WO2003056052A1 - Acier austenitique durcissant par precipitation - Google Patents

Acier austenitique durcissant par precipitation Download PDF

Info

Publication number
WO2003056052A1
WO2003056052A1 PCT/SE2002/002299 SE0202299W WO03056052A1 WO 2003056052 A1 WO2003056052 A1 WO 2003056052A1 SE 0202299 W SE0202299 W SE 0202299W WO 03056052 A1 WO03056052 A1 WO 03056052A1
Authority
WO
WIPO (PCT)
Prior art keywords
weight
content
strength
heat treatment
precipitation hardenable
Prior art date
Application number
PCT/SE2002/002299
Other languages
English (en)
Inventor
Gustaf Zetterholm
Håkan HOLMBERG
Original Assignee
Sandvik 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 Sandvik Ab filed Critical Sandvik Ab
Priority to AU2002360028A priority Critical patent/AU2002360028A1/en
Publication of WO2003056052A1 publication Critical patent/WO2003056052A1/fr

Links

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
    • C22C38/02—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
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • 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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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

Definitions

  • Precipitation har enable austenitic steel.
  • the present invention relates to an austenitic stainless steel alloy, more precisely a high-strength precipitation hardenable austenitic stainless steel alloy containing a well balanced aluminium content and a high silicon content, a product which is reduced by cold working, especially drawing, without intermediate heat treatment, the strength of which increases through final heat treat- ment at 300 °C to 500 °C by not less than 14 %, which shows a loss of force that is lower than 3.0 % at 1400 N during 24 hours for use in spring applications, such as springs of round wire and strip steel and in medical applications, such as surgical and dental instruments.
  • the cold-worked austenitic stainless springsteels of type AISI 302 assume a dominating position. This is based on a combination of relatively good corrosion resistance and a possibility to cold- work the material to a considerable strength, which is a prerequisite for a good spring material. Based on the cold-worked state, the mechanical properties may be increased additionally by means of a simple heat treatment. Steel of the type AISI 631 is alloyed with aluminium in order to additionally enhance the increase of strength at heat treatment. During cold-working, a transformation takes place from the annealed structure's principal constituent of austenite to deformation martensite, which is harder than the phase from which it is formed.
  • These steels are higher alloyed and have a lower carbon content than steels of the type AISI 302 and AISI 631. This entails that a higher rate of reduction can be allowed in this type of steel.
  • the disadvantage of these steels is that the resulting product properties that are essential for a good spring function frequently are worse than for steels of AISI 302 and AISI 631.
  • One example of such a property is the resistance to relaxation, which describes the ability of a spring to retain spring strength over time.
  • the alloy according to US-A-6 048 416 contains no precipitation-hardening element. Summary of the Invention
  • Figure 1 shows the loss of feree of the springs after 24 hours of materials according to the invention compared with AISI 302 and charge no. 150725.
  • Figure 2 shows the ultimate tensile strength of materials according to the invention compared with AISI 302* (* - with intermediate heat treatment) and charge no. 150725.
  • Figure 3 shows the ultimate tensile strength as a logarithmic func- tion of the cumulative reduction rate of materials according to the invention compared with charge no. 150725.
  • Figure 4 shows schematically a segment of a possible embodiment of an expanding ring in a side view.
  • Figure 5 shows in Figure 5a the ring seen from above. The ends are pressed against each other by the force F, in Figure 5b the ring is shown seen from the side, the ends being pressed against each other by the force F and in Figure 5c a part of the expanding ring is shown that constitutes a flat spring element and how this is influenced by the force F.
  • Figure 6 shows different embodiments for strip springs.
  • Carbon (C) has a high propensity to combine with chromium which means that chromium carbides is precipitated in the crystal grain boundaries, whereby the surrounding the bulk is depleted of chromium.
  • the corrosion properties of the material deteriorate, problems also arise with embrit- tlement that foremost causes problem when the wire is shaped to springs. Therefore, the carbon content should be held at as low a level as possible, maximum 0.07 weight-%, preferably 0.025 weight-%.
  • Silicon (Si) has a ferrite-stabilising effect, which entails that too a high silicon content produces a two-phase structure. Therefore, the silicon content should not exceed 3.0 weight-%.
  • the silicon content should not be lower than 0,5 weight-% and should be in the range of 0.5 to 3.0 weight-%, preferably between 0.5 and 2.5 weight-%, most preferably 0.5 to 1.5 weight-%.
  • Nitrogen (N) is an alloying element that together with aluminium forms non- desirable brittle slags in the form of aluminium nitrides. Further, nitrogen increases the deformation-hardening at cold-working, which is a disadvantage in the present invention. Therefore, it is of highest importance that the nitrogen content is held on as low a level as possible, maximum 0.1 weight-%, preferably 0.05 weight-%.
