EP1586671B1 - Acier au chrome déformable à froid - Google Patents

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EP1586671B1
EP1586671B1 EP05000782A EP05000782A EP1586671B1 EP 1586671 B1 EP1586671 B1 EP 1586671B1 EP 05000782 A EP05000782 A EP 05000782A EP 05000782 A EP05000782 A EP 05000782A EP 1586671 B1 EP1586671 B1 EP 1586671B1
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Prior art keywords
steel
chromium
bis
minutes
precipitates
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EP1586671A1 (fr
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Oskar Pacher
Guido Nicolini
Gisbert Kloss-Ulitzka
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Stahlwerk Ergste Westig GmbH
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Stahlwerk Ergste Westig GmbH
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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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/02—Modifying the physical properties of iron or steel by deformation by cold 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys 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
    • C21D9/0068—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for particular articles not mentioned below
    • 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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C22C38/007—Ferrous alloys, e.g. steel alloys containing silver
    • 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
    • C22C38/18—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
    • C22C38/50—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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals

Definitions

  • the invention relates to a cold-formable chromium steel with ferritic microstructure.
  • Cold-formable and corrosion-resistant ferritic chromium steels possess poor machinability without special alloying measures, which can be attributed to adhesions and welds that occur in the area of sharp tool edges during machining. The consequence of this is breakage and chipping of the cutting edge or a high tool wear and also a low surface quality of the machined workpieces.
  • adhesions and welds also have a very disadvantageous effect, since they preferably occur in the area of high surface pressure and there worsen the surface quality of the formed workpieces. In addition, they shorten the service life of the tools.
  • the steels require a certain minimum strength which can only be achieved by alloy constituents which form carbides or carbonitrides such as titanium, vanadium, niobium, zirconium and molybdenum. These are present in the microstructure as hard and poorly soluble precipitation phases and tend to accumulate locally in the microstructure and thus to form agglomerates, nests or linear structures.
  • Steels of the type mentioned are known. They have a good magnetizability, as in the U.S. Patent 4,714,502 described soft magnetic chromium steel with up to 0.03% carbon, 0.40 to 1.10% silicon, up to 0.50% manganese, 9.0 to 19% chromium, up to 2.5% molybdenum, up to 0.5% nickel, to 0.5% copper, 0.02 to 0.25% titanium, 0.010 to 0.030% sulfur, to 0.03% nitrogen, 0.31 to 0.60% aluminum, 0.10 to 0.30% lead and 0.02 to 0.10% zirconium.
  • the steel is stainless and cold formable; it is suitable as a material for producing cores for solenoid valves, electromagnetic clutches or housings of electronic injection systems for internal combustion engines.
  • Another soft magnetic stainless chromium steel with up to 0.05% carbon, up to 6% silicon, 11 to 20% chromium, up to 5% aluminum, 0.03 to 0.40% lead, 0.001 to 0.009% calcium and 0.01 to 0 , 30% tellurium is from the U.S. Patent 3,925,063 known and has due to its contents of lead, calcium and tellurium a good machinability.
  • German Offenlegungsschrift describes 101 43 390 A1 a cold-workable, corrosion resistant ferritic chromium steel containing 0.005% to 0.1% carbon, 0.2% to 1.2% silicon, 0.4% to 2.0% manganese, 8% to 20% chromium, 0.1% to 1 , 2% molybdenum, 0.01% to 0.5% nickel, 0.5% to 2.0% copper, 0.001% to 0.6% bismuth, 0.002% to 0.1% vanadium, 0.002% to 0, 1% titanium, 0.002% to 0.1% niobium, 0.15% to 0.8% sulfur and 0.001% to 0.08% nitrogen, the remainder iron, including impurities caused by melting, which, due to its good machinability, in particular its good machinability , its good wear resistance and surface quality as a material for fine mechanical applications and precision equipment, especially for spinning and spray nozzles and writing instruments, tips and heads.
