JP6322145B2 - Duplex steel with improved notched impact strength and machinability - Google Patents
Duplex steel with improved notched impact strength and machinability Download PDFInfo
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- JP6322145B2 JP6322145B2 JP2014555177A JP2014555177A JP6322145B2 JP 6322145 B2 JP6322145 B2 JP 6322145B2 JP 2014555177 A JP2014555177 A JP 2014555177A JP 2014555177 A JP2014555177 A JP 2014555177A JP 6322145 B2 JP6322145 B2 JP 6322145B2
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- 229910000831 Steel Inorganic materials 0.000 title claims description 42
- 239000010959 steel Substances 0.000 title claims description 42
- 229910001039 duplex stainless steel Inorganic materials 0.000 claims description 39
- 239000011651 chromium Substances 0.000 claims description 22
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 20
- 229910001566 austenite Inorganic materials 0.000 claims description 19
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 18
- 229910000859 α-Fe Inorganic materials 0.000 claims description 15
- 239000000126 substance Substances 0.000 claims description 12
- 239000000203 mixture Substances 0.000 claims description 11
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 10
- 229910052804 chromium Inorganic materials 0.000 claims description 10
- 229910052757 nitrogen Inorganic materials 0.000 claims description 10
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 9
- 229910052799 carbon Inorganic materials 0.000 claims description 9
- 229910052742 iron Inorganic materials 0.000 claims description 9
- 239000012535 impurity Substances 0.000 claims description 7
- 229910052710 silicon Inorganic materials 0.000 claims description 7
- 239000010703 silicon Substances 0.000 claims description 7
- 229910000885 Dual-phase steel Inorganic materials 0.000 claims 4
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 39
- 230000007797 corrosion Effects 0.000 description 33
- 238000005260 corrosion Methods 0.000 description 33
- 229910045601 alloy Inorganic materials 0.000 description 32
- 239000000956 alloy Substances 0.000 description 32
- 239000011572 manganese Substances 0.000 description 18
- 229910052759 nickel Inorganic materials 0.000 description 15
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 14
- 229910052750 molybdenum Inorganic materials 0.000 description 14
- 239000011733 molybdenum Substances 0.000 description 14
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 13
- 239000010949 copper Substances 0.000 description 13
- 229910052748 manganese Inorganic materials 0.000 description 13
- 239000000463 material Substances 0.000 description 11
- 238000002844 melting Methods 0.000 description 10
- 230000008018 melting Effects 0.000 description 10
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 8
- 238000005275 alloying Methods 0.000 description 8
- 229910052802 copper Inorganic materials 0.000 description 8
- 229910001220 stainless steel Inorganic materials 0.000 description 7
- 230000000694 effects Effects 0.000 description 6
- 229910000851 Alloy steel Inorganic materials 0.000 description 5
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 5
- 230000000087 stabilizing effect Effects 0.000 description 5
- 238000005266 casting Methods 0.000 description 4
- 238000004519 manufacturing process Methods 0.000 description 4
- 239000010935 stainless steel Substances 0.000 description 4
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 3
- 230000008092 positive effect Effects 0.000 description 3
- VEXZGXHMUGYJMC-UHFFFAOYSA-M Chloride anion Chemical compound [Cl-] VEXZGXHMUGYJMC-UHFFFAOYSA-M 0.000 description 2
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 2
- 239000002253 acid Substances 0.000 description 2
- 239000000654 additive Substances 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 239000000155 melt Substances 0.000 description 2
- 229910052717 sulfur Inorganic materials 0.000 description 2
- 239000011593 sulfur Substances 0.000 description 2
- 238000003466 welding Methods 0.000 description 2
- 229910000640 Fe alloy Inorganic materials 0.000 description 1
- MBMLMWLHJBBADN-UHFFFAOYSA-N Ferrous sulfide Chemical compound [Fe]=S MBMLMWLHJBBADN-UHFFFAOYSA-N 0.000 description 1
- 229910001182 Mo alloy Inorganic materials 0.000 description 1
- 229910000990 Ni alloy Inorganic materials 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- 230000002378 acidificating effect Effects 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- JZQOJFLIJNRDHK-CMDGGOBGSA-N alpha-irone Chemical compound CC1CC=C(C)C(\C=C\C(C)=O)C1(C)C JZQOJFLIJNRDHK-CMDGGOBGSA-N 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 239000012141 concentrate Substances 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000001066 destructive effect Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 238000007689 inspection Methods 0.000 description 1
- 230000003993 interaction Effects 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- CADICXFYUNYKGD-UHFFFAOYSA-N sulfanylidenemanganese Chemical compound [Mn]=S CADICXFYUNYKGD-UHFFFAOYSA-N 0.000 description 1
- 239000013589 supplement Substances 0.000 description 1
- 230000007704 transition Effects 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
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
-
- 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- 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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- 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
- 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
- C21D2211/005—Ferrite
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Description
本発明は、新しい二相鋼、特に、ノッチ付き衝撃強さ及び機械加工性を改善した省合金型二相鋼に関する。 The present invention relates to a new duplex steel, particularly an alloy-saving duplex stainless steel with improved notched impact strength and machinability.