  • Chromium (Cr) is a very important alloying element what concerns the corrosion resistance of the material. This is due to the ability of chromium to form a passive layer of Cr 2 ⁇ 3 on the surface of the steel. In order for that passive layer to form, it is required that the chromium content exceeds approximately 12.0 weight-%, in addition, the corrosion resistance increases with added chromium content. Another advantage of chromium is that the austenitic structure of the material is stabilized against transition to martensite at cold-working. However, chromium is ferrite-stabilising, and therefore the content should not be too high. Therefore, in the alloy according to the present invention the chromium content should not be lower than 15.0 weight-% and not be higher than 20.0 weight-%, preferably be in the range of 16.0 to 19.0 weight-%.
  • Nickel (Ni) is an alloying element that in a sufficient amount guarantees that the material gets an austenitic structure at room temperature. Furthermore, the ductility is improved with an increased nickel content. However, nickel is an expensive alloying element and high contents entail a slow deformation-hardening, which in its turn entails difficulties to attain a sufficient strength. There- fore, the nickel content should be within the range of 7.0 till12.0 weight-%, preferably between 8.0 tilh 1.0 weight-%, most preferably within the range of 9.0 to 10.0 weight-%.
  • Aluminium is a central alloying element in the present invention. Aluminium is added as a precipitation hardening element in order to increase the strength, which in turn influences the relaxation resistance. During precipitation-hardening at 350-500 °C of the cold-worked wire, precipitations in the form of ⁇ -NiAL are formed, which improves the mechanical properties unlike materials known until now. This effect is of highest importance when the wire is to be used as springs, the relaxation resistance of which has to meet very high requirements.
  • a disadvantage of aluminium is that it is ferrite-stabilizing, for what reason the aluminium content should be limited to maximum 1.5 weight-%. However, in the light of the above-mentioned, the aluminium content should be at least 0.25 weight-% and preferably be in the range of 0.4-1.0 weight-%.
  • Copper (Cu) is an alloying element that has two important properties. Firstly, copper is an austenite-stabilizing element and secondly copper decreases the deformation-hardening of the material and entails improved ductility. Since the material has to withstand extreme reductions without intermediate annealings, the copper content has to be as high as possible. However, with an increasing copper content, the risk of unwanted precipitations increases, which decreases the ductility of the material. Therefore, the copper content should be in the range of 0 ⁇ Cu > 4.0 weight-%, preferably between 2.0 to 3.5 weight-%, most preferably between 2.4 to 3.0 weight-%.
  • Manganese (Mn) has similar effect as nickel, both with regard to forming austenite at setting as well as stabilizing the same against transformation into martensite at cold-working. However, manganese increases the deformation- hardening, which nickel does not. This results in a faster deformation-hardening and diminishes the greatest possible reduction rate between the annealings. Therefore, the manganese content should be limited to maximum 3.0 weight-%, preferably to 1.0 weight-%.
  • Molybdenum (Mo) is a ferrite-stabilizing element that has a strongly favourable effect on the corrosion resistance in chloride environments.
  • Established PRE (Pitting Resistance Equivalent) formulas allocate molybdenum a factor of «3 in comparison with the effect of chromium.
  • a high molybdenum content stabilises the ferrite phase in the steel.
  • Titanium (Ti) is, like aluminium, a precipitation-hardening element that is added in order to increase the strength, which in turn influences the relaxation resistance. Furthermore, titanium together with silicon gives a strong heat treatment effect already at low contents of titanium. However, titanium is strongly ferrite- stabilizing, for what reason the content should not be too high. Therefore, the titanium content is limited up to 1.0 weight-%, preferably maximum 0.75 weight- %.
  • test materials were produced by melting in a high frequency furnace. Subsequently, all test ingots were fully ground before they were forged. Forging was performed on the ingot to 103 x 103 mm length in stock. The heating tempera- ture was in the range between 1240 °C and 1260 °C. The holding time at full temperature was 1 h. At the subsequent blank treatment, the blanks were fully ground and ultrasonically tested.
  • the wire rod in the dimension range of 0 5.50 mm - 0 5.60 mm was produced by warming the blanks to 1200 °C-1240 °C, whereupon they were rolled to final dimension and then cooled by water quenching. The hot-rolled wires were then cold-worked by drawing in a conventional drawing machine.
  • the chemical composition, in weight-%, of the alloys in the test program and reference materials are given in Table 1.
  • the heat treatment was accomplished with the same purpose as for spring steel of the type AISI 302, when an increase of the mechanical properties is obtained. Thereby, several important spring properties, such as, for example, the relaxation resistance, are influenced but in a stronger way than known hitherto. Table 2. Ultimate tensile strength before and after heat treatment.
