JPH02258956A - Highly corrosion resistant duplex phase stainless steel excellent in hot workability - Google Patents
Highly corrosion resistant duplex phase stainless steel excellent in hot workabilityInfo
- Publication number
- JPH02258956A JPH02258956A JP7748489A JP7748489A JPH02258956A JP H02258956 A JPH02258956 A JP H02258956A JP 7748489 A JP7748489 A JP 7748489A JP 7748489 A JP7748489 A JP 7748489A JP H02258956 A JPH02258956 A JP H02258956A
- Authority
- JP
- Japan
- Prior art keywords
- stainless steel
- hot workability
- steel
- corrosion resistance
- phase
- 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
- 230000007797 corrosion Effects 0.000 title claims abstract description 49
- 238000005260 corrosion Methods 0.000 title claims abstract description 49
- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract 5
- 239000010935 stainless steel Substances 0.000 title claims abstract 5
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 9
- 229910052760 oxygen Inorganic materials 0.000 claims abstract description 7
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 6
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 6
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 6
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 5
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 5
- 229910052759 nickel Inorganic materials 0.000 claims abstract 4
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract 4
- 229910052710 silicon Inorganic materials 0.000 claims abstract 4
- 229910000831 Steel Inorganic materials 0.000 claims description 36
- 239000010959 steel Substances 0.000 claims description 36
- 229910001039 duplex stainless steel Inorganic materials 0.000 claims description 27
- 229910052721 tungsten Inorganic materials 0.000 claims description 3
- 229910052758 niobium Inorganic materials 0.000 claims description 2
- 238000000034 method Methods 0.000 abstract description 7
- 239000000203 mixture Substances 0.000 abstract description 6
- 239000003129 oil well Substances 0.000 abstract description 4
- 229910052799 carbon Inorganic materials 0.000 abstract 2
- 230000001105 regulatory effect Effects 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 34
- 238000012545 processing Methods 0.000 description 6
- 230000007423 decrease Effects 0.000 description 5
- UIIMBOGNXHQVGW-UHFFFAOYSA-M Sodium bicarbonate Chemical compound [Na+].OC([O-])=O UIIMBOGNXHQVGW-UHFFFAOYSA-M 0.000 description 4
- 230000002411 adverse Effects 0.000 description 3
- 238000001816 cooling Methods 0.000 description 3
- 238000005336 cracking Methods 0.000 description 3
- 238000005242 forging Methods 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 229910052802 copper Inorganic materials 0.000 description 2
- 239000012535 impurity Substances 0.000 description 2
- 239000004615 ingredient Substances 0.000 description 2
- 238000012423 maintenance Methods 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 230000007246 mechanism Effects 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 229910000030 sodium bicarbonate Inorganic materials 0.000 description 2
- 235000017557 sodium bicarbonate Nutrition 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- VEXZGXHMUGYJMC-UHFFFAOYSA-M Chloride anion Chemical compound [Cl-] VEXZGXHMUGYJMC-UHFFFAOYSA-M 0.000 description 1
- 241000316887 Saissetia oleae Species 0.000 description 1
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 150000001805 chlorine compounds Chemical class 0.000 description 1
- 238000004140 cleaning Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 230000001276 controlling effect Effects 0.000 description 1
- 230000000875 corresponding effect Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 229910052761 rare earth metal Inorganic materials 0.000 description 1
- 239000013535 sea water Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
Abstract
Description
【発明の詳細な説明】
〈産業上の利用分野〉
この発明は、油井用ラインパイプや化学工業用配管類の
高耐食性素材として好適で、かつ熱間加工時(例えば鋼
板や鋼管の製造時)の疵発生が極めて少ない熱間加工性
に優れた高耐食二相ステンレス鋼に関するものである。[Detailed Description of the Invention] <Industrial Application Field> The present invention is suitable as a highly corrosion-resistant material for oil well line pipes and chemical industry piping, and is suitable for use during hot processing (for example, when manufacturing steel plates and steel pipes). The present invention relates to a highly corrosion-resistant duplex stainless steel with excellent hot workability and extremely low occurrence of defects.
〈従来技術とその課題〉
Crを多量に含有する二相ステンレス鋼は、塩化物るよ
る孔食、隙間腐食並びに応力腐食等に対して強い抵抗性
を備えているため、海水を用いる熱交換器を始め、化学
製造機器や油井用配管材料等として広い用途を誇ってし
−るが、一方で二相ステンレス鋼には高温変形能が一般
に劣ると言う欠点も指摘されていた。つまり、二相ステ
ンレス鋼は熱間加工性が低く、熱間加工後の冷却過程で
“シグマ脆化”、“475℃脆化”と呼ばれる脆化機構
により鋼片の表面割れを誘起し易い材料であった。<Prior art and its problems> Duplex stainless steel containing a large amount of Cr has strong resistance to pitting corrosion, crevice corrosion, stress corrosion, etc. caused by chlorides, so it cannot be used in heat exchangers using seawater. Although it boasts a wide range of uses including chemical manufacturing equipment and oil well piping materials, it has been pointed out that duplex stainless steel also has the drawback of generally being inferior in high-temperature deformability. In other words, duplex stainless steel has low hot workability, and is a material that easily induces surface cracking of steel pieces due to embrittlement mechanisms called "sigma embrittlement" and "475°C embrittlement" during the cooling process after hot working. Met.
