EP0738783B1 - Acier inoxydable austénitique pour l'élaboration notamment de fil - Google Patents

Acier inoxydable austénitique pour l'élaboration notamment de fil Download PDF

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Publication number
EP0738783B1
EP0738783B1 EP96400736A EP96400736A EP0738783B1 EP 0738783 B1 EP0738783 B1 EP 0738783B1 EP 96400736 A EP96400736 A EP 96400736A EP 96400736 A EP96400736 A EP 96400736A EP 0738783 B1 EP0738783 B1 EP 0738783B1
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EP
European Patent Office
Prior art keywords
inclusions
steel
less
composition
mgo
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Revoked
Application number
EP96400736A
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German (de)
English (en)
French (fr)
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EP0738783A1 (fr
Inventor
Frédéric Descaves
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Ugitech SA
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Ugine Savoie Imphy SA
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Application filed by Ugine Savoie Imphy SA filed Critical Ugine Savoie Imphy SA
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    • 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
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
    • 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

Definitions

  • the present invention relates to an austenitic stainless steel for the elaboration in particular of thread, having an inclusive cleanliness suitable for use in the field of wire drawing of diameter less than 0.3 mm and in the area of production of submitted parts to fatigue.
  • stainless steels we mean iron alloys containing minus 10.5% chromium. Other elements enter into the composition steels to modify their structure and properties.
  • Austenitic stainless steels have a composition determined. The austenitic structure is ensured after transformation, by a heat treatment of the hyper quenching type.
  • gamma-genes favor the appearance of austenite phase of metallographic structure of cubic type with faces centered.
  • these elements are carbon, nitrogen, manganese, copper, nickel.
  • stainless steels may, in the liquid state, contain in solution, due to the production processes, oxygen and sulfur contents of less than 100.10 -4 %. During the cooling of the steel in liquid or solid state, the solubility of the oxygen and sulfur elements decreases and the energy of formation of the oxides or sulphides is reached.
  • the object of the invention is to produce a stainless steel austenitic with selected inclusiveness, steel capable of be used in particular in the field of wire drawing with a diameter less than 0.3 mm and in the area of production of parts subject to tired.
  • Figures 1 and 2 respectively present an image of a example of slightly distorted, thick inclusion and an image of an example of inclusions contained in a steel according to the invention.
  • the steel according to the invention contains in its weight composition less than 200. 10 -3 % of carbon, less than 200.10 -3 % of nitrogen, from 0.3% to 4% of manganese, from 14% to 23% chromium, 5% to 17% nickel, 0.3% to 2% silicon, less than 10.10 -3 % sulfur, 50.10 -4 % to 120.10 -4 % total oxygen, 0, 1.10 -4 % to 20.10 -4 % aluminum, less than 2.10 -4 % magnesium, from 0.1.10 -4 % to 5.10 -4 % calcium, less than 5.10 -3 % titanium.
  • Carbon, nitrogen, chromium, nickel, manganese, silicon are the usual elements for obtaining a stainless steel austenitic.
  • the manganese, chromium, sulfur contents in proportion are chosen to generate deformable sulfides of good composition determined.
  • composition intervals of the silicon and manganese elements ensure according to the invention, the presence of inclusions of the silicate type, rich in SiO 2 and containing a non-negligible amount of MnO.
  • Mobybdenum can be added to the composition of steel austenitic stainless steel to improve corrosion resistance.
  • Copper can also be added to the composition of steel according to the invention because it improves the cold deformation properties and this fact stabilizes the austenite.
  • the copper content is limited to 3% to avoid difficulties of hot transformation because the copper lowers appreciably the upper limit of steel reheating temperature before rolling.
  • the intervals in total oxygen, aluminum and calcium make it possible, according to the invention, to obtain inclusions of the manganese silicate type containing a non-zero fraction of Al 2 O 3 and CaO.
  • the aluminum and calcium contents are greater than 0.1 ⁇ 10 -4 % so that the inclusions sought contain more than 1% of CaO and more than 3% of Al 2 O 3 .
  • the values of the total oxygen contents are according to the invention between 50 ppm and 120 ppm.