従来、ステンレス特殊鋼の市場においてとりわけ重要性が高いのが、オーステナイト系ステンレス鋼である。これが次第に二相鋼に取って代わられている。現在、二相鋼には主に以下の４種類、すなわち汎用二相鋼、スーパー二相鋼、ハイパー二相鋼及び省合金型二相鋼が知られている。これらにおける違いは、化学組成、並びにさまざまな機械特性及び腐食特性である。二相鋼は、ほぼ同じ割合のフェライト相（α鉄）とオーステナイト相（γ鉄）から成る二相組織が基盤になっている。二相鋼はその特性の組み合わせを特徴としており、フェライト相は基本的に剛性と応力腐食割れ（ＳＣＣ，Ｓｔｒｅｓｓ Ｃｏｒｒｏｓｉｏｎ Ｃｒａｃｋｉｎｇ）に対する耐性が高く、オーステナイト相は延性と全体的な耐食性を備えている。耐食・耐酸鋼に属する二相鋼は、７０年以上前から存在する。 Conventionally, austenitic stainless steel is particularly important in the stainless steel market. This is gradually being replaced by duplex stainless steel. At present, the following four types of duplex steels are known: general-purpose duplex stainless steel, super duplex stainless steel, hyper duplex stainless steel and alloy-saving duplex duplex steel. The differences in these are the chemical composition and various mechanical and corrosion properties. Duplex steel is based on a duplex structure consisting of approximately the same proportion of ferrite phase (α iron) and austenite phase (γ iron). Duplex steels are characterized by a combination of their properties, the ferrite phase is basically highly rigid and resistant to stress corrosion cracking (SCC), and the austenitic phase has ductility and overall corrosion resistance. Duplex steels belonging to corrosion and acid resistant steels have existed for over 70 years.
近年、合金元素、とりわけニッケルとモリブデンの価格が大幅に上がっている。特に、ニッケル価格の高騰がきっかけとなり、高価なニッケルとモリブデンの合金含有量が大幅に少なくても、同様の高い剛性特性と実質的に同様の腐食特性を備える特殊鋼特性を有する代替合金を調達するための開発が促進された。 In recent years, the price of alloying elements, especially nickel and molybdenum, has increased significantly. In particular, the rise in nickel prices has led to the procurement of alternative alloys with special steel properties that have similar high stiffness characteristics and substantially similar corrosion properties, even though the content of expensive nickel and molybdenum alloys is significantly lower Development to promote was promoted.
この開発の成果が省合金型二相鋼である。数年前まで、ニッケルとモリブデンの合金含有量が少ないこの耐食二相鋼の製造は非常に手間が掛かり高価であった。新しい製造方法により、工業生産向けの省合金型二相鋼の製造の実現に成功した。応力亀裂及び孔食に対する省合金型二相鋼の耐性は、同等のオーステナイト系特殊鋼よりも高い。熱負荷と熱伝導率が同じ場合、この鋼はあまり膨張しない。さらに、基本的に同じ割合のフェライト相とオーステナイト相から成る材料は、溶接した状態でも、オーステナイト鋼と比べて基本剛性が２倍高い。これらの特性は、建築技術において固定要素の構造的なスリム化に利用することができる。例えば、比較的少ない固定点で済むため、組み立てが簡素化し、ファサード建築では熱橋の数が減少する。省合金型二相鋼では、製造時に炭素含有量を減らすことにより、粘性が向上し、延性特性も改善する。 The result of this development is alloy-saving duplex steel. Until a few years ago, the production of this corrosion-resistant duplex stainless steel with a low alloy content of nickel and molybdenum was very laborious and expensive. We succeeded in producing alloy-saving duplex stainless steel for industrial production by a new production method. The resistance of alloy-saving duplex stainless steels to stress cracking and pitting corrosion is higher than comparable austenitic special steels. When the heat load and thermal conductivity are the same, this steel does not expand much. Furthermore, a material consisting essentially of the same proportion of ferrite phase and austenite phase has twice the basic rigidity compared to austenitic steel, even in a welded state. These properties can be used for structural slimming of the fixing elements in building technology. For example, relatively few fixed points are required, simplifying assembly and reducing the number of thermal bridges in facade construction. In alloy-saving duplex stainless steel, viscosity is improved and ductility is improved by reducing the carbon content during production.
フェライト−オーステナイト系二相鋼の分野では、鍛造合金又は鋳造合金について多数の記述がある。以下に、先行技術に基づく提案を個々に説明する。
まず、米国特許第４ ７９８ ６３５号明細書（特許文献１）には、高い耐食性と良好な溶接性を備えたフェライト−オーステナイト系合金鋼が記載されている。この合金鋼は主に以下の元素から成る。
Ｃ ：０．０６重量％以下
Ｓｉ：１．５重量％以下
Ｍｎ：２．０重量％以下
Ｃｒ：２１．０〜２４．５重量％
Ｎｉ：２．０〜５．５重量％
Ｃｕ：０．０１〜１．０重量％
Ｎ ：０．０５〜０．３重量％
鉄及び一般的な不純靴：残部
この場合、元素の含有量は、フェライト相αの含有量が３５〜６５％であるように互いに調整されている。この合金は、合金温度が６０℃超であり、同時に塩化物の量が最大１．０００ｐｐｍである環境に特に適しており、オーステナイト相は、１０〜３０％の範囲において冷間加工に強い。
In the field of ferritic-austenitic duplex steels, there are numerous descriptions of forged alloys or cast alloys. In the following, proposals based on the prior art will be described individually.
First, U.S. Pat. No. 4,798,635 (Patent Document 1) describes a ferrite-austenite alloy steel having high corrosion resistance and good weldability. This alloy steel mainly consists of the following elements.
C: 0.06 wt% or less Si: 1.5 wt% or less Mn: 2.0 wt% or less Cr: 21.0-24.5 wt%
Ni: 2.0 to 5.5% by weight
Cu: 0.01 to 1.0% by weight
N: 0.05 to 0.3% by weight
Iron and general impure shoes: balance In this case, the contents of the elements are adjusted to each other so that the content of the ferrite phase α is 35 to 65%. This alloy is particularly suitable for environments where the alloy temperature is above 60 ° C. and at the same time the amount of chloride is at most 1.000 ppm, and the austenitic phase is resistant to cold working in the range of 10-30%.
この合金は、合金費用を削減するため、鍛造分野で開発された。合金元素のニッケルとモリブデンを節約したことにより、同等の剛性を有してはいるものの、耐食性が低下した二相鋼が製造された。この合金は鋳造合金としても適している。 This alloy was developed in the forging field to reduce alloy costs. By saving the alloying elements nickel and molybdenum, a duplex stainless steel was produced that had the same rigidity but reduced corrosion resistance. This alloy is also suitable as a casting alloy.