そこで、従来、この二相ステンレス鋼の高温変形能を改
善すべく次に示すような手段が提案され、相応の効果が
得られるとの報告がなされている。Therefore, the following measures have been proposed to improve the high-temperature deformability of this duplex stainless steel, and it has been reported that a corresponding effect can be obtained.
^) γ相の比率を15〜55%に規制して十分に多い
α相を確保できるように成分設計すると共に、鋼塊成分
をバランスさせることによって高温でのγ相とα相との
強度を近付け、かつBの添加により結晶粒界を強化する
方法(特公昭59−14099号公報)。^) In addition to controlling the ratio of γ phase to 15 to 55% and designing the composition to ensure a sufficient amount of α phase, we also balanced the steel ingot components to increase the strength of γ phase and α phase at high temperatures. A method of strengthening grain boundaries by increasing the grain boundaries and adding B (Japanese Patent Publication No. 59-14099).
B) 鋼中のS及びOを低減すると共に、必要に応じて
希土類元素を添加して鋼溶製時の脱O及び脱Sを強化す
る方法(特公昭57−15660号公報)。B) A method of reducing S and O in steel and, if necessary, adding rare earth elements to enhance O and S removal during steel melting (Japanese Patent Publication No. 15660/1983).
C) AβとCaとを複合添加して介在物の形態を変
える方法(特公昭54−24364号公報)。C) A method of changing the form of inclusions by adding Aβ and Ca in combination (Japanese Patent Publication No. 54-24364).
ところで、二相ステンレス鋼は、多くの場合、耐食性を
高めるためにMoやNが添加されるが、耐隙間腐食性を
より高める目的で上記元素に加えてV、W、Cu等が添
加されることがある。しかしながら、これらの元素は耐
食性向上のためには非常に有効であるが、−面で熱間加
工性を著しく阻害するものでもあり、中でも■は靭性を
著しく劣化することが知られている。By the way, in duplex stainless steel, Mo and N are often added to improve corrosion resistance, but V, W, Cu, etc. are added in addition to the above elements for the purpose of further increasing crevice corrosion resistance. Sometimes. However, although these elements are very effective for improving corrosion resistance, they also significantly impede hot workability on the - side, and it is known that - in particular, significantly deteriorates toughness.
従って、前述した如くただでさえ熱間加工性が低くて鋼
片表面割れを誘起し易い二相ステンレス鋼に、耐隙間腐
食性に著効があるとは言えV等を多量に含有した場合に
は、その脆化が更に助長されることとなり、高温変形能
改善のための前記各方法をそのまま適用したとしても鋼
片の表面割れを防止するのが困難で、著しい鋼片手入れ
歩留の低下を余儀無くされる結果となっていた。Therefore, as mentioned above, when duplex stainless steel, which has low hot workability and is prone to cracking the surface of steel pieces, contains a large amount of V, etc., although it has a significant effect on crevice corrosion resistance. The embrittlement will be further promoted, and even if the above-mentioned methods for improving high-temperature deformability are applied as they are, it will be difficult to prevent surface cracking of the steel billet, and the steel billet yield will be significantly reduced. As a result, he was forced to do so.
そのため、■等を多量に含有させて耐隙間腐食性を一段
と改善した実用的な二相ステンレス鋼は未だ存在しない
と言うのが現状であった。Therefore, the current situation is that there is still no practical duplex stainless steel in which the crevice corrosion resistance is further improved by containing a large amount of (2) or the like.
このようなことから、本発明の目的、■を始めとする耐
食性改善成分を添加してより優れた耐食性能を付与し、
なおかつ優れた熱間加工性をも備えた二相ステンレス鋼
の提供に置かれた。For this reason, the purpose of the present invention is to add corrosion resistance improving ingredients such as (1) to impart better corrosion resistance performance,
The aim was to provide a duplex stainless steel that also had excellent hot workability.
く課題を解決するための手段〉
そこで、本発明者等は上記目的を達成すべく、まず、
a)一般に二相ステンレス鋼の熱間加工性はγ相が少な
いほど向上することが知られているが、γ相を少なくす
ると逆に靭性が劣化するようになる。Means for Solving the Problems> Therefore, in order to achieve the above object, the present inventors first conducted the following steps: a) It is generally known that the hot workability of duplex stainless steel improves as the amount of the γ phase decreases. However, if the γ phase is reduced, the toughness will deteriorate.
b)一方、シグマ相はγ相が多くなると析出が促進され
る。b) On the other hand, the precipitation of the sigma phase is promoted when the γ phase increases.
C)シグマ脆化等に起因する鋼片表面割れの多くは熱間
加工割れを起点とし、鋼片冷却時又は手入れ時に発生す
る応力によって助長されている。C) Many of the surface cracks of steel slabs caused by sigma embrittlement etc. originate from hot working cracks and are promoted by stress generated during cooling or maintenance of the steel slab.
