JPS62238351A - Martensitic stainless steel for cold forging - Google Patents
Martensitic stainless steel for cold forgingInfo
- Publication number
- JPS62238351A JPS62238351A JP7988486A JP7988486A JPS62238351A JP S62238351 A JPS62238351 A JP S62238351A JP 7988486 A JP7988486 A JP 7988486A JP 7988486 A JP7988486 A JP 7988486A JP S62238351 A JPS62238351 A JP S62238351A
- Authority
- JP
- Japan
- Prior art keywords
- steel
- less
- stainless steel
- tensile strength
- martensitic stainless
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
- 229910001105 martensitic stainless steel Inorganic materials 0.000 title claims abstract description 9
- 238000010273 cold forging Methods 0.000 title claims abstract 5
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 229910052802 copper Inorganic materials 0.000 claims abstract description 3
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 3
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 3
- 230000007797 corrosion Effects 0.000 abstract description 23
- 238000005260 corrosion Methods 0.000 abstract description 23
- 239000000463 material Substances 0.000 abstract description 5
- 229910052804 chromium Inorganic materials 0.000 abstract description 4
- 239000000203 mixture Substances 0.000 abstract description 4
- 229910052758 niobium Inorganic materials 0.000 abstract description 3
- 229910001220 stainless steel Inorganic materials 0.000 abstract description 3
- 239000010935 stainless steel Substances 0.000 abstract description 3
- 229910052748 manganese Inorganic materials 0.000 abstract description 2
- 229910052759 nickel Inorganic materials 0.000 abstract description 2
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 abstract 1
- 230000015572 biosynthetic process Effects 0.000 abstract 1
- 229910052593 corundum Inorganic materials 0.000 abstract 1
- 230000002542 deteriorative effect Effects 0.000 abstract 1
- 229910001845 yogo sapphire Inorganic materials 0.000 abstract 1
- 229910000831 Steel Inorganic materials 0.000 description 45
- 239000010959 steel Substances 0.000 description 45
- 238000010586 diagram Methods 0.000 description 5
- 230000009466 transformation Effects 0.000 description 5
- 238000001816 cooling Methods 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 238000005275 alloying Methods 0.000 description 1
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 1
- 239000013535 sea water Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
Abstract
Description
【発明の詳細な説明】
(産業上の利用分野)
本発明は、船舶用スチームタービン、ブレード材、ネジ
、ボルト等に用いられる、焼なまし状態で優れた冷間鍛
造性を有し、かつ耐食性と、焼入硬化能が著しく優れた
高強度マルテンサイト系ステンレス鋼に関する。Detailed Description of the Invention (Field of Industrial Application) The present invention has excellent cold forgeability in an annealed state and is used for steam turbines for ships, blade materials, screws, bolts, etc. This invention relates to high-strength martensitic stainless steel with outstanding corrosion resistance and quench hardenability.
(従来技術)
マルテンサイト系ステンレス鋼として、一般にSOS
403 (0,I C−12Cr)力頌(食性と強度
を有することから船舶用スチームタービン、ブレード材
、ネジ、ボルト等に広く使用されている。(Prior art) SOS is generally used as martensitic stainless steel.
403 (0, I C-12Cr) Strength (It is widely used in steam turbines for ships, blade materials, screws, bolts, etc. due to its edibility and strength.
(解決するための問題点)
しかし、前記SUS 403は焼なまし状態での引張強
さが55kg / m m程度と高いため、冷間鍛造性
については必ずしも充分ではなかった。(Problems to be Solved) However, since the SUS 403 has a high tensile strength of about 55 kg/mm in an annealed state, its cold forgeability is not necessarily sufficient.
また耐食性についても苛酷な腐食条件では錆が発生する
など、耐食性についても改善が求められていた。There was also a need for improvement in corrosion resistance, as rust occurs under severe corrosive conditions.
