EP2799582B1 - Acier austénitique résistant à l'usure et présentant une ductilité améliorée, et son procédé de production - Google Patents

Acier austénitique résistant à l'usure et présentant une ductilité améliorée, et son procédé de production Download PDF

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EP2799582B1
EP2799582B1 EP12862562.1A EP12862562A EP2799582B1 EP 2799582 B1 EP2799582 B1 EP 2799582B1 EP 12862562 A EP12862562 A EP 12862562A EP 2799582 B1 EP2799582 B1 EP 2799582B1
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Prior art keywords
steel
comparative sample
carbides
carbon
manganese
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German (de)
English (en)
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EP2799582A1 (fr
EP2799582A4 (fr
Inventor
Soon-Gi Lee
Jong-Kyo Choi
Hee-Goon Noh
Hyun-Kwan Cho
In-Shik Suh
Hak-Cheol Lee
In-Gyu Park
Hong-Ju Lee
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Posco Holdings Inc
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Posco Co Ltd
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Priority claimed from KR1020110145213A external-priority patent/KR101353665B1/ko
Priority claimed from KR1020120151507A external-priority patent/KR101461735B1/ko
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Publication of EP2799582A4 publication Critical patent/EP2799582A4/fr
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    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/02—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling heavy work, e.g. ingots, slabs, blooms, or billets, in which the cross-sectional form is unimportant ; Rolling combined with forging or pressing
    • B21B1/026—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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot 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
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • 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
    • C22C38/04—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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing 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
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/36—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.7% by weight of carbon
    • 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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese

