SE420623B - AUSTENITIC, EXCEPTION CARDABLE STAINLESS CHROME-NICKEL ALUMINUM STEEL - Google Patents

AUSTENITIC, EXCEPTION CARDABLE STAINLESS CHROME-NICKEL ALUMINUM STEEL

Info

Publication number
SE420623B
SE420623B SE7910719A SE7910719A SE420623B SE 420623 B SE420623 B SE 420623B SE 7910719 A SE7910719 A SE 7910719A SE 7910719 A SE7910719 A SE 7910719A SE 420623 B SE420623 B SE 420623B
Authority
SE
Sweden
Prior art keywords
cardable
austenitic
exception
aluminum steel
steel
Prior art date
Application number
SE7910719A
Other languages
Swedish (sv)
Other versions
SE7910719L (en
Inventor
F G S Angel
N G E Malmgren
B Solly
Original Assignee
Fagersta Ab
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Fagersta Ab filed Critical Fagersta Ab
Priority to SE7910719A priority Critical patent/SE420623B/en
Priority to EP19800850186 priority patent/EP0031800B1/en
Priority to DE8080850186T priority patent/DE3065923D1/en
Priority to ES498616A priority patent/ES498616A0/en
Priority to JP18949080A priority patent/JPS56105457A/en
Publication of SE7910719L publication Critical patent/SE7910719L/en
Publication of SE420623B publication Critical patent/SE420623B/en

Links

Classifications

    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/18Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40Ferrous alloys, e.g. steel alloys containing chromium with nickel

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)
  • Heat Treatment Of Sheet Steel (AREA)
  • Sealing Battery Cases Or Jackets (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
  • Gasket Seals (AREA)
  • Exhaust Silencers (AREA)

Description

15 20 25 30 35 1919719-9 Stålet smältes i en 10-ton högfrekvensugn, göts i kokiller och valsades till trâdämnen. Dessa har ämnesbehand- lats och valsats till tråd 0 6.0 mm av charge 3423-71 och 0 5.6 mm av charge #029-71. Normal glödgning vid 105000, bet- ning och syning har utförts innan tråden dragits. 15 20 25 30 35 1919719-9 The steel was melted in a 10-ton high-frequency furnace, cast in molds and rolled into wire blanks. These have been blank treated and rolled to wire 0 6.0 mm of charge 3423-71 and 0 5.6 mm of charge # 029-71. Normal annealing at 105000, pickling and sewing have been carried out before the wire is pulled.

Som jämförelse har en charge (3226-71) tillverkats på samma sätt i stål av typ 17-7 PHÅAISI 631), vilket_är ett ut- skiljningshärdande Cr-Ni-Al-stål med följande analys.For comparison, a batch (3226-71) has been manufactured in the same way in steel of type 17-7 PHÅAISI 631), which is a precipitation hardening Cr-Ni-Al steel with the following analysis.

Tabell 2 ___ë_Cha1"e E §iM_H-_Pi § 02 111212 H flLi 3226-71 .073 .74 .74 .013 .006 16.4 7.1 .l5 .0Ul .QR .09 Charge 3423-71 enligt tabell l och charge 3226-71 har dragits från valstråd 0 6.0 mm i enkeldrag. Brottgräns (Rm), sträckgräns (Re) och kontraktion (Z) jämföres i bifogade fig. l. Som synes ökar sträck- och brottgräns långsammare för le- geringen enligt uppfinningen (heldragen linje) vilket medför att dragbarheten mätt som areareduktíon ökar från 75% till 92%. Dessutom är duktiliteten mätt som kontraktion hela ti- den högre för legeringen enligt uppfinningen särskilt vid större reduktioner. Anmärkningsvärt är att materialet saknar spänningssprickor vid en så stor areareduktion som 92% jäm- fört med 17-7 PH där risken för spänningssprickor finns redan vid 45% reduktion.Table 2 ___ ë_Cha1 "e E §iM_H-_Pi § 02 111212 H fl Li 3226-71 .073 .74 .74 .013 .006 16.4 7.1 .l5 .0Ul .QR .09 Charge 3423-71 according to table l and charge 3226-71 The breaking limit (Rm), yield strength (Re) and contraction (Z) are compared in the attached Fig. 1. As can be seen, the yield strength and yield strength increase more slowly for the alloy according to the invention (solid line) which In addition, the ductility measured as contraction is always higher for the alloy according to the invention, especially at larger reductions. It is noteworthy that the material lacks stress cracks at as large an area reduction as 92%. brought with 17-7 PH where the risk of stress cracks is already at 45% reduction.

Den utskiljningshärdande effekten hos legeringen enligt uppfinningen har provats vid två olika reduktioner och givit resultaten enligt aabell 3 nedan.The precipitation hardening effect of the alloy according to the invention has been tested at two different reductions and has given the results according to Table 3 below.