との事実に着目し、真空溶解により得た”V等を含有量
する二相ステンレス鋼”の種々の鋼塊について熱間鍛造
・空冷の実験を数多く繰り返しながら研究を重ねた結果
、[V等の耐食性改善元素を含有する二相ステンレス鋼
では、鋼中のS及びO量を著しく低い領域にまで低減す
ると共にCa及びBを複合添加し、かつ熱間加工の低温
域(1000〜800℃)でのγ相の割合が30〜70
%と中程度になるように成分組成設定を行った場合には
、その熱間加工性が顕著に向上して鋼片の手入れ歩留を
95%以上にまで改善でき、従って上記方法によれば■
成分等の添加により耐食性が高められ、しかも優れた熱
間加工性をも備えた二相ステンレス鋼の実現が可能であ
る」との知見を得るに至ったのである。Focusing on the fact that the In duplex stainless steel containing elements that improve corrosion resistance, the amounts of S and O in the steel are reduced to extremely low levels, combined addition of Ca and B, and the low temperature range of hot working (1000 to 800°C) is achieved. The ratio of γ phase is 30 to 70
If the composition is set to be at a medium level of %, the hot workability will be significantly improved and the processing yield of the steel billet can be improved to over 95%. Therefore, according to the above method, ■
They came to the conclusion that it is possible to create a duplex stainless steel that has improved corrosion resistance and excellent hot workability by adding other ingredients.
この発明は、上記知見に基づいてなされたものであり、
「二相ステンレス鋼を、
C: 0.03%以下(以降、成分割合を表わす%は重
量%とする)。This invention was made based on the above knowledge, and it is based on the following: ``C: 0.03% or less of duplex stainless steel.
Si : 0.1〜1.0%、 Mn : 0.3
〜2.0%。Si: 0.1-1.0%, Mn: 0.3
~2.0%.
P : 0.035%以下、 S : 0.002
0%以下。P: 0.035% or less, S: 0.002
Less than 0%.
Ni : 4.0〜9.0%、 Cr : 20〜
28%。Ni: 4.0~9.0%, Cr: 20~
28%.
門o : 0.5〜5.0%、 V:0.1〜1.
0%。Gate o: 0.5-5.0%, V: 0.1-1.
0%.
sol、 Aj! : 0.005〜0.05%。Sol, Aj! : 0.005-0.05%.
Ca : 0.0010〜0.0100%。Ca: 0.0010-0.0100%.
B : 0.0005〜0.0100%、 N :
0.08〜0.2%。B: 0.0005-0.0100%, N:
0.08-0.2%.
0 : 0.006%以下
を含有するか、或いはこれに加えて更にC1l : 0
.1〜1.5%。0: Contains 0.006% or less, or in addition, C1l: 0
.. 1-1.5%.
W:0.1〜1.5%。W: 0.1-1.5%.
Nb : 0.05〜0.5%
のうちの1種以上をも含むと共に残部が実質的にFeよ
り成り、かつ鋳込状態でのT相割合が30〜70%であ
る成分組成に構成することにより、優れた耐食性をその
まま維持した上で優れた熱間加工性をも兼備せしめた点
」
を特徴としたものである。Contains at least one type of Nb: 0.05 to 0.5%, the remainder is substantially composed of Fe, and the composition has a composition in which the T phase ratio in the cast state is 30 to 70%. This makes it possible to maintain excellent corrosion resistance while also providing excellent hot workability.
ここで、二相ステンレス鋼の成分含有割合並びに鋳込状
態でのγ相の割合を前記の如(に限定した理由は次の通
りである。Here, the reason why the content ratio of the components of the duplex stainless steel and the ratio of the γ phase in the cast state are limited to the above-mentioned values is as follows.
く作用〉
(al C
C含有量が0.03%を超えると炭化物が粒界析出する
ようになり、耐食性及び靭性が劣化し易くなることから
、C含有量は0.03%以下と定めた。(Al C If the C content exceeds 0.03%, carbides will precipitate at grain boundaries, and corrosion resistance and toughness will tend to deteriorate. Therefore, the C content was set at 0.03% or less. .
(bl 5i
Siは鋼の脱酸のために不可欠な成分であり、十分な脱
酸効果を確保するには0.1%以上含有させる必要があ
るが、1.0%を超えて含有させると靭性の劣化を招く
ようになることから、Si含有量は0.1〜1.0%と
定めた。(bl 5i Si is an essential component for deoxidizing steel, and to ensure a sufficient deoxidizing effect, it must be contained at 0.1% or more, but if it is contained in excess of 1.0%, The Si content was set at 0.1 to 1.0% since this would lead to deterioration of toughness.
(e) Mn
Mn成分もSiと同様に脱酸作用を有しているが、その
含有量が0.3%未満では該作用による所望の効果が得
られない。一方、Mn含有量2.0%までは鋼に格別な
悪影響が及ぼされることがないため、?In含存含有量
、3〜2.0%と定めた。(e) Mn Although the Mn component also has a deoxidizing effect like Si, if its content is less than 0.3%, the desired effect due to this effect cannot be obtained. On the other hand, since Mn content up to 2.0% does not have any particular adverse effect on steel,? The In content was determined to be 3 to 2.0%.
