US20080210344A1 - Precipitation Hardenable Martensitic Stainless Steel - Google Patents

Precipitation Hardenable Martensitic Stainless Steel Download PDF

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Publication number
US20080210344A1
US20080210344A1 US11/793,442 US79344205A US2008210344A1 US 20080210344 A1 US20080210344 A1 US 20080210344A1 US 79344205 A US79344205 A US 79344205A US 2008210344 A1 US2008210344 A1 US 2008210344A1
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United States
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max
stainless steel
content
martensitic stainless
steel alloy
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Abandoned
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US11/793,442
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English (en)
Inventor
Håkan Holmberg
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Sandvik Intellectual Property AB
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Sandvik Intellectual Property AB
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Publication of US20080210344A1 publication Critical patent/US20080210344A1/en
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    • 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
    • C22C38/18—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
    • C22C38/04—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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • 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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium

Definitions

  • Precipitation hardenable martensitic stainless steels are for example used in various high strength applications, such as springs, surgical needles, clips, fine tubes, parts for instruments and parts exposed to wear.
  • the material needs to posses certain properties.
  • the steel should be able to be produced by an easy manufacturing process, including alloying, casting, hot working as well as cold working, rendering a high strength material that is easy to fabricate by mechanical cutting methods into finished parts starting from wire, sheet, strip, bar or tube material.
  • the material should preferably be ductile and thus allowing severe forming such as bending, coiling, pressing, twisting etc. in the as received condition.
  • a very good corrosion resistance is often required, allowing the material to be used in different environments without having to consider additional corrosion protection such as painting or any other type of surface coating.
  • the steel should be able to be hardened to a high final hardness by a simple, low temperature, alloy treatment that causes minimal shape disturbance.
  • Austenitic stainless steels are, dependent on their composition, either soft and ductile in the annealed condition or hard and less ductile in the cold deformed condition. In the harder conditions austenitic steels are also very difficult to machine.
  • a further group is the precipitation hardenable stainless steels that can be formed in fairly soft condition and subsequently alloy treated to achieve a high hardness. Also this group of steels are more difficult to machine compared e.g. to the group of hardenable martensitic steels.
  • a precipitation hardenable stainless chromium nickel steel having the following composition in weight %:
  • the stainless steel according to the invention comprises titanium sulphides.
  • the stainless steel is hardened at a low temperature and has good machinability when subjected to drilling, turning, milling and other cutting operations.
  • FIG. 2 a SEM photograph of FIG. 1 marked with test point Spectrum 1 .
  • FIG. 3 a SEM photograph of FIG. 1 marked with test point Spectrum 2 .
  • FIG. 4 a SEM photograph of FIG. 1 marked with test point Spectrum 3 .
  • FIG. 7 a SEM photograph of FIG. 5 marked with test point Spectrum 2 .
  • FIG. 8 a SEM photograph of FIG. 5 marked with test point Spectrum 3 .
  • FIG. 9 a SEM photograph of FIG. 5 marked with test point Spectrum 4 .
  • Silicon is a ferrite-forming element and may also in higher contents reduce the hot working properties of the steel.
  • the content should therefore be max 1.5% more preferably max 1.0%.
  • Manganese is an austenite-forming element that in a similar way as nickel makes the steel less prone to a martensitic transformation at cold deformation.
  • the minimum content of manganese of the steel according to the invention is 0.2% by weight.
  • the manganese content has to be max 5%, preferably max 3% and most preferably 2.5%.
  • Manganese will together with sulfur form ductile non-metallic inclusions that for example are beneficial for the machining properties.
