EP3061838A1 - Produit longitudinal bainitique nu et son procédé de fabrication - Google Patents

Produit longitudinal bainitique nu et son procédé de fabrication Download PDF

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Publication number
EP3061838A1
EP3061838A1 EP16157945.3A EP16157945A EP3061838A1 EP 3061838 A1 EP3061838 A1 EP 3061838A1 EP 16157945 A EP16157945 A EP 16157945A EP 3061838 A1 EP3061838 A1 EP 3061838A1
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EP
European Patent Office
Prior art keywords
bainitic
long product
bare
bis
steel
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.)
Granted
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EP16157945.3A
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German (de)
English (en)
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EP3061838B1 (fr
Inventor
Mirkka Ingrid LEMBKE
Guido Olschewski
Heiko Haupt-Peter
Hans Roelofs
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Swiss Steel AG
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Swiss Steel AG
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Publication of EP3061838A1 publication Critical patent/EP3061838A1/fr
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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
    • 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
    • C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
    • 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
    • C22C38/02—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
    • C22C38/04—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
    • C22C38/40—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
    • C22C38/48—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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • 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
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the invention relates to a bare bainitic long product according to the preamble of claim 1 and uses thereof and a process for its preparation.
  • Bainitic steels cooled continuously from the forming heat offer similar strength and toughness properties under static load as heat-treated steels with a hardened structure. However, while tempered steels soften under dynamic load, the bainitic steels are solidified. Due to the TRIP effect (deformation-induced transformation of austenite into martensite), bainitic steels also behave more favorably with overloads (voltage peaks). This manifests itself in a higher time stability.
  • bainitic materials with a tensile strength of about 1,300 MPa would increase the performance of common rails or injectors and thus of the entire internal combustion engine.
  • the WO 2009/090155 A1 describes such an application for a bainitic-ferritic material without TRIP effect.
  • EP 2103704 A1 describes such a product.
  • By the manufacturing process described therein can be dispensed with the addition of aluminum and titanium. This avoids the formation of abrasive oxide inclusions.
  • a high sulfur content of 0.04 to 0.25% additionally improves the machinability.
  • the sulfur forms with manganese sulfide inclusions, which on the one hand facilitate the chip breaking and on the other hand form a protective layer on the tool. Tool life and productivity are increased.
  • the manganese sulfides are also material weaknesses, which can cause cracks under dynamic load. This reduces the life expectancy of dynamically loaded components. Therefore, this steel can not be used for highly stressed safety components.
  • EP 1426453 A1 describes a forging of a bainitic steel, which should be suitable for machining.
  • the good machinability in this case also only by alloying with sulfur, tellurium, selenium, bismuth or lead (see there claims 6 and 7). Both the environmental compatibility and the suitability for highly stressed components is thereby limited.
  • WO 2011/124851 refers to components made by forging or machining long steel. It is therefore not drawn components, which are known to have a relatively low yield ratio.
  • the steels described therein have a low silicon content of at most 0.1% by weight.
