WO2020078472A1 - 一种800MPa级热冲压桥壳钢及其制造方法 - Google Patents

一种800MPa级热冲压桥壳钢及其制造方法 Download PDF

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WO2020078472A1
WO2020078472A1 PCT/CN2019/111982 CN2019111982W WO2020078472A1 WO 2020078472 A1 WO2020078472 A1 WO 2020078472A1 CN 2019111982 W CN2019111982 W CN 2019111982W WO 2020078472 A1 WO2020078472 A1 WO 2020078472A1
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axle housing
mpa
hot stamping
housing steel
steel
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PCT/CN2019/111982
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English (en)
French (fr)
Chinese (zh)
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刘刚
张华伟
王巍
陆敏
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宝山钢铁股份有限公司
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Priority to KR1020217008010A priority Critical patent/KR102495857B1/ko
Priority to DE112019005199.7T priority patent/DE112019005199T5/de
Publication of WO2020078472A1 publication Critical patent/WO2020078472A1/zh

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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
    • B21D22/02—Stamping using rigid devices or tools
    • B21D22/022—Stamping using rigid devices or tools by heating the blank or stamping associated with heat treatment
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D53/00—Making other particular articles
    • B21D53/88—Making other particular articles other parts for vehicles, e.g. cowlings, mudguards
    • B21D53/90—Making other particular articles other parts for vehicles, e.g. cowlings, mudguards axle-housings
    • 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
    • C21D1/02—Hardening articles or materials formed by forging or rolling, with no further heating beyond that required for the formation
    • 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
    • C21D6/02—Hardening by precipitation
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips 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
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0463—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment following 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
    • C22C38/001—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
    • C22C38/02—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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing 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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • 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
    • C21D2211/005—Ferrite

Definitions

  • the invention relates to a steel type and a manufacturing method thereof, in particular to an 800MPa hot stamping axle housing steel and a manufacturing method thereof.
  • the axle housing As a key load-bearing component of automobiles, the axle housing has high requirements for safety and needs to meet strict component fatigue performance. That is to say, for the steel used for axle housings, stable performance of the steel plate, low temperature impact resistance and good weldability are required. Segregation and inclusions are strictly controlled.
  • China's hot stamping axle housing steels are mainly 16Mn, Q345C, Q420C, Q460C and other common C-Mn structural steels.
  • the strength of such C-Mn steel after hot stamping further decreases, for example, the yield strength of Q460C after hot stamping drops to about 400MPa.
  • axle housing steel which can reach the strength level of 800 MPa, and at the same time, the plasticity and fatigue performance of the steel plate are also good, which is more suitable for the manufacture of axle housings.
  • One of the objects of the present invention is to provide a 800 MPa class hot stamping axle housing steel, which can reach 800 MPa strength level, and at the same time, the 800 MPa class hot stamping axle housing steel also has good plasticity and fatigue performance, and is very suitable for manufacturing axles shell.
  • the present invention proposes an 800MPa hot stamping axle housing steel, the chemical element mass percentage is:
  • C In the 800 MPa hot stamping axle housing steel described in the present invention, carbon plays a role of solid solution strengthening. Adding C can increase the strength of lower bainite. In addition, C can also be used in the hot stamping air cooling process of the axle housing. Fe reacts to form dispersed Fe 3 C, which increases the strength of the steel sheet after hot stamping. However, if the mass percentage of C is too high, it is not conducive to the weldability of the steel plate. Therefore, in the 800 MPa grade hot stamping axle housing steel described in the present invention, the mass percentage of C is controlled to be 0.15 to 0.21%.
  • Si In the 800 MPa grade hot stamping axle housing steel described in the present invention, Si can suppress the precipitation of cementite at high temperature, which is beneficial to the formation of lower bainite, and at the same time, Si can also form fine infiltration in the steel plate Carbon body particles to improve the strength of lower bainite. However, too much Si content is not conducive to the weldability of the steel plate. Therefore, in the technical solution of the present invention, the mass percentage of Si is controlled to be 0.30 to 0.80%.
  • Mn For the technical solution described in the present invention, the addition of a certain content of Mn element is beneficial to promote the formation of lower bainite, and Mn can play a certain solid solution strengthening effect on the lower bainite structure.
  • Mn element is beneficial to the formation of finer ferrite or bainite during hot stamping of the steel sheet, which is beneficial to increase the strength of the steel sheet after hot stamping.
  • an excessively high content of Mn is not conducive to the weldability of the steel sheet. Therefore, the mass percentage of Mn in the 800 MPa grade hot stamping axle housing steel described in the present invention is 1.75-2.10%.
