EP1358359B1 - Acier et procede de production d'un produit intermediaire - Google Patents

Acier et procede de production d'un produit intermediaire Download PDF

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Publication number
EP1358359B1
EP1358359B1 EP02719725A EP02719725A EP1358359B1 EP 1358359 B1 EP1358359 B1 EP 1358359B1 EP 02719725 A EP02719725 A EP 02719725A EP 02719725 A EP02719725 A EP 02719725A EP 1358359 B1 EP1358359 B1 EP 1358359B1
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EP
European Patent Office
Prior art keywords
max
steel
steels
hot forming
mass
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.)
Expired - Lifetime
Application number
EP02719725A
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German (de)
English (en)
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EP1358359A2 (fr
Inventor
Claudia Ernst
Bernd Milo Gehricke
Frank Bredenbreuker
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Deutsche Edelstahlwerke GmbH
Original Assignee
EDELSTAHL WITTEN KREFELD GmbH
Edelstahl Witten-Krefeld GmbH
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 EDELSTAHL WITTEN KREFELD GmbH, Edelstahl Witten-Krefeld GmbH filed Critical EDELSTAHL WITTEN KREFELD GmbH
Publication of EP1358359A2 publication Critical patent/EP1358359A2/fr
Application granted granted Critical
Publication of EP1358359B1 publication Critical patent/EP1358359B1/fr
Anticipated expiration legal-status Critical
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Classifications

    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/02—Hardening articles or materials formed by forging or rolling, with no further heating beyond that required for the formation
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
    • 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
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys

Definitions

  • Machining processes are an essential one Part of industrial production technology and a major cost bearer in the manufacture of tools for plastics processing.
  • the economic Usability of steels of the type mentioned at the beginning therefore depends essentially on their machinability and their Corrosion resistance, which in turn is crucial is influenced by the chromium content of the steels.
  • machinability is used in this context understood the property of a material to have certain conditions machined.
  • a martensitic stainless steel with good Machinability is known from EP 0 721 513 B1.
  • the known steel contains 10 to 14% by mass of chromium. to He also shows improvement in machinability at least 0.15% sulfur and 1.0 to 3.5% copper. The addition of copper also has a positive effect Influence on the hardness of the alloy.
  • the known steels are processed in Dependence on the respective carbon and Carbide. So the steels are the ones in question kind on the one hand remunerated by the tool manufacturer Condition used with a hardness of 285 to 325 HB. at This hardness is a machining of the Material still possible. On the other hand, the steels in the soft annealed condition processed, the hardness of the Then steels is a maximum of 250 HB. So less hard Steels are easier to process. It must however, heat treatment after processing be performed to the usually required Achieve hardness of 46 to 60 HRC. Subsequently finishing is required.
  • Machining can be done by the The high final hardness required by the known Do not carry out steel economically anymore. This The problem is caused by the processing in the soft annealed condition with downstream Solved heat treatment. A disadvantage of the final However, heat treatment exists in addition to that for this additional operation costs incurred in that it thereby to crack formation and distortion of the component as a result the warming can come.
  • JP-A-01 215 489 discloses a steel consisting of 0.05-0.17% C, 0.01-1.5% Si, 0.01-2% Mr, ⁇ 0.025% P, ⁇ 0.015% S, 8-12% Cr, ⁇ 0.8% Ni, 0.5-3% Mo, 0.5-3% W, 0.1-0.2% Nb, ⁇ 0.04% Al, 0.03-0.05% N, ⁇ 0.010 and 0.0005-0.01 Ca, rest iron.
  • the object of the invention is a especially for the manufacture of tools for the plastics processing industry suitable steel find that with high hardness and corrosion resistance one that meets the practical requirements Toughness, machinability and weldability.
  • a method for the production of Intermediate products from such a steel will be specified.
  • Intermediate product in this Context also long products, flat products or others Objects understood, which then another Processing to be fed.
  • the nioballoyed tool steel according to the invention has an optimized combination of machinability, hardness, Corrosion resistance, weldability and toughness on. It reaches hardness layers that are between 300 and 450 HB lie. Despite the relatively high sulfur content, it shows good toughness for steels of the generic type on the requirements that arise in practice enough.
  • the invention Steels sulfur-alloyed, the proportion of which is less than 0.15 mass%.
  • the steel preferably has at least 0.04 mass .-%, whereby a good Machinability can be guaranteed safely. Yet better machinability can be taken into account other conditions imposed on the composition can be achieved when steel according to the invention contains at least 0.07% by mass of sulfur.
  • steel according to the invention has good toughness. This is achieved in that the steel together with the Sulfur at least one of the elements calcium, manganese or contains cerium in quantities the total of which is more than 0.0002 however at most 0.015 mass%. These elements enable the formation of sulfides in the matrix of the Steel and thus improve its toughness. This can be achieved unerringly, for example, if the steel according to the invention 0.001 - 0.009 mass% Contains calcium.
  • Hard phases are formed which lead to the hardness of 300 contribute up to 450 HB. At the same time, the hard phases in particularly fine and evenly distributed what a has a positive influence on the toughness properties.
  • the toughness of the known tool steels mentioned at the beginning is determined by the carbon and carbide content as well as by the Amount of sulfur, distribution and morphology the sulfides negatively affected.
  • Steel according to the invention contains a maximum of 0.12% carbon. That way its carbide content is also limited.
  • one steel according to the invention in that the contents in it grain-limiting elements is reduced to a minimum, toughness compared to other sulfur alloyed steels elevated.
  • the hot forming of the primary material to the intermediate product is the Structural structure and the material isotropy influenced.
  • a improved structure of the structure and a higher isotropy of the Material can be achieved in that the Hot forming using a degree of deformation ⁇ of is carried out at least 1.5.
  • the Hot forming as forging or, to manufacture larger ones Dimensions to be carried out as hot rolling.
  • the Hot forming is preferred at temperatures of 850 ° C - 1100 ° C. In this temperature range the material used according to the invention has a low one Yield stress and high toughness, so that a optimal formability is given.
  • the hot forming leaves thus quickly, inexpensively and with high output carry out.
  • the workpiece produced according to the invention is after Hot forming from the forming heat, preferably in air stored.
  • the material becomes slow and completely from austenitic to martensitic Condition transferred.
  • Such slow cooling will on the one hand, the desired hardness of the material of up to 450 HB set.
  • heat and Conversion voltages largely avoided, so that none Delays or stress cracks in the finished intermediate product occur.
  • Table 1 compares the alloys of steels A, B, C according to the invention with the compositions of four comparative steels D, E, F, G lying outside the invention.
  • Table 2 also shows the Brinell hardness values belonging to steels A to G as well as the hardness (H f ), sweat (S f ) and embrittlement factors (KG f ).
  • the impact bending test according to steel-iron test sheet 1314 carried out. This trial is used as a measure of that Toughness of a material used to smash unscarred samples necessary impact bending work determined.
  • the samples used with the dimension 7 x 10 x 55 mm were from the direction of deformation of the checked steels A - G taken with a hardness from 300 to 400 HB.
  • the test was carried out at room temperature. Like the one in Diag. 2 summarized values for the impact bending work (mean values from 3 tested individual samples) show, with increasing embrittlement factor KG f a significant decrease in the measured impact bending work can be determined.
  • the steels A, B and C according to the invention have the desired high level of toughness with values well above 200 J, while for the steels D, E, F and G listed for comparison only values between 50 and 150 J could be measured with increasing embrittlement factor, their toughness was therefore significantly lower.
  • Comparable has been found in connection with the value to be observed for the weldability factor S f of steels according to the invention.
  • the comparative steels, the welding factor S f of which are above the limit value provided according to the invention, have a significantly poorer welding behavior than the steels according to the invention. This is particularly evident in the occurrence of welding cracks, which can be avoided in the case of the steels not according to the invention, which require extensive preheating and post-treatment.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Organic Low-Molecular-Weight Compounds And Preparation Thereof (AREA)

Claims (15)