(d) P
Pは鋼の熱間加工性並びに耐食性を劣化させる不純物元
素であるが、0.035%までは許容されることから、
P含有量は0.035%以下と定めた。(d) P P is an impurity element that deteriorates the hot workability and corrosion resistance of steel, but since it is allowed up to 0.035%,
The P content was set at 0.035% or less.
(el S、及びO
8及びOは、過剰に存在すると粒界に偏析して熱間加工
性を劣化すると共に、Ca、 AJ!等と結合して粗大
な介在物を生成し耐食性を劣化するため極力低減すべき
不純物元素である。しかし、S含有量を0.0020%
以下に、またC含有量を0.006%以下にそれぞれ抑
えることで所望の高い熱間加工性及び耐食性を得ること
ができることから、これらの含有量は各々前記の如くに
限定した。(el S and O 8 and O, if present in excess, segregate at grain boundaries and deteriorate hot workability, and also combine with Ca, AJ!, etc. to form coarse inclusions and deteriorate corrosion resistance. Therefore, it is an impurity element that should be reduced as much as possible.However, if the S content is reduced to 0.0020%
In addition, since the desired high hot workability and corrosion resistance can be obtained by suppressing the C content to 0.006% or less, these contents were each limited as described above.
ffl Ni
Ni成分は鋼の機械的性質、加工性及び一般耐食性を向
上させると共に、鋼の組織をオーステナイト−フェライ
トの二相Ni織とするために不可欠なものであるが、そ
の含有量が4.0%未満では上記効果が得られず、一方
、9.0%を超えて含有させてもコストに見合う特性改
善効果が得られないことから、Ni含有量は4.0〜9
.0%と定めた。ffl Ni Ni The Ni component is essential for improving the mechanical properties, workability, and general corrosion resistance of steel, and for making the steel structure into an austenite-ferrite two-phase Ni woven structure. If the Ni content is less than 0%, the above effects cannot be obtained, and on the other hand, if the Ni content exceeds 9.0%, the property improvement effect that is commensurate with the cost cannot be obtained.
.. It was set as 0%.
(gl Cr
Crは鋼の一般耐食性を向上させる重要な成分であり、
二相ステンレス鋼に求められる所望の耐食性を確保する
ためには20%以上を含有させることが必要である。一
方、28%を超えてCrを含有させると加工性に悪影響
が出るようになることから、Cr含有量は20〜28%
と定めた。(gl Cr Cr is an important component that improves the general corrosion resistance of steel,
In order to ensure the desired corrosion resistance required for duplex stainless steel, it is necessary to contain 20% or more. On the other hand, if Cr content exceeds 28%, workability will be adversely affected, so the Cr content should be 20 to 28%.
It was determined that
(h! M。(h! M.
Mo成分には鋼の局部耐食性を著しく向上させる作用が
あるので、耐食性合金ではCrと共に添加して耐食性の
更なる改善が図られるが、その含有量が0.5%未満で
あると前記作用による所望の効果が得られず、一方、5
.0%を超えて含有させるとコスト上昇に見合うだけの
効果が確保できないばかりか、加工性に悪い影響を及ぼ
すことが懸念されることから、Mo含有量は0.5〜5
.0%と定めた。Since the Mo component has the effect of significantly improving the local corrosion resistance of steel, it is added together with Cr in corrosion-resistant alloys to further improve the corrosion resistance, but if the Mo content is less than 0.5%, the above effect will occur. On the other hand, 5
.. If the Mo content exceeds 0%, not only will it not be possible to ensure an effect commensurate with the cost increase, but there is also concern that it will have a negative impact on workability, so the Mo content should be 0.5 to 5%.
.. It was set as 0%.
(1) V
■成分にはCr、Mo等と適量共存させることにより塩
化物溶液等に対する綱の耐食性、隙間腐食性を向上させ
る作用があるが、その含有量が0.1%未満では前記作
用による所望の効果が得られず、一方、1.0%を超え
て含有させると熱間加工性及び靭性が著しく劣化するよ
うになることから、■含有量は0.1〜1.0%と定め
た。(1) Component V (2) has the effect of improving the corrosion resistance and crevice corrosion resistance of steel against chloride solutions etc. by coexisting with Cr, Mo, etc. in appropriate amounts, but if its content is less than 0.1%, the above effect will be reduced. On the other hand, if the content exceeds 1.0%, the hot workability and toughness will be significantly deteriorated. Established.
(Jl sol、AR
Afは脱酸成分として不可欠なものであり、十分な脱酸
効果を確保するためにはsot、AIで0.005%以
上含有させる必要があるが、0.05%を超えて含有さ
せるとAINとして析出し耐食性を劣化すると共に靭性
低下をも招くようになることから、AI含有量はsol
、AIで0.005〜0.05%と定めた。(Jl sol and AR Af are indispensable as deoxidizing components, and in order to ensure sufficient deoxidizing effects, it is necessary to contain them at 0.005% or more in sot and AI; If it is contained in sol, it will precipitate as AIN, which will deteriorate the corrosion resistance and also cause a decrease in toughness.