  • the relaxation test was accomplished by loading blued springs with a constant load. The load was read each minute under the first five minutes and then the number of read-outs was cut down. Each test was stopped after twenty-four hours. Springs from the respective charge were loaded initially on four different levels. The relaxation was calculated by means of equation 3 and the results are summarised in Figure 1.
  • Equation 3 ((F 1 -F 2 )/F 1 )*100
  • the steel according to the present invention is subjected to a strong cold deformation. It can be shaped to different cross-section geometries, for example, round, oval wire, profiles of different cross-sections, for example, rectangular, triangular or more complicated embodiments and geometries. Round wire may even be flat-rolled.
  • Example 1 Springs of round wire
  • springs of wire made from the alloy according to invention are wound. These springs have good spring properties in the form of relaxation, i.e. the retention of spring force under a long period and are advantageously used in typical spring applications, such as, for instance, springs in locking applications, i.e. mechanical parts in the locking device, springs in aerosol containers, pens, especially ball point pens, pump springs, springs in indus- trial looms, springs in the vehicle industry, electronics, computers and fine mechanics.
  • springs in locking applications i.e. mechanical parts in the locking device
  • springs in aerosol containers, pens, especially ball point pens, pump springs, springs in indus- trial looms springs in the vehicle industry, electronics, computers and fine mechanics.
  • the torque is a decisive quantity.
  • the torque can be expressed as
  • T spring strip thickness
  • n number of working turns
  • a so-called reverse winding may be accomplished.
  • the spring is preformed by being wound in a direction opposite the working direction. Then a heat treatment of the spring takes place, after which it is wound-in in the opposite direction in the spring housing.
  • the strip is formed on a tack, after which heat treatment takes place. Then the spring is wound in the opposite direction into the spring housing.
  • An expander is a bit of wire, which is corrugated and shaped to a flat spring connected in series. This spring is used, for instance, in order to regulate the pressure of the oil scraper rings against the cylinder wall in an internal combustion engine.
  • a typical expander for car motors is seen as the corrugated wire between two piston rings.
  • a possible embodiment of such a corrugated ring is shown schematically in Figure 4.
  • a drawback of motor-driven vehicles today is the great energy con- sumption that is necessary in order to give the vehicle the desired performance thereof.
  • the easiest ways to achieve a reduced energy consumption is, among other things, to diminish the internal friction of the drive and to reduce the total mass of the vehicle.
  • the piston core accounts for more than half of the friction of a motor. Therefore, it is a continuous aim to improve the material and preci- sion of the rings, pistons and cylinder walls with the purpose of reducing tare weights and bearing pressure.
  • the expander is the spring that regulates the pressure of the oil scraper rings against the cylinder wall and thereby also oil consumption and part of the internal friction of a motor.
  • the load of the expander wire consists of the force F, as shown in Figures 5a to 5c.
  • Expression (3) shows that the wire thickness that is required for a given property depends on the design of the expander. If the allowed tension of the material is increased, a smaller bending radius can be allowed, which is of great interest since rings of smaller types can be manufactured. The possibility of being able to manufacture smaller rings becomes more and more important since the demand for small motors increases as the environmental requirements are raised.
  • Expression (4) shows that a certain elastic energy for given modulus of elasticity is a function of the specific volume, material use and allowed maximum tension. An increased maximal allowed tension increases as a rule the material- use constant, which in combination gives a major impact on the required specific volume. Thus, it is possible to diminish the material volume increased allowed tension for retained level of elastic energy.
  • the material may be formed in a relatively soft state so as to later be heat treated in the finished form, whereupon the desired spring properties are obtained by precipitation hardening.
  • This embodiment according to the present invention is used especially in applications that make great demands on the relaxation properties of the steel, since it should resist a force without being preformed.
  • Example 5 Round and flat wire as well as strip steel for medical applications
  • Wire, manufactured from the alloy according to invention may even be used in medical applications, for instance, in the form of dental instruments as files, such as root canal files, nerve extractor and the like, as well as surgical nee- dies.
  • Flat-rolled wire of the steel according to invention may advantageously be used for the production of dental and surgical instruments.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Heat Treatment Of Steel (AREA)
  • Materials For Medical Uses (AREA)
  • Dental Preparations (AREA)
  • Dental Tools And Instruments Or Auxiliary Dental Instruments (AREA)
  • Preventing Corrosion Or Incrustation Of Metals (AREA)
  • Springs (AREA)
  • Heat Treatment Of Articles (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)