  • oxygen fixes the elements magnesium, calcium, aluminum and does not form the inclusion of oxides rich in SiO 2 and MnO.
  • the calcium content is less than 5.10 -4 % so that the desired inclusions do not contain more than 30% CaO.
  • the aluminum content is less than 20.10 -4 % to avoid that the desired inclusions contain more than 25% of Al 2 O 3 , which also promotes crystallization.
  • the invention relates to an austenitic stainless steel containing inclusions of chosen composition obtained voluntarily, the composition being related to the overall composition of the steel, so that the physical properties of these inclusions favor their deformation during hot processing of steel.
  • austenitic stainless steel contains inclusions of determined composition which have their softening point close to the rolling temperature of the steel and such that the appearance of crystals harder than steel at the temperature of rolling as in particular the defined compounds, SiO 2 , in the form of tridymite, christobalite, quartz; 3CaO-SiO 2 ; CaO; MgO; Cr 2 O 3 ; anorthite, mullite, gehlenite, corundum, spinel of the Al 2 O 3 -MgO or Al 2 O 3 -Cr 2 O 3 -MnO-MgO type; CaO-Al 2 O 3 ; CaO-6Al 2 O 3 ; CaO-2Al 2 O 3 , TiO 2 is inhibited.
  • the steel mainly contains inclusions of oxide of composition such as these form a vitreous mixture or amorphous during all the successive operations of shaping steel.
  • the viscosity of the inclusions chosen is sufficient for the growth of crystallized oxide particles in inclusions resulting from the invention is totally inhibited from the fact that, in a inclusion of oxide, short-range diffusion is weak and Convective displacements are very limited.
  • These inclusions remained glassy in the temperature range of hot steel treatments also have a lower hardness and modulus of elasticity than crystallized inclusions of corresponding composition. So the inclusions can be further deformed, crushed and elongated, when for example, wire drawing and the concentration of stresses neighborhood of the inclusions is greatly reduced, which attenuates important the risk of appearance, for example, of fatigue cracks or wire drawing breaks.
  • austenitic stainless steel contains inclusions of oxides of defined composition such as their viscosity in the temperature range of hot rolling steel is not too high. Therefore, the flow constraint of inclusion is clearly lower than that of steel under hot rolling conditions whose temperatures are generally between 800 ° C and 1350 ° C.
  • oxide inclusions deform at the same time as steel during hot rolling and therefore after rolling, these inclusions are perfectly elongated, and very thin, which allows to avoid any problem of breakage during, for example, an operation of wire drawing.
  • SiO 2 content is less than 40%, the viscosity of the oxide inclusions is too low and the growth mechanism of oxide crystals is not inhibited. If SiO 2 is greater than 60%, very hard harmful particles of silica are formed in the form of trydimite or christobalite or quartz.
  • the MnO content between 5% and 50% makes it possible to greatly lower the softening point of the mixture of oxides containing in particular SiO 2 , CaO, Al 2 O 3 , and promotes the creation of inclusions which remain in a state vitreous under the rolling conditions of the steel according to the invention.
  • crystals of MnO-Al 2 O 3 or of mullite are formed.
  • the CaO content is greater than 30%, crystals of CaO-SiO 2 or (Ca, Mn) O-SiO 2 are formed .
  • crystals of MgO are formed; 2MgO-SiO 2 ; MgO-SiO 2 ; Al 2 O 3 -MgO, which are extremely hard phases.
  • Al 2 O 3 is less than 3%, wollastonite crystals are formed and when Al 2 O 3 is greater than 25%, crystals of mullite, anorthite, corundum and spinels, especially of Al 2 type, appear O 3 -MgO or Al 2 O 3 -Cr 2 O 3 -MgO-MnO or alternatively of aluminates of the CaO-6Al 2 O 3 or CaO-2Al 2 O 3 or CaO-Al 2 O 3 type , or of gehlenite .
  • Oxides and sulfides inclusions are generally considered harmful with regard to the properties of use in the in the field of fine wire drawing and in the field of fatigue resistance, in particular, in bending and / or in torsion. It is usual to characterize the concentration of oxide and sulphide inclusions by observation a long polished cut of rolling on a wire rod rolled to hot diameter between 5 and 10 mm. We call cleanliness inclusionary the result of this characterization carried out according to different standards based on end use.
  • a form factor which is the ratio of length to thickness.
  • the shape is generally very high, i.e. up to 10 or 20 and therefore, the thickness of the inclusion is extremely small.