Definitions

  • the present disclosure relates to wear resistant austenitic steel having superior ductility, and a method for producing the wear resistant austenitic steel.
  • Hadfield steel having high wear resistance has been mainly been used.
  • Hadfield steel is high-strength steel having a high manganese content, and there have been steady efforts to improve the wear resistance of such steel by adding large amounts of carbon and manganese thereto to increase the formation of austenite and wear resistance therein.
  • carbides may be formed at high temperature in a network manner along austenite grain boundaries of the Hadfield steel, and thus the physical properties of the Hadfield steel (particularly, ductility) are markedly worsened.
  • alloying elements such as manganese or carbon inevitably segregate in a high-manganese ingot or slab during solidification, and such segregation is facilitated in a post processing process such as a hot rolling process.
  • carbides may partially precipitate in the form of a network along intensive segregation zones of a final product, and thus the microstructure of the final product may be inhomogeneous, resulting in poor physical properties.
  • the content of carbon in steel may be increased to improve the wear resistance of steel, and the content of manganese in the steel may be increased to prevent the deterioration of physical properties of the steel caused by the precipitation of carbides.
  • this method increases the amounts of alloying elements and thus the manufacturing cost of steel.
  • the addition of manganese to steel decreases the corrosion resistance of the steel as compared with general carbon steel. Thus, such steel may not be used in fields requiring corrosion resistant steel.
  • Ru 2102518 C1 discloses steel comprising(wt %): 0.9-1.4 carbon; 9.0-14.5 manganese; 0.30-0.65 silicon; 0.10-0.20 titanium; 0.020-0.120 phosphorus; 0.005-0.05 sulfur; 0.03-0.55 zirconium; 0.8-1.2 copper; 0.20-0.30 vanadium; 0.005-0.015 calcium; 0.001-0.005 barium; 0.05-0.20 strontium; 0.01-0.14 aluminium; and iron as balance.
  • WO 2007/024092 A1 discloses a hot rolled steel sheet comprising, by weight%, C: 0.2% ⁇ 1%, Mn: 8 ⁇ 15%, S: 0.05% or less, P: 0.03% or less, and the balance of Fe and other unavoidable impurities.
  • WO 03/060174 A1 discloses a corrosion and erosion resistant High Chromium, Nitrogen bearing alloy, comprising the following composition in wt. %: 28 - 48 chromium, 0.01 - 0.7 nitrogen, 0.5 - 30 manganese, 0.01 - 5 boron, 0.3 - 2.5 carbon, up to 0.01 - 25 cobalt plus nickel, up to 0.01 - 5 silicon, up to 0.01 - 8 copper, up to 0.01 - 6 molybdenum, up to 2% of each one selected from group consisting of zirconium, vanadium, cerium, titanium, tungsten, niobium, aluminum, calcium, and rare earth elements with the balance being essentially iron and other trace elements or inevitable impurities.
  • aspects of the present disclosure may provide austenitic steel having improved ductility, and wear resistance through suppressing the formation of carbides, and a method for producing the austenitic steel.
  • wear resistant austenitic steel having superior ductility consists of, by weight%, 8% to 15% of manganese (Mn), carbon (C) satisfying 23 ⁇ 33.5C-Mn ⁇ 37%, copper (Cu) satisfying 1.6C-1.4(%) ⁇ Cu ⁇ 5%, 2% to 8% of chromium (Cr), and, optionally, 0.03% to 0.1% of sulfur (S) and 0.001% to 0.01% of calcium (Ca), and the balance of iron (Fe) and inevitable impurities, wherein the wear resistant austenitic steel has a microstructure comprising 90 area% or more of austenite, and wherein the wear resistant austenitic steel comprises 10 area% or less of carbides.
  • a method for producing wear resistant austenitic steel having superior ductility includes: reheating a steel slab to a temperature of 1050°C to 1250°C, the steel slab consists of, by weight%, 8% to 15% of manganese (Mn), carbon (C) satisfying 23 ⁇ 33.5C-Mn ⁇ 37%, copper (Cu) satisfying 1.6C-1.4(%) ⁇ Cu ⁇ 5%, 2% to 8% of chromium (Cr), and ,optionally, 0.03% to 0.1% of sulfur (S) and 0.001% to 0.01% of calcium (Ca), and the balance of iron (Fe) and inevitable impurities; performing a finish hot rolling process on the steel slab within a temperature range of 800°C to 1050°C to form a steel sheet; and cooling the hot-rolled steel sheet to a temperature of 600°C or lower at a cooling rate of 10°C/s to 100°C/s, wherein the wear resistant austenitic steel has a microstructure
  • the formation of carbides in the austenitic steel may be suppressed to prevent the deterioration of the austenitic steel, and the wear resistance of the austenitic steel may be sufficiently improved. Therefore, the austenitic steel may be used for an extended period of time, even in corrosive environments.
  • wear resistant austenitic steel having superior ductility and a method for producing the wear resistant austenitic steel will be described in detail according to embodiments of the present disclosure, so that those of ordinary skill in the related art may clearly understand the scope of the embodiments of the present disclosure.
  • the inventors found that if the composition of steel is properly adjusted, the steel has a high degree of wear resistance without a decrease in ductility caused by carbides and a high degree of machinability. Based on this knowledge, the inventors invented wear resistant austenitic steel and a method of producing the wear resistant austenitic steel.
  • manganese and carbon are added to the steel of the embodiments of the present disclosure to improve the wear resistance of the steel while controlling the content of the carbon relative to the content of the manganese to minimize the formation of carbides. Furthermore, additional elements are added to the steel to further suppress the formation of carbides and thus to sufficiently improve the toughness of the steel in addition to improving the wear resistance of the steel, and in conjunction therewith, the contents of calcium and sulfur in the steel are adjusted to markedly improve the machinability of the steel (austenitic high-manganese steel).