Abstract

La présente invention concerne un alliage d'acier inoxydable, plus particulièrement un alliage inoxydable austénitique, durcissant par précipitation et hautement résistant, contenant une quantité bien appropriée d'aluminium, et une forte teneur en silicium. La composition de cet alliage donne les proportions pondérales (en %) suivantes: C 0-0,07; Si 0,5-3,0; N 0-0,1; Cr 15,0-20,0; Ni 7,0-12,0; Al 0,25-1,5; Cu: 0≤Cu≤4,0; Mn 0-3,0; Mo 0-2,0; Ti 0-1,0; le complément à 100 étant assuré par Fe avec les impuretés et additifs habituels. L'invention concerne également un produit qui est réduit par traitement à froid, plus particulièrement par emboutissage, la résistance augmentant par traitement thermique final entre 300 °C et 500 °C. Cette augmentation n'est jamais inférieure à 14 %, la perte de force étant inférieure à 3 % à 1400N pendant 24H. Cet acier convient particulièrement pour les ressorts en fil rond ou en bandes d'acier, et pour des applications médicales telles que les instruments chirurgicaux et de dentisterie.
PCT/SE2002/002299 2001-12-11 2002-12-11 Acier austenitique durcissant par precipitation WO2003056052A1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
AU2002360028A AU2002360028A1 (en) 2001-12-11 2002-12-11 Precipitation hardenable austenitic steel

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
SE0104192A SE526881C2 (sv) 2001-12-11 2001-12-11 Utskiljningshärdbar austenitisk legering, användning av legeringen samt framställning av en produkt av legeringen
SE0104192-0 2001-12-11

Publications (1)

Publication Number Publication Date
WO2003056052A1 true WO2003056052A1 (fr) 2003-07-10

Family

ID=20286302

Family Applications (2)

Application Number Title Priority Date Filing Date
PCT/SE2002/002299 WO2003056052A1 (fr) 2001-12-11 2002-12-11 Acier austenitique durcissant par precipitation
PCT/SE2002/002300 WO2003056053A1 (fr) 2001-12-11 2002-12-11 Acier austenitique durcissable par precipitation

Family Applications After (1)