Tabell 3 Rm N/mmz Re N/mmz Charge Dimension Reduktion Oanlöpt Anlöpt Oanlöpt Anlöpt mm % 0 3423-71 2.68 80.0 1810 1995 1830 1855 4029-71 1.83 89.4 2116 2525 1976 2357 Anlöpningstemperatur 95000 under 30 minuter.Table 3 Rm N / mmz Re N / mmz Charge Dimension Reduction Tempered Tempered Tempered Tempered mm% 0 3423-71 2.68 80.0 1810 1995 1830 1855 4029-71 1.83 89.4 2116 2525 1976 2357 Temperature temperature 95000 for 30 minutes.

Sçm synes får man en anlöpningseffekt på ca. 200 N/mm2 för charge 3423-71 och ca. 400 N/mmz för charge 4029-71. Den stora skillnaden mellan dessa effekter förklaras av att charge 3H23-71 ej.har reducerats tillräckligt före anlöpning, d.v.s. austeniten har ej i tillräcklig grad omvandlats till martensit. 1a' 15 20. 25 30 7910719-9 5 ° n Legeringen enligt uppfinningen har främst tagits fram- för att förbättra kallbearbetbarheten hos utskiljningshärdan- de rostfria cr-Ni-Al-srál. inom ytan Aßcn i fig. 2 kan man rikta analysen så att man vid glödgning i temperaturområdet 600-950°C får en höjning av Ms-temperaturen genom karbidut- skiljning. Därefter kan materialet släckas och eventuellt ky- las till temperaturer under rumstemperatur för att få en om- vandling till martensit som sedan kan anlöpas.It seems that you get a tempering effect of approx. 200 N / mm2 for charge 3423-71 and approx. 400 N / mmz for charge 4029-71. The large difference between these effects is explained by the fact that charge 3H23-71 has not been reduced sufficiently before tempering, i.e. the austenite has not been sufficiently converted to martensite. 1a '15 20. 25 30 7910719-9 5 ° n The alloy according to the invention has mainly been developed to improve the cold workability of precipitation-curing stainless cr-Ni-Al-srál. within the surface Aßcn in Fig. 2, the analysis can be directed so that when annealing in the temperature range 600-950 ° C, an increase in the Ms temperature is obtained by carbide precipitation. Thereafter, the material can be quenched and possibly cooled to temperatures below room temperature to obtain a conversion to martensite which can then be annealed.

En intressant tillämpning är särskilt kallstukning då så låga brotthållfastheter som SUG-560 N/mmz har uppmätta på material som glödgats vid temperaturen 105000. Detta gäller båda chargerna 3423-71 och H029-71.An interesting application is particularly cold spreading when such low breaking strengths as SUG-560 N / mmz have been measured on materials annealed at the temperature 105000. This applies to both charges 3423-71 and H029-71.

Den tekniska effekten hos uppfinningen framgår av att dragbarheten väsentligt förbättras samtidigt som man behåller en utskiljningshärdande effekt. Pâ goda grunder kan man för- moda att den goda svetsbarheten kan förbättras med tillsatser av zirkonium och uran i stället för titan. Då legeringen har en mycket trög martensitomvandling i glödgat tillstånd kan materialet lagras och transporteras utomhus vid kall väderlek utan risk för spontan martensitbildning. _ Krom och nickel skall ligga inom ytan ABCD enligt fig. 2 där krom delvis kan ersättas av molybden med upp till max 2% enligt formeln Cr' (kromekvivalenten) = % Cr + % Mo, varjämte nickel kan delvis ersättas av mangan enligt formeln Ni' (nickel- ekvivalenten) = % Ni + 1/2 (% Mn - 1%). Vid den speciellt före- dragna utföringsformen skall krom- och nickelekvivalenterna Cr' och Ni' ligga inom ytan abcd i_figur~g¿ Legeringen enligt uppfinningen glödgas inom temperatur- området 600-950°C, släckes och kyles under rumstemperatur.The technical effect of the invention is apparent from the fact that the drawability is significantly improved while maintaining a precipitation hardening effect. On good grounds, it can be assumed that good weldability can be improved with the addition of zirconium and uranium instead of titanium. As the alloy has a very slow martensite conversion in the annealed state, the material can be stored and transported outdoors in cold weather without the risk of spontaneous martensite formation. Chromium and nickel must be within the surface ABCD according to Fig. 2 where chromium can be partially replaced by molybdenum by up to a maximum of 2% according to the formula Cr '(chromium equivalent) =% Cr +% Mo, and nickel can be partially replaced by manganese according to formula Ni '(nickel equivalents) =% Ni + 1/2 (% Mn - 1%). In the particularly preferred embodiment, the chromium and nickel equivalents Cr 'and Ni' should be within the surface of the figure. The alloy according to the invention is annealed in the temperature range 600-950 ° C, quenched and cooled below room temperature.