  • the steel includes, by weight%, 8% to 15% of manganese (Mn), carbon (C) satisfying 23 ⁇ 33.5C-Mn ⁇ 37%, copper (Cu) satisfying 1.6C-1.4(%) ⁇ Cu ⁇ 5%, 2% to 8% of chromium (Cr), and ,optionally, 0.03% to 0.1% of sulfur (S) and 0.001% to 0.01% of calcium (Ca) and the balance of iron (Fe) and inevitable impurities, wherein the wear resistant austenitic steel has a microstructure comprising 90 area% or more of austenite, and wherein the wear resistant austenitic steel comprises 10 area% or less of carbides.
  • Mn manganese
  • C carbon
  • Cu copper
  • Cr chromium
  • S sulfur
  • Fe iron
  • the wear resistant austenitic steel has a microstructure comprising 90 area% or more of austenite
  • the wear resistant austenitic steel comprises 10 area% or less of carbides.
  • Manganese is a main element for stabilizing austenite in high manganese steel like the steel of the embodiments of the present disclosure.
  • the content of manganese is 8% or greater for forming austenite as a main component of the microstructure of the steel. If the content of manganese is less than 8%, ferrite may be formed, and thus austenite may not be sufficiently formed.
  • the content of manganese is greater than 15%, problems such as decrease in a corrosion resistance of the steel, increase in difficulties in the manufacturing process and increase in manufacturing costs may occur. Also, the work hardenability of the steel may be decreased due to a decreased in tensile strength.
  • Carbon is an element for stabilizing austenite and forming austenite at room temperature. Carbon increases the strength of the steel. Particularly, carbon dissolved in austenite of the steel increases the work hardenability of the steel and thus increases the wear resistance of the steel. However, as described above, if the content of carbon in the steel is insufficient, the stability of austenite is low, and the wear resistance of the steel may be insufficient due to the formation of martensite or a low degree of work hardenability of austenite. On the other hand, if the content of carbon in the steel is excessive, it is difficult to suppress the formation of carbides.
  • the content of carbon in the steel may be determined according to the contents of other elements in the steel.
  • the inventors found a relationship between carbon and manganese in the formation of carbides, and the relationship is illustrated in FIG. 1 .
  • carbides are formed from carbon, the formation of carbides is not affected only by carbon but is affected by a ratio of carbon and manganese.
  • FIG. 1 illustrates a proper content of carbon in relation to the content of manganese.
  • the value of 33.5C-Mn is adjusted to be 37 or less (where C and Mn refer to the content of carbon and the content of manganese in weight%), so as to prevent the formation of carbides. This corresponds to the right boundary of the parallelogram region in FIG. 1 . If 33.5C-Mn is greater than 37, carbides may be formed to a degree worsening the ductility of the steel. However, if the content of carbon in the steel is too low (that is, if 33.5C-Mn is less than 23), the wear resistance of the steel may not be improved by the work hardenability of the steel. Therefore, 33.5C-Mn is equal to or greater than 23. That is, the content of carbon satisfies 23 ⁇ 33.5C-Mn ⁇ 37.
  • copper Due to a low solid solubility of copper in carbides and a low diffusion rate of copper in austenite, copper tends to concentrate in interfaces between austenite and carbides. Therefore, if fine carbide nuclei are formed, copper may surround the fine carbide nuclei, and thus additional diffusion of carbon and growth of carbides may be retarded. That is, copper suppresses the formation and growth of carbides. Therefore, in the embodiments of the present disclosure, copper is added to the steel.
  • the content of copper in the steel is not independently determined but may be determined according to the formation behavior of carbides. For example, the content of copper is set to be equal to or greater than 1.6C-1.4 weight% so as to effectively suppress the formation of carbides.
  • the content of copper in the steel is less than 1.6C-1.4 weight%, the conversion of carbon into carbides may not be suppressed.
  • the content of copper in the steel is greater than 5 weight%, the hot workability of the steel may be lowered. Therefore, the upper limit of the content of copper is set to 5 weight%.
  • the content of copper may preferably be 0.3 weight% or greater, more preferably, 2 weight% or greater, so as to obtain a sufficient effect of suppressing the formation of carbides.
  • the other component of the steel is iron (Fe).
  • Fe iron
  • impurities in raw materials or manufacturing environments may be inevitably included in the steel, and such impurities may not be able to be removed from the steel.
  • Such impurities are well-known to those of ordinary skill in the art to which the present disclosure pertains, and thus descriptions thereof will not be given in the present disclosure.
  • sulfur (S) and calcium (Ca) may be further included in the steel in addition to the above-described elements, so as to improve the machinability of the steel.
  • sulfur added together with manganese forms manganese sulfide which is easily cut and separated during a cutting process. That is, sulfur is known as an element improving the machinability of steel. Sulfur is melted by heat generated during a cutting process, and thus reduces friction between chips and cutting tools. That is, sulfur increases the lifespan of cutting tools by lubricating the surface of the cutting tools, reducing the wear on the cutting tools, and preventing accumulation of cutting chips on the cutting tool.
  • the upper limit of the content of sulfur in the steel is 0.1%. If the content of sulfur in the steel is less than 0.03%, the machinability of the steel may not be improved, and thus the lower limit of the content of sulfur in the steel is 0.03%