  1. Acier, en particulier pour des outils sollicités par la corrosion, qui présente la composition suivante (en % en poids) :
    C :
    au minimum 0,02 % et au maximum 0,12 %
    Si :
    au maximum 1,5 %
    Mn :
    supérieur à 1,0 - 2,50 %,
    P :
    au maximum 0,035 %,
    S :
    au minimum 0,04 % et inférieur à 0,15 %,
    Cr:
    supérieur à 8,0 % et inférieur à 12 %,
    Mo :
    supérieur à 0,0 % et au maximum 0,20 %,
    V :
    supérieur à 0,0 % et au maximum 0,25 %,
    Nb :
    supérieur à 0,1 % et au maximum 0,5 %,
    N :
    au minimum 0,02 % et au maximum 0,12 %,
    Ni :
    au maximum 0,5 %,
    B :
    au maximum 0,005 %,
    Cu :
    au maximum 0,3 %,
    Al :
    au maximum 0,035 %,
    Sn :
    au maximum 0,035 %,
    As :
    au maximum 0,02 %,
    au moins un des éléments Ca, Mg ou Ce, la somme des teneurs de ces éléments étant égale au minimum à 0,0002 % et au maximum à 0,015 %,
    le reste étant du fer et des impuretés inévitables.
  2. Acier selon la revendication 1, caractérisé en ce qu'il contient 0,001 à 0,009 % en poids de Ca.
  3. Acier selon la revendication 1 ou 2, caractérisé en ce que son facteur de dureté Hf remplit la condition suivante : 0,047 < Hf ≤ 0,095, sachant que Hf = 0,11 - % Nb / 7,14 et % Nb désigne la teneur respective en Nb de l'acier.
  4. Acier selon l'une quelconque des revendications précédentes, caractérisé en ce que son facteur de soudabilité Sf remplit la condition suivante : Sf < 3,99, sachant que Sf = % C + 5x % B + 2x % Cu + (% P + % S)/2 + (% Mo + % Cr)/4 + % Mn/10 et % C, % B, % Cu, % P, % S, % Mo, % Cr, % Mn désignent dans chaque cas les teneurs respectives en C, en B, en Cu, en P, en S, en Mo, en Cr, en Mn de l'acier.
  5. Acier selon l'une quelconque des revendications précédentes, caractérisé en ce que son facteur de fragilité KGf remplit la condition suivante : KGf < 1,07, sachant que KGf= 2,97x % Cu + 3,2x(% Sn + % As) + 0,55x % Al + 5,42x % P + 0,98 % N et % Cu, % Sn, % As, % Al, % P, % N désignent les teneurs respectives en Cu, en Sn, en As, en Al, en P et en N de l'acier.
  6. Acier selon l'une quelconque des revendications précédentes, caractérisé en ce qu'il contient au minimum 0,05 % en poids de soufre.
  7. Acier selon l'une quelconque des revendications précédentes, caractérisé en ce qu'il contient au minimum 0,07 % en poids de soufre.
  8. Procédé de préparation d'un demi-produit pour la fabrication d'éléments de construction, en particulier pour la construction d'outils sollicités par la corrosion, à partir d'un acier ayant la composition selon l'une quelconque des revendications 1 à 7, comprenant les étapes suivantes :
    fusion de l'acier,
    coulée de l'acier pour obtenir un produit de départ, tel que des lingots, des brames, des barres de coulée continue, des brames minces ou un feuillard coulé,
    homogénéisation du produit de départ à une température de 1 200 à 1 280°C,
    formage à chaud du produit de départ ayant subi une homogénéisation, en vue d'obtenir le demi-produit.
  9. Procédé selon la revendication 8, caractérisé en ce que le formage à chaud effectué est un forgeage.
  10. Procédé selon la revendication 8, caractérisé en ce que le formage à chaud effectué est un laminage à chaud.
  11. Procédé selon l'une quelconque des revendications 7 à 10, caractérisé en ce que, après le formage à chaud, le demi-produit est stocké à l'air.
  12. Procédé selon l'une quelconque des revendications 7 à 11, caractérisé en ce que le formage à chaud est effectué à des températures de 850°C à 1 150°C.
  13. Procédé selon l'une quelconque des revendications 7 à 12, caractérisé en ce que le demi-produit, à la suite du formage à chaud, subit un traitement thermique à des températures de 850°C à 1 050°C et, après le traitement thermique, est refroidi de manière contrôlée avec un milieu de refroidissement, tel que l'air, l'huile, l'eau ou un polymère.
  14. Procédé selon la revendication 13, caractérisé en ce que, à l'issue du refroidissement, est effectué un traitement de revenu à des températures de 400°C à 650°C.
  15. Utilisation d'un acier ayant la composition selon l'une quelconque des revendications 1 à 6, destiné à la construction d'outils pour la transformation des matières plastiques.
EP02719725A 2001-01-25 2002-01-25 Acier et procede de production d'un produit intermediaire Expired - Lifetime EP1358359B1 (fr)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
DE10103290 2001-01-25
DE10103290A DE10103290A1 (de) 2001-01-25 2001-01-25 Stahl und Verfahren zur Herstellung eines Zwischenproduktes
PCT/EP2002/000746 WO2002059389A2 (fr) 2001-01-25 2002-01-25 Acier et procede de production d'un produit intermediaire