  • Nb For the 800 MPa hot stamping axle housing steel described in the present invention, during the controlled rolling and cooling stage, a small amount of Nb in the steel plate reacts with C to form fine NbC particles, which is conducive to refine the steel plate structure and at the same time It can also improve the strength, plasticity and toughness of the steel plate. In addition, NbC precipitates in the lower bainite structure, which can produce a strong precipitation strengthening effect. In addition, NbC can also refine the austenite grains during the hot stamping heating stage and improve the strength of the axle housing steel sheet after hot stamping. However, when the Nb element content is too high, the NbC particles are large, and the effect of suppressing the growth of austenite grains is weakened. Therefore, the mass percentage of Nb in the 800 MPa grade hot stamping axle housing steel described in the present invention is controlled at 0.015 to 0.040%.
  • Ti element will react with C during the phase transformation of austenite to ferrite after the steel sheet is rolled to form TiC particles with a diameter of several nanometers to several tens of nanometers, thereby producing precipitation strengthening Effect, especially in the range of 680 ⁇ 730 °C can produce finer interphase precipitation.
  • the fine TiC particles in the hot stamping heating stage can suppress the growth of austenite grains, and then refine the structure after hot stamping, and improve the strength of the bridge shell steel sheet after hot stamping.
  • the mass percentage of Ti in the 800 MPa hot stamping axle housing steel described in the present invention is controlled at 0.020 to 0.060%.
  • B In the 800 MPa grade hot stamped axle housing steel described in the present invention, a small amount of B can promote the formation of bainite. However, when the B element content is too high, B brittleness problems are likely to occur, which deteriorates the impact toughness of the steel plate. In addition, in the hot stamping stage of the axle housing, trace elements of B are beneficial to promote the formation of finer bainite and improve the strength of the steel plate. Therefore, the mass percentage of B in the 800 MPa grade hot stamping axle housing steel described in the present invention is controlled at 0.0015 to 0.0030%.
  • Al is an important deoxidizer, usually 0.02% or more of Al is added.
  • the oxide chain inclusions of Al need to be controlled, so the Al content is controlled in a lower range. Therefore, the mass percentage of Al in the 800 MPa hot stamping axle housing steel described in the present invention is controlled to 0.005 to 0.015%.
  • Ca For the 800 MPa hot stamping axle housing steel described in this invention, trace elements of Ca can act as a scavenger in the steel smelting process, improving the toughness and fatigue properties of the steel; meanwhile, Ca treatment can improve MnS The shape of the inclusions prevents the formation of elongated MnS inclusions. However, Ca content exceeding 0.001% tends to form larger size Ca compounds, but deteriorates toughness and fatigue performance. Therefore, the mass percentage of Ca in the 800 MPa hot stamping axle housing steel described in the present invention is controlled at 0.0004 to 0.001%.
  • N For the 800 MPa hot stamping axle housing steel described in the present invention, the N element needs to be controlled in a narrow range in this case. Trace elements of N can react with Ti to form TiN particles, which can effectively suppress the growth of austenite grains during welding and hot stamping, refine the welding heat affected zone and the structure after hot stamping, and improve the heat affected zone and heat The strength, low temperature toughness and fatigue performance of stamped steel plates. However, when the N content is too high, the formed TiN particles are too large, which will deteriorate the low temperature toughness and fatigue performance of the steel plate. Therefore, the mass percentage of N in the 800 MPa grade hot stamping axle housing steel described in the present invention is controlled at 0.001 to 0.004%.
  • P, S, and O are inevitable harmful impurity elements in steel materials, which are not conducive to steel performance.
  • P as an impurity element is prone to cold and brittle problems; S is easy to react with Mn to produce MnS inclusions, which is not conducive to fatigue performance in steel; O It is easy to react with Al to produce Al 3 O chain inclusions, which is not conducive to fatigue performance in steel.
  • the content of P, S, and O in steel needs to be as low as possible, but considering the economics of steel smelting costs, the mass percentage of the above inevitable impurity elements is controlled in a certain appropriate range, when the inevitable When the impurity elements are controlled within the appropriate range, the harmful effects of the inevitable impurity elements can be minimized, so that there is no obvious adverse effect on the performance of the steel.
  • the other inevitable impurities satisfy at least one of the following items: P ⁇ 0.015%, S ⁇ 0.0020%, O ⁇ 0.003% .
  • each related element also satisfies: Ti / N ⁇ 5, which is because by controlling Ti / N to ⁇ 5, it is beneficial to retain sufficient Ti element Reacts with C to form TiC precipitation strengthening.
