WO2021169941A1 - 一种矿用链条钢及其制造方法 - Google Patents
一种矿用链条钢及其制造方法 Download PDFInfo
- Publication number
- WO2021169941A1 WO2021169941A1 PCT/CN2021/077430 CN2021077430W WO2021169941A1 WO 2021169941 A1 WO2021169941 A1 WO 2021169941A1 CN 2021077430 W CN2021077430 W CN 2021077430W WO 2021169941 A1 WO2021169941 A1 WO 2021169941A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- steel
- mining
- strength
- chain steel
- rolling
- Prior art date
Links
Images
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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0087—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for chains, for chain links
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J9/00—Forging presses
- B21J9/02—Special design or construction
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21L—MAKING METAL CHAINS
- B21L11/00—Making chains or chain links of special shape
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/10—Supplying or treating molten metal
- B22D11/11—Treating the molten metal
- B22D11/113—Treating the molten metal by vacuum treating
-
- 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
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
- C21D1/60—Aqueous agents
-
- 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
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
-
- 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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—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
- 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
- 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
- C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
-
- 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
- C22C38/02—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
- C22C38/46—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
- C22C38/54—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
- C22C38/60—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
- 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 high-strength steel, in particular to a high-strength and tough mining chain steel and a manufacturing method thereof.
- High-strength and tough steel bars are usually used in high-safety machinery and structural parts.
- mining circular chains are the key vulnerable parts of coal mining machinery. They should have high strength, high toughness, wear resistance, corrosion resistance and high fatigue. Performance, etc.
- Mn-Cr-Ni-Mo series alloy steel is widely used in construction machinery, automobiles, bridges, marine equipment and other fields because of its good strength and toughness. Its safe use strength level is generally 900 ⁇ 1000MPa, while the higher strength level steel Application can not only make the equipment lighter, but also save resources, so the high strength of alloy steel is the inevitable trend of future development. However, as the strength of steel increases, the difficulty of processing and manufacturing increases, and its susceptibility to hydrogen embrittlement is bound to increase. Microstructure refinement, microalloying, grain boundary strengthening and the addition of alloying elements can greatly reduce the hydrogen-induced delayed fracture sensitivity of high-strength steels.
- the highest strength level of steel for circular chain for mining is 1180MPa
- the mechanical performance indicators are: yield strength R eL ⁇ 1060MPa, tensile strength R m ⁇ 1180MPa, elongation A ⁇ 10%, reduction of area Z ⁇ 50%, Charpy Impact energy A kv ⁇ 60J.
- the highest-strength grade mining chain steel in use by China's coal mining machinery is quenched and tempered (880°C quenched + 400°C tempered).
- the mechanical performance indicators are: yield strength R eL ⁇ 980MPa, tensile strength R m ⁇ 1180MPa, elongation A ⁇ 10%, reduction of area Z ⁇ 50%, Charpy impact energy A kU ⁇ 40J.
- Mn-Cr-Ni-Mo series alloy steel chains are subject to heavy loads and dynamic impacts, and are prone to stress corrosion, severely brittle fractures can occur, causing huge economic losses and even safety accidents.
- the purpose of the present invention is to provide a high-strength and toughness mine chain steel and its manufacturing method.
- the high-strength steel has good impact toughness, elongation and area shrinkage, is resistant to stress corrosion cracking and has good weather resistance and wear resistance. It can be used in applications requiring high-strength and tough steel such as engineering machinery and marine engineering.
- a kind of high-strength and toughness chain steel for mining its composition mass percentages are: C: 0.20 ⁇ 0.28%, Si: 0.01 ⁇ 0.40%, Mn: 0.50 ⁇ 1.50%, P ⁇ 0.015%, S ⁇ 0.005%, Cr: 0.30 ⁇ 2.00%, Ni: 0.50 ⁇ 2.00%, Mo: 0.10 ⁇ 0.80%, Cu: 0.01 ⁇ 0.30%, Al: 0.01 ⁇ 0.05%, Nb: 0.001 ⁇ 0.10%, V: 0.001 ⁇ 0.10%, H ⁇ 0.00018%, N ⁇ 0.0150%, O ⁇ 0.0020%, the balance is Fe and unavoidable impurities; and,
- microalloying element coefficient r M/N is: 1.0 ⁇ 9.9;
- J H ([P]+[Sn]+[As]+[Pb]+[Sb]+[Bi])*([Si]+[Mn])*10000.
- [Al], [Nb], [V], [N], etc. in the formulas of the present invention represent the mass percentages of the corresponding elements in the steel.
- [Al], [Nb], [V ], [N], etc. are the values before the percent sign. For example, if the Al content in Example 1 is 0.020%, the value should be 0.020 instead of 0.00020. The substitution of other elements can be deduced by analogy. ,No longer.
- B Preferably, among the unavoidable impurities, B ⁇ 0.0010%, Ti ⁇ 0.003%, and Ca ⁇ 0.005%.
- the microstructure of the high-strength and toughness mining chain steel of the present invention is tempered martensite, a small amount of bainite and retained austenite, wherein the volume content of bainite is less than or equal to 10%.
- the high-strength and toughness mining chain steel of the present invention has a yield strength R p0.2 ⁇ 1000MPa, a tensile strength R m ⁇ 1200MPa, an elongation rate A ⁇ 12%, a section reduction rate Z ⁇ 50%, and a Charpy impact energy A kv ⁇ 60J, hydrogen embrittlement coefficient ⁇ (Z) ⁇ 15%.
- C can improve the hardenability of steel and make the steel form a phase transformation structure with higher hardness during the quenching and cooling process.