(問題点を解決するための手段)
本発明は、前記のSO3403の上記欠点を鑑みて、1
2%Crステンレス鋼について、焼なまし状態での引張
強さに及ぼすCX5l−、Mn、、Crs N等の合金
元素の影響について鋭意研究を重ねた結果、clを01
07%以下と極力低下させることにより、焼なまし状態
で引張強さ47kg/mrJ以下とし、冷間鍛造性を改
善するとともに焼入、焼もどし状態での引張強さを60
kg / m m以上とし、低C量であるが現用のSU
S 403と同等の強度を得ることができ、さらに耐食
性についても大幅に改善できることに成功したものであ
る。(Means for Solving the Problems) In view of the above-mentioned drawbacks of SO3403, the present invention provides:
As a result of intensive research on the influence of alloying elements such as CX5l-, Mn, and CrsN on the tensile strength in the annealed state of 2%Cr stainless steel, we found that Cl was 01.
By reducing the tensile strength to 0.7% or less, the tensile strength in the annealed state is 47 kg/mrJ or less, improving cold forgeability, and the tensile strength in the quenched and tempered state is 60%.
kg/mm or more, and has a low C content, but the current SU
It was possible to obtain strength equivalent to that of S403, and also succeeded in significantly improving corrosion resistance.
すなわち、第1図に示したように、12%Cr鋼におい
て、c4と焼なまし状態での引張強さとの関係を調査し
、C量を0.07%以下に抑制することにより引張強さ
を47kg / m tr?以下となし、優れた冷間S
(2造性を得ること、まだ、第2図はC量と50℃、海
水に体する腐食速度との関係を調査し、C量を0.07
%以下とすることにより腐食速度を25g/rr?・1
)「以下とし、耐食性を改善すること、さらに、第3図
はCr当量とγ−M相変態量との関係を調査し、Cr当
量を10.5以下とすることにより、γ−M相変態量を
100%とし得ること、また第4図はγ−M相変態量1
00%の鋼においてC量と焼入、焼もどし状態での引張
強さとの関係を調査し、ciが0.01%で引張強さ6
0kg / m m以上となし、高強度とすること、さ
らに第5図はCr当量と1)00℃における絞り値との
関係を調査したもので、Cr当量を9.0以上とするこ
とにより絞り値を85%以上とし、熱間加工性を改善す
ることを見出したものである。That is, as shown in Figure 1, the relationship between c4 and tensile strength in an annealed state was investigated for 12% Cr steel, and by suppressing the C content to 0.07% or less, the tensile strength 47kg/mtr? Excellent cold S without the following
(Figure 2 shows the relationship between the amount of C and the corrosion rate in seawater at 50℃, and the amount of C is 0.07.
% or less, the corrosion rate can be reduced to 25g/rr?・1
) "By setting the Cr equivalent to 10.5 or less and improving the corrosion resistance, and furthermore, Fig. 3 investigates the relationship between the Cr equivalent and the amount of γ-M phase transformation, and by setting the Cr equivalent to 10.5 or less, the γ-M phase transformation is Fig. 4 shows that the amount of γ-M phase transformation can be 100%.
The relationship between the amount of C and the tensile strength in the quenched and tempered state was investigated for 0.00% steel, and the tensile strength was 6 when ci was 0.01%.
0kg/mm or more to achieve high strength.Furthermore, Figure 5 investigates the relationship between Cr equivalent and 1) aperture value at 00°C. It has been found that the value is 85% or more and hot workability is improved.
本発明はこれらの知見を基に、焼なまし状態で優れた冷
間鍛造性を有し、かつ耐食性と焼入硬化能が著しく優れ
た鋼を得るためのC,Sis Crs Nの最適含有量
を見出したものである。Based on these findings, the present invention aims to determine the optimum content of C, Sis Crs N, in order to obtain a steel that has excellent cold forgeability in an annealed state and has significantly excellent corrosion resistance and quench hardenability. This is what we discovered.
本発明は、重量比にしてC0.07%以下、Si0.4
0%以下、Mn 0.10〜1.0%、Cr 10.0
〜13.0%、N 0.02%以下を含有し、残部Fe
ならびに不純物元素からなり、かつCr当量が9.0〜
10.5であるもので、第2発明鋼は第1発明鋼のSを
0.003%以下、Oを0.0040%以下とし、第1
発明鋼の冷間鍛造性をさらに改善したものであり、第3
発明鋼は第1発明鋼に、さらにNi 0.50%以下、
CuO150%以下、Mo 1.5%以下、Tj 0.