さらに、国際公開第０２／２７０５６（Ａ１）号パンフレット（欧州特許出願公開第１ ３２７ ００８（Ａ１）号明細書）（特許文献２）は、微細構造を有するフェライト−オーステナイト系ステンレス鋼を扱っている。このステンレス鋼は基本的に３５〜６５体積％のフェライト相及び３５〜６５体積％のオーステナイト相から成り、以下の化学組成（重量パーセント）を有する。
Ｃ ：０．００５〜０．０７
Ｓｉ：０．１〜２．０
Ｍｎ：３〜８
Ｃｒ：１９〜２３
Ｎｉ：０．５〜１．７
Ｍｏ及び／又はＷ：必要に応じて、総量が最大１．０（Ｍｏ＋Ｗ／２）
Ｃｕ：必要に応じて、最大１．０まで
Ｎ ：０．１５〜０．３０
鉄及び不純物：残部
Furthermore, WO 02/27056 (A1) pamphlet (European Patent Application Publication No. 1 327 008 (A1)) (Patent Document 2) deals with a ferrite-austenite stainless steel having a microstructure. . This stainless steel basically consists of 35 to 65 volume% ferrite phase and 35 to 65 volume% austenitic phase and has the following chemical composition (weight percent).
C: 0.005-0.07
Si: 0.1-2.0
Mn: 3-8
Cr: 19-23
Ni: 0.5-1.7
Mo and / or W: If necessary, the total amount is up to 1.0 (Mo + W / 2)
Cu: If necessary, up to 1.0 N: 0.15 to 0.30
Iron and impurities: balance
さらに、フェライト系材料及びオーステナイト系材料、すなわちクロム当量及びニッケル当量にはそれぞれ以下の条件が該当する。
２０＜Ｃｒｅｑ＜２４．５
１０＜Ｎｉｅｑ、このとき、
Ｃｒｅｑ＝Ｃｒ＋１．５ Ｓｉ＋Ｍｏ＋２ Ｔｉ＋０．５ Ｎｂ、かつ、
Ｎｉｅｑ＝Ｎｉ＋０．５ Ｍｎ＋３０（Ｃ＋Ｎ）＋０．５（Ｃｕ＋Ｃｏ）
Furthermore, the following conditions correspond to the ferrite material and the austenite material, that is, the chromium equivalent and the nickel equivalent, respectively.
20 <Cr eq <24.5
10 <Ni eq ,
Cr eq = Cr + 1.5 Si + Mo + 2 Ti + 0.5 Nb, and
Ni eq = Ni + 0.5 Mn + 30 (C + N) +0.5 (Cu + Co)
合金費用をさらに削減するために、この鋼のクロム含有量をさらに減らし、高価なニッケルを一部マンガンに置き換えた。 In order to further reduce the alloy costs, the steel was further reduced in chromium content and some of the expensive nickel was replaced by manganese.
特許文献２と同一の化学組成のステンレス鋼は、特に鋳造合金として国際公開第２００９／１３８５７０（Ａ１）号パンフレット（欧州特許出願公開第２ ２７９ ２７６（Ａ１）号明細書）（特許文献３）に記載されている。この合金は、記載されている高いマンガン含有量、及び鍛造合金と比べて大きな粒径のために、遷移温度が変化し、また、適用温度が低い場合には材料が脆化する。 Stainless steel having the same chemical composition as Patent Document 2 is disclosed in WO 2009/138570 (A1) pamphlet (European Patent Application Publication No. 2 279 276 (A1) specification) (Patent Document 3) as a cast alloy. Have been described. This alloy has a high manganese content and a large grain size compared to the forged alloy, so the transition temperature changes and the material becomes brittle when the application temperature is low.
欧州特許出願公開第１ ８６７ ７４８（Ａ１）号明細書（特許文献４）に従った先行技術に基づいて、以下の組成を有する合金も知られている。
Ｃ≦０．０５重量％
２１重量％≦Ｃｒ≦２５重量％
１重量％≦Ｎｉ≦２．９５重量％
０．１６重量％≦Ｎ≦０．２８重量％
Ｍｎ≦２．０重量％
Ｍｏ＋Ｗ／２≦０．５重量％
Ｍｏ≦０．４５重量％
Ｗ≦０．１５重量％
Ｓｉ≦１．４重量％
Ａｌ≦０．０５重量％
０．１１重量％≦Ｃｕ≦０．５０重量％
Ｓ≦０．０１０重量％
Ｐ≦０．０４０重量％
Ｂ≦０．０００５重量％
Ｃｏ≦０．５重量％
ＲＥＭ≦０．１重量％
Ｖ≦０．５重量％
Ｔｉ≦０．１重量％
Ｎｂ≦０．３重量％
Ｍｇ≦０．１重量％
鉄及び不純物：残部
Based on the prior art according to EP 1 867 748 (A1) (Patent Document 4), an alloy having the following composition is also known.
C ≦ 0.05% by weight
21 wt% ≦ Cr ≦ 25 wt%
1 wt% ≦ Ni ≦ 2.95 wt%
0.16% by weight ≦ N ≦ 0.28% by weight
Mn ≦ 2.0% by weight
Mo + W / 2 ≦ 0.5% by weight
Mo ≦ 0.45% by weight
W ≦ 0.15% by weight
Si ≦ 1.4% by weight
Al ≦ 0.05% by weight
0.11 wt% ≦ Cu ≦ 0.50 wt%
S ≦ 0.010% by weight
P ≦ 0.040% by weight
B ≦ 0.0005% by weight
Co ≦ 0.5% by weight
REM ≦ 0.1% by weight
V ≦ 0.5% by weight
Ti ≦ 0.1% by weight
Nb ≦ 0.3% by weight
Mg ≦ 0.1% by weight
Iron and impurities: balance
したがって、これは２％以下のマンガンを含むが、銅を含まない鍛造合金である。 This is therefore a forged alloy containing up to 2% manganese but no copper.
