US20220178007A1 - Binary alloy design method for marine stress corrosion-resistant high-strength low-alloy (hsla) stress corrosion-resistant steel - Google Patents

Binary alloy design method for marine stress corrosion-resistant high-strength low-alloy (hsla) stress corrosion-resistant steel Download PDF

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US20220178007A1
US20220178007A1 US17/498,779 US202117498779A US2022178007A1 US 20220178007 A1 US20220178007 A1 US 20220178007A1 US 202117498779 A US202117498779 A US 202117498779A US 2022178007 A1 US2022178007 A1 US 2022178007A1
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marine
stress corrosion
hsla
hydrogen
resistant steel
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Zhiyong Liu
Xiaogang Li
Wei Wu
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University of Science and Technology Beijing USTB
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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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment 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
    • 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
    • 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
    • C22C38/18—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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur

Definitions

  • the present disclosure belongs to the field of alloy composition design of high-strength low-alloy (HSLA) steels, and in particular, relates to a binary alloy design method for a marine HSLA stress corrosion-resistant steel.
  • HSLA high-strength low-alloy
  • the mechanism of anodic dissolution is related to a local microenvironment.
  • the enrichment of Cl ⁇ at the bottom of a rust layer leads to acidification of the environment and accelerates the process of local corrosion.
  • an acidic Cl ⁇ -enriched local microenvironment spot corrosion pits are initiated and developed rapidly under strong self-catalytic action, providing effective nucleation sites for the initiation and propagation of microcracks and resulting in anodic dissolution induced stress corrosion cracking.
  • the mechanism of hydrogen embrittlement is related to the diffusion, distribution and concentration of hydrogen atoms in a steel.
  • hydrogen atoms can diffuse into the steel matrix and gather in various defects and stress distortion regions. Once a local hydrogen atom concentration reaches a critical hydrogen concentration, it will lead to the initiation and propagation of cracks and hence hydrogen embrittlement induced stress corrosion cracking.
  • the stress corrosion cracking in the marine environment is usually caused by the two synergistic mechanisms as described above. It is desirable to prevent the synergistic effect of the two mechanisms by using technical means so as to avoid the stress corrosion cracking in the marine environment.
  • the stress corrosion resistance of a HSLA steel is improved creatively by alloying against anodic dissolution and hydrogen embrittlement in the present disclosure.
  • alloying is conducted to render the two corresponding mechanisms inoperative simultaneously with no adverse effect on the toughness and corrosion resistance of the marine HSLA steel.
  • the destructive action of a corrosive element in a rust layer is weakened, accompanied with reduction of local acidification degree, inhibition of the mass transfer or electrochemical process of a corrosive medium, and alleviation of anodic dissolution at the bottom of the rust layer.
  • Such a binary alloy design method can permit synergistic inhibition of the mechanisms of anodic dissolution and hydrogen embrittlement of HSLA steels in the marine environment, significant improvement of the stress corrosion resistance of HSLA steels, and reduction of the stress corrosion risk.
  • the new method of backward design has not yet been proposed.
  • the present disclosure provides a binary microalloy design method against the mechanisms of anodic dissolution and hydrogen embrittlement.
  • the method can improve the stress corrosion resistance of a HSLA steel in the marine environment by alloying of a plurality of elements.
  • An objective of the present disclosure is to provide a binary alloy design method for a marine HSLA stress corrosion-resistant steel.
  • a HSLA steel designed by this method can have a significant decrease in stress corrosion sensitivity in the marine environment compared with control groups.
  • the present disclosure provides a binary alloy design method for a marine HSLA stress corrosion-resistant steel, where synergistic inhibition of anodic dissolution and hydrogen embrittlement is achieved by binary alloying to prepare 690 MPa marine HSLA stress corrosion-resistant steel, so that the 690 MPa marine HSLA steel has an increase of more than 50% in stress corrosion resistance in a simulated SO 2 polluted marine atmospheric environment.
  • one of two alloying elements used in the binary alloying is one or more alloying elements that are capable of improving enrichment of Cl ⁇ in a rust layer and thus induced acidification in the marine environment while reducing the electrochemical activity of a matrix in an acidic Cl ⁇ -containing environment, while the other one is one or more alloying elements that are capable of inhibiting cathodic hydrogen evolution in the marine environment, forming irreversible hydrogen traps and improving a microstructure.
  • the inhibiting cathodic hydrogen evolution in the marine environment may be achieved by reducing an electric current density for hydrogen evolution; the forming irreversible hydrogen traps may be achieved by increasing a hydrogen trap density in the steel; and the improving a microstructure may be achieved by enhancing hydrogen resistance at special interfaces.