Application Number Title Priority Date Filing Date
PCT/SE2002/002300 WO2003056053A1 (fr) 2001-12-11 2002-12-11 Acier austenitique durcissable par precipitation

Country Status (10)

Country Link
US (2) US20050126661A1 (fr)
EP (1) EP1472383B1 (fr)
JP (1) JP4327601B2 (fr)
KR (1) KR100966068B1 (fr)
AT (1) ATE360104T1 (fr)
AU (2) AU2002360028A1 (fr)
BR (1) BR0214816B1 (fr)
DE (1) DE60219693T2 (fr)
SE (1) SE526881C2 (fr)
WO (2) WO2003056052A1 (fr)

Families Citing this family (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20060266439A1 (en) * 2002-07-15 2006-11-30 Maziasz Philip J Heat and corrosion resistant cast austenitic stainless steel alloy with improved high temperature strength
DE102005024029B3 (de) * 2005-05-23 2007-01-04 Technische Universität Bergakademie Freiberg Austenitischer Leichtbaustahl und seine Verwendung
PL2136089T3 (pl) * 2008-06-16 2011-04-29 Gally S P A Nakrętka samozakleszczająca się
IT1396294B1 (it) * 2009-10-05 2012-11-16 Gally S P A Dadi autobloccanti
JP6259579B2 (ja) * 2012-03-29 2018-01-10 新日鐵住金ステンレス株式会社 耐熱へたり性に優れた高強度ステンレス鋼線、高強度ばね並びにその製造方法
KR101420782B1 (ko) * 2013-12-30 2014-07-17 광일토건환경 주식회사 흙막이 가시설 시공방법
JP6747639B2 (ja) * 2014-08-28 2020-09-02 国立大学法人豊橋技術科学大学 金属材料および加工処理方法
AT516453B1 (de) * 2014-11-03 2018-02-15 Berndorf Band Gmbh Metallische Bänder und deren Herstellungsverfahren
AT516464B1 (de) * 2014-11-03 2018-02-15 Berndorf Band Gmbh Metallische Bänder und deren Herstellungsverfahren
CN105483502A (zh) * 2015-12-03 2016-04-13 浙江腾龙精线有限公司 一种弹簧线的生产方法
CN108977727A (zh) * 2018-06-29 2018-12-11 柳州市横阳机械有限公司 不锈钢丝的制备方法
CN112941423A (zh) * 2019-11-26 2021-06-11 上海微创医疗器械（集团）有限公司 医用合金及支架
CN114959423B (zh) * 2022-06-07 2023-04-14 甘肃酒钢集团宏兴钢铁股份有限公司 一种高硅含钛奥氏体不锈钢的冶炼方法

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3910788A (en) * 1973-04-21 1975-10-07 Nisshin Steel Co Ltd Austenitic stainless steel
EP0735154A1 (fr) * 1995-03-31 1996-10-02 Nippon Yakin Kogyo Co., Ltd. Aciers austénitiques inoxydables pour moulage à pression
JP2001081535A (ja) * 1999-09-16 2001-03-27 Nisshin Steel Co Ltd 成形性および熱間加工性に優れたプレス成形用オーステナイト系ステンレス鋼および鋼板