20%以下、■0.15%以下、Nb 0.10%以下
のうち1種ないし2種以上を含有させ第1発明鋼の耐食
性をさらに改善したものである。The present invention has C0.07% or less and Si0.4% by weight.
0% or less, Mn 0.10-1.0%, Cr 10.0
~13.0%, N 0.02% or less, balance Fe
and impurity elements, and has a Cr equivalent of 9.0 to
10.5, and the second invention steel has S of the first invention steel of 0.003% or less and O of 0.0040% or less, and
This is a product that further improves the cold forgeability of the invented steel, and is the third
The invention steel is the first invention steel plus Ni 0.50% or less,
CuO 150% or less, Mo 1.5% or less, Tj 0.
The corrosion resistance of the first invention steel is further improved by containing one or more of Nb 20% or less, Nb 0.15% or less, and Nb 0.10% or less.
なお、Cr当量は次式によって算出したものである。C
r当fi=cr+2 Si−Mn −30C−25N
−2Ni−0,3Cu+ 1.5 (Mo+ Tt)
÷1.75Nb+ 5V以下に本発明鋼の成分限定理
由を説明する。Note that the Cr equivalent was calculated using the following formula. C
r hitfi=cr+2 Si-Mn-30C-25N
-2Ni-0,3Cu+ 1.5 (Mo+Tt)
÷1.75Nb+5V The reason for limiting the composition of the steel of the present invention will be explained below.
Cは焼なまし状態での引張強さを高め、冷間鍛造性を低
下させる元素であり、その含有量を極力低下させる必要
があり、上限を0.07%とした。C is an element that increases tensile strength in an annealed state and reduces cold forgeability, and its content must be reduced as much as possible, and the upper limit was set at 0.07%.
Siは脱酸に効果のある元素であるが、強力なフェライ
ト生成元素でもあり、また、冷間鍛造性を低下させる元
素でもあり、その上限を0゜40%とした。Although Si is an effective deoxidizing element, it is also a strong ferrite-forming element and also an element that reduces cold forgeability, so its upper limit was set at 0°40%.
Mnは脱酸に効果のある元素であるとともに強力なオー
ステナイト生成元素でもあり、下限を0.10%とした
。しかし多量に含有すると焼なまし状態での引張強さを
増加するので、その上限をi、oo%とした。Mn is an element effective in deoxidizing and is also a strong austenite-forming element, and the lower limit was set at 0.10%. However, if it is contained in a large amount, the tensile strength in an annealed state increases, so the upper limit is set as i,oo%.
Crはステンレス鋼の耐食性を付与する基本元素であり
、この効果を得るには10.0%以上含有させる必要が
あり下限を10.0%とした。しかしCrは強力なフェ
ライト生成元素でもあり、焼入性を損なうのでその上限
を13.0%とした。Cr is a basic element that imparts corrosion resistance to stainless steel, and to obtain this effect, it must be contained in an amount of 10.0% or more, and the lower limit was set at 10.0%. However, Cr is also a strong ferrite-forming element and impairs hardenability, so the upper limit was set at 13.0%.
Nは焼なまし状態での引張強さを高める元素であり、そ
の含有量を規制する必要があり上限を0.020%とし
た。N is an element that increases the tensile strength in an annealed state, and it is necessary to regulate its content, so the upper limit was set at 0.020%.
SはMr+Sを生成して冷間鍛造性を著しく低下させる
元素であり、その含有量の上限を0.003%とした。S is an element that generates Mr+S and significantly reduces cold forgeability, and the upper limit of its content is set to 0.003%.
0はn l )9の酸化物を生成して冷間鍛造性を著し
く低下させる元素であり、その含有量の上限を0.00
40%とした。0 is an element that produces oxides of n l )9 and significantly reduces cold forgeability, and the upper limit of its content is set to 0.00.
It was set at 40%.
