EP0738783A1 - Rostfreier austenitischer Stahl geeignet für die Herstellung von Drähte - Google Patents

Rostfreier austenitischer Stahl geeignet für die Herstellung von Drähte Download PDF

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Publication number
EP0738783A1
EP0738783A1 EP96400736A EP96400736A EP0738783A1 EP 0738783 A1 EP0738783 A1 EP 0738783A1 EP 96400736 A EP96400736 A EP 96400736A EP 96400736 A EP96400736 A EP 96400736A EP 0738783 A1 EP0738783 A1 EP 0738783A1
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EP
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Prior art keywords
inclusions
steel
less
composition
mgo
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EP96400736A
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English (en)
French (fr)
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EP0738783B1 (de
Inventor
Frédéric Descaves
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Ugitech SA
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Ugine Savoie 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 preparation in particular of wire, having an inclusive cleanliness suitable for use in the field of wire drawing of wire of diameter less than 0.3 mm and in the field of the production of parts subjected to tiredness.
  • stainless steels means iron alloys containing at least 10.5% chromium. Other elements enter into the composition of steels in order to modify their structure and their properties.
  • Austenitic stainless steels have a specific composition. The austenitic structure is ensured after transformation, by a heat treatment of the hyper quenching type.
  • gamma-genes favor the appearance of the austenite phase of metallographic structure of cubic type with centered faces.
  • 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 an austenitic stainless steel having a selected inclusion cleanliness, steel which can be used in particular in the field of wire drawing with a diameter of less than 0.3 mm and in the field of production of parts subject to tired.
  • FIGS. 1 and 2 respectively present an image of an example of inclusion which is slightly deformed, thick 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 allowing the production of an austenitic stainless steel.
  • the contents of manganese, chromium, sulfur, in proportion are chosen to generate deformable sulphides of well defined composition.
  • 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 austenitic stainless steel to improve corrosion resistance.
  • Copper can also be added to the composition of the steel according to the invention because it improves the cold deformation properties and therefore stabilizes the austenite.
  • the copper content is limited to 3% to avoid difficulties in hot transformation because the copper significantly lowers the upper temperature limit for reheating the steel 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 in relation to the overall composition of the steel, so that the physical properties of these inclusions promote their deformation during hot transformation 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 oxide inclusions of composition such that these form a vitreous or amorphous mixture during all the successive operations of shaping the steel.
  • the viscosity of the inclusions chosen is sufficient for the growth of the crystallized oxide particles in the resulting inclusions of the invention to be completely inhibited because, in an oxide inclusion, the short distance diffusion is low and the convective displacements are very limited.
  • These inclusions which remain vitreous in the temperature range of the hot treatments of the steel also have a lower hardness and modulus of elasticity than crystallized inclusions of corresponding composition.
  • the inclusions can be further deformed, crushed and elongated, during operation for example, by wire drawing and the concentration of stresses in the vicinity of the inclusions is greatly reduced, which considerably reduces the risk of appearance, for example , fatigue cracks or wire drawing breaks.
  • austenitic stainless steel contains inclusions of oxides of defined composition such that their viscosity in the field of hot rolling temperatures of the steel is not too high. Therefore, the flow constraint of inclusion is clearly lower than that of steel under hot rolling conditions, the temperatures of which are generally between 800 ° C. and 1350 ° C.
  • the oxide inclusions deform at the same time as the steel during hot rolling and therefore after rolling, these inclusions are perfectly elongated, and of very small thickness which makes it possible to avoid any problem of breakage during, by example, a wire drawing operation.
  • the size distribution of the inclusions on the raw casting product is relatively independent of the composition thereof. Therefore, before hot rolling, the same sizes and the same distribution of inclusions are found in steels.
  • 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 .
  • the sulfur content must be less than 0.010% in order to obtain sulphide inclusions of thickness not exceeding 5 ⁇ m on the rolled product.
  • inclusions of the manganese sulfide and chromium type are perfectly deformable under the following conditions: 5% ⁇ Cr ⁇ 30% 30% ⁇ Mn ⁇ 60% 35% ⁇ S ⁇ 45%
  • Inclusions of the oxide and sulphide type are generally considered to be harmful with regard to the properties of use in the field of fine wire drawing and in the field of fatigue resistance, in particular in bending and / or torsion. It is customary to characterize the concentration of oxide and sulphide inclusions by observing a polished cut in the long direction of rolling on a hot rolled wire rod with a diameter between 5 and 10 mm. The result of this characterization carried out according to different standards depending on the end use is called inclusive cleanliness.
  • a form factor which is the ratio of length to thickness.
  • the form factor is generally very high, that is to say up to 10 or 20 and consequently, the thickness of the inclusion is extremely low.
  • an inclusion which does not deform or undergoes a small deformation is characterized by a low form factor, that is to 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 inclusion on the raw casting product. Consequently, in the following description, the thickness of each inclusion observed on the laminated wire is retained as a simple and effective characterization criterion with respect to the properties of use of the laminated wire.
  • Figures 1 and 2 show respectively on a polished section of laminated wire of diameter 5.5 mm, an example of very thick and slightly deformed inclusion 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.
  • FIG. 2 presents four examples of inclusions less than 2 micrometers thick, 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.
  • TABLE 1 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
  • Table 1 presents compositions of steels considered of insufficient quality and Table 2 presents compositions of steel according to the invention having a remarkable inclusiveness.
  • the inclusionary characteristics are materialized by the fact that on a sampled surface of 1000 mm 2 of less than 5 inclusions of oxides thicker 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 SiO2, 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 sulphides. Furthermore, the other contents of the composition are within acceptable ranges and the inclusions of oxides obtained are of a vitreous nature, on wire and deformable as in the steel according to the invention.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Manufacturing & Machinery (AREA)
  • Crystallography & Structural Chemistry (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 Rostfreier austenitischer Stahl geeignet für die Herstellung von Drähte Revoked EP0738783B1 (de)