, set at 0.005 to 0.05% by AI.
(kl Ca
Ca成分には鋼中のSを硫化物として固定して熱間加工
性を改善する作用があるが、その含有量が0.0010
%未満では前記作用による所望の効果が得られず、一方
、0.0100%を超えて含有量させると、逆に熱間加
工性を害するばかりか耐食性をも劣化するようになるた
め、Ca含有量はo、ooio 〜o、oto。(kl Ca The Ca component has the effect of fixing S in steel as sulfide and improving hot workability, but when its content is 0.0010
If the content is less than 0.0100%, the desired effect cannot be obtained by the above action, while if the content exceeds 0.0100%, it not only impairs hot workability but also deteriorates corrosion resistance. The amount is o, ooio ~ o, oto.
%と定めた。%.
(1) B
B成分は鋼の熱間加工性を改善する作用を有するが、そ
の機構はCa添加の場合とは異なるので、Caと共存さ
せることによって広い温度域の熱間加工性を達成するこ
とができる。ただ、Bの含有■が0.0005%未満で
あると熱間加工性改善効果が十分でなく、一方、0.0
100%を超えて含有させると溶融脆化を促進して逆に
熱間加工性を害するようになることから、B含有量はo
、ooos〜0.0100%と定めた。(1) B The B component has the effect of improving the hot workability of steel, but the mechanism is different from that in the case of Ca addition, so by coexisting with Ca, hot workability in a wide temperature range is achieved. be able to. However, if the B content (■) is less than 0.0005%, the effect of improving hot workability is insufficient;
B content exceeding 100% promotes melt embrittlement and impairs hot workability;
,ooos~0.0100%.
(mlN
N成分には母材のみならず溶接部の耐孔食性及び耐隙間
腐食性を向上させる作用があるが、その含有量が0.0
8%未満では上記作用に所望の効果が得られず、一方、
0.30%を超えて含有させると窒化物が析出し易くな
って耐食性及び靭性に悪影響を及ぼすことから、N含有
量は0.08〜0.30%と定めた。(mlN The N component has the effect of improving the pitting corrosion resistance and crevice corrosion resistance not only of the base metal but also of the welded part, but when its content is 0.0
If it is less than 8%, the desired effect cannot be obtained in the above action;
If the N content exceeds 0.30%, nitrides tend to precipitate and have an adverse effect on corrosion resistance and toughness, so the N content was set at 0.08 to 0.30%.
(o) Cu、 W、及びNb
これらの成分は何れも二相ステンレス鋼の耐食性を更に
改善する効果を有するので、必要により1種又は2種以
上含有せしめられるが、それぞれの成分の含有量は次の
理由によって定められた。(o) Cu, W, and Nb Each of these components has the effect of further improving the corrosion resistance of duplex stainless steel, so one or more of these components may be included if necessary, but the content of each component is It was established for the following reasons.
イ) Cu
Cu成分には二相ステンレス鋼の耐孔食性、耐隙間腐食
性及び一般耐食性を向上する作用があるが、その含有量
が0.1%未満では上記作用による所望の効果が得られ
ず、一方、1.5%を超えて含有させると高温変形能を
害するばかりかε−phaseを析出して逆に耐食性を
劣化するようになることから、Cuを含有させる場合に
はその含有量は0.1〜1.5%と定めた。b) Cu Cu component has the effect of improving the pitting corrosion resistance, crevice corrosion resistance, and general corrosion resistance of duplex stainless steel, but if its content is less than 0.1%, the desired effects due to the above effects cannot be obtained. On the other hand, if Cu is contained in an amount exceeding 1.5%, it not only impairs high-temperature deformability but also precipitates ε-phase and deteriorates corrosion resistance. was set at 0.1 to 1.5%.
口)W
W成分には二相ステンレス鋼の耐局部腐食性を向上する
作用があるが、その含有量が0.1%未満では前記作用
による所望の効果が得られず、一方、1,5%を超えて
含有量させても更なる耐食性向上効果を得ることが困難
であることから、Wを含有させる場合にはその含有量は
0.1〜1.5%と定めた。Mouth) W The W component has the effect of improving the local corrosion resistance of duplex stainless steel, but if its content is less than 0.1%, the desired effect due to the above effect cannot be obtained; Since it is difficult to obtain a further corrosion resistance improvement effect even if the content exceeds W, the content is set at 0.1 to 1.5% when W is included.
ハ)Nb
Nb成分には、■と同様に二相ステンレス鋼の耐局部腐
食性を向上する作用があるが、その含有量が0.05%
未満では上記作用による所望の効果が得られず、一方、
0.5%を超えて含有させてもコスト上昇に見合うだけ
の効果が気体できないことから、Nb含有量は0.05
〜0,5%と定めた。C) Nb The Nb component has the effect of improving the local corrosion resistance of duplex stainless steel as in (3), but its content is 0.05%.
