EP3128032A1 - Dickes stahlblech und verfahren zur herstellung davon - Google Patents

Dickes stahlblech und verfahren zur herstellung davon Download PDF

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EP3128032A1
EP3128032A1 EP15774087.9A EP15774087A EP3128032A1 EP 3128032 A1 EP3128032 A1 EP 3128032A1 EP 15774087 A EP15774087 A EP 15774087A EP 3128032 A1 EP3128032 A1 EP 3128032A1
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steel plate
temperature
content
thick steel
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French (fr)
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EP3128032A4 (de
EP3128032B1 (de
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Shinichi Miura
Masao YUGA
Akio Ohmori
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JFE Steel Corp
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JFE Steel Corp
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    • C—CHEMISTRY; METALLURGY
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    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
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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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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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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    • C22C38/00—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
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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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
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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
    • 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
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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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
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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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
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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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the present invention relates to a thick steel plate which can preferably be used for members of, for example, industrial machines and transporting and conveying devices which are required to have abrasion resistance against, for example, rock, sand, ore, and slurry materials and a method for manufacturing the steel plate.
  • the members of, for example, industrial machines such as power shovels, bulldozers, hoppers, buckets, and dump trucks and transporting and conveying devices such as steel pipes used for transporting slurry materials, which are used in the field sites of, for example, construction, civil engineering, and mines, are subjected to abrasion in use due to, for example, earth and sand.
  • Patent Literature 1 proposes a steel plate having a chemical composition containing, by mass%, C: 0.13% to 0.18%, appropriate amounts of Si, Mn, P, S, Al, B, and N, Cr: 0.5% to 2.0%, Mo: 0.03% to 0.3%, and Nb: 0.03% to 0.1%, in which the constituent chemical elements satisfy the condition that HI is 0.7 or more, in which Ceq is more than 0.50, and in which HB is 360 or more and 440 or less at a temperature of 25°C.
  • HI [C] + 0.59[Si] - 0.58[Mn] + 0.29[Cr] + 0.39[Mo] + 2.11([Nb]-0.02) - 0.72[Ti] + 0.56[V]
  • Ceq [C] + [Si]/24 + [Mn]/6 + [Ni]/40 + [Cr]/5 + [Mo]/4 + [V]/14, where the atomic symbols respectively denote the contents (mass%) of the corresponding alloy chemical elements.
  • Patent Literature 1 describes that, according to the technique described above, by forming a martensite structure having a HB of about 400 by performing a quenching treatment, and by increasing the amount of a solid solution Nb, it is possible to increase high-temperature abrasion resistance.
  • Patent Literature 2 proposes a steel plate having a chemical composition containing, by mass%, C: 0.10% to 0.45%, appropriate amounts of Si, Mn, P, S, and N, and Ti: 0.10% to 1.0%, in which the number of TiC precipitates or compound precipitates of TiC with TiN and TiS having a grain diameter of 0.5 ⁇ m or more is 400 or more per 1 mm 2 , and in which Ti*, which is expressed by a particular relational expression, is 0.05% or more and less than 0.4%.
  • Patent Literature 3 proposes an abrasion-resistant steel plate excellent in terms of workability, the steel plate having a chemical composition containing, by mass%, C: 0.05% to 0.35%, appropriate amounts of Si, Mn, and Al, Ti: 0.1% to 1.2%, in which DI*, which is expressed by a particular relational expression, is less than 60, and a microstructure including a ferrite phase-bainite phase structure as a matrix structure, in which hard phases are dispersed.
  • Patent Literature 2 and Patent Literature 3 describe that, according to the techniques described above, by forming precipitates mainly including TiC having a large grain diameter in a solidification process, it is possible to increase abrasion resistance at low cost.
  • an object of the present invention is to provide an inexpensive thick steel plate excellent in terms of workability and abrasion resistance and a method for manufacturing the steel plate.