Applications Claiming Priority (2)

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

Publications (2)

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

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EP96400736A Revoked EP0738783B1 (de) 1995-04-21 1996-04-05 Rostfreier austenitischer Stahl geeignet für die Herstellung von Drähte

Country Status (23)

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

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0859064A1 (de) * 1997-02-18 1998-08-19 UGINE SAVOIE (société anonyme) Rostfrei Stahl zum Herstellun von gezogenen Draht, insbesondere von Reifenverstärkungsdraht, und Herstellungsverfahren
FR2776306A1 (fr) * 1998-03-18 1999-09-24 Ugine Savoie Sa Acier inoxydable austenitique pour l'elaboration notamment de fil
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
FR2818289A1 (fr) * 2000-12-15 2002-06-21 Usinor Acier inoxydable pour une mise en forme severe et notamment l'emboutissage profond d'une tole
EP1221494A1 (de) * 2001-01-09 2002-07-10 Nisshin Steel Co., Ltd. Austenitischer Edelstahl, weniger empfindlich gegen Rissbildung bei einem Formgebungsverfahren und dessen Herstellungsverfahren
CN107760973A (zh) * 2017-10-26 2018-03-06 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

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* Cited by examiner, † Cited by third party
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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
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
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
US20230099909A1 (en) * 2020-01-15 2023-03-30 Nippon Steel Stainless Steel Corporation Ferritic stainless steel

Citations (4)

* 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
FR2456785A1 (fr) * 1979-05-17 1980-12-12 Daido Steel Co Ltd Acier de decolletage contenant des inclusions determinees et un procede de sa preparation
EP0567365A1 (de) * 1992-04-17 1993-10-27 Ugine Savoie Rostfreier austenitischer Stahl mit guter Zerspanbarkeit und verbesserten Kaltverformungseigenschaften
US5314549A (en) * 1993-03-08 1994-05-24 Nkk Corporation High strength and high toughness stainless steel sheet and method for producing thereof

Family Cites Families (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS55122858A (en) * 1979-03-13 1980-09-20 Daido Steel Co Ltd High carbon high manganese steel with high machinability

Patent Citations (4)