If it is less than that, the desired effect due to the above action cannot be obtained; on the other hand,
Even if the Nb content exceeds 0.5%, the gas cannot have an effect commensurate with the cost increase, so the Nb content is 0.05%.
It was set at ~0.5%.
(p) 鋳込み状態でのγ相の割合
通常の二相ステンレス鋼においてはγ相の比率は110
0℃以上で著しく減少するが、熱間加工の低温域(10
00〜800℃)では大きな変動はなく、鋳込状態での
γ相の割合によって代表させることができる。そして、
この鋳込状態でのγ相の割合が30%を下回った場合に
は靭性が劣化して熱間加工後の鋼片の手入れ時にヒート
クランクが発生し易くなり(後述する実施例を参照され
たい)、鋼片の手入れ歩留が低下する。一方、鋳込状態
でのγ相の割合が70%を超えると熱間加工性が著しく
低下すると共に、シグマ相に起因する割れが生じ易くな
り、やはり鋼片の手入れ歩留が低下する。(p) Ratio of γ phase in the cast state In normal duplex stainless steel, the ratio of γ phase is 110.
It decreases significantly above 0℃, but in the low temperature range of hot working (10
00 to 800°C), there is no large variation, and it can be represented by the ratio of γ phase in the cast state. and,
If the ratio of the γ phase in the cast state is less than 30%, the toughness will deteriorate and heat crank will easily occur when cleaning the billet after hot working (see Examples below). ), the processing yield of steel billets decreases. On the other hand, if the ratio of the γ phase in the cast state exceeds 70%, hot workability is significantly reduced, and cracks due to the sigma phase are likely to occur, resulting in a decrease in the processing yield of the steel billet.
従って、本発明に係る二相ステンレス鋼では、鋳込状態
でのγ相の割合を30〜70%と限定した。Therefore, in the duplex stainless steel according to the present invention, the proportion of the γ phase in the cast state is limited to 30 to 70%.
なお、上記γ相の割合は、本発明の規定範囲内で各成分
の含有割合を調整して達成することができる。Note that the above ratio of the γ phase can be achieved by adjusting the content ratio of each component within the specified range of the present invention.
続いて、この発明を実施例により、比較例と対比しなが
ら更に具体的に説明する。Next, the present invention will be described in more detail using Examples and in comparison with Comparative Examples.
〈実施例〉
まず、真空溶解炉で第1表に示す如き成分組成の各二相
ステンレス鋼を溶製し、25kg丸鋼塊に鋳込んだ。<Example> First, each duplex stainless steel having the composition shown in Table 1 was melted in a vacuum melting furnace and cast into a 25 kg round steel ingot.
次いで、これら丸綱塊の表面に存在する黒皮を研削によ
って除去し、鋼塊のボトム面については更に研磨仕上げ
を行ってからフェライトメータによりフェライト相率(
α%)を測定した。そして、「γ%=100−α%」に
よりγ相率(1%)を求めた。Next, the black scale existing on the surface of these round steel ingots is removed by grinding, and the bottom surface of the steel ingot is further polished and finished, and then the ferrite phase ratio (
α%) was measured. Then, the γ phase ratio (1%) was determined by “γ%=100−α%”.
次に、研削した上記鋼塊を1250℃の炉で2時間加熱
した後に炉出しして鍛造を開始し、鋼片の表面温度が9
00℃を下回った時点で再炉入れすると言う、都合2回
の加熱・鍛造操作によって6011厚×100重曹幅X
40Ora長の鋼片とし、そのまま空冷して重量を測定
した。そして、上記鍛造によって鋼片表面に発生した疵
を研削によって除去した後の重量も測定し、この“疵除
去後の重量″の“鍛造後の無手入れ鋼片重量”に対する
割合を算出して「鋼片手入れ歩留」とした。Next, the ground steel ingot was heated in a furnace at 1250°C for 2 hours and then taken out of the furnace to start forging.
6011 thickness x 100 baking soda width x 6011 thickness x 100 baking soda width x
A steel piece with a length of 40 ora was made, and the weight was measured after cooling in the air. Then, the weight after the scratches generated on the surface of the steel billet due to the forging were removed by grinding was also measured, and the ratio of this "weight after scratch removal" to the "weight of the billet without maintenance after forging" was calculated. "Steel yield rate".
上記“鋼片手入れ歩留の算出結果”を“γ相率(1%)
の測定結果”と共に第1表に併せて示す。The above “calculation result of steel single-handed processing yield” is calculated as “γ phase ratio (1%)”
The measurement results are also shown in Table 1.
第1表に示される結果からも明らかなように、本発明に
係る二相ステンレス鋼では鋼片手入れ歩留:95%以上
と言う高い値を示し、従来鋼に比べて熱間加工性に優れ
ていることが分かる。As is clear from the results shown in Table 1, the duplex stainless steel according to the present invention shows a high value of 95% or more in steel single-hand processing yield, and has excellent hot workability compared to conventional steel. I can see that
なお、本発明に係る二相ステンレス鋼は、腐食試験によ
って十分に優れた耐食性を有していることも確認された
。In addition, it was also confirmed by a corrosion test that the duplex stainless steel according to the present invention has sufficiently excellent corrosion resistance.