  • Calcium is usually used to control the formation of manganese sulfide. Since calcium has a high affinity for sulfur, calcium forms calcium sulfide together with sulfur, and along with this, calcium is dissolved in manganese sulfide. Since manganese sulfide crystallizes around calcium sulfide functioning as crystallization nuclei, during a hot working process, manganese sulfide may be less elongated and may be maintained in a spherical shape. Therefore, the machinability of the steel may be improved. However, if the content of calcium is greater than 0.01%, the above-described effect is saturated.
  • the percentage recovery of calcium is low, a large amount of calcium raw material may have to be used, and thus the manufacturing cost of the steel may be increased.
  • the content of calcium in the steel is less than 0.001%, the above-described effect is insignificant.
  • the lower limit of the content of calcium is 0.001%.
  • chromium (Cr) is included in the steel in addition to the above-described elements so as to further improve the corrosion resistance of the steel.
  • manganese lowers the corrosion resistance of steel. That is, in the embodiments of the present disclosure, manganese included in the steel in the above-described content range may lower the corrosion resistance of the steel, and thus chromium is added to the steel to improve the corrosion resistance of the steel. In addition, if chromium is added to the steel in an amount within the above-described range the strength of the steel may also be improved. However, if the content of chromium in the steel is greater than 8 weight%, the manufacturing cost of the steel is increased, and carbon dissolved in the steel may be converted into carbides along grain boundaries to lower the ductility of the steel and particularly resistance of the steel to sulfide stress cracking.
  • the steel may be formed in the steel, and thus austenite may not be formed as a main microstructure in the steel. Therefore, the upper limit of the content of chromium is 8 weight%. Particularly, to maximize the effect of improving the corrosion resistance of the steel, the content of chromium in the steel is set to be 2 weight% or greater. Since the corrosion resistance of the steel is improved by the addition of chromium, the steel may be used for forming slurry pipes or as an anti sour gas material.
  • the steel having the above-described composition is austenitic steel having 90 area% or more of austenite.
  • austenite of the steel may be markedly hardened, and thus the steel may have a high degree of hardness.
  • some other microstructures such as martensite, bainite, pearlite, and ferrite may be inevitably formed in the steel as impurity microstructures.
  • the sum of the amounts of the phases of the steel is put as 100%, and the content of each microstructure is denoted as a proportion of the sum without considering the amounts of precipitates such as a carbide precipitate.
  • the steel includes 10 area% or less of carbides (based on the total area of the steel). Since carbides lower the ductility of the steel, the amounts of carbides in the steel may be adjusted to be low. For example, in the embodiments of the present disclosure, since the area fraction of carbides in the steel is 10% or less, when the steel is used as wear resistant steel, problems caused by low ductility such as premature fracturing and a decrease in impact toughness may not arise.
  • the steel may be produced by a manufacturing method commonly known in the related art, and the manufacturing method of the related art may include a conventional hot rolling process in which a slab is reheated, roughly-rolled, and finish-rolled. After the hot rolling process, the steel may be cooled by a conventional cooling method.
  • the steel is produced by an exemplary method proposed by the inventors as follows.
  • a steel slab is prepared, which includes, by weight%, 8% to 15% of manganese (Mn), carbon (C) satisfying 23 ⁇ 33.5C-Mn 37%, copper (Cu) satisfying 1.6C-1.4(%) ⁇ Cu ⁇ 5%, 2% to 8% of chromium (Cr), and, optionally 0.03% to 0.1% of sulfur (S) and 0.001% to 0.01% of calcium (Ca) and the balance of iron (Fe) and inevitable impurities.
  • Mn manganese
  • carbon C
  • Cu copper
  • Cr chromium
  • S sulfur
  • Fe iron
  • the steel slab is reheated to a temperature of 1050°C to 1250°C.
  • the steel slab (or ingot) may be reheated in a reheating furnace for a hot rolling process. If the steel slab is reheated to a temperature lower than 1050°C, the load acting on a rolling mill may be markedly increased, and alloying elements may not be sufficiently dissolved in the steel slab. On the other hand, if the reheating temperature of the steel slab is too high, crystal grains may excessively grow, and thus the strength of the steel slab may be lowered. Particularly, in the above-described composition range of the steel of the present disclosure, carbides may melt in grain boundaries, and if the steel slab is reheated to a temperature equal to or higher than the solidus line of the steel slab, hot-rolling characteristics of the steel slab may deteriorate. Therefore, the upper limit of the reheating temperature is set to be 1250°C.
  • the steel slab is finish-rolled at a temperature of 800°C to 1050°C to form a steel sheet.
  • the steel slab is rolled within the temperature range of 800°C to 1050°C. If the steel slab is rolled at a temperature lower than 800°C, the load of rolling may be large, and carbides may precipitate and grow coarsely. Thus, desired ductility may not be obtained.
  • the upper limit of the rolling temperature is set to be 1050 °C.
  • the steel sheet formed by hot rolling is cooled to a temperature of 600°C or lower at a cooling rate of 10°C/s to 100°C/s.