  • the European disclosure 1 288 323 A1 also describes a ferritic cold-formable corrosion resistant chromium steel having 8 to 20% chromium, 0.005 to 0.1% carbon, to 0.08% nitrogen, 0.2 to 1.2% silicon, 0.4 to 2.0% manganese, 0 , 05 to 1.2% molybdenum, 0.01 to 0.5% nickel, 0.5 to 2.0% copper and up to 0.05% lead, selenium and / or tellurium.
  • this steel is as free of arsenic as one from the Japanese patent application 2001-131 716 known ferritic steel with 15.0 to 25.0% chromium to 0.12% carbon, to 0.05% nitrogen, 0.05 to 1.00% silicon, 0.50 to 2.50% manganese, 0.01 to 0.50% nickel, 0.01 to 0.50% copper, 0.02 to 0.25% sulfur and 0.0050 to 0.00400% oxygen, which also includes molybdenum, selenium, lead, bismuth, niobium , Vanadium, titanium and zirconium in an undisclosed amount.
  • the problem underlying the invention is a ferritic chromium steel To create, which not only excellently, ie in particular without the formation of adhesions and welds chop but also directionally accurate micro-work leaves.
  • the mechanical properties of the steel according to the invention depend not only on the presence of certain precipitation phases, but also very much on their physical properties and distribution in the microstructure.
  • the microstructure therefore contains both metal sulfides and metal selenides, which in turn interact with carbides and sulfocarbides and thereby bring about an improvement in the chip breaking behavior.
  • the invention seeks to release certain alloying elements in the vicinity of the precipitates by means of rearrangement and exchange reactions so as to surround the hard precipitates with a lubricant zone of metals and / or metal compounds which act as lubricant zones and improve machinability.
  • Precipitates of sulfides, selenides or tellurides or mixtures thereof, as well as precipitates due to rearrangement or exchange reactions with carbides form at different temperatures in the solid state of the steel.
  • primary exudates are formed, which grow on further cooling, coarsen and cause the known disadvantages.
  • inventive tuning certain elements such as lead and / or bismuth and / or arsenic and / or antimony and / or vanadium, titanium, niobium and zirconium with the excretors carbon, nitrogen, sulfur, selenium and tellurium results in a very large number of reaction options that prevent the harmful growth of primary excretions.
  • the non-metallic precipitants - carbon, sulfur, selenium, tellurium and optionally nitrogen - are present in low concentration to avoid supersaturation, otherwise rapidly growing coarse precipitates form. These would be very difficult to reduce or dissolve in their grain size. It is particularly important to have a low carbon content in order to shift the reaction equilibrium towards the formation of substoichiometric carbides.
  • precipitation preferably forms on cooling
  • diffusion effects solid-state diffusion in the steel
  • low atomic mass elements diffuse easier and faster than heavy atoms.
  • carbides and nitridic precipitates are very easily formed, which are called primary exudations. Only after their elimination arise sulfides and / or selenides or other excretions such as sulfocarbides and sulfocarboselenides.
  • the substoichiometric primary carbides are formed according to the equation Me I + xC ⁇ Me I C x , (1) where Me I denotes the elements titanium, vanadium, niobium and zirconium and x is the stoichiometric factor.
  • Me I denotes the elements titanium, vanadium, niobium and zirconium and x is the stoichiometric factor.
  • these elements can also react with nitrogen, sulfur and selenium (tellurium). This produces sulfocarbides, sulfoselenides or sulfocarboselenides.
  • Sub stoichiometric precipitates are thus also very reactive after their formation.
  • the composition of the primary carbides (or primary precipitates) of the Me I metals can vary widely without sacrificing the lattice structure of the precipitates.
  • titanium carbide has a particularly wide range of resistance. This ranges from TiC 0.22 to TiC 1.0 .
  • Equation 1 would be for titanium: Ti + 0.5 C ⁇ TiC 0.5 (1a)
  • Me I elements do not form carbides, carbonitrides, and consequently no sulfocarbides.
  • precipitates that have already formed are dissolved and new ones formed and, for example, copper can also be produced which acts as a lubricant in the vicinity of the primary precipitates. Since the rearrangement reactions take place predominantly during cooling, the precipitates are inevitably very fine. For the rearrangement reactions, it is beneficial if sufficient time is available, since the mass transfer for the rearrangement reactions by diffusion occurs.