- Increasing the C content will increase the hard phase ratio and increase the hardness of the steel material, but will result in a decrease in toughness. Too low C content will result in low content of phase transformation structures such as martensite and bainite, and high tensile strength cannot be obtained.
- the C content is set to 0.20 to 0.28%.
- Si is beneficial to strength improvement in steel.
- a proper amount of Si can avoid the formation of coarse carbides during tempering, but a higher Si content will reduce the impact toughness of the steel.
- the present invention adopts a low Si component system, and the Si content is set to be 0.01 to 0.40%.
- Mn mainly exists in the form of solid solution in steel. It can improve the hardenability of steel, form a high-strength low-temperature phase transformation structure during quenching, and the obtained steel has good wear resistance. Too high Mn content will lead to the formation of more retained austenite, reduce the yield strength of the steel, and easily lead to center segregation.
- the Mn content is set to 0.50 to 1.50%.
- the P content is set as: ⁇ 0.015%.
- S will segregate in steel and form more sulfide inclusions, reducing impact resistance.
- the S content is set as: ⁇ 0.005%.
- Cr can improve the hardenability of steel, form a hardened martensite structure, and increase the strength of steel. If the Cr content is too high, coarse carbides will be formed and the impact performance will be reduced. In the present invention, the Cr content is set to 0.30 to 2.00%.
- Ni exists in the steel as a solid solution, which can improve the low-temperature impact performance of the steel.
- an excessively high Ni content will cause the retained austenite content in the steel to be too high, thereby reducing the strength of the steel.
- the Ni content is set to 0.50% to 2.00%.
- Mo can dissolve in the steel and help to improve the hardenability of the steel and increase the strength of the steel. Tempering at a higher temperature will form fine carbides to further increase the strength of the steel. Considering the cost of the precious alloy Mo element, in the present invention, the Mo content is set to 0.10 to 0.80%.
- the Cu can increase the strength of steel and is beneficial to improve the corrosion resistance of steel. If the Cu content is too high, it will be concentrated in the grain boundary during heating, causing the grain boundary to weaken and cause cracking. In the present invention, the Cu content is set to 0.01 to 0.30%.
- Al forms fine AlN precipitates in steel, which can inhibit the growth of austenite grains. Too high Al content will lead to the formation of larger Al oxides, and coarse AlN hard inclusions will reduce the impact toughness and fatigue properties of the steel.
- the Al content is set to be 0.01 to 0.05%.
- Nb is added to steel to form fine precipitated phases, which can inhibit the recrystallization of steel and can refine grains. If the Nb content is too high, coarse NbC particles will be formed during the smelting process, which will reduce the impact toughness. Grain refinement plays an important role in improving the mechanical properties of steel, especially the strength and toughness. At the same time, grain refinement also helps reduce the hydrogen embrittlement sensitivity of steel.
- the Nb content is set to 0.001 to 0.10%.
- V can form precipitates with C or N in steel to increase the strength of steel. If the content of C and V is too high, coarse VC particles will be formed. In the present invention, the V content is set to be 0.001 to 0.10%.
- the Ti content is set as: ⁇ 0.003%.
- the content of B is controlled to be less than or equal to 0.0010%.
- Ca element to steel can improve the size and morphology of sulfide inclusions and avoid deterioration of impact toughness.
- Ca element is easy to form inclusions and affect the fatigue performance of the final product. Control the Ca content to: ⁇ 0.005%.
- N is an interstitial atom and also an MX-type precipitate-forming element.
- the N content in the composition design of the present invention as: ⁇ 0.015%. Control the ratio of the content of microalloying elements Al, Nb, V to the N content, and define the coefficient of microalloying elements r M/N : 1.0 ⁇ 9.9,
- the microalloying coefficient is related to the nano-scale precipitates.
- a higher microalloying coefficient will result in the presence of coarse precipitates in the steel, which cannot play a precipitation strengthening effect. Instead, it will cause the adverse effects of similar inclusions and reduce the fatigue strength.
- a lower microalloy coefficient will result in a smaller number of precipitates, which cannot achieve the effect of dispersion strengthening.
- the microalloying element coefficient r M/N is 1.0 to 6.0.
- Sn, Sb, As, Bi, Pb and other trace elements segregate to the grain boundary at the tempering temperature, which weakens the intergranular bonding force. Mn and Si can promote the segregation of harmful elements and increase embrittlement. And Sn, Sb, As, Bi, Pb and other elements are harmful to the environment. In the present invention, As: ⁇ 0.05%, Pb: ⁇ 0.05%, Sn: ⁇ 0.02%, Sb: ⁇ 0.01%, Bi: ⁇ 0.01 %. And considering the influence of P, define the harmful element coefficient J H ⁇ 500;
- J H ([P]+[Sn]+[As]+[Pb]+[Sb]+[Bi])*([Si]+[Mn])*10000.
- H will accumulate at defects in steel, and hydrogen-induced delayed fracture will occur in steel with a tensile strength level of more than 1000MPa.
- the tensile strength exceeds 1200 MPa, and the H content is controlled to be less than or equal to 0.00018%.
- N forms nitrides or carbonitrides in the steel to refine the austenite grains, but too high N content will form coarse grains, which will not play the role of grain refinement. It acts as interstitial atoms in Enrichment at grain boundaries and defects will reduce impact toughness.
- the N content is controlled within: ⁇ 0.0150%.
- O and Al in the steel form oxides and composite oxides. In order to ensure the uniformity of the steel structure, low-temperature impact energy and fatigue performance, in the present invention, the content of O is controlled as follows: ⁇ 0.0020%.
- Ceq carbon equivalent
- the atmospheric corrosion resistance index I value is: ⁇ 7.0.
- the microstructure of the high-strength and toughness mining chain steel of the present invention is tempered martensite, a small amount of bainite and retained austenite.