  • a bright bainitic long product with a bainitic microstructure that can be machined well in machining is currently not yet available for use in dynamically stressed components.
  • the object of the invention is to provide a bright bainitic long product, with which in particular the above disadvantages are avoided. Further objects of the invention relate to uses of the long product according to the invention. Yet another object of the invention is to provide a process for producing a bare bainitic long product.
  • the tensile test according to ISO 6892-1 is a standard procedure for characterizing the mechanical properties of a material. The associated terms are defined in the standard ISO 6892-1.
  • the yield strength Rp0.2 indicates which stress is present at a plastic strain of 0.2%. This parameter is used when there is no sharp transition between elastic and plastic material behavior.
  • the tensile strength Rm is the maximum stress in the measured stress-strain diagram. The tensile strength is reached the moment the sample starts to constrict (local taper of the sample cross-section).
  • the elongation at break A5 is the extension of the sample at the time of fracture, wherein the index 5 refers to the ratio of the initial measuring length L0 to the initial diameter d0.
  • the steel composition according to the invention can be machined significantly better at a constant predetermined tensile strength if the yield ratio Rp0.2 / Rm is above 0.87.
  • the significantly improved machinability manifests itself in significantly longer tool life.
  • the alloying components are selected so that at normal cooling rates from the rolling heat of 0.1 to 8.0 K / s a bainitic-martensitic microstructure always results with a tensile strength level of 900 to 1,200 MPa, without costly Alloy elements and / or special equipment for accelerated cooling from the rolling heat must be used.
  • the product In order to be able to adjust the properties according to the invention, the product must be drawn in the temperature range between room temperature and 600 ° C. and then tempered in a temperature range of 250 and 600 ° C.
  • the yield ratio Rp0.2 / Rm decreases, and according to the invention it is to be maintained above 0.87.
  • the yield ratio Rp0.2 / Rm usually falls below this value.
  • the yield ratio Rp0.2 / Rm is in the range of 0.87 to 0.94.
  • the upper limit of the carbon to 0.26% ensures that the tensile strength does not rise above 1400 MPa. Higher strength values degrade machinability in the downstream drawing or machining process. Higher carbon contents also promote the formation of carbides, which adversely affects ductility.
  • Silicon suppresses the formation of hard and in machining abrasive Fe 3 C precipitates (cementite).
  • the selected silicon concentration allows a one-hour tempering treatment at 400 ° C without coarse Zementitaus- decisions (based on the description of the carbide-free bainite in WO 96/22396 ). Since silicon is an efficient solid solution in the bainite, its content must be limited to at most 1.2 wt .-%, so as not to exceed the maximum desired tensile strength of 1400 MPa.
  • the lower limit in manganese to 1.20% by weight and chromium to 0.70% by weight ensures that a bainitic structure can be produced from the forming heat when the air cools down.
  • the manganese content must be limited to 1.70 wt .-%.
  • Chromium constricts the bainite area, which favors the formation of martensite. For this reason, the chromium content must be limited to 1.60 wt .-%.
  • molybdenum can be alloyed to suppress possible temper embrittlement.
  • the precipitation of iron carbides at the primary grain boundaries and a related loss of toughness can thus be prevented.
  • the molybdenum content is to be chosen as low as necessary and is therefore at most 0.3 wt .-%, in particular about 0.15 to 0.28 wt .-%.
  • Nickel improves notched impact strength and therefore has a negative impact on machinability. Therefore, the nickel content is limited to 0.30 wt%, more preferably about 0.05 to 0.1 wt%.
  • Sulfur is a steel pest. It forms manganese sulfide precipitates and weakens the microstructure. This has a negative effect on the fatigue strength of dynamically loaded components. Because of this, the sulfur content became limited to 0.03 wt .-%. Preferably, the sulfur content is 0.010 to 0.020 wt .-% and in particular about 0.015 wt .-%.
