US20230235435A1 - Steel for mining chain and manufacturing method thereof - Google Patents

Steel for mining chain and manufacturing method thereof Download PDF

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US20230235435A1
US20230235435A1 US17/800,800 US202117800800A US2023235435A1 US 20230235435 A1 US20230235435 A1 US 20230235435A1 US 202117800800 A US202117800800 A US 202117800800A US 2023235435 A1 US2023235435 A1 US 2023235435A1
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steel
mining chain
mpa
billet
rolling
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Jiaqiang Gao
Sixin Zhao
Wei Wang
Jun Zhang
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Baoshan Iron and Steel Co Ltd
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Baoshan Iron and Steel Co Ltd
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Assigned to BAOSHAN IRON & STEEL CO., LTD. reassignment BAOSHAN IRON & STEEL CO., LTD. ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: GAO, Jiaqiang, ZHAO, SIXIN, WANG, WEI, ZHANG, JUN
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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
    • 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
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    • 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
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    • 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")
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    • 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
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
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    • 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
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    • C21D6/00—Heat treatment of ferrous alloys
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    • 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
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    • 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
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    • 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
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    • 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
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    • 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
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    • 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
    • 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
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    • 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
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C—CHEMISTRY; METALLURGY
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    • 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
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    • 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
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    • 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
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the present invention relates to steels having high strength, and specifically to a steel for mining chain having high strength and toughness and a manufacturing method thereof.
  • Steel bars having high strength and toughness are usually used in high-safety machinery and structural components.
  • round link chains for mines are the key wearing parts of the mining machinery. Therefore, they should have high strength, high toughness, high wear resistance, high corrosion resistance and high fatigue resistance, etc.
  • Mn-Cr-Ni-Mo alloy steels are widely used in the fields such as construction machinery, automobiles, bridges, and marine equipment due to their good strength and toughness.
  • the strength level for safe use of those steels is 900 ⁇ 1000 MPa.
  • the application of the steels having higher strength can not only make equipment lighter, but also save resources. Therefore, alloy steels having high strength are an inevitable trend of future development.
  • the manufacturing difficulty increases, and their susceptibility to hydrogen embrittlement is bound to increase.
  • the susceptibility to hydrogen-induced delayed fracture of high-strength steels can be greatly reduced by microstructure refinement, microalloying, strengthening of grain boundaries and the addition of alloying elements.
  • the mechanical properties of chain steels having the highest strength grade in use in China’s mining machinery after quenching and tempering are as follows: yield strength R eL ⁇ 980 MPa, tensile strength R m ⁇ 1180 MPa, elongation A ⁇ 10%, reduction of area Z ⁇ 50%, and Charpy impact work A kU ⁇ 40 J.
  • Mn-Cr-Ni-Mo alloy steel chains are subject to large loads and dynamic shocks, and prone to stress corrosion. In some severe cases, those chains become very brittle and are easy to fracture, which might cause huge economic losses and even safety accidents.
  • the purpose of the present invention is to provide a steel for mining chain and a manufacturing method thereof.
  • the chain steel has good impact roughness, good elongation and reduction of area.
  • the steel can resist stress corrosion cracking and has good weather resistance, good wear resistance and fatigue resistance. Therefore, the steel can be used in scenarios where steels having high strength and roughness are required, such as construction machinery and marine engineering.
  • the present invention provides the following technical solutions.
  • a steel for mining chain comprising by weight: 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%, and the balance being Fe and inevitable impurities; and
  • [Al], [Nb], [V], [N], etc. in the formulas of the present invention represent the weight percentage of the corresponding elements in the steel. Substitute [Al], [Nb], [V], [N], etc. in the formulas with the values before the percent sign when doing calculations. For example, the content of Al in Example 1 is 0.020%, then substitute [Al] in the formula with 0.020 instead of 0.00020. The substitutions of other elements are similar.
  • B Preferably, in said inevitable impurities, B ⁇ 0.0010%, Ti ⁇ 0.003%, Ca ⁇ 0.005%.
  • microstructures of the steel for mining chain in the present invention are tempered martensite, bainite, and retained austenite, wherein the volume percentage of bainite is 10% or less.