  • the microstructure is ferrite + lower bainite, and the average width of the lower bainite lath is ⁇ 500 nm. 5-10%.
  • the average width of the lower bainite lath is ⁇ 400 nm.
  • nano-scale TiC interphase precipitates are formed in the ferrite, and the particle diameter of 70% or more of the TiC interphase precipitates in the ferrite is Below 30nm. This is for the present case, the finer the precipitates, the better the precipitation strengthening effect.
  • the grades of all types of non-metallic inclusions are below grade 1.0, and the total rating of all non-metallic inclusions is controlled below 3.0, and it does not have long strips Shaped inclusions.
  • the rating of non-metallic inclusions can be controlled to no greater than 1.0, and the overall rating of all non-metallic inclusions should be controlled below 3.0, while suppressing long strips
  • another object of the present invention is to provide a method for manufacturing the above 800MPa hot stamping axle housing steel.
  • the 800MPa hot stamping axle housing steel obtained by the manufacturing method can reach the strength level of 800MPa, while the 800MPa
  • the plasticity and fatigue performance of the grade hot stamping axle housing steel is also good, which is very suitable for manufacturing axle housing.
  • the present invention proposes a method for manufacturing the above 800MPa hot stamping axle housing steel, which includes the steps of:
  • Cooling cooling in two stages after rolling, first cooling the steel plate at a rate of 80-200 ° C / s to 680-730 ° C, natural air cooling for 5-7s; then cooling the steel plate at a rate of 30-70 ° C / s To 360 ⁇ 450 °C, then coiled or natural air cooled to room temperature.
  • the manufacturing method can obtain a small amount of ferrite + lower bainite structure through sectional cooling control combined with coiling in the middle temperature range of 360 to 450 ° C,
  • the average width of the lower bainite lath is ⁇ 500 nm, so that the steel plate finally obtained has a yield strength ⁇ 800 MPa, a tensile strength ⁇ 900 MPa, an elongation A 50 ⁇ 22%, and an impact energy of -20 ° C above 60J.
  • step (3) the reduction rate of the last pass rolling is controlled to be> 15%; the final rolling temperature is 820 to 900 ° C, in order to enable the austenite to accumulate enough before the bainite transformation Deformation promotes the formation of finer bainite structures. If the rolling temperature is too low, the high-temperature phase transformation of ferrite is likely to occur, which reduces the strength of the steel; if the rolling temperature is too high, the deformation accumulated in the austenite will be restored, which is not conducive to refining the structure after phase transformation.
  • step (4) the steel plate is first cooled at a cooling rate of 80 to 200 ° C / s to 680 to 730 ° C, in order to quickly cool to the temperature range of ferrite formation, natural air cooling is 5-7s, and the formation ratio is 5-10% ferrite.
  • a cooling rate of 80 to 200 ° C / s to 680 to 730 ° C in order to quickly cool to the temperature range of ferrite formation, natural air cooling is 5-7s, and the formation ratio is 5-10% ferrite.
  • the steel plate is rapidly cooled to a lower temperature of 360-450 ° C at a cooling rate of 30-70 ° C / s, and then coiled or naturally air-cooled to room temperature.
  • rapid cooling is to suppress the ferrite from continuing to change phase It is cooled to 360 ⁇ 450 °C coiling or natural air cooling is to form a fine lower bainite structure, while keeping the temperature at a lower temperature is conducive to inhibit the continued growth of precipitate particles.
  • step (2) the slab is heated in a furnace with a target temperature range of 1180 to 1270 ° C. After warming to the target temperature, heat preservation starts, and the heat preservation time is> 1.5h.
  • the slab is heated in a furnace with a target temperature ranging from 1180 to 1270 ° C.
  • the heat preservation is started.
  • the heat preservation time is> 1.5h to ensure that the alloy elements are fully solidified. Dissolve.
  • the slab heating furnace has three stages of preheating, heating and soaking. Whether the current core of the slab is heated to the target temperature is calculated according to the calculation model provided by the heating furnace equipment supplier, which can be calculated The time required for the billet in the three stages of preheating, heating, and soaking to reach the target temperature, and the calculation model was checked with a thermocouple in the early stage of development.
  • the heating temperature exceeds 1270 ° C
  • the austenite grains grow excessively, causing the intergranular bonding strength to be weakened, and cracks are easy to occur during rolling; in addition, the heating temperature exceeding 1270 ° C may easily cause decarburization of the slab surface and the mechanics of the final steel Performance is adversely affected.