  • Sulfur is an element that will form sulfides in the steel. Sulfides are beneficial during machining as they will act as chip-breakers. The content of sulfur is therefore min 0.01% and more preferably min 0.015%, even more preferably 0.05% and most preferably min 0.1%. Sulfides may however act as weak areas in the steel from a corrosion resistance point of view. Further, high contents of sulfur may also be detrimental for the hot working properties. The content should therefore be max 0.4% and preferably max 0.3%.
  • the composition of the alloy according to the invention is so selected that the alloy comprises titanium sulphides. The titanium sulphides are principally present in the form of TiS or Ti 2 S.
  • Molybdenum is essential for the steel according to the invention, as it will contribute to the corrosion resistance of the steel. Molybdenum is also an active element during the precipitation hardening. The minimum content is therefore 1% or preferably, minimum 2% and most preferably minimum 3%. A too high content of molybdenum will however promote the formation of ferrite to a content that may result in problems during hot working. Further, a high content of molybdenum will also suppress the martensite formation during cold deformation. The content of molybdenum is therefore maximized to 6% and more preferable maximum 5%. Furthermore, it is expected that Mo could be partly or totally replaced by tungsten according to the common practice known to a person skilled in the art while still achieving the desired properties of the alloy.
  • Titanium is an essential alloying element in the invention due to at least two reasons. Firstly, titanium is used as a strong element for precipitation hardening and must therefore be present to be able to harden the steel for the final strength. Secondly, titanium will together with sulfur form titanium sulfides (TiS or possibly Ti 2 S). In general, titanium is a stronger sulfide former than manganese. As TiS are electrochemically nobler that MnS it is possible to achieve improved machining properties without deterioration of the corrosion resistance that is the normal case for free machining steels that utilize MnS for the increased machinability. Therefore, the minimum content of titanium is 0.3% and more preferably 0.5%. Too high titanium contents will promote ferrite formation in the steel and also increase the brittleness. The maximum content of titanium should therefore be restricted to 2.5% preferably 2% and most preferably not more than 1.5%.
  • Nitrogen is a powerful element as it will increase the strain hardening. However, it will also stabilize the austenite towards martensite transformation at cold forming. Nitrogen also has a high affinity to nitride formers such as titanium, aluminum and chromium. The nitrogen content should be restricted to maximum 0.1%, preferably 0.07% and most preferably max 0.05%.
  • the alloy is substantially free of manganese sulfides.
  • the wear was measured as the wear at clearance face on the cutting edge (flank wear), corner wear by built up edge and possible edge damages.
  • the tests were in some cases performed for two samples of each alloy composition.
  • the damages/wear was then graded after a scale with respect of the different types of wear/damages wherein as low of a grade as possible is desirable. A low value indicates a longer tool life compared to a high value.
  • Table 8 The results are disclosed in Table 8.
  • the ranking of the average of the tool wear of the two tests per alloy is seen in Table 9. A lower ranking indicates a longer tool life than a higher ranking.
  • the reference alloy 830207 and the 830211 alloy according to the invention were analyzed by means of Scanning Electron Microscope (SEM) using Back Scattered Electrons (BSE). The surfaces of the materials were in un-etched condition. A photograph of the reference alloy taken in the SEM is shown in FIG. 1 . Three different test points; Spectrum 1 illustrated in FIG. 2 a , Spectrum 2 illustrated in FIG. 3 a and Spectrum 3 illustrated in FIG. 4 a ; were investigated by Energy Dispersive X-ray analysis (EDX). The results are shown in FIGS. 2 b , 3 b , and 4 b , respectively. As can be clearly seen from the results, there are no titanium sulfides. This is considered to be a result of the low sulphur content of the alloy.
  • SEM Scanning Electron Microscope
  • BSE Back Scattered Electrons
  • FIG. 5 A photograph of the 830211 alloy of the invention taken in the SEM is shown in FIG. 5 . The difference can be clearly seen when comparing to FIG. 1 .
  • the composition of these test points were analyzed with EDX and the results are given in FIGS. 6 b , 7 b , 8 b and 9 b , respectively.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
US11/793,442 2004-12-23 2005-12-22 Precipitation Hardenable Martensitic Stainless Steel Abandoned US20080210344A1 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
SE0403176-1 2004-12-23
SE0403176A SE528454C3 (sv) 2004-12-23 2004-12-23 Utskiljningshärdbart martensitiskt rostfritt stål innefattande titansulfid
PCT/SE2005/001997 WO2006068610A1 (en) 2004-12-23 2005-12-22 Precipitation hardenable martensitic stainless steel