  • the addition of aluminum is not mandatory for the production of the product according to the invention and is therefore at most 0.01% by weight, in particular 0.005 to 0.009% by weight.
  • Phosphorus is a steel pest. It goes to the Austenitkorngrenzen and weakens the structure. This has a negative effect on the fatigue strength of dynamically loaded components. For this reason, the phosphorus content was limited to 0.03 wt .-% and is in particular 0.01 to 0.02 wt .-%.
  • Copper is a steel pest. At high copper contents, red brittleness occurs in hot forming. For this reason, the copper content is limited to 0.25 wt .-% and is in particular 0.1 to 0.2 wt .-%.
  • Hard oxide or nitride inclusions have a negative effect on the machinability above a certain size.
  • titanium titanium oxides and coarse titanium carbonitrides
  • aluminum hard Al 2 O 3 compounds
  • niobium and vanadium a negative effect must also be assumed.
  • the micro-alloying elements titanium, niobium and vanadium are therefore limited to 0.01 wt .-%.
  • Boron is usually alloyed with bainitic steels to suppress the formation of ferrite.
  • the nitrogen present in the steel must be bound with titanium. Because the addition of Titanium is to be avoided, this alloy concept can not be applied here. Boron will therefore be present only in traces to 0.001 wt .-%.
  • oxide inclusions should be set with an Al 2 O 3 content of ⁇ 50 wt .-%.
  • the metallurgical treatment according to claim 4 is carried out so that soft, glassy silicate inclusions arise with the following relative proportions by weight: 20 to 50% CaO, 25 to 65% SiO 2 and less than 30% Al 2 O 3 . The tool life of the tools used in machining is then significantly extended.
  • a heat treatment of up to 2 hours at 300 to 600 ° C. according to claim 7 may be expedient. Tensions introduced by strain hardening are thereby reduced.
  • a steel melt "steel 1" was cast and then rolled into bar steel.
  • the molten steel was produced by the electrical steel process with a secondary metallurgical treatment on a ladle and subsequent casting to 150 ⁇ 150 mm 2 sticks in a continuous casting plant.
  • the billets were then reheated in a walking beam oven to 1'150 to 1'200 ° C and then rolled into bar steel in diameter 043 mm.
  • the cooling of the rods after rolling was carried out in air (cooling rate about 1.0 K / s).
  • the rods were shot peened to remove the iron oxide skin. Thereafter, the rods were either drawn at room temperature or in the temperature range between 350 and 450 ° C by a multi-stage die to the final dimension of 040 mm and directed in a two-roll straightening machine. The final conductive heating at 350 resp. 500 ° C was used to reduce deformation-induced surface tensions.
  • the machinability of the manufactured variants was tested in a standard test at the ISF in Dortmund.
  • the test specimens used were double-turned and one-sided center bored rods with a length of 190 mm.
  • the tests were carried out under the type Becher Avantin 3309 emulsion with a concentration of about 6-8%.
  • the turning tool (CNMG120404-PF4215) was selected to allow the standard steel 42CrMo4 + QT (at Rm ⁇ 1'000 MPa) to have an industrially common machining time of 18 minutes without violating a wear mark width criterion of V Bmax ⁇ 300 ⁇ m.
  • the cutting speed was 200 m / min
  • Table 1 shows the steel compositions used for this comparison.
  • the composition of the existing oxide inclusions was analyzed by scanning electron microscopy using EDX.
  • the structural components of steel 1 were determined quantitatively in the scanning electron microscope (for bainite and ferrite) and in the X-ray diffractometer (for retained austenite). Within the measuring accuracy the differences of the three variants are small. The results are shown in Table 2 for the various heat treatments. For steel 2 there is a 100% compensation structure (tempered martensite). The steels 3 and 4, similar to steel 1, have a mixed structure of bainite, martensite and retained austenite.