  • the 800MPa hot stamping axle housing steel described in the present invention is excellent in strength, impact, fatigue, welding, etc. It controls the inclusions that affect fatigue through rationally optimized alloy design, for example, in controlling rolling, Sectional cooling, and coiling in the middle temperature range or natural air cooling to room temperature, to control the formation of the required ferrite + lower bainite, and is conducive to the formation of nano-scale precipitate particles in ferrite, which ultimately makes the present invention
  • the 800 MPa grade hot stamping axle housing steel described above achieves a high plasticity at the 800 MPa yield strength level, that is, an elongation A 50 ⁇ 22%, and its low temperature impact performance and welding performance are good.
  • the 800 MPa hot stamping axle housing steel described in the present invention specifically controls the components and inclusions that may affect the fatigue performance of the steel plate, it is conducive to improving the fatigue performance of the steel plate and is beneficial to suppressing the Austrian The growth of the austenite and refine the final structure, so as to achieve a higher strength after hot stamping of the steel plate.
  • the technical solution described in the present invention obtains a small amount of ferrite + lower bainite structure by controlling the content of Ti, B and other elements, combined with controlled rolling and controlled cooling, which improves the plasticity and fatigue performance of the steel plate and is very suitable for use in Manufacturing axle housings.
  • FIG. 1 is a metallurgical structure diagram of 800 MPa hot stamping axle housing steel of Example 2.
  • FIG. 1 is a metallurgical structure diagram of 800 MPa hot stamping axle housing steel of Example 2.
  • FIG. 2 is a metallurgical structure diagram of 800 MPa grade hot stamping axle housing steel of Example 3.
  • FIG. 1 is a metallurgical structure diagram of 800 MPa grade hot stamping axle housing steel of Example 3.
  • FIG. 3 is a scanning metallographic structure diagram of 800 MPa hot stamping axle housing steel of Example 2.
  • FIG. 3 is a scanning metallographic structure diagram of 800 MPa hot stamping axle housing steel of Example 2.
  • FIG. 4 is a scanning metallographic structure diagram of 800 MPa grade hot stamping axle housing steel of Example 3.
  • FIG. 4 is a scanning metallographic structure diagram of 800 MPa grade hot stamping axle housing steel of Example 3.
  • FIG. 5 schematically shows the size, morphology and distribution of typical inclusions of the 800 MPa hot stamping axle housing steel of Example 1.
  • FIG. 5 schematically shows the size, morphology and distribution of typical inclusions of the 800 MPa hot stamping axle housing steel of Example 1.
  • FIG. 6 schematically shows the size, morphology and distribution of typical inclusions of the 800 MPa hot stamping axle housing steel of Example 2.
  • FIG. 6 schematically shows the size, morphology and distribution of typical inclusions of the 800 MPa hot stamping axle housing steel of Example 2.
  • FIG. 7 schematically shows the size, morphology and distribution of typical inclusions of the 800 MPa hot stamping axle housing steel of Example 3.
  • FIG. 7 schematically shows the size, morphology and distribution of typical inclusions of the 800 MPa hot stamping axle housing steel of Example 3.
  • FIG. 8 schematically shows the size, morphology and distribution of typical inclusions of the 800 MPa hot stamping axle housing steel of Example 4.
  • FIG. 8 schematically shows the size, morphology and distribution of typical inclusions of the 800 MPa hot stamping axle housing steel of Example 4.
  • Table 1 lists the mass percentage of each chemical element in the 800 MPa class hot stamping axle housing steel of Examples 1-6.
  • the 800 MPa grade hot stamping axle housing steels of Examples 1-6 were prepared using the following steps (see Table 2 for specific process parameters):
  • the slab is heated in a furnace with a target temperature ranging from 1180 to 1270 ° C. After the core of the slab is heated to the target temperature, heat preservation is started, and the heat preservation time is> 1.5h. ;
  • Cooling cooling in two stages after rolling, first cooling the steel plate at a rate of 80-200 ° C / s to 680-730 ° C, natural air cooling for 5-7s; then cooling the steel plate at a rate of 30-70 ° C / s To 360 ⁇ 450 °C, then coiled or natural air cooled to room temperature.
  • Table 2 lists the specific process parameters of the method for manufacturing the 800 MPa hot stamping axle housing steel of Examples 1-6.
  • the performance test was performed on the 800 MPa grade hot stamping axle housing steel of Examples 1-6, and the test results are listed in Table 3. Among them, the tensile test (yield strength, tensile strength, elongation) is tested using GB / T 228.1-2010 "Metal material room temperature tensile test method” standard, and the impact test GB / T 229-2007 “Metal material Charpy pendulum Impact test method "standard test.