さらに、２０１０年１０月１３〜１５日にフランスのボーヌで開催された二相ステンレス鋼に関する第８回会議で、Ｕｇｉｔｅｃｈ社の新しい合金（材料番号１．４６６９）が紹介された。しかしながら、この合金はマンガン含有量が１〜３重量％であり、そのため、同じく本発明による合金とは区別される。 In addition, a new alloy (material number 1.4669) from Ugtech was introduced at the 8th meeting on duplex stainless steel held in Beaune, France on October 13-15, 2010. However, this alloy has a manganese content of 1 to 3% by weight and is therefore also distinguished from the alloy according to the invention.
したがって、本発明の課題は、先行技術の欠点を回避し、市販されている従来の二相鋼と比べて高価な合金元素の割合が少ないながらも、良好な特性、とりわけ高い剛性及び良好な耐食性、良好な可鍛性及び加工性を備えた、フェライト−オーステナイト系ステンレス鋼を提供することである。特に、この合金ではニッケル及びモリブデンの含有量が低減されながらも、同時に、二相鋼に求められる良好な特性が実現されるはずである。 The object of the present invention is therefore to avoid the disadvantages of the prior art and to have good properties, in particular high rigidity and good corrosion resistance, while the proportion of the expensive alloying elements is low compared to conventional duplex stainless steels that are commercially available. To provide a ferritic-austenitic stainless steel having good malleability and workability. In particular, this alloy should achieve the good properties required for duplex stainless steels while at the same time reducing the nickel and molybdenum contents.
上述の課題は、本発明に従ってノッチ付き衝撃強さ及び機械加工性を改善した二相鋼により解決される。この二相鋼は以下の化学組成を有するか、又は以下から成る。
Ｃ ＜０．０７０重量％
Ｓｉ ＜１．５重量％
Ｍｎ ＜１．０重量％
Ｃｒ ２１．０〜２３．０重量％
Ｎｉ １．０〜３．０重量％
Ｃｕ １．０〜３．０重量％
Ｎ ０．１０〜０．３０重量％
Ｍｏ ＜０．５重量％
鉄及び不純物：残部
The above problems are solved by the duplex stainless steel with improved notched impact strength and machinability according to the present invention. This duplex stainless steel has the following chemical composition or consists of:
C <0.070 wt%
Si <1.5 wt%
Mn <1.0% by weight
Cr 21.0-23.0 wt%
Ni 1.0-3.0 wt%
Cu 1.0-3.0 wt%
N 0.10 to 0.30% by weight
Mo <0.5 wt%
Iron and impurities: balance
これに従って、改善されたノッチ付き衝撃強さ及び機械加工性を有するフェライト−オーステナイト系ステンレス鋼、特に省合金型二相鋼、好ましくは省合金型二相鋳造合金が提供される。本発明に従って、合金組成の選択により、低温（例えば−４０℃）であっても、高い剛性に加えて良好なノッチ付き衝撃強さを備える合金が得られた。 Accordingly, a ferritic-austenitic stainless steel, particularly an alloy-saving duplex steel, preferably an alloy-saving duplex casting alloy, having improved notched impact strength and machinability is provided. In accordance with the present invention, selection of the alloy composition resulted in an alloy with good notched impact strength in addition to high stiffness, even at low temperatures (eg, -40 ° C).
本発明による合金鋼は良好な溶接性も示す。溶接後の熱処理の必要性及び種類は、材料及び溶接補助剤の化学組成、部材の形態、肉厚、溶接条件、剛性特性、非破壊検査の範囲によって、また、必要に応じて、追加的な条件の遵守に応じて異なる。 The alloy steel according to the invention also exhibits good weldability. The need and type of post-weld heat treatment depends on the chemical composition of the materials and welding aids, the shape of the parts, the wall thickness, the welding conditions, the stiffness characteristics, the scope of non-destructive inspection and, if necessary, additional Varies depending on compliance with conditions.
さらに、本発明に従って得られる鋼は良好な耐食性を有する。耐孔食性指数（ＰＲＥ：ｐｉｔｔｉｎｇ ｒｅｓｉｓｔａｎｃｅ ｅｑｕｉｖａｌｅｎｔの略語）（「孔食指数」とも呼ばれる）は、孔食又は隙間腐食に対するニッケル含有合金の耐食性を評価するのに用いられる。孔食は、一般に、金属表面上に小さく現れる、又は点状の腐食箇所を意味し、この腐食が表面の下側に著しく広がっている場合がある。隙間腐食は局所的に加速する腐食で、隙間（接合部隙間など）の範囲に腐食が集中する。こうした形態の腐食を防ぐ鋼の能力は、合金元素の含有量によって決まる。孔食指数は、以下の式によって計算される：
ＰＲＥ＝Ｃｒ［重量％］＋３．３Ｍｏ［重量％］＋１６Ｎ［重量％］
上式では、クロム、モリブデン及び窒素元素の百分率を重量％にて式に算入する。孔食指数が高いほど、孔食又は隙間腐食に対する材料の耐性が高い。
Furthermore, the steel obtained according to the invention has good corrosion resistance. The pitting resistance index (PRE: abbreviation for Pitting Resistance Equivalent) (also called “pitting corrosion index”) is used to evaluate the corrosion resistance of nickel-containing alloys against pitting corrosion or crevice corrosion. Pitting corrosion generally refers to small or point-like corrosion spots that appear on the metal surface, which may spread significantly below the surface. The crevice corrosion is locally accelerated corrosion, and the corrosion concentrates in a range of a gap (such as a joint gap). The ability of steel to prevent this form of corrosion depends on the alloying element content. The pitting index is calculated by the following formula:
PRE = Cr [wt%] + 3.3 Mo [wt%] + 16 N [wt%]
In the above formula, the percentages of chromium, molybdenum and nitrogen elements are included in the formula in weight%. The higher the pitting index, the higher the resistance of the material to pitting or crevice corrosion.