Legeringen kan sedan utskiljningshärdas.The alloy can then be hardened by precipitation.

Legeringen kan också snabbkylas direkt efter varmvaïs- ning och kallbearbetas och utskiljningshärdas därefter.The alloy can also be quenched immediately after hot forging and cold worked and precipitation hardened thereafter.

Claims (2)

7916719-9 Patentkrav7916719-9 Patent claims 1. Anstenitiskt, utskiljningshärdbart, rostfritt krom- nickel-aluminiumstål med god kallbearbetbarhet, k ä n n e - t e c k n a t av att krom-ekvivalenten Cr' definierad enligt for- meln Cr' = % Cr+% Mo ligger mellan 16,5% och 18,2% samt nickel- ekvivalenten Ni' definierad enligt formeln Ni' = % Ni + 1/2 . (% Mn- 1 %) ligger mellan 8,25% och 9,75% inom ytan abcd på bifo- gade ritningsfigur 2, varjämte stålet innehåller 10,5 - 18,2% Cr, 5,0 - 9,75% Ni, C upp till 0,15%, Si upp till 3,0%, Mn upp till 8,0%, P upp till 0,0#5%, S upp till 0,040%, Mo upp till 2,0%, N upp till 0,15%, 0,5 - 2,5% Al samt företrädesvis en eller flera av metallerna Ti, Zr och U upp till 2%, varvid resten utgöres av järn och i rostfria stål normalt förekommande föroreningar.Anstenitic, precipitation hardenable, stainless chromium-nickel-aluminum steel with good cold workability, characterized in that the chromium equivalent Cr 'defined according to the formula Cr' =% Cr +% Mo is between 16.5% and 18.2 % and the nickel equivalent Ni 'defined according to the formula Ni' =% Ni + 1/2. (% Mn- 1%) is between 8.25% and 9.75% within the surface abcd of the attached drawing figure 2, and the steel contains 10.5 - 18.2% Cr, 5.0 - 9.75% Ni , C up to 0.15%, Si up to 3.0%, Mn up to 8.0%, P up to 0.0 # 5%, S up to 0.040%, Mo up to 2.0%, N up to 0.15%, 0.5 - 2.5% Al and preferably one or more of the metals Ti, Zr and U up to 2%, the remainder being iron and stainless steel normally found in impurities. 2. Stål enligt krav 1, k ä n n e t e c k n a t av att det endera innehåller Ti upp till 0,5% eller Zr upp till 0,5% eller U upp till 1%.Steel according to claim 1, characterized in that it contains either Ti up to 0.5% or Zr up to 0.5% or U up to 1%.
SE7910719A 1979-12-28 1979-12-28 AUSTENITIC, EXCEPTION CARDABLE STAINLESS CHROME-NICKEL ALUMINUM STEEL SE420623B (en)

Priority Applications (5)

Application Number Priority Date Filing Date Title
SE7910719A SE420623B (en) 1979-12-28 1979-12-28 AUSTENITIC, EXCEPTION CARDABLE STAINLESS CHROME-NICKEL ALUMINUM STEEL
EP19800850186 EP0031800B1 (en) 1979-12-28 1980-12-10 Austenitic, precipitation hardenable stainless steel
DE8080850186T DE3065923D1 (en) 1979-12-28 1980-12-10 Austenitic, precipitation hardenable stainless steel
ES498616A ES498616A0 (en) 1979-12-28 1980-12-24 PROCEDURE FOR CONVERTING AUSTENITIC STEEL.
JP18949080A JPS56105457A (en) 1979-12-28 1980-12-27 Austenite type precipitation hardening antiirust steel

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
SE7910719A SE420623B (en) 1979-12-28 1979-12-28 AUSTENITIC, EXCEPTION CARDABLE STAINLESS CHROME-NICKEL ALUMINUM STEEL

Publications (2)

Publication Number Publication Date
SE7910719L SE7910719L (en) 1981-06-29
SE420623B true SE420623B (en) 1981-10-19

Family

ID=20339661

Family Applications (1)

Application Number Title Priority Date Filing Date
SE7910719A SE420623B (en) 1979-12-28 1979-12-28 AUSTENITIC, EXCEPTION CARDABLE STAINLESS CHROME-NICKEL ALUMINUM STEEL

Country Status (5)

Country Link
EP (1) EP0031800B1 (en)
JP (1) JPS56105457A (en)
DE (1) DE3065923D1 (en)
ES (1) ES498616A0 (en)
SE (1) SE420623B (en)