  • a slow cooling or holding times at 700 to 500 ° C and / or a final heat treatment.
  • Dissolution reactions according to Equation 4 are very important, since they advantageously dissolve or dissolve coarse or line-shaped Me "sulfides (for example manganese sulfides), forming-according to Equation 4-new very fine microscopic precipitates. Steel therefore has a structure with many fine precipitates ( Fig. 4 ).
  • the steel should first be subjected to one or more deformations that are as strong as possible, which leads to sliding displacements and to an improved thorough mixing of the structural constituents. Furthermore, the distances between the precipitations are advantageously changed and depletion zones are reduced.
  • a particular advantage of the strong deformation lies in the shortening of the diffusion paths, which in turn causes a significant increase in the reactivity.
  • the preferably cold-worked steel is annealed at 750 to 1080 ° C ( Fig. 5 ).
  • dissolution and release reactions take place with the formation of new or compositionally altered precipitates, for example according to Equation 4.
  • final annealing may take place at up to 450 ° C to solidify liberated lubricant metals or newly formed ultrafine precipitates, cure in the steel matrix, relieve stress, and adjust the hardness or strength of the steel.
  • a progressive decrease in hardness can already occur at a temperature of> 350 ° C, which suggests that the matrix has softened.
  • the steel is annealed after at least one cold work with a degree of deformation of over 65% for 30 to 60 minutes at 750 to 1080 ° C and then cooled within 30 to 180 minutes with low energy input to a temperature of 500 to 700 ° C ( Fig. 5 ).
  • the precipitates formed during annealing are stabilized in a diffusion-controlled manner.
  • the steel is kept at a temperature of, for example, 680 ° C by a short-term increase in the supply of heat ( Fig. 5 , Equation 4).
  • Table I the compositions of the falling under the invention alloy E2 and of comparative alloys E1, E3 to E5 and V1 to V8 are compiled.
  • Table II shows the respective K1, K2 and K3 values as well as the results of the processing trials.
  • BV denotes a characteristic for the bore progression
  • BG the degree width
  • BWG an index for the surface quality.
  • a raw wire of the composition E2 with a diameter of 6 mm was after a pickling initially subjected to a three-stage cold working with a total deformation of 85% and then annealed for 30 minutes at a temperature of 840 ° C in a protective gas atmosphere and then controlled within 120 minutes to a Temperature of 600 ° C cooled. During cooling, a two-minute 15 minute intermediate heating at a temperature of 760 or 680 ° C took place without raising the temperature in order to achieve a stepped cooling to stabilize the precipitates (cf. Fig. 5 ).
  • the wire was cooled in air without further energy input and then calibrated at 15% strain rate. The calibration was followed by a 15 minute final anneal at 340 ° C. The wire had excellent machinability with micro tools.
  • a raw wire of the non-inventive composition E3 with a diameter also of 6 mm was again subjected to a three-stage cold working with a degree of deformation of 80% and then annealed at 900 ° C for 35 minutes under inert gas and from the annealing temperature within 160 minutes with low energy constant cooling rate initially cooled to a temperature of 620 ° C cooled. This was followed by a cooling in air to room temperature.
  • the wire was then calibrated to a degree of deformation of 20% and tempered at 280 ° C for 30 minutes and subjected to a micromachining machined condition with the results reported in Table II.
  • the degree of width BG at the edge of the hole was measured at an angle of 20 to 30 °.
  • the machinability in terms of the extent and frequency of eruptions and breakouts inside the bore, was determined microscopically and found to have a BWG value of 1 to 4.
  • the BWG value of 1 indicates an error-free hole, while a BWG value of 4 indicates strong flare-outs.
  • the representation in Fig. 7 illustrates a smooth bore with a BWG value of 1, while the representation in Fig. 8 a hole with numerous Ausroökelept and a BWG value of 4 reflects.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
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  • Heat Treatment Of Steel (AREA)