- the previous chain steel is a low-temperature tempered martensite structure, and the chemical composition designed by the present invention makes full use of the influence of various alloying elements and microalloying elements on the phase transformation and microstructure. After quenching + tempering heat treatment, it forms The multiphase microstructure of tempered martensite, a small amount of bainite and retained austenite.
- the method for manufacturing high-strength and toughness mining chain steel of the present invention includes smelting, casting, heating, forging or rolling, quenching heat treatment and tempering heat treatment steps; in the heating process, the heating temperature is 1050-1250°C, The holding time is 3 ⁇ 24h; in the forging or rolling process, the final rolling temperature or final forging temperature is ⁇ 800°C; the heating temperature of quenching heat treatment is 850 ⁇ 1000°C, and the holding time is 60 ⁇ 240min. After austenitizing, water is used Quenching treatment; the tempering temperature of tempering heat treatment is 350 ⁇ 550°C, the holding time is 60 ⁇ 240min, air cooling or water cooling after tempering.
- the smelting may adopt electric furnace smelting or converter smelting, and undergo refining and vacuum treatment.
- the casting adopts die casting or continuous casting.
- the heating temperature of the intermediate billet is 1050 ⁇ 1250°C, and the holding time is 3 ⁇ 24h.
- the billet is discharged from the heating furnace and then rolled after being descaled by high-pressure water, and air cooling or slow cooling is adopted after the rolling.
- the high-strength and toughness mining chain steel of the present invention has a yield strength R p0.2 ⁇ 1000MPa, a tensile strength R m ⁇ 1200MPa, an elongation rate A ⁇ 12%, a section reduction rate Z ⁇ 50%, and a Charpy impact energy A kv ⁇ 60J, hydrogen embrittlement coefficient ⁇ (Z) ⁇ 15%.
- Such high-strength and tough steels have good strength, plasticity and toughness, as well as good weather resistance and stress corrosion resistance.
- the high-strength and toughness mining chain steel of the present invention can be used in applications requiring high-strength bars such as mining, and the size range of the bars is ⁇ 50-170mm.
- the high-strength and toughness mining chain steel of the present invention is fully austenitized by heating at 1050°C to 1250°C.
- Al, Nb, V carbides and nitrides and carbonitrides, Cr and Mo carbides are partially or completely dissolved in austenite.
- Al, Nb and V form fine precipitates.
- Mn, Cr and Mo dissolved in austenite can improve the hardenability of steel and increase the hardness and strength of martensite.
- Under the condition of final rolling or final forging temperature ⁇ 800°C a complex matrix structure with refined martensite, a small amount of bainite and retained austenite is formed, and there are fine dispersed precipitates.
- the steel After the steel is rolled or forged, it is heated to 850 ⁇ 1000°C for heat preservation and then quenched. Fully austenitizing is achieved during this heat preservation process. During the heating process, the precipitates of the carbide forming elements Al, Nb, V, Cr and Mo partially dissolve, and the undissolved precipitates pin the grain boundaries and inhibit the coarse austenite grains (austenite grain size ⁇ 6 ). During the quenching and cooling process, the alloying elements in solid solution in austenite make the steel have high strength and good toughness. The quenched steel is subjected to tempering heat treatment at 350-550°C. Al, Nb, V, Cr and Mo will form fine precipitates with C and N, which improves the strength and ductility of the steel. Within the quenching + tempering temperature range of the present invention, the steel can be guaranteed to have good strong plasticity and toughness, which is beneficial to the processing and use of bars, such as the production of high-performance mining chains by forging or welding.
- the "Alloy steel composition and chain products fabricated in such alloy steel" disclosed in US patent US006146583 has the following composition: C: 0.15 to 0.28%, Cr: 0.2 to 1.0%, Mo: 0.1 to 1.0%, Ni: 0.3 to 1.5% , V: 0.05-0.2%, the balance is Fe and unavoidable impurities, the strength can reach 800MPa, and it has stress corrosion resistance. After forging, welding and heat treatment, a high-strength chain is formed.
- the present invention has different Cu content in the composition, and the present invention optimizes the content of C, N and alloying elements such as Mn, Cr, Ni, Mo and microalloying elements Al, V, Nb and other elements.
- the invention utilizes the design of C, Ni and Cu elements, combined with the optimization of Mn, Cr, Mo and other elements, to form a complex microstructure of tempered martensite and a small amount of bainite and retained austenite. And the mechanical properties are obviously better than the patent.
- Chinese Patent Publication No. CN103276303A discloses "a high-strength mining chain steel and its preparation method", its composition is: C: 0.21 ⁇ 0.25%, Mn: 0.20 ⁇ 0.25%, Si: 0.15 ⁇ 0.35%, Cr: 0.40 ⁇ 0.65%, Ni: 0.60 ⁇ 0.70%, Cu: 0.07 ⁇ 0.15%, Alt: 0.02 ⁇ 0.05%, N ⁇ 0.012%, S ⁇ 0.015%, P ⁇ 0.015%, the balance is Fe.
- the preparation method includes: electric furnace or converter smelting process, out-of-furnace refining process, billet continuous casting process and heating rolling process to obtain straight bars with a specification of ⁇ 20-50mm, and then obtain high-strength mining chain steel after annealing.
- the present invention has completely different contents of Cr, Mn, Ni, and Mo in the composition, and the present invention optimizes the composition range of C, Cu, Al, Nb, V, etc., and limits the contents of N and Ca.
- the alloy element range of the present invention a microstructure of tempered martensite and retained austenite is formed, which has high strength and toughness mechanical properties.