  • the 800 MPa grade hot stamped axle housing steel of Examples 1-6 has a yield strength ⁇ 800 MPa, a tensile strength ⁇ 900 MPa, an elongation A 50 ⁇ 22%, and an impact energy -20 ° C ⁇ 60J. It can be seen from this that the 800 MPa class hot stamping axle housing steel of each embodiment of the present case can reach 800 MPa strength level. At the same time, the 800 MPa class hot stamping axle housing steel has good plasticity and fatigue performance, and is very suitable for manufacturing axle housings.
  • Figure 1 and Figure 2 were taken with LEICACTR6500 optical metallurgical microscope, which was taken at 200 times magnification.
  • Figures 3 and 4 use the JCM7000 scanning electron microscope, which was taken at 20,000 and 10,000 times magnification, respectively.
  • Figures 5 to 8 were taken with the LEICACTR6500 optical metallurgical microscope, magnified 50 times and referenced to the national standard "Microscopic Inspection Method for the Standard Rating Chart for the Determination of the Content of Nonmetallic Inclusions in Steel" (GB / T 10561-2005).
  • FIG. 1 is a metallurgical structure diagram of 800 MPa hot stamping axle housing steel of Example 2.
  • FIG. 2 is a metallurgical structure diagram of 800 MPa grade hot stamping axle housing steel of Example 3.
  • FIG. 1 is a metallurgical structure diagram of 800 MPa hot stamping axle housing steel of Example 2.
  • FIG. 2 is a metallurgical structure diagram of 800 MPa grade hot stamping axle housing steel of Example 3.
  • microstructure of the 800 MPa grade hot stamping axle housing steel of Examples 2 and 3 of the present case is ferrite + lower bainite, and the comparative example of ferrite is 5-10%.
  • FIG. 3 is a scanning metallographic structure diagram of 800 MPa hot stamping axle housing steel of Example 2.
  • FIG. 4 is a scanning metallographic structure diagram of 800 MPa grade hot stamping axle housing steel of Example 3.
  • the average width of the lower bainite lath in FIG. 4 is ⁇ 400 nm.
  • Nanoscale TiC interphase precipitates are formed in the ferrite of 800 MPa grade hot stamped axle housing steel in Example 2 of this case, where the particle diameter of more than 70% of the TiC interphase precipitates in ferrite is below 30 nm.
  • the 800 MPa hot stamping axle housing steel of Example 3 lower bainite is precipitated, and the width of the lower bainite lath is 300 nm or less.
  • FIGS. 5 to 8 and Table 4 schematically shows the size, morphology and distribution of inclusions of the 800 MPa hot stamping axle housing steel of Example 1.
  • 6 schematically shows the size, morphology and distribution of inclusions in the 800 MPa hot stamping axle housing steel of Example 2.
  • FIG. 7 schematically shows the size, morphology and distribution of inclusions in the 800 MPa hot stamping axle housing steel of Example 3.
  • FIG. 8 schematically shows the size, morphology and distribution of inclusions in the 800 MPa hot stamping axle housing steel of Example 4.
  • FIG. 5 schematically shows the size, morphology and distribution of inclusions of the 800 MPa hot stamping axle housing steel of Example 1.
  • 6 schematically shows the size, morphology and distribution of inclusions in the 800 MPa hot stamping axle housing steel of Example 2.
  • FIG. 7 schematically shows the size, morphology and distribution of inclusions in the 800 MPa hot stamping axle housing steel of Example 3.
  • FIG. 8 schematically shows the size, morphology and distribution of inclusions in the 800 MP
  • Table 4 lists the non-metallic inclusion rating results for the 800 MPa hot stamping axle housing steel of Examples 1-6.
  • the 800 MPa hot stamping axle housing steel described in this case is designed by reasonably optimizing alloy elements, and controlling the ratio of each alloy element and the level of inclusions, and at the same time, the process is controlled by rolling and cooling to obtain The required microstructure is obtained, a small amount of ferrite + lower bainite is obtained, and a large number of nano-scale TiC particles are formed in the ferrite, so that the final 800MPa hot stamping bridge shell steel can reach more than 800MPa
  • the yield strength, combined with good plasticity, low temperature toughness and fatigue performance, is very suitable for high-strength weight reduction of hot stamping axle housings.

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PCT/CN2019/111982 2018-10-19 2019-10-18 一种800MPa级热冲压桥壳钢及其制造方法 WO2020078472A1 (zh)

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