  • the steel for mining chain in the present invention has a yield strength R p0.2 ⁇ 1000 MPa, a tensile strength R m ⁇ 1200 MPa, a elongation A ⁇ 12%, a reduction of area Z ⁇ 50%, a Charpy impact work A kv ⁇ 60 J, and a coefficient of hydrogen embrittlement ⁇ (Z) ⁇ 15%.
  • the C can improve the hardenability of the steel, so that the phase transformation structures with high hardness can be formed in steel in the process of quenching and cooling.
  • Increasing the C content will increase the proportion of the hard phase and thus increase the hardness of the steel, but will lead to a decrease in toughness. If the C content is too low, the content of the phase transformation structures such as martensite and bainite will be low, and the steel having a high tensile strength cannot be obtained.
  • the C content is set to 0.20 ⁇ 0.28%.
  • Si is beneficial to strength enhancement in steel.
  • An appropriate amount of Si can avoid the formation of coarse carbides during tempering. But a high Si content will reduce the impact toughness of the steel.
  • a composition system of low Si are adopted in the present invention, and the Si content is set to 0.01 ⁇ 0.40%.
  • Mn mainly exists in the form of solid solution in steel. It can improve the hardenability of the steel and form low-temperature phase transformation structures with high strength during quenching. Therefore, the steel having good wear resistance can be obtained. If the Mn content is too high, much retained austenite will be formed, leading to the reduction of the yield strength of the steel, and easily resulting in the central segregation in steel. In the present invention, the Mn content is set to 0.50 ⁇ 1.50%.
  • the segregation of P at the grain boundaries in steel will reduce the grain boundary binding energy and deteriorate the impact toughness of the steel.
  • the P content is set to 0.015% or less.
  • S will segregate in steel and form many sulfide inclusions, leading to the reduction of impact resistance.
  • the S content is set to 0.005% or less.
  • the Cr can improve the hardenability of the steel. It can also form hardened martensite structures, leading to the improvement of the steel strength. 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 0.30-2.00%.
  • Ni exists in the form of solid solution in steel, which can improve the low-temperature impact performance of the steel.
  • an excessively high Ni content will lead to an excessively high content of retained austenite in steel, thereby reducing the strength of the steel.
  • the Ni content is set to 0.50 ⁇ 2.00%.
  • Mo can be dissolved in the form of solid-solution in steel and help to improve the hardenability and the strength of the steel. Mo will form fine carbides when the steel is tempered at a high temperature, which can further increase the strength of the steel. Considering the cost of the precious metal Mo, in the present invention, the Mo content is set to 0.10 ⁇ 0.80%.
  • Cu can improve the strength and the corrosion resistance of the steel. If the Cu content is too high, Cu will accumulate at the grain boundaries during heating, resulting in the weakening of the grain boundaries and then the steel cracking. In the present invention, the Cu content is set to 0.01 ⁇ 0.30%.
  • Al forms fine AlN precipitates in steel, which can inhibit the growth of austenite grains. If the Al content is too high, the coarse Al oxides will be formed, those coarse and hard inclusions will result in reduced impact toughness and fatigue properties of the steel. In the present invention, the Al content is set to 0.01 ⁇ 0.05%.
  • Nb is added to the steel to form fine precipitates, which can inhibit the recrystallization of the steel and refine the grains. If the Nb content is too high, coarse NbC particles will be formed during smelting, which will reduce the impact toughness of the steel. Grain refinement plays an important role in improving the mechanical properties of the steel, especially the strength and the toughness. In the meanwhile, grain refinement also helps to reduce the hydrogen embrittlement susceptibility of the steel. In the present invention, the Nb content is set to 0.001 ⁇ 0.10%.
  • V can form precipitates with C or N in steel to improve the steel strength. If the C and V contents are too high, coarse VC particles will be formed. In the present invention, the V content is set to 0.001 ⁇ 0.10%.
  • the Ti content is set to 0.003% or less.
  • the B element Since the B element is easy to segregate, the B content is limited to 0.0010% or less.
  • the addition of Ca element to the steel can improve the size and morphology of sulfide inclusions and avoid the deterioration of the impact toughness.
  • Ca element is easy to form inclusions and affect the fatigue performance of the final product.
  • the Ca content is controlled at 0.005% or less.
  • N is a type of interstitial atoms, and is also an element for forming MX-type precipitates.
  • the N content is set to 0.015% or less.
