017-05-31 | Outokumpu Oy | Delayed fracture resistant stainless steel and method for its production |
| CN107741449B (en) * | 2017-09-14 | 2019-12-13 | 浙江大学 | testing device for martensite volume fraction in austenitic stainless steel |
| CN107741452B (en) * | 2017-09-14 | 2019-12-13 | 浙江大学 | method for testing volume fraction of martensite in austenitic stainless steel |
| KR102415777B1 (en) * | 2018-03-30 | 2022-07-01 | 닛테츠 스테인레스 가부시키가이샤 | Two-phase stainless steel clad steel sheet and its manufacturing method |
| FR3084375A1 (en) * | 2018-07-25 | 2020-01-31 | Metallo Corner | PROCESS FOR REMOVAL OF HYDROGEN FROM A MECHANICAL PART OF TEMPERED AND REVENTED STEEL |
| CN111721663B (en) * | 2019-03-21 | 2022-06-28 | 宝山钢铁股份有限公司 | Method for evaluating fish scaling performance of steel for enamel |
| WO2022014172A1 (en) * | 2020-07-14 | 2022-01-20 | Ｊｆｅスチール株式会社 | Dehydrogenation method for steel material and steel product, and manufacturing method for steel material and steel product |
| CN116034172A (en) * | 2020-07-14 | 2023-04-28 | 杰富意钢铁株式会社 | Dehydrogenation method for steel material and steel product, and method for producing steel material and steel product |
| KR20230029864A (en) * | 2020-07-14 | 2023-03-03 | 제이에프이 스틸 가부시키가이샤 | Dehydrogenation device and steel plate manufacturing system, and steel plate manufacturing method |
| CN111996345A (en) * | 2020-07-30 | 2020-11-27 | 中国科学院金属研究所 | Oxidation-free dehydrogenation treatment process for austenitic stainless steel welding material |
| CN114196810B (en) * | 2020-09-17 | 2024-03-08 | 宝山钢铁股份有限公司 | Method for removing hydrogen from high-strength steel coil |
| WO2023181821A1 (en) * | 2022-03-25 | 2023-09-28 | Ｊｆｅスチール株式会社 | Dehydrogenation device, system for manufacturing steel sheet, and method for manufacturing steel sheet |
| CN117444552B (en) * | 2023-12-25 | 2024-03-12 | 中北大学 | Method for improving hydrogen embrittlement resistance of 316L stainless steel hydrogen conveying pipe |
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| JPH0649538A (en) * | 1992-07-29 | 1994-02-22 | Nippon Nuclear Fuel Dev Co Ltd | Method for testing hydrogen embrittlement sensitivity of metallic material |
| JP3542239B2 (en) * | 1996-10-15 | 2004-07-14 | 新日本製鐵株式会社 | High-strength stainless wire with excellent resistance to longitudinal cracking and its wire |
| JP3718308B2 (en) | 1997-01-13 | 2005-11-24 | 株式会社東芝 | Manufacturing method of vacuum valve |
| WO1999009229A1 (en) * | 1997-08-19 | 1999-02-25 | Mitsubishi Heavy Industries, Ltd. | Austenitic stainless steel with resistance to deterioration by neutron irradiation |
| JPH11181517A (en) * | 1997-12-16 | 1999-07-06 | Nippon Steel Corp | Method for dehydrogenating steel |
| JP3966493B2 (en) * | 1999-05-26 | 2007-08-29 | 新日本製鐵株式会社 | Cold forging wire and method for producing the same |
| JP4489928B2 (en) * | 2000-11-09 | 2010-06-23 | 新日鐵住金ステンレス株式会社 | High strength austenitic stainless steel wire |
| US6699335B2 (en) * | 2000-11-15 | 2004-03-02 | Nsk Ltd. | Machine part |
| US7648586B2 (en) * | 2002-07-31 | 2010-01-19 | National Institute Of Advanced Industrial & Technology | Ultra-low carbon stainless steel |
| JP4331975B2 (en) | 2003-05-15 | 2009-09-16 | 新日本製鐵株式会社 | Manufacturing method and forming method of stainless steel plate for polymer electrolyte fuel cell separator |
| JP3867142B2 (en) | 2003-06-18 | 2007-01-10 | 独立行政法人産業技術総合研究所 | Method for judging austenitic stainless steel |
| JP4319083B2 (en) * | 2004-04-14 | 2009-08-26 | 新日鐵住金ステンレス株式会社 | Metastable austenitic stainless steel wire for high strength steel wire for springs with excellent rigidity |
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2007
- 2007-10-05 JP JP2007262057A patent/JP2008208451A/en active Pending
- 2007-10-05 US US12/301,707 patent/US20090263269A1/en not_active Abandoned
- 2007-10-05 KR KR1020087025288A patent/KR20090109466A/en not_active Application Discontinuation
- 2007-10-05 CA CA002649355A patent/CA2649355A1/en not_active Abandoned
- 2007-10-05 WO PCT/JP2007/069589 patent/WO2008093453A1/en active Application Filing
- 2007-10-05 CN CN2007800172824A patent/CN101443469B/en not_active Expired - Fee Related
- 2007-10-05 EP EP07829327A patent/EP2108710A4/en not_active Withdrawn
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Also Published As
| Publication number | Publication date |
|---|---|
| WO2008093453A1 (en) | 2008-08-07 |
| EP2108710A1 (en) | 2009-10-14 |
| CN101443469A (en) | 2009-05-27 |
| EP2108710A4 (en) | 2010-07-14 |
| KR20090109466A (en) | 2009-10-20 |
| CN101443469B (en) | 2012-10-24 |
| US20090263269A1 (en) | 2009-10-22 |
| US20100154939A1 (en) | 2010-06-24 |
| JP2008208451A (en) | 2008-09-11 |
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