Ni、 Cuは耐食性を向上する元素であるが、反面、
焼なまし状態での引張強さを高める元素でもありその上
限をNiは0.50%、Cuは0.50%とした。Ni and Cu are elements that improve corrosion resistance, but on the other hand,
It is also an element that increases the tensile strength in an annealed state, and the upper limit was set to 0.50% for Ni and 0.50% for Cu.
MO% i’i、 v、 Nbは焼もどし状態での引張
強さの改善に寄!j、ず元素であるが、反面、強力なフ
ェライト生成元素で焼入性を損なうのでその上限をN。MO% i'i, v, Nb contributes to improving the tensile strength in the tempered state! Although it is a j,z element, on the other hand, it is a strong ferrite-forming element and impairs hardenability, so the upper limit is set to N.
は1.5%、Tiは0.20%、V4.t0.15%、
Nb&;to、10%とした。is 1.5%, Ti is 0.20%, V4. t0.15%,
Nb&;to, 10%.
C「5置を10.5以下としたのはr−M相変態!10
0%を得るためであり、9.0未満では熱間加工性が低
下し、またl005を越えると所望の焼もどし硬さが得
られないためである。C “The reason why the 5 position is less than 10.5 is r-M phase transformation!10
This is because if it is less than 9.0, hot workability deteriorates, and if it exceeds 1005, the desired tempering hardness cannot be obtained.
(実施例)
つぎに本発明鋼の特徴を従来鋼、比較鋼と比べて実施例
でもって明らかにする。(Example) Next, the characteristics of the steel of the present invention will be clarified by comparing it with conventional steel and comparative steel through examples.
第1表はこれらの供試鋼の化学成分を示すものである。Table 1 shows the chemical composition of these test steels.
第1表において、A−S鋼は本発明鋼で、A〜F鋼は第
1発明鋼、G〜i鋼は第2発明鋼、J〜S鋼は第3発明
鋼、T−W鋼は比較鋼で、Xは従来鋼テ5l15403
である。In Table 1, A-S steel is the invention steel, A-F steel is the first invention steel, G-i steel is the second invention steel, J-S steel is the third invention steel, and T-W steel is the third invention steel. In the comparison steel, X is the conventional steel 5l15403
It is.
第2表は第1表の供試鋼について、900℃×1)1「
保持し、冷却速度25℃/Hrで600℃まで炉冷し、
ついで空冷という条件で焼なましを施したもの、第3表
は970℃×30分保持し、油境入れし、ついで600
〜750℃×2■「焼もどしを行ったものについて、硬
さと機械的性質を示したものである。Table 2 shows the test steel in Table 1 at 900°C x 1) 1"
and furnace cooling to 600°C at a cooling rate of 25°C/Hr.
Those that were annealed under the condition of air cooling, Table 3, were held at 970°C for 30 minutes, soaked in oil, and then heated to 600°C.
〜750℃×2■ This shows the hardness and mechanical properties of those that have been tempered.
0.2%、耐力、引張り強さ、伸び、絞りについてはJ
IS4号試験片を作製して測定した。0.2%, J for yield strength, tensile strength, elongation, and reduction of area.
An IS4 test piece was prepared and measured.
第2表
第3表
第2表より明らかなように、従来鋼であるX鋼は焼l(
まし状態での硬さがIlv 1(iQ、また0□2%耐
力が32.5kg/w、引張強さが55.6kg/mm
と高く、さらに絞り値が73.1%と冷間鍛造性が劣る
ものであり、また比較鋼であるX鋼は絞り値が78.1
%と低く冷間鍛造性が劣るものであり、さらにtJ、V
、W鋼は硬さがHv145〜156、また引張強さが4
5.6ス
〜51.9kg / 龍と高く、従来鋼であるI鋼と同
様に冷間鍛造性が劣るものである。As is clear from Table 2, Table 3, and Table 2, the conventional steel X steel is
Hardness in a better state is Ilv 1 (iQ, 0□2% proof stress is 32.5 kg/w, tensile strength is 55.6 kg/mm
Furthermore, the cold forgeability is poor at 73.1%, and the comparative steel X steel has a reduction of area of 78.1%.