Family Cites Families (24)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2553330A (en) * 1950-11-07 1951-05-15 Carpenter Steel Co Hot workable alloy
US3282686A (en) * 1965-02-01 1966-11-01 Armco Steel Corp Stainless steel and articles
US3282684A (en) * 1963-07-31 1966-11-01 Armco Steel Corp Stainless steel and articles
US3362813A (en) * 1964-09-15 1968-01-09 Carpenter Steel Co Austenitic stainless steel alloy
US3357868A (en) * 1964-11-17 1967-12-12 Armco Steel Corp Stainless steel and method
US3376780A (en) * 1966-09-19 1968-04-09 Armco Steel Corp Stainless steel, products and method
US3408178A (en) * 1967-06-27 1968-10-29 Carpenter Steel Co Age hardenable stainless steel alloy
US3957545A (en) * 1970-07-28 1976-05-18 Nippon Kokan Kabushiki Kaisha Austenitic heat resisting steel containing chromium and nickel
US3969109A (en) * 1974-08-12 1976-07-13 Armco Steel Corporation Oxidation and sulfidation resistant austenitic stainless steel
SE419102C (sv) * 1974-08-26 1985-12-23 Avesta Ab Anvendning av ett kromnickelstal med austenitisk struktur till konstruktioner som erfordrar hog extrem krypbestendighet vid konstant temperatur upp till 1200?59c
US4102225A (en) * 1976-11-17 1978-07-25 The International Nickel Company, Inc. Low chromium oxidation resistant austenitic stainless steel
US4218268A (en) * 1977-06-30 1980-08-19 Kubota Ltd. High corrosion resistant and high strength medium Cr and low Ni stainless cast steel
JPS54120223A (en) * 1978-03-11 1979-09-18 Kawasaki Steel Co Production of stainless steel spring material with fatigue resistance
JPS59162254A (ja) * 1983-03-01 1984-09-13 Takeshi Masumoto 加工性に優れたＦｅ基合金材料
JPS6036649A (ja) * 1983-08-05 1985-02-25 Nisshin Steel Co Ltd 靭性に優れたマルテンサイト系析出硬化型ステンレス鋼
EP0273279B1 (fr) * 1986-12-30 1993-10-27 Nisshin Steel Co., Ltd. Procédé pour la fabrication de rubans d'acier inoxydable au chrome à structure biphasée ayant une résistance et un allongement élevés ainsi qu'une anisotropie réduite
TW290592B (fr) * 1993-07-08 1996-11-11 Asahi Seiko Co Ltd
US5496421A (en) * 1993-10-22 1996-03-05 Nkk Corporation High-strength martensitic stainless steel and method for making the same
DE4498699T1 (de) * 1993-11-09 1996-01-25 Nisshin Steel Co Ltd Rostfreier Stahl mit ausgezeichnetem Korrosionswiderstand gegenüber Schmelzsalz sowie Verfahren zur Herstellung dieses Stahls
JPH07138704A (ja) * 1993-11-12 1995-05-30 Nisshin Steel Co Ltd 高強度高延性複相組織ステンレス鋼およびその製造方法
US5411513A (en) * 1994-02-24 1995-05-02 Danek Medical, Inc. Transmission mechanism for a surgical cutting instrument
JPH08104953A (ja) * 1994-08-11 1996-04-23 Nisshin Steel Co Ltd 抗菌性を有するオーステナイト系ステンレス鋼
US5681528A (en) * 1995-09-25 1997-10-28 Crs Holdings, Inc. High-strength, notch-ductile precipitation-hardening stainless steel alloy
MY118759A (en) * 1995-12-15 2005-01-31 Nisshin Steel Co Ltd Use of a stainless steel as an anti-microbial member in a sanitary environment

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3910788A (en) * 1973-04-21 1975-10-07 Nisshin Steel Co Ltd Austenitic stainless steel
EP0735154A1 (fr) * 1995-03-31 1996-10-02 Nippon Yakin Kogyo Co., Ltd. Aciers austénitiques inoxydables pour moulage à pression
JP2001081535A (ja) * 1999-09-16 2001-03-27 Nisshin Steel Co Ltd 成形性および熱間加工性に優れたプレス成形用オーステナイト系ステンレス鋼および鋼板

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
DATABASE WPI Week 200133, Derwent World Patents Index; Class M27, AN 2001-314036 *

Also Published As

Publication number Publication date
EP1472383A2 (fr) 2004-11-03
WO2003056053B1 (fr) 2004-04-08
AU2002358375A1 (en) 2003-07-15
AU2002360028A1 (en) 2003-07-15
US20050126661A1 (en) 2005-06-16
DE60219693T2 (de) 2007-12-27
EP1472383B1 (fr) 2007-04-18
DE60219693D1 (de) 2007-05-31
KR100966068B1 (ko) 2010-06-28
JP4327601B2 (ja) 2009-09-09
SE0104192L (sv) 2003-06-12
WO2003056053A1 (fr) 2003-07-10
SE526881C2 (sv) 2005-11-15
ATE360104T1 (de) 2007-05-15
JP2005513273A (ja) 2005-05-12
BR0214816A (pt) 2004-08-31
KR20040061028A (ko) 2004-07-06
SE0104192D0 (sv) 2001-12-11
US20070041863A1 (en) 2007-02-22
BR0214816B1 (pt) 2011-02-08