Families Citing this family (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
SE8102015L (en) * 1980-04-07 1981-10-08 Armco Inc FERRIT-FREE SEPARATION HARDENABLE STAINLESS STEEL
JPS5993856A (en) * 1982-11-18 1984-05-30 Nippon Seisen Kk Fine stainless steel wire
SE466265B (en) * 1990-05-29 1992-01-20 Uddeholm Tooling Ab EXCELLENT HANDLING TOOL STEEL
DE102005024029B3 (en) * 2005-05-23 2007-01-04 Technische Universität Bergakademie Freiberg Austenitic lightweight steel and its use
DE102005030413C5 (en) * 2005-06-28 2009-12-10 Technische Universität Bergakademie Freiberg High-strength austenitic-martensitic lightweight steel and its use
DE102006033973A1 (en) * 2006-07-20 2008-01-24 Technische Universität Bergakademie Freiberg Stainless austenitic cast steel and its use
CN100464000C (en) * 2007-06-12 2009-02-25 江阴康瑞不锈钢制品有限公司 Austenite cold-forged stainless-steel and steel wire making method
JP5744678B2 (en) * 2010-10-07 2015-07-08 新日鐵住金ステンレス株式会社 Precipitation hardening type metastable austenitic stainless steel wire excellent in fatigue resistance and method for producing the same
CN102747307A (en) * 2012-06-06 2012-10-24 兰州理工大学 High aluminum stainless steel sheet material and rolling method
CN103447348A (en) * 2013-07-25 2013-12-18 张家港市胜达钢绳有限公司 Manufacturing method of stainless steel wire
SE541925C2 (en) 2018-04-26 2020-01-07 Suzuki Garphyttan Ab A stainless steel

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2505762A (en) * 1946-09-06 1950-05-02 Armco Steel Corp Stainless steel and method
US3117861A (en) * 1956-11-14 1964-01-14 Armco Steel Corp Stainless steel and article
US3253908A (en) * 1959-11-20 1966-05-31 Armco Steel Corp Stainless steel and method
US3071460A (en) * 1959-11-20 1963-01-01 Armco Steel Corp Stainless steel composition
US3347663A (en) * 1964-09-23 1967-10-17 Int Nickel Co Precipitation hardenable stainless steel
US3408178A (en) * 1967-06-27 1968-10-29 Carpenter Steel Co Age hardenable stainless steel alloy

Also Published As

Publication number Publication date
SE7910719L (en) 1981-06-29
EP0031800A1 (en) 1981-07-08
ES8206655A1 (en) 1982-08-01
EP0031800B1 (en) 1983-12-14
DE3065923D1 (en) 1984-01-19
ES498616A0 (en) 1982-08-01
JPS56105457A (en) 1981-08-21

Similar Documents

Publication Publication Date Title
CN108220821B (en) High-strength austenitic stainless steel alloy material and preparation method thereof
EP0249117A2 (en) A process for preparing a crevice corrosion-resistant non-magnetic steel
SE420623B (en) AUSTENITIC, EXCEPTION CARDABLE STAINLESS CHROME-NICKEL ALUMINUM STEEL
JP2954922B1 (en) Heat treatment method for precipitation hardening high silicon steel products
CN104726789B (en) Low nickel stainless steel
Abbasi et al. Improvement of mechanical properties of Cr-Ni-Mo-Cu-Ti stainless steel with addition of vanadium
JP5291479B2 (en) Duplex stainless steel and steel and steel products using the same
JPH0382741A (en) Shape memory staiinless steel excellent in stress corrosion cracking resistance and shape memory method therefor
US4259126A (en) Method of making razor blade strip from austenitic steel
JPH0320408A (en) Production of high tensile steel stock excellent in toughness at low temperature
JPH11209851A (en) Gas turbine disk material
JPH05311345A (en) Ferritic heat resistant steel excellent in high temperature strength and toughness
JPH11117019A (en) Production of heat resistant parts
JPH0579727B2 (en)
JP2000273580A (en) Steel for cold heading excellent in cold workability and production therefor
JP2021165431A (en) Steel sheet and method for producing the same
JP3775371B2 (en) Low alloy steel
JPH05311342A (en) Ferritic heat resistant steel excellent in creep strength
JP2625572B2 (en) Heat treatment method for cast steel products
JPH07110970B2 (en) Method for producing acicular ferritic stainless steel with excellent resistance to stress corrosion cracking
JPH09291308A (en) Production of high chrome ferritic heat resistant steel
SU852945A1 (en) Method of thermal treatment of stainless martensite aged steels
JPS61147812A (en) Production of high strength steel superior in delayed breaking characteristic
JPH05311344A (en) Ferritic heat resistant steel excellent in high temperature strength and toughness
JP3587271B2 (en) Semi-austenite precipitation hardened stainless steel with excellent cold workability

Legal Events

Date Code Title Description
NAL Patent in force

Ref document number: 7910719-9

Format of ref document f/p: F