* 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
FR2456785A1 (fr) * 1979-05-17 1980-12-12 Daido Steel Co Ltd Acier de decolletage contenant des inclusions determinees et un procede de sa preparation
EP0567365A1 (de) * 1992-04-17 1993-10-27 Ugine Savoie Rostfreier austenitischer Stahl mit guter Zerspanbarkeit und verbesserten Kaltverformungseigenschaften
US5314549A (en) * 1993-03-08 1994-05-24 Nkk Corporation High strength and high toughness stainless steel sheet and method for producing thereof

Cited By (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0859064A1 (de) * 1997-02-18 1998-08-19 UGINE SAVOIE (société anonyme) Rostfrei Stahl zum Herstellun von gezogenen Draht, insbesondere von Reifenverstärkungsdraht, und Herstellungsverfahren
FR2759709A1 (fr) * 1997-02-18 1998-08-21 Ugine Savoie Sa Acier inoxydable pour l'elaboration de fil trefile notamment de fil de renfort de pneumatique et procede de realisation dudit fil
AU734559B2 (en) * 1997-02-18 2001-06-14 Ugitech Process for producing a drawn wire made of stainless steel, in particular a wire for reinforcing tyres, and wire obtained by the process
US6440579B1 (en) 1997-02-18 2002-08-27 Ugine Savoie Societe De Production Internationale De Trefiles Process for producing a drawn wire made of stainless steel, in particular a wire for reinforcing tires, and wire obtained by the process
FR2776306A1 (fr) * 1998-03-18 1999-09-24 Ugine Savoie Sa Acier inoxydable austenitique pour l'elaboration notamment de fil
EP0947591A1 (de) * 1998-03-18 1999-10-06 Ugine-Savoie Imphy Rostfreier austenitischer Stahl, geeignet zur Herstellung von Drähten
US6123784A (en) * 1998-03-18 2000-09-26 Ugine-Savoie Imphy Austenitic stainless steel especially for making wire
CN1098372C (zh) * 1998-03-18 2003-01-08 尤吉纳－萨瓦依安费公司 奥氏体不锈钢，特别是用于制造钢丝的奥氏体不锈钢
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
FR2818289A1 (fr) * 2000-12-15 2002-06-21 Usinor Acier inoxydable pour une mise en forme severe et notamment l'emboutissage profond d'une tole
EP1221494A1 (de) * 2001-01-09 2002-07-10 Nisshin Steel Co., Ltd. Austenitischer Edelstahl, weniger empfindlich gegen Rissbildung bei einem Formgebungsverfahren und dessen Herstellungsverfahren
CN107760973A (zh) * 2017-10-26 2018-03-06 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

Also Published As

Publication number Publication date
SI9600129A (en) 1996-10-31
CZ291422B6 (cs) 2003-03-12
NO961531D0 (no) 1996-04-18
UA44716C2 (uk) 2002-03-15
ES2145395T3 (es) 2000-07-01
GR3033479T3 (en) 2000-09-29
IL117977A (en) 2000-11-21
RU2106425C1 (ru) 1998-03-10
IL117977A0 (en) 1996-08-04
KR960037853A (ko) 1996-11-19
PL185044B1 (pl) 2003-02-28
EP0738783B1 (de) 2000-03-08
FR2733252B1 (fr) 1997-05-23
ATE190361T1 (de) 2000-03-15
NO312469B1 (no) 2002-05-13
NO961531L (no) 1996-10-22
EG21379A (en) 2001-09-30
US5651937A (en) 1997-07-29
FR2733252A1 (fr) 1996-10-25
CZ113996A3 (en) 1996-11-13
RO116098B1 (ro) 2000-10-30
DK0738783T3 (da) 2000-07-31
TR199600325A2 (tr) 1996-11-21
PT738783E (pt) 2000-07-31
CA2174567A1 (fr) 1996-10-22
DE69606902T2 (de) 2000-11-09
CA2174567C (fr) 2001-10-23
JPH08337852A (ja) 1996-12-24
TW399100B (en) 2000-07-21
DE69606902D1 (de) 2000-04-13

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