  • the present inventors in order to achieve the object described above, diligently conducted investigations regarding the influence of various factors on abrasion resistance, and, as a result, found that, by optimizing the chemical composition of a steel material, by controlling a value which is defined as the total content of plural alloy chemical elements in the chemical composition to be a certain value, and by forming a steel microstructure in which the area fraction of a bainite phase is 60% or more, the area fraction of Martensite-Austenite constituent (hereafter referred to as 'MA constituent') in the bainite phase is 5% or more and less than 20%, and the balance is one, two, or all of a ferrite phase, a pearlite phase, and a martensite phase, it is possible to provide a steel material with excellent abrasion resistance while maintaining good workability without excessively increasing the hardness of the steel material.
  • a value which is defined as the total content of plural alloy chemical elements in the chemical composition to be a certain value
  • 'MA constituent' the area fraction of Mart
  • the present invention has been completed on the basis of the knowledge described above and additional investigations. That is, the subjective matter of the present invention is as follows.
  • an abrasion-resistant steel plate excellent in terms of workability and stably having excellent abrasion resistance which has a marked effect on the industry.
  • Fig. 1 is a diagram illustrating an abrasion test machine.
  • % refers to mass%
  • C is a chemical element which contributes to the formation of MA constituent and which is important for achieving excellent abrasion resistance.
  • the C content is less than 0.200%, it is not possible to sufficiently realize the effects described above.
  • the C content is more than 0.350%, there is a decrease in weldability and workability. Therefore, the C content is limited to be 0.200% or more and 0.350% or less, or preferably 0.210% or more and 0.300% or less.
  • Si 0.05% or more and 0.45% or less
  • Si is an effective chemical element which functions as a deoxidizing agent for molten steel and which has a function of contributing to the formation of MA constituent by increasing hardenability.
  • the Si content is set to be 0.05% or more.
  • the Si content is limited to be 0.05% or more and 0.45% or less, or preferably 0.15% or more and 0.40% or less.
  • Mn 0.50% or more and 2.00% or less
  • Mn is an effective chemical element which has a function of contributing to the formation of MA constituent by increasing hardenability. In order to realize such an effect, it is necessary that the Mn content be 0.50% or more. On the other hand, in the case where the Mn content is more than 2.00%, there is a decrease in weldability, and a large amount of MnS, which becomes the starting point at which fracturing occurs when work such as bending is performed, is formed. Therefore, the Mn content is limited to be 0.50% or more and 2.00% or less, or preferably 0.60% or more and 1.70% or less.
  • the P content in steel is large, there is a decrease in toughness. Therefore, it is preferable that the P content be as small as possible. In the present invention, it is acceptable that the P content be 0.020% or less. Therefore, the P content is limited to be 0.020% or less. Here, since excessively decreasing the P content causes an increase in refining costs, it is preferable that the P content be 0.005% or more.
  • the S content in steel is large, since S is precipitated in the form of MnS, there is a decrease in toughness, and MnS becomes the starting point at which fracturing occurs when work is performed. Therefore, it is preferable that the S content be as small as possible. In the present invention, it is acceptable that the S content be 0.005% or less. Therefore, the S content is limited to be 0.005% or less. Here, since excessively decreasing the S content causes an increase in refining costs, it is preferable that the S content be 0.0005% or more.
  • Al 0.005% or more and 0.100% or less
  • Al is an effective chemical element which functions as a deoxidizing agent for molten steel. In order to realize such an effect, it is necessary that the Al content be 0.005% or more. In the case where the Al content is less than 0.005%, it is not possible to sufficiently realize such an effect. On the other hand, in the case where the Al content is more than 0.100%, there is a decrease in weldability and toughness. Therefore, the Al content is limited to be 0.005% or more and 0.100% or less, or preferably 0.015% or more and 0.040% or less.
  • CI 60 C + 8 Si + 22 Mn + 10 Cu + Ni + 14 Cr + 21 Mo + 15 V ⁇ 40
  • CI is limited to be 40 or more, or preferably 44 or more.
  • CI is preferable that CI be 80 or less, or more preferably 75 or less.
  • the chemical composition described above is the basic chemical composition, and the balance is Fe and inevitable impurities.
  • one, or two or more selected from among Cu, Ni, Cr, Mo, V, Nb, Ti, B, REM, Ca, and Mg may be added as selective chemical elements.