  • an inclusion which does not deform or undergoes a weak deformation is characterized by a low form factor, say of the order of 1, therefore, the thickness of the inclusion remains high and of the same order of magnitude as the size of the original product inclusion raw casting. Consequently, in the following description, we retain as a simple and effective characterization criterion with regard to properties of use of the laminated wire, the thickness of each inclusion observed on the wire the mine.
  • Figures 1 and 2 show respectively on a polished section of laminated wire with a diameter of 5.5 mm, an example of very thick inclusion and little distorted and an example of fine and very well deformed inclusions contained in the steel according to the invention.
  • Figure 1 shows a mixed inclusion called two-phase, consisting of a central crystalline non-deformable part of the Al 2 O 3 -MgO type, denoted AlMg in the figure, and two end portions, denoted in the figure SiAlMg, consisting of a slightly deformable phase rich in SiO 2 , Al 2 O 3 and MgO.
  • This inclusion has a thickness of 11 micrometers, a length of 40 micrometers and is particularly harmful for wire drawing applications or for producing parts subjected to fatigue.
  • Figure 2 shows four examples of inclusions less than 2 micrometers of thickness, of variable length, such as those contained in the steel according to the invention.
  • the inclusion characteristics are defined by counting the number of inclusions with a thickness equal to or greater than a given dimension for a sample surface of 1000 mm 2 .
  • Tables 1 and 2 below show steels showing the influence of the composition of the steel and of the composition of the oxide inclusions on the number of inclusions of given thickness.
  • STEEL AT B VS D E F G %VS 0.093 0.065 0.067 0.093 0.060 0.055 0.083 %NOT 0.030 0.045 0.045 0.026 0.041 0.056 0.040 %Yes 1.81 0.49 0.54 1.75 0.48 0.56 0.75 % Mn 1.32 0.26 0.30 1.25 0.58 0.53 1.08 % Cr 17.65 18.46 18.32 17.60 18.27 18.24 17.95 %Or 7.85 8.49 8.47 7.75 8.61 8.57 8.30 % Mo 0.71 0.10 0.17 0.73 0.24 0.28 0.33 % Cu 0.22 0.32 0.33 0.15 0.48 0.51 0.25 Ot ppm 25 40 48 28 129 138 65 Al ppm 43 10 8 26 25 13 18 Ca ppm 9 13 2 1 54 11 2 Mg ppm 1 1 1 3 2 1 1 Ti ppm
  • Table 1 presents compositions of steels considered of insufficient quality and Table 2 presents steel compositions according to the invention having remarkable inclusiveness.
  • the inclusion characteristics are materialized by the presence on a sampled surface of 1000 mm 2 of less than 5 inclusions of oxides with a thickness of more than 10 ⁇ m.
  • the sulfide inclusions are, in number, less than 10 having a thickness of more than 5 ⁇ m, for an area of 1000 mm 2 .
  • Steel A has a low total oxygen content and a high aluminum content.
  • the inclusions seen in the steel are poor in SiO 2 and MnO, very rich in Al 2 O 3 and MgO, of crystalline spin type Al 2 O 3 -MgO.
  • Steel B has a low total oxygen content and a high calcium content. Despite an acceptable aluminum content, the inclusions observed contain too much Al 2 O 3 and this is reflected, on the hot-rolled wire, by the presence of thick inclusions.
  • Steel D like steel C, has a low total oxygen content but a high content of aluminum and magnesium. On the steel, inclusions rich in SiO 2 and MgO are observed, inclusions which are not sufficiently deformable.
  • Steel E has a high sulfur content which causes the appearance of numerous, slightly deformed sulfides. In addition, it has a high content of oxygen, aluminum, calcium. This leads to the appearance of inclusions containing little SiO 2 , a lot of CaO, and very little MnO. These inclusions are not very deformable and numerous. Steel F also has high sulfur and oxygen contents, but the aluminum and calcium contents are quite low. In this steel, the inclusions are rich in SiO 2 and Cr 2 O 3 , which leads to the appearance of very hard Cr 2 O 3 crystals and viscous SiO 2 phases.
  • Steel G has a high sulfur content, which results in the appearance of numerous sulfides.
  • the other contents of the composition are within acceptable ranges and inclusions of oxides obtained are of a vitreous nature, on a wire and deformable as in the steel according to the invention.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Manufacturing & Machinery (AREA)
  • Thermal Sciences (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
  • Metal Extraction Processes (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
  • Materials For Medical Uses (AREA)
  • Conductive Materials (AREA)
EP96400736A 1995-04-21 1996-04-05 Acier inoxydable austénitique pour l'élaboration notamment de fil Revoked EP0738783B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR9504782 1995-04-21
FR9504782A FR2733252B1 (fr) 1995-04-21 1995-04-21 Acier inoxydable austenitique pour l'elaboration notamment de fil