本発明の鋼、特に省合金型二相鋳造合金の化学組成は、ここで、以下の式で定められる２６超のＰＲＥ値を有する。
ＰＲＥ＝Ｃｒ［重量％］＋３．３Ｍｏ［重量％］＋１６Ｎ［重量％］＞２６
The chemical composition of the steel of the present invention, in particular an alloy-saving two-phase cast alloy, now has a PRE value of more than 26 as defined by the following formula:
PRE = Cr [wt%] + 3.3 Mo [wt%] + 16 N [wt%]> 26
さらに、本発明による二相鋼は、とりわけ良好な機械特性を備える。 Furthermore, the duplex stainless steel according to the invention has particularly good mechanical properties.
本発明に従ったＲＴにおける材料の最低要件は以下の通りである。
降伏強度：Ｒｐ０．２＞４００ＭＰａ
引張強度：Ｒｍ＞６００ＭＰａ
伸長：Ａ＞３０％
ノッチ付き衝撃エネルギー：Ａｖ＞８０Ｊ
Ａｖ（−４０℃）＞２７Ｊ
The minimum requirements for materials in RT according to the present invention are as follows.
Yield strength: R p0.2 > 400 MPa
Tensile strength: R m > 600 MPa
Elongation: A> 30%
Notched impact energy: Av> 80J
Av (−40 ° C.)> 27 J
本発明による鋼は、好ましくは、その特性に基づいて二相鋼が有益である場所に用いることができる。これは例えば、特に低温であっても、高い剛性、良好な溶接性、良好な機械加工性、良好なノッチ付き衝撃強さが役割を果たす領域である。単なる例示として、遠心機又はデカンタ構造のドラムシェル、圧力容器（溶接構造の形態でも）、化学工業及び製紙業で用いるローラーを挙げることができる。 The steel according to the invention can preferably be used where a duplex steel is beneficial based on its properties. This is for example the region where high stiffness, good weldability, good machinability, and good notched impact strength play a role, even at low temperatures. By way of example only, a drum shell with a centrifuge or a decanter structure, a pressure vessel (even in the form of a welded structure), and a roller used in the chemical and paper industries can be mentioned.
以下に、本発明による省合金型二相鋼の個々の合金元素を、その特性、鋼における重要性と相互作用に関して詳細に説明する。
合金元素は、原則的にカーバイド系、オーステナイト系又はフェライト系のいずれの材料であるかによって、つまり、どのような目的で鋼に合金するかで区別することができる。それぞれの合金元素が、その含有量に応じて鋼に固有の特性を付与している。数多くの合金元素が、場合によっては効果を高めることができるが、逆効果を有し、相互に相応に影響を及ぼし合う可能性もあるため、容易に予測できない複雑な全体的効果が生じる可能性がある。現時点での鋼における特定の合金元素は、所望の特性の要件を満たしているにすぎず、加工及び熱処理をして初めて実際に目的とする特徴を示す。
In the following, the individual alloying elements of the alloy-saving duplex steel according to the present invention will be described in detail with respect to their properties, importance and interaction in the steel.
The alloying element can be distinguished depending on whether it is a carbide-type, austenite-type or ferrite-type material, that is, for what purpose it is alloyed with steel. Each alloy element imparts unique properties to the steel depending on its content. Many alloying elements can be effective in some cases, but can have complex overall effects that are not easily predictable because they can be counterproductive and can affect each other accordingly. There is. The specific alloying elements in steel at the present time only satisfy the requirements of the desired properties, and only after processing and heat treatment show the actual desired characteristics.
炭素（融点３９７４℃）：
本発明による合金鋼において、炭素は任意の構成要素である。炭素はオーステナイト相を安定化させるための元素である。炭素は、鉄の合金元素として融点を低下させ、格子間溶解合金元素として剛性を高める。炭素含有量が増えると、Ｍ２３Ｃ６カーバイドの形成の危険が高まり、それにより延性、粘性及び耐食性が低下する。そのため、本発明に従って、耐食性を改善するために、０．０７０重量％より少ない、好ましくは０．０５０重量％より少ない、さらに好ましくは０．０３０重量％より少ない炭素が用いられる。
Carbon (melting point 3974 ° C.):
In the alloy steel according to the present invention, carbon is an optional component. Carbon is an element for stabilizing the austenite phase. Carbon lowers the melting point as an iron alloy element and increases rigidity as an interstitial melting alloy element. Increasing the carbon content increases the risk of forming M 23 C 6 carbide, thereby reducing ductility, viscosity, and corrosion resistance. Therefore, in accordance with the present invention, less than 0.070 wt%, preferably less than 0.050 wt%, more preferably less than 0.030 wt% carbon is used to improve corrosion resistance.
ケイ素（融点１４１０℃）：
ケイ素は、同じく本発明の合金鋼の任意の構成要素にすぎず、フェライト相安定化元素であり、脱酸剤として機能する。含有量が多いと、脆性金属間相（σ相及び同様の相）の形成が加速し、これにより鋼の延性が低下するという悪影響がある。ケイ素は剛性と耐摩耗性を向上させ、溶鋼の流動性を高め、それにより鋳造時の表面欠陥を低減する。ケイ素の含有量が多い場合は、添加剤でスケーリング抵抗性、耐酸性及び耐食性を高める。そのため、本発明に従って、粘性を改善するために、１．５重量％より少ない、好ましくは１．０重量％より少ない、さらに好ましくは０．５０重量％より少ない含有量でケイ素が用いられる。
Silicon (melting point 1410 ° C.):
Silicon is also only an optional component of the alloy steel of the present invention, is a ferrite phase stabilizing element, and functions as a deoxidizer. When the content is large, the formation of brittle intermetallic phases (σ phase and similar phases) is accelerated, which has the adverse effect of reducing the ductility of the steel. Silicon improves rigidity and wear resistance and increases the fluidity of the molten steel, thereby reducing surface defects during casting. If the silicon content is high, the additive increases the scaling resistance, acid resistance and corrosion resistance. Therefore, in accordance with the present invention, silicon is used with a content of less than 1.5% by weight, preferably less than 1.0% by weight, more preferably less than 0.50% by weight, in order to improve the viscosity.