  • Cu is a chemical element which has an effect of contributing to the formation of MA constituent by increasing quench hardenability. In order to realize such an effect, it is necessary that the Cu content be 0.03% or more. On the other hand, in the case where the Cu content is more than 1.00%, there is a decrease in hot workability, and there is an increase in manufacturing costs. Therefore, in the case where Cu is added, it is preferable that the Cu content be limited to be 0.03% or more and 1.00% or less. Here, it is more preferable that the Cu content be limited to be 0.03% or more and 0.50% or less from the viewpoint of inhibiting a decrease in hot workability and of decreasing cost.
  • Ni 0.03% or more and 2.00% or less
  • Ni is a chemical element which increases quench hardenability and which contributes to an increase in low-temperature toughness. In order to realize such effects, it is necessary that the Ni content be 0.03% or more. On the other hand, in the case where the Ni content is more than 2.00%, there is an increase in manufacturing costs. Therefore, in the case where Ni is added, it is preferable that the Ni content be limited to be 0.03% or more and 2.00% or less. Here, it is more preferable that the Ni content be limited to be 0.03% or more and 0.50% or less from the viewpoint of decreasing cost.
  • Cr is a chemical element which has an effect of contributing to the formation of MA constituent by increasing quench hardenability. In order to realize such an effect, it is necessary that the Cr content be 0.05% or more. On the other hand, in the case where the Cr content is more than 2.00%, there is a decrease in weldability, and there is an increase in manufacturing costs. Therefore, in the case where Cr is added, the Cr content is limited to be 0.05% or more and 2.00% or less, preferably 0.07% or more and 1.50% or less, or more preferably 0.20% or more and 1.00% or less.
  • Mo is a chemical element which has an effect of contributing to the formation of MA constituent by increasing quench hardenability. In order to realize such an effect, it is necessary that the Mo content be 0.05% or more. On the other hand, in the case where the Mo content is more than 1.00%, there is a decrease in weldability, and there is an increase in manufacturing costs. Therefore, in the case where Mo is added, the Mo content is limited to be 0.05% or more and 1.00% or less, preferably 0.10% or more and 0.80% or less, or more preferably 0.20% or more and 0.50% or less.
  • V 0.005% or more and 0.100% or less
  • V is a chemical element which increases quench hardenability and which contributes to an increase in toughness through the effect of decreasing the grain diameter of a microstructure as a result of being precipitated in the form of carbonitrides.
  • the V content be 0.005% or more.
  • the V content is limited to be 0.005% or more and 0.100% or less.
  • Nb 0.005% or more and 0.100% or less
  • Nb is a chemical element which effectively contributes to an increase in toughness through the effect of decreasing the grain diameter of a microstructure as a result of being precipitated in the form of carbonitrides.
  • the Nb content be 0.005% or more.
  • the Nb content is limited to be 0.005% or more and 0.100% or less.
  • the Nb content be 0.010% or more and 0.030% or less from the viewpoint of decreasing the grain diameter of a microstructure.
  • Ti is a chemical element which contributes to an increase in toughness through fixing of solid solution N as a result of being precipitated in the form of TiN. In order to realize such an effect, it is necessary that the Ti content be 0.005% or more. On the other hand, in the case where the Ti content is more than 0.100%, since carbonitrides having a large grain diameter are precipitated, there is a decrease in toughness. Therefore, in the case where Ti is added, the Ti content is limited to be 0.005% or more and 0.100% or less. Here, it is preferable that the Ti content be limited to be 0.005% or more and 0.030% or less from the viewpoint of decreasing cost.
  • B is a chemical element which contributes to an increase in quench hardenability when added in small amounts. In order to realize such an effect, it is necessary that the B content be 0.0003% or more. On the other hand, in the case where the B content is more than 0.0030%, there is a decrease in toughness. Therefore, in the case where B is added, the B content is limited to be 0.0003% or more and 0.0030% or less.
  • the REM inhibits a decrease in toughness and the formation of MnS, which causes fracturing when work is performed, by fixing S. In order to realize such effects, it is necessary that the REM content be 0.0005% or more. On the other hand, in the case where the REM content is more than 0.0080%, since there is an increase in the amount of inclusions in steel, there is a decrease in toughness. Therefore, in the case where REM is added, the REM content is limited to be 0.0005% or more and 0.0080% or less, and preferably 0.0005% or more and 0.0020% or less.