Publications (1)

Publication Number Publication Date
US20080210344A1 true US20080210344A1 (en) 2008-09-04

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US11/793,442 Abandoned US20080210344A1 (en) 2004-12-23 2005-12-22 Precipitation Hardenable Martensitic Stainless Steel

Country Status (7)

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US (1) US20080210344A1 (de)
EP (1) EP1831417A1 (de)
JP (1) JP2008525637A (de)
KR (1) KR20070086564A (de)
CN (1) CN100540712C (de)
SE (1) SE528454C3 (de)
WO (1) WO2006068610A1 (de)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US11692232B2 (en) 2018-09-05 2023-07-04 Gregory Vartanov High strength precipitation hardening stainless steel alloy and article made therefrom

Families Citing this family (15)

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FR2887558B1 (fr) * 2005-06-28 2007-08-17 Aubert & Duval Soc Par Actions Composition d'acier inoxydable martensitique, procede de fabrication d'une piece mecanique a partir de cet acier et piece ainsi obtenue
EP2265739B1 (de) 2008-04-11 2019-06-12 Questek Innovations LLC Durch kupfer-nukleierte nitridablagerungen gehärteter martensitischer edelstahl
US7931758B2 (en) * 2008-07-28 2011-04-26 Ati Properties, Inc. Thermal mechanical treatment of ferrous alloys, and related alloys and articles
WO2011040876A1 (en) * 2009-10-02 2011-04-07 Nanoxis Ab Screening of binders on immobilized native membrane proteins
JP5502575B2 (ja) 2010-04-16 2014-05-28 株式会社日立製作所 析出硬化型マルテンサイト系ステンレス鋼及び蒸気タービン動翼
DE102010025287A1 (de) 2010-06-28 2012-01-26 Stahlwerk Ergste Westig Gmbh Chrom-Nickel-Stahl
CN102168228A (zh) * 2011-03-28 2011-08-31 徐英忱 一种医用沉淀硬化不锈钢材料及其制备方法
JP5764503B2 (ja) * 2012-01-19 2015-08-19 三菱日立パワーシステムズ株式会社 析出硬化型マルテンサイト系ステンレス鋼、それを用いた蒸気タービン長翼、タービンロータ及び蒸気タービン
JP6111763B2 (ja) 2012-04-27 2017-04-12 大同特殊鋼株式会社 強度及び靭性に優れた蒸気タービンブレード用鋼
CN105908099A (zh) * 2016-04-18 2016-08-31 和县隆盛精密机械有限公司 一种地坪打磨机械臂及制备方法
SE539763C2 (en) * 2016-06-16 2017-11-21 Uddeholms Ab Steel suitable for plastic molding tools
CN107326300A (zh) * 2017-06-20 2017-11-07 上海大学兴化特种不锈钢研究院 一种耐蚀抗菌医用外科器件马氏体不锈钢及其制备方法
CN107587080B (zh) * 2017-10-17 2019-06-18 中国华能集团公司 一种沉淀强化耐热钢及其制备工艺
EP3891316A1 (de) * 2018-12-06 2021-10-13 Aperam Edelstahl, daraus hergestellte produkte und verfahren zur herstellung davon
KR102270898B1 (ko) * 2019-11-06 2021-06-30 주식회사 한중엔시에스 석출경화형 스테인리스강의 열처리 방법 및 이를 이용한 커플러 제조방법

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US3658513A (en) * 1969-03-06 1972-04-25 Armco Steel Corp Precipitation-hardenable stainless steel
US3764302A (en) * 1970-11-12 1973-10-09 Sandvik Ab Stainless steel
US4837108A (en) * 1985-07-31 1989-06-06 Daido Tokushuko Kabushiki Kaisha Austenitic free cutting stainless steels
US5512237A (en) * 1991-10-07 1996-04-30 Sandvik Ab Precipitation hardenable martensitic stainless steel
US20040154706A1 (en) * 2003-02-07 2004-08-12 Buck Robert F. Fine-grained martensitic stainless steel and method thereof
US20050126662A1 (en) * 2003-12-10 2005-06-16 Wei-Di Cao High strength martensitic stainless steel alloys, methods of forming the same, and articles formed therefrom

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US6238455B1 (en) * 1999-10-22 2001-05-29 Crs Holdings, Inc. High-strength, titanium-bearing, powder metallurgy stainless steel article with enhanced machinability
JP2001131713A (ja) * 1999-11-05 2001-05-15 Nisshin Steel Co Ltd Ｔｉ含有超高強度準安定オーステナイト系ステンレス鋼材および製造法
DE10251413B3 (de) * 2002-11-01 2004-03-25 Sandvik Ab Verwendung eines korrosionsbeständigen, martensitisch aushärtenden Stahls
SE522813C2 (sv) * 2003-03-07 2004-03-09 Sandvik Ab Användning av ett utskiljningshärdbart, martensitiskt rostfritt stål för tillverkning av implantat och osteosyntesprodukter
JP4030925B2 (ja) * 2003-06-06 2008-01-09 山陽特殊製鋼株式会社 快削析出硬化型ステンレス鋼
JP4152872B2 (ja) * 2003-12-12 2008-09-17 山陽特殊製鋼株式会社 被削性に優れた冷間加工用析出硬化型ステンレス鋼

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3658513A (en) * 1969-03-06 1972-04-25 Armco Steel Corp Precipitation-hardenable stainless steel
US3764302A (en) * 1970-11-12 1973-10-09 Sandvik Ab Stainless steel
US4837108A (en) * 1985-07-31 1989-06-06 Daido Tokushuko Kabushiki Kaisha Austenitic free cutting stainless steels
US5512237A (en) * 1991-10-07 1996-04-30 Sandvik Ab Precipitation hardenable martensitic stainless steel
US20040154706A1 (en) * 2003-02-07 2004-08-12 Buck Robert F. Fine-grained martensitic stainless steel and method thereof
US20050126662A1 (en) * 2003-12-10 2005-06-16 Wei-Di Cao High strength martensitic stainless steel alloys, methods of forming the same, and articles formed therefrom

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US11692232B2 (en) 2018-09-05 2023-07-04 Gregory Vartanov High strength precipitation hardening stainless steel alloy and article made therefrom

Also Published As

Publication number Publication date
CN100540712C (zh) 2009-09-16
EP1831417A1 (de) 2007-09-12
KR20070086564A (ko) 2007-08-27
JP2008525637A (ja) 2008-07-17
SE0403176D0 (sv) 2004-12-23
WO2006068610A1 (en) 2006-06-29
SE528454C2 (sv) 2006-11-14
SE0403176L (sv) 2006-06-24
CN101087897A (zh) 2007-12-12
SE528454C3 (sv) 2007-01-09

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