Publications (2)

Publication Number Publication Date
EP0738783A1 EP0738783A1 (fr) 1996-10-23
EP0738783B1 true EP0738783B1 (fr) 2000-03-08

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ID=9478329

Family Applications (1)

Application Number Title Priority Date Filing Date
EP96400736A Revoked EP0738783B1 (fr) 1995-04-21 1996-04-05 Acier inoxydable austénitique pour l'élaboration notamment de fil

Country Status (23)

Country Link
US (1) US5651937A (el)
EP (1) EP0738783B1 (el)
JP (1) JPH08337852A (el)
KR (1) KR960037853A (el)
AT (1) ATE190361T1 (el)
CA (1) CA2174567C (el)
CZ (1) CZ291422B6 (el)
DE (1) DE69606902T2 (el)
DK (1) DK0738783T3 (el)
EG (1) EG21379A (el)
ES (1) ES2145395T3 (el)
FR (1) FR2733252B1 (el)
GR (1) GR3033479T3 (el)
IL (1) IL117977A (el)
NO (1) NO312469B1 (el)
PL (1) PL185044B1 (el)
PT (1) PT738783E (el)
RO (1) RO116098B1 (el)
RU (1) RU2106425C1 (el)
SI (1) SI9600129A (el)
TR (1) TR199600325A2 (el)
TW (1) TW399100B (el)
UA (1) UA44716C2 (el)