  • Ca inhibits a decrease in toughness and the formation of MnS, which causes fracturing when work is performed, by fixing S. In order to realize such effects, it is necessary that the Ca content be 0.0005% or more. On the other hand, in the case where the Ca content is more than 0.0050%, since there is an increase in the amount of inclusions in steel, there is a decrease in toughness. Therefore, in the case where Ca is added, the Ca content is limited to be 0.0005% or more and 0.0050% or less, or preferably 0.0005% or more and 0.0030% or less.
  • Mg 0.0005% or more and 0.0050% or less
  • Mg inhibits a decrease in toughness and the formation of MnS, which causes fracturing when work is performed, by fixing S. In order to realize such effects, it is necessary that the Mg content be 0.0005% or more. On the other hand, in the case where the Mg content is more than 0.0050%, since there is an increase in the amount of inclusions in steel, there is a decrease in toughness. Therefore, in the case where Mg is added, it is preferable that the Mg content be limited to be 0.0005% or more and 0.0050% or less, and more preferably 0.0005% or more and 0.0040% or less.
  • Bainite phase 60% or more in terms of area fraction
  • the content of a bainite phase is set to be 60% or more, and preferably 80% or more, in terms of area fraction.
  • MA constituent 5% or more and less than 20% in terms of area fraction
  • MA constituent finely disperses in a bainite phase and has a high hardness, MA constituent contributes to an increase in abrasion resistance.
  • the area fraction of MA constituent is less than 5% with respect to the whole microstructure, it is not possible to achieve the desired abrasion resistance.
  • the area fraction described above is 20% or more, the effect of increasing abrasion resistance becomes saturated, and there is an excessive increase in the hardness of a steel plate, which results in a decrease in workability and toughness. Therefore, the area fraction described above is set to be 5% or more and less than 20%.
  • MA constituent is formed between the laths of a bainite phase or at the grain boundaries of a bainite phase, and has a small grain diameter, it is difficult to distinguish between a bainite phase and MA constituent by using an optical microscope. Therefore, MA constituent is seen as a part of a bainite phase. That is, in the calculation of the above-described area fraction of the bainite phase, the area of MA constituent is included in the area of the bainite phase. However, the area fraction of MA constituent is calculated with respect to the whole microstructure.
  • the remaining constituent phases of the steel microstructure other than a bainite phase are one, or two or more of a ferrite phase, a pearlite phase, and a martensite phase.
  • a steel material having the chemical composition described above has the specified temperature after casting has been performed
  • the steel material is subjected to hot rolling without cooling the steel material or after having first cooled and then heated the steel material in order to obtain a steel plate having specified dimensions and shape.
  • molten steel be prepared by using a known casting method such as one using a converter and that the molten steel be made into a slab having specified dimensions by using a known method such as a continuous casting method.
  • An ingot casting-slabbing method may also be used in order to obtain a slab.
  • the slab heating temperature is limited to be 950°C or higher and 1250°C or lower.
  • the heating temperature is lower than 950°C, since there is an excessive increase in rolling load due to an increase in deformation resistance, there is a decrease in rolling efficiency.
  • it is necessary to uniformly form MA constituent across the whole steel plate.
  • the heating temperature is lower than 950°C, since there is insufficient diffusion of segregated chemical elements such as C and Mn existing in a micro-segregation portion in a steel material, MA constituent is preferentially formed in the segregation portion, which results in an uneven distribution of MA constituent.
  • the heating temperature is limited to be 950°C or higher and 1250°C or lower.
  • slab heating temperature refers to an average temperature in the thickness direction of the slab derived by thermal transfer-thermal conduction calculation. The average temperature in the thickness direction of a slab is almost equal to the temperature at a position located at 1/4 of the thickness.
  • Hot rolling is performed with a finishing delivery temperature equal to or higher than Ar 3 .
  • the finishing delivery temperature is set to be equal to or higher than the Ar 3 .
  • the upper limit of the finishing delivery temperature be 930°C or lower.