マンガン（融点１２２１℃）：
マンガンはオーステナイト相安定化元素である。例えば、窒素の溶解性を高めるのに役立つ。マンガンは硫化マンガンとして硫黄と結合することにより硫化鉄の望ましくない影響を低減し、二相ステンレス鋼の溶解中に脱酸化効果を有し、また、鋼の熱加工性を改善するのに役立つ。したがって、マンガンは鍛造性及び溶接性に良い影響をもたらす。降伏強度、剛性及び耐摩耗性は、マンガンの添加によって向上する。マンガンは、引張強度と、それに伴い負荷能力も高める。しかしながら、マンガンを大量に加えると耐食性が損なわれ、望ましくない脆性金属間相が形成されやすくなる。そのため、本発明に従って、マンガン含有量は、粘性を改善するために、１．０重量％未満、さらに好ましくは０．５０重量％未満に抑えられる。マンガンは、本発明による鋼において、任意の構成要素として、まったく含まなくてもよい。
Manganese (melting point 1221 ° C.):
Manganese is an austenite phase stabilizing element. For example, it helps to increase the solubility of nitrogen. Manganese combines with sulfur as manganese sulfide to reduce the undesirable effects of iron sulfide, has a deoxidizing effect during melting of the duplex stainless steel, and also helps to improve the heat workability of the steel. Therefore, manganese has a positive effect on forgeability and weldability. Yield strength, rigidity and wear resistance are improved by the addition of manganese. Manganese increases the tensile strength and the load capacity associated therewith. However, when manganese is added in a large amount, corrosion resistance is impaired, and an undesirable brittle intermetallic phase is easily formed. Therefore, according to the present invention, the manganese content is suppressed to less than 1.0% by weight, more preferably less than 0.50% by weight, in order to improve the viscosity. Manganese may not be included at all as an optional component in the steel according to the invention.
クロム（融点１９２０℃）：
本発明による鋼において、クロムは、とりわけ耐食性の保持に関して、及びフェライト相／オーステナイト相比の調整のために重要な元素である。クロムはフェライト相を安定化させる。クロム含有量が多すぎると、σ相のように金属間結合の形成が促進され、それに伴って材料の脆性が生じる。したがって、本発明による二相鋼では、２１．０〜２３．０重量％のクロムが使用される。
Chromium (melting point 1920 ° C.):
In the steel according to the invention, chromium is an important element, inter alia for maintaining corrosion resistance and for adjusting the ferrite phase / austenite phase ratio. Chromium stabilizes the ferrite phase. When there is too much chromium content, formation of an intermetallic bond will be accelerated | stimulated like (sigma) phase and the brittleness of material will arise in connection with it. Therefore, 21.0-23.0% by weight of chromium is used in the duplex stainless steel according to the invention.
ニッケル（融点１４５５℃）：
ニッケルは面心立方体構造の元素で、そのため溶液焼きなまし温度の範囲内でオーステナイト相を安定化させる効果を有する。オーステナイト相の積層欠陥エネルギーを高めるため、鋼の粘性に良い影響を及ぼす。積層欠陥エネルギーが高まると、マルテンサイト相においてオーステナイト相の機械及び／又は熱変換が妨げられ、それにより鋼の粘性が向上する。クロム及びモリブデン含有量が一定でニッケル含有量が多すぎると、オーステナイト相の含有量が増え、それに伴って剛性が低下する。ニッケルの原料価格は他の合金元素と比べると高く、変動が激しいことから、ニッケルを補うために、本発明に従って、可能な限り別の合金元素が使用される。そのため、本発明に従って、ニッケルは１．０〜３．０重量％、好ましくは２．０〜３．０重量％の含有量で使用される。
Nickel (melting point 1455 ° C.):
Nickel is an element having a face-centered cubic structure, and therefore has an effect of stabilizing the austenite phase within the range of the solution annealing temperature. To increase the stacking fault energy of the austenite phase, it has a positive effect on the viscosity of the steel. Increased stacking fault energy impedes mechanical and / or thermal conversion of the austenite phase in the martensite phase, thereby improving the viscosity of the steel. If the chromium and molybdenum contents are constant and the nickel content is too large, the austenite phase content increases and the rigidity decreases accordingly. Since the raw material price of nickel is high and fluctuates compared to other alloy elements, other alloy elements are used as much as possible in accordance with the present invention to supplement nickel. Therefore, according to the present invention, nickel is used in a content of 1.0 to 3.0% by weight, preferably 2.0 to 3.0% by weight.
銅（融点１０８３℃）：
銅もオーステナイト相の安定化元素であり、さらに、特に酸性媒質中で耐食性に良い影響を及ぼす。二相鋼のフェライト相における銅の溶解性は、低温時には急激に低下するため、フェライトにおいて銅リッチ相が溶出する。これにより、降伏強度／剛性比が高まる。さらに、銅は耐孔食性又は耐腐食性を低下させる場合がある。そのため、本発明に従って、銅は１．０〜３．０重量％、好ましくは１．５〜２．５重量％の含有量で使用される。さらに、銅はニッケルのように低温粘性に良い影響を及ぼす。
Copper (melting point 1083 ° C.):
Copper is also a stabilizing element of the austenite phase, and has a good effect on corrosion resistance, especially in acidic media. Since the solubility of copper in the ferrite phase of the duplex stainless steel decreases rapidly at low temperatures, the copper-rich phase elutes in the ferrite. This increases the yield strength / rigidity ratio. Furthermore, copper may reduce pitting corrosion resistance or corrosion resistance. Therefore, according to the present invention, copper is used in a content of 1.0 to 3.0% by weight, preferably 1.5 to 2.5% by weight. Furthermore, copper has a positive effect on low temperature viscosity like nickel.