  • the ratio of contents of microalloying elements Al, Nb and V to the content of N has to be controlled, and thus a coefficient of microalloying elements is defined as r M/N , wherein r M/N is 1.0 ⁇ 9.9, and
  • r M / N A l / 2 + N b / 7 + V / 4 / N .
  • the coefficient of microalloying elements is related to the nano-scale precipitates.
  • a high coefficient of microalloying elements will lead to the presence of coarse precipitates in steel, which cannot achieve the effect of precipitation strengthening.
  • the high coefficient of microalloying elements will lead to adverse effects similar to inclusions, resulting in a decrease in fatigue strength.
  • a low coefficient of microalloying elements will lead to a small amount of precipitates, which cannot achieve the effect of dispersion strengthening.
  • the coefficient r M/N of microalloying elements is 1.0-6.0.
  • Trace elements such as Sn, Sb, As, Bi, and Pb segregate to grain boundaries at the tempering temperature, leading to the weakening of the intergranular bonding force. Mn and Si can promote the segregation of those harmful elements and thus increase the embrittlement of the steel.
  • Sn, Sb, As, Bi, and Pb are harmful to the environment, in the present invention, the contents of those elements are set as follows: As ⁇ 0.05%, Pb ⁇ 0.05%, Sn ⁇ 0.02%, Sb ⁇ 0.01%, and Bi ⁇ 0.01%.
  • the coefficient J H of harmful elements is ⁇ 500, and
  • J H P + S n + A s + P b + S b + B i ⁇ S i + M n ⁇ 10000 .
  • H will accumulate at the defects in steel.
  • the tensile strength exceeds 1200 MPa, and the H content has to be controlled at 0.00018% or less.
  • N forms nitrides or carbonitrides in steel, which plays a role of refining austenite grains. But a high N content leads to the formation of coarse particles, which will not help to refine the grains.
  • N is an interstitial atom and will accumulate in the grain boundaries, resulting in the decrease of the impact toughness.
  • the N content is controlled at 0.0150% or less.
  • O and Al in steel form oxides and composite oxides, etc. In order to ensure the uniformity of the steel structure, and the low-temperature impact energy and the fatigue performance of the steel, in the present invention, the content of O is controlled at 0.0020% or less.
  • the carbon equivalent Ceq of the steel has to be controlled at 0.80 or less, wherein
  • the index I of atmospheric corrosion resistance is 7.0 or more, wherein
  • microstructures of the steel for mining chain in the present invention are tempered martensite, bainite, and retained austenite.
  • the manufacturing method of the steel for mining chain in the present invention comprising steps of smelting, casting, heating, forging or rolling, quenching heat treatment and tempering heat treatment processes; wherein in said heating process, the heating temperature is 1050 ⁇ 1250° C., the holding time is 3 ⁇ 24 hr.; in said forging or rolling process, the final forging temperature or the final rolling temperature is ⁇ 800° C.; in said quenching heat treatment, the heating temperature is 850 ⁇ 1000° C., the holding time is 60 ⁇ 240 min, and a water quenching is implemented after austenitization; in said tempering heat treatment, the tempering temperature is 350 ⁇ 550° C., the holding time is 60 ⁇ 240 min, and after tempering, a steel billet is air cooled or water cooled.
  • said smelting can be smelting in electric furnace or smelting in converter, and then the molten steel is subject to refining and vacuum treatment.
  • said casting is die casting or continuous casting.
  • a steel billet is directly forged to size of final product; in said rolling process, a steel billet is directly rolled to size of final product, or a steel billet is rolled to a specified intermediate billet size, and then heated and rolled to size of final product, wherein the heating temperature of the intermediate billet is 1050 ⁇ 1250° C., and the holding time is 3 ⁇ 24 hr.
  • a steel billet is subjected to descaling of high pressure water when out of the heating furnace and is then rolled, and after rolling, the steel billet air cooled or slow cooled.
  • the steel for mining chain in the present invention has a yield strength R p0.2 ⁇ 1000 MPa, a tensile strength R m ⁇ 1200 MPa, a elongation A ⁇ 12%, a reduction of area Z ⁇ 50%, a Charpy impact work A kv ⁇ 60 J, and a coefficient of hydrogen embrittlement ⁇ (Z) ⁇ 15%.