  • Accelerated cooling is started immediately after the hot rolling has been performed. "Immediately” means “within 30 seconds” after the hot rolling has been performed.
  • the cooling rate is set to be 5°C/sec or more, and the cooling stop temperature is set to be 400°C or higher and 650°C or lower. In the case where the cooling rate is less than 5°C/sec, since ferrite is formed, a sufficient amount of bainite is not formed. Therefore, the cooling rate is set to be 5°C/sec or more.
  • practical cooling rate is 80°C/sec or less.
  • cooling rate refers to an average cooling rate at a position located at 1/4 of the thickness between the time accelerated cooling is started and the time accelerated cooling is stopped.
  • the cooling start temperature, the cooling rate, the cooling stop temperature are specified in terms of the temperature at a position located at 1/4 of the thickness, because it is considered that the temperature at a position located at 1/4 of the thickness represent a temperature intermediate between that of the surface of the steel plate and that at a position at 1/2 of the thickness of the steel plate, and represents the average temperature of the whole thickness of the steel plate.
  • the cooling stop temperature is set to be 400°C or higher and 650°C or lower.
  • cooling stop temperature refers to the temperature at a position located at 1/4 of the thickness when accelerated cooling is stopped.
  • the accelerated cooling process may be performed after a process in which radiation cooling is performed after hot rolling has been performed to a temperature lower than 400°C in terms of the temperature at a position located at 1/4 of the thickness at which ferrite transformation or bainite transformation is completed and in which reheating is then performed to a temperature equal to or higher than Ac 3 and 950°C or lower. It is necessary that the accelerated cooling process be started before the temperature of the steel plate is lowered and ferrite transformation begins. Therefore, it is preferable that the accelerated cooling process be started within 30 seconds after the steel plate has been brought out of a reheating furnace.
  • the reheating temperature is lower than Ac 3 , reverse transformation from ferrite to austenite does not sufficiently occur. Since it is necessary that the microstructure of the whole steel plate be transformed into austenite in the reheating process, reheating is performed to a temperature equal to or higher than the Ac 3 in terms of the temperature at a position located at 1/2t of the steel plate. In the case where the reheating temperature is higher than 950°C, there is a negative effect on toughness due to an increase in austenite grain diameter, and there is an increase in energy consumption. Therefore, the reheating temperature is set to be equal to or higher than the Ac 3 and 950°C or lower.
  • Heating temperature refers to the temperature at a position located at 1/2t of a steel plate, and the reheating temperature is derived by thermal transfer-thermal conduction calculation.
  • the Ac 3 transformation temperature it is possible to determine the Ac 3 transformation temperature from a thermal expansion curve obtained when heating is performed from a temperature range for forming ferrite to a temperature range for forming austenite.
  • molten steels having the chemical compositions given in Table 1 By preparing molten steels having the chemical compositions given in Table 1 by using a vacuum melting furnace, and by casting the molten steel into a casting mold, 150 kg of steel ingots (slabs) were manufactured. The obtained slabs were heated and subjected to hot rolling, and then accelerated cooling was performed. Here, some of the steel plates were cooled with air after hot rolling had been performed, further reheated, and then subjected to accelerated cooling.
  • testing methods are as follows.
  • abrasion test piece having a thickness of 10 mm, a width of 25 mm, and a length of 75 mm
  • the abrasion test piece was mounted in a direction at a right angle to the rotational axis of the rotor of the abrasion test machine so that the surface of 25 mm x 75 mm faces in the tangential direction of the circumference of the rotational circle, and then an abrasion material was loaded into the drum.
  • Silica stone having an average grain diameter of 30 mm was used as an abrasion material.
  • a 180-degree bending test was performed on a steel sample (having a width of 100 mm, a length of 300 mm, and the thickness of the original steel plate (t mm)) by using a pressing bend method with a bending radius of 2.0t (t: thickness) in accordance with JIS Z 2248 (2006).
  • a visual test a case where a defect such as a crack or other was not found in the sample after the bending test had been performed was judged as the case of good bending workability.

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  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
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BR112016022532B1 (pt) 2021-05-25
KR101898567B1 (ko) 2018-09-13
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