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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)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Steel (AREA)
EP16157945.3A 2015-02-27 2016-02-29 Produit longitudinal bainitique nu et son procédé de fabrication Active EP3061838B1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
EP16157945.3A EP3061838B1 (fr) 2015-02-27 2016-02-29 Produit longitudinal bainitique nu et son procédé de fabrication

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
EP15156898.7A EP3061837A1 (fr) 2015-02-27 2015-02-27 Produit longitudinal bainitique nu et son procédé de fabrication
EP16157945.3A EP3061838B1 (fr) 2015-02-27 2016-02-29 Produit longitudinal bainitique nu et son procédé de fabrication

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EP3061838A1 true EP3061838A1 (fr) 2016-08-31
EP3061838B1 EP3061838B1 (fr) 2019-03-13

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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN114811207A (zh) * 2021-01-28 2022-07-29 横滨橡胶株式会社 软管用金属线的规格决定方法及软管
WO2022253912A1 (fr) 2021-06-02 2022-12-08 Ascometal France Holding Sas Pièce en acier mise en forme à chaud et procédé de fabrication

Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1996022396A1 (fr) 1995-01-20 1996-07-25 British Steel Plc Perfectionnements apportes aux aciers bainitiques exempts de carbure, et procedes de production d'aciers de ce type
EP1425453A1 (fr) 2001-07-18 2004-06-09 Eos S.R.L. Fils et toiles ignifuges, leur production et leur utilisation pour la realisation de produits ignifuges, resistants a la chaleur, et isolants
EP1426453A1 (fr) 2002-12-03 2004-06-09 Ascometal Procédé de fabrication d'une pièce forgée en acier et pièce ainsi obtenue
EP1870482A1 (fr) * 2005-03-30 2007-12-26 Kabushiki Kaisha Kobe Seiko Sho Tole d'acier lamine a froid de haute resistance, excellente en terme d'allongement uniforme, et son procede de fabrication
WO2009090155A1 (fr) 2008-01-15 2009-07-23 Robert Bosch Gmbh Élément de construction, en particulier composant pour véhicule automobile, en acier biphasique
EP2103704A1 (fr) 2008-03-10 2009-09-23 Swiss Steel AG Produit longitudinal laminé à chaud et son procédé de fabrication
WO2011124851A2 (fr) 2010-04-07 2011-10-13 Ascometal Pièce mécanique en acier à hautes caractéristiques et son procédé de fabrication
WO2012048841A1 (fr) * 2010-10-12 2012-04-19 Tata Steel Ijmuiden B.V. Procédé de formage à chaud d'un flan d'acier et pièce formée à chaud
EP2557184A1 (fr) * 2011-08-10 2013-02-13 Swiss Steel AG Armature en acier profilée et laminée à chaud pour pièces en béton armé dotées d'une résistance au feu améliorée et son procédé de fabrication

Patent Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1996022396A1 (fr) 1995-01-20 1996-07-25 British Steel Plc Perfectionnements apportes aux aciers bainitiques exempts de carbure, et procedes de production d'aciers de ce type
EP1425453A1 (fr) 2001-07-18 2004-06-09 Eos S.R.L. Fils et toiles ignifuges, leur production et leur utilisation pour la realisation de produits ignifuges, resistants a la chaleur, et isolants
EP1426453A1 (fr) 2002-12-03 2004-06-09 Ascometal Procédé de fabrication d'une pièce forgée en acier et pièce ainsi obtenue
EP1870482A1 (fr) * 2005-03-30 2007-12-26 Kabushiki Kaisha Kobe Seiko Sho Tole d'acier lamine a froid de haute resistance, excellente en terme d'allongement uniforme, et son procede de fabrication
WO2009090155A1 (fr) 2008-01-15 2009-07-23 Robert Bosch Gmbh Élément de construction, en particulier composant pour véhicule automobile, en acier biphasique
EP2103704A1 (fr) 2008-03-10 2009-09-23 Swiss Steel AG Produit longitudinal laminé à chaud et son procédé de fabrication
WO2011124851A2 (fr) 2010-04-07 2011-10-13 Ascometal Pièce mécanique en acier à hautes caractéristiques et son procédé de fabrication
WO2012048841A1 (fr) * 2010-10-12 2012-04-19 Tata Steel Ijmuiden B.V. Procédé de formage à chaud d'un flan d'acier et pièce formée à chaud
EP2557184A1 (fr) * 2011-08-10 2013-02-13 Swiss Steel AG Armature en acier profilée et laminée à chaud pour pièces en béton armé dotées d'une résistance au feu améliorée et son procédé de fabrication

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
BIERMANN, D.; HARTMANN, H.: "Innovative Bearbeitungsverfahren für die wirtschaftliche Fertigung", STAHL- UND GUSSZERSPANUNG, 2013, pages 129 - 138

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN114811207A (zh) * 2021-01-28 2022-07-29 横滨橡胶株式会社 软管用金属线的规格决定方法及软管
CN114811207B (zh) * 2021-01-28 2023-11-10 横滨橡胶株式会社 软管用金属线的规格决定方法及软管
WO2022253912A1 (fr) 2021-06-02 2022-12-08 Ascometal France Holding Sas Pièce en acier mise en forme à chaud et procédé de fabrication
FR3123659A1 (fr) 2021-06-02 2022-12-09 Ascometal France Holding Sas Pièce en acier mise en forme à chaud et procédé de fabrication

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EP3061837A1 (fr) 2016-08-31

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