  • the alloying element for inhibiting the anodic dissolution is selected from the group consisting of P, Sb, Co, Cr, Ni, Cu, Mo, Re, Zr, Ca, Mg, and dispersive oxides thereof, and the alloying element for inhibiting the hydrogen embrittlement is (anti-damage element for short) is selected from the group consisting of Nb, V, Ti, Zr, Re, Mo and W.
  • the marine HSLA stress corrosion-resistant steel may be composed of the following chemical elements in mass percentage: C: 0.04%-0.08%, Si: 0.2%-0.3%, Mn: 1.45%-1.65%, P ⁇ 0.015%, S ⁇ 0.005%, Cr: 0.4%-0.5%, Cu: 0.25%-0.35%, Ni: 0.75%-0.85%, Ti: 0.005%-0.015%, Nb: 0.03%-0.06%, Sb: 0.05%-0.1%, and the balance of Fe.
  • the HSLA stress corrosion-resistant steel may be prepared specifically by the following process:
  • a slow strain rate tensile test may be conducted on the finished marine HSLA stress corrosion-resistant steel under the following conditions: SO 2 polluted marine atmospheric environment simulated by using 3.5 wt % NaCl+0.05 M NaHSO 3 with 100% humidity; experimental temperature: room temperature; and a slow strain tension rate: 0.5*10 ⁇ 6 to 1.5*10 ⁇ 6 S ⁇ 1 .
  • the loss of elongation percentage and the loss of section shrinkage percentage of the HSLA steel may be calculated to evaluate the stress corrosion sensitivity of the finished marine HSLA stress corrosion-resistant steel in the simulated SO 2 polluted marine atmospheric environment.
  • the loss of elongation percentage of the HSLA steel may be 11.05%-15.21%, while the loss of section shrinkage percentage may be 12.1%-14.33%, with a maximum decrease of approximate 60% in the stress corrosion sensitivity compared with a traditional HSLA steel.
  • the anodic dissolution is one of the major mechanisms during the stress corrosion cracking of a HSLA steel in the marine environment, which is related to a corrosive microenvironment and the electrochemical activity of a matrix.
  • the enrichment of Cl ⁇ at the bottom of a rust layer in the marine environment can induce spot corrosion. Acidification at the bottom in spot corrosion pits accelerates dissolution and microcracks are initiated under the action of stress, thus resulting in anodic dissolution induced stress corrosion cracking.
  • an alloying element against the mechanism of anodic solution is required to be effective in: first, alleviating enrichment of Cl ⁇ in a rust layer and thus induced acidification in the marine environment; and second, reducing the electrochemical activity of a matrix in an acidic Cl ⁇ -containing environment.
  • Investigations with respect to the effects in the two aspects revealed that the alloying of trace amount of element Sb could alleviate the enrichment of Cl ⁇ in the rust layer, weaken local acidification and reduce the electrochemical activity of a low-alloy steel in the acidic Cl ⁇ -containing environment, with a potential effect of inhibiting the mechanism of anodic solution.
  • the microalloying element Sb can improve the corrosion resistance of a low-alloy steel in the acidic Cl ⁇ -containing environment, specifically by facilitating the redeposition of element Cu and oxides thereof in the acidic Cl ⁇ -containing environment by synergistic action with Cu in steel, thereby enhancing the microalloying effect of Cu. Moreover, Sb can form Sb2O3 and Sb2O5 that are hardly soluble in acidic environment and may gather on the inner side of the rust layer to improve the properties of the rust layer. Under this action, Sb is microalloyed and thus enabled to reduce the electrochemical activity and alleviate the enrichment of Cl ⁇ and acidification in the rust layer, thus achieving the effect of inhibiting the anodic dissolution.
  • the inhibiting effect of Sb present in a particular amount on the anodic dissolution has been demonstrated by conducting tests on high-strength steels different in content of Sb in simulated marine atmospheric environment with respect to stress corrosion sensitivity.
  • the content of Sb was 0.05%
  • the inhibiting effect of Sb microalloying was not obvious; and when the content of Sb was 0.1%, the inhibiting effect of Sb microalloying was significant.
  • Alloying element design against the mechanism of hydrogen embrittlement is related to the concentration, diffusion and distribution of hydrogen atoms in steel.
  • Cathodic hydrogen evolution reaction is the main way for hydrogen to enter a steel matrix in the marine environment. A higher electric current density for hydrogen evolution and longer hydrogen evolution reaction time will result in a higher concentration of hydrogen atoms in steel.
  • Hydrogen traps in steel determine the diffusion and distribution of hydrogen atoms, and a higher density and more uniform distribution of hydrogen traps reflect a higher trapping ability of the hydrogen traps, and hence a smaller concentration of diffusible hydrogen in steel, a lower diffusion ability of hydrogen and a lower degree of hydrogen accumulation.