- H in the environment will be adsorbed to cause delayed cracking, and large-size high-strength steel bars are more sensitive to hydrogen. Therefore, the H element in the steel is limited in the present invention.
- the tensile strength of the present invention is R m ⁇ 1200MPa
- the yield strength R p0.2 is ⁇ 1000MPa
- the impact energy A kv ⁇ 60J is the impact energy A kv ⁇ 60J.
- the strength grade of the present invention is better than that of the patent, and it has excellent impact toughness and stress corrosion cracking resistance.
- the present invention develops high-strength and tough steel by rationally designing the chemical composition and combining the optimization process.
- the rolled or forged bar After quenching, the rolled or forged bar adopts a tempering heat treatment process to form tempered martensite and a small amount of bainite and residues.
- composition and process design of the steel are reasonable, and the process window is loose, and mass commercial production can be realized on the bar or high-speed wire production line.
- the steel produced by the present invention has a yield strength R p0.2 ⁇ 1000MPa, a tensile strength R m ⁇ 1200MPa, an elongation A ⁇ 12%, a reduction of area Z ⁇ 50%, and a Charpy impact energy A kv ⁇ 60J.
- the engineering field usually adopts the change of elongation under environmental conditions to reflect the stress corrosion tendency.
- the present invention refers to the requirements of Det Norske Veritas for hydrogen embrittlement sensitivity in accordance with GB/T2975-2018 "Steel and Steel Product Mechanical Performance Test Sampling Position and Sample Preparation ⁇ Prepare a circular cross-section sample with a diameter of 10mm.
- the tensile test is carried out according to the national standard GB/T 228.1, the strain rate is ⁇ 0.0003/s, the reduction of area Z is obtained, and the hydrogen embrittlement coefficient ⁇ (Z) is defined to evaluate the stress corrosion resistance of the steel:
- the hydrogen embrittlement coefficient ⁇ (Z) of the steel produced by the invention is less than or equal to 15%, and has good stress corrosion resistance.
- Figure 1 is a metallographic photo of the microstructure of round steel in Example 2 of the present invention (magnification 500 times);
- Figure 2 is a metallographic photograph of the microstructure of the chain prepared in Example 2 of the present invention (magnification 500 times).
- composition of the round steel examples and comparative examples of the present invention are shown in Table 1.
- the high-strength and tough steels of Examples 1 to 7 of the present invention and Comparative Examples 1 to 3, and the composition coefficients are shown in Table 2. It can be seen that the ratio coefficient r M/N of the microalloying elements Al, Nb, V content and the N content of the examples is in the range of 1.0 ⁇ 9.9; carbon equivalent Ceq ⁇ 0.80; harmful element coefficient J H ⁇ 500.
- the implementation is the same as in Example 1, wherein the heating temperature is 1080°C, the holding time is 3h, the final rolling temperature is 880°C, and the intermediate billet size is 220 ⁇ 220 mm.
- the intermediate billet is heated to 1120°C, the holding time is 3h, the final rolling temperature is 850°C, and the finished bar specification is ⁇ 75mm.
- Air cooling after rolling Quenching heating temperature is 870°C, heating time is 100min, tempering temperature is 550°C, tempering time is 60min, water cooling after tempering.
- the implementation is the same as in Example 1, wherein the heating temperature is 1120°C, the holding time is 8h, the final rolling temperature is 940°C, and the intermediate billet size is 260 ⁇ 260 mm.
- the intermediate billet is heated to 1200°C, the holding time is 5h, the final rolling temperature is 880°C, and the finished bar specification is ⁇ 100mm.
- Air cooling after rolling Quenching heating temperature is 890°C, heating time is 150min, tempering temperature is 430°C, tempering time is 100min, air cooling after tempering.
- the implementation is the same as in Example 1, wherein the heating temperature is 1250°C, the holding time is 14h, hot continuous rolling is formed, the final rolling temperature is 900°C, and the finished bar specification is ⁇ 150mm. Air cooling after rolling. Quenching heating temperature is 990°C, heating time is 210min, tempering temperature is 350°C, tempering time is 180min, water cooling after tempering.
- the chemical composition shown in Table 1 it is smelted in a converter, refined and vacuum treated, and then cast into a steel ingot.
- the heating temperature is 1180°C
- the holding time is 3.5h
- the final rolling temperature is 980°C
- the intermediate billet size is 280 ⁇ 280mm.
- the intermediate billet is heated to 1250°C
- the holding time is 12h
- the final rolling temperature is 950°C
- the finished bar specification is ⁇ 160mm.
- the quenching heating temperature is 900°C
- the heating time is 210min
- the tempering temperature is 450°C
- the tempering time is 190min. After tempering, it is water-cooled.
- the implementation mode is the same as that in Example 5, in which the heating temperature is 1220°C, the holding time is 24h, the forging is formed, the final forging temperature is 920°C, and the finished bar specification is ⁇ 170mm. Air-cooled after forging.
- the quenching heating temperature is 920°C
- the heating time is 240min
- the tempering temperature is 420°C
- the tempering time is 240min. After tempering, it is air-cooled.
- the implementation mode is the same as in Example 2, wherein the heating temperature is 1080°C, the holding time is 3h, the final rolling temperature is 880°C, and the intermediate billet size is 220 ⁇ 220mm.
- the intermediate billet is heated to 1100°C, the holding time is 3h, the final rolling temperature is 850°C, and the finished bar specification is ⁇ 65mm.
- Air cooling after rolling The quenching heating temperature is 880°C, the heating time is 150min, the tempering temperature is 400°C, and the tempering time is 100min. After tempering, it is water-cooled.