く効果の総括〉
以上に説明した如く、この発明によれば、V添加によっ
て著しく高い耐食性を示し、しかも優れた熱間加工性を
有する二相ステンレス鋼を提供することが可能となり、
化学工業用配管や油井用ラインパイプ等の性能向上やコ
スト低減に大きく寄与することが期待できるなど、産業
上極めて有用な効果がもたらされる。Summary of Effects> As explained above, according to the present invention, it is possible to provide a duplex stainless steel that exhibits significantly high corrosion resistance by adding V and has excellent hot workability.
It is expected to greatly contribute to improving the performance and reducing costs of chemical industry piping, oil well line pipes, etc., and will bring extremely useful effects industrially.
Claims (2)
0.3〜2.0%、P:0.035%以下、S:0.0
020%以下、Ni:4.0〜9.0%、Cr:20〜
28%、Mo:0.5〜5.0%。 V:0.1〜1.0%、sol.Al:0.005〜0
.05%、Ca:0.0010〜0.0100%、 B:0.0005〜0.0100%、N:0.08〜0
.3%、O:0.006%以下 を含むと共に残部が実質的にFeより成り、かつ鋳込状
態でのγ相割合が30〜70%である熱間加工性に優れ
た高耐食二相ステンレス鋼。(1) C: 0.03% or less, Si: 0.1-1.0%, Mn:
0.3-2.0%, P: 0.035% or less, S: 0.0
020% or less, Ni: 4.0 to 9.0%, Cr: 20 to
28%, Mo: 0.5-5.0%. V: 0.1-1.0%, sol. Al: 0.005~0
.. 05%, Ca: 0.0010-0.0100%, B: 0.0005-0.0100%, N: 0.08-0
.. 3%, O: 0.006% or less, the balance is substantially made of Fe, and the γ phase ratio in the cast state is 30 to 70%. Highly corrosion-resistant duplex stainless steel with excellent hot workability. steel.
0.3〜2.0%、P:0.035%以下、S:0.0
020%以下、Ni:4.0〜9.0%、Cr:20〜
28%、Mo:0.5〜5.0%、V:0.1〜1.0
%、sol.Al:0.005〜0.05%、Ca:0
.0010〜0.0100%、 B:0.0005〜0.0100%、N:0.08〜0
.3%、O:0.006%以下 を含有し、更に Cu:0.1〜1.5%、 W:0.1〜1.5%、 Nb:0.05〜0.5% のうちの1種以上をも含むと共に残部が実質的にFeよ
り成り、かつ鋳込状態でのγ相割合が30〜70%であ
る熱間加工性に優れた高耐食二相ステンレス鋼。(2) C: 0.03% or less, Si: 0.1 to 1.0%, Mn:
0.3-2.0%, P: 0.035% or less, S: 0.0
020% or less, Ni: 4.0 to 9.0%, Cr: 20 to
28%, Mo: 0.5-5.0%, V: 0.1-1.0
%, sol. Al: 0.005-0.05%, Ca: 0
.. 0010-0.0100%, B: 0.0005-0.0100%, N: 0.08-0
.. 3%, O: 0.006% or less, and further contains Cu: 0.1 to 1.5%, W: 0.1 to 1.5%, and Nb: 0.05 to 0.5%. A highly corrosion-resistant duplex stainless steel having excellent hot workability, containing at least one type of stainless steel, the remainder being substantially composed of Fe, and having a γ phase ratio of 30 to 70% in a cast state.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP1077484A JPH0717987B2 (en) | 1989-03-29 | 1989-03-29 | Highly corrosion resistant duplex stainless steel with excellent hot workability |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP1077484A JPH0717987B2 (en) | 1989-03-29 | 1989-03-29 | Highly corrosion resistant duplex stainless steel with excellent hot workability |
Publications (2)
Publication Number | Publication Date |
---|---|
JPH02258956A true JPH02258956A (en) | 1990-10-19 |
JPH0717987B2 JPH0717987B2 (en) | 1995-03-01 |
Family
ID=13635258
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP1077484A Expired - Lifetime JPH0717987B2 (en) | 1989-03-29 | 1989-03-29 | Highly corrosion resistant duplex stainless steel with excellent hot workability |
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Country | Link |
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JP (1) | JPH0717987B2 (en) |
Cited By (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH05132741A (en) * | 1991-11-11 | 1993-05-28 | Sumitomo Metal Ind Ltd | High strength duplex stainless steel excellent in corrosion resistance |
JPH0681037A (en) * | 1992-08-31 | 1994-03-22 | Sumitomo Metal Ind Ltd | Production of hot rolled strip of dual phase stainless steel |
WO1996018751A1 (en) * | 1994-12-16 | 1996-06-20 | Sumitomo Metal Industries, Ltd. | Duplex stainless steel excellent in corrosion resistance |
EP0818552A2 (en) * | 1996-07-13 | 1998-01-14 | Schmidt + Clemens GmbH + Co. | Ferritic-austenitic stainless steel casting alloy |
EP1995341A1 (en) * | 2007-03-26 | 2008-11-26 | Sumitomo Metal Industries Limited | Oil well pipe for expansion in well and two-phase stainless steel for use as oil well pipe for expansion |