  • an alloy element against the mechanism of hydrogen embrittlement is required to be effective in: first, inhibiting the cathodic hydrogen evolution in the marine environment and reducing an electric current density electric current; second, forming irreversible hydrogen traps and increasing a hydrogen trap density in steel; and third, improving a microstructure and enhancing hydrogen resistance at special interfaces.
  • Nb is an important microalloying element for improving hydrogen behaviors in steel.
  • the microalloying of Nb can reduce the cathodic hydrogen evolution and help to reduce the total hydrogen concentration in steel.
  • Nb can form a large amount of stable, fine and dispersed nano-sized NbC precipitated phase with element C in steel.
  • the mechanical properties of steel can be improved by grain refining and precipitation strengthening.
  • the NbC precipitated phase can serve as high-energy hydrogen traps to trap hydrogen, thereby reducing the concentration of diffusible hydrogen, alleviating local hydrogen enrichment and improving the hydrogen resistance of the structure.
  • the inhibiting effect of Nb present in a particular amount on the hydrogen embrittlement has been demonstrated by conducting tests on high-strength steels different in content of Nb in simulated marine atmospheric environment with respect to stress corrosion sensitivity.
  • the content of Nb was 0.03%, the inhibiting effect of Nb microalloying was not obvious; when the content of Nb was 0.06%, the inhibiting effect of Nb microalloying was good; and when the content of Nb was 0.09%, part of Nb was accumulated in an inclusion, so that the content of the precipitated phase was not significantly increased, and the inhibiting effect of Nb microalloying was not significantly enhanced in this case.
  • the two effects of inhibiting the anodic dissolution and the hydrogen embrittlement by alloying are the core idea of the binary alloy design in the present disclosure, and there are no specific limitations to the number and levels of alloying elements for achieving the effects.
  • the effects can be achieved by an arbitrary combination of an element (such as Sb, Sn, and Mo) for inhibiting the anodic dissolution and an element (such as Nb, V, and Ti) for inhibiting the hydrogen embrittlement.
  • the illustrated elements Sb and Nb are merely representative alloying elements, which means two or more alloying elements can be used in the present disclosure.
  • the elements each in a particular amount can be used for microalloying or in low alloying design and main alloying design.
  • a HSLA designed by the binary alloy method as described above can be used in the marine environment or in other environments in which stress corrosion cracking may occur.
  • FIG. 1A shows a transmission electron microscope (TEM) image of precipitated phases in an example of a binary alloy design method for a marine HSLA stress corrosion-resistant steel of the present disclosure.
  • TEM transmission electron microscope
  • FIG. 1B shows a TEM of precipitated phases in comparative example 1 of a binary alloy design method for a marine HSLA stress corrosion-resistant steel of the present disclosure.
  • FIG. 1C shows a TEM image of precipitated phases in comparative example 5 of a binary alloy design method for a marine HSLA stress corrosion-resistant steel of the present disclosure.
  • FIG. 2 shows a graph of electrochemical polarization curves in an example and comparative examples 1-5 of a binary alloy design method for a marine HSLA stress corrosion-resistant steel of the present disclosure.
  • FIG. 3A shows interface morphology and element distribution images of rust layers in an example of a marine HSLA stress corrosion-resistant steel of the present disclosure.
  • FIG. 3B shows interface morphology and element distribution images of rust layers in comparative example 1 of a marine HSLA stress corrosion-resistant steel of the present disclosure.
  • the technical problem to be solved in the present disclosure is how to improve the stress corrosion resistance of a HSLA steel in the marine atmospheric environment.
  • the present disclosure provides a binary alloy design method for a marine HSLA stress corrosion-resistant steel, where synergistic inhibition of anodic dissolution and hydrogen embrittlement is achieved by binary alloying to prepare 690 MPa marine HSLA stress corrosion-resistant steel, so that the 690 MPa marine HSLA steel has an increase of more than 50% in stress corrosion resistance in a simulated SO 2 polluted marine atmospheric environment.
  • one of two alloying elements used in the binary alloying is one or more alloying elements that are capable of alleviating enrichment of Cl ⁇ in a rust layer and thus induced acidification in the marine environment while reducing the electrochemical activity of a matrix in an acidic Cl ⁇ -containing environment, while the other one is one or more alloying elements that are capable of inhibiting cathodic hydrogen evolution in the marine environment, forming irreversible hydrogen traps and improving a microstructure.