- the comparative example 1 contains high Nb, the microalloy coefficient is 10.1, the precipitation strengthening effect is poor, the strength is low, the impact toughness is low, and the fatigue life is short;
- the comparative example 2 contains high P content and harmful elements The coefficient is 678, the atmospheric corrosion resistance coefficient is 5.3, the impact toughness and stress corrosion cracking resistance are poor, and the hydrogen embrittlement coefficient is high; the high content of S in Comparative Example 3 results in poor impact toughness.
- the yield strength of the high-strength and tough steel materials in Examples 1-7 of the present invention are all R p0.2 ⁇ 1000MPa, tensile strength R m ⁇ 1200MPa, elongation A ⁇ 12%, reduction of area Z ⁇ 50%, Charpy impact Work A kv ⁇ 60J, hydrogen embrittlement coefficient ⁇ (Z) ⁇ 15%.
- Example 6 due to the one-time heating and rolling process and the large bar size, the structure compactness is slightly worse. Compared with other examples, the strength and impact performance are reduced; in Example 7, due to atmospheric corrosion resistance The coefficient is relatively low, resulting in a slightly inferior effect on impact toughness, hydrogen embrittlement coefficient, and anti-corrosion cracking performance compared with other embodiments.
- the microstructure of the round steel prepared in Example 2 and the mining chain prepared in Example 2 as raw materials were studied.
- the optical microscope photos are shown in Figure 1 and Figure 2. It can be seen from the figure that the microstructure of the round steel is tempered martensite and a small amount of bainite and retained austenite, while the microstructure of the chain obtained by further preparing the round steel prepared in Example 2 is refined Tempered martensite and a small amount of bainite.
Landscapes
- 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)
- Thermal Sciences (AREA)
- Manufacturing & Machinery (AREA)
- Heat Treatment Of Steel (AREA)
- Gears, Cams (AREA)
- Heat Treatment Of Articles (AREA)
- Heat Treatment Of Strip Materials And Filament Materials (AREA)
Priority Applications (6)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP21760437.0A EP4089197A4 (en) | 2020-02-28 | 2021-02-23 | CHAIN STEEL FOR USE IN MINING AND METHOD FOR ITS MANUFACTURE |
BR112022016824A BR112022016824A2 (pt) | 2020-02-28 | 2021-02-23 | Aço para cadeia de mineração e método de fabricação deste |
KR1020227028750A KR20220129609A (ko) | 2020-02-28 | 2021-02-23 | 광산 체인용 스틸 및 그 제조방법 |
US17/800,800 US20230235435A1 (en) | 2020-02-28 | 2021-02-23 | Steel for mining chain and manufacturing method thereof |
MX2022010591A MX2022010591A (es) | 2020-02-28 | 2021-02-23 | Acero para cadena de mineria y metodo de fabricacion del mismo. |
JP2022550659A JP7497447B2 (ja) | 2020-02-28 | 2021-02-23 | 採掘チェーン用鋼およびその製造方法 |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CN202010129796.6A CN113322409B (zh) | 2020-02-28 | 2020-02-28 | 一种高强韧矿用链条钢及其制造方法 |
CN202010129796.6 | 2020-02-28 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2021169941A1 true WO2021169941A1 (zh) | 2021-09-02 |
Family
ID=77412659
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/CN2021/077430 WO2021169941A1 (zh) | 2020-02-28 | 2021-02-23 | 一种矿用链条钢及其制造方法 |
Country Status (8)
Country | Link |
---|---|
US (1) | US20230235435A1 (ja) |
EP (1) | EP4089197A4 (ja) |
JP (1) | JP7497447B2 (ja) |
KR (1) | KR20220129609A (ja) |
CN (1) | CN113322409B (ja) |
BR (1) | BR112022016824A2 (ja) |