Similar Documents

Publication Publication Date Title
US20070041863A1 (en) Precipitation hardenable austenitic steel
JP5215855B2 (ja) Ｆｅ基合金及びその製造方法
CA2079734C (fr) Acier a ressort a haute resistance
EP1803831A2 (fr) Pièce en acier microalliée nitrocarburisée
EP1154027A1 (fr) Fil en alliage resistant a la chaleur
EP1236809A2 (fr) Acier inoxydable martensitique à haute dureté, ayant une bonne résistance à la corrossion
US20050016645A1 (en) Co-Ni-base alloy
EP0838533A1 (fr) Alliage réfractaire pour soupape d'échappement et procédé pour la fabrication de la soupape d'échappement
EP1449933B1 (fr) Courroie de transmission
EP1801255A1 (fr) Fil d'acier à ressort formable à froid présentant une aptitude à la coupe à froid et des propriétés de fatigue excellentes, et son procédé de fabrication
EP0657558B1 (fr) Superalliage à base de Fe
EP1469093A1 (fr) Fil d'acier pour ressorts thermoresistants, ressorts thermoresistants, et procede de production de ressorts thermoresistants
CN116075600A (zh) 奥氏体不锈钢及其制造方法
JP2000017395A (ja) Ｆｅ系形状記憶合金及びその製造方法
JPH0796697B2 (ja) 高強度ばね用鋼
JPH05148581A (ja) 高強度ばね用鋼および高強度ばねの製造方法
JP4057208B2 (ja) 良好な冷間加工性及び高温強度を具備したエンジンバルブ用Ｆｅ基耐熱合金
JPH1180906A (ja) 降伏応力を高めた高強度ステンレス鋼帯およびその製造方法
JP3216837B2 (ja) 耐熱ボルト用鉄基超耐熱合金
JP2003138330A (ja) 銅系合金及びその製造方法
JP2000063947A (ja) 高強度ステンレス鋼の製造方法
JPH07138680A (ja) 耐焼付性，耐摩耗性に優れた摺動材料用アルミニウム青銅
JP3387235B2 (ja) 析出硬化型ステンレス鋼
JP2002206147A (ja) 優れた冷間加工性と高い疲労強度をもつ析出硬化型マルテンサイト系鋼及びその製造方法
JP3216824B2 (ja) 高強度低熱膨張合金

Legal Events

Date Code Title Description
AK Designated states

Kind code of ref document: A1

Designated state(s): AE AG AL AM AT AU AZ BA BB BG BR BY BZ CA CH CN CO CR CU CZ DE DK DM DZ EC EE ES FI GB GD GE GH GM HR HU ID IL IN IS JP KE KG KP KR KZ LC LK LR LS LT LU LV MA MD MG MK MN MW MX MZ NO NZ OM PH PL PT RO RU SD SE SG SK SL TJ TM TN TR TT TZ UA UG US UZ VN YU ZA ZM ZW

AL Designated countries for regional patents

Kind code of ref document: A1

Designated state(s): GH GM KE LS MW MZ SD SL SZ TZ UG ZM ZW AM AZ BY KG KZ MD RU TJ TM AT BE BG CH CY CZ DE DK EE ES FI FR GB GR IE IT LU MC NL PT SE SI SK TR BF BJ CF CG CI CM GA GN GQ GW ML MR NE SN TD TG

121 Ep: the epo has been informed by wipo that ep was designated in this application
DFPE Request for preliminary examination filed prior to expiration of 19th month from priority date (pct application filed before 20040101)
122 Ep: pct application non-entry in european phase
NENP Non-entry into the national phase

Ref country code: JP

WWW Wipo information: withdrawn in national office

Country of ref document: JP