% and poor cold forgeability, and furthermore, tJ, V
, W steel has a hardness of Hv145-156 and a tensile strength of 4
The weight is as high as 5.6 to 51.9 kg/dragon, and the cold forgeability is poor like the conventional steel I steel.
これらに対して、本発明鋼であるA−5鋼は焼なまし状
態での硬さが1)■1)1〜139.0.2%耐力が2
1.5〜25.7b/n+s引張強さが39.3〜46
.5kg/宵曹と低く、また絞り値が79.8〜85.
1%と高く冷間鍛造性が優れたものである。In contrast, A-5 steel, which is the steel of the present invention, has a hardness of 1) ■ 1) 1 to 139.0.2% proof stress in an annealed state of 2
1.5-25.7 b/n+s tensile strength 39.3-46
.. It's as low as 5kg/Yoiso, and the aperture value is 79.8-85.
It has a high cold forgeability of 1%.
また、第3表から明らかなように、焼入、焼もどし状態
での従来鋼であるX鋼の腐食速度は65.3g / m
h、 rと速く、耐食性については満足し得るもので
なかった。また比較鋼であるT、U、■鋼についても腐
食速度が29.5〜42.0g/mhrと速く、耐食性
については低いものであり、さらにW鋼の腐食速度は6
0.5g / m h rと従来鋼と同様に速く、耐食
性については劣るものである。Furthermore, as is clear from Table 3, the corrosion rate of conventional steel X steel in the quenched and tempered state is 65.3 g/m.
h and r, and the corrosion resistance was not satisfactory. In addition, the comparison steels T, U, and ■ steels also have a fast corrosion rate of 29.5 to 42.0 g/mhr, and their corrosion resistance is low, and the corrosion rate of W steel is 6
It is as fast as conventional steel at 0.5 g/m hr, but its corrosion resistance is inferior.
これらに対して、本発明鋼であるA ”−3鋼は硬さが
llv 205〜232と高く、また0、2%耐力は4
5.1〜56.1kg / m m 、引張強ざが66
、1” 74.9kg l rn mと高く、強度につ
いては優れたものであり、また腐食速度については12
.0〜22.0g / m h rと少なく、耐食性に
ついても優れたものである。In contrast, the A''-3 steel, which is the steel of the present invention, has a high hardness of LLV 205 to 232, and a 0 and 2% yield strength of 4.
5.1~56.1kg/mm, tensile strength 66
, 1” 74.9 kg lrn m, excellent strength, and corrosion rate of 12
.. It has a low corrosion resistance of 0 to 22.0 g/mhr and has excellent corrosion resistance.
(本発明の効果)
本発明は、上述のように焼なまし状態での引張強さが4
7kg / m m以下と低く、冷間鍛造性については
優れたものであり、また焼入、焼もどし状態での引張強
さが(iQkg / m m以上と高く、強度について
も優れたものであり、さらに耐食性についても優れたも
のであり、本発明鋼は船舶用スチームタービン、ブレー
ド材、ネジ、ボルトなどに好Jなマルテンサイト系ステ
ンレス鋼である。(Effects of the present invention) As mentioned above, the present invention has a tensile strength of 4 in the annealed state.
It has a low strength of less than 7 kg/mm, and has excellent cold forgeability. It also has a high tensile strength (iQ kg/mm or more) in the quenched and tempered state, and has excellent strength. Furthermore, it has excellent corrosion resistance, and the steel of the present invention is a martensitic stainless steel suitable for use in steam turbines for ships, blade materials, screws, bolts, etc.
第1図はclと焼なまし状態での引張強さとの関係を示
した線図で、第2図はcHと焼入、焼もどし状態での腐
食速度との関係を示した線図で、第3図はCr当量と相
変態量との関係を示した線図′乙第4図はC量と焼入、
焼もどし状態での引張強さとの関係を示した線図で、第
5図はCr当量と1)00℃での絞り値との関係を示し
た線図である。Figure 1 is a diagram showing the relationship between Cl and tensile strength in the annealed state, and Figure 2 is a diagram showing the relationship between cH and corrosion rate in the quenched and tempered states. Figure 3 is a diagram showing the relationship between the Cr equivalent and the amount of phase transformation.