  • This kind of steels has good strength, good plasticity, good roughness, and good weather resistance and stress corrosion resistance.
  • the steel for mining chain in the present invention can be used in scenarios where high-strength steel bars are required, wherein the size and gauge range ⁇ of the steel bar is 50 ⁇ 170 mm.
  • the steel for mining chain with high strength and roughness in the present invention is heated at 1050 ⁇ 1250° C. to be completely austenitized.
  • carbides, nitrides and carbonitrides of Al, Nb, V and carbides of Cr and Mo can be 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 the steel, thereby increasing the hardness and strength of martensite.
  • the temperature of final rolling or final forging is ⁇ 800° C., complex matrix structures of refined martensite, a small amount of bainite, and retained austenite are formed, and fine and dispersed precipitates are formed as well.
  • Al, Nb, V, Cr and Mo will form fine precipitates with C and N, which improves the matching of the steel strength and plastic toughness.
  • the steel has good strength and plasticity and good toughness, which is beneficial to the processing and application of the steel bars. For example, produce mining chains having good performance by forging or welding.
  • the U.S. Pat. US006146583 discloses an alloy steel composition and chain products fabricated in such alloy steel, wherein the components of the steel are: C: 0.15 ⁇ 0.28%, Cr: 0.2 ⁇ 1.0%, Mo: 0.1 ⁇ 1.0%, Ni: 0.3 ⁇ 1.5%, V: 0.05 ⁇ 0.2%, and the balance is Fe and inevitable impurities.
  • the strength of the steel can reach 800 MPa grade, and the steel has stress corrosion resistance.
  • the chains having high strength and roughness can be obtained by forgoing, welding, and heat treatment.
  • the present invention adopts different Cu content in the composition and optimizes the contents of C, N, and the contents of alloying elements such as Mn, Cr, Ni, Mo, and the contents of microalloying elements such as Al, V, and Nb.
  • the present invention adopts the composition design comprising C, Ni and Cu elements and optimizes the contents of Mn, Cr, and Mo, and thus complex microstructures of tempered martensite, a small amount of bainite, and retained austenite can be formed.
  • the mechanical properties of the steel in the present invention are obviously better than those of the steel in the US patent.
  • the Chinese Patent CN103276303A discloses a high-strength steel for mining chain and the manufacturing method thereof.
  • the components of the chain steel are: 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%, and the balance is Fe.
  • the manufacturing method comprises: smelting process in electric furnace or converter, out-of-furnace refining process, billet continuous casting process, and heating and rolling process to obtain straight bars with a gauge ⁇ of 20 ⁇ 50 mm, and a high-strength steel for mining chain can be obtained after annealing.
  • the contents of Cr, Mn, Ni and Mo in the steel of the present invention are completely different.
  • the present invention optimizes the contents of C, Cu, Al, Nb, and V, and limits the contents of N and Ca.
  • the microstructures of tempered martensite and retained austenite are formed, and the steels show the mechanical properties of high strength and toughness.
  • the high-strength steel having a tensile strength greater than 1000 MPa it will adsorb H in the environment, thereby causing delayed cracking of the steel.
  • High-strength steel bars with heavy gauge are more sensitive to hydrogen.
  • the content of H in steel is controlled in the present invention, but there is no such requirement in the Chinese patent application. Therefore, the stress corrosion resistance and delayed cracking resistance of the steel in the present invention are better than those of the steel in the Chinese patent application. That patent is used to manufacture straight bars of ⁇ 20 ⁇ 50 mm, while the present invention can be used to manufacture steel bars of ⁇ 50 ⁇ 170 mm, the method of the present invention has wider application and can be used to manufacture the steels with heavier gauges.
  • the present invention is completely different with the above-mentioned patent from the technical route in terms of composition, organization and process design.
  • the steel has a tensile strength R m ⁇ 1200 MPa, a yield strength R p0.2 ⁇ 1000 MPa, and an impact energy A kv ⁇ 60 J.
  • the strength grade of the steel in the present invention is greater than that of the steel in the above-mentioned patent.
  • the steel in the present invention has excellent impact toughness and stress corrosion cracking resistance.