MX (1) | MX2022010591A (ja) |
WO (1) | WO2021169941A1 (ja) |
Cited By (17)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN113789474A (zh) * | 2021-09-14 | 2021-12-14 | 鞍钢股份有限公司 | 一种经济型非开挖钻杆用无缝钢管及其制造方法 |
CN113862568A (zh) * | 2021-09-23 | 2021-12-31 | 天津钢管制造有限公司 | 煤矿勘探放水用无缝钢管及制造方法 |
CN113957341A (zh) * | 2021-10-16 | 2022-01-21 | 宝鼎重工有限公司 | 炉水循环泵用泵壳体锻件及制作方法 |
CN113957358A (zh) * | 2021-10-12 | 2022-01-21 | 北京科技大学 | 抗拉强度大于2200MPa高强度热成形钢基板及制备方法 |
CN114000034A (zh) * | 2021-11-02 | 2022-02-01 | 攀钢集团攀枝花钢铁研究院有限公司 | 一种低屈强比高强贝氏体钢轨及其生产方法 |
CN114032472A (zh) * | 2021-11-02 | 2022-02-11 | 西京学院 | 一种新型无钴马氏体时效钢及其强韧化处理工艺 |
CN114540716A (zh) * | 2022-03-04 | 2022-05-27 | 马鞍山钢铁股份有限公司 | 一种壁厚≥600mm高强韧高寿命水下采油树阀体用钢及其热处理方法和生产方法 |
CN114574762A (zh) * | 2022-03-04 | 2022-06-03 | 马鞍山钢铁股份有限公司 | 一种在高废钢比下冶炼的高强韧耐蚀水下采油树阀体用钢及其热处理方法和生产方法 |
CN114592153A (zh) * | 2021-11-22 | 2022-06-07 | 宝山钢铁股份有限公司 | 一种具有优良耐候性能的高强度钢材及其制造方法 |
CN114635081A (zh) * | 2022-02-11 | 2022-06-17 | 包头钢铁(集团)有限责任公司 | 一种高品质圆环链盘条的生产方法 |
CN114774630A (zh) * | 2022-04-21 | 2022-07-22 | 河南中原特钢装备制造有限公司 | 低成本低合金超高强钢及其制造方法 |
CN114875322A (zh) * | 2022-05-18 | 2022-08-09 | 湖南华菱涟钢特种新材料有限公司 | 钢材及其制备方法 |
CN114990450A (zh) * | 2022-06-30 | 2022-09-02 | 马鞍山钢铁股份有限公司 | 一种高耐磨弹性车轮用轮箍及其热处理工艺 |
CN115161439A (zh) * | 2022-07-20 | 2022-10-11 | 国家能源集团新疆能源有限责任公司 | 链条制造方法以及通过该方法获得的链条 |
CN115233089A (zh) * | 2022-05-16 | 2022-10-25 | 季华实验室 | 一种柔轮用特殊钢及其制备工艺 |
CN115505852A (zh) * | 2022-10-26 | 2022-12-23 | 河北普阳钢铁有限公司 | 一种耐蚀农机用钢材及其制造方法 |
WO2023160613A1 (zh) * | 2022-02-23 | 2023-08-31 | 上海茵矩材料科技有限公司 | 一种系泊链钢及生产方法以及系泊链及生产方法 |
Families Citing this family (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN112048665B (zh) | 2020-08-17 | 2022-03-22 | 莱芜钢铁集团银山型钢有限公司 | 一种极地海洋工程用钢板及其制备方法 |
CN114959443B (zh) * | 2022-03-17 | 2023-09-12 | 宝山钢铁股份有限公司 | 一种耐海水腐蚀高强度钢材、圆钢及其制造方法 |
CN115125445B (zh) * | 2022-06-28 | 2023-08-11 | 宝山钢铁股份有限公司 | 一种具有良好强韧性的高强钢及其制造方法 |
CN115094204A (zh) * | 2022-07-18 | 2022-09-23 | 重庆齿轮箱有限责任公司 | 中碳合金钢的一种热处理方法 |
CN117467911A (zh) * | 2022-07-29 | 2024-01-30 | 宝山钢铁股份有限公司 | 一种耐腐蚀性耐磨钢板及其制造方法 |
CN115369319B (zh) * | 2022-08-05 | 2023-08-29 | 张家口三信同达机械制造有限公司 | 一种可焊高强高韧耐磨材料及其热处理工艺 |
CN115747630B (zh) * | 2022-08-30 | 2023-09-12 | 张家港海锅新能源装备股份有限公司 | 一种深海采油装备管道连接器用钢及其锻造方法 |
CN115838897A (zh) * | 2022-11-18 | 2023-03-24 | 莱芜钢铁集团银山型钢有限公司 | 一种415hb级泥沙输送管道用马氏体耐磨耐蚀钢管及其制备方法 |
KR20240100531A (ko) * | 2022-12-22 | 2024-07-02 | 주식회사 포스코 | 강판 및 그 제조방법 |
Citations (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US6146583A (en) | 1995-12-20 | 2000-11-14 | Parsons Chain Company Limited | Alloy steel composition and chain products fabricated in such alloy steel |
CN1490426A (zh) * | 2002-10-16 | 2004-04-21 | 天津航道勘察设计研究院 | 疏浚机具用耐磨铸造合金及其制备方法 |
KR100823598B1 (ko) * | 2006-10-24 | 2008-04-21 | 주식회사 포스코 | 등방성이 우수한 고탄소강 및 그 제조방법 |
CN102747299A (zh) * | 2012-07-23 | 2012-10-24 | 西华大学 | 高寒地区铁路辙叉高性能贝氏体耐磨钢及制造方法 |
CN103276303A (zh) | 2013-06-07 | 2013-09-04 | 南京钢铁股份有限公司 | 一种高强度矿用链条钢及其制备方法 |
KR20150002956A (ko) * | 2013-06-27 | 2015-01-08 | 현대제철 주식회사 | 라인파이프용 후강판 및 그 제조 방법 |
KR20150050701A (ko) * | 2013-10-30 | 2015-05-11 | 현대제철 주식회사 | 유정용 강관 및 그 제조 방법 |
CN106854738A (zh) * | 2015-12-08 | 2017-06-16 | 重庆葛利兹模具技术有限公司上海分公司 | 一种易切削塑料模具钢及其热处理方法 |
CN108004469A (zh) * | 2017-12-08 | 2018-05-08 | 北京科技大学 | 一种低合金高韧性q-p-t耐磨钢板及其制备方法 |
Family Cites Families (12)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS526847B2 (ja) * | 1972-05-19 | 1977-02-25 | ||
SE515623C2 (sv) | 2000-02-14 | 2001-09-10 | Ovako Steel Ab | Kättingstål |