  • the steel sheet may be cooled at a sufficiently high cooling rate to suppress the formation of carbides in grain boundaries. If the cooling rate is less than 10°C/s, the formation of carbides may not be sufficiently suppressed, and thus carbides may precipitate in grain boundaries during cooling. This may cause problems such as premature fracture, a ductility decrease, and a wear resistance decrease. Therefore, the cooling rate may be adjusted to be high, and the upper limit of the cooling rate is limited to 100° C/s.
  • the steel sheet is cooled at a high cooling rate, if the cooling of the steel sheet is terminated at a high temperature, carbides may be formed and grow in the steel sheet. Therefore, in the embodiment of the present disclosure, the steel sheet is cooled to a temperature of 600°C or lower.
  • Comparative Sample A1 33.5C-Mn of Comparative Sample A1 was 6.8 which was outside of the range of the embodiments of the present disclosure. Thus, due to a lack of carbon stabilizing austenite, a large amount of martensite was formed in Comparative Sample A1, and a desired austenitic microstructure was not formed in Comparative Sample A1.
  • Comparative Sample A2 had manganese and carbon within the content ranges of the embodiments of the present disclosure. However, copper was not added to Comparative Sample A2, and thus the formation of carbides was not suppressed. That is, large amounts of carbides were formed along grain boundaries of Comparative Sample A2, and thus a desired microstructure and elongation were not obtained. In Comparative Sample A2, a sufficient degree of work hardenability was not obtained due to premature fracture and a decreased amount of dissolved carbon caused by the formation of carbides. Therefore, the wear amount of Comparative Sample A2 was relatively large.
  • Comparative Samples A3 and A4 had manganese and carbon within the content ranges of the embodiments of the present disclosure.
  • the content of copper in each of Comparative Samples A3 and A4 was outside of the range of the embodiments of the present disclosure. Therefore, like in Comparative Sample A2, large amounts of carbides were formed in Comparative Samples A3 and A4, and thus a desired microstructure and elongation were not obtained. Since the contents of copper in Comparative Samples A3 and A4 were outside of the range of the embodiments of the present disclosure, the formation of carbides was not effectively suppressed, and thus the amounts of dissolved carbon and elongation of Comparative Samples A3 and A4 were reduced to cause premature fracture. Thus, a sufficient degree of work hardenability was not obtained in Comparative Sample A3 and A4, and thus the wear resistance of Comparative Samples A3 and A4 was reduced.
  • Comparative Sample A5 In manufacturing of Comparative Sample A5, the cooling rate of Comparative Sample A5 after a rolling process was outside of the range of the embodiments of the present disclosure. That is, due to a low cooling rate, the formation of carbides was not effectively suppressed, and thus the ductility of Comparative Sample A5 was decreased.
  • Inventive Samples A1 to A2 having elements and compositions according to the embodiments of the present disclosure, the formation of carbides in grain boundaries was effectively suppressed owing to the addition of copper, and thus physical properties of Inventive Samples A1 to A2 were not worsened.
  • Inventive Samples A1 to A2 had high carbon contents, the formation of carbides was effectively suppressed owing to the addition of copper, and thus Inventive Samples A1 and A2 had desired microstructures and properties.
  • FIG. 2 is a microstructure image of Comparative Sample A7.
  • Comparative Sample A7 has a high carbon content, carbides are not present in Comparative Sample A7 owing to the addition of copper within the content range of the embodiments of the present disclosure.
  • the austenite fraction, carbide fraction, elongation, yield strength, and tensile strength of each of the steel sheets were measured as illustrated in Table 7. Holes were repeatedly formed in each of the steel sheets by using a drill having a diameter of 10 mm and formed of high speed tool steel in conditions of a drill speed of 130 rpm and a drill movement rate of 0.08 mm/rev. The number of holes formed in each steel sheet until the drill was worn down to the end of its lifespan was counted as illustrated in Table 3. [Table 7] No.
  • inventive samples B1, B2 having carbon and manganese within the content ranges of the embodiments of the present disclosure, the formation of carbides in grain boundaries was effectively suppressed owing to the addition of copper, and thus physical properties of the inventive sample were not worsened.
  • inventive samples B1, B2 had high carbon contents, the formation of carbides was effectively suppressed owing to the addition of copper, and thus the inventive samples B1, B2 had desired microstructures and properties. Since carbon was sufficiently dissolved in austenite and the formation of carbides in grain boundaries was effectively suppressed, the elongation of the inventive samples was stably maintained, and the tensile strength of the inventive samples was high. Therefore, the work hardenability of the inventive samples was sufficient, and thus the wear amounts of the inventive samples were small.
  • Comparative Samples B1 to B4 The machinability of Comparative Samples B1 to B4 was poor because sulfur and calcium were not added to Comparative Samples B1 to B4 or the contents of sulfur and calcium in Comparative Samples B1 to B4 were outside of the ranges of the embodiments of the present disclosure.
  • Comparative Samples B5 to B8 including sulfur and calcium within the content ranges of the embodiments of the present disclosure had superior machinability as compared with the comparative samples.
  • the machinability thereof was improved in proportion to the content of sulfur.
  • FIG. 3 illustrates machinability with respect to the content of sulfur. Referring to FIG. 3 , machinability improves in proportion to the content of sulfur.