窒素：
窒素はオーステナイト系材料であり、つまり、オーステナイト相の構成要素を安定化させる。通常、窒素は二相鋼の格子間に溶解しており、オーステナイト相には窒素の９５％が集まっている。これによりオーステナイト相の格子歪みが大きくなり、それに伴って、オーステナイト相の硬度が向上し、また、全体的に二相鋼の剛性が向上する。オーステナイト相のこの格子歪みは、気温の低下に伴って粘性を低下させる。溶解窒素の含有量が多くなると、孔食及び隙間腐食に対する耐性も向上する。
nitrogen:
Nitrogen is an austenitic material, that is, it stabilizes the components of the austenite phase. Normally, nitrogen is dissolved between the lattices of the duplex stainless steel, and 95% of the nitrogen is collected in the austenite phase. As a result, the lattice strain of the austenite phase is increased, and accordingly, the hardness of the austenite phase is improved, and the rigidity of the duplex stainless steel is improved as a whole. This lattice distortion of the austenite phase reduces the viscosity with decreasing temperature. When the content of dissolved nitrogen is increased, resistance to pitting corrosion and crevice corrosion is also improved.
しかしながら、未溶解窒素は、フェライト相で窒化物を形成することによって粘性を低下させる。そのため、本発明に従って、窒素含有量は０．１０〜０．３０重量％、好ましくは０．１５〜０．２５重量％となる。 However, undissolved nitrogen reduces viscosity by forming nitrides in the ferrite phase. Therefore, according to the present invention, the nitrogen content is 0.10 to 0.30% by weight, preferably 0.15 to 0.25% by weight.
モリブデン（融点２６２２℃）：
モリブデンは、本発明による二相合金鋼の任意の構成要素である。モリブデンは、フェライト相の安定化に用いられる。モリブデンは鉄と比べ、原子が非常に大きい。したがって、溶解した置換原子として、降伏強度及び引張強度の向上をもたらす。モリブデンの添加剤を加えることで、特に塩化物含有媒質において、耐食性も改善される。モリブデンの含有量が多すぎると、その製造時に鋼の脆性につながる。モリブデンは原料価格が非常に高く、揮発性であることから、０．５重量％未満のわずかな含有量でモリブデンが使用される。
Molybdenum (melting point 2622 ° C.):
Molybdenum is an optional component of the duplex stainless steel according to the present invention. Molybdenum is used to stabilize the ferrite phase. Molybdenum has much larger atoms than iron. Therefore, yield strength and tensile strength are improved as dissolved substitution atoms. Addition of molybdenum additives also improves corrosion resistance, especially in chloride-containing media. If the molybdenum content is too high, the steel will become brittle during its production. Since molybdenum is very expensive and volatile, molybdenum is used with a slight content of less than 0.5% by weight.
上に説明した元素の他に、本発明による鋼は、好ましくは、基本的にそれ以上の構成要素が添加されないが、鉄及び不可避の不純物のみ有する。不可避の不純物とは、例えば硫黄、リンなどである。 Besides the elements described above, the steel according to the invention preferably has only iron and inevitable impurities, although essentially no further components are added. Inevitable impurities include, for example, sulfur and phosphorus.
したがって、本発明による二相ステンレス鋼は、とりわけ省合金型二相合金、好ましくは省合金型二相鋳造合金の形態で、オーステナイト鋼の低価格の代替物であり、これは、特に低温（例えば−４０℃）時において改善されたノッチ付き衝撃強さ、良好な機械加工性、高い剛性及び熱後処理不要の良好な溶接性など、とりわけ良好な特性を備える。本発明の、特に鋳造合金の形態における二相ステンレス鋼は、本発明による鋼がとりわけ適しているような要求仕様があるさまざまな適用において特に有利である。 The duplex stainless steel according to the invention is therefore a low-cost alternative to austenitic steel, in particular in the form of alloy-saving duplex alloys, preferably alloy-saving duplex casting alloys, especially at low temperatures (eg It has particularly good properties, such as improved notched impact strength, good machinability, high rigidity and good weldability without the need for a thermal aftertreatment. The duplex stainless steel of the present invention, particularly in the form of a cast alloy, is particularly advantageous in a variety of applications where the required specifications are such that the steel according to the present invention is particularly suitable.
圧力及び／又は０℃未満の温度が重要である領域における本発明による二相鋼の使用も本発明の対象である。とりわけ好ましい使用として、遠心機及びデカンタ構造において、特にドラムシェル、あらゆる種類の圧力容器、化学工業及び製紙業で用いるローラーを挙げることができる。 The use of the duplex stainless steel according to the invention in areas where pressure and / or temperatures below 0 ° C. are also of interest. Particularly preferred uses include rollers used in centrifuge and decanter structures, especially in drum shells, all kinds of pressure vessels, chemical industry and paper industry.
以下に、本発明による教えを具体的に示す実施例に基づいて本発明を解説するが、これらに限定されるものではない。 In the following, the present invention will be explained based on examples specifically showing the teachings of the present invention, but the present invention is not limited thereto.
（実施例）
本発明による二相鋼に従った化学組成を有する、以下の表１に示す溶融物を製造した。
The melts shown in Table 1 below were produced having the chemical composition according to the duplex steel according to the invention.
表１に記載した溶融物について、以下の表２に示す室温における機械特性値を測定した。
低温時のノッチ付き衝撃エネルギーについて、以下の表３に示す特性値を算出した。
算出し、表２及び表３に示した特性値は、本発明による二相鋼の有利な特性を立証している。 The property values calculated and shown in Tables 2 and 3 demonstrate the advantageous properties of the duplex stainless steel according to the invention.