Claims (12)

  1. Acier au chrome composé de
    14 % à 20 % de chrome,
    0,005 % à 0,05 % de carbone,
    jusqu'à 0,01 % d'azote,
    0,2 % à 0,6 % de silicium,
    0,3% à 1,0 % de manganèse,
    0,1 % à 1,0 % de molybdène,
    jusqu'à 0,8 % de nickel,
    0,2 % à 1,0 % de cuivre,
    0,02 % à 0,2 % de sélénium,
    0,01 % à 0,1 % d'arsenic,
    ainsi que séparément ou simultanément
    0,01 % à 0,1 % de plomb,
    0,01 % à 0,5 % de bismuth,
    0,01 % à 0,1 % d'antimoine,
    0,005 % à 0,08 % de vanadium,
    0,005 % à 0,08 % de titane,
    0,005 % à 0,08 % de niobium,
    0,005 % à 0,08 % de zirconium,
    0,15 % à 0,65 % de soufre,
    jusqu'à 0,20 % de tellure,
    le reste comprenant des impuretés de fer conditionnées par la fusion.
  2. Acier au chrome selon la revendication 1, composé de
    14 % à 18 % de chrome,
    0,01 % à 0,03 % de carbone,
    jusqu'à 0,01 % d'azote,
    0,3 % à 0,5 % de silicium,
    0,4 % à 0,7 % de manganèse,
    0,1 % à 0,6 % de molybdène,
    jusqu'à 0,5 % de nickel,
    0,2 % à 0,6 % de cuivre,
    0,02 % à 0,2 % de sélénium,
    0,01 % à 0,05 % d'arsenic,
    ainsi que séparément ou simultanément
    0,01 % à 0,05 % de plomb,
    0,01 % à 0,3 % de bismuth,
    0,01 % à 0,05 % d'antimoine,
    0,005 % à 0,08 % de vanadium,
    0,005 % à 0,08 % de titane,
    0,005 % à 0,08 % de niobium,
    0,005 % à 0,08 % de zirconium,
    0,15 % à 0,65 % de soufre,
    0,01 % à 0,20 % de tellure,
    le reste comprenant des impuretés de fer conditionnées par la fusion.
  3. Acier au chrome selon la revendication 1 ou 2, caractérisé par la condition K ⁢ 1 = % Ti + % V + % Nb + % Zr / % C = 3 à 12.
    Figure imgb0011
  4. Acier au chrome selon l'une des revendications 1 à 3, caractérisé par la condition K ⁢ 2 = % S + 3 % Se + 3 % Te / 10 % C + % N = 1 , 5 à 3 , 5.
    Figure imgb0012
  5. Acier au chrome selon l'une des revendications 1 à 4, caractérisé par la condition % S / % S + % Se + % Te = 0 , 68 à 0 , 98.
    Figure imgb0013
  6. Procédé de traitement thermique d'un acier déformé à froid ayant la composition selon l'une des revendications 1 à 5, caractérisé en ce que l'acier, après au moins une déformation à froid selon un degré de déformation de 65 % à 90 % au total, est soumis à recuit pendant 30 à 60 minutes, à une température comprise entre 750 et 1080 °C.
  7. Procédé selon la revendication 6, caractérisé en ce que l'acier est refroidi depuis la température de recuit jusqu'à 700 à 500 °C en l'espace de 30 à 180 minutes, avec un faible apport d'énergie.
  8. Procédé selon la revendication 7, caractérisé en ce que la température de l'acier pendant le refroidissement est maintenue approximativement constante au moins une fois pendant 10 à 30 minutes.
  9. Procédé selon l'une des revendications 6 à 8, caractérisé en ce que l'acier est finalement soumis pendant au moins 30 minutes à une augmentation de la température jusqu'à 450 °C au maximum.
  10. Utilisation d'un alliage selon l'une des revendications 1 à 9 pour fabriquer des objets destinés à l'usinage avec des outils de façonnage.
  11. Utilisation d'un alliage selon l'une des revendications 1 à 9 en tant que matériau pour des objets qui sont fabriqués par micro-usinage par enlèvement de copeaux.
  12. Utilisation d'un alliage selon l'une des revendications 1 à 9 pour fabriquer des buses d'imprimante, des pointes de stylo, des injecteurs pour appareils chimiques et électroniques, des filières, ainsi que des objets présentant de petites dimensions et/ou de petits évidements.
EP05000782A 2004-04-01 2005-01-15 Acier au chrome déformable à froid Expired - Lifetime EP1586671B1 (fr)

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DE102004015992 2004-04-01
DE102004015992 2004-04-01
DE102004063161A DE102004063161B4 (de) 2004-04-01 2004-12-29 Kaltverformbarer Chromstahl
DE102004063161 2004-12-29

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EP1586671B1 true EP1586671B1 (fr) 2010-06-09

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US (2) US20050217769A1 (fr)
EP (1) EP1586671B1 (fr)
CN (1) CN100434563C (fr)
DE (1) DE102004063161B4 (fr)
ES (1) ES2347255T3 (fr)

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JP2010116622A (ja) * 2008-11-14 2010-05-27 Nisshin Steel Co Ltd ヒートパイプ用フェライト系ステンレス鋼および鋼板並びにヒートパイプおよび高温排熱回収装置
DE102009038386A1 (de) 2009-08-24 2011-03-03 Stahlwerk Ergste Gmbh Weichmagnetischer ferritischer Chromstahl
UA111115C2 (uk) 2012-04-02 2016-03-25 Ейкей Стіл Пропертіс, Інк. Рентабельна феритна нержавіюча сталь
CN110819906A (zh) * 2019-11-12 2020-02-21 武汉科技大学 一种改善残余元素Cu、As、Sn恶化冷轧带钢深冲性能的方法
JP7427722B2 (ja) 2022-07-12 2024-02-05 東北特殊鋼株式会社 被削性に優れた析出硬化型軟磁性フェライト系ステンレス鋼

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DE102004063161A1 (de) 2005-11-03
ES2347255T3 (es) 2010-10-27
US20100136357A1 (en) 2010-06-03
EP1586671A1 (fr) 2005-10-19
CN1676655A (zh) 2005-10-05
US20050217769A1 (en) 2005-10-06
CN100434563C (zh) 2008-11-19

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