CN101397636B (zh) | 2007-09-25 | 2010-12-01 | 宝山钢铁股份有限公司 | 一种高强韧性矿用圆环链用钢及其制造方法 |
JP5235452B2 (ja) * | 2008-02-28 | 2013-07-10 | 新日鐵住金ステンレス株式会社 | 耐食性と耐磨耗性に優れる織機部材用マルテンサイト系ステンレス鋼とその鋼帯の製造方法 |
CN102453841A (zh) * | 2010-10-22 | 2012-05-16 | 江阴兴澄特种钢铁有限公司 | 海洋采油平台r4s级系泊链条用钢及其制造方法 |
CN102534423B (zh) * | 2012-02-29 | 2016-01-20 | 宝山钢铁股份有限公司 | 高强度钢板及其制造方法 |
CN102747303B (zh) * | 2012-06-29 | 2015-01-21 | 宝山钢铁股份有限公司 | 一种屈服强度1100MPa级高强度钢板及其制造方法 |
CN103667953B (zh) * | 2013-11-28 | 2016-09-28 | 江苏亚星锚链股份有限公司 | 一种低环境裂纹敏感性超高强韧性海洋系泊链钢及其制造方法 |
JP6439248B2 (ja) | 2013-12-18 | 2018-12-19 | 新日鐵住金株式会社 | 打ち抜き性に優れる中・高炭素鋼板およびその製造方法 |
CN106521316B (zh) * | 2016-11-15 | 2018-08-07 | 江阴兴澄特种钢铁有限公司 | 一种紧固件用高淬透性中碳低合金圆钢及其制造方法 |
JP7062973B2 (ja) | 2018-01-26 | 2022-05-09 | 日本製鉄株式会社 | 係留チェーン用鋼および係留チェーン |
CN109136737A (zh) * | 2018-06-20 | 2019-01-04 | 宝山钢铁股份有限公司 | 一种抗拉强度1100MPa级超高强韧钢及其制造方法 |
-
2020
- 2020-02-28 CN CN202010129796.6A patent/CN113322409B/zh active Active
-
2021
- 2021-02-23 US US17/800,800 patent/US20230235435A1/en active Pending
- 2021-02-23 WO PCT/CN2021/077430 patent/WO2021169941A1/zh unknown
- 2021-02-23 KR KR1020227028750A patent/KR20220129609A/ko unknown
- 2021-02-23 MX MX2022010591A patent/MX2022010591A/es unknown
- 2021-02-23 EP EP21760437.0A patent/EP4089197A4/en active Pending
- 2021-02-23 BR BR112022016824A patent/BR112022016824A2/pt unknown
- 2021-02-23 JP JP2022550659A patent/JP7497447B2/ja active Active
Patent Citations (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US6146583A (en) | 1995-12-20 | 2000-11-14 | Parsons Chain Company Limited | Alloy steel composition and chain products fabricated in such alloy steel |
CN1490426A (zh) * | 2002-10-16 | 2004-04-21 | 天津航道勘察设计研究院 | 疏浚机具用耐磨铸造合金及其制备方法 |
KR100823598B1 (ko) * | 2006-10-24 | 2008-04-21 | 주식회사 포스코 | 등방성이 우수한 고탄소강 및 그 제조방법 |
CN102747299A (zh) * | 2012-07-23 | 2012-10-24 | 西华大学 | 高寒地区铁路辙叉高性能贝氏体耐磨钢及制造方法 |
CN103276303A (zh) | 2013-06-07 | 2013-09-04 | 南京钢铁股份有限公司 | 一种高强度矿用链条钢及其制备方法 |
KR20150002956A (ko) * | 2013-06-27 | 2015-01-08 | 현대제철 주식회사 | 라인파이프용 후강판 및 그 제조 방법 |
KR20150050701A (ko) * | 2013-10-30 | 2015-05-11 | 현대제철 주식회사 | 유정용 강관 및 그 제조 방법 |
CN106854738A (zh) * | 2015-12-08 | 2017-06-16 | 重庆葛利兹模具技术有限公司上海分公司 | 一种易切削塑料模具钢及其热处理方法 |
CN108004469A (zh) * | 2017-12-08 | 2018-05-08 | 北京科技大学 | 一种低合金高韧性q-p-t耐磨钢板及其制备方法 |
Cited By (22)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN113789474A (zh) * | 2021-09-14 | 2021-12-14 | 鞍钢股份有限公司 | 一种经济型非开挖钻杆用无缝钢管及其制造方法 |
CN113862568A (zh) * | 2021-09-23 | 2021-12-31 | 天津钢管制造有限公司 | 煤矿勘探放水用无缝钢管及制造方法 |
CN113957358A (zh) * | 2021-10-12 | 2022-01-21 | 北京科技大学 | 抗拉强度大于2200MPa高强度热成形钢基板及制备方法 |
CN113957341A (zh) * | 2021-10-16 | 2022-01-21 | 宝鼎重工有限公司 | 炉水循环泵用泵壳体锻件及制作方法 |
CN114000034A (zh) * | 2021-11-02 | 2022-02-01 | 攀钢集团攀枝花钢铁研究院有限公司 | 一种低屈强比高强贝氏体钢轨及其生产方法 |
CN114032472A (zh) * | 2021-11-02 | 2022-02-11 | 西京学院 | 一种新型无钴马氏体时效钢及其强韧化处理工艺 |
CN114032472B (zh) * | 2021-11-02 | 2023-02-07 | 西京学院 | 一种无钴马氏体时效钢及其强韧化处理工艺 |
CN114592153A (zh) * | 2021-11-22 | 2022-06-07 | 宝山钢铁股份有限公司 | 一种具有优良耐候性能的高强度钢材及其制造方法 |
CN114635081A (zh) * | 2022-02-11 | 2022-06-17 | 包头钢铁(集团)有限责任公司 | 一种高品质圆环链盘条的生产方法 |
WO2023160613A1 (zh) * | 2022-02-23 | 2023-08-31 | 上海茵矩材料科技有限公司 | 一种系泊链钢及生产方法以及系泊链及生产方法 |
CN114574762B (zh) * | 2022-03-04 | 2022-11-08 | 马鞍山钢铁股份有限公司 | 一种在高废钢比下冶炼的高强韧耐蚀水下采油树阀体用钢及其热处理方法和生产方法 |
CN114574762A (zh) * | 2022-03-04 | 2022-06-03 | 马鞍山钢铁股份有限公司 | 一种在高废钢比下冶炼的高强韧耐蚀水下采油树阀体用钢及其热处理方法和生产方法 |
CN114540716A (zh) * | 2022-03-04 | 2022-05-27 | 马鞍山钢铁股份有限公司 | 一种壁厚≥600mm高强韧高寿命水下采油树阀体用钢及其热处理方法和生产方法 |