Claims (14)
Ｃ ＜０．０７０重量％
Ｓｉ ＜１．５重量％
Ｃｒ ２１．０〜２３．０重量％
Ｎｉ １．０〜３．０重量％
Ｃｕ １．０〜３．０重量％
Ｎ ０．１０〜０．３０重量％
Ｍｏ ＜０．５重量％
鉄及び不純物：残部 A dual phase steel with improved notched impact strength and machinability, said Ri consists duplex stainless steel of the following chemical composition, dual phase steel containing no Mn.
C <0.070 wt%
Si <1.5 wt%
Cr 21.0-23.0 wt%
Ni 1.0-3.0 wt%
Cu 1.0-3.0 wt%
N 0.10 to 0.30% by weight
Mo <0.5 wt%
Iron and impurities: balance
Ｃ ＜０．０７０重量％
Ｓｉ ＜１．５重量％
Ｍｎ ＜０．５０重量％
Ｃｒ ２１．０〜２３．０重量％
Ｎｉ ２．０〜３．０重量％
Ｃｕ １．０〜３．０重量％
Ｎ ０．１０〜０．３０重量％
Ｍｏ ＜０．５重量％
鉄及び不純物：残部 Notched impact strength and a dual phase steel with improved machinability, the duplex stainless steel has the following chemical composition or we made two-phase steel.
C <0.070 wt%
Si <1.5 wt%
Mn <0.50 wt%
Cr 21.0-23.0 wt%
Ni 2.0-3.0% by weight
Cu 1.0-3.0 wt%
N 0.10 to 0.30% by weight
Mo <0.5 wt%
Iron and impurities: balance
ＰＲＥ＝Ｃｒ［重量％］＋３．３Ｍｏ［重量％］＋１６Ｎ［重量％］によって定められる孔食指数（ＰＲＥ）が２６超であることを特徴とする、請求項１〜９のうちいずれか一項に記載の二相鋼。 The following formula:
Wherein the PRE = Cr weight% + 3.3Mo [wt%] + 16N defined by [wt%] pitting index (PRE) is 26 greater than any one of claims 1-9 Duplex steel described in 1.
圧力容器、
化学工業及び製紙業で用いるローラー、
における、請求項１〜１２のうちいずれか一項に記載の二相鋼の使用。 Centrifuge or decanter structure drum shell,
Pressure vessel,
Rollers used in the chemical and paper industries,
Use of the duplex stainless steel according to any one of claims 1 to 12 .
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| DE102012100908A DE102012100908A1 (en) | 2012-02-03 | 2012-02-03 | Duplex steel with improved notched impact strength and machinability |
| DE102012100908.2 | 2012-02-03 | ||
| PCT/EP2013/051721 WO2013113718A1 (en) | 2012-02-03 | 2013-01-30 | Duplex steel with improved notch-impact strength and machinability |
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| JP6322145B2 true JP6322145B2 (en) | 2018-05-09 |
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| JP (1) | JP6322145B2 (en) |
| KR (1) | KR20140127843A (en) |
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| DE (1) | DE102012100908A1 (en) |
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| GB1106501A (en) * | 1966-02-24 | 1968-03-20 | Crucible Steel Co America | Free machining stainless steels |
| SE451465B (en) * | 1984-03-30 | 1987-10-12 | Sandvik Steel Ab | FERRIT-AUSTENITIC STAINLESS STEEL MICROLEGATED WITH MOLYBID AND COPPER AND APPLICATION OF THE STEEL |
| JPH0768603B2 (en) * | 1989-05-22 | 1995-07-26 | 新日本製鐵株式会社 | Duplex stainless steel for building materials |
| JPH05230535A (en) * | 1991-07-16 | 1993-09-07 | Kubota Corp | Production of suction roll for paper-making machine |
| SE517449C2 (en) * | 2000-09-27 | 2002-06-04 | Avesta Polarit Ab Publ | Ferrite-austenitic stainless steel |
| JP4760032B2 (en) * | 2004-01-29 | 2011-08-31 | Ｊｆｅスチール株式会社 | Austenitic ferritic stainless steel with excellent formability |
| EP1867748A1 (en) * | 2006-06-16 | 2007-12-19 | Industeel Creusot | Duplex stainless steel |
| JP5156293B2 (en) * | 2007-08-02 | 2013-03-06 | 新日鐵住金ステンレス株式会社 | Ferritic / austenitic stainless steel with excellent corrosion resistance and workability and manufacturing method thereof |
| US20100126644A1 (en) * | 2007-08-02 | 2010-05-27 | Masaharu Hatano | Ferritic-austenitic stainless steel excellent in corrosion resistance and workability andmethod of production of same |
| FI125458B (en) | 2008-05-16 | 2015-10-15 | Outokumpu Oy | Stainless steel product, use of product and process for its manufacture |
| JP5288980B2 (en) * | 2008-10-02 | 2013-09-11 | 新日鐵住金ステンレス株式会社 | Duplex stainless steel with excellent impact toughness and its manufacturing method |
| JP5511208B2 (en) * | 2009-03-25 | 2014-06-04 | 新日鐵住金ステンレス株式会社 | Alloy-saving duplex stainless steel material with good corrosion resistance and its manufacturing method |
| JP5366609B2 (en) * | 2009-03-26 | 2013-12-11 | 新日鐵住金ステンレス株式会社 | Alloy-saving duplex stainless steel material with good corrosion resistance and its manufacturing method |
| JP5404280B2 (en) * | 2009-09-25 | 2014-01-29 | 新日鐵住金ステンレス株式会社 | High-strength, alloy-saving duplex stainless steel with excellent corrosion resistance in the heat affected zone |
| JP5406233B2 (en) * | 2011-03-02 | 2014-02-05 | 新日鐵住金ステンレス株式会社 | Clad steel plate made of duplex stainless steel and method for producing the same |
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| EP2809818A1 (en) | 2014-12-10 |
| CN104254627A (en) | 2014-12-31 |
| KR20140127843A (en) | 2014-11-04 |
| EP2809818B1 (en) | 2016-04-06 |
| JP2015511272A (en) | 2015-04-16 |
| ES2581524T3 (en) | 2016-09-06 |
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