  • the inhibiting cathodic hydrogen evolution in the marine environment is achieved by reducing an electric current density for hydrogen evolution; the forming irreversible hydrogen traps is achieved by increasing a hydrogen trap density in the steel; and the improving a microstructure is achieved by enhancing hydrogen resistance at special interfaces.
  • the alloying element for inhibiting the anodic dissolution is selected from the group consisting of P, Sb, Co, Cr, Ni, Cu, Mo, Re, Zr, Ca, Mg, and dispersive oxides thereof
  • the alloying element for inhibiting the hydrogen embrittlement is selected from the group consisting of Nb, V, Ti, Zr, Re, Mo and W.
  • the marine HSLA stress corrosion-resistant steel is composed of the following chemical elements in mass percentage: C: 0.04%-0.08%, Si: 0.2%-0.3%, Mn: 1.45%-1.65%, P ⁇ 0.015%, S ⁇ 0.005%, Cr: 0.4%-0.5%, Cu: 0.25%-0.35%, Ni: 0.75%-0.85%, Ti: 0.005%-0.015%, Nb: 0.03%-0.06%, Sb: 0.05%-0.1%, and the balance of Fe.
  • the marine HSLA stress corrosion-resistant steel is prepared specifically by the following process:
  • a slow strain rate tensile test is conducted on the finished marine HSLA stress corrosion-resistant steel under the following conditions: SO 2 polluted marine atmospheric environment simulated by using 3.5 wt % NaCl+0.05 M NaHSO 3 with 100% humidity; experimental temperature: room temperature; and a slow strain tension rate: 0.5*10 ⁇ 6 to 1.5*10 ⁇ 6 S ⁇ 1 .
  • the loss of elongation percentage and the loss of section shrinkage percentage of the HSLA steel are calculated to evaluate the stress corrosion sensitivity of the finished marine HSLA stress corrosion-resistant steel in the simulated SO 2 polluted marine atmospheric environment.
  • the loss of elongation percentage of the HSLA steel is 11.05%-15.21%, while the loss of section shrinkage percentage is 12.1%-14.33%, with a maximum decrease of approximate 60% in the stress corrosion sensitivity compared with a traditional HSLA steel.
  • Table 1 shows chemical components in weight percentage in an example and comparative examples of HSLA steels obtained by the binary alloy design method of the present disclosure.
  • a steel plate was obtained by a controlled rolling and cooling process. Specifically, the billet steel was heated to an austenitizing temperature of 1200° C., and the temperature was kept for 2 hours to homogenize the billet steel. The billet steel was then cooled in the furnace to an initial rolling temperature of 1000° C. and subjected to 15 passes of reciprocating rolling into a 12 mm steel plate, with a finishing rolling temperature controlled within a range of 860-900° C. After rolling, the steel plate was cooled in a laminar water flow zone at a cooling rate controlled within a range of 25-30° C./s, ensuring that the billet steel was at a temperature ranging from 420 to 440° C. when taken out of water. Subsequently, the steel plate was air-cooled to room temperature.
  • the loss of elongation percentage and the loss of section shrinkage percentage of the HSLA steel were calculated to evaluate the stress corrosion sensitivity of the finished marine HSLA stress corrosion-resistant steel in the simulated SO 2 polluted marine atmospheric environment.
  • Table 2 shows the comparison of stress corrosion sensitivity between example 1 and comparative examples 1, 2, 3, 4, and 5 in the simulated SO 2 polluted marine atmospheric environment.
  • the stress corrosion sensitivity of the steel constantly decreased with the addition of elements Nb and Sb.
  • the HSLA steel had significantly reduced stress corrosion sensitivity in the simulated SO 2 polluted marine atmospheric environment as compared with comparative example 1, with a maximum decrease of approximate 60%.
  • the two effects of inhibiting the anodic dissolution and the hydrogen embrittlement by alloying are the core idea of the binary alloy design in the present disclosure, and there are no specific limitations to the number and levels of alloying elements for achieving the effects.
  • the effects can be achieved by an arbitrary combination of an anti-corrosion element (such as Sb, Sn, and Mo) and an anti-corrosion damage element (such as Nb, V, and Ti).
  • the illustrated elements Sb and Nb are merely representative alloying elements, which means two or more alloying elements can be used in the present disclosure.
  • the elements each in a particular amount can be used for microalloying or in low alloying design and main alloying design.
  • a HSLA designed by the binary alloy method as described above can be used in the marine environment or in other environments in which stress corrosion cracking may occur.

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Corrosion behavior of experimental copper-antimony-molybdenum carbon steels in industrial and marine atmospheres and in a sulphuric acid aqueous solution (Year: 2017) *
Effect of Nb on the hydrogen-induced cracking of high-strength low-alloy steel Zhang Shiqi (Year: 2018) *
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