CN114774630A (zh) * | 2022-04-21 | 2022-07-22 | 河南中原特钢装备制造有限公司 | 低成本低合金超高强钢及其制造方法 |
CN114774630B (zh) * | 2022-04-21 | 2024-05-03 | 河南中原特钢装备制造有限公司 | 低成本低合金超高强钢及其制造方法 |
CN115233089A (zh) * | 2022-05-16 | 2022-10-25 | 季华实验室 | 一种柔轮用特殊钢及其制备工艺 |
CN114875322A (zh) * | 2022-05-18 | 2022-08-09 | 湖南华菱涟钢特种新材料有限公司 | 钢材及其制备方法 |
CN114990450A (zh) * | 2022-06-30 | 2022-09-02 | 马鞍山钢铁股份有限公司 | 一种高耐磨弹性车轮用轮箍及其热处理工艺 |
CN114990450B (zh) * | 2022-06-30 | 2023-08-11 | 马鞍山钢铁股份有限公司 | 一种高耐磨弹性车轮用轮箍及其热处理工艺 |
CN115161439A (zh) * | 2022-07-20 | 2022-10-11 | 国家能源集团新疆能源有限责任公司 | 链条制造方法以及通过该方法获得的链条 |
CN115161439B (zh) * | 2022-07-20 | 2023-11-24 | 国家能源集团新疆能源有限责任公司 | 链条制造方法以及通过该方法获得的链条 |
CN115505852A (zh) * | 2022-10-26 | 2022-12-23 | 河北普阳钢铁有限公司 | 一种耐蚀农机用钢材及其制造方法 |
Also Published As
Publication number | Publication date |
---|---|
JP2023515115A (ja) | 2023-04-12 |
CN113322409B (zh) | 2022-06-28 |
JP7497447B2 (ja) | 2024-06-10 |
BR112022016824A2 (pt) | 2022-10-11 |
MX2022010591A (es) | 2022-09-07 |
EP4089197A4 (en) | 2023-07-26 |
KR20220129609A (ko) | 2022-09-23 |
EP4089197A1 (en) | 2022-11-16 |
US20230235435A1 (en) | 2023-07-27 |
CN113322409A (zh) | 2021-08-31 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
WO2021169941A1 (zh) | 一种矿用链条钢及其制造方法 | |
CA2962472C (en) | High-toughness hot-rolled high-strength steel with yield strength of grade 800 mpa and preparation method thereof | |
JP6466582B2 (ja) | 降伏強度800MPa級高強度鋼及びその製造方法 | |
WO2016095721A1 (zh) | 一种屈服强度900~1000MPa级调质高强钢及制造方法 | |
WO2020238851A1 (zh) | 一种钢、棒材及棒材的制造方法 | |
WO2007074984A1 (en) | High-strength steel bolt having excellent resistance for delayed fracture and method for producing the same | |
WO2022152158A1 (zh) | 一种高强韧易切削非调质圆钢及其制造方法 | |
WO2019119725A1 (zh) | 一种布氏硬度大于550hb的高级别低合金耐磨钢板及制造方法 | |
CN102796967A (zh) | 一种800MPa经济型耐腐蚀高强度钢板 | |
AU2022208884A9 (en) | High-strength and toughness free-cutting non-quenched and tempered round steel and manufacturing method therefor | |
CN111748737B (zh) | 一种冷裂纹敏感系数≤0.25的易焊接超高强钢及生产方法 | |
CN114592153A (zh) | 一种具有优良耐候性能的高强度钢材及其制造方法 | |
CN114134431B (zh) | 一种方坯连铸连轧2000Mpa级高强高韧高淬透性弹簧钢及其制造方法 | |
CN110846571A (zh) | 一种高韧性低合金耐磨钢厚板及其制造方法 | |
CN115125445B (zh) | 一种具有良好强韧性的高强钢及其制造方法 | |
CN114134387B (zh) | 一种抗拉强度1300MPa级厚规格超高强钢板及其制造方法 | |
AU2020455074A1 (en) | 800 MPa construction machinery medium-manganese medium-thickness steel and manufacturing method therefor | |
RU2801655C1 (ru) | Сталь для цепей горнодобывающего оборудования и способ её изготовления | |
CN111321346A (zh) | 一种具有优异耐氢致延迟断裂性能的超高强度弹簧钢及其生产方法 | |
CN103981437A (zh) | 一种高强度、高韧性合金钢、制备方法及其在钢构中的应用 | |
CN115386783B (zh) | 一种屈服强度1000MPa级超高强钢板及其制备方法 | |
CN117344206A (zh) | 高强度钢及其制造方法 | |
CN118064796A (zh) | 一种焊接性能优良的超高强钢及其制造方法 | |
CN117535583A (zh) | 一种850MPa级高延伸率调质钢板及其生产方法 | |
CN113430457A (zh) | 一种1300MPa级高延伸率低延迟开裂敏感性热成形钢及其生产方法 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 21760437 Country of ref document: EP Kind code of ref document: A1 |
|
ENP | Entry into the national phase |
Ref document number: 2021760437 Country of ref document: EP Effective date: 20220809 |
|
ENP | Entry into the national phase |
Ref document number: 2022550659 Country of ref document: JP Kind code of ref document: A |
|
REG | Reference to national code |
Ref country code: BR Ref legal event code: B01A Ref document number: 112022016824 Country of ref document: BR |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
ENP | Entry into the national phase |
Ref document number: 112022016824 Country of ref document: BR Kind code of ref document: A2 Effective date: 20220823 |