  • the round section test pieces are prepared referring to the requirements of DNV (DET NORSKE VERITAS) on the susceptibility to hydrogen embrittlement and following GB/T 2975-2018 “Steel and steel products-Location and preparation of samples and test pieces for mechanical testing”, wherein the diameter of the test pieces is 10 mm.
  • the tensile testing is carried out according to the national standard GB/T 228.1, the strain rate is ⁇ 0.0003/s, and thus the reduction of area Z is obtained.
  • the coefficient of hydrogen embrittlement ⁇ (Z) is defined to evaluate the stress corrosion resistance of the steel:
  • a small coefficient of hydrogen embrittlement ⁇ (Z) indicates a small stress corrosion tendency.
  • the coefficient of hydrogen embrittlement ⁇ (Z) of the steel in the invention is 15% or less, indicating that the steel has good stress corrosion resistance.
  • FIG. 1 is a metallographic microstructure photograph of the round steel of Example 2 in the present invention (the magnification is 500 times);
  • FIG. 2 is a metallographic microstructure photograph of the link chain of Example 2 in the present invention (the magnification is 500 times).
  • the chemical components of the round steels of the examples in the present invention and comparative examples are shown in Table 1.
  • the coefficients of components of the steels having high strength and roughness of Examples 1 ⁇ 7 in the present invention and those of the Comparative Examples 1 ⁇ 3 are shown in Table 2. It can be seen that in examples of the present invention, the coefficient r M/N of microalloying elements ranges from 1.0 ⁇ 9.9, the carbon equivalent Ceq is 0.80 or less, and the coefficient J H of harmful elements is 500 or less.
  • r M/N is the ratio of the content of microalloying elements Al, Nb, and V to the content of N.
  • test pieces are prepared following GB/T 2975-2018 “Steel and steel products-Location and preparation of samples and test pieces for mechanical testing”.
  • the mechanical testing is carried out following GB/T 228.1-2010 “Metallic materials-Tensile testing-Part 1: Method of test at room temperature”.
  • the impact roughness at room temperature is tested following GB/T 229-2007 “Metallic materials-Charpy pendulum impact test method”. 3 samples were tested and 3 values of impact work were obtained.
  • Molten steel is smelted in electric furnace and then subject to refining and vacuum treatment according to the chemical compositions shown in Table 1. After that, the molten steel is casted into continuous casting billet. Then the continuous casting billet is heated to 1050° C., the holding time is 4 hr. The steel billet is subjected to descaling of high pressure water when out of the heating furnace and is then rolled to an intermediate billet. The final rolling temperature is 850° C., and the intermediate billet size is 200 mm ⁇ 200 mm.
  • the intermediate billet is heated to 1050° C., the holding time is 24 hr., the intermediate billet is subjected to descaling of high pressure water when out of the heating furnace and is then rolled, the final rolling temperature is 800° C., and the size ⁇ of finished the steel bar is 50 mm.
  • the steel billet is stack cooled after rolling.
  • the quenching heating temperature is 850° C., the heating time is 60 min, the tempering temperature is 390° C., and the tempering time is 90 min.
  • the steel billet is air cooled after tempering.
  • the manufacturing method is implemented in the same way as Example 1, wherein the heating temperature is 1080° C., the holding time is 3 hr., the final rolling temperature is 880° C., and the intermediate billet size 220 mm ⁇ 220 mm.
  • the intermediate billet is heated to 1120° C., the holding time is 3h, the final rolling temperature is 850° C., and the size ⁇ of the finished steel bar is 75 mm.
  • the steel billet is air cooled after rolling.
  • the quenching heating temperature is 870° C., the heating time is 100 min, the tempering temperature is 550° C., and the tempering time is 60 min.
  • the steel billet is water cooled after tempering.
  • the manufacturing method is implemented in the same way as Example 1, wherein the heating temperature is 1120° C., the holding time is 8 hr., the final rolling temperature is 940° C., and the intermediate billet size is 260 mm ⁇ 260 mm.
  • the intermediate billet is heated to 1200° C., the holding time is 5 hr., the final rolling temperature is 880° C., and the size ⁇ of the finished steel bar is 100 mm.
  • the steel billet is air cooled after rolling.
  • the quenching heating temperature is 890° C., the heating time is 150 min, the tempering temperature is 430° C., and the tempering time is 100 min.
  • the steel billet is air cooled after tempering.