Publications (2)

Publication Number Publication Date
EP1358359A2 EP1358359A2 (fr) 2003-11-05
EP1358359B1 true EP1358359B1 (fr) 2004-06-23

Family

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Application Number Title Priority Date Filing Date
EP02719725A Expired - Lifetime EP1358359B1 (fr) 2001-01-25 2002-01-25 Acier et procede de production d'un produit intermediaire

Country Status (12)

Country Link
US (1) US20040050459A1 (fr)
EP (1) EP1358359B1 (fr)
JP (1) JP3943499B2 (fr)
AT (1) ATE269911T1 (fr)
AU (1) AU2002250853B2 (fr)
CA (1) CA2424074C (fr)
DE (2) DE10103290A1 (fr)
DK (1) DK1358359T3 (fr)
ES (1) ES2223037T3 (fr)
PT (1) PT1358359E (fr)
TR (1) TR200402213T4 (fr)
WO (1) WO2002059389A2 (fr)

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2872825B1 (fr) * 2004-07-12 2007-04-27 Industeel Creusot Acier inoxydable martensitique pour moules et carcasses de moules d'injection

Family Cites Families (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2287521A1 (fr) * 1974-10-11 1976-05-07 Ugine Aciers Acier de decolletage
US4434006A (en) * 1979-05-17 1984-02-28 Daido Tokushuko Kabushiki Kaisha Free cutting steel containing controlled inclusions and the method of making the same
US4294613A (en) * 1979-07-03 1981-10-13 Henrik Giflo Acid resistant, high-strength steel suitable for polishing
JPS59153831A (ja) * 1983-02-23 1984-09-01 Sumitomo Metal Ind Ltd フエライト系耐熱ステンレス鋼板の製造法
JPH01215489A (ja) * 1988-02-19 1989-08-29 Sumitomo Metal Ind Ltd 高Ｃｒフェライト鋼用溶接材料
JP3068216B2 (ja) * 1990-12-28 2000-07-24 東北特殊鋼株式会社 高冷鍛性電磁ステンレス鋼
US5362337A (en) * 1993-09-28 1994-11-08 Crs Holdings, Inc. Free-machining martensitic stainless steel
US6090230A (en) * 1996-06-05 2000-07-18 Sumitomo Metal Industries, Ltd. Method of cooling a steel pipe
JP2000144334A (ja) * 1998-11-06 2000-05-26 Daido Steel Co Ltd 耐溶損性に優れたＡｌダイカスト金型用鋼

Also Published As

Publication number Publication date
WO2002059389A3 (fr) 2002-09-19
PT1358359E (pt) 2004-11-30
DE50200545D1 (de) 2004-07-29
WO2002059389A2 (fr) 2002-08-01
TR200402213T4 (tr) 2004-10-21
ATE269911T1 (de) 2004-07-15
CA2424074A1 (fr) 2003-03-28
US20040050459A1 (en) 2004-03-18
EP1358359A2 (fr) 2003-11-05
DK1358359T3 (da) 2004-10-18
DE10103290A1 (de) 2002-08-22
AU2002250853B2 (en) 2006-08-03
CA2424074C (fr) 2011-03-15
JP2004520487A (ja) 2004-07-08
ES2223037T3 (es) 2005-02-16
JP3943499B2 (ja) 2007-07-11

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