JP2014074209A (en) * | 2012-10-05 | 2014-04-24 | Kobe Steel Ltd | Duplex stainless steel material and duplex stainless steel pipe |
JP2014532811A (en) * | 2011-11-04 | 2014-12-08 | オウトクンプ オサケイティオ ユルキネンOutokumpu Oyj | Duplex stainless steel |
JP2016003377A (en) * | 2014-06-18 | 2016-01-12 | 新日鐵住金株式会社 | Two-phase stainless steel tube |
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JPS56142855A (en) * | 1980-04-04 | 1981-11-07 | Nippon Yakin Kogyo Co Ltd | Two-phase stainless steel excellent in hot processability and local corrosion resistance |
JPS5715660A (en) * | 1980-06-25 | 1982-01-27 | Nitto Kohki Co Ltd | Special grinder device |
JPS59218295A (en) * | 1983-05-24 | 1984-12-08 | Sumitomo Metal Ind Ltd | Filler metal for welding two-phase stainless steel |
JPS60262946A (en) * | 1984-06-11 | 1985-12-26 | Kawasaki Steel Corp | Two-phase stainless steel with superior hot workability |
JPS612743A (en) * | 1984-06-15 | 1986-01-08 | Mitsubishi Rayon Co Ltd | Porous membrane |
JPS645101A (en) * | 1987-06-09 | 1989-01-10 | Thomson Csf | Tunable microwave filter equipped with dielectric resonator and application of the same |
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JPS56142855A (en) * | 1980-04-04 | 1981-11-07 | Nippon Yakin Kogyo Co Ltd | Two-phase stainless steel excellent in hot processability and local corrosion resistance |
JPS5715660A (en) * | 1980-06-25 | 1982-01-27 | Nitto Kohki Co Ltd | Special grinder device |
JPS59218295A (en) * | 1983-05-24 | 1984-12-08 | Sumitomo Metal Ind Ltd | Filler metal for welding two-phase stainless steel |
JPS60262946A (en) * | 1984-06-11 | 1985-12-26 | Kawasaki Steel Corp | Two-phase stainless steel with superior hot workability |
JPS612743A (en) * | 1984-06-15 | 1986-01-08 | Mitsubishi Rayon Co Ltd | Porous membrane |
JPS645101A (en) * | 1987-06-09 | 1989-01-10 | Thomson Csf | Tunable microwave filter equipped with dielectric resonator and application of the same |
Cited By (12)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH05132741A (en) * | 1991-11-11 | 1993-05-28 | Sumitomo Metal Ind Ltd | High strength duplex stainless steel excellent in corrosion resistance |
US5298093A (en) * | 1991-11-11 | 1994-03-29 | Sumitomo Metal Indusries, Ltd. | Duplex stainless steel having improved strength and corrosion resistance |
JPH0681037A (en) * | 1992-08-31 | 1994-03-22 | Sumitomo Metal Ind Ltd | Production of hot rolled strip of dual phase stainless steel |
WO1996018751A1 (en) * | 1994-12-16 | 1996-06-20 | Sumitomo Metal Industries, Ltd. | Duplex stainless steel excellent in corrosion resistance |
US5672215A (en) * | 1994-12-16 | 1997-09-30 | Sumitomo Metal Industries, Ltd. | Duplex stainless steel excellent in corrosion resistance |
EP0818552A2 (en) * | 1996-07-13 | 1998-01-14 | Schmidt + Clemens GmbH + Co. | Ferritic-austenitic stainless steel casting alloy |
EP0818552A3 (en) * | 1996-07-13 | 1998-03-25 | Schmidt + Clemens GmbH + Co. | Ferritic-austenitic stainless steel casting alloy |
EP1995341A1 (en) * | 2007-03-26 | 2008-11-26 | Sumitomo Metal Industries Limited | Oil well pipe for expansion in well and two-phase stainless steel for use as oil well pipe for expansion |
EP1995341A4 (en) * | 2007-03-26 | 2010-03-10 | Sumitomo Metal Ind | Oil well pipe for expansion in well and two-phase stainless steel for use as oil well pipe for expansion |
JP2014532811A (en) * | 2011-11-04 | 2014-12-08 | オウトクンプ オサケイティオ ユルキネンOutokumpu Oyj | Duplex stainless steel |
JP2014074209A (en) * | 2012-10-05 | 2014-04-24 | Kobe Steel Ltd | Duplex stainless steel material and duplex stainless steel pipe |
JP2016003377A (en) * | 2014-06-18 | 2016-01-12 | 新日鐵住金株式会社 | Two-phase stainless steel tube |
Also Published As
Publication number | Publication date |
---|---|
JPH0717987B2 (en) | 1995-03-01 |
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