  • the manufacturing method is implemented in the same way as Example 1, wherein the heating temperature is 1250° C., the holding time is 14 hr., and the steel billet is formed by hot continuous rolling.
  • the final rolling temperature is 900° C.
  • the size ⁇ of the finished steel bar is 150 mm.
  • the steel billet is air cooled after rolling.
  • the quenching heating temperature is of 990° C.
  • heating time is 210 min
  • the tempering temperature is 350° C.
  • tempering time is 180 min.
  • the steel billet is water cooled after tempering.
  • the heating temperature is 1180° C.
  • the holding time is 3.5 hr.
  • the final rolling temperature is 980° C.
  • the intermediate billet size is 280 mm ⁇ 280 mm.
  • the intermediate billet is heated to 1250° C.
  • the holding time is 12 hr.
  • the final rolling temperature is 950° C.
  • the size ⁇ of the finished steel bar is 160 mm.
  • the steel billet is slow cooled after rolling.
  • the quenching heating temperature is 900° C., the heating time is 210 min, the tempering temperature is 450° C., and the tempering time is 190 min.
  • the steel billet is water cooled after tempering.
  • the manufacturing method is implemented in the same way as Example 5, wherein the heating temperature is 1220° C.; the holding time is 24 hr.
  • the steel billet is formed by forging, the final forging temperature is 920° C., and the size ⁇ of the finished steel bar is 170 mm.
  • the steel billet is air cooled after forging.
  • the quenching heating temperature is 920° C., the heating time is 240 min, the tempering temperature is 420° C., and the tempering time is 240 min.
  • the steel billet is air cooled after tempering.
  • the manufacturing method is implemented in the same way as Example 2, wherein the heating temperature is 1080° C., the holding time is 3 hr., the final rolling temperature is 880° C., and the intermediate billet size is 220 mm ⁇ 220 mm. Then the intermediate billet is heated to 1100° C., the holding time is 3 hr., the final rolling temperature is 850° C., the size ⁇ of the finished steel bar is 65 mm. The steel billet is air cooled after rolling. The quenching heating temperature is 880° C., the heating time is 150 min, the tempering temperature is 400° C., and the tempering time is 100 min. The steel billet is water cooled after tempering.
  • Comparative Examples 1 ⁇ 3 are commercial materials from different manufacturers, the heat treatment processes refer to the recommended parameters of the supplier, see Table 3.
  • the Comparative Example 1 has a high Nb content and a microalloying coefficient of 10.1. It shows a poor precipitation strengthening effect, a low strength, a low impact toughness, and a short fatigue life.
  • the Comparative Example 2 has a high P content, a coefficient of harmful elements of 678, and an index of atmospheric corrosion resistance of 5.3. It shows poor impact toughness and stress corrosion cracking resistance, and a high coefficient of hydrogen embrittlement.
  • the Comparative Example 3 has a high S content, resulting in poor impact toughness.
  • the high-strength steels of Examples 1-7 in the present invention have the yield strength R p0.2 ⁇ 1000 MPa, the tensile strength R m ⁇ 1200 MPa, the elongation A ⁇ 12%, the reduction of area Z ⁇ 50%, the Charpy impact work A kv ⁇ 60 J, and the coefficient of hydrogen embrittlement ⁇ (Z) ⁇ 15%.
  • the steel of Example 6 shows relatively poor structure denseness due to the one-time heating and rolling process and the large bar size. Its strength and impact properties are slightly degraded compared with steels of other Examples.
  • the steel of Example 7 shows degraded impact toughness, coefficient of hydrogen embrittlement, and corrosion cracking resistance due to the lower atmospheric corrosion resistance index, and has poor performance compared with steels of other Examples.
  • microstructures of the round steel of Example 2 and the mining chain prepared using the steel of Example 2 were studied, and the optical microscope photographs are shown in FIGS. 1 and 2 . It can be seen from the figures that the microstructures of the round steel are tempered martensite, a small amount of bainite, and retained austenite, while the microstructures of the mining chain further prepared using the round steel of Example 2 are refined tempered martensite and a small amount of bainite.

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MX2022010591A (es) 2022-09-07
EP4089197A4 (en) 2023-07-26
KR20220129609A (ko) 2022-09-23
EP4089197A1 (en) 2022-11-16
CN113322409A (zh) 2021-08-31

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