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Claims (2)

  1. Acier austénitique résistant à l'usure et à ductilité supérieure, l'acier austénitique résistant à l'usure comprenant, en pourcentage de poids, 8 % à 15 % de manganèse (Mn), du carbone (C) vérifiant 23 % ≤ 33.5C-Mn ≤ 37 %, du cuivre (Cu) vérifiant 1,6C-1,4 (%) ≤ Cu ≤ 5 %, 2 % à 8 % de chrome (Cr) et, éventuellement, 0,03 % à 0,1 % de soufre (S) et 0,001 % à 0,01 % de calcium (Ca) et le reste étant constitué de fer (Fe) et d'impuretés inévitables, l'acier austénitique résistant à l'usure présentant une microstructure comprenant au moins 90 % d'austénite en surface, et l'acier austénitique résistant à l'usure comprenant au plus 10 % de carbures en surface.
  2. Procédé de production d'acier austénitique résistant à l'usure et à ductilité supérieure, le procédé consistant à :
    réchauffer une brame d'acier à une température de 1 050 °C à 1 250 °C, la brame d'acier étant constituée, en pourcentage de poids, de 8 % à 15 % de manganèse (Mn), du carbone (C) vérifiant 23 % ≤ 33,5C-Mn ≤ 37 %, du cuivre (Cu) vérifiant 1.6C-1,4 (%) ≤ Cu ≤ 5 %, 2 % à 8 % de chrome (Cr) et, éventuellement, 0,03 % à 0,1 % de soufre (S) et 0,001 % à 0,01 % de calcium (Ca) et le reste étant constitué de fer (Fe) et d'impuretés inévitables ;
    exécuter un processus de laminage à chaud de finition sur la brame d'acier, dans une plage de températures de 800 °C à 1 050 °C, pour former une tôle d'acier ; et
    refroidir la tôle d'acier laminée à chaud à une température inférieure ou égale à 600 °C à une vitesse de refroidissement de 10 °C/s à 100 °C/s, l'acier austénitique résistant à l'usure présentant une microstructure comprenant au moins 90 % d'austénite en surface, et l'acier austénitique résistant à l'usure comprenant au plus 10 % de carbures en surface.
EP12862562.1A 2011-12-28 2012-12-27 Acier austénitique résistant à l'usure et présentant une ductilité améliorée, et son procédé de production Active EP2799582B1 (fr)

Applications Claiming Priority (3)

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KR1020110145213A KR101353665B1 (ko) 2011-12-28 2011-12-28 내마모성과 연성이 우수한 오스테나이트 강재
KR1020120151507A KR101461735B1 (ko) 2012-12-21 2012-12-21 피삭성과 연성이 우수한 내마모 오스테나이트계 강재 및 그의 제조방법
PCT/KR2012/011536 WO2013100613A1 (fr) 2011-12-28 2012-12-27 Acier austénitique résistant à l'usure et présentant une usinabilité et une ductilité améliorées, et procédé de production correspondant

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EP2799582A4 EP2799582A4 (fr) 2016-02-24
EP2799582B1 true EP2799582B1 (fr) 2019-06-19

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US20140356220A1 (en) 2014-12-04
CN104204262A (zh) 2014-12-10
EP2799582A1 (fr) 2014-11-05
WO2013100613A1 (fr) 2013-07-04
EP2799582A4 (fr) 2016-02-24
CN104204262B (zh) 2018-02-02
JP2015507700A (ja) 2015-03-12
JP6014682B2 (ja) 2016-10-25

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