Families Citing this family (17)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2759709B1 (fr) * 1997-02-18 1999-03-19 Ugine Savoie Sa Acier inoxydable pour l'elaboration de fil trefile notamment de fil de renfort de pneumatique et procede de realisation dudit fil
FR2776306B1 (fr) * 1998-03-18 2000-05-19 Ugine Savoie Sa Acier inoxydable austenitique pour l'elaboration notamment de fil
JP3504521B2 (ja) * 1998-12-15 2004-03-08 株式会社神戸製鋼所 疲労特性に優れたばね用鋼
FR2818290A1 (fr) * 2000-12-15 2002-06-21 Ugine Savoie Imphy Acier inoxydable pour une mise en forme severe et notamment la frappe ou le trefilage d'un fil
FR2818289B1 (fr) * 2000-12-15 2003-08-08 Usinor Acier inoxydable pour une mise en forme severe et notamment l'emboutissage profond d'une tole
JP2002206148A (ja) * 2001-01-09 2002-07-26 Nisshin Steel Co Ltd 加工割れ感受性が低いオーステナイト系ステンレス鋼板およびその製造方法
JP2003041349A (ja) * 2001-08-01 2003-02-13 Nisshin Steel Co Ltd 電気抵抗材料
JP4150054B2 (ja) * 2006-06-21 2008-09-17 株式会社神戸製鋼所 鍛造用鋼およびその製造方法並びに鍛造品
US7985304B2 (en) 2007-04-19 2011-07-26 Ati Properties, Inc. Nickel-base alloys and articles made therefrom
JP4673343B2 (ja) * 2007-06-06 2011-04-20 日本冶金工業株式会社 耐食性、溶接性および表面性状に優れるステンレス鋼板およびその製造方法
KR20090066000A (ko) * 2007-12-18 2009-06-23 주식회사 포스코 고진공, 고순도 가스 배관용 오스테나이트계 스테인리스강
JP5853281B2 (ja) * 2011-03-25 2016-02-09 日新製鋼株式会社 表面光沢性に優れたオーステナイト系ステンレス鋼板
JP6491983B2 (ja) * 2015-08-28 2019-03-27 新日鐵住金ステンレス株式会社 高強度・高延性の極細線用ステンレス鋼線材、高強度・高延性の極細線用ステンレス鋼線
JP7042057B2 (ja) * 2017-10-25 2022-03-25 日鉄ステンレス株式会社 スラグスポット発生抑止能に優れるステンレス鋼材並びに溶接構造部材およびその製造法
CN107760973B (zh) * 2017-10-26 2019-04-02 江西省中蔚建设集团有限公司 一种建筑用奥氏体不锈钢的加工方法
CN110791710A (zh) * 2019-11-12 2020-02-14 江阴康瑞成型技术科技有限公司 环保节能型奥氏体冷镦不锈钢丝及其生产工艺
BR112022013350A2 (pt) * 2020-01-15 2022-09-13 Nippon Steel Stainless Steel Corp Aço inoxidável ferrítico

Family Cites Families (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3933480A (en) * 1972-09-18 1976-01-20 Republic Steel Corporation Method of making stainless steel having improved machinability
JPS55122858A (en) * 1979-03-13 1980-09-20 Daido Steel Co Ltd High carbon high manganese steel with high machinability
DE3018537A1 (de) * 1979-05-17 1980-11-27 Daido Steel Co Ltd Kontrollierte einschluesse enthaltender automatenstahl und verfahren zu seiner herstellung
FR2690169B1 (fr) * 1992-04-17 1994-09-23 Ugine Savoie Sa Acier inoxydable austénitique à haute usinabilité et à déformation à froid améliorée.
US5314549A (en) * 1993-03-08 1994-05-24 Nkk Corporation High strength and high toughness stainless steel sheet and method for producing thereof

Also Published As

Publication number Publication date
SI9600129A (en) 1996-10-31
NO961531D0 (no) 1996-04-18
GR3033479T3 (en) 2000-09-29
DE69606902T2 (de) 2000-11-09
CZ291422B6 (cs) 2003-03-12
CZ113996A3 (en) 1996-11-13
TW399100B (en) 2000-07-21
FR2733252B1 (fr) 1997-05-23
US5651937A (en) 1997-07-29
ES2145395T3 (es) 2000-07-01
PT738783E (pt) 2000-07-31
FR2733252A1 (fr) 1996-10-25
RU2106425C1 (ru) 1998-03-10
NO312469B1 (no) 2002-05-13
PL185044B1 (pl) 2003-02-28
IL117977A0 (en) 1996-08-04
EP0738783A1 (fr) 1996-10-23
ATE190361T1 (de) 2000-03-15
TR199600325A2 (tr) 1996-11-21
UA44716C2 (uk) 2002-03-15
CA2174567A1 (fr) 1996-10-22
IL117977A (en) 2000-11-21
RO116098B1 (ro) 2000-10-30
KR960037853A (ko) 1996-11-19
EG21379A (en) 2001-09-30
JPH08337852A (ja) 1996-12-24
CA2174567C (fr) 2001-10-23
DE69606902D1 (de) 2000-04-13
DK0738783T3 (da) 2000-07-31
NO961531L (no) 1996-10-22

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