This is a diagram showing the relationship between tensile strength in a tempered state, and FIG. 5 is a diagram showing the relationship between Cr equivalent and 1) reduction of area value at 00°C.
Claims (3)
以下、Mn0.10〜1.0%、Cr10.0〜13.
0%、N0.02%以下を含有し、残部Feならびに不
純物元素からなり、かつCr当量が9.0〜10.5で
あることを特徴とする冷間鍛造用マルテンサイト系ステ
ンレス鋼。(1) C 0.07% or less, Si 0.40% by weight
Below, Mn0.10-1.0%, Cr10.0-13.
A martensitic stainless steel for cold forging, characterized in that it contains 0.0% and 0.02% or less of N, the balance is Fe and impurity elements, and has a Cr equivalent of 9.0 to 10.5.
以下、Mn0.10〜1.0%、Cr10.0〜13.
0%、N0.02%以下を含有し、さらにS0.003
%以下、O0.0040%以下であり、残部Feならび
に不純物元素からなり、かつCr当量が9.0〜10.
5であることを特徴とする冷間鍛造用マルテンサイト系
ステンレス鋼。(2) C0.07% or less, Si 0.40% by weight
Below, Mn0.10-1.0%, Cr10.0-13.
0%, N0.02% or less, and S0.003
% or less, O0.0040% or less, the balance consists of Fe and impurity elements, and the Cr equivalent is 9.0 to 10.
A martensitic stainless steel for cold forging characterized by a temperature of 5.
以下、Mn0.10〜1.0%、Cr10.0〜13.
0%、N0.02%以下を含有し、さらにNi0.50
%以下、Cu0.50%以下、Mo1.5%以下、Ti
0.2%以下、V0.15%以下、Nb0.10%以下
のうち1種ないし2種以上を含有し、残部Feならびに
不純物元素からなり、かつCr当量が9.0〜10.5
であることを特徴とする冷間鍛造用マルテンサイト系ス
テンレス鋼。(3) C 0.07% or less, Si 0.40% by weight
Below, Mn0.10-1.0%, Cr10.0-13.
0%, N0.02% or less, and further Ni0.50
% or less, Cu 0.50% or less, Mo 1.5% or less, Ti
Contains one or more of 0.2% or less, V 0.15% or less, and Nb 0.10% or less, with the balance consisting of Fe and impurity elements, and has a Cr equivalent of 9.0 to 10.5.
Martensitic stainless steel for cold forging, characterized by:
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP61079884A JPH0617544B2 (en) | 1986-04-07 | 1986-04-07 | Martensitic stainless steel for cold forging |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP61079884A JPH0617544B2 (en) | 1986-04-07 | 1986-04-07 | Martensitic stainless steel for cold forging |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS62238351A true JPS62238351A (en) | 1987-10-19 |
JPH0617544B2 JPH0617544B2 (en) | 1994-03-09 |
Family
ID=13702681
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP61079884A Expired - Lifetime JPH0617544B2 (en) | 1986-04-07 | 1986-04-07 | Martensitic stainless steel for cold forging |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH0617544B2 (en) |
Families Citing this family (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP3004495U (en) * | 1994-05-23 | 1994-11-15 | メーコー工業株式会社 | Chair |
Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5113463A (en) * | 1974-07-24 | 1976-02-02 | Sharp Kk | Shitsukikokantaino seizohoho |
JPS58174554A (en) * | 1982-04-07 | 1983-10-13 | Nippon Steel Corp | Stainless steel excellent in ductility and corrosion resistance at weld zone |
-
1986
- 1986-04-07 JP JP61079884A patent/JPH0617544B2/en not_active Expired - Lifetime
Patent Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5113463A (en) * | 1974-07-24 | 1976-02-02 | Sharp Kk | Shitsukikokantaino seizohoho |
JPS58174554A (en) * | 1982-04-07 | 1983-10-13 | Nippon Steel Corp | Stainless steel excellent in ductility and corrosion resistance at weld zone |
Also Published As
Publication number | Publication date |
---|---|
JPH0617544B